=LDR 03286nas a2200733 i 4500 =001 MPC001 =003 IN-ChSCO =005 20120920061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 120920c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed Sep. 20, 2012). =588 \\$aLatest issue consulted: Volume 1, Issue 1 (viewed Sep. 20, 2012). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/112012.htm =LDR 03286nas a2200733 i 4500 =001 MPC008 =003 IN-ChSCO =005 20151231061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 151231c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed Dec. 31, 2015). =588 \\$aLatest issue consulted: Volume 4, Issue 3 (viewed Dec. 31, 2015). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/432015.htm =LDR 03286nas a2200733 i 4500 =001 MPC006 =003 IN-ChSCO =005 20150515061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 150515c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed May 15, 2015). =588 \\$aLatest issue consulted: Volume 4, Issue 1 (viewed May 15, 2015). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/332014.htm =LDR 03286nas a2200733 i 4500 =001 MPC007 =003 IN-ChSCO =005 20150929061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 150929c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed Sep. 29, 2015). =588 \\$aLatest issue consulted: Volume 4, Issue 2 (viewed Sep. 29, 2015). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/422015.htm =LDR 03286nas a2200733 i 4500 =001 MPC009 =003 IN-ChSCO =005 20160331061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 160331c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed Mar. 31, 2016). =588 \\$aLatest issue consulted: Volume 5, Issue 1 (viewed Mar. 31, 2016). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/512016.htm =LDR 03286nas a2200733 i 4500 =001 MPC014 =003 IN-ChSCO =005 20170624061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 170624c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed June 24, 2017). =588 \\$aLatest issue consulted: Volume 6, Issue 1 (viewed June 24, 2017). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/612017.htm =LDR 03286nas a2200733 i 4500 =001 MPC015 =003 IN-ChSCO =005 20170624061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 170624c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed June 24, 2017). =588 \\$aLatest issue consulted: Volume 6, Issue 2 (viewed June 24, 2017). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/622017.htm =LDR 03286nas a2200733 i 4500 =001 MPC016 =003 IN-ChSCO =005 20170624061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 170624c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed June 24, 2017). =588 \\$aLatest issue consulted: Volume 6, Issue 3 (viewed June 24, 2017). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/632017.htm =LDR 03286nas a2200733 i 4500 =001 MPC017 =003 IN-ChSCO =005 20171226061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 171226c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed Dec. 26, 2017). =588 \\$aLatest issue consulted: Volume 6, Issue 4 (viewed Dec. 26, 2017). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/642017.htm =LDR 03286nas a2200733 i 4500 =001 MPC018 =003 IN-ChSCO =005 20171226061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 171226c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed Dec. 26, 2017). =588 \\$aLatest issue consulted: Volume 6, Issue 5 (viewed Dec. 26, 2017). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/652017.htm =LDR 03286nas a2200733 i 4500 =001 MPC019 =003 IN-ChSCO =005 20180405061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 180405c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed April 05, 2018). =588 \\$aLatest issue consulted: Volume 7, Issue 1 (viewed April 05, 2018). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/712018.htm =LDR 03286nas a2200733 i 4500 =001 MPC020 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1 (2012); title from table of contents page (publisher's website, viewed April 05, 2018). =588 \\$aLatest issue consulted: Volume 7, Issue 2 (May 2018) (viewed February 11, 2019). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/722018.htm =LDR 03286nas a2200733 i 4500 =001 MPC021 =003 IN-ChSCO =005 20190527061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190527c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed April 05, 2018). =588 \\$aLatest issue consulted: Volume 8, Issue 2 (January 2019) (viewed May 27, 2019). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/822019.htm =LDR 03286nas a2200733 i 4500 =001 MPC022 =003 IN-ChSCO =005 20200125061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200125c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed April 05, 2018). =588 \\$aLatest issue consulted: Volume 8, Issue 3 (September 2019) (viewed Jan 25, 2020). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/832019.htm =LDR 03286nas a2200733 i 4500 =001 MPC023 =003 IN-ChSCO =005 20200125061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200125c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed April 05, 2018). =588 \\$aLatest issue consulted: Volume 8, Issue 4 (September 2019) (viewed Jan 25, 2020). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/842019.htm =LDR 03286nas a2200733 i 4500 =001 MPC024 =003 IN-ChSCO =005 20200125061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200125c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed April 05, 2018). =588 \\$aLatest issue consulted: Volume 8, Issue 5 (October 2019) (viewed Jan 25, 2020). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/852019.htm =LDR 03286nas a2200733 i 4500 =001 MPC025 =003 IN-ChSCO =005 20200125061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200125c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed April 05, 2018). =588 \\$aLatest issue consulted: Volume 8, Issue 6 (November 2019) (viewed Jan 25, 2020). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/862019.htm =LDR 03286nas a2200733 i 4500 =001 MPC026 =003 IN-ChSCO =005 20200125061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200125c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed April 05, 2018). =588 \\$aLatest issue consulted: 2019 Volume 8, Issue 1 (viewed Jan 25, 2020). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/812019.htm =LDR 03286nas a2200733 i 4500 =001 MPC027 =003 IN-ChSCO =005 20201013061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201013c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed October 13, 2020). =588 \\$aLatest issue consulted: 2020 Volume 9, Issue 2 (July 2020) (viewed October 13, 2020). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/922020.htm =LDR 03286nas a2200733 i 4500 =001 MPC028 =003 IN-ChSCO =005 20201013061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201013c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed October 13, 2020). =588 \\$aLatest issue consulted: 2020 Volume 9, Issue 3 (August 2020) (viewed October 13, 2020). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/932020.htm =LDR 03286nas a2200733 i 4500 =001 MPC029 =003 IN-ChSCO =005 20201013061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201013c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed October 13, 2020). =588 \\$aLatest issue consulted: 2020 Volume 9, Issue 4 (September 2020) (viewed October 13, 2020). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/942020.htm =LDR 03286nas a2200733 i 4500 =001 SCOPEJ031 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504c20129999pau|||||o|||||||||||eng|| =022 \\$z2379-1365 =022 \\$a2165-3992 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization $h[electronic resource]. =246 3\$aMPC =246 3\$aASTM International materials performance and characterization =264 \1$aWest Conshohocken, Pa. :$bASTM International, $c2012. =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVol. 1, issue 1- =530 \\$aAlso available online via the World Wide Web. Tables of contents and abstracts freely available; full-text articles available by subscription. =588 \\$aDescription based on: Vol. 1, issue 1; title from table of contents page (publisher's website, viewed January 12, 2021). =588 \\$aLatest issue consulted: 2020 Volume 9, Issue 1 (October 2020) (viewed May 04, 2021). =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aComposite materials$vPeriodicals. =650 \0$aPolymers $vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tASTM Materials performance and characterization. =776 08$iPrint version: $tMaterials performance and characterization.$dWest Conshohocken, Pa. : ASTM International, 2012-$z2379-1365 =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/912020.htm =LDR 01427nas 2200301 a 4500 =001 SCOPEJ032 =005 20210723061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210723c20129999pau|||||o||||||||||0eng|d =022 \\$z2379-1365 =022 \\$a2165-3992 =030 \\$aMPCACD =040 \\$aASTM$cSCOPE =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization $h[electronic resource]. =246 3\$aMPC =246 3\$aASTM International materials performance and characterization =264 \1$aWest Conshohocken, Pa. :$bASTM International, $c2012. =310 \\$aAnnual =362 0\$aVol. 1, issue 1- =530 \\$aAlso available online via the World Wide Web. Tables of contents and abstracts freely available; full-text articles available by subscription. =588 \\$aDescription based on: Vol. 1, issue 1; title from table of contents page (publisher's website, viewed January 12, 2021). =588 \\$aLatest issue consulted: 2021 Volume 10, Issue 2 (June 2021) (viewed July 23, 2021). =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aComposite materials$vPeriodicals. =650 \0$aPolymers $vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tASTM Materials performance and characterization. =776 08$iPrint version: $tMaterials performance and characterization.$dWest Conshohocken, Pa. : ASTM International, 2012-$z2379-1365 =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/TOC/1022021.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140034 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140034$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140034$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN695 =082 04$a671.37$223 =100 1\$aOluwasegun, K.,$eauthor. =245 10$aAppraisal of Solution Heat Treatment on Elimination of Hafnium Rich γ–γ Eutectic and Prior Particle Boundary Precipitate in a Superalloy Powder /$cK. Oluwasegun, J. Olawale, M. Adeoye, O. Olorunniwo, O. Ige, P. Atanda. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b35 =520 3\$aNear-net shape hot isostatic pressing (HIPping) in powder metallurgy (P/M) has been on the increase in the production of superalloys for aero and land based turbine disc applications. A critical challenge related to net-shape HIPping PM is the presence hafnium rich γ–γ eutectic in some superalloys powder, which promotes the formation of hafnium oxide. This encourages the formation of prior particle boundary (PPB) precipitates during HIPping, which decreases the bonding strength between powder particles during HIPping and thus becomes the crack initiation and growth sites under loading. Hence, this study aims at dissolving hafnium rich γ–γ eutectic in RR1000 superalloy powder and eliminating the PPB precipitates after HIPping by heat treating the powder prior HIPping. As-received powder was heat treated at 900, 1000, 1100, and 1200°C for 2 h, and their microstructure was characterized before the application of pressure for its consolidation. From the outcome of the study, 1200°C was found to be the optimum heat treatment temperature where hafnium rich γ–γ eutectic dissolved and where prior particle boundary (PPB) precipitates were eliminated during HIPping for the RR1000 superalloy powder studied. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aHot isostatic pressing. =650 \0$aMetallurgy. =650 \0$apowder metallurgy. =650 \0$aPrior particle boundary precipitates. =650 \0$asuperalloys powder. =650 \0$aTurbine disc. =650 14$aHot isostatic pressing. =650 24$aPowder metallurgy. =650 24$aPrior particle boundary precipitates. =650 24$aSuperalloys powder. =650 24$aTurbine disc. =700 1\$aAdeoye, M.,$eauthor. =700 1\$aAtanda, P.,$eauthor. =700 1\$aIge, O.,$eauthor. =700 1\$aOlawale, J.,$eauthor. =700 1\$aOlorunniwo, O.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140034.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140043 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140043$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140043$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP860.5 =082 04$a666.1$223 =100 1\$aManjunatha, C.,$eauthor. =245 10$aEnhanced Fatigue Performance of a Polymer Nanocomposite under Spectrum Loads /$cC. Manjunatha, Ramesh Bojja, N. Jagannathan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b43 =520 3\$aA thermosetting epoxy polymer was modified by incorporating 10 wt. % of silica nanoparticles, which were well dispersed in the polymer. Two different glass-fiber-reinforced plastic (GFRP) composite laminates were prepared to give: (1) a GFRP composite with an unmodified epoxy matrix (GFRP neat), and (2) a GFRP composite with a silica-nanoparticle-modified epoxy matrix (GFRP nano). Fatigue tests were undertaken employing a standard wind-turbine spectrum-load sequence, WISPERX. The fatigue life of the GFRP nanocomposite was about four times longer than that of the GFRP neat composite. This was reflected in (1) the development of matrix cracking, and (2) the rate of degradation of the stiffness of the composite, both being more severe in the GFRP neat composite, compared to the GFRP nanocomposite. The underlying mechanisms for the observed improvement in the spectrum fatigue life of the GFRP nanocomposite are discussed. Further, constant amplitude fatigue tests were conducted at various stress ratios. Using the static and fatigue data, constant life diagrams (CLD) were constructed. The spectrum fatigue life was then predicted following a standard procedure using the CLD. Very good correlation was observed between the predicted and experimental fatigue life for both GFRP neat and GFRP nanocomposites. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFatigue. =650 \0$aglass fiber. =650 \0$aLife prediction. =650 \0$amatrix cracking. =650 \0$ananocomposite. =650 14$aNanocomposite. =650 24$aFatigue. =650 24$aGlass fiber. =650 24$aLife prediction. =650 24$aMatrix cracking. =700 1\$aBojja, Ramesh,$eauthor. =700 1\$aJagannathan, N.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140043.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140020 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140020$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140020$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357.5.C38 =082 04$a620.1064$223 =100 1\$aMeged, Y.,$eauthor. =245 10$aDuctility and Brittleness in Rotating Disc Cavitation Erosion Testing /$cY. Meged. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b10 =520 3\$aDuctile and brittle failures have been long detected in metallic specimens when tested in tensile and impact tests. Recent observations indicate that these failures occur in cavitation erosion tests as well. Brittle failures in cavitation erosion tests take place under high cavitation loads, especially in rotating disc (RD) rigs. In the framework of the international cavitation erosion test (ICET), 264 tests were performed using seven test methods. One of these methods, the RD, proved to exert the highest cavitation erosion load on the test specimens, resulting in 29 brittle failures in 50 tests. The high percentage of brittle failures called for a close study of this failure mode, as detected in testing of five ICET reference metallic materials. In some cases, areas in the erosion-time domain were located, in which the ductile-to-brittle transition is highly probable. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$abrittleness. =650 \0$aCavitation erosion tests. =650 \0$acavitation erosion. =650 \0$aDuctility. =650 \0$aICET reference materials. =650 \0$arotating disc test. =650 14$aCavitation erosion tests. =650 24$aBrittleness. =650 24$aDuctility. =650 24$aICET reference materials. =650 24$aRotating disc test. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140020.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130092 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130092$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130092$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQE601.2 =082 04$a552/.06$223 =100 1\$aSharma, V.,$eauthor. =245 10$aLow Cycle Fatigue Behavior of AA2219-T87 at Room Temperature /$cV. Sharma, G. Rao, S. Sharma, Koshy George. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b27 =520 3\$aThe low cycle fatigue behavior of AA2219-T87 was studied at ambient temperature using fully reversed total strain controlled fatigue tests in longitudinal and transverse orientations. Tension-compression cyclic tests were carried out under total strain amplitude control with strain ratio R? = –1 and at a frequency of 0.5 Hz. The total strain amplitude was varied from ±0.4 to ±1.5 %. The low cycle fatigue results were analyzed to determine the cyclic stress strain curves. The cyclic strain hardening parameters were evaluated from the cyclic stress-strain curves. Important fatigue parameters namely fatigue ductility coefficient, fatigue ductility exponent, and fatigue strength coefficient were evaluated. The material exhibited cyclic strain softening in both longitudinal and transverse directions. Analysis of the experimental results showed that the stress-strain hysteresis loops exhibited inflections in the first few cycles and the plastic strain amplitude versus fatigue-life plots exhibited bi-linear relationship. The geometry of hysteresis loops and the occurrence of Masing behavior are analyzed and found that the alloy in peak aged condition exhibited tendency towards Masing behavior. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum alloys. =650 \0$aCyclic stress-strain curve. =650 \0$aFatigue testing. =650 \0$afractography. =650 \0$alow cycle fatigue. =650 \0$aStrain-life plots. =650 14$aFatigue testing. =650 24$aAluminum alloys. =650 24$aCyclic stress-strain curve. =650 24$aFractography. =650 24$aLow cycle fatigue. =650 24$aStrain-life plots. =700 1\$aGeorge, Koshy,$eauthor. =700 1\$aRao, G.,$eauthor. =700 1\$aSharma, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130092.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130040 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130040$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130040$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD9705.5.B434 =082 04$a338.7/669142/0973$223 =100 1\$aManigandan, K.,$eauthor. =245 14$aThe Cyclic Strain Resistance, Stress Response, Fatigue Life, and Fracture Behavior of a High Performance Alloy Steel /$cK. Manigandan, T. Srivatsan, D. Tammana, B. Poorganji, V. Vasudevan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b31 =520 3\$aIn this paper, the results of a recent study aimed at understanding the role of microstructure on cyclic stress response, cyclic strain resistance, deformation, fatigue life, and fracture behavior of the high strength alloy steel PremoMet 290 is presented and discussed. The cyclic strain amplitude-controlled fatigue properties, deformation, and resultant fracture behavior of the alloy steel specimens are discussed when cyclically deformed over a range of strain amplitudes. The intrinsic mechanisms governing stress response, stress versus strain response fatigue life, deformation, and final fracture behavior are presented and discussed in light of the competing and mutually interactive influences of intrinsic microstructural effects, deformation characteristics of the microstructural constituents, cyclic strain amplitude, and concomitant response stress. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAlloy steel. =650 \0$aBearings industry. =650 \0$aCyclic strain amplitude. =650 \0$aDeformation and fracture. =650 \0$aFatigue life. =650 \0$aMachine parts industry. =650 \0$aMicrostructure. =650 \0$aSteel alloy industry. =650 \0$aStress response. =650 14$aAlloy steel. =650 24$aCyclic strain amplitude. =650 24$aDeformation and fracture. =650 24$aFatigue life. =650 24$aMicrostructure. =650 24$aStress response. =700 1\$aPoorganji, B.,$eauthor. =700 1\$aSrivatsan, T.,$eauthor. =700 1\$aTammana, D.,$eauthor. =700 1\$aVasudevan, V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130040.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130022 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130022$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130022$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD181.U7 =082 04$a353.008722$223 =100 1\$aWoydt, Mathias,$eauthor. =245 10$aSlip-Rolling Resistance and Load Carrying Capacity of 36NiCrMoV1-5-7 Steel /$cChristian Scholz, Mathias Woydt, Hardy Mohrbacher. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b20 =520 3\$aThe approaching CO2 targets have now enforced automotive OEMs to engage R&D efforts also in powertrain to reduce friction, increase lifetime properties, and load carrying capacities of running systems. Martensitic steels such as 36NiCrMoV1-5-7 have a great potential to be used in automotive powertrain applications due to its favorable mechanical properties. In order to realize lightweight strategies, it is essential that steels with improved fracture toughness values and higher annealing temperatures with regard to higher contact pressures and possible thin film coating application be considered. State-of-the-art steels, like 16MnCr5, 21NiCrMo, 30CrMoV9, and 100Cr6 are not able to sustain a further increase in torque or load during operating time as well as annealing effects under higher oil or deposition temperatures. Therefore, the recent research on the slip-rolling resistance, frictional, and wear behavior of steels such as 36NiCrMoV1-5-7, Cronidur 30 (AMS 5898), 20MnCr5 (SAE 4820 or 5120), and 100Cr6H (SAE E52100) showed that possible lean alloying concept alternatives with promising performance characteristics are already available. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBearing. =650 \0$aDiagnostic Imaging. =650 \0$aGear. =650 \0$aHigh contact pressure. =650 \0$aMolybdenum$xisolation & purification. =650 \0$aMolybdenum. =650 \0$aOil. =650 \0$aQuality Control. =650 \0$aSlip-rolling resistance. =650 \0$aSteel. =650 14$aMolybdenum. =650 24$aBearing. =650 24$aGear. =650 24$aHigh contact pressure. =650 24$aOil. =650 24$aSlip-rolling resistance. =650 24$aSteel. =700 1\$aMohrbacher, Hardy,$eauthor. =700 1\$aWoydt, Mathias,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130022.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120002 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120002$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120002$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ1075 =082 04$a621.8/9$223 =100 1\$aWoydt, Mathias,$eauthor. =245 10$aStribeck-Type Curves of Alternative Engine Oils :$nPart I :$bGray Cast Iron Liners /$cMathias Woydt, Norbert Kelling, Falk Hannemann, Niklas Berberich, Holger Ziegele. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aWear tests are often used in engine development in order to characterize the functional profile of surfaces interacting with lubricants. This paper proposes a new test procedure to determine Stribeck-type curves for the tribosystem piston ring/cylinder liner involving test pieces prepared from engine components. The variation of the friction coefficient with sliding speed depends on the structure and constitution of the base oil, the viscosity index, the surface topography of the liner and ring, and the friction modifiers used. Novel organic friction modifiers of low molecular mass not only reduce the friction coefficients under mixed / boundary lubrication, but also in the fluid film regime. In addition, the influence of surface roughness on the wettability of surfaces can be significant for both static and dynamic wetting. For this reason, the interaction of the lubricant with the surfaces was also investigated to enable a correlation between the surface properties of the liquid and solid phases and the tribological behavior. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAutomotive. =650 \0$aLubrication and lubricants$vHandbooks, manuals, etc. =650 \0$aLubrication and lubricants. =650 \0$aLubrication. =650 \0$aMaterials. =650 \0$aMixed/boundary lubrication. =650 \0$aPiston ring/cylinder. =650 \0$aSurface topography. =650 \0$aTribology. =650 \0$aWear tests. =650 \0$aWetting. =650 14$aTribology. =650 24$aAutomotive. =650 24$aLubrication. =650 24$aMaterials. =650 24$aMixed/boundary lubrication. =650 24$aPiston ring/cylinder. =650 24$aSurface topography. =650 24$aWear tests. =650 24$aWetting. =700 1\$aBerberich, Niklas,$eauthor. =700 1\$aHannemann, Falk,$eauthor. =700 1\$aKelling, Norbert,$eauthor. =700 1\$aZiegele, Holger,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120002.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130017 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130017$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130017$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.23 =082 04$a548.028$223 =100 1\$aKalpana Nayak, I.,$eauthor. =245 10$aDepth Profiling of Residual Stress for Shot-Peened “U”-Bend Alloy-800 Tubes for the PHWR Steam Generator /$cI. Kalpana Nayak, S. Ramana Rao, K. Kapoor. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b11 =520 3\$aResidual tensile stresses influence the mechanical behavior in terms of fatigue and fracture resistance, stress corrosion behavior, and dimensional stability of critical components of nuclear reactors. Glass-bead shot-peened “U”-bend Alloy-800 tubes are used as steam generators in pressurized heavy water reactors (PHWRs), where stress corrosion cracking is the common cause of its premature failure. Therefore, compressive residual stresses are induced by glass-bead shot peening to overcome the tensile stresses generated more along the bend region. The variation of these compressive residual stresses as a function of depth from the surface has been estimated by successive material removal followed by stress measurement. Optimization of electropolishing parameters for removal of a fixed amount of material is carried out. Stepwise removal of material by electropolishing is proved to be better for stress analysis instead of removal “at-a-time.” Effect of shot-peening pressure is also studied as a function of stress pattern developed along the depth from the surface of the straight tube and bent tube. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCompressive residual stress. =650 \0$aDepth profiling. =650 \0$aElectropolishing. =650 \0$aGlass-bead shot peening. =650 \0$aMaterials$xMicroscopy. =650 \0$aSteam generator tube. =650 \0$aTransmission electron microscopy. =650 \0$aX-ray crystallography. =650 \0$aX-ray diffraction. =650 14$aSteam generator tube. =650 24$aAlloy 800. =650 24$aCompressive residual stress. =650 24$aDepth profiling. =650 24$aElectropolishing. =650 24$aGlass-bead shot peening. =650 24$aX-ray diffraction. =700 1\$aKapoor, K.,$eauthor. =700 1\$aRamana Rao, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130017.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130035 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130035$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130035$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357.5.C38 =082 04$a620.1064$223 =100 1\$aMeged, Y.,$eauthor. =245 10$aEvaluation of Fifty-Two Cavitation Erosion Tunnel Tests /$cY. Meged. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b7 =520 3\$aIn the framework of the International Cavitation Erosion Test (ICET), 52 cavitation erosion tests were performed in cavitation tunnels. These tests were performed by six labs in eight test groups, on five metallic reference materials. The subjects studied are: cavitation erosion trail, test specimen, calculation of mean depth of erosion (MDE), values, cavitation erosion-time curves, measuring accuracy, variation of test results, and material classification. In all these categories, deficiencies were detected such as: lack of data on eroded areas, water flow velocity at the specimen's surface, and an evaluation misconception based on the assumption that the eroded area is equal to the specimen area. These deficiencies cast heavy doubt on the reliability of the test results. Only eighteen tests were found relevant for obtaining quantitative data. Recommendations are made to overcome some of the detected deficiencies and to improve both reliability and applicability of future cavitation erosion tunnel test results. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCavitation erosion. =650 \0$aCavitation tunnel tests. =650 \0$aCavitation. =650 \0$aEroded area. =650 \0$aErosion trail. =650 \0$aErosion. =650 \0$aInternational Cavitation Erosion Test. =650 \0$aReference materials. =650 \0$aTest specimen. =650 \0$avibratory cavitation erosion. =650 14$aCavitation erosion. =650 24$aCavitation tunnel tests. =650 24$aEroded area. =650 24$aErosion trail. =650 24$aInternational Cavitation Erosion Test. =650 24$aMDE calculations. =650 24$aReference materials. =650 24$aTest specimen. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130035.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140024 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140024$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140024$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTH7687.5 =082 04$a697$223 =100 1\$aOlawale, J.,$eauthor. =245 10$aProduction of Austempered Gray Iron (AGI) Using Forced Air Cooling /$cJ. Olawale, K. Oluwaseguun, D. Ezemenaka, S. Adisa. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b31 =520 3\$aThis paper presents the outcome of the production of austempered gray iron (AGI) using forced air cooling as the quenching medium. Samples from Class 20 gray cast iron were prepared for micrographic analysis, x-ray diffraction (XRD) analysis, and mechanical testing. The prepared samples were austenitized at 920°C, soaked for 1 h, force air-cooled to the austempering temperature range of 250°C to 400°C (at 25°C intervals), held for another hour at the austempered temperature to allow for complete phase transformation, and then air-cooled to room temperature. The optical micrograph revealed a unique microstructure consisting of ferrite (?) and high carbon austenite (?HC) called ausferrite, the coarseness of which increases as the austempering temperatures increases. XRD analysis revealed only the peak of the ? phase. The estimated effective particle size d? of this phase increases with an increase in austempering temperature. The results of mechanical tests showed significant increases in the tensile strength, hardness, toughness, and ductility of austempered samples of Class-20 grade gray cast iron. Conclusively, AGI has a unique combination of high strength and ductility that makes it suitable for the manufacture of parts in which high strength, high wear resistance, and high ductility are required. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAir Cooling. =650 \0$aAusferrite. =650 \0$aaustempering. =650 \0$aClass 20 gray cast iron. =650 \0$aFerrite. =650 \0$agraphite flakes. =650 14$aClass 20 gray cast iron. =650 24$aAusferrite. =650 24$aAustempering. =650 24$aFerrite. =650 24$aGraphite flakes. =700 1\$aAdisa, S.,$eauthor. =700 1\$aEzemenaka, D.,$eauthor. =700 1\$aOluwaseguun, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140024.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130025 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130025$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130025$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC569.5.P37 =082 04$a616.85/8$223 =100 1\$aBaragetti, S.,$eauthor. =245 10$aNotch Effect and Fatigue Performance of Ti-6Al-4 V Sheets in Saline Environment /$cS. Baragetti, R. Gerosa. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b12 =520 3\$aTi-6Al-4 V grade is a well-known and largely employed alloy for many critical applications, especially when high mechanical and corrosion properties are needed. In the technical literature one of its negative aspects, i.e., its notch sensitivity in case of fatigue loading, especially in aggressive environments, is well described. The present experimental work is, hence, aimed at studying the fatigue behavior of notched Ti-6Al-4 V alloy samples (machined from a 5-mm-thick sheet) in standard laboratory conditions and in a saline solution with 3.5 wt. % NaCl. Axial fatigue (R = 0.1) loading was chosen and different notches were machined to obtain Kt values ranging from 2.55 to 13.34 [calculated by finite element method (FEM)]. By the step-loading technique, the fatigue limits for a constant life of 2 x 105 cycles varying the Kt factor and the test environment were determined. Finally, by replicas, the fatigue-crack lengths were measured and, by scanning electron microscopy (SEM), the fracture surfaces were observed and related with the fatigue-crack propagation rates. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aaggressive environment. =650 \0$aaggressive. =650 \0$aFatigue. =650 \0$aNotch sensitivity. =650 \0$aPassive-aggressive personality. =650 14$aFatigue. =650 24$aAggressive environment. =650 24$aNotch sensitivity. =700 1\$aGerosa, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130025.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130023 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130023$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130023$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.A5 =082 04$a669/.722$223 =100 1\$aBrown, Lloyd,$eauthor. =245 10$aPhysical and Mechanical Characterization of a Nanocarbon Infused Aluminum-Matrix Composite /$cLloyd Brown, Peter Joyce, David Forrest, Lourdes Salamanca-Riba. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b17 =520 3\$aA new class of nanocarbon-infused materials, termed covetics, has been developed by Third Millennium Materials, LLC. In this paper we have evaluated the enhanced performance prospects for strength and electrical conductivity of a nanocarbon infused 6061 aluminum composite by comparing properties to those of 6061 aluminum. Unlike most metal matrix carbon composites, this material is unique in that the nanocarbon is so strongly bound to the metal that it is stable in the molten state. The proprietary manufacturing process is still in the early stages of development, and we had an opportunity to evaluate a limited amount of extruded 6061 aluminum covetic sample material. This paper examines the effects of covetic processing on the physical, electrical, and mechanical properties of 6061 aluminum using chemical, optical, and scanning electron microscopy, density measurement, microindentation hardness testing, electrical conductivity measurement, quasi-static tensile testing, and high strain-rate compression (Hopkinson bar) testing. In the as-extruded condition (warm worked at 227°C) the results show that the nanocarbon provides approximately a 30 % improvement in yield strength compared to baseline 6061-T0. This could be explained using electron microscopy observations which showed that the covetic 6061 was more resistant to grain growth and coarsening during extrusion. High strain rate, Split Hopkinson Pressure Bar (SHPB) tests revealed an opposite trend-the as-extruded covetic material exhibited lower stresses at equivalent strains. However, 6061 aluminum is not normally processed in the low strength as-extruded condition, so the covetic material was heat treated to the T6 condition. In the T6 condition, the strength and ductility of 6061 with and without 3 wt. % nanocarbon were approximately equal at all strain rates. Whereas the nanoscale carbon increased the electrical conductivity of 6061 by 43 % in the as-extruded condition, the conductivity only improved 15 %-19 % in the T6 condition. The nanocarbon/aluminum composite displays potential as an improved strength aluminum alloy with much higher electrical conductivity than is typical for other aluminum alloys and aluminum matrix composites. This study identified a clear need for standards development for the chemical analysis of nanocarbon in covetic materials. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum alloys$x Metallography. =650 \0$aAluminum alloys. =650 \0$aAluminum-Matrix Composite. =650 \0$aCharacterization. =650 \0$aConductivity. =650 \0$aCovetics. =650 \0$aMetal matrix composites. =650 \0$aNano carbon. =650 \0$aPhysical properties. =650 14$aMetal matrix composites. =650 24$aCharacterization. =650 24$aConductivity. =650 24$aCovetics. =650 24$aNano carbon. =650 24$aPhysical properties. =700 1\$aForrest, David,$eauthor. =700 1\$aJoyce, Peter,$eauthor. =700 1\$aSalamanca-Riba, Lourdes,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130023.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130087 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130087$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130087$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD156 =082 04$a333.730913$223 =100 1\$aYoganandh, J.,$eauthor. =245 10$aErosion Wear Characteristics of Surface Modified Grey Cast Iron by WC-Co-Cr/NiCrBSi Coating Using HVOF Thermal Spray Process /$cJ. Yoganandh, S. Natarajan, S. Kumaresh Babu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b50 =520 3\$aPump casings made of grey cast iron (GCI) used in lignite mines for dewatering are subjected to erosive wear and fail catastrophically. An attempt was made to modify the surface of GCI by WC-Co-Cr/NiCrBSi coating using HVOF process for the application under mining conditions. Grey cast iron samples with and without WC-Co-Cr/NiCrBSi coating were subjected to slurry jet erosion tests by varying the impingent velocity and angle under two different pH conditions of 3 and 7 which pertain to the mining environment. XRD characterization was done to identify and confirm phase composition. Eroded surface morphology studies were carried by SEM on both the substrate and coating, which revealed the erosion of GCI surface, predominantly due to ploughing mechanism. In the case of WC-Co-Cr and NiCrBSi coating, at an oblique angle of impact, the material removal from the surface is by micro cutting of the matrix, ploughing, and abrasive mode mechanisms. At normal impingement, the fluctuating stress creates the cracks, which interlink each other to form lips and craters followed by material degradation through fatigue. Performance of WC-Co-Cr coating is found to be better than NiCrBSi Coating. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aerosion. =650 \0$aGrey cast iron. =650 \0$aNiCrBSi. =650 \0$aSoil erosion. =650 \0$aThermal Spray Process. =650 14$aGrey cast iron. =650 24$aErosion. =650 24$aNiCrBSi. =650 24$aThermal spray process. =650 24$aWC-Co-Cr. =700 1\$aKumaresh Babu, S.,$eauthor. =700 1\$aNatarajan, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130087.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130051 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130051$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130051$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD9705.5.B434 =082 04$a338.7/669142/0973$223 =100 1\$aBind, A.,$eauthor. =245 10$aInfluence of Soaking Temperature and Time on Microstructure and Mechanical Properties of Water Quenched Zr-2.5Nb Alloy /$cH. Khandelwal, R. Singh, A. Bind, S. Sunil, B. Rath, J. Singh, S. Kumar, J. Chakravartty. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aIn heavy water cooled nuclear reactors, Zr-2.5Nb alloy is used for pressure tubes under cold worked and stress relieved (CWSR) condition in Canadian Deuterium Uranium (CANDU) reactors and under quenched and aged condition in RBMK and Fugen reactors. Because of its ease of use and the lower cost of fabrication, most of the work reported in literature is focused on the development and characterization of cold worked and stress relieved pressure tube material. However, recent work showed that the tubes manufactured using quenched and aged route showed a lower and predictable rate of in-reactor deformation during reactor operation as compared to those fabricated using the CWSR route. One of the important stages in the fabrication of heat treated pressure tube material is solution heat treatment (SHT), which governs the microstructure and hence, the mechanical properties of pressure tubes. Usually, SHT is carried out in two phase (? + ?) region at a temperature closer to the ? transus. The present work characterizes the influence of different SHT parameters such as soaking temperature (850, 870, and 890°C) and duration (15 and 30 min) on microstructure, texture, and Nb partitioning between phases and mechanical properties such as tensile properties, hardness, and fracture toughness. Fracture toughness parameters were determined as per ASTM standard E1820-11. Optical microscopy was used for microstructure, X-ray diffraction for texture, and EPMA for Nb partitioning investigation. The fracture surfaces were examined using SEM. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBearings industry. =650 \0$aFracture toughness. =650 \0$aMachine parts industry. =650 \0$aPressure tube. =650 \0$aPressurized heavy water reactor. =650 \0$aSolution heat treatment. =650 \0$aSteel alloy industry. =650 \0$aTensile strength. =650 14$aZr-2.5Nb alloy. =650 24$aFracture toughness. =650 24$aPressure tube. =650 24$aPressurized heavy water reactor. =650 24$aSolution heat treatment. =650 24$aTensile strength. =700 1\$aBind, A.,$eauthor. =700 1\$aChakravartty, J.,$eauthor. =700 1\$aKumar, S.,$eauthor. =700 1\$aRath, B.,$eauthor. =700 1\$aSingh, J.,$eauthor. =700 1\$aSingh, R.,$eauthor. =700 1\$aSunil, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130051.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130021 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130021$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130021$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aBalakrishnan, M.,$eauthor. =245 10$aEffect of Hardfacing Processes on Ballistic Performance of Q&T Steel Joints /$cM. Balakrishnan, V. Balasubramanian, G. Madhusudhan Reddy. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aThis study was carried out to evaluate the effect of hardfacing processes on the ballistic performance of armour grade quenched and tempered (Q&T) steel welded joints. Two joints were fabricated using 4 mm thick tungsten carbide (WC) hardfaced middle layer, above and below which austenitic stainless steel (SS) layers were deposited on both sides of the hardfaced interlayer. Plasma transferred arc (PTA) hardfacing and shielded metal arc (SMA) hardfacing processes were used to deposite WC interlayer. In both joints, SS layers were deposited by shielded metal arc welding (SMAW) process. The fabricated joints were tested for its ballistic performance and the results were compared with respect to depth of penetration (DOP) on weld metal and HAZ locations. From the ballistic test results, it is observed that both the joints successfully stopped the bullet penetration at weld center line. Of the two joints, the joint made with SMA hardfacing offered a maximum resistance to the bullet penetration with a DOP of 16 mm without any bulge at the rear side of the weld center line. The gradual increment in hardness in the front layer is the primary reason for the successful intact of the bullet with a lesser depth of penetration. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBallistic impact. =650 \0$aMetallography. =650 \0$aSandwich structures. =650 \0$aSteel$xMetallurgy. =650 \0$aSteel. =650 \0$aWelding. =650 14$aQuenched and tempered steel. =650 24$aBallistic impact. =650 24$aMetallography. =650 24$aSandwich structures. =650 24$aWelding. =700 1\$aBalasubramanian, V.,$eauthor. =700 1\$aMadhusudhan Reddy, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130021.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140047 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140047$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140047$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357.5.C38 =082 04$a620.1064$223 =100 1\$aMeged, Y.,$eauthor. =245 10$aVibratory Cavitation Erosion With Vibrating and Stationary Specimens /$cY. Meged. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (30 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b5 =520 3\$aIn the framework of the International Cavitation Erosion Test (ICET), 119 vibratory cavitation erosion tests were performed. Seventy of these tests were with vibrating specimens (VRV), and forty-nine with stationary specimens (VRS). From these tests, twenty tests of each type were chosen for this study. VRV tests are covered by ASTM G32-10, whereas for VRS, no standard has yet been published. This anomaly stems from the difficulties encountered in both testing and evaluating of VRS tests. All forty cavitation erosion-time curves were analyzed by the Transient Response for Erosion (TRE) method. For each curve, all three parameters were determined, namely: time lag (TL), time constant (?), and the asymptotic value of the mean depth of erosion, mean depth of erosion (MDE) MDEMAX. These parameters were further applied to calculate the scatter of test results as obtained from various specimens tested under identical conditions. This method enables the determination of the absolute and relative scatter values at any time value along the test. Finally, several guidelines are specified for preparation of a future VRS standard. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$acavitation erosion. =650 \0$aErosion. =650 \0$aStandoff clearance. =650 \0$aStationary specimen. =650 \0$aTransient response for erosion method. =650 \0$aVibrating specimen. =650 \0$avibratory cavitation erosion. =650 14$aVibratory cavitation erosion. =650 24$aICET. =650 24$aStandoff clearance. =650 24$aStationary specimen. =650 24$aTransient response for erosion method. =650 24$aVibrating specimen. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140047.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130048 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130048$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130048$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN719.5 =082 04$a669.1413$223 =100 1\$aAtanda, P.,$eauthor. =245 10$aEffect of Process Parameters on the Microstructures and Mechanical Properties of Iso-Thermally Treated Ductile Iron /$cP. Atanda, O. Olorunniwo, B. Imasogie. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aThe effect of process parameters on the mechanical properties of iso-thermally treated ductile irons was investigated in this study. Sets of ductile irons produced by sandwich method from a rotary furnace melt were given iso-thermal austempering treatments using commercial neutral salt baths. The samples were preheated at 350°C and held for 1 h in a muffle furnace, followed by ausenitizing in an ausenitizing salt bath furnace containing a mixture of BaCl2 and NaCI, (in the ratio 3:2) at 900°C and soaking at that temperature for 1 h. The samples were immediately transferred to the austempering salt bath furnace containing a mixture of NaNO3 and KNO2 in the ratio 1:1. Sets of the samples were soaked at 300°C for between 5 to 240 min and were all later cooled in air. The austempering procedure was repeated at 350 and 400°C for a second and third groups of samples, respectively. The results showed that austempering at lower temperature (300°C) produced a relatively high tensile strength of 1400 MPa, after 150 min holding compared with austempering at the higher temperature (400°C) which produced a relatively lower strength of 1200 MPa at the same holding time. However, the optimal processing window for the austempering was established to be the intermediate temperature of 350°C after a holding time of 150 min. At this processing window, austempering yielded the optimum combination of mechanical properties of 1502 MPa UTS, 7.5 % elongation, and impact energy of 108 J. These properties correspond to a microstructure consisting of a plate-like morphology of ausferrite and retained austenite. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aaustempering. =650 \0$aDuctile Iron. =650 \0$aHardness. =650 \0$aHolding times. =650 \0$aImpact energy. =650 \0$aSandwich. =650 \0$atensile strength. =650 14$aSandwich. =650 24$aAustempering. =650 24$aHardness. =650 24$aHolding times. =650 24$aImpact energy. =650 24$aTensile strength. =700 1\$aImasogie, B.,$eauthor. =700 1\$aOlorunniwo, O.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130048.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130091 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130091$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130091$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.P5 =082 04$a668.4$223 =100 1\$aLeddy, Michael.,$eauthor. =245 10$aEffect of Arthropod Repellents on the Mechanical Properties of Common Materials Used by U.S. Service Members /$cMichael Leddy, Evan Langdale, Louis Jasper, Stephen Belkoff. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b3 =520 3\$aArthropod-borne infectious diseases represent a serious threat to U.S. military personnel, and insect repellents are commonly used as the first line of defense against those illnesses. Recent feedback from the field suggests that currently provided repellents, which are based on N,N-diethyl-meta-toluamide (DEET), damage or alter some of the military-relevant materials. The aim of the current study was to evaluate the effect of DEET and non-DEET repellents on the mechanical properties and appearance of commonly available synthetic materials (substrates) routinely used in military application. We measured the visual appearance, visible light transmittance, strength, and stiffness of four materials exposed or left unexposed to six repellents. Sheet materials were tested in four-point bending, and the thread material was tested in uniaxial tension. Some of the repellents significantly altered the strength and bending stiffness of the sheet material and reduced light transmission. The sheet materials tested are commonly used in lens applications, so the reduction in light transmission and visibility has practical implications. For the thread (Kevlar) material tested, two repellents significantly reduced thread strength. Kevlar is used in the manufacture of body armor, but it is unknown if a reduction in Kevlar strength reduces the protective value of the body armor. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aarthropod repellent. =650 \0$aKevlar. =650 \0$amaterial properties. =650 \0$aplexiglas. =650 14$aArthropod repellent. =650 24$aKevlar. =650 24$aLexan. =650 24$aMaterial properties. =650 24$aPlexiglas. =700 1\$aBelkoff, Stephen,$eauthor. =700 1\$aJasper, Louis,$eauthor. =700 1\$aLangdale, Evan,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130091.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130033 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130033$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130033$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.F55 =082 04$a363.72/88$223 =100 1\$aJha, Bhagwanjee,$eauthor. =245 10$aQuantification of Transitions Occurring in a Hydrothermally Activated Fly Ash /$cBhagwanjee Jha, D. Singh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b20 =520 3\$aInteraction of fly ash with NaOH results in formation of several transition compounds (viz., zeolites), which are polycrystalline in nature and their crystal wise quantification is a challenging task. In fact, various parameters (viz., oxides, minerals present in the fly ash, pH and EC of NaOH) control the outcome of such interaction at 100°C. Hence, extensive monitoring of these controlling parameters and the zeolites becomes essential. With this in view, a three-stage methodology to quantify transitions occurring in the fly ash has been proposed in this manuscript. Interestingly, it has been observed that Stage-3 of the fly ash-alkali interaction results in formation of 47 types of zeolite-crystals (viz., Na-P1, faujasite, chabazite, hydroxysodalite, and analcime), which exhibits polymerization of these zeolites and wide variation in their size (ranging from 30 to 2346 nm). This sort of transition encourages application of the residues in waste water treatment and other environmental cleanup projects. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAlkali. =650 \0$aEnvironmental cleanup. =650 \0$aFly ash$x Environmental aspects. =650 \0$aFly ash$xIndustrial applications. =650 \0$aFly ash. =650 \0$aThree-stage activation. =650 \0$aZeolites. =650 14$aFly ash. =650 24$aAlkali. =650 24$aEnvironmental cleanup. =650 24$aThree-stage activation. =650 24$aZeolites. =700 1\$aSingh, D.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130033.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130030 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130030$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130030$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA684 =082 04$a624.1/821$223 =100 1\$aHamdoon, Muhsin,$eauthor. =245 10$aEffect of Combined Cold Temperature and Fatigue Load on Performance of G40.21 Steel /$cMuhsin Hamdoon, Sreekanta Das, Nader Zamani. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aMany structures such as bridge decks and ship hulls are required to withstand fatigue load cycles throughout their service life. These structures are also required to withstand zero and subzero temperatures if located in northern and Arctic regions, where winter temperatures can drop down to –40°C. The combined effects of cold temperature and cyclic loads can lead to potential damage to the material performance and subsequent failure. In this study, CSA G40.21 350WT steel, which is typically used in ship building, was tested in strain-controlled fatigue load cycles to determine the effect of zero and subzero temperatures on the mechanical properties and fatigue life. The experimental results show a significant effect of temperature on the fatigue life of this steel. The tensile strength was not affected by low temperatures. The yield strength and fracture strength increased and the ductility decreased at low temperatures. This paper discusses the test procedure, test parameters, and test data obtained from this study. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCyclic loading. =650 \0$aFatigue life. =650 \0$aFatigue Load. =650 \0$aMechanical properties. =650 \0$aproperties. =650 \0$aRoom. =650 \0$aSteel. =650 \0$aSubzero temperature. =650 14$aFatigue life. =650 24$aCyclic loading. =650 24$aMechanical properties. =650 24$aRoom. =650 24$aSubzero temperature. =700 1\$aDas, Sreekanta,$eauthor. =700 1\$aZamani, Nader,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130030.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130088 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130088$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130088$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.P68 =082 04$a668.4234$223 =100 1\$aZuanetti, Bryan,$eauthor. =245 10$aMulti-rate and Multi-modal Characterization of an Advanced Poly(etherimide) :$bUltem 1000 /$cBryan Zuanetti, Nathan Mutter, Ali Gordon. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (27 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b54 =520 3\$aThe key to the effective implementation of polymers in structural applications is an understanding of the mechanical response under a variety of conditions. In this study, an unreinforced poly(etherimide) (PEI) known as Ultem 1000 was characterized under quasi-static and high-strain-rate loading. Standard tension, compression, and torsion experiments were conducted in order to investigate the multi-regime response of this material. The elastic response of the material to multiple loading conditions was correlated using the Ramberg-Osgood model. The effects of thermal and mechanical rejuvenation processes on the mechanical response were investigated; the upper yield strength of the material was reduced, and the strain softening regime responsible for strain localization was largely eliminated. The fracture toughness of the material was evaluated using a Charpy impact test, and the mechanisms of failure were shown to be brittle. The high-strain-rate response of the material to uniaxial compression was evaluated by means of a miniaturized split Hopkinson pressure bar, and the strain-rate dependence of the material was modeled using the Ree-Eyring equations. Finally, a combination of the Ramberg-Osgood model and a novel model was employed to correlate the elastoplastic response of rejuvenated PEI to quasi-static mechanical loading. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBilinear model. =650 \0$aDuctility. =650 \0$aDynamic response. =650 \0$aExperimental mechanics. =650 \0$aglassy polymer. =650 \0$aPoly(etherimide) =650 \0$aStrain-rate sensitivity. =650 \0$athermoplastics. =650 \0$aToughness. =650 14$aBilinear model. =650 24$aDuctility. =650 24$aDynamic response. =650 24$aExperimental mechanics. =650 24$aGlassy polymer. =650 24$aKolsky bar. =650 24$aStrain-rate sensitivity. =650 24$aThermoplastics. =650 24$aToughness. =700 1\$aGordon, Ali,$eauthor. =700 1\$aMutter, Nathan,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130088.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130079 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130079$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130079$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.7.H55 =082 04$a620.11217$223 =100 1\$aSreenivasan, P.,$eauthor. =245 10$aEstimation of ASTM E1921 Master Curve of Ferritic Steels From Instrumented Impact Test of CVN Specimens Without Precracking /$cP. Sreenivasan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b38 =520 3\$aA semi-empirical cleavage fracture stress (CFS) model, mainly depending on the CFS, ?f, has been derived for estimating the ASTM E1921 reference temperature (T0) and demonstrated for ferritic steels with yield strength in the range 400-750 MPa. This requires only instrumented impact test of CVN specimens without precracking and static yield stress data. The T0 estimate based on the CFS model, TQcfs, lies within a ±20°C band, being conservative for most of the steels, but less conservative than TQIGC based on the IGC-procedure (see Nomenclature for definition). Applicability and acceptability of the present calibration curves for highly irradiated steels need further examination. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCharpy V-notch. =650 \0$aCleavage fracture stress. =650 \0$afracture toughness. =650 \0$aInstrumented impact test. =650 \0$aLight metals$x Metallurgy. =650 \0$areference temperature. =650 14$aCharpy V-notch. =650 24$aCleavage fracture stress. =650 24$aFracture toughness. =650 24$aInstrumented impact test. =650 24$aReference temperature. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130079.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130028 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130028$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130028$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS227.2 =082 04$a671.5/2$223 =100 1\$aDebnath, Subhrajit,$eauthor. =245 10$aStudy on Microstructure and Mechanical Properties of Thick Low-Alloy Quench and Tempered Steel Welded Joint /$cSubhrajit Debnath, Manidipto Mukherjee, Tapan Kumar Pal. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (27 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b37 =520 3\$aLow-alloy quench and tempered (Q&T) steel plates having yield strength of a minimum of 670 MPa are used extensively for the fabrication of impellers, penstocks, excavators, dumpers, and raw material handling devices, where welding is an important and probably most economic and productive process of joining. Thick low-alloy Q&T steel plates having a relatively high carbon equivalent (~0.6) are frequently susceptible to a crack-sensitive microstructure leading to cold cracking. Thus, the welding parameters need to be carefully selected for these grades of steel to obtain the desired microstructure and properties. The present study deals with the characterization of microstructure evolution and mechanical properties of thick (38 mm) welded low-alloy quench and tempered steel plates (A 517 Grade F by ASTM) with the shielded metal arc welding process using a low hydrogen covered electrode (E 11018 M). The microstructural characterization was done for top (P1), middle (P2), and bottom (P3) regions of the weldment by optical microscope and transmission electron microscope to understand the microstructural features. The micrographs of the weld and coarse-grain heat-affected zone (CGHAZ) of the three regions mainly show variation in lath martensite and different morphologies of ferrite. Interestingly, the weld metal and CGHAZ in the middle (P2) region show coarse grains compared to the other two regions where grain size is more or less the same and finer. Furthermore, among the three regions, the P3 region, in general, has comparatively higher hardness and toughness. The high cycle fatigue test under two load ratios (i.e., R = 0.1 and –1) conducted only on specimens extracted from the P3 region, because of its better properties, shows better fatigue performance of weld joint under R = 0.1. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFatigue. =650 \0$aGrain size. =650 \0$aHardness. =650 \0$aLow-alloy Q&T steel. =650 \0$aMicrostructure. =650 \0$aSteel, Structural$xCorrosion. =650 \0$aSteel, Structural$xWelding. =650 \0$aToughness. =650 \0$aWelded joints. =650 \0$aWelding. =650 14$aLow-alloy Q&T steel. =650 24$aFatigue. =650 24$aGrain size. =650 24$aHardness. =650 24$aMicrostructure. =650 24$aToughness. =650 24$aWelding. =700 1\$aMukherjee, Manidipto,$eauthor. =700 1\$aPal, Tapan Kumar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130028.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160049 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160049$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160049$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.52 =082 04$a620.1/1296$223 =100 1\$aHanke, Larry,$eauthor. =245 10$aBroad Beam Ion Milling for Microstructure Characterization /$cLarry Hanke, Kurt Schenk, Dieter Scholz. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b7 =520 3\$aOptimum sample preparation is essential to obtain reliable data in microstructure analysis. Whereas traditional metallographic preparation techniques, using mechanical polishing and chemical etching, are sufficient for many applications, these methods can be unsatisfactory for high-technology materials, complex assemblies, and smaller components. Broad-beam argon ion milling (AIM), using high-energy ion bombardment to remove material or modify the surface of a specimen, can provide a substantial improvement in specimen quality for many difficult materials and components. Directing energetic argon ions toward the specimen at a low angle of incidence gradually removes material at the atomic level to produce flat surfaces with no deformation or other disturbance of the material microstructure. Especially for multi-phase materials with low hardness or soft constituents, polishing by ion milling at low-angles results in optimum surfaces for light microscopy, scanning electron microscopy (SEM), or electron backscattered diffraction (EBSD). Surface modification to produce contrast between phases or reveal other microstructural features can be realized with higher milling angles. This provides a great advantage for components consisting of noble metals, like gold and platinum, or corrosion-resistant alloys bonded to less noble metals, which are frequently difficult or impossible to prepare with chemical etching. Microstructure contrast with ion milling is also useful for extremely fine structures, such as ultra-fine grains, that can be obscured by chemical etching. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aArgon ion milling. =650 \0$aBroad-beam ion milling. =650 \0$aMaterials$xThermal properties. =650 \0$aMetallography. =650 \0$aMicrostructure. =650 \0$aSCIENCE$xNanoscience. =650 \0$aSpecimen preparation. =650 \0$aThermodynamics. =650 14$aArgon ion milling. =650 24$aBroad-beam ion milling. =650 24$aMetallography. =650 24$aMicrostructure. =650 24$aSpecimen preparation. =700 1\$aSchenk, Kurt,$eauthor. =700 1\$aScholz, Dieter,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160049.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160068 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160068$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160068$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96/142$223 =100 1\$aKish, L.,$eauthor. =245 10$aFormation of Bainite in Advanced High-Strength Steels During Isothermal Transformation /$cL. Kish, D. Haezebrouck, S. Tan, C. Garcia. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b9 =520 3\$aThe isothermal transformation of bainite in an advanced high-strength steel (AHSS) in the temperature range of 422°C to 482°C for transformation times of 10-6000 s has been examined using light optical microscopy (LOM), and orientation imaging microscopy (OIM). Thermodynamic calculations were done using equilibrium thermodynamic simulation software to produce a theoretical time-temperature-transformation (TTT) diagram, to which the experimental results of this study were compared. Advanced microstructural techniques, such as orientation-imaging-microscopy-electron-backscatter-diffraction (OIM-EBSD), image quality (IQ) phase identification, and polarized light microscopy, were used to observe and quantify the progress of the bainitic transformation during isothermal transformation. Orientation imaging microscopy using electron backscatter diffraction image quality (EBSD-IQ) was used with each sample to quantify the amount of bainite transformed. Results showed that the isothermal transformation at 422°C had 80.1 % bainite, whereas the isothermal transformation at 482°C had 85.5 % bainite transformed after 1200 s; while, after 6000 s, the amount of bainite increased to 90.1 % and 93.4 % respectively. As a result the chemical composition of the steel investigated and the microstructural characteristics of the bainite observed, it was not possible to discern the type of bainite formed at higher and lower temperatures because of the absence of carbides. The kinetics of transformation from the experimental results clearly indicated that the isothermal transformation is slower than that predicted by the theoretical thermodynamic program. The results of this study are presented and discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBainite formation. =650 \0$aCooling curves. =650 \0$aCourbes TTT. =650 \0$aIsothermal transformation. =650 \0$aKinetics. =650 \0$aRetained austenite. =650 14$aBainite formation. =650 24$aEBSD-IQ. =650 24$aIsothermal transformation. =650 24$aKinetics. =650 24$aRetained austenite. =700 1\$aGarcia, C.,$eauthor. =700 1\$aHaezebrouck, D.,$eauthor. =700 1\$aTan, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160068.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160062 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160062$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160062$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ184 =082 04$a621.8/33$223 =100 1\$aBeardsley, A.,$eauthor. =245 10$aEBSD Characterization of Pilgered Alloy 800H After Heat Treatment /$cA. Beardsley, C. Bishop, M. Kral. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b35 =520 3\$aAustenitic stainless steel alloy 800H pipes were received in an as-pilgered condition. The pilgering process produces high levels of cold work through complex deformation processes. The pipes are subsequently solution annealed. To assess the influence of heat-treatment parameters on 800H, samples of the as-pilgered material were heat treated in the temperature range 600°C-1200°C for varying lengths of time. Using electron backscatter diffraction (EBSD), the recrystallization dynamics and grain size of all samples was measured. Additionally, the kernel average misorientation and grain orientation spread methods were employed to qualitatively analyze fine details in the strain levels in the matrix of both deformed and recrystallized grains. For 1-h anneal times, it was found that recrystallization of 800H initiates above heat-treatment temperatures of 800°C, and complete recrystallization of deformed material occurs above heat-treatment temperatures of 950°C. No significant increases in average grain size were observed until temperatures reached in excess of 1000°C. Increasing the heat-treatment time to more than 1 h had a negligible effect on the grain size for every heat-treatment temperature that was assessed. In high-temperature applications, pipes typically fail because of diffusion-based creep mechanisms. Therefore, accurate control of the grain size and microstructure during heat treatments is obligatory. This work provides a framework for controlling manufacturing processes to produce favorable microstructures in 800H for creep-based applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aGearing$xHeat treatment. =650 \0$aGrain orientation spread. =650 \0$aGrain size. =650 \0$aHeat treatment. =650 \0$aKernel average misorientation. =650 \0$aRecrystallization. =650 14$aAlloy 800H. =650 24$aGrain orientation spread. =650 24$aGrain size. =650 24$aHeat treatment. =650 24$aKernel average misorientation. =650 24$aRecrystallization. =700 1\$aBishop, C.,$eauthor. =700 1\$aKral, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160062.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160025 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160025$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160025$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.52 =082 04$a620.1/1296$223 =100 1\$aKazakov, A.,$eauthor. =245 10$aQuantitative Characterization of Hypoeutectic Aluminum-Silicon-Copper As-Cast Alloy Microstructures /$cA. Kazakov, A. Kur, E. Kazakova, D. Kiselev. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b19 =520 3\$aThere are only two kinds of qualitative methods for the estimation of aluminum alloy structures: (1) bar charts (degree of eutectic fineness, porosity content, etc.), and (2) atlases of microstructures, mainly for rejection (overheating, for example). In this paper, the development of quantitative methods for the characterization of hypoeutectic Al-Si-Cu as-cast alloy microstructures using panoramic image analysis is described. As-cast and solution-annealed Al-6Si-2Cu alloy microstructures were studied. Parameters for monitoring the quality of the structure of this alloy were proposed. New algorithms for automatic estimation of eutectic fineness and its volume fraction were developed. Correlations among different microstructural parameters were found and interpreted using thermodynamic simulation. The grade of porosity according to GOST 1583-93 versus pore volume fraction, calculated by ASTM E1245, was defined. Bar charts for estimation of the average length of eutectic silicon particles were proposed. The eutectic modification grade, according to the American Foundry Society chart for microstructure control of hypoeutectic alloys, versus both the length and the elongation of eutectic silicon particles was determined. The relationships between alloy hardness and tensile elongation versus the proposed microstructural parameters for Al-6Si-2Cu alloy were defined. These relationships describe various grades of hypoeutectic Al-Si-Cu alloys in both the as-cast and as-solution-annealed conditions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum-silicon-copper alloys. =650 \0$aMaterials$xThermal properties. =650 \0$aMicrostructure. =650 \0$aQuantitative characterization. =650 \0$aSCIENCE$xNanoscience. =650 \0$aStructure-property relationships. =650 \0$aThermodynamics. =650 14$aAluminum-silicon-copper alloys. =650 24$aMicrostructure. =650 24$aQuantitative characterization. =650 24$aStructure-property relationships. =700 1\$aKazakova, E.,$eauthor. =700 1\$aKiselev, D.,$eauthor. =700 1\$aKur, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160025.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160033 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160033$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160033$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA465 =082 04$a620.1/76$223 =100 1\$aAmorim, M.,$eauthor. =245 10$aMechanical and Metallographic Effects of Laser Hardening of Two AHSS Steels /$cM. Amorim, D. Neves, F. de Azevedo Silva. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aThe search for suitable materials for the transport industry, to meet more stringent regulations related to crashworthiness, emissions, and fuel economy led to the development of advanced high-strength steels (AHSS). Thermal treatments, for example, using lasers as a process tool, can locally improve some characteristics of these materials like plastic deformation capability. The high energetic efficiency of a laser process, and its capability to be automated, are some of the advantages of using such a process. This study aims to investigate the effects of local heat treatment (involving changes in the solid state), by laser radiation, in the mechanical properties and microstructures of two types of advanced high-strength steels, the dual-phase DP 600, and the transformation-induced plasticity TRIP 750. A method to evaluate the interaction between laser radiation and the materials is proposed. Previous studies in this area focused, basically, in welding or cutting technology, and for the modern TRIP steel studied here, there is a scarcity of published material regarding laser-material interaction. Hardness and tensile tests revealed, for the range of process parameters studied, an improvement (up to 30 % with relation to the base material) in yield strength and ultimate strength (up to 15 %). Revealed also is a dramatic reduction in the elongation (up to 80 %) for both materials. Optical metallography analysis revealed that the resulting microstructures presented grain refinement and formation of lath martensite according to the level of laser absorption, improving up to twice the original hardness. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAdvanced high-strength steels. =650 \0$aDual-phase steel. =650 \0$aLaser materials processing. =650 \0$aLocal heat treatment. =650 \0$aMaterials characterization. =650 \0$aSteel$xFracture. =650 \0$aTRIP steel. =650 14$aAdvanced high-strength steels. =650 24$aDual-phase steel. =650 24$aLaser materials processing. =650 24$aLocal heat treatment. =650 24$aMaterials characterization. =650 24$aTRIP steel. =700 1\$ade Azevedo Silva, F.,$eauthor. =700 1\$aNeves, D.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160033.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160008 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160008$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160008$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRA643 =082 04$a614.4$223 =100 1\$aFang, S.,$eauthor. =245 10$aSurface Topography Quantification of Super Hard Abrasive Tools by Laser Scanning Microscopy /$cS. Fang, L. Llanes, M. Engstler, D. Baehre, F. Soldera, F. Muecklich. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b35 =520 3\$aNon-conventional super hard abrasive tools are made of composite materials containing super hard grains, e.g., diamond or cubic boron nitride (CBN) grains, bound by a metallic constitutive phase. These tools are usually produced by means of sintering, and are widely applied in the abrasive machining processes of modern manufacturing, especially in precision machining. The abrasive grains, which induce the material removal processes, are embedded in the metallic binder. They emerge as a consequence of self-dressing, resulting in a self-sharping effect. Therefore, the cutting surface of the tool displays an irregular topography. Quantification of surface topography scenario may supply valuable information to evaluate and understand its correlation to wear mechanisms. In this study, an experimental protocol consisting of five steps: specimen preparation, surface scanning, image assembly, image digital processing and surface quantification, was proposed and validated by characterizing two CBN honing tools used for precision machining: B151/L2/2010/50 (B151) and B91/128/x44/35 (B91) CBN honing stones. It involved the use of laser scanning microscopy and digital imaging processing for assessing significant dimensional, geometrical, and positional properties of CBN grains at the surface of super hard abrasive tools. It was shown that surface topography quantification is an effective method to evaluate and obtain the defined parameters. However, smaller grains may require images with higher resolution; thus, scanning must be refined. Finally, a critical comparative analysis of the experimental results attained for the studied tools pointed out honing stone B91 as more appropriated than B151 one for achieving a higher machining quality of the workpiece. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAbrasive tools. =650 \0$aCBN composite. =650 \0$aCommunicable Diseases$xepidemiology. =650 \0$aDisease Outbreaks. =650 \0$aEpidemiologic Methods. =650 \0$aLaser scanning microscopy. =650 \0$aQuantification. =650 \0$aSurface topography. =650 14$aAbrasive tools. =650 24$aCBN composite. =650 24$aLaser scanning microscopy. =650 24$aQuantification. =650 24$aSurface topography. =700 1\$aBaehre, D.,$eauthor. =700 1\$aEngstler, M.,$eauthor. =700 1\$aLlanes, L.,$eauthor. =700 1\$aMuecklich, F.,$eauthor. =700 1\$aSoldera, F.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160008.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160001 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160001$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160001$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQA273.6 =082 04$a519.2/4$223 =100 1\$aVander Voort, G.,$eauthor. =245 10$aEvaluation of Normal Versus Non-Normal Grain Size Distributions /$cG. Vander Voort, O. Pakhomova, A. Kazakov. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b15 =520 3\$aASTM E112-13 states that it covers test methods to determine the average grain size of specimens with a uni-modal distribution of grain areas, diameters, or intercept lengths. It states that these distributions are approximately log-normal. However, it does not describe how one can determine if the specimen's grain size distribution is a uni-modal normal (Gaussian) distribution. ASTM E1181-02(2015) says it covers test methods to characterize grain size in products with any other distribution (other than a “single log-normal distribution of grain sizes”). However, the only example given in Appendix X2 shows the percentage of the number of intercept measurements in 38 length classes from 0 to 1 to 37 to 38 mm. Thirty eight classes is far too many to properly reveal the grain size distribution. This procedure revealed a log-normal distribution, but it is not in terms of ASTM grain size numbers, which makes it less useful. No guidance was given in ASTM E1181 to determine the nature of the grain size distribution. In this paper, a mathematical and graphical approach was defined. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBinomial distributions. =650 \0$aDistribution (Probability theory) =650 \0$aDuplex grain size. =650 \0$aGrain size distribution. =650 \0$aMultivariate analysis. =650 \0$aNon-normal distributions. =650 \0$aNormal (Gaussian) distribution. =650 14$aGrain size distribution. =650 24$aALA grain size. =650 24$aASTM E1181. =650 24$aASTM E930. =650 24$aBinomial distributions. =650 24$aDuplex grain size. =650 24$aNon-normal distributions. =650 24$aNormal (Gaussian) distribution. =700 1\$aKazakov, A.,$eauthor. =700 1\$aPakhomova, O.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160001.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160040 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160040$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160040$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA459.T3842013 =082 04$a629.10923478$223 =100 1\$aKazakov, A.,$eauthor. =245 10$aInterpretation and Classification of Non-Metallic Inclusions /$cA. Kazakov, A. Zhitenev, S. Ryaboshuk. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b23 =520 3\$aThe non-metallic inclusions in steel are one of the most important parameters of metallurgical quality. Despite the extensive progress in thermodynamic description of non-metallic inclusions formation in the liquid and solidifying steel, a complete simulation of their evolution during secondary metallurgy, casting and solidification is impossible. The processes for non-metallic inclusion formation, growth and elimination, taking into account macro- and micro-segregation evolution, are too complicated. Therefore, a statistically reliable estimation of the amount, morphology, size distribution and chemical composition of non-metallic inclusions obtained by modern experimental approaches could be an important basis for understanding steelmaking technology. Automated feature SEM/EDS analysis of the chemical composition, size, and volume fraction of more than 600 non-metallic inclusions in rail steel was conducted. Analysis of these non-metallic inclusions' database by developed software found the following clusters of inclusions: (1) oxides, Al-Ca-Si-Mn-S-O; (2) predominantly sulfides, Mn-S-Al-Ti-O; (3) oxides and sulfides, Mn-S-O; and (4) complex non-metallic inclusions, Ti-Mn-O(N). All found compositions of non-metallic inclusions were placed on the ternary diagram Mn-Al-S and they lined up from the Al corner to the MnS point on the Mn-S axis. The chemical compositions of the non-metallic inclusions evolved from Al-Ca-Si-Mn-S-O to Mn-S-Al-Ti-O and, finally, to the Mn-S-O+Ti-Mn-O(N) system. Interpretation of the chemical composition of non-metallic inclusions by thermodynamic modeling revealed the nature of each cluster with correspondence to the secondary metallurgy stage where they were formed. This information could be useful for improvement of steelmaking technology. Accumulation of cluster analysis results for non-metallic inclusions in different steels could be a basis for the development of a universal classification of non-metallic inclusions produced by modern secondary metallurgy technologies. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAutomated feature analysis for assessment of non-metallic inclusions compositions. =650 \0$aAutomated feature SEM/EDS analysis. =650 \0$aCluster analysis of the non-metallic inclusions composition. =650 \0$aMetallic coatings. =650 \0$aMetals. =650 \0$aNon-metallic inclusions in steel. =650 \0$aThermodynamic simulation of non-metallic inclusions formation in liquid and in solidifying steel. =650 14$aNon-metallic inclusions in steel. =650 24$aAutomated feature analysis for assessment of non-metallic inclusions compositions. =650 24$aAutomated feature SEM/EDS analysis. =650 24$aCluster analysis of the non-metallic inclusions composition. =650 24$aThermodynamic simulation of non-metallic inclusions formation in liquid and in solidifying steel. =700 1\$aRyaboshuk, S.,$eauthor. =700 1\$aZhitenev, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160040.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160057 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160057$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160057$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC482.D5 =082 04$a548/.83$223 =100 1\$aEdmonds, David,$eauthor. =245 10$aX-Ray and Neutron Diffraction Studies of Quenched and Partitioned (Q&P) Multiphase Steel Microstructures /$cDavid Edmonds, Timothy Bigg. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b29 =520 3\$aNovel advanced steel developments in recent years have resulted in many steels with complex multiphase microstructures. Foremost currently are steels that contain significant fractions of untransformed parent austenite phase. “Quenched and partitioned” steels, commonly referred to as Q&P steels, important as potential advanced high-strength (AHS) automotive steels, are an example in which the austenite is chemically stabilized by carbon partitioning from martensite following an interrupted quench above the martensite finish temperature, Mf. It is evident that the progress of microstructural change during this novel quenching and partitioning treatment, the volume of untransformed austenite stabilized during partitioning and the behavior of this austenite according to its carbon content should be understood. In relation to these requirements, recent analysis of X-ray powder diffraction (XRD) and neutron diffraction experiments will be considered. Initially, the effect of sample preparation between the two measurement techniques is considered, followed by observation of the partitioning process in real time allowed by specially prepared Mn-containing experimental alloys, with and without a crucial silicon addition required to enable austenite retention during Q&P treatment. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAmorf materiaal. =650 \0$aMartensite. =650 \0$aNeutron diffraction. =650 \0$aRayons X$xDiffraction. =650 \0$aRetained austenite. =650 \0$aX-Ray Diffraction. =650 14$aQuenching and partitioning (Q&P) =650 24$aMartensite. =650 24$aNeutron diffraction. =650 24$aRetained austenite. =650 24$aX-ray diffraction. =700 1\$aBigg, Timothy,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160057.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160055 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160055$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160055$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7871.99.A45 =082 04$a621.3815/2$223 =100 1\$aNagarajan, D.,$eauthor. =245 10$aMicrostructure and Wear Behavior of a Functionally Gradient Al-Si Alloy Prepared Using the Cast-Decant-Cast (CDC) Process /$cD. Nagarajan, P. Mohana Sivam. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aA bulk functionally gradient Al-Si alloy with two varying Si contents [high (11 %) and low (4 %) hypoeutectic compositions-alloys A and B, respectively] was prepared through a novel casting technique named cast-decant-cast (CDC) process. Casting was done by pouring liquid alloy A first into a mold, allowed to solidify partially in the mold until a layer of ~15 mm was formed against the mold walls, and decanting the remaining unsolidified alloy A by turning the mold upside down. The superheated liquid alloy B was then poured into the mold and allowed to solidify fully. Optical micrographs of the functionally gradient casting revealed no abrupt interface layer between the high- and low-Si regions, and the scanning-electron-microscopy-energy-dispersive-X-ray (SEM-EDX) analysis carried out across the cross section of the casting showed a linear silicon concentration gradient of ~10 mm across the interface. Wear tests carried out on the individual sections of alloys A, B, and functionally gradient regions showed that the percentage cumulative weight loss was lower for the functionally gradient region (i.e., higher wear resistance) compared with the high- and low-Si regions. The SEM images taken after wear testing of the functionally gradient region showed finer and smoother wear tracks with very little random delamination of the matrix surface. This is attributed to the presence of both needle-shaped and round-shaped eutectic Si particles and their strong reinforcement in the primary aluminum-rich ? matrix, which resulted in higher wear resistance of the functionally gradient region. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum-silicon alloys. =650 \0$aAmorphous semiconductors$xDesign and construction. =650 \0$aCast-decant-cast process. =650 \0$aFunctionally gradient material. =650 \0$aPlasma-enhanced chemical vapor deposition. =650 \0$aWear behavior. =650 14$aFunctionally gradient material. =650 24$aAluminum-silicon alloys. =650 24$aCast-decant-cast process. =650 24$aWear behavior. =700 1\$aMohana Sivam, P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160055.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160028 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160028$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160028$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN690 =082 04$a669/.95$223 =100 1\$aStrobl, S.,$eauthor. =245 10$aMicrostructural Characterization of Ferrous Materials Forged by the Damascus Technique /$cS. Strobl, R. Haubner. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b9 =520 3\$aDamascus steels are related to composites which combine the properties of diverse steel qualities. By forging steel plates with different compositions, in particular differences in the carbon content, a multilayered workpiece is manufactured. Forging of cast iron has not been common because of its low melting point and brittleness at lower temperatures. Wolfgang Scheiblechner, a blacksmith from Palfau in Austria, combined ductile cast iron and soft iron to a unique composite material, which was investigated by means of metallographic methods. The intersections of cast iron and iron are of high interest, where carbon diffusion from ductile cast iron (graphite 100 % C) to soft iron (0 % C) takes place. In this case, all the microstructures characteristic for cast irons, steels, and soft iron were present. The microstructures were additionally influenced by forging and quenching. The cast iron region was dominated by nodular graphite and bainite; ledeburite was observed occasionally. The soft iron regions showed coarse equiaxed ferrite and grain boundary cementite. In the transition areas, ferrite showed a wide variety of shapes, and the microstructure changed from hypereutectoid to hypoeutectoid steel. The various microstructures were characterized by light optical microscopy and confirmed by Vicker's microhardness measurements. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCarbon diffusion. =650 \0$aDamascus technique. =650 \0$aDuctile cast iron. =650 \0$aMetallography. =650 \0$aMicrostructure. =650 \0$aPhysical metallurgy. =650 \0$aSoft iron. =650 14$aDamascus technique. =650 24$aCarbon diffusion. =650 24$aDuctile cast iron. =650 24$aMetallography. =650 24$aMicrostructure. =650 24$aSoft iron. =700 1\$aHaubner, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160028.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160029 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160029$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160029$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.52 =082 04$a620.1/1296$223 =100 1\$aBöhm, J.,$eauthor. =245 10$aMicrostructure of a Heat Treated Nickel-Aluminum Bronze and Its Corrosion Behavior in Simulated Fresh and Sea Water /$cJ. Böhm, P. Linhardt, S. Strobl, R. Haubner, M. Biezma. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b17 =520 3\$aNickel-aluminum bronzes (NAB) are a family of alloys with excellent mechanical and corrosion resistance properties, even in highly corrosive environments, attributed to the complex as-cast microstructures. Heat treatment, in-service conditions or welding procedures induce microstructural transformations resulting in changes of the properties. To evaluate the corrosion behavior of one selected NAB alloy, different heat treatments were performed and the relation between microstructural changes and corrosion behavior was studied. Under common casting conditions, CuAl10Fe5Ni5 bronze consists of the ?-phase, ?-phase, and several intermetallic phases, collectively referred to as ?-phases. The microstructures of the as-cast and heat treated samples were characterized by metallographic methods. After grinding and polishing, the samples were etched with FeCl3-as well as Cu(NH4)2Cl4-solutions and examined by light optical and scanning electron microscopy. Finally, electrochemical corrosion tests of both as-cast and heat treated samples were carried out in simulated fresh water and sea water under potentiostatic conditions. Four specimens of each sample type were polarized simultaneously at different potentials for 70 h. These specimens were used to study the corrosion progress of the different specific microstructural features and constituents by metallographic investigations. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCorrosion test. =650 \0$aElectrochemistry. =650 \0$aHeat treatment. =650 \0$aMaterials$xThermal properties. =650 \0$aMetallography. =650 \0$aMicrostructure. =650 \0$aNickel-aluminum bronze. =650 \0$aSCIENCE$xNanoscience. =650 \0$aThermodynamics. =650 14$aNickel-aluminum bronze. =650 24$aCorrosion test. =650 24$aElectrochemistry. =650 24$aHeat treatment. =650 24$aMetallography. =650 24$aMicrostructure. =700 1\$aBiezma, M.,$eauthor. =700 1\$aHaubner, R.,$eauthor. =700 1\$aLinhardt, P.,$eauthor. =700 1\$aStrobl, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160029.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160048 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160048$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160048$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC482.D5 =082 04$a548/.83$223 =100 1\$aFernandes, F.,$eauthor. =245 10$aLow Temperature Plasma Nitriding and Nitrocarburising of a Superaustenitic Stainless Steel /$cF. Fernandes, L. Casteletti, J. Gallego. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b19 =520 3\$aLow temperature surface engineering of stainless steels by dissolving large quantities of nitrogen and carbon has become a favorable technological process. Such treatments usually yield the so-called expanded austenite, which is a super-saturated diffusion zone and can be produced by a salt, gas, or plasma-based processes. The present manuscript addressed the production of expanded austenite on a superaustenitic stainless steel at low temperature. Gas mixtures with nitrogen or both nitrogen and carbon bearing gases were applied in a plasma atmosphere at 400°C for 5 h. Microstructural characterization was conducted applying light optical microscopy, X-ray diffraction, and transmission electron microscopy. In addition, microhardness measurements were performed at the surface of the samples. Plasma nitriding and nitrocarburising at 400°C resulted in a homogeneous case composed solely by expanded austenite as detected by X-ray diffraction. Similar microhardness was observed for both processes, whereas nitrocarburising provided a thicker diffusion zone when compared to nitriding. Fine iron-chromium nitride precipitation was only identified by transmission electron microscopy (TEM). Selected area electron diffraction yields similar lattice parameters for both processes. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAmorf materiaal. =650 \0$aPlasma nitriding. =650 \0$aPlasma nitrocarburising. =650 \0$aRayons X$xDiffraction. =650 \0$aSuperaustenitic stainless steel. =650 \0$aTransmission eletron microscopy. =650 \0$aX-Ray Diffraction. =650 14$aSuperaustenitic stainless steel. =650 24$aPlasma nitriding. =650 24$aPlasma nitrocarburising. =650 24$aTransmission eletron microscopy. =650 24$aX-ray diffraction. =700 1\$aCasteletti, L.,$eauthor. =700 1\$aGallego, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160048.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160045 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160045$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160045$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP261.G7 =082 04$a662/.92$223 =100 1\$aEdmonds, D.,$eauthor. =245 10$aHigh-Resolution Metallography of a Coarse Microstructure :$bGraphite Formation in the Solid-State in Steel /$cD. Edmonds, R. Brydson, A. Inam. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aThe equilibrium form of carbon in iron and steel is graphite. In higher carbon cast irons graphite is normally formed from the liquid state. In lower carbon steels, carbon invariably exists in the form of metastable cementite, due to slow graphitization kinetics in the solid, but in fact, graphite formation is also more likely to be prevented by alloying to stabilize the microstructure for service. Relatively few high-resolution studies of graphite formation have thus been made in the past; this is also because of probable difficulties associated with specimen preparation of a relatively coarse aggregate microstructure. More recently, new investigative techniques and methods have allowed closer examination of graphite formation in steels. Examples are given of HRTEM, EELS, ELNES, EFTEM, and FIB/FEGSEM recently applied to observations of graphite nucleation and growth in the solid state in steel. This has importance, for example, in the potential development of more economic and user-friendly machining steels, which would rely upon internal lubrication by graphite particles in the microstructure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFree-machining steel. =650 \0$aGraphene. =650 \0$aGraphite composites. =650 \0$aGraphitization. =650 \0$aRaman spectrometry. =650 14$aGraphitization. =650 24$aFree-machining steel. =650 24$aHRTEM;EELS;ELNES;EFTEM;FIB/FEGSEM. =650 24$aRaman spectrometry. =700 1\$aBrydson, R.,$eauthor. =700 1\$aInam, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160045.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160069 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160069$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160069$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aCatteau, S.,$eauthor. =245 10$aDilatometric Study of Phase Transformations in Steels :$bSome Issues /$cS. Catteau, T. Sourmail, A. Moine. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b22 =520 3\$aDilatometry is widely used in the investigation of phase transformation in steels, not only by research laboratories but also by most steel makers. Its application includes the determination of CCT and TTT diagrams, and more generally the investigation of phase transformation kinetics under controlled temperature conditions. A basic and often undiscussed assumption in the exploitation of dilatation measurements as a function of temperature is that of a constant and uniform temperature distribution in the specimen, and of a homogeneous material. In the present paper, various issues encountered with a widely used quenching dilatometer were discussed, including longitudinal temperature gradients, deformation anisotropy, or vacuum evaporation of some chemical species. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDeformation anisotropy. =650 \0$aDilatometry. =650 \0$aPhase transformation. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 \0$aSteel. =650 \0$aThermal gradient. =650 \0$aVacuum effusion. =650 14$aDilatometry. =650 24$aDeformation anisotropy. =650 24$aPhase transformation. =650 24$aSteel. =650 24$aThermal gradient. =650 24$aVacuum effusion. =700 1\$aMoine, A.,$eauthor. =700 1\$aSourmail, T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160069.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160050 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160050$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160050$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQL807 =082 04$a611/.018$223 =100 1\$aNarayana Murty, S. V.,$eauthor. =245 10$aMicrostructural Analysis of a Failed Cu-Cr-Ti-Zr Thrust Chamber Liner of a Cryogenic Engine /$cS. V. Narayana Murty, Sushant Manwatkar, Mathew George, P. Ramesh Narayanan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aDuring the routine testing of a cryogenic engine, failure of a copper alloy (Cu-Cr-Ti-Zr) liner was noticed which led to the test abort. On close inspection of the liner, a circumferential crack with a length of 78 mm was observed on the divergent side of the thrust chamber. Roughening of the inner wall of the thrust chamber was noticed at the cracked location and extended circumference. Thinning of the copper liner wall was observed at the location of the crack indicating plastic yielding of the material at the location of failure. Fracture surface observations by scanning electron microscopy revealed features of material flow and softening at many locations indicative of exposure of fracture surface to high temperature after failure. Further, striation marks were noticed on the fracture surface indicative of fatigue. Very fine recrystallized grains were noticed in optical microscopy at the location of the crack. This is attributed to dynamic recrystallization occurring during deformation at high temperatures. Strain markings and slip bands were noticed in the interior of grains near the fracture edge. Based on extensive microstructural analysis of the failed hardware, it is concluded that the throat of thrust chamber failed due to “thermal ratcheting.”. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aGewebe. =650 \0$aHistology. =650 \0$aOptical microscopy. =650 \0$aOrgan. =650 \0$aScanning electron microscopy. =650 \0$aThermal ratcheting. =650 \0$aThrust chamber. =650 14$aCu-Cr-Ti-Zr alloy. =650 24$aOptical microscopy. =650 24$aScanning electron microscopy. =650 24$aThermal ratcheting. =650 24$aThrust chamber. =700 1\$aGeorge, Mathew,$eauthor. =700 1\$aManwatkar, Sushant,$eauthor. =700 1\$aRamesh Narayanan, P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160050.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160002 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160002$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160002$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN23 =082 04$a622 s$223 =100 1\$aVander Voort, G.,$eauthor. =245 10$aResults of Interlaboratory Test Programs to Assess the Precision of Inclusion Ratings by Methods A, C, and D of ASTM E45 /$cG. Vander Voort. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b6 =520 3\$aOver the years, ASTM Committee E4 on metallography has conducted interlaboratory test programs to evaluate the precision and bias associated with measurements of microstructure using proposed and existing test methods. ASTM decided in the late 1970s that all test methods that generated numerical data must have a precision and bias section defining the repeatability and reproducibility of the method. Defining bias associated with a test method is difficult unless there is an absolute known value for the quantity being measured and this is not possible when microstructural features are being measured. This paper shows the results for an interlaboratory test using Method A, “worst-field” ratings of inclusions in steels using the original Plates I and III of ASTM E45, using Method C, a worst-field rating using Plate II; and, using Method D, a quantitative approach where every field is rated using Plates I and III. The results from nine people who were reported to be qualified, regular users of the method revealed consistent problems of misclassification of inclusion types and a wide range of severity ratings for each specimen. The test results using an image analyzer will be compared to that of the manual raters. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminates. =650 \0$aAnorthosite. =650 \0$aGlobular oxides. =650 \0$aIndigenous inclusions. =650 \0$aManganese sulfides. =650 \0$aNonmetallic inclusions. =650 \0$aQuantitative ratings. =650 \0$aSilica. =650 \0$aSilicates. =650 \0$aSintering. =650 \0$aWorst-field ratings. =650 14$aNonmetallic inclusions. =650 24$aAluminates. =650 24$aGlobular oxides. =650 24$aIndigenous inclusions. =650 24$aManganese sulfides. =650 24$aQuantitative ratings. =650 24$aSilicates. =650 24$aWorst-field ratings. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160002.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160034 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160034$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160034$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.52 =082 04$a620.1/1296$223 =100 1\$aSustaita-Torres, I.,$eauthor. =245 10$aAging of Cast 35Cr-45Ni Heat Resistant Alloys With Different Carbon Content /$cI. Sustaita-Torres, S. Haro-Rodríguez, R. Colás. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b37 =520 3\$aThe changes in microstructure that took place in two heat-resistant after aging alloys at 750°C for a period of time of up to 1000 h are reported in this work. The alloys selected had a similar composition, with the exception in carbon content that was of 0.15 and 0.50 %. The material was obtained from centrifugal cast pipes and their microstructure was made of an austenitic dendrite matrix with interdendritic primary cabides; light optical and scanning electron microscopy analyses were conducted to identify these carbides as NbC and Cr7C3. Selected area analyses were conducted to quantify the primary carbides in the as-cast and aged conditions; these analyses revealed that their amount was unaffected by aging, but depended on the carbon content, with the predominance of NbC in the alloy with lower carbon content, due to the higher affinity of carbon to niobium. Aging affected the NbC particles, as they transformed into silicides, precipitation of secondary Cr23C6 particles took place, while Cr7C3 remained unaffected. The changes in microstructure that were observed by microscopy were confirmed by X-ray diffraction. The mechanical properties of the materials changed, as hardness and tensile strength increased, while the ductility in both alloys was reduced. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAging. =650 \0$aHeat resistant alloy. =650 \0$aMaterials$xThermal properties. =650 \0$aMicrostructure. =650 \0$aPrecipitation. =650 \0$aSCIENCE$xNanoscience. =650 \0$aThermodynamics. =650 14$aAging. =650 24$aHeat resistant alloy. =650 24$aMicrostructure. =650 24$aPrecipitation. =700 1\$aColás, R.,$eauthor. =700 1\$aHaro-Rodríguez, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160034.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160067 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160067$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160067$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS301 =082 04$a338.47$223 =100 1\$aBritz, D.,$eauthor. =245 10$aReproducible Surface Contrasting and Orientation Correlation of Low-Carbon Steels by Time-Resolved Beraha Color Etching /$cD. Britz, A. Hegetschweiler, M. Roberts, F. Mücklich. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b15 =520 3\$aColor etchants have a huge potential in industrial applications and numerous investigations have been made to obtain a better understanding of the etching process. However, reproducibility and a solid knowledge of the ongoing processes are still missing. The work presented is a systematic study of the reproducibility of the Beraha color etching with potassium metabisulfite. By in situ observation of the etching process, the different states of the Beraha etching could be followed. It was shown that, at the beginning of the etching of dual-phase steels, the contrasting of the second phase by dissolving the less noble part of the second phase is the predominant contrast. Uncommonly, grain boundaries are hardly attacked. The color development of matrix grains is orientation sensitive and it was shown by comparison with electron backscatter diffraction (EBSD) measurements, that similar orientated grains have similar colors. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aColor metallography. =650 \0$aCorrelative microscopy. =650 \0$aElectron backscatter diffraction (EBSD) =650 \0$aLight optical microscope (LOM) =650 \0$aLow-carbon steels. =650 \0$aSteel industry. =650 \0$aSteel$xHandbooks, manuals, etc. =650 \0$aSteel. =650 14$aColor metallography. =650 24$aCorrelative microscopy. =650 24$aElectron backscatter diffraction (EBSD) =650 24$aIn-situ investigation. =650 24$aLight optical microscope (LOM) =650 24$aLow-carbon steels. =700 1\$aHegetschweiler, A.,$eauthor. =700 1\$aMücklich, F.,$eauthor. =700 1\$aRoberts, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160067.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160032 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160032$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160032$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQL807 =082 04$a611/.018$223 =100 1\$aNarayana Murty, S.,$eauthor. =245 10$aMicrostructural Characterization and Mechanical Properties of Fusion Welded Dissimilar Joints of AA2219-AA5083 at RT, 77K and 20K /$cS. Narayana Murty, Sushant Manwatkar, M. Sunil, Reji Joseph, P. Ramesh Narayanan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aIn the present study, 3 mm thick sheets of aluminium-copper alloy AA2219 were welded to aluminium-magnesium alloy AA5083 by tungsten inert gas (TIG) welding using AA2319 filler wire. The welded specimens were evaluated for mechanical properties at RT, 77 K, and 20 K. The failure of the tensile specimens was predominantly on the AA2219 side of the weld bead at all test temperatures down to 20 K. Microstructural analysis was carried out by optical and scanning electron microscopy. Based on extensive analysis of the weld joints tested at room and cryogenic temperatures down to 20 K, it was observed that the grain boundary copper rich films formed at the partially melted zone on the AA2219 side of the weld joint were weaker compared to the eutectics formed at fusion line/HAZ on the AA5083 side. This is further aided by the absence of phase mixtures of undesirable morphology in the weld region. This phenomenon is further corroborated with the dependence of the orientation of AA2219 grains with loading axis in repair welded AA2219-AA5083 weld specimens. When the tensile axis is perpendicular to AA2219 grains, failure was on the AA2219 side of the weld indicating that the strength of copper rich films in a partially welded zone decides the strength of weld joints. Finally, it is concluded that reliable dissimilar weld joints of AA2219-AA5083 of aerospace quality can be manufactured. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDissimilar welding. =650 \0$aEnergy dispersive spectroscopy. =650 \0$aGewebe. =650 \0$aHistology. =650 \0$aOptical microstructure. =650 \0$aOrgan. =650 \0$aScanning electron microscopy. =650 \0$aTIG welding. =650 14$aAA2219. =650 24$aAA5083. =650 24$aDissimilar welding. =650 24$aEnergy dispersive spectroscopy. =650 24$aOptical microstructure. =650 24$aScanning electron microscopy. =650 24$aTIG welding. =700 1\$aJoseph, Reji,$eauthor. =700 1\$aManwatkar, Sushant,$eauthor. =700 1\$aRamesh Narayanan, P.,$eauthor. =700 1\$aSunil, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160032.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160047 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160047$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160047$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC377 =082 04$a616.8/34$223 =100 1\$aBagnall, C.,$eauthor. =245 10$aAnalysis of a Casting Fracture and Identification of Fatigue From Tire Track Markings /$cC. Bagnall, C. Holp, W. Moorhead. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b6 =520 3\$aKnuckle connectors on railcars are required to sustain thousands of cyclic stress events. Manufacturers continue to develop, test, and improve the life of these castings, which are now designed to exceed 400,000 cycles when subjected to tests involving cumulative cyclic sinusoidal load range settings varying between 6800 and 127,000 kgf at room temperature. This paper addressed real-world difficulties of differentiating between component failures due to overload and casting defects, and those that result from fatigue damage. Fatigue fractures in castings are rarely planar and comprise areas where solidification kinetics are different, and locations where porosity or large inclusions are present. The cumulative effect these factors have on fracture is to generate a rough topography, which may exhibit no beachmarks or other outward sign by which a fatigue fracture is commonly recognized. In this paper, an advantage was gained over a field failure because the fracture was produced in a laboratory test. Cycles to failure was recorded and details of the applied cyclic stress were also known. The difficulty regarding scanning electron microscope (SEM) analysis was that classic fatigue features normally visible to the naked eye, such as beachmarks, thumbnail initiation sites and planar areas, were not evident on the fracture face. In addition to documentation of numerous defect features on the fracture surface, SEM analysis revealed a rare but proof-positive form of evidence for propagation of the early stages of fracture by fatigue. The feature has been described in the literature as “tire tracks,” alluding to their similarity to ATV tire impressions or Lunar Rover tracks on the moon. A brief review of earlier literature examples of tire track features is provided, and the generally accepted mechanism for their formation is assessed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFatigue features. =650 \0$aFracture analysis. =650 \0$aMultiple sclerosis$xExercise therapy. =650 \0$aMultiple sclerosis. =650 \0$aRail coupler casting. =650 \0$aTire tracks. =650 14$aFracture analysis. =650 24$aFatigue features. =650 24$aRail coupler casting. =650 24$aTire tracks. =700 1\$aHolp, C.,$eauthor. =700 1\$aMoorhead, W.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160047.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160061 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160061$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160061$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN690 =082 04$a671.3/6$223 =100 1\$aLanda, R.,$eauthor. =245 10$aRecrystallization Study of Nb-Bearing HSLA Steels After Laboratory Batch Annealing Using OIM-EBSD Techniques /$cR. Landa, L. Kish, S. Tan, R. Ordoñez, C. Isaac Garcia. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aThe present work studied the recrystallization kinetics of a Nb-bearing high strength low alloy (HSLA) steel using a fully-computer controlled laboratory batch annealing (BA) process. This work was designed to study the effect of thermo-mechanical processing (TMP), transformation products, and the amount of cold deformation on the kinetics of recrystallization. The amount of deformation above and below the non-recrystallization (Tnr) temperature of the steel used in this study was investigated in terms of the grain boundary character distribution (GBCD) assessed in the hot band condition. The hot band condition was then subjected to 60 % cold deformation prior to the BA studies. The cold rolled samples were placed in the laboratory BA furnace using the simulated cold spot temperature (CST) annealing process. The selected annealing temperature was 650°C and the holding times varied between 15 minutes and 12 h. The central focus of this work was to understand how the TMP schedule affects the GBCD of the hot band; how the frequency of this initial GBCD changes with the amount of cold deformation; and how the steel composition, stored energy, GBCD, and annealing processing parameters influence the annealing behavior of the steel used in this study. Advanced microstructural techniques including orientation imaging microscopy and electron back-scattered diffraction (EBSD) provided the evolution of the GBCD, the changes in stored energy with annealing times. The results of this investigation clearly showed that when the TMP is conducted in a temperature range where the deformation of austenite favors twin formation, leading to higher levels of high angles grain boundaries (HAGB) and special coincidence site lattice (CSL) boundaries, the kinetics of recrystallization are increased. The results of this work were presented and discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAnnealing. =650 \0$aOIM analysis. =650 \0$aRecrystallization (Metallurgy) =650 \0$aRecrystallization. =650 \0$aStored energy. =650 14$aAnnealing. =650 24$aEBSD. =650 24$aHSLA steel. =650 24$aOIM analysis. =650 24$aRecrystallization. =650 24$aStored energy. =700 1\$aIsaac Garcia, C.,$eauthor. =700 1\$aKish, L.,$eauthor. =700 1\$aOrdoñez, R.,$eauthor. =700 1\$aTan, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160061.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160037 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160037$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160037$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTC78.7.T6 =082 04$a616.07572$223 =100 1\$aRao, Suraj,$eauthor. =245 10$aMeasurement and Analysis of Porosity in Al-10Si-1Mg Components Additively Manufactured by Selective Laser Melting /$cSuraj Rao, Ross Cunningham, Tugce Ozturk, Anthony Rollett. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b33 =520 3\$aAluminum alloys are candidate materials for weight critical applications because of their excellent strength and stiffness to weight ratio. However, defects such as voids decrease the strength and fatigue life of these alloys, which can limit the application of Selective Laser Melting. In this study, the average volume fraction, average size, and size distribution of pores in Al10-Si-1Mg samples built using Selective Laser Melting have been characterized. Synchrotron high energy X-rays were used to perform computed tomography on volumes of order one cubic millimeter with a resolution of approximately 1.5 ?m. Substantial variations in the pore size distributions were found as a function of process conditions. Even under conditions that ensured that all locations were melted at least once, a significant number density was found of pores above 5 ?m in diameter. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAdditive manufacturing. =650 \0$aAnatomy, Regional. =650 \0$aPorosity. =650 \0$aSelective laser melting. =650 \0$aSynchrotron. =650 \0$aX-ray computed tomography (XCT) =650 14$aAdditive manufacturing. =650 24$aAl10-Si-1Mg. =650 24$aPorosity. =650 24$aSelective laser melting. =650 24$aSynchrotron. =650 24$aX-ray computed tomography (XCT) =700 1\$aCunningham, Ross,$eauthor. =700 1\$aOzturk, Tugce,$eauthor. =700 1\$aRollett, Anthony,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 5 Special Issue on Metallography, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160037.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150041 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150041$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150041$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aHeck, S.,$eauthor. =245 10$aInfluence of Pack Boriding on the Wear and Corrosion Resistance of AISI H13 Steel /$cS. Heck, A. Neto, C. Picon, G. Totten, L. Casteletti. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b15 =520 3\$aThis work investigates the effect of pack boriding time and temperature on the wear and corrosion resistance of AISI H13 tool steel. Steel samples were pack borided at 900 and 1000°C for periods of 2 and 4 h; followed by non-abrasive fixed-ball microwear tests on borided and non-borided samples. The corrosion resistance was evaluated by potentiodynamic polarization tests in HCl 0.1 M. High hardness layers were formed on the samples for all treatment conditions employed. The layer's properties, such as hardness, thickness, layer/substrate interface morphology, and phases formed, were influenced by steel composition. For AISI H13 steel, which has a larger amount of alloying elements than carbon steel, the formed layers were hard, thin, with a smoother interface. For all treatment conditions, the presence of Fe2B, FeB, and CrB were identified. The wear and corrosion resistance of borided samples was significantly increased. The best results were obtained for samples borided at 1000°C. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBoriding. =650 \0$aCorrosion. =650 \0$aPack boriding. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 \0$aWear. =650 14$aPack boriding. =650 24$aAISI H13. =650 24$aBoriding. =650 24$aCorrosion. =650 24$aWear. =700 1\$aCasteletti, L.,$eauthor. =700 1\$aNeto, A.,$eauthor. =700 1\$aPicon, C.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150041.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160003 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160003$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160003$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.1/86$223 =100 1\$aNayak, I.,$eauthor. =245 10$aEffect of Heat Treatment and Surface Condition on Inter-Granular Corrosion of Alloy 800 /$cI. Nayak, S. Rao, K. Kapoor. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b14 =520 3\$aThe alloy 800 is being used for steam generator tubings for pressurized heavy-water reactors (PHWRs). This material is susceptible to degradation because of severe operating conditions, like high temperature, stress, and corrosive environment. These degradation mechanisms include primary water stress corrosion cracking (PWSCC), secondary side or outer diameter stress corrosion cracking (ODSCC), inter-granular corrosion (IGC), fretting, wear, denting, high cycle fatigue, corrosion fatigue, etc. The present study was conducted to analyze the effect of solution annealing temperatures, sensitization treatments, and surface conditions on the corrosion rate. The alloy 800 tubular samples were investigated by means of a conventional corrosion test (according to ASTM G28-02) and an electrochemical potentiokinetic reactivation (EPR) test. Susceptibility to inter-granular corrosion under various experimental parameters was examined by using both the test methods and the results are compared. The observed trends in corrosion rate obtained by using conventional method and EPR test were found to be similar. These results were used to obtain most optimum heat-treatment parameters and surface condition, which will yield best corrosion resistance. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum alloys. =650 \0$aDegree of sensitization. =650 \0$aInter-granular corrosion. =650 \0$aMetals$xHeat treatment. =650 \0$aShot peening. =650 \0$aSolution annealing. =650 \0$aSteam generator. =650 14$aInter-granular corrosion. =650 24$aAlloy 800. =650 24$aDegree of sensitization. =650 24$aEPR. =650 24$aPHWR. =650 24$aShot peening. =650 24$aSolution annealing. =650 24$aSteam generator. =700 1\$aKapoor, K.,$eauthor. =700 1\$aRao, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160003.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150030 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150030$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150030$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.52 =082 04$a620.1/1296$223 =100 1\$aGowda, S.,$eauthor. =245 10$aQuasi-Static, Cyclic Fatigue and Fracture Behavior of Alloy Steel for Structural Applications :$bInfluence of Orientation /$cS. Gowda, C. Hotz, K. Manigandan, T. Srivatsan, A. Patnaik, J. Payer. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aIn this paper, the results of a study aimed at understanding the extrinsic influence of test specimen orientation, with respect to a wrought alloy-steel plate, on the stress-controlled cyclic fatigue properties and fracture behavior of a structural steel is highlighted. The alloy steel chosen was ASTM A572 grade 50. Samples of this alloy steel, prepared from both the longitudinal and transverse orientations, were cyclically deformed over a range of maximum stress and the corresponding number of cycles to failure (NF) was recorded. The influence of test specimen orientation and intrinsic microstructural effects on cyclic fatigue life and fracture behavior are presented and discussed. Overall, the macroscopic fracture mode was essentially identical regardless of orientation of the test specimen with respect to the wrought plate. The microscopic mechanisms governing cyclic deformation, fatigue life, and final fracture behavior are presented in light of the mutually interactive influences of magnitude of applied stress, intrinsic microstructural effects, orientation of test specimen, and deformation characteristics of the key microstructural constituents. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAlloy steel. =650 \0$aFatigue. =650 \0$aFracture behavior. =650 \0$aMaterials$xThermal properties. =650 \0$aMicrostructure. =650 \0$aOrientation. =650 \0$aTensile properties. =650 \0$aThermodynamics. =650 14$aAlloy steel. =650 24$aFatigue. =650 24$aFracture behavior. =650 24$aMicrostructure. =650 24$aOrientation. =650 24$aTensile properties. =700 1\$aHotz, C.,$eauthor. =700 1\$aManigandan, K.,$eauthor. =700 1\$aPatnaik, A.,$eauthor. =700 1\$aPayer, J.,$eauthor. =700 1\$aSrivatsan, T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150030.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150042 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150042$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150042$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a620.17$223 =100 1\$aVatavuk, J.,$eauthor. =245 10$aComparative Impact Behavior of High-C Steel After Conventional Quenching, Tempering, and Austempering /$cJ. Vatavuk, G. Totten, J. Nucci, L. Albano, L. Canale. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b22 =520 3\$aUsually bainitic microstructures exhibit good toughness and austempering is typically the preferred heat treatment when toughness is the primary requirement of the component. Several reports have shown such characteristics when compared to tempered martensite. High-carbon steel may exhibit brittle characteristics but it is a good steel with respect to mechanical properties and wear resistance. The objective of this study was to compare the impact properties of AISI O1, a high-carbon tool steel, designated VND in Brazil. This was done by comparing Charpy impact strength under different heat-treatment cycles. Steel test specimens were quenched from 820°C and tempered at 450°C to obtain tempered martensite, then austenitized, cooled, and held at 350°C to obtain bainite by holding at temperature for 20, 40, and 60 min. Because hardness influences impact behavior, comparative studies were performed at the same surface hardness level. The austempered samples with bainite microstructures obtained at a constant temperature and, by varying holding times, exhibited lower impact properties as compared to the quenched and tempered condition. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBainite. =650 \0$aBainitic steel. =650 \0$aImpact properties. =650 \0$aTempered martensite. =650 14$aBainite. =650 24$aImpact properties. =650 24$aTempered martensite. =700 1\$aAlbano, L.,$eauthor. =700 1\$aCanale, L.,$eauthor. =700 1\$aNucci, J.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150042.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150011 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150011$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150011$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.52 =082 04$a620.1/1296$223 =100 1\$aDevaraj, S.,$eauthor. =245 10$aElectric Erosion Induced Microstructure and Mechanical Properties in Spark Plasma Sintered Al-4.5 wt. % Cu Alloy /$cS. Devaraj, R. Kumar, S. Sankaran. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b20 =520 3\$aThe Al-4.5 wt.% Cu powder was compacted by spark plasma sintering at three compaction pressures namely 30, 40, and 50 MPa maintaining temperature constant at 500°C. Porosity seems to be closed in all the 3 cases. Relative density of S-50 is decreased due to increase in electrical erosion holes. Transmission electron microscopy studies reveal the presence of dislocations in all the compacts and shear bands observed only in the compact sintered at 50 MPa. A power law creep mechanism involving dislocations is found to be observed in all the compacts sintered at all pressures, which is evident from the TEM micrographs as well. The dissolution of Al2Cu precipitates in the aluminum matrix, and the increase in electric erosion holes were noticed with increase in pressure from 30 to 50 MPa. The decrease in the volume fraction of Al2Cu phase and the increase in the formation of electric erosion holes resulted in reduced hardness and compression strengths of the compacts. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCompression strength. =650 \0$aElectric erosion hole. =650 \0$aHardness. =650 \0$aMaterials$xThermal properties. =650 \0$aMechanism. =650 \0$aMicrostructure. =650 \0$aSpark plasma sintering. =650 \0$aThermodynamics. =650 14$aSpark plasma sintering. =650 24$aCompression strength. =650 24$aElectric erosion hole. =650 24$aHardness. =650 24$aMechanism. =650 24$aMicrostructure. =700 1\$aKumar, R.,$eauthor. =700 1\$aSankaran, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150011.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150036 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150036$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150036$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aCasteletti, L.,$eauthor. =245 10$aInfluence of Boronizing Treatment on Fe-Mn-Al-Si-C Steel /$cL. Casteletti, G. Takeya, A. Neto, C. Picon, G. Totten. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b10 =520 3\$aAustenitic Fe-Mn-Al-Si-C steel provides excellent cold formability and lower density compared to conventional stainless steels. These steels owe their corrosion and oxidation resistance to their aluminum and silicon contents, and the stability of their gamma phase is due to manganese and carbon alloying elements. The production of a boride layer with high hardness can significantly increase its surface hardness and consequently its wear resistance. In this work, Fe-31Mn-7.5Al-1.3Si-0.9C steel samples were subjected to a boriding treatment for 4 h at 900°C. The composition of the bath was 90 % borax and 10 % aluminum. Boride layers with high hardness levels were obtained (1900 HV). There was also a marked increase in wear resistance of the material. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBoronizing. =650 \0$aCorrosion. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 \0$aWear. =650 14$aAustenitic Fe-Mn-Al-Si-C steel. =650 24$aBoronizing. =650 24$aCorrosion. =650 24$aWear. =700 1\$aNeto, A.,$eauthor. =700 1\$aPicon, C.,$eauthor. =700 1\$aTakeya, G.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150036.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160046 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160046$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160046$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.52 =082 04$a620.1/1296$223 =100 1\$aSantra, S.,$eauthor. =245 14$aThe Effect of Thermal Treatment on Microstructure and Corrosion of Nickel Base Alloy 690 (UNS N0 6690) /$cS. Santra, S. Ramana Rao, K. Kapoor. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aAlloy 690 in the thermally treated (TT) condition is an advanced steam generator tubing material. The effect of thermal ageing treatments on the intergranular corrosion (IGC) behavior of the alloy was probed. Isothermal ageing was carried out at 600, 700, and 800°C with varying ageing time. Morphology of the carbides was studied as a function of thermal treatment temperature and duration. The carbides morphology was observed to affect the IGC resistance. Grain boundaries devoid of carbides (solutionized condition) or with coarse carbide particles (formed at 800°C) enhanced IGC resistance, whereas dendritic fine carbides formed at lower ageing temperature yield inferior IGC resistance. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCarbide. =650 \0$aGrain boundary. =650 \0$aIntergranular corrosion. =650 \0$aMaterials$xThermal properties. =650 \0$aSCIENCE$xNanoscience. =650 \0$aThermal treatment. =650 \0$aThermodynamics. =650 14$aAlloy 690. =650 24$aCarbide. =650 24$aGrain boundary. =650 24$aIntergranular corrosion. =650 24$aThermal treatment. =700 1\$aKapoor, K.,$eauthor. =700 1\$aRamana Rao, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160046.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150072 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150072$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150072$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQE606 =082 04$a553.282$223 =100 1\$aKarsim, L.,$eauthor. =245 10$aExperimental Investigation of the Effect of Polyisobutilene Additives to Mineral Oil on Cooling Characteristics /$cP. Lohvynenko, A. Moskalenko, N. Kobasko, L. Karsim, S. Riabov. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aResults of an experimental study of the effect of polyisobutilene additives to mineral oils I-20A, I-12A, and I-8A on their cooling characteristics are provided. It is shown that a small amount of the polyisobutilene oligomer in mineral oil I-20A (3 %) can completely eliminate a film-boiling process during the quenching of steel parts and make a significantly shorter period of film-boiling during quenching in oils I-12A and I-8A. In this case, a surface of steel parts is cooled intensively and constantly, the part distortion is minimal, and hardness is greater and more consistent. The results of the study were applied to bearing products produced by the Svenska Kullagerfabriken AB (SKF) bearing plant (Lutsk, Ukraine) =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aConsistence cooling. =650 \0$aDistortion. =650 \0$aFaults (Geology) =650 \0$aFluid dynamics. =650 \0$aHydrocarbon reservoirs. =650 \0$aMineral oils. =650 \0$aOligomer. =650 \0$aPolyisobutilene. =650 \0$aSolutions. =650 14$aPolyisobutilene. =650 24$aConsistence cooling. =650 24$aDistortion. =650 24$aMineral oils. =650 24$aOligomer. =650 24$aSolutions. =700 1\$aKarsim, L.,$eauthor. =700 1\$aKobasko, N.,$eauthor. =700 1\$aMoskalenko, A.,$eauthor. =700 1\$aRiabov, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150072.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150027 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150027$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150027$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC482.D5 =082 04$a548/.83$223 =100 1\$aFujita, Takumi,$eauthor. =245 10$aEvaluation of Rolling Contact Fatigue Using X-Ray Diffraction Ring /$cTakumi Fujita, Naoya Kamura, Yoichi Maruyama, Toshihiko Sasaki. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b37 =520 3\$aIn this report, a novel approach for evaluating the progressive degree of rolling contact fatigue (RCF) is introduced. The rolling contact surface after two-cylinder testing was evaluated by a new X-ray analyzer, which can rapidly obtain tri-axial residual stresses and the orientation of crystallite from an X-ray diffraction ring (Debye ring) on a two-dimensional detector. The non-uniform intensity of the Debye ring was observed for the tested sample under boundary lubrication. This makes it clear that RCF, under asperity contact conditions, accompanies the formation of an oriented texture of martensite grain. In addition, characteristic residual stresses that differ from the plane stress condition were observed for asperity contact surface, and residual von Mises stress, derived from their tri-axial residual stresses, demonstrates severe plastic deformation close to yield stress of hardened bearing steel. The behaviors of martensite grain orientation, tri-axial residual stress, and surface damage were investigated for several samples under different RCF conditions to clarify the mechanism of surface-initiated failure. The Debye ring analyzer can rapidly obtain more information regarding accumulation of fatigue, criteria of fracture, crack development, and shake-down in rolling contact subsurface, as compared with conventional X-ray diffraction analyzers. This new system is a promising method, not only to investigate the mechanism of RCF, but also to allow for the quantitative estimation of the progressing degree of RCF. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAmorf materiaal. =650 \0$aRayons X$xDiffraction. =650 \0$aRolling contact fatigue. =650 \0$aTri-axial residual stresses. =650 \0$aX-Ray Diffraction. =650 14$aRolling contact fatigue. =650 24$aDebye ring, residual stress. =650 24$aSasaki-Hirose method. =650 24$aTri-axial residual stresses. =650 24$aX-ray diffraction. =700 1\$aKamura, Naoya,$eauthor. =700 1\$aMaruyama, Yoichi,$eauthor. =700 1\$aSasaki, Toshihiko,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150027.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150046 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150046$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150046$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN664 =082 04$a669.2$223 =100 1\$aMartínez-Cazares, G.,$eauthor. =245 10$aEnhanced Hardenability and Tempering Resistance of AISI 4130 Steel by Ni Addition /$cG. Martínez-Cazares, A. Almanza, E. Almanza, D. Lozano. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b8 =520 3\$aThe AISI 4130 steel grade is commonly used in piping systems, where optimum chemical composition and heat treatment can exhibit high yield strength, good ductility, and moderate weldability depending on composition. However, this steel grade is characterized by its low hardenability, which limits a good transformation during quenching in heavy sections. In order to improve hardenability, Ni was added and C was reduced for the same level of CE (0.7). Two chemical compositions were used; samples were quenched at critical cooling rate and tempered. With the addition up to 0.5 wt. % Ni, the alloy exhibited great improvement on strength and toughness; additionally, the alloy allowed an increase of 40°C on the tempering temperature for the same strength level. In the case of post-welding, heat treatment is required so that the alloy is less susceptible to suffering a drop in mechanical properties. Results of chemical composition, strength, and toughness are discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aHardenability. =650 \0$aMines and mineral resources. =650 \0$aNickel$xMetallurgy. =650 \0$aNickel. =650 \0$aPlatinum group$xMetallurgy. =650 \0$aQuenching. =650 14$a4130. =650 24$aHardenability. =650 24$aNickel. =650 24$aQuenching. =700 1\$aAlmanza, A.,$eauthor. =700 1\$aAlmanza, E.,$eauthor. =700 1\$aLozano, D.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150046.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150048 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150048$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150048$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a629.1$223 =100 1\$aHussain, M.,$eauthor. =245 10$aFatigue Life Prediction of a Unidirectional Carbon Fiber Composite Under Off-Axis Spectrum Loads Using 3D Constant Life Diagram /$cM. Hussain, A. Anilchandra, N. Jagannathan, C. Manjunatha. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b37 =520 3\$aIn this study, a novel concept of 3D constant life diagram (CLD) for fatigue life prediction of a unidirectional (UD) polymer composite under spectrum load is proposed. Further, it is constructed and used to predict the fatigue life of a UD carbon fiber composite (CFC) subjected to a standard spectrum load sequence at an arbitrary off-axis angle. First, UD IMA/M21 CFC laminates were fabricated by an autoclave process. Static mechanical tests were conducted to determine the tensile and compressive strength at various off-axis angles ranging from 0° to 90°. Then the constant amplitude (CA) fatigue tests at three different stress ratios, R = ?min/?max of 0.1 (tension-tension), –1.0 (tension-compression), and 10.0 (compression-compression) and at various off-axis angles between 0° and 90° at each of these stress ratios were performed to determine stress-life curves. Using the static and CA fatigue data generated, 3D CLD for UD CFC was constructed. Further, fatigue life of UD CFC subjected to a standard mini-FALSTAFF spectrum load sequence at an arbitrary off-axis angle of 20° was predicted following an empirical method using 3D CLD. Fatigue tests under the mini-FALSTAFF spectrum load sequence at an off-axis angle of 20° were also conducted at various reference stresses and compared with the predictions. A reasonably good correlation was observed between the predicted and experimental fatigue lives under off-axis spectrum loads. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAerospace engineering. =650 \0$aConstant life diagram. =650 \0$aFatigue. =650 \0$aLife prediction. =650 \0$aPolymer composite. =650 \0$aPolymer composites. =650 \0$aSpectrum loading. =650 14$aPolymer composite. =650 24$aConstant life diagram. =650 24$aFatigue. =650 24$aLife prediction. =650 24$aSpectrum loading. =700 1\$aAnilchandra, A.,$eauthor. =700 1\$aJagannathan, N.,$eauthor. =700 1\$aManjunatha, C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150048.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160004 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160004$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160004$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC88.9.M6 =082 04$a616.02/52$223 =100 1\$aDee, S.,$eauthor. =245 10$aDevelopment of a Slip Hazard :$bPartially Wetted Floors and Film Formation /$cS. Dee, R. Ogle, B. Cox. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b31 =520 3\$aSlip and fall hazards on wetted surfaces represent a substantial safety concern both in the home and workplace. In the presence of liquid contaminants, the hazards associated with potential slip and fall accidents are greatly increased. However, it is unclear at what point a partially wetted floor transitions from being a slip-resistant surface to a slip hazard. The presented work examines the relationship between film formation and slip hazards on flooring surfaces. First, a theoretical model was developed to predict the approximate onset of film formation for liquid droplets deposited uniformly across a surface. Then, the slip hazard of wetted flooring samples at various liquid contaminant surface densities was determined using a British Pendulum skid tester and an English XL tribometer. These experimental results were then compared with the theoretical model in an effort to further understand the role film formation plays in forming slip hazards on partially wetted floors. Using the combined approach, the minimum surface density loading required for a potential slip and fall hazard on a partially wetted surface was determined. This threshold value can inform safety professions of the potential injury risk of floors as they transition between dry to wet conditions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAnd falls. =650 \0$aFilm formation. =650 \0$aFirst aid in illness and injury. =650 \0$aInjury prevention. =650 \0$aOutdoor medical emergencies. =650 \0$aSlips. =650 \0$aWetted floors. =650 \0$aWilderness. =650 14$aSlips. =650 24$aAnd falls. =650 24$aFilm formation. =650 24$aInjury prevention. =650 24$aTrips. =650 24$aWetted floors. =700 1\$aCox, B.,$eauthor. =700 1\$aOgle, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160004.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150060 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150060$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150060$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.F55 =082 04$a363.72/88$223 =100 1\$aManakari, V.,$eauthor. =245 10$aEffects of Hollow Fly-Ash Particles on the Properties of Magnesium Matrix Syntactic Foams :$bA Review /$cV. Manakari, G. Parande, M. Gupta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b46 =520 3\$aIn the past decade, magnesium has been seen as one of the most potential metals for weight-critical engineering applications. As magnesium is the lightest structural metal, it has higher weight-saving capabilities when compared to aluminum. Significant research efforts have been carried out on magnesium matrix alloys and composites to tailor and enhance mechanical properties based on end applications. This paper provides a review on fly-ash-reinforced magnesium matrix syntactic foams. Fly-ash cenospheres are made up of mainly alumina and silica and also contains large number of trace elements, which makes it intriguing to analyze the microstructure and interfacial responses of the end composites. In comparison with aluminum matrix syntactic foams, the research on magnesium matrix syntactic foams is still at an incipient stage. This paper provides an insight on processing techniques, microstructural and mechanical evaluations of pure Mg, AZ, and ZC alloy series, and their syntactic foams. This paper also reviews the weight-saving ability of magnesium matrix syntactic foams and their potential scope and applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFly ash$xEnvironmental aspects. =650 \0$aFly-ash cenospheres. =650 \0$aMagnesium. =650 \0$aSyntactic foams. =650 14$aMagnesium. =650 24$aFly-ash cenospheres. =650 24$aSyntactic foams. =700 1\$aGupta, M.,$eauthor. =700 1\$aParande, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150060.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150047 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150047$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150047$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA640.2 =082 04$a624.1/71$223 =100 1\$aMcMillan, A.,$eauthor. =245 10$aExplicit Finite Element Modelling as a Development Tool for New Ultrasound Testing Methodologies for Detection and Characterization of Porosity and Defects in Composites /$cA. McMillan, K. Holeczek. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b29 =520 3\$aComposite components frequently contain porosity or defects, which might, in some circumstances, be deemed benign. Other defects could lead to progressive or sudden failure in service; hence reliable and accurate material condition monitoring and health assessment is an important prerequisite for further design for the use of composite materials in high duty and life sensitive engineering components. The objective of this paper was to demonstrate the use of explicit finite element as an effective development tool in the development of ultrasound testing methodologies for the characterization of porosity in composites - a virtual ultrasound vibration laboratory. This would enable an improved inspection sentencing capability for as-manufactured composite structural components. It would also be of benefit in sentencing components subject to foreign object damage (FOD) in order to determine whether the component can continue in service, possibly with in-service monitoring or cosmetic repair, or must be condemned. In this work, finite element models simulating damage and porosity were presented. The models were compared with ultrasound tests on real specimens with practically relevant defects. Experimental tests, making use of wave superposition from two piezo-electric vibration sources, were shown to detect energy absorbing damage in the specimen, such as might have been created by impact or crush loads. The same piezo-electric vibration system was also used to measure the dissipated energy. Computational analysis, using simple material model variations, was able to replicate the Lamb wave generation and evolve a wave form resembling a “standing wave.” The computational material model was modified to represent porosity in composites. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aComposites. =650 \0$aContinuum mechanics. =650 \0$aExplicit finite element. =650 \0$aPorosity detection. =650 \0$aSolid wave interferences. =650 \0$aStructural analysis (Engineering) =650 \0$aStructural health monitoring. =650 14$aStructural health monitoring. =650 24$aComposites. =650 24$aExplicit finite element. =650 24$aPorosity detection. =650 24$aSolid wave interferences. =700 1\$aHoleczek, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150047.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150031 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150031$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150031$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD257.7 =082 04$a661.8$223 =100 1\$aHassan, A.,$eauthor. =245 10$aModeling Effective Thermal Conductivity of Randomly Distributed Loads of Mono-Sized Parts of Arbitrary Geometry /$cA. Hassan, M. Hamed. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b31 =520 3\$aA new model of the effective thermal conductivity of randomly distributed loads of mono-sized metal parts of arbitrary geometry heated under natural convective and radiation heat transfer has been developed. A series of transient heating experiments has been performed in a batch-type furnace using loads comprised of parts of various geometries, sizes, steel grades, and void fractions and at various furnace set point temperatures. Experimental results showed a strong dependency of the load effective thermal conductivity on: (1) load void fraction, (2) internal radiation between parts, and (3) external radiation between parts and furnace enclosure. An assessment of a number of effective thermal conductivity models reported in the literature and developed for packed beds and porous media has been carried out. This assessment led to the development of the present model, which incorporates a new additional temperature difference term that accounts for external radiation and a new generalized characteristic length scale that can be used for parts of any arbitrary geometry. All thermophysical properties of solid and gaseous phases have been considered as functions of the parts temperature. The proposed model is in good agreement, within ±25 %, with the experimental data obtained for the various part geometries, load void fractions, and the surrounding temperatures considered in this investigation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aEffective thermal conductivity. =650 \0$aModel. =650 \0$aMono-sized parts. =650 \0$aOrganic compounds$vHandbooks, manuals, etc. =650 \0$aOrganic compounds. =650 \0$aRadiative conductivity. =650 \0$aRandomly distributed load. =650 14$aEffective thermal conductivity. =650 24$aModel. =650 24$aMono-sized parts. =650 24$aRadiative conductivity. =650 24$aRandomly distributed load. =700 1\$aHamed, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150031.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160007 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160007$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160007$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC320 =082 04$a536.2$223 =100 1\$aLišcic, B.,$eauthor. =245 10$aMeasurement and Recording of Quenching Intensity in Workshop Conditions Based on Temperature Gradients /$cB. Lišcic. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b8 =520 3\$aThe cooling characteristics of a liquid quenchant are usually determined by a laboratory test using a small cylindrical probe with one thermocouple in its geometrical center. The reasons why the results of the laboratory tests do not represent the real quenching intensity of quenching workpieces in workshop conditions are described. Instead, a new Lišcic/Petrofer probe with a larger mass, having three thermocouples, is used for measurement and recording real quenching intensity during industrial practice. The working principle of this probe is the measurement of dynamic of heat extraction, which is best represented by the change of temperature gradients. The temperature gradient method and the Lišcic/Petrofer probe are described using an example of quenching in mineral oil at room temperature, without agitation. Calculation of the heat-transfer coefficient, as well as distinctive characteristics of the cooling curves recorded and heat-transfer data calculated when using the Lišcic/Petrofer probe is explained. For impartial analysis and use of results obtained by using the new probe, six characteristic criteria from the relevant diagrams are used. Based on selected tests with the new probe, the influence of quenchant temperature and agitation rate on the quenching intensity is shown in numerical form for mineral oil and for water. A series of 26 tests has proved that: (1) the results obtained by the new probe and method have provided information that is not obtainable from small laboratory probes; (2) the new method is sufficiently sensitive to clearly differentiate the results when changes of some quenching parameters (bath temperature or agitation rate) occur; and (3) the Lišcic/Petrofer probe can be used for different kinds of liquid quenchants at different quenching conditions typically encountered in industrial practice. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aHeat$xTransmission. =650 \0$aHeat-transfer coefficient. =650 \0$aQuenching intensity. =650 \0$aTemperature gradient method. =650 \0$aWarmtetransport. =650 14$aQuenching intensity. =650 24$aHeat-transfer coefficient. =650 24$aTemperature gradient method. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160007.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150021 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150021$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150021$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.1/920427$223 =100 1\$aPant, S.,$eauthor. =245 10$aIn-Situ Characterization of Isotropic and Transversely Isotropic Elastic Properties Using Ultrasonic Wave Velocities /$cS. Pant, J. Laliberte, M. Martinez, B. Rocha. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aIn this paper, a one-sided, in situ method based on the time of flight measurement of ultrasonic waves was described. The primary application of this technique was to non-destructively measure the stiffness properties of isotropic and transversely isotropic materials. The method consists of generating and receiving quasi-longitudinal and quasi-shear waves at different through-thickness propagation angles. First, analytical equations were provided to calculate the ultrasonic wave velocities. Then, an inverse method based on non-linear least square technique was used to calculate the stiffness constants using the ultrasonic wave velocities. Sensitivity analysis was performed by randomly perturbing the velocity data, thus observing the effects of perturbations on the calculated stiffness constants. An improved algorithm was proposed and tested to reduce the effects of random errors. Based on the sensitivity analysis, minimum number of angles required to inversely calculate the stiffness constants were suggested for isotropic and transversely isotropic material. The method was experimentally verified on an isotropic 7050-T7451 aluminum with two different thicknesses and a transversely isotropic composite laminate fabricated using 24 plies of CYCOM 977-2 12 k HTA unidirectional carbon fiber reinforced polymer (CFRP) prepregs. The results demonstrated that this technique is able to accurately measure the material properties of isotropic material. As for the transversely isotropic material, this method was able to accurately measure the material properties if the experimental errors can be reduced to less than 1 %. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aComposite. =650 \0$aMaterial characterization. =650 \0$aMaterial stiffness constants. =650 \0$aNon-destructive evaluation. =650 \0$aPolymeric composites$xNon-destructive testing. =650 \0$aUltrasound wave velocities. =650 14$aMaterial characterization. =650 24$aComposite. =650 24$aMaterial stiffness constants. =650 24$aNon-destructive evaluation. =650 24$aUltrasound wave velocities. =700 1\$aLaliberte, J.,$eauthor. =700 1\$aMartinez, M.,$eauthor. =700 1\$aRocha, B.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150021.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150033 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150033$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150033$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.L4 =082 04$a669.4$223 =100 1\$aDaoud, A.,$eauthor. =245 10$aAging Behavior of Pb Alloy-45 Volume % Fly Ash Microballoon Composites /$cA. Daoud, M. Abou El-Khair, F. Fairouz, E. Mohammed, A. Lotfy, P. Rohatgi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b20 =520 3\$aComposites comprising Pb alloys and 45 Volume % of nickel-coated flay ash (FA) microballoons were manufactured by stir casting method. Aging studies were carried out on the Pb alloys and composites in order to investigate the influence of the microballoons' presence on the aging behavior. The Pb matrix alloys and their composites were solution treated at 280°C for 5 h, and water quenched and aged at 60 and 100°C for various times. Aging investigation revealed that the peak hardness attained in the composite is higher than that of the Pb matrix alloy because of the refined structures of the composites in comparison to those of the Pb alloys, the presence of the microballoons, as well as increasing dislocation density in the composites. Also, the existence of FA microballoons in the Pb-0.06 Ca-1.2 Sn alloy results in an accelerating the age hardening kinetics of the composites. However, in case of Pb-0.13Ca -0.3 Sn-0.014 Al and Pb-0.065Ca-1.1 Sn-0.014 Ag based composites, the presence of the microballoons do not significantly affect the time for peak aging. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAging behavior. =650 \0$aLead alloys. =650 \0$aLead. =650 \0$aMetal-matrix composites (MMCs) =650 14$aMetal-matrix composites (MMCs) =650 24$aAging behavior. =650 24$aFA. =650 24$aLead alloys. =700 1\$aAbou El-Khair, M.,$eauthor. =700 1\$aFairouz, F.,$eauthor. =700 1\$aLotfy, A.,$eauthor. =700 1\$aMohammed, E.,$eauthor. =700 1\$aRohatgi, P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150033.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150039 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150039$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150039$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.1/7$223 =100 1\$aMariani, F.,$eauthor. =245 10$aHeat Treatment of Precipitation-Hardening Stainless Steels Alloyed With Niobium /$cF. Mariani, G. Takeya, L. Casteletti, A. Neto, G. Totten. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b15 =520 3\$aPrecipitation-hardening stainless steels are iron-nickel-chromium alloys containing precipitation hardening elements such as aluminum, titanium, niobium, and copper. In this work, heat treatment of a novel precipitation hardening stainless steel using niobium as a forming element for the hardening precipitates was carried out in order to increase its hardness. The steel composition was 0.03C - 0.22Si - 17.86Cr - 3.91Ni - 2.19Mo - 1.96Nb (in wt.%). The samples were solution annealed at 1100°C for 2 h. Cooling was done in oil and the samples were subsequently aged at 500, 550, and 600°C. The solution annealed samples exhibited an average hardness of 30 Hardness Rockwell-Scale C and after the aging treatments, the hardness increased to 46 HRC. The hardness increases during the aging treatments were very fast. A 5 min treatment achieved hardness levels that were close to the maximum obtained for this alloy. Niobium was an efficient precipitation hardeners forming a Laves phase of the type Fe2Nb. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAging. =650 \0$aBuilding materials. =650 \0$aEngineering design. =650 \0$aHeat treatment. =650 \0$aNiobium. =650 \0$aPrecipitation-hardening. =650 \0$aStainless steel. =650 14$aStainless steel. =650 24$aAging. =650 24$aHeat treatment. =650 24$aNiobium. =650 24$aPrecipitation-hardening. =700 1\$aCasteletti, L.,$eauthor. =700 1\$aNeto, A.,$eauthor. =700 1\$aTakeya, G.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150039.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130099 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130099$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD9524.C2 =082 04$a338.4/7671/0971$223 =100 1\$aBucquet, Thibaud,$eauthor. =245 10$aFlow Optimization of Gas Quenching Processes Using Perforated Plates /$cThibaud Bucquet, Udo Fritsching. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aIndustrial gas quenching is a cost-effective, environmental-friendly alternative to conventional fluid-based quenching processes used for the heat treatment of workpieces mainly in the automotive industry. The influence of the heat exchanger geometry in a novel gas quenching chamber on the gas flow was investigated through measurement in parallel to CFD-simulations. With reduced quenching chamber dimensions, a flow guiding system utilizing a perforated plate placed between the heat exchanger and the batch has been found to play a significant role on the velocity and turbulence distribution of the gas flow. The use of various perforated plates in this gas quenching process focuses on the exploration of two main parameters: plate porosity and perforation hole diameters. By combining in situ flow and CFD-simulations of heat and fluid flow, optimized parameters have been determined indicating improved uniformity and intensity of the velocity distribution in the quenching chamber, thus obtaining the potential of an overall improvement of the gas quenching process. Geometric parameters of perforated plates introduced into the gas quenching chamber facility are investigated as, e.g., the distance between the plate and the batch. More generally, the use of a perforated plate system to optimize gas flows may be extended to other applications where tube bundle heat exchangers in gas flow processes are involved. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$agas quenching. =650 \0$aHeat exchanger industry. =650 \0$aHeat exchanger. =650 \0$aHeat transfer simulation. =650 \0$aHeat treatment. =650 \0$aIndustrial gas quenching. =650 \0$aPerforated plate. =650 \0$aSteel industry. =650 14$aIndustrial gas quenching. =650 24$aHeat exchanger. =650 24$aHeat transfer simulation. =650 24$aHeat treatment. =650 24$aPerforated plate. =700 1\$aFritsching, Udo,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130099.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130115 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130115$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aPS3566.A822 =082 04$a813/.54$223 =100 1\$aAronov, M.,$eauthor. =245 10$aOverview on Super Strengthening Phenomenon Taking Place During Intensive Quenching of Steels /$cN. Kobasko, M. Aronov. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b26 =520 3\$aThis paper presents an overview on the super strengthening phenomenon that takes place during intensive quenching (IQ) of steels. It is shown that for obtaining an additional strengthening of material, one should pay special attention to whether the part cooling rate within the martensite range is high enough and whether compressive stresses are formed at the surface of steel parts. For hardening high carbon alloy steels with a low martensite start temperature, a two-step quenching procedure is recommended. At the first step of quenching, the martensite transformation is delayed, and, at the second step of quenching, the part cooling rate is accelerated within the martensite range. For hardening low and medium carbon steels, an IQ-3 quench method is recommended when a so-called direct convection cooling is applied for providing a maximal cooling rate within the martensite range and maximal compressive stresses at the surface of steel parts. To calculate a part cooling rate within the martensite range, a generalized equation is provided. Data on mechanical properties for different steels proving a presence of the super strengthening effect are provided also. A practical use of the super strengthening phenomenon is discussed in the paper. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCompressive stresses. =650 \0$acooling rate. =650 \0$amechanical properties. =650 \0$aPhenomenon. =650 \0$aService life. =650 \0$aSuper strengthening. =650 14$aSuper strengthening. =650 24$aCompressive stresses. =650 24$aCooling rate. =650 24$aMechanical properties. =650 24$aService life. =700 1\$aAronov, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130115.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130108 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130108$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN672 =082 04$a671.3/6$223 =100 1\$aStormvinter, Albin,$eauthor. =245 10$aInduction Hardening-Establishing the Process Window for Induction Quenching by Using Experimental Results and Computational Tools /$cAlbin Stormvinter, Hans Kristoffersen, Eva Troell. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aTo establish the process window for the spray quenching step of the induction hardening process is essential for quality control and optimized use of the quenching capacity supplied by the quenching unit. In general, the process window is established by an empirical approach, where the processing is related to the mechanical properties. On the other hand, there has been a rapid development of computational tools that may facilitate and accelerate process optimization. In the present work it is demonstrated how such tools, e.g., FE-simulation and multivariate analysis, can be applied to couple quenching characteristics to mechanical properties. The methodology is applied to induction hardened steel cylinders that were quenched with different flow rates, temperatures and composition of the quenchant. The results show how mechanical properties can be related to characteristics of the quenching, e.g., heat transfer coefficients and characteristics of the cooling curve. Moreover, the work discusses and exemplifies how the process window can be established and how computational tools allow the user to virtually alter the processing and estimate the impact it may have on the mechanical properties. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aheat treatment simulation. =650 \0$ainduction hardening. =650 \0$aquenching. =650 14$aInduction hardening. =650 24$aHeat treatment simulation. =650 24$aQuenching. =700 1\$aKristoffersen, Hans,$eauthor. =700 1\$aTroell, Eva,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130108.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140039 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140039$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQP752.O42 =082 04$a615.8/54$223 =100 1\$aCivera, C.,$eauthor. =245 10$aVegetable Oils as Quenchants for Steels :$bResidual Stresses and Dimensional Changes /$cC. Civera, B. Rivolta, R. Simencio-Otero, J. Lúcio, G. Totten, L. Canale. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b38 =520 3\$aThe development of non-toxic, biodegradable vegetable oils as alternatives to petroleum derived quenchants and their influence on residual stresses and dimensional changes of AISI 4140 and AISI H13 modified C-ring steel test specimens is discussed. The C-ring test specimens were quenched in 6 different vegetable oil blends based on soybean oil and the results were compared to 2 different commercially available petroleum oil quenchants. Residual stresses were determined by X-ray analysis on cylindrical test specimens after quenching. Some measurements were also performed using the hole-drilling method to confirm the results obtained using X-ray analysis. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aC-ring. =650 \0$adistortion. =650 \0$aQuenchant. =650 \0$aresidual stress. =650 \0$avegetable oil. =650 14$aQuenchant. =650 24$aC-ring. =650 24$aDistortion. =650 24$aResidual stress. =650 24$aVegetable oil. =700 1\$aCanale, L.,$eauthor. =700 1\$aLúcio, J.,$eauthor. =700 1\$aRivolta, B.,$eauthor. =700 1\$aSimencio-Otero, R.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140039.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140019 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140019$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ853.4.M53 =082 04$a620.1/064$223 =100 1\$aŽupan, Josip,$eauthor. =245 10$aCooling Characteristics of Water Based Nanofluids With Agitation /$cJosip Župan, Darko Landek, Tomislav Filetin. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b19 =520 3\$aA series of quenching experiments was performed according to the ISO 9950, ASTM 6200-01, and ASTM D6482-06 standards. Water based nanofluids with 0.01, 0.1, and 0.2 g/L TiO2 were prepared using a two-step method and ultrasonic homogenization. The nanofluids were tested to see the possibility of their application as high temperature heat transfer fluids. Nanoparticles used in this series of experiments were 50 nm in diameter. All of the cooling curves were recorded and analyzed using the ivf SmartQuench system. The first set of experiments was conducted under still conditions according to the ISO 9950 standard. Pure water and nanofluids were investigated. The addition of nanoparticles showed an effect on the full film phase duration, an increase in the maximum cooling rate, and a change in transition temperature. A second series of quenching experiments was conducted according to ASTM D 6482-06. For this purpose, a quenching bath with agitation was built at the QRC. Three levels of agitation were tested: one according to the standard, 1000 rpm, one below, and one above the specified speed. Experiments with pure water and all three nanofluids were conducted and cooling curves recorded. The cooling curves were analyzed using software ivf SQintegra ver4.0. The effects of agitation and nanoparticles contents on cooling characteristics were compared. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCooling curve analysis. =650 \0$aheat-transfer coefficient. =650 \0$ananofluids. =650 \0$aquenching. =650 14$aQuenching. =650 24$aCooling curve analysis. =650 24$aNanofluids. =650 24$aTiO2 nanoparticles. =700 1\$aFiletin, Tomislav,$eauthor. =700 1\$aLandek, Darko,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140019.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140006 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140006$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357 =082 04$a620.1/06$223 =100 1\$aSinger, Saša,$eauthor. =245 10$aSensitivity of the Heat-Transfer Coefficient Calculation /$cSaša Singer. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (26 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b23 =520 3\$aThe purpose of the Lišcic/Petrofer probe is to determine the cooling intensity during liquid quenching in laboratory and workshop environments. The surface heat-transfer coefficient is calculated by the one-dimensional finite-volume method from the smoothed temperature curve, measured at a near-surface point in the probe. Smoothed reference temperature curves for oil and water, based on measurements made with the probe, are used in a series of numerical experiments to investigate the sensitivity of the calculation with respect to various input parameters of the problem, such as thermal properties of the material, the near-surface thermocouple position, and the diameter of the probe. These results are relevant for other liquid quenchants, at least qualitatively, if not quantitatively. A similar type of analysis is conducted with respect to the variation of numerical simulation parameters in the finite-volume method-the choice of space and time steps for problem discretization. When the input curves are sufficiently smooth, the method itself is very reliable. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCore temperature. =650 \0$aFinite-volume method. =650 \0$agas quenching. =650 \0$aHeat exchanger industry. =650 \0$aHeat-transfer coefficient. =650 \0$aNumerical simulation. =650 \0$aQuenching. =650 \0$aSensitivity. =650 \0$aSteel industry. =650 \0$aSurface temperature. =650 14$aQuenching. =650 24$aCore temperature. =650 24$aFinite-volume method. =650 24$aHeat-transfer coefficient. =650 24$aNumerical simulation. =650 24$aSensitivity. =650 24$aSurface temperature. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140006.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130095 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130095$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC145.2 =082 04$a532/.057$223 =100 1\$aKobasko, N.,$eauthor. =245 10$aInvestigations of Nucleate Boiling Processes During Quenching Based on Possibilities of Noise Control System /$cN. Kobasko, A. Moskalenko, L. Deyneko. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b14 =520 3\$aA new method for evaluating and control of the optimal concentration of water salt solutions is proposed which is based on the possibilities of sound control system. Water salt solutions as quenchants are used in the practice to intensify hardening processes. In this paper, it is shown that water salt solutions are used for low and medium carbon alloy steels to create high compressive residual stresses at the surface of steel parts and improve mechanical properties of steels. It is underlined that quenching in water salt solutions must be interrupted at the appropriate time to prevent crack formation during fast cooling. When interruption occurs at the surface of steel parts, compressive residual stresses are formed and self-tempering takes place. During this time, at the core, a bainitic structure is formed which has enough strength and high plastic properties to prevent crack formation at the core where tensile stresses could be. It is shown that salt solutions can be also used for quenching of big steel parts like rollers and rotors. The benefits from the technology proposed are discussed in this paper. In the future, organic salt solutions can be replaced by organic salt solutions which prevent corrosion completely. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBenefits. =650 \0$aCompressive stresses. =650 \0$aHeat$x Transmission. =650 \0$amechanical properties. =650 \0$aNucleate Boiling. =650 \0$aOptimal concentration. =650 \0$aSalt solution. =650 \0$aSound control. =650 14$aSalt solution. =650 24$aBenefits. =650 24$aCompressive stresses. =650 24$aMechanical properties. =650 24$aOptimal concentration. =650 24$aSound control. =700 1\$aDeyneko, L.,$eauthor. =700 1\$aMoskalenko, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130095.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130089 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130089$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS320 =082 04$a672$223 =100 1\$aBoniardi, Marco,$eauthor. =245 10$aLarge Forgings :$bMicrostructural Evolution and Residual Stresses Due to Quenching Treatments-A Combined Numerical and Experimental Approach /$cMarco Boniardi, Mario Guagliano, Andrea Casaroli, Riccardo Andreotti, Filippo Ballerini. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b27 =520 3\$aBased on numerical and experimental data, an FEM model was implemented to simulate quench treatments on large forging components. After experimental validation of convection coefficient laws between water and component surface, time-temperature curves were determined for a large forged piece for different corss section of the component itself. Then superimposing these curves to the continuous cooling transformation diagram for the material, it was possible to identify the microstructural constituents of the steel after quenching. The component residual stress field was obtained by implementing the volumetric expansion law due to the phase transition during cooling. The ability to simulate the heat treatment of heavy size parts must be considered very useful due to quickly managing of all variables that govern the problem (initial and final temperatures, holding times, quenching mode, size, and geometry of components) and the possibility to predict final characteristics of the workpiece. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFEM simulation. =650 \0$alarge forgings. =650 \0$aquench treatments. =650 \0$aResidual stresses. =650 \0$aSteel forgings. =650 14$aLarge forgings. =650 24$aFEM simulation. =650 24$aQuench treatments. =650 24$aResidual stresses. =700 1\$aAndreotti, Riccardo,$eauthor. =700 1\$aBallerini, Filippo,$eauthor. =700 1\$aCasaroli, Andrea,$eauthor. =700 1\$aGuagliano, Mario,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130089.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130096 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130096$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD9705.5.B434 =082 04$a338.7/669142/0973$223 =100 1\$aKobasko, N.,$eauthor. =245 10$aBatch Intensive Quenching Processes for Minimizing Steel Part Distortion and Improving Part Performance Characteristics /$cN. Kobasko, M. Aronov, SH. Guseynov, J. Rimshans. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aThis paper discusses an intensive quenching method known as the IQ-2 process. The IQ-2 method is a two- or three-step quenching process for steel parts conducted in highly agitated water. The method is based on the use of a self-regulated thermal process that takes place during the quenching of steel parts in cold liquids such as water or water-salt solution. This quenching method eliminates the film boiling process and provides better control of the martensitic transformation during quenching, resulting in a significant reduction of part distortion after quenching. It also improves material mechanical properties and the performance characteristics of steel parts. It is underlined that proper software and equipment should be used when applying the IQ-2 quenching method for steel parts. Several practical examples of the application of the IQ-2 process are provided. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBearings industry. =650 \0$aEquipment. =650 \0$aHigh quality of steel parts. =650 \0$aIQ-2 technology. =650 \0$aMachine parts industry. =650 \0$aMonitoring. =650 \0$aSelf-regulated thermal process. =650 \0$aSoftware. =650 \0$aSteel alloy industry. =650 14$aIQ-2 technology. =650 24$aEquipment. =650 24$aHigh quality of steel parts. =650 24$aMonitoring. =650 24$aSelf-regulated thermal process. =650 24$aSoftware. =700 1\$aAronov, M.,$eauthor. =700 1\$aGuseynov, SH.,$eauthor. =700 1\$aRimshans, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130096.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140008 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140008$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA473 =082 04$a620.1/76$223 =100 1\$aLozano, D.,$eauthor. =245 10$aPartial Decarburization and Intensive Quenching to Increase Fatigue Limit of Quenched Small Parts /$cD. Lozano, G. Totten, G. Martinez-Cazares, R. Mercado-Solis. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aThe 5160 spring steel is mainly used to endure fatigue and since its Mf is below room temperature, retained austenite is usually present after conventional quenching, which is detrimental from a fatigue point of view. To reduce the amount of retained austenite, a partial decarburization was promoted (to increase the Ms and Mf, respectively) by austenitizing the steel at different temperatures and times in air, prior to performing an interrupted quenching in an accelerated media (brine) instead of the conventional oil quenching. The same quenching conditions with partial decarburization and without decarburization are compared. In addition, conventional oil quenching was performed as reference. Results showed that with a controlled partial decarburization, it is possible to increase the fatigue limit compared to the conditions without decarburization (both interrupted quenching and oil quenching). Fatigue experiments were carried out in a rotating bending fatigue type tester. Cooling curves, decarburization profiles, fraction of martensite plots, and fatigue data are discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$afatigue. =650 \0$aIntensive quenching. =650 \0$aInterrupted quenching. =650 \0$aspring steel. =650 \0$aSteel$x Fatigue. =650 14$aInterrupted quenching. =650 24$a5160 spring steel. =650 24$aFatigue. =650 24$aIntensive quenching. =700 1\$aMartinez-Cazares, G.,$eauthor. =700 1\$aMercado-Solis, R.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140008.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130112 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130112$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC319.8 =082 04$a621$223 =100 1\$aFrerichs, F.,$eauthor. =245 10$aDetermination of Heat Transfer Coefficients in High Speed Quenching Processes /$cF. Frerichs, S. Sander, T. Lübben, S. Schüttenberg, U. Fritsching. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b15 =520 3\$aRapid water quenching of steel specimen in heat treatment processes can evoke compressive residual stresses near the specimen surface. Thereby a significant increase in the fatigue limit of the components may be achieved. For applying this process, knowledge and control of heat transfer coefficients (HTC) in various process conditions during quenching is necessary. For HTC lower than 10 kW/m2K, temperature measurements with thermocouples below the surface of steel components may be performed. However, for measurements of HTC above 10 kW/m2K, the local cooling rates are huge near to and at the surface and the resulting temperature gradients are high. For these rapid temperature changes, the response times of sheathed thermocouples are not sufficient and because of the high temperature gradients also the positioning of the thermocouples within the specimen must be very accurate. The most appropriate possibility to determine HTC above 10 kW/m2K is temperature measurement directly at the surface using thermocouples with a small response time. Another possibility to determine HTC in high speed quenching processes is the use of probe material that provide higher thermal conductivity than steel, such as copper with about 27 times higher heat conductivity compared to austenitic steel. Higher heat conductivity of the specimen to be quenched lowers the temperature gradients within the specimen and the cooling rates. Therefore, measurements with commonly used sheathed thermocouples are feasible. Both techniques for HTC-evaluation in rapid quenching process have been tested. The resulting HTC values will be compared with HTC data from numerical heat and fluid flow calculations and from empirical equations. Results of these evaluations show that heat transfer coefficients of about 50 kW/m2K can be achieved by high speed quenching. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aConjugate heat transfer problem. =650 \0$acooling curve analysis. =650 \0$aFlow and heat transfer simulation. =650 \0$aheat transfer analysis. =650 \0$aHeat transfer coefficient evaluation. =650 \0$aHigh speed quenching. =650 \0$aNumerical HTC evaluation. =650 \0$aquenching. =650 \0$aSurface temperature measurement. =650 14$aHigh speed quenching. =650 24$aConjugate heat transfer problem. =650 24$aFlow and heat transfer simulation. =650 24$aHeat transfer coefficient evaluation. =650 24$aNumerical HTC evaluation. =650 24$aSurface temperature measurement. =700 1\$aFritsching, U.,$eauthor. =700 1\$aLübben, T.,$eauthor. =700 1\$aSander, S.,$eauthor. =700 1\$aSchüttenberg, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130112.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130067 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130067$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD251 =082 04$a547$223 =100 1\$aElmi Hosseini, S.,$eauthor. =245 10$aCooling Curve Analysis of Heat Treating Oils and Correlation With Hardness and Microstructure of a Low Carbon Steel /$cS. Elmi Hosseini, A. Zabett, Zhuguo Li. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b69 =520 3\$aOil is one of the most common quenchants used in the heat treating industry. Since the cooling properties of a quench oil varies with the degree of aging, it is important that quenching cooling rates be monitored with respect to use time. In addition, there is insufficient general information about various oil quenchants in general and cooling rates in particular. This problem is compounded by complaints from heat treating shops that quenching oils of nominally the same type, and which are alleged to contain the same additive packages, exhibit very different quenching performance in practice. Therefore, at the request of the heat treating industry in Iran, measuring system was designed and built to determine the cooling rate of quenching oils. This system includes of a tubular furnace, oil tank, probe for measuring the temperature, a system for probe transfer from the furnace to the quenchant, and a data acquisition system. This new system is capable of measuring the cooling rate of quenching oils according to various national and international standards. In the study reported here, two types of oils were comparatively evaluated: Behran 145 Oil (New Oil) and Used Behran 145 Oil. The cooling rate of these quenching oils was measured, and the effect of their cooling rate differences on the hardness and the microstructure of a low carbon steel was determined. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCarbon compounds. =650 \0$aCooling curve. =650 \0$aHardness. =650 \0$aLow Carbon Steel. =650 \0$amicrostructure. =650 \0$aProbe. =650 \0$aQuench oil. =650 \0$aSteel. =650 14$aQuench oil. =650 24$aCooling curve. =650 24$aHardness. =650 24$aMicrostructure. =650 24$aProbe. =650 24$aSteel. =700 1\$aLi, Zhuguo,$eauthor. =700 1\$aZabett, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130067.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130113 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130113$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7874 =082 04$a621.381/046$223 =100 1\$aArimoto, Kyozo,$eauthor. =245 10$aFirst Prototype of Rotary-Arm Type Test System Using a Small Ball Probe for Determination of Cooling Characteristics of Quenchants /$cKyozo Arimoto, Fumiaki Ikuta, Hideo Yokota. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b30 =520 3\$aQuenchants should be maintained based on their cooling characteristics, measured on a daily basis at every worksite for keeping their performance. A test system for this purpose is required to be compact, convenient, and reasonable. A rotary-arm type measurement apparatus using a small ball probe, which was reported by Tawara in 1941, is recognized as a compact one with an automatic device to specify a circular motion of the probe for its transfer from furnace to quenchant as well as a subsequent cooling process. In this study, the concept of Tawara's method was assessed by producing its prototype based on current heating and rotation devices, and also measurement and control systems. Trends obtained from limited results of the prototype were consistent with those of Tawara. Reasonable repeatability in measured cooling characteristics of polymer solutions was verified by systematical tests. Relative flow that occurs steadily around the probe by its circular motion is a unique point of this apparatus to enhance its accuracy and repeatability. After reviewing test methods using rotary-arm and ball probes, and standards for cooling characteristics of quenchants critically, contents, results, and outlooks on the prototype were described. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBall probe. =650 \0$aCooling characteristics. =650 \0$acooling properties. =650 \0$ahardening. =650 \0$aMicroelectronics$xCooling. =650 \0$aQuenchant. =650 \0$aRotary-arm type test. =650 14$aQuenchant. =650 24$aBall probe. =650 24$aCooling characteristics. =650 24$aRotary-arm type test. =700 1\$aIkuta, Fumiaki,$eauthor. =700 1\$aYokota, Hideo,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130113.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140014 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140014$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN271.P4 =082 04$a622/.1828$223 =100 1\$aTiwary, Vivek,$eauthor. =245 10$aCooling Performance of Select Mineral Oil and Polymer Quenchants /$cVivek Tiwary, Narayan Prabhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aIn the present investigation, quench severity was determined for industrial oil quenchants and varying concentrations of PAG polymer. Viscosity, thermal conductivity, density, flash point, and fire point were measured for all quenchants. Cooling curve parameters were determined based on cooling curve analysis ISO/DIS 9950 technique. An Inconel 600 probe was used for this purpose. Severity of quenching was determined based on the Grossmann technique. Viscosity and thermal conductivity had a significant effect on quench severity. Heat flux and HTC at the metal/quenchant interface were computed by both lumped capacitance and Inverse modeling techniques. The effect of ultrasonic and Tensi agitation on cooling curve parameters was assessed. Polymer quenchants of lower concentrations showed marginally higher heat transfer rates compared to water particularly during unagitated condition. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAgitation. =650 \0$aheat flux. =650 \0$amineral oil. =650 \0$aOil fields$x Production methods. =650 \0$aPAG. =650 \0$aQuench severity. =650 \0$aQuenchants. =650 14$aQuenchants. =650 24$aAgitation. =650 24$aHeat flux. =650 24$aMineral oil. =650 24$aPAG. =650 24$aQuench severity. =700 1\$aPrabhu, Narayan,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140014.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130093 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130093$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.1/86$223 =100 1\$aYokota, Hideo,$eauthor. =245 10$aDevelopment of a New Method for Testing Cooling Power Using a Silver Probe and a New Reference Quenching Fluid /$cHideo Yokota. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aCooling curve tests have been the most useful means of testing the cooling power of liquid quenchants such as oils and polymer quenchants. The JIS method for evaluating the cooling power of oils (JIS K 2242) was established in 1965. A cylindrical silver probe was adopted for the JIS method because of the following advantages: measurement results will not be affected by phase transformations or surface oxidation, and the probe has high sensitivity and excellent reproducibility. In the JIS method, 80°C di-2-ethylhexyl phthalate (DOP) is used as a reference quenching fluid for initial calibration and for periodic calibration checks of the probe and the overall system. However, it has been pointed out that DOP may be an environmental pollutant. Therefore, the JIS Technical Committee on heat treating fluids looked at new reference quenching fluids that could replace DOP. Through a series of round-robin tests, mineral oil having a flash point within a prescribed range and a viscosity of ISO VG22 was selected as the new reference quenching fluid. This mineral oil is specified as the reference quenching fluid in the revised standard for heat treating fluids, JIS K 2242:2012. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum alloys. =650 \0$aCooling power. =650 \0$aHeat treatment. =650 \0$aMetals$xHeat treatment. =650 \0$aMineral oil. =650 \0$aQuenchant. =650 \0$aReference fluid. =650 14$aHeat treatment. =650 24$aCooling power. =650 24$aDOP. =650 24$aMineral oil. =650 24$aQuenchant. =650 24$aReference fluid. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130093.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130103 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130103$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aMaisuradze, M.,$eauthor. =245 10$aInvestigation and Development of Spray Cooling Device for Heat Treatment of Large Steel Forgings /$cM. Maisuradze, Yu. Yudin, M. Ryzhkov. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b39 =520 3\$aMethods for determining the main service characteristics of cooling devices (irrigation density, its distribution on the cooling surface, and dependence of the heat-transfer coefficient versus temperature) are described. An investigation of technological and design parameters of spraying jets and their effect on cooling capability of large steel forgings (e.g., hot-rolling mill rolls) are presented. The technological parameters under consideration are water pressure in spraying jets and the number of spraying jets in a cooling device. The varied design parameters of spraying jets are the diameters of the channels in spraying jets, the distance between the jets, and the distance from the cooling surface. The results of the experiments were applied to obtain the dependency between technological and design parameters versus main service characteristics of spraying jets to develop and optimize the technology of heat treatment of large steel forgings. These relations were applied for modeling spray cooling of hot-rolling mill rolls. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aHeat treatment. =650 \0$aHeat-transfer coefficient. =650 \0$aHot-rolling mill rolls. =650 \0$aLarge forgings. =650 \0$aModeling. =650 \0$aSpray cooling. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 \0$aSteel. =650 14$aSteel. =650 24$aHeat treatment. =650 24$aHeat-transfer coefficient. =650 24$aHot-rolling mill rolls. =650 24$aLarge forgings. =650 24$aModeling. =650 24$aSpray cooling. =700 1\$aRyzhkov, M.,$eauthor. =700 1\$aYudin, Yu.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130103.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140002 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140002$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7874 =082 04$a621.381/046$223 =100 1\$aPrabhu, K.,$eauthor. =245 12$aA Dimensional Parameter for Prediction of Cooling Performance of Quenchants /$cK. Prabhu, G. Ramesh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aComputer aided cooling curve analysis was carried out during immersion quenching of ISO/DIS 9950 quench probe. Water, brine solutions, polymer solutions, mineral oils, and vegetable oils were used as quench media. The results showed that the quench medium used had a significant effect on the quench probe cooling curve parameters. An empirical correlation was proposed to predict the average cooling rate from surface tension, wetting angle, thermal conductivity, and kinematic viscosity of the quench medium. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$acooling properties. =650 \0$ahardening. =650 \0$aMicroelectronics$xCooling. =700 1\$aRamesh, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140002.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130104 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130104$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS320 =082 04$a672.3$223 =100 1\$aDeng, Xiao-Hu,$eauthor. =245 10$aModeling and Simulation of Carbide Precipitation During Tempering of Alloy Tool Steel /$cXiao-Hu Deng, Dong-Ying Ju. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b14 =520 3\$aIn order to study the carbide transformation during tempering, a modified model has been proposed to simulate the phase composition and mechanical properties during the tempering process in tool steels. The model considers the simultaneous precipitation reactions of several carbides. The precipitation sequence and volume fraction of a carbide can be simulated quantitatively. In order to validate the model, we employed it to simulate the tempering process of SKD11 steel. The predicted volume fraction of retained austenite showed good agreement with measurement results. Furthermore, the calculated carbide results agreed well with the theoretical conclusions. The agreement indicates that the model is effective for simulation of the tempering process in tool steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aalloy carbide. =650 \0$ahardness. =650 \0$aPrecipitation. =650 \0$aTempering. =650 \0$atool steel. =650 14$aTempering. =650 24$aAlloy carbide. =650 24$aHardness. =650 24$aPrecipitation. =650 24$aTool steel. =700 1\$aJu, Dong-Ying,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130104.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130102 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130102$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ853.4.M53 =082 04$a620.1/064$223 =100 1\$aLišcic, Božidar,$eauthor. =245 10$aCurrent Investigations at Quenching Research Centre /$cBožidar Lišcic, Tomislav Filetin, Darko Landek, Josip Župan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aQuenching Research Centre (QRC) was established at the beginning of 2010 through the financial support for excellence of the Ministry of Science Education and Sport, of the Republic of Croatia. The main investigation and research possibilities and potentials of the QRC are: quenching in liquids or in a salt bath and cooling by high pressure gases. As a result of long term research, the Temperature Gradient System has been designed, together with a unique cylindrical probe of 50 mm diameter by 200 mm instrumented with three thermocouples. Another device used at the Centre was the IVFSmartQuench® system according to ISO 9950, using a quenching device with agitation according to the ASTM D6482 standard. That equipment is used to investigate liquid quenchants and process parameters, including development of new quenchants: water, oil, and polymer based nanofluids, agitated by ultrasonic vibrations as a novel technology. QRC is also equipped with unique high pressure gas quenching facilities, providing the hardware for controllable heat extraction. The aim of using that equipment is to develop the method for measuring hardenability of high-alloyed steels when they are gas quenched and where a Jominy test is not applicable. QRC is also one of the initiators and an active participant in the project Global database on cooling intensities of liquid quenchants, which is coordinated and conducted by International Federation for Heat Treatment and Surface Engineering (IFHTSE) =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFluidic devices. =650 \0$agas quenched steels. =650 \0$aHardenability of gas quenched steels. =650 \0$aNanofluids. =650 \0$aQuenching. =650 \0$aTemperature gradient system. =650 14$aQuenching. =650 24$aHardenability of gas quenched steels. =650 24$aNanofluids. =650 24$aTemperature gradient system. =700 1\$aŽupan, Josip,$eauthor. =700 1\$aFiletin, Tomislav,$eauthor. =700 1\$aLandek, Darko,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130102.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140003 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140003$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7874 =082 04$a621.381/046$223 =100 1\$aPrasanna Kumar, T.,$eauthor. =245 10$a“Reference QuenchProbe”-An Alternative Probe Design for In-Situ Estimation of Cooling Rates, Heat Flux, and Hardenability During Immersion Quenching of Hardenable Steels /$cT. Prasanna Kumar, B. Hernandez-Morales, G. Totten. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b45 =520 3\$aThis article reviews some of the limitations of the standard cooling curve analysis and the Jominy hardenability test in extending the results to actual quenching in industrial setups and reports the development of a new portable tool-Reference QuenchProbe-for estimating cooling rates, hardness, and microstructure distributions in hardenable steel grades during immersion quenching, which can be used by the heat treater in the plant. The specimen is made of the same grade of steel as the quenched component with section thickness matching that of the component, which is a departure from standard laboratory tests. The test is carried out in the plant under actual conditions dispensing the need to correlate the standard cooling curve data and end quench hardenability tests done in the laboratory to industrial practice. To test the suite of mathematical models associated with the Reference QuenchProbe hardware and software, specimens of different grades of steels were instrumented with a single thermocouple near the surface of the specimen. Using the cooling data at the point of measurement, the cooling rates, microstructure, and hardness at other critical locations were computed. An enthalpy-based non-linear inverse heat conduction model was coupled with austenite decomposition models for handling the latent heat liberated during quenching. Several steels ranging from low carbon to medium alloy steels were both end-quenched by water and immersion quenched in several industrial quenchants. The computed hardness of end quenched and immersion quenched specimens were shown to be in good agreement with the measured values. The Reference QuenchProbe is thus shown to generate data needed for heat treatment process design including quenchant selection, which can be directly used in practice. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$acooling properties. =650 \0$ahardening. =650 \0$aMicroelectronics$xCooling. =700 1\$aHernandez-Morales, B.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140003.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140021 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140021$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA478 =082 04$a620.17$223 =100 1\$aMartínez-Cázares, G.,$eauthor. =245 10$aHigh-Speed Quenching of High Carbon Steel /$cG. Martínez-Cázares, D. Lozano, M. Guerrero-Mata, R. Colás, G. Totten. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b9 =520 3\$aMedium and high carbon steels are usually quenched in polymer and oil in order to avoid cracking and distortion; however, recent studies have proved that it is possible to minimize cracking using water as a coolant of these steels by promoting extremely high cooling rates. By great agitation and velocity of quenchant, the vapor blanket is reduced or prevented during water quench, allowing uniform hardening of the surface. In this study, the cooling severity of a spray quenching system and a high-speed quenching chamber are studied. Cylindrical samples of AISI 304 stainless steel (20 mm in diameter and 100 mm length) were employed to characterize the cooling severity. Thermal data was acquired through K-type thermocouples placed in the sample at three positions, 1 mm below surface, mid-radius and at center of the specimen, connected to a data acquisition system. High thermal gradients were observed in both systems, being the high-speed chamber the severest cooling. The maximum cooling rate obtained at the surface was 470 and 300°C/s for the high-speed chamber and the spray system, respectively. In addition, 5160 spring steel samples were quenched for short times in both systems; the cooling was interrupted to avoid through transformation and to produce a case-core type microstructure. Different cooling times were used for the interrupted quenching to modify the martensite case thickness. No cracks were observed. Thermal results and microstructures are discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCarbon Steel. =650 \0$aHigh-speed quenching. =650 \0$aquenching. =650 \0$aspray quenching. =650 14$aQuenching. =650 24$aHigh-speed quenching. =650 24$aSpray quenching. =700 1\$aColás, R.,$eauthor. =700 1\$aGuerrero-Mata, M.,$eauthor. =700 1\$aLozano, D.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140021.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130101 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130101$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a620.17$223 =100 1\$aPolishetty, Ashwin,$eauthor. =245 12$aA Comparative Assessment of the Hardness of Nano-Structured Bainitic Steel Affected by Using Various Quenchants /$cAshwin Polishetty, Chinmay Sonavane, Guy Littlefair. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b9 =520 3\$aQuenching, in heat treatment, plays a vital role in controlling material properties. It is the most important step in manipulating the strength of steel. It involves cooling the material from the austenitizing temperature at different cooling rates using variations in quenchants to obtain corresponding material properties. The commonly used quenchants are water, oil, and brine. The cooling rate is the rate at which heat is ejected from the material by the quenchant. The effectiveness of the quenchant is judged by its ability to absorb heat from the material and thermally conduct. Because of stringent regulations regarding use and disposal, there is a need to develop new, environmentally friendly quenchants. The experimental design in this study consisted of quenching austenitized nano-structured bainitic steel in four different quenchants, namely, water, oil, brine, and 1 m sodium carbonate solution. This research gives the insight of substituting conventional quenchants with 1 m sodium carbonate solution. The final four samples were characterized using metallography. A comparative study of the hardness of nano-structured bainitic steel quenched in the newly developed quenchant (i.e., 1 m sodium carbonate solution) and of steel quenched with the conventional one is done. All the results are tabulated, and the applicability of the quenchants is discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBainite. =650 \0$abainitic steel. =650 \0$aHardness. =650 \0$aNano-structured bainitic steel. =650 \0$aQuenchant. =650 14$aNano-structured bainitic steel. =650 24$aHardness. =650 24$aQuenchant. =700 1\$aLittlefair, Guy,$eauthor. =700 1\$aSonavane, Chinmay,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130101.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130109 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130109$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC319.8 =082 04$a621$223 =100 1\$aLandek, Darko,$eauthor. =245 12$aA Prediction of Quenching Parameters Using Inverse Analysis /$cDarko Landek, Josip Župan, Tomislav Filetin. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aThe cooling curves of still water and of water-based polymer quenchant polyalkylene glycol (PAG) were recorded with the ISO Inconel 600 probe with 12.5 diameter and 60 mm length equipped with a type K thermocouple inserted into the probe's geometric center. The research included recording of cooling curves for still water in temperature range from 20 to 60°C, as well as quenching experiments with water based polymer solutions with concentration from 10 to 30 Volume % of PAG. The possibility of a new cooling curve determination method for any given water temperature based on interpolation model and experimental data for cooling curves at three different water temperatures was tested. Surface temperature, heat flux density, and heat transfer coefficient (HTC) were estimated based on the recorded cooling curve at the center of the ISO Inconel 600 probe using the solutions of inverse heat conduction problem (IHCP). The results of the inverse heat transfer analysis of the ISO Inconel 600 probe cooling in water and water based polymer solutions were compared to the results of the commercial software ivf SQintegra ver4.0 for the same cooling experiments. The proposed inverse determination of HTC can be used for the specification of boundary conditions in numerical simulations of quenching axisymmetric work pieces with similar dimensions to the ISO Inconel 600 probe. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$acooling curve analysis. =650 \0$aheat transfer analysis. =650 \0$aInverse heat transfer analysis. =650 \0$aquenching. =650 14$aQuenching. =650 24$aCooling curve analysis. =650 24$aInverse heat transfer analysis. =650 24$aISO 9950. =650 24$aWater-based polymer quenchant PAG. =700 1\$aŽupan, Josip,$eauthor. =700 1\$aFiletin, Tomislav,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130109.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130107 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130107$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.C3 =082 04$a620.1/93$223 =100 1\$aGao, Weimin,$eauthor. =245 10$aMolecular Dynamics Simulation of Heat Transfer during Quenching in CNT Nanofluids /$cWeimin Gao, Lingxue Kong, Peter Hodgson. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b63 =520 3\$aNanofluids exhibit superior thermal properties to conventional fluid and particle-fluid suspensions and show a great potential as quenching media for quench hardening of steel components. The heat transfer mechanism in nanofluid is very complex and unclear. In this paper, molecular dynamics (MD) simulation method is used to theoretically study the heat transfer from a metal surface at different temperatures to a water-based nanofluid with functionalized carbon nanotubes (FCNTs). To model the quenching process, an initial temperature jump between the nanofluid and an iron slab is employed, and non-equilibrium molecular dynamics (NEMD) simulations are performed. The MD results reveal the heat transfer process in the initial stage of quenching and at the first moment of contact of a liquid nanofluid with a hot metal surface. The thermodynamics and transport properties of the nanofluid and the heat transfer characteristics are discussed with the atomistic details of the interactions of the FCNT with the iron atoms and the water molecules. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$acarbon nanotube. =650 \0$aheat transfer. =650 \0$aMolecular dynamics. =650 \0$ananofluid. =650 \0$aQuenching. =650 14$aHeat transfer. =650 24$aCarbon nanotube. =650 24$aMolecular dynamics. =650 24$aNanofluid. =650 24$aQuenching. =700 1\$aHodgson, Peter,$eauthor. =700 1\$aKong, Lingxue,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130107.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130086 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130086$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN672 =082 04$a671.36$223 =100 1\$aLuo, Xinmin,$eauthor. =245 10$aDistortion Control :$bQuenching Apparatus for Hardening Parts: An Overview /$cXinmin Luo, George Totten. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (28 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b41 =520 3\$aDuring the production and quality control of heat treatment, especially during drastic cooling operations, avoiding heat-related distortions is critical if relatively stringent geometrical requirements stipulated by industrial manufacturing specifications are to be achieved. Therefore, specialized distortion minimization procedures are often used, which includes: the use of clamps and spreaders for fixturing workpieces in a designated position, and/or to controlling the flow direction and flux of coolants as they impinge on to the cooling workpiece surface. In addition, some assistive devices are required to implement designed movement of workpieces during the quenching process in order to meet the technical requirements of workpieces undergoing heat treatment. Quenching apparatuses are also used to fix workpieces to avoid any possible damage due to unexpected mutual contact or collision between them, and more importantly to ensure uniform heating and reasonable quenching of workpieces. On many occasions, some specially designed accessories are also considered as quenching apparatus to form a complete set with available heating or cooling equipment. Therefore, the quenching apparatuses are discussed in this paper for their role and function both in heat treatment production and especially for controlling quenching distortion. The main principles of the apparatus design are briefly described, and some apparatuses for typical heat treatment purposes are introduced, such as core rods, quenching machines, fixtures for press quenching, copying mould for quenching of aluminum alloy structural components, and apparatuses for induction hardening, and the use of quenchant flow tunnels. The management and the development trends of quenching apparatus are also briefly discussed. Characterization by digital technology, CFD, and computer control quenching apparatus has already become an important part of modern heat treatment production, and the synchronous increases of both production cost and heat treatment quality has been achieved. The popularization of the use quenching apparatuses implies that the fundamental solution to heat treatment distortion, which is based on effective movement constraints of workpiece upon quenching, suggests the programming cooling of workpiece and the reasonable design of quenchant flow tunnel for hardening is approaching. In the meantime, quenching apparatus design is becoming less empirical by increasing the use of established quenching theory and technology. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aComponent. =650 \0$acooling technology. =650 \0$aDistortion. =650 \0$aHardening. =650 \0$aMetals$xQuenching. =650 \0$aquenching apparatus. =650 14$aHardening. =650 24$aComponent. =650 24$aCooling technology. =650 24$aDistortion. =650 24$aQuenching apparatus. =700 1\$aTotten, George,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130086.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130106 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130106$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ853.4.M53 =082 04$a620.1/064$223 =100 1\$aDolinsky, A.,$eauthor. =245 10$aCooling Characteristics of Meso- and Nanofluids Prepared by the DPIE Method /$cA. Dolinsky, L. Grabov, A. Moskalenko, T. Grabova, P. Logvinenko. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b39 =520 3\$aThe authors have evaluated eco-friendly base fluids for hardening steel such as canola oil and soybean oil to identify alternative renewable quenchants using basestocks available in Ukraine. Meso- and nanofluids were prepared by the discrete-pulse input of energy (DPIE) method. It has been established that the cooling intensity of these quenchants depends not only on the composition of the base fluid and the meso- or nanoparticles but also on the methods of preparation. The influence of the DPIE method on cooling characteristics of vegetable oils was studied. High-temperature cooling properties within the temperature range of 200°C-850°C exceed the observed properties of traditional mineral oil-based quenchants. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCooling intensity. =650 \0$aFilm boiling. =650 \0$aFluidic devices. =650 \0$agas quenched steels. =650 \0$aHeat-transfer coefficient. =650 \0$aVegetable oils. =650 14$aDPIE method. =650 24$aCooling intensity. =650 24$aFilm boiling. =650 24$aHeat-transfer coefficient. =650 24$aVegetable oils. =700 1\$aGrabov, L.,$eauthor. =700 1\$aGrabova, T.,$eauthor. =700 1\$aLogvinenko, P.,$eauthor. =700 1\$aMoskalenko, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130106.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130114 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130114$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.58 =082 04$a620.1/121$223 =100 1\$aShekriladze, Irakli,$eauthor. =245 10$aNucleate Boiling Heat Transfer :$bTemperature Pulsations or Local Thermal Shocks /$cIrakli Shekriladze. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b37 =520 3\$aThis paper discusses thermo-mechanical consequences of the pumping effect of growing bubble (PEGB) resulting in surface thermal stresses during nucleate boiling. Unfortunately, the unavailability of boiling heat transfer studies specifically addressing the scope and duration of the PEGB effect, including lack of models and universal correlations of boiling heat transfer, has hindered the overall understanding of nucleate boiling heat transfer to date. As a result, specific types of cyclic thermal stresses at the surface which are capable of producing thermal shocks in some boiling regimes and that are attributable to PECB have remained unexplored. This has prevented complete theoretical determination of the service life of heating surfaces of boiling systems such as boiling water reactors (BWR) and metal quenching technology. In this paper, some preliminary estimates of the tasks required for experimental studies required for further theoretical development are presented. With regard to the quenching processes, discussions regarding the probable negligible consequences of thermal stresses caused by the PEGB are presented. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aNucleate boiling. =650 \0$aPumping effect. =650 \0$aquenching. =650 \0$aTemperature pulsations. =650 \0$athermal shock. =650 \0$athermal stresses. =650 14$aNucleate boiling. =650 24$aPumping effect. =650 24$aQuenching. =650 24$aTemperature pulsations. =650 24$aThermal shock. =650 24$aThermal stresses. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130114.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130105 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130105$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7874 =082 04$a621.381/046$223 =100 1\$aMatijevic, Božidar,$eauthor. =245 10$aInfluence of Additive Chemistry on the Physical, Chemical, and Cooling Properties of Quenching Oils /$cBožidar Matijevic, Ljiljana Pedišic. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b19 =520 3\$aQuenching, the most common method of hardening metals, involves continuous cooling from a given austenitization temperature to achieve full transformation into martensite. Thus, optimal mechanical properties are obtained. The quenching media contains a base oil and different types of additives depending on application requirements. The cooling rate mainly depends on the thermal characteristics of metals, section thickness of workpieces, and heat-removal properties of the quenching medium. For the base oil, it is possible to use petroleum oils, synthetic oils, and natural oils separately or in combination. Petroleum base oils are widely used because of their thermal-oxidative stability advantages in comparison to natural oils, or lower prices in comparison to synthetic oils. There are numerous compounds available for potential use based on their functional properties. Environmental and safety requirements also exhibit a strong influence on additive selection. For this reason, the current use ofbarium-containing additives must be replaced with less harmful compounds. Petroleum basestocks should be replaced by renewable basestocks that are biodegradable, as is the current general trend in lubricant development. By changing the composition of quenching oils, base oils, and/or additives, the heat transfer characteristics are also changed. In this study, quenching oils with different types of additives are tested and the results regarding their physical and chemical properties as well as cooling characteristics are presented. Cooling curves of the tested oils have been evaluated according to ISO 9950:1995. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAdditives. =650 \0$aCooling properties. =650 \0$aHardening. =650 \0$aHeat sinks (Electronics) =650 \0$aHeat treatment. =650 \0$aMicroelectronic packaging$xMaterials$xThermal properties. =650 \0$aMicroelectronics$xCooling. =650 \0$aQuenchants. =650 \0$aQuenching oils. =650 14$aHeat treatment. =650 24$aAdditives. =650 24$aCooling properties. =650 24$aHardening. =650 24$aQuenchants. =650 24$aQuenching oils. =700 1\$aPedišic, Ljiljana,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130105.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130110 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130110$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.Q4 =082 04$a672.36$223 =100 1\$aGospodinov, Danail,$eauthor. =245 10$aInfluence of External Factors on the Cooling Ability of Vacuum Quenching Oils /$cDanail Gospodinov, Maria Nikolova, Plamen Danev. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b8 =520 3\$aThis paper presents research on vacuum quenching oils at different pressure conditions during the cooling stage of the heat treatment process. The aim of this work is to reveal the influence of the pressure, agitation (laminar or turbulent flow), and oil temperature on the cooling oil. Medium and low viscosity oils are investigated. The research is novel because it expands knowledge of quenching oil behavior at low and high pressure conditions (from 1 mbar to 2.5.103 mbars). The findings are presented as integral diagrams (time-temperature and cooling rate versus temperature curves) and tables of the local cooling ability valuations. It is found that the pressure in the chamber is the main factor that influences the cooling ability of the examined media. The trend of pressure influence can be generalised as: the greater the cooling oil ability, the stronger the pressure value influence. In addition to the above, the possibility of routine change of the pressure makes it a prospective factor to control the cooling oil ability. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$acooling ability. =650 \0$acooling curve. =650 \0$aquenching. =650 \0$aVacuum heat treatment. =650 \0$aVacuum quenching oils. =650 14$aVacuum heat treatment. =650 24$aCooling ability. =650 24$aCooling curve. =650 24$aQuenching. =650 24$aVacuum quenching oils. =700 1\$aDanev, Plamen,$eauthor. =700 1\$aNikolova, Maria,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130110.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140005 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1404-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140005$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN757.C5 =082 04$a672.36$223 =100 1\$aLandek, Darko,$eauthor. =245 10$aModeling of Dimensional Changes and Residual Stresses After Transformation-Free Cooling /$cDarko Landek, Dragutin Lisjak, Thomas Lübben, Josip Župan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aPredicting thermal distortions and residual stresses after steel heat treatment is a complex task in which the solution involves the use of a number of process parameters and nonlinear variation of steel properties. Former investigations in transformation-free cooling processes of long cylindrical work pieces in a gas nozzle field showed a typical behavior of the dimensional changes which indicated the possibility of introducing dimensionless numbers to predict thermal distortions. It was found that the changes in the dimensions of cylinders correlate well with only a few dimensionless numbers which are defined as function of shape and dimensions of components, its initial temperature, temperature of the quenching media, heat transfer coefficient, heat conductivity, heat capacity, density, thermal expansion coefficient, Young's modulus, Poisson's ratio, yield strength, and strain hardening behavior. For a systematic investigation of impacts on dimensional changes and residual stresses after transformation-free cooling, a representative group of 28 austenitic stainless steels was selected from literature. Their properties were statistically analyzed and three representative combinations of steel properties have been selected. The numerical simulations were carried out by use of the commercial finite element (FE) program SYSWELD 2005 with the aim to predict residual stresses and change of dimensions of a long cylinder made of austenitic stainless steel after gas cooling from the high temperature down to room temperature. The FE results were analyzed with the nonlinear regression methods and with genetic programming methods. From these analyses, two dimensionless mathematical models were proposed, one for prediction of thermal distortions and the other for prediction of equivalent residual stresses. The proposed dimensionless regression models allow the portability of the calculation results to similar cooling conditions (temperature independent heat transfer) for a transformation-free cooling of long cylinders made from any austenitic steel selected from the considered representative group of steels. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAustenitic stainless steel. =650 \0$aaustenitic steel. =650 \0$aDimensionless numbers. =650 \0$aResidual stresses. =650 \0$athermal strains. =650 \0$aTransformation-free cooling. =650 14$aTransformation-free cooling. =650 24$aAustenitic steel. =650 24$aDimensionless numbers. =650 24$aResidual stresses. =650 24$aThermal strains. =700 1\$aŽupan, Josip,$eauthor. =700 1\$aLübben, Thomas,$eauthor. =700 1\$aLisjak, Dragutin,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 4 Special Issue on Advances in Methods, Quenchants, and Equipment for Hardening Steel.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140005.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160056 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1602-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160056$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQE33.2.R4 =082 04$a621.3678$223 =100 1\$aGiles, H.,$eauthor. =245 10$aCrude Oil Analysis :$bHistory and Development of Test Methods From 1854 to 2016 /$cH. Giles. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (169 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b455 =520 3\$aIn 1854, Benjamin Silliman, Jr. completed his classic report on the analysis of a sample of “rock oil from Venago Co., PA.” By today's standards, his methods were primitive, but they marked the beginning of modern petroleum analysis. Over the next century and a half, hundreds of papers have been published on developments in analytical methodology and advances in instrumental technology. These have contributed to significant improvements in test methods enabling determination of crude oil properties more easily, in less time, and with greater accuracy. This article traces development of many of the test methods routinely used today for analyzing crude oils. Few of these were initially developed for crude oils, but were originally for analysis of products such as illuminating and lubricating oils. Over time, they were adapted to crude oils. The test methods described encompass those used for fundamental properties such as API gravity and total sulfur, and extend to complex operations such as fractional distillation. The article provides numerous references related to the development of each test method. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAnalysis. =650 \0$aAnalytical advances. =650 \0$aCrude oil. =650 \0$aGeophysics. =650 \0$aHistory. =650 \0$aPetroleum$xGeology. =650 \0$aRemote sensing. =650 \0$aTest methods. =650 14$aCrude oil. =650 24$aAnalysis. =650 24$aAnalytical advances. =650 24$aHistory. =650 24$aTest methods. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 2 Special Issue on Crude Oil Analysis: History and Development of Test Methods From 1854 to 2016.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160056.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150025 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150025$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150025$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP245.N8 =082 04$a546/.683$223 =100 1\$aSchöppl, Oskar,$eauthor. =245 10$aTesting Methods on Ceramic Rolling Elements for Hybrid Bearings /$cOskar Schöppl, Tanja Lube. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b35 =520 3\$aDifferent manufacturing routes for ceramic balls and rollers used in hybrid bearings can lead to different microstructures and mechanical properties of a silicon nitride grade, even being delivered by one supplier. This fact, experienced by the authors, makes it necessary to do testing on the different balls or rollers themselves. This will make sure that the minimum properties on strength, fracture toughness, and microstructure requirements according to ASTM F2094/F2094M-14 and ISO 26602 are fulfilled on the bearing component and not only on special bar samples prepared for bending tests. A first approach done in the bearing industry was a simple crush test of two or three balls on top of each other. This gave a very rough estimate of a “static load rating.” The material resistance to cracks and Hertzian contact damage was tested by indentations with tungsten carbide spheres or doing impact strength testing. A first approach for “real” strength measurement of ceramic spheres was introduced by using a diametrally compressed “C-Sphere” specimen. This was further developed to be more easily machinable and was simply called “Notched ball test.” A similar test was also developed in recent times for ceramic cylindrical roller rollers, called the “Notched roller test.” The goal of this paper was to discuss and summarize test methods for strength and combinations of strength with other properties or effects like toughness and/or residual stresses for ceramic rolling elements that have been established so far for hybrid bearings. This supported the understanding for the need to establish the notched ball test, which was already established as a National Standard ÖNORM M6341:2013 in Austria, and also in ISO and ASTM. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCeramic rolling elements. =650 \0$aFracture toughness. =650 \0$aMechanical characterization. =650 \0$aSilicon nitride. =650 \0$aStrength testing. =650 14$aMechanical characterization. =650 24$aCeramic rolling elements. =650 24$aFracture toughness. =650 24$aSilicon nitride. =650 24$aStrength testing. =700 1\$aLube, Tanja,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150025.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150028 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150028$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150028$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS1892 =082 04$a547.8426$223 =100 1\$aHoward, Samuel,$eauthor. =245 10$aSuperelastic Ball Bearings :$bMaterials and Design to Avoid Mounting and Dismounting Brinell Damage in an Inaccessible Press-Fit Application. Part II: Detailed Analysis /$cSamuel Howard, Christopher DellaCorte, Kelly Carney. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b8 =520 3\$aRolling element bearings utilized in precision rotating machines require proper alignment, preload, and interference fits to ensure overall optimum performance. Hence, careful attention must be given to bearing installation and machine assembly procedures to ensure the above conditions are met. Usually, machines are designed such that bearings can be pressed into housings or onto shafts through the races without loading the rolling elements. However, in some instances, either because of limited size or access, a bearing must be installed or removed in such a way that the load path travels through the rolling elements. This can cause high-contact stresses between the rolling elements and the races and introduces the potential for Brinell denting of the races. In this paper, an in-depth treatment is given to the design of a dent-resistant bearing utilizing a superelastic alloy, 60NiTi, for the races. A companion paper by the authors (Part I [1]) discusses material selection and the general design philosophy for the bearing. Here, a common bearing analysis tool based on rigid body dynamics is used to design the bearing in combination with finite-element simulations to further understand the limitations of the design. The primary design constraints are prevention of denting and avoiding the balls riding over the edge of the race groove during a blind disassembly process where the load passes through the rolling elements. Through an iterative process, the resulting bearing geometry is tailored to improve axial static load capability compared to a deep-groove ball bearing of the same size. The results suggest that careful selection of materials and bearing geometry can enable blind disassembly without damage to the raceways, which is necessary in the current application (a compressor in the International Space Station distillation assembly), and results in design flexibility for other applications, especially small machines with miniature bearings. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBearings. =650 \0$aElasticity. =650 \0$aMaterials. =650 \0$aMechanical components. =650 \0$aRubber. =650 \0$aShock load resistance. =650 \0$aSuperelastic materials. =650 \0$aTribology. =650 14$aMaterials. =650 24$aBearings. =650 24$aMechanical components. =650 24$aShock load resistance. =650 24$aSuperelastic materials. =650 24$aTribology. =700 1\$aCarney, Kelly,$eauthor. =700 1\$aDellaCorte, Christopher,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150028.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150024 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150024$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150024$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP339 =082 04$a621.31/2429$223 =100 1\$aHaynes, Comas,$eauthor. =245 10$aCyber-Physical Simulation for Virtual Characterization of SOFC Thermomechanical Response Within Hybrid Fuel-Cell/Gas Turbines /$cComas Haynes, Dimitri Hughes, David Tucker. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (27 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aSolid-oxide fuel-cell (SOFC)/gas-turbine hybrid systems possess the capacity for unprecedented performances, such as electric efficiencies nearly twice that of conventional heat engines at variable scale power ratings inclusive of distributed generation; however, reliably integrating such technologies is critical. Dynamic operability challenges ranging from surge-stall events in the turbomachinery to threatening thermally induced stresses within the fuel cells are formidable. An effective means of characterizing the operability of such systems requires a simulation approach of high fidelity yet reduced sacrificial risk associated with empirical investigation of SOFC stacks. Accordingly, a unique cyber-physical simulation (CPS) was developed inclusive of a spatio-temporal SOFC computational model interfaced with a retrofitted turbine. The model had an extensively broad operating range, as compared to other models that have been developed, with the capability to characterize inert heating, electrochemical start-up, and on and off design operation. A comprehensive parametric characterization was done for initial electrochemical light-off with variability in compressor by-pass valve position and initial fuel-cell load for both closed loop and open loop (OL) turbine speed system configurations. The impact of cold-air (CA) by-pass, as well as initial fuel-cell load on system parameters that directly affect SOFC operation, such as inlet air temperature, pressure, and flow, along with turbine speed and thermal effluent dynamics are presented and discussed. Additionally, the full spatio-temporal capability was exhibited and utilized in examining the impact of electrochemical start-up upon SOFC temperature and temperature gradients as a result of local current density and by-product heat distribution. Ultimately, a comprehensive parametric study, characterizing SOFC and hybrid system response to electrochemical start-up along the decision variable values of initial fuel-cell load, as well as CA by-pass valve position, was completed; this illustrated an advanced simulation platform for gathering such insights about developmental fuel-cell systems. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBiomass energy. =650 \0$aBiomasse$xConversion. =650 14$aSolid-oxide fuel-cell (SOFC)/gas-turbine hybrid cyber-physical simulation. =700 1\$aHughes, Dimitri,$eauthor. =700 1\$aTucker, David,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150024.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150032 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150032$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150032$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP339 =082 04$a662/.88$223 =100 1\$aYang, Zhiyuan,$eauthor. =245 10$aImpact of Synthetic Hydrocarbon in Biofuels on Two Polysulfide Aircraft Fuel-Tank Sealants /$cZhiyuan Yang, Hua Liu, Liwei Ye, Kai Chen. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aThe impacts of synthetic hydrocarbon in biofuels on two fuel-tank polysulfide sealants were systematically studied in this research. Synthetic hydrocarbon was derived from waste oils and fats and produced by hydroprocessed esters and fatty acids process (HEFA). The experimental results revealed that the volume of two polysulfide sealants shrunk after being immersed in the pure biofuels for 28 days at 93°C. Furthermore, mechanical properties, such as elongation rate and hardness, failed to satisfy the requirement of the specification. The experimental results also showed that the volume swell of two polysulfide sealants varied from jet reference fuel (JRF) more than 5 % after being immersed in the blended fuels when neat biofuel component was mixed with No. 3 jet fuel in a volume ratio of 50/50. The mechanical properties of elongation and hardness still cannot meet the requirements of the specification. The results demonstrated that synthetic hydrocarbons in biofuels would have a significant impact on the polysulfide sealants of the aircraft fuel tank. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBiofuel. =650 \0$aBiomass energy. =650 \0$aBiorefinery. =650 \0$aPolysulfide sealants. =650 \0$aSynthetic hydrocarbon. =650 14$aSynthetic hydrocarbon. =650 24$aBiofuel. =650 24$aPolysulfide sealants. =700 1\$aChen, Kai,$eauthor. =700 1\$aLiu, Hua,$eauthor. =700 1\$aYe, Liwei,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150032.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150019 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150019$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150019$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357.5.C38 =082 04$a620.1064$223 =100 1\$aMeged, Y.,$eauthor. =245 10$aElectrical Analogy for Cavitation Erosion Test Results /$cY. Meged. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aElectrical systems are analogous to many systems such as acoustic, fluidic, hydraulic, mechanic, magnetic, optic, pneumatic, and thermal systems. As such, electrical systems are applied to study the response of the latter systems to various inputs. A similar analogy is valid between electrical circuits and cavitation erosion systems. The adequate circuit for this purpose is the RC circuit, comprising of a power source, a resistor, and a capacitor. In the cumulative erosion-time curves, obtained by all reviewed cavitation erosion test methods, the erosion rate varies with time. In long-term tests, this rate approaches a constant value asymptotically. This curve was very similar to that obtained during charging and discharging of a capacitor in a RC circuit and was the basis for the analogy between these phenomena. The electrical analogy for cavitation erosion enabled: (a) definition of the cavitation erosion process by a first-order differential equation with three parameters; (b) long-term prediction of erosion values based on short-term tests; (c) comparison of materials and cavitation erosion test methods; and (d) simplification of cavitation erosion standards. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCavitation erosion testing. =650 \0$aCavitation. =650 \0$aElectrical analogy. =650 \0$aErosion. =650 \0$aFirst order systems. =650 \0$aRC circuit. =650 \0$aTransient response. =650 \0$avibratory cavitation erosion. =650 14$aCavitation erosion testing. =650 24$aElectrical analogy. =650 24$aFirst order systems. =650 24$aRC circuit. =650 24$aTransient response. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150019.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140062 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140062$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140062$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK1056 =082 04$a621.47$223 =100 1\$aAbdollahzadeh Jamalabadi, M.,$eauthor. =245 10$aNumerical Investigation of Thermal Radiation Effects on Electrochemical Impedance Spectroscopy of a Solid Oxide Fuel Cell AnodesThis paper is a contribution to the Materials Performance and Characterization Special Issue on Current Status and Future Advances in Fuel Cell Technology,' Guest Editors :$bYan Zhou, George E. Totten, Hong Liang, and Ke Wang. /$cM. Abdollahzadeh Jamalabadi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (29 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b29 =520 3\$aThe electrochemical impedance spectroscopy (EIS) method is an authoritative, prompt, and precise non-destructive practice. EIS is often used to understand the interfacial manners in electrochemical systems and for performance optimization, failure mode diagnosis, revealing dynamic properties, and for obtaining information on individual losses in solid oxide fuel cells (SOFCs) with measuring the current response of a fuel cell to a small sinusoidal perturbation in voltage. The difference in frequency response makes it possible to distinguish procedures and mechanisms in the electrochemical phenomenon that are happening at electrode shells. The purpose of the current study was to present modeling and simulation of the transient impedance of SOFC anodes caused by gas-phase transport processes with thermal radiation effects when a periodic variation of over potential is imposed. This model fully coupled electrochemical kinetics with gas phase diffusion. The electrochemistry at the anode was modeled using the Butler-Volmer equation, and the gas diffusion model was based on the species equations of Maxwell-Stefan. SOFCs are energy conversion devices that produce electricity and heat directly from fuel by electrochemical reaction. For evaluating the performance of SOFCs, efforts were devoted to developing numerical analysis tools capable of investigating the transport and electrochemical phenomena within the passageways of fuel cells. A simulation study was also carried out by changing parameters, such as temperature and the cell dimensions, and the results were discussed. The diameter of the impedance semicircle in Nyquist plot changes with flow field properties; hence the gas phase transport curb acting as a significant character in SOFC performance. This impedance feature is related to concentration polarization. The results were in qualitatively good agreement with experimental data. Finally, results showed that the considered thermal radiation effects increase the gas diffusion capacitance and decrease the pressure, density, H2 concentrations, and cell current. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aElectrochemical impedance spectroscopy. =650 \0$aImpedance analysis. =650 \0$aSolar thermal energy. =650 \0$asolid oxide fuel cell. =650 \0$athermal radiation. =650 \0$aTransient simulation. =650 14$aThermal radiation. =650 24$aElectrochemical impedance spectroscopy. =650 24$aImpedance analysis. =650 24$aSolid oxide fuel cell. =650 24$aTransient simulation. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140062.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150018 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150018$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150018$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQE604 =082 04$a624.1/5132$223 =100 1\$aAbu-Hakmeh, Khaldoon,$eauthor. =245 10$aEffect of Uniaxial Deformation on Structure and Transport in Hydrated Nafion 117 :$bMolecular Dynamics Simulation Study /$cKhaldoon Abu-Hakmeh, Parveen Sood, Byeong Jae Chun, Ji Il Choi, Seung Soon Jang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b45 =520 3\$aThe deformation of hydrated Nafion 117 was implemented using full-atomistic molecular dynamics simulation method to elucidate how the mechanical deformation affects the structure and transport of hydrated Nafion membrane. First, Nafion 117 membrane was equilibrated with 20 wt. % water content through an annealing procedure. The simulated characteristic correlation length and the diffusion coefficient of water and hydronium ions were analyzed for comparison with those observed in experiments. Then, the equilibrated Nafion membrane was deformed uniaxially up to 300 % of strain with a constant strain rate. The change in nanophase-segregation of hydrated Nafion during the deformation process was characterized using a directional structure factor as well as the pair correlation function in order to achieve fundamental understanding of the relationship of such structural change as a function of strain with the proton transport. It was found from the pair correlation analysis that the sulfonate distribution and sulfonate-hydronium correlation became stronger through the deformation while the hydronium ion solvation and the internal structure of water phase were not dependent on the deformation. From the directional structure factor profile, it was found that the long range correlation was developed in the perpendicular direction to the extension. The diffusions of water and hydronium ions were enhanced by 30 and 2 %, respectively, after the deformation. From this study, we suggested that it is desirable to investigate the proton transport using simulation methods covering larger dimensions with a long time scale. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCivil engineering. =650 \0$aDeformation. =650 \0$aEnvironnement. =650 \0$aMolecular dynamics simulation. =650 \0$aNafion. =650 \0$aNanophase-segregation. =650 \0$aTransport theory. =650 \0$aTransport. =650 14$aMolecular dynamics simulation. =650 24$aDeformation. =650 24$aNafion. =650 24$aNanophase-segregation. =650 24$aTransport. =700 1\$aChoi, Ji Il,$eauthor. =700 1\$aJae Chun, Byeong,$eauthor. =700 1\$aJang, Seung Soon,$eauthor. =700 1\$aSood, Parveen,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150018.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140053 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140053$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140053$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.F55 =082 04$a363.72/88$223 =100 1\$aKoshy, Nevin,$eauthor. =245 10$aSynthesis and Characterization of Ca and Na Zeolites (Non-Pozzolanic Materials) Obtained From Fly Ash-Ca(OH)2 Interaction /$cNevin Koshy, Bhagwanjee Jha, Srinivas Kadali, D. Singh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b31 =520 3\$aThe conventional method for alkali activation of fly ash utilizes Ca(OH)2 and NaOH for the formation of pozzolanic material and fly ash zeolites, respectively. Sodium-based fly ash zeolites (say, Na-zeolite) mostly employ NaOH (the high-grade mineralizer and alkali) for activation of fly ash before its application as an absorbent. However, the Na-zeolites as absorbents (in agro- and aqua-culture) result in sodicity (i.e., excess of Na, present as impurity in the zeolite), which in turn reduces their holding capacity of moisture, nutrient [i.e., nitrogen, phosphorous, and potassium (NPK fertilizers)], microorganisms (viz., microbial spores), or heavy metals and negatively affect the growth of plant and aquatic life. To resolve such problems, the present study is focused on synthesis of agro-grade blend (dominated by Ca-zeolite) of zeolites by using Ca(OH)2 as major alkali and two well-established mineralizers, NaOH and NaCl, used in the trace quantity. To monitor activation of the fly ash in two different conditions, the synthesis of zeolites could be carried out by employing (1) conventional (the open hydrothermal system), and (2) autoclaving (the closed hydrothermal system) methods. The main attributes that control the entire study include temperature and reaction times for both methods. In addition, the present study demonstrates (1) effectiveness of Ca(OH)2 in creation of blend of zeolites with considerable cation exchange capacity when an optimum chemical composition (comparable to a pure agro- and aqua-grade zeolite 4A), and (2) suitability of the conventional hydrothermal method over autoclave method in synthesizing the blend of Ca- and Na-zeolites possessing a cation exchange capacity up to 394 meq/100 g. The formation of needle/star/spherule/small cube-shaped crystals (i.e., Na-P1, the Na-zeolite) and prismatic/cuboidal shaped crystals (i.e., heulandite, the Ca-zeolite), confirms suitability of the end product as a good sorbent and manure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCalcium zeolite. =650 \0$aFly ash$xEnvironmental aspects. =650 \0$aFly ash. =650 \0$aHydrothermal system. =650 \0$aIndustrial applications. =650 \0$aSodium zeolite. =650 \0$aZeolites. =650 14$aFly ash. =650 24$aCalcium zeolite. =650 24$aHydrothermal system. =650 24$aIndustrial applications. =650 24$aSodium zeolite. =650 24$aZeolites. =700 1\$aJha, Bhagwanjee,$eauthor. =700 1\$aKadali, Srinivas,$eauthor. =700 1\$aSingh, D.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140053.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150023 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150023$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150023$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS1892 =082 04$a547.8426$223 =100 1\$aDellaCorte, Christopher,$eauthor. =245 10$aSuperelastic Ball Bearings :$bMaterials and Design to Avoid Mounting and Dismounting Brinell Damage in an Inaccessible Press-Fit Application-Part I Design Approach /$cChristopher DellaCorte, S. Howard. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aBall bearings require proper fit and installation into machinery structures (onto shafts and into bearing housings) to ensure optimal performance. For many applications, the inner and/or outer races must be mounted with an interference fit and care must be taken during assembly and disassembly to avoid placing heavy static loads between the balls and races, otherwise Brinell dent-type damage can occur. In this paper, a highly dent resistant superelastic alloy, 60NiTi, was considered for rolling element bearing applications that encounter excessive static axial loading during assembly or disassembly. A small (R8) ball bearing was designed for an application where access was limited and precluded the use of disassembly tools. First principles based analyses showed that by careful selection of materials, raceway curvature, and land geometry, a bearing can be designed that allows blind assembly and disassembly without incurring raceway damage due to ball denting. Though such blind assembly applications are uncommon, the availability of bearings with unusually high static load capability may enable more such applications with additional benefits, especially for miniature bearings. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBearings. =650 \0$aElasticity. =650 \0$aRubber. =650 \0$aShock load resistance. =650 \0$aSuperelastic materials. =650 14$aBearings. =650 24$aShock load resistance. =650 24$aSuperelastic materials. =700 1\$aHoward, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150023.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140064 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140064$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140064$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.1/86$223 =100 1\$aDominguez Almaraz, Gonzalo,$eauthor. =245 10$aEffect of Roughness and Residual Compression Stresses on the Ultrasonic Fatigue Endurance of Aluminum Alloy AISI 6061-T6 /$cGonzalo Dominguez Almaraz. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b31 =520 3\$aUltrasonic fatigue tests were carried out on the aluminum alloy AISI 6061-T6, presenting different values for the principal surface roughness parameters: Ra, Rq, and Rz. For fatigue life comprised between 3 x 105 ~ 6 x 106 cycles, crack initiates at the specimen surface induced by stress-concentration and micro-plastic deformation (micro-void coalescence); whereas for the very high cycle fatigue (>107 cycles), the mechanism of crack initiation moves to subsurface or inside the specimen and is associated with internal imperfections such as micro-porosities or nonmetallic inclusions. For the first fatigue life regime, compression residual stresses induced by the work-hardening machining process and the associated micro-plastic deformation are the principal factors controlling the fatigue endurance on this aluminum alloy. Experimental results show that fatigue endurance is higher for the high surface roughness in the 3 x 105 ~ 6 x 106 cycles of fatigue life, whereas this behavior is inversed in the very high-cycle fatigue regime. These results are analyzed in terms of residual compression stresses induced by the work-hardening machining process, the surface roughness, and the reverse yielding or Bauschinger effect. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum alloys. =650 \0$aCompression residual stresses. =650 \0$aFatigue endurance. =650 \0$aMetals$xHeat treatment. =650 \0$aReverse yielding. =650 \0$aSurface roughness. =650 \0$aUltrasonic fatigue testing. =650 14$aSurface roughness. =650 24$aCompression residual stresses. =650 24$aFatigue endurance. =650 24$aReverse yielding. =650 24$aUltrasonic fatigue testing. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140064.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140057 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140057$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140057$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC931.O73 =082 04$a616.7/16$223 =100 1\$aChen, Yunyun,$eauthor. =245 10$aComputational Study in Effects of Nail- and Plate-Implants on the Treatment of Pertrochanteric and Intertrochanteric Fractures /$cYunyun Chen, Guodong Wang, Dongsheng Zhou, Hong Liang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b34 =520 3\$aThis research is to evaluate and identify the most suitable implants for the treatment of trochanteric fractures. Using finite element analysis method (FEM), we developed trochanteric-fractured 3D models based on Arbeitsgemeinschaftfür Osteosynthesefragen (AO) classification. Three types of trochanteric fractured models were assembled with four different implants leading to 12 models. The trochanteric fractures were identified as 31-A1.1, 31-A2.1, and 31-A3.1 fracture fixed with short proximal femur nail antirotation (PFNA), long PFNA, dynamic hip screw (DHS), and PF-locking compression plate 4.5/5.0. The assembled models were calculated and analyzed using the FEM. The simulation illustrated the von Mises stress distribution and displacement on 12 models. The intramedullary nail implant is superior to the external plate. Short PFNA and DHS are suitable to fix pertrochanteric fractures; long PFNA is considered a priority to treat intertrochanteric fractures. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aExternal plate implants. =650 \0$aFinite elements analysis (FEA) =650 \0$aFractures, Bone$xprevention & control. =650 \0$aHealth Promotion. =650 \0$aIntramedullary nail implants. =650 \0$aOsteoporosis$xtherapy. =650 \0$aOsteosynthesis. =650 \0$aTrochanteric fracture. =650 14$aFinite elements analysis (FEA) =650 24$aExternal plate implants. =650 24$aIntramedullary nail implants. =650 24$aOsteosynthesis. =650 24$aTrochanteric fracture. =700 1\$aLiang, Hong,$eauthor. =700 1\$aWang, Guodong,$eauthor. =700 1\$aZhou, Dongsheng,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140057.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140046 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140046$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140046$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.1/86$223 =100 1\$aDoglione, R.,$eauthor. =245 10$aRolling Effect on Serrated Flow in an Al-Li-Cu-Mg Alloy Plate /$cR. Doglione, P. Haghi Ashtiani, C. Berdin. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b37 =520 3\$aThe occurrence of serrated flow has been studied experimentally in a commercial aluminium Al-Li-Cu-Mg alloy (8090). A 12-mm thick rolled plate with marked textures, with difference between the surface layer and the core, was chosen to obtain some insight into the effect of texture on serrated flow. Tension tests have shown that the serrations are more intense in the core than in the surface layer. Microstructural investigations were performed to explain this behavior. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum alloys. =650 \0$aDislocation slip. =650 \0$aMetals$xHeat treatment. =650 \0$aSerrated flow. =650 \0$aTexture. =650 14$aAluminum alloys. =650 24$aDislocation slip. =650 24$aEBSD. =650 24$aSerrated flow. =650 24$aTEM. =650 24$aTexture. =700 1\$aAshtiani, P. Haghi,$eauthor. =700 1\$aBerdin, C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140046.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140063 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140063$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140063$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.1/7$223 =100 1\$aSrinath, J.,$eauthor. =245 10$aMetallurgical Analysis of a Failed 17-4 PH Stainless Steel Pyro Bolt Used in Launch Vehicle Separation Systems /$cJ. Srinath, K. Manwatkar, S. V. S. Murty, P. Narayanan, S. C. Sharma, M. George. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aPrecipitation hardenable stainless steels are widely used in aerospace applications because of their excellent combination of strength and corrosion resistance. In view of this advantage, Fe-17Cr-4Ni (17-4 PH) steel is used in pyro bolts in space ordnance systems for stage separation in a satellite launch vehicle. These systems typically consist of a pyro charge to sever a given material resulting in stage separation, and these materials are exposed to high strain rates. In one such application, although perfect severance took place, secondary cracks were noticed longitudinally, which are not desirable. This steel, in view of its composition, has delta ferrite in a martensitic matrix in the hardened and tempered condition. In wrought products worked unidirectionally, delta ferrite gets oriented along the direction of thermomechanical processing. The effect of delta ferrite orientation on the impact properties of 17-4 PH stainless steel was studied in various heat-treatment conditions with a view to understand the effect of microstructure on impact properties. It was found that the transverse impact properties are severely affected by the presence of highly oriented delta ferrite stringers for any given heat-treatment condition. This has been attributed to the weak delta ferrite-martensite interface, which facilitates easy crack propagation. Finally, it was suggested that the anisotropy in impact properties need to be carefully considered in the design of components for applications that involve high strain rates. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAdiabatic shear bands. =650 \0$aAnisotropy. =650 \0$aBuilding materials. =650 \0$aDelta ferrite. =650 \0$aEngineering design. =650 \0$aImpact properties. =650 \0$aNanoindentation. =650 \0$aPyro bolt. =650 \0$aSeparation system. =650 14$a17-4 PH stainless steel. =650 24$aAdiabatic shear bands. =650 24$aAnisotropy. =650 24$aDelta ferrite. =650 24$aImpact properties. =650 24$aNanoindentation. =650 24$aPyro bolt. =650 24$aSeparation system. =700 1\$aGeorge, M.,$eauthor. =700 1\$aManwatkar, K.,$eauthor. =700 1\$aMurty, S. V. S.,$eauthor. =700 1\$aNarayanan, P.,$eauthor. =700 1\$aSharma, S. C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140063.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150014 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150014$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150014$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP339 =082 04$a621.31/2429$223 =100 1\$aLin, Lianshan,$eauthor. =245 10$aMaterials Databases Infrastructure Constructed by First Principles Calculations :$bA Review /$cLianshan Lin. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b67 =520 3\$aFirst principles calculations, especially calculations based on the high-throughput density functional theory (DFT), have been widely accepted as the major approach in atom scale materials design. First principles calculations performed in a high-performance computing environment have been used to generate hundreds of thousands of crystal and compound records. The exponential growth of computational materials is one of the main drivers to develop an advanced materials database systems to ensure efficient data storage, management, query, presentation, and manipulation. This review covered the most cutting edge materials database systems in materials design and in important applications, such as fuel cells. By comparing the advantages and drawbacks of these high-throughput first principles materials database systems, an optimized computational framework was suggested to meet the specific needs of fuel cell applications. Further development of high-throughput DFT materials databases, which in essence accelerates materials innovation, was also discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBiomass energy. =650 \0$aBiomasse$xConversion. =650 \0$aFirst principles. =650 \0$aFuel cells. =650 \0$aMaterials database. =650 14$aMaterials database. =650 24$aFirst principles. =650 24$aFuel cells. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150014.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150029 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150029$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150029$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL788.4 =082 04$a629.44/2$223 =100 1\$aLoewenthal, Stuart,$eauthor. =245 10$aSpace Station Solar Array Joint Repair /$cStuart Loewenthal, Curtis Allmon, Carter Reznik, Justin Mcfatter, Robert Davis. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b4 =520 3\$aIn October 2007, the International Space Station (ISS) crew noticed a vibrating camera in the vicinity of Starboard Solar Alpha Rotary Joint (SARJ). It had less than 5 months of run time when the anomaly was observed. This 3.2 m-diameter bearing joint supports solar arrays that power the station critical to its operation. The crew performed an EVA to identify what was causing the vibration. It was discovered that one of the 3 bearing tracks of this unconventional bearing had significant spalling damage. This paper discussed the SARJ's unique bearing design and the vulnerability in its design leading to the observed anomaly. The design of an SARJ vacuum test rig was also described along with the results of a life test that validated the proposed repair should extend the life of the SARJ a minimum of 18 years on-orbit. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBearing. =650 \0$aHistories. =650 \0$aInternational cooperation. =650 \0$aInternational Space Station. =650 \0$aLubrication. =650 \0$aSolar alpha rotary joint. =650 \0$aSpace station. =650 14$aSolar alpha rotary joint. =650 24$aBearing. =650 24$aLubrication. =650 24$aSpace station. =700 1\$aAllmon, Curtis,$eauthor. =700 1\$aDavis, Robert,$eauthor. =700 1\$aMcfatter, Justin,$eauthor. =700 1\$aReznik, Carter,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150029.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150016 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150016$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150016$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aK1210 =082 04$a343.0965$223 =100 1\$aKleinohl, N.,$eauthor. =245 10$aResults for a Fuel Cell System Consisting of an SOFC Fed by an Adiabatic Pre-Reforming Fuel Processor With European Standard Road Diesel /$cN. Kleinohl, J. Hansen, P. Nehter, H. Modarresi, A. Bauschulte, J. vom Schloß, K. Lucka. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aIn the near future, ships will need more efficient power generation technologies for auxiliary power supply than those used currently. In the project SchiffsIntegration BrennstoffZelle (SchIBZ), a fuel cell system is being developed to increase the electrical efficiency of on-board power supply systems. In order to avoid the limitation of hydrogen storage, the on-site fuel processing of hydrocarbons offered an opportunity for the hydrogen supply of fuel cell systems to be operated in remote locations. As fuel standard European road diesel was processed with the process of adiabatic pre-reforming, a steam-reforming derivate. A solid oxide fuel cell (SOFC) was coupled with this fuel processor and was fed with standard European diesel fuel. Two flexible test rigs were developed to test the fuel processor and the SOFC either combined or independently. During combined operation, the SOFC modules were fed with feedstock gas from the fuel processor, which ran on standard European diesel fuel. Combined operation of both test rigs at steady state was achieved for more than 1000 h. For the whole experimental runtime, the fuel processor delivered sufficient feedstock quality for the SOFC, and no significant voltage degradation (about 0.5 %) of the SOFC modules was observed over 1000 h of operation. This low value of degradation is known for the operation of SOFC with pure hydrogen and methane without impurities. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDiesel. =650 \0$aExperimental. =650 \0$aFuel processing. =650 \0$aMarine application. =650 \0$amarine marchande. =650 \0$amerchant marine. =650 \0$aPre-reforming. =650 \0$aworking conditions. =650 14$aFuel processing. =650 24$aDiesel. =650 24$aExperimental. =650 24$aMarine application. =650 24$aPre-reforming. =650 24$aSOFC. =700 1\$aBauschulte, A.,$eauthor. =700 1\$aHansen, J.,$eauthor. =700 1\$aLucka, K.,$eauthor. =700 1\$aModarresi, H.,$eauthor. =700 1\$aNehter, P.,$eauthor. =700 1\$avom Schloß, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150016.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150017 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150017$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150017$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.52 =082 04$a620.1/1296$223 =100 1\$aHussain, Shahadat,$eauthor. =245 10$aEffects of Different Quaternary Additions in the Properties of a Cu-Al-Mn Shape Memory Alloy /$cShahadat Hussain, Pravir Kumar, Ashish Kumar Jain, Abhishek Pandey, Rupa Dasgupta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b30 =520 3\$aIn the present study, Cu-12.5 wt. %Al-5 wt. %Mn-80.5 wt. % shape memory alloy is chosen as the base alloy and 2 wt. % of quaternary additions of Fe, Ni, and Ti added to the base alloy. The effects of these additions on in terms of feasibility, microstructure, hardness, and transformation temperature were studied. The findings suggest the possibility to improve martensite formation, attain higher transitions temperatures, and longer retention over the base alloy through such additions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aMartensite. =650 \0$aMaterials$xThermal properties. =650 \0$aMicrostructure. =650 \0$aPhase precipitation. =650 \0$aShape memory alloys. =650 \0$aThermodynamics. =650 \0$aTransition temperature. =650 \0$aX-ray-diffraction studies. =650 14$aShape memory alloys. =650 24$aMartensite. =650 24$aMicrostructure. =650 24$aPhase precipitation. =650 24$aTransition temperature. =650 24$aX-ray-diffraction studies. =700 1\$aDasgupta, Rupa,$eauthor. =700 1\$aJain, Ashish Kumar,$eauthor. =700 1\$aKumar, Pravir,$eauthor. =700 1\$aPandey, Abhishek,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150017.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150003 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150003$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150003$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK9145 =082 04$a333.792/4$223 =100 1\$aLin, L.,$eauthor. =245 10$aInteroperability of Materials Database Systems in Support of Nuclear Energy Development and Potential Applications for Fuel Cell Material Selection /$cL. Lin, T. Austin, W. Ren. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aMaterials database interoperability has been of great interest in recent years for information exchange in support of research and development (R&D). In response to data and knowledge sharing needs of the Gen IV International Forum (GIF) for global collaboration in nuclear energy R&D, the European Commission JRC Institute for Energy and Transport (JRC-IET) and the Oak Ridge National Laboratory (ORNL) established a materials database interoperability project that developed techniques for automated materials data exchange between systems hosted at the two institutes-MatDB Online at JRC-IET and the Gen IV Materials Handbook at ORNL, respectively. The work to enable automated exchange of data between the two systems leveraged the XML data import and export functionalities of both systems in combination with recently developed standards for engineering materials data. The preliminary results of data communication between the two systems demonstrated the feasibility and efficiency of materials database interoperability, which constructs an interoperation framework that can be seamlessly integrated into the high-throughput First Principles material databases and thus advance the discovery of novel materials in fuel cell applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFuel cell material selection. =650 \0$aInteroperability. =650 \0$aMaterials database. =650 \0$aNuclear energy. =650 \0$aNuclear engineering. =650 \0$aNuclear power plants. =650 \0$aPower resources$xForecasting. =650 14$aMaterials database. =650 24$aFuel cell material selection. =650 24$aInteroperability. =650 24$aNuclear engineering. =700 1\$aAustin, T.,$eauthor. =700 1\$aRen, W.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150003.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150049 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150049$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC377 =082 04$a616.8/34$223 =100 1\$aNieslony, A.,$eauthor. =245 10$aUniversal Method for Applying the Mean-Stress Effect Correction in Stochastic Fatigue-Damage Accumulation /$cA. Nieslony, M. Böhm. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b38 =520 3\$aMost of the models used for taking into account the influence of mean stress on fatigue life work on the basis of the correction of stress amplitudes of particular loading cycles. This can be done directly on the amplitudes or through the modification of the reference S-N curve. The mentioned procedure is also applicable for variable amplitude loading where, after rainflow cycle counting, all loading cycles described by amplitude and mean-stress value are designated. Mean-stress correction can be difficult to apply in stochastic fatigue-damage accumulation, also called the spectral method, where the load and the stress level is defined in the frequency domain using the appropriate power spectral density (PSD) function. The PSD function by itself does not give information to the user about the level of mean stress and only provides us with some statistical information of the fluctuating part of the random loading processes. The aim of the paper is to present how we can perform the mean-stress effect correction directly on a PSD function of stress using well-known models, such as proposed by Gerber, Goodman, Soderberg, or Morrow. The correction can be performed depending on the frequency component, which is a significant advantage of the presented method. The theoretical elaborations were used to develop a computer simulation used to compare the frequency-domain with the time-domain computation path. To show the effectiveness of the presented method, fatigue life has been estimated and compared with experimental fatigue test results for S355JR steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFatigue-life prediction. =650 \0$aFrequency domain. =650 \0$aMean stress. =650 \0$aMultiple sclerosis$xExercise therapy. =650 \0$aMultiple sclerosis. =650 \0$aPDF of stress amplitudes. =650 \0$aPSD of stress. =650 14$aMean stress. =650 24$aFatigue-life prediction. =650 24$aFrequency domain. =650 24$aPDF of stress amplitudes. =650 24$aPSD of stress. =700 1\$aBöhm, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150049.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150062 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150062$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA473 =082 04$a620.1/76$223 =100 1\$aJames, M.,$eauthor. =245 12$aA Methodology for Partitioning Residual Stress Effects From Fatigue Crack Growth Rate Test Data /$cM. James, K. Maciejewski, G. Wang, D. Ball, R. Bucci. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aThis paper described an improved fatigue crack growth rate (FCGR) material characterization process that partitioned residual stress effects from the material “true” FCGR behavior, leading to FCGR design curves that are free of residual stress bias. The material used in the program had high residual stress intentionally introduced. Two test methods from the literature were used to characterize the material: the adjusted compliance ratio (ACR) test method for closure correction, and the crack compliance test method for measuring the stress-intensity factor due to residual stress (Kres). Both test methods operated independently on compliance data collected during FCGR tests. Two independent data reduction methods were used to analyze the FCGR data. In the first, the closure corrected ACR data were combined with the Kres data using a power law relationship to normalize the curves into a residual stress free “master” curve, which was then transformed into a more traditional closure free ?Keff curve. In the second, the Kres data were used in a superposition approach along with a closure model to reduce the data directly to the closure free ?Keff curve. The two ?Keff curves were shown to be in good agreement. The closure model was also used to reintroduce the stress ratio effect to generate the familiar da/dN-?K family of design curves that were free of residual stress bias. Validation examples were included where curves for the material with high residual stress were compared with data from similar material that had minimal residual stress, and those results were in good agreement. A summary of fatigue crack growth life predictions was also included to show that when residual stress effects are removed from FCGR characterization data and reintroduced in the fatigue life analysis, fatigue life is predictable within the usual 2x scatter factor for damage tolerance analysis. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDesign curve. =650 \0$aFatigue crack growth rate. =650 \0$aResidual stress. =650 \0$aResidual stresses$vHandbooks, manuals, etc. =650 \0$aSteel$xFatigue$vHandbooks, manuals, etc. =650 \0$aStress-intensity factor. =650 14$aFatigue crack growth rate. =650 24$aDesign curve. =650 24$aResidual stress. =650 24$aStress-intensity factor. =700 1\$aBall, D.,$eauthor. =700 1\$aBucci, R.,$eauthor. =700 1\$aMaciejewski, K.,$eauthor. =700 1\$aWang, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150062.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150053 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150053$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQA273.6 =082 04$a519.24$223 =100 1\$aHarlow, D.,$eauthor. =245 10$aStatistical Modeling of High Cycle Fatigue with Censored Data /$cD. Harlow, H. Cao, P. Schmidt. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aCharacterization and prognosis of materials subjected to very high cycle fatigue is an important aspect of life cycle design and management for structural components. This procedure is even more critical for components in devices that are implanted into humans because of the lack of opportunities for periodic inspection and the severe consequences of failure. The primary structural component of a commercially available heart valve consists of highly-resilient, cold-worked Elgiloy wire, a cobalt-chromium based alloy. In order to be assured of sufficiently high reliability for the component, an extensive high cycle fatigue testing program was conducted. According to one medical device regulatory guidance, the structural component is expected to have a fatigue life in excess of 600 million cycles under worst case physiologic conditions. Using basic principles for fatigue life evaluation, a constant lifeline for mean stress versus stress amplitude was statistically established. The fundamental model for the analysis was a generalized Weibull distribution for which the parameters were stress-dependent. The model was optimized using maximum likelihood methods and confirmed by chi-squared goodness-of-fit evaluation. The methodology used for this investigation, well established in fatigue engineering, was shown to be equally effective when applied to life science problems, with the potential for benefit to patients. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCensored life data. =650 \0$aFatigue. =650 \0$aGoodman diagram. =650 \0$aMATHEMATICS$xApplied. =650 \0$aStrength-life properties. =650 \0$aWeibull distribution. =650 14$aFatigue. =650 24$aCensored life data. =650 24$aGoodman diagram. =650 24$aStrength-life properties. =650 24$aWeibull distribution. =700 1\$aCao, H.,$eauthor. =700 1\$aSchmidt, P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150053.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150055 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150055$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC377 =082 04$a616.8/34$223 =100 1\$aSmith, Luciano,$eauthor. =245 10$aValidation Testing and Analysis of Cracked-Hole Continuing Damage Solutions /$cLuciano Smith, Robert Pilarczyk, James Feiger. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aIn performing damage tolerance analysis (DTA) for aircraft structures, there are instances in which it is necessary to determine not only the life of a crack from a hole to the edge of a part, but the growth of a secondary crack on the opposite side of the hole to failure. These types of fracture mechanics models have recently been added to the commercially available crack growth software programs used for DTA. Southwest Research Institute and the United States Air Force performed testing designed to simulate continuing damage scenarios in which a crack from a hole has failed the primary ligament and a secondary crack is growing from the opposite side of the hole. This testing included constant amplitude testing of two geometries for fracture mechanics model validation and spectrum testing at four combinations of material, geometry, and stress level for validation of retardation parameters. Test results were then compared analytically to stress intensity values calculated using AFGROW, NASGRO, DSTO-developed equations, and the p-version finite element software StressCheck. Because of the nature of the cracking, there is significant in-plane bending, and the different methods available to model the boundary conditions played a large role in the accuracy of the results. When boundary conditions were applied in a manner that closely modeled the testing, stress intensities matched well except near the transition from corner crack to through crack. Deviations from test results in this area and in spectrum test results seem to be caused by differences in crack aspect ratio compared to what is expected analytically. Further investigation is recommended-and planned-to determine the reasons for differences in crack aspect ratio across geometries and loading. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aContinuing damage. =650 \0$aDamage tolerance. =650 \0$aFatigue crack growth. =650 \0$aFracture mechanics modeling. =650 \0$aMultiple sclerosis$xExercise therapy. =650 \0$aMultiple sclerosis. =650 \0$aValidation. =650 14$aFatigue crack growth. =650 24$aContinuing damage. =650 24$aDamage tolerance. =650 24$aFracture mechanics modeling. =650 24$aValidation. =700 1\$aFeiger, James,$eauthor. =700 1\$aPilarczyk, Robert,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150055.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150035 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150035$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aRuggieri, Claudio,$eauthor. =245 12$aA Modified Weibull Stress Approach to Determine the Reference Temperature in a Pressure Vessel Steel /$cClaudio Ruggieri, Robert Dodds. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b45 =520 3\$aThis work describes a micromechanics methodology based upon a local failure criterion incorporating the effects of plastic strain on cleavage fracture coupled with the statistics of microcracks to correct effects of constraint loss on fracture toughness and to determine the reference temperature, T0, based on the master curve procedure. The methodology approaches the modeling of cleavage fracture from the point of view of a coupling between the local plastic strain and the number of eligible Griffith-like microcracks nucleated from brittle particles dispersed into the ferrite matrix. A modified Weibull stress, ˜σw, incorporating the effects of plastic strain on cleavage fracture emerges as a probabilistic fracture parameter to define conditions leading to (local) material failure. Fracture toughness testing conducted on an A515 Grade 65 pressure vessel steel provides the cleavage fracture resistance data in terms of Jc-values needed to estimate T0. Very detailed non-linear finite-element analyses for 3D models of the fracture specimens provide the relationship between ˜σw and J from which the variation of fracture toughness across different crack configurations is predicted. For the tested material, the modified Weibull stress methodology yields estimates for the reference temperature, T0, from small fracture specimens, which are in very good agreement with the corresponding estimates derived from testing of much larger crack configurations. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCleavage fracture. =650 \0$aConstraint effects. =650 \0$aLocal approach. =650 \0$aPCVN specimen. =650 \0$aPlastic strain. =650 \0$aReference temperature. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 \0$aWeibull stress. =650 14$aCleavage fracture. =650 24$aConstraint effects. =650 24$aLocal approach. =650 24$aPCVN specimen. =650 24$aPlastic strain. =650 24$aReference temperature. =650 24$aWeibull stress. =700 1\$aDodds, Robert,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150035.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150059 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150059$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA473 =082 04$a620.1/76$223 =100 1\$aThielen, M.,$eauthor. =245 10$aUsing Barkhausen Noise and Digital Image Correlation to Investigate the Influence of Local Residual Stresses on Fatigue-Crack Propagation /$cM. Thielen, M. Marx, M. Sheikh-Amiri, C. Boller, C. Motz. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b36 =520 3\$aFatigue-crack propagation is, by far, the most crucial failure mechanism of technical systems. The key to understanding microscopic processes that lead to failure lies in the knowledge of local stresses, the driving force of cracks. We present the mapping of stress and strain fields induced by a single overload on a fatigue crack and their influence on transient crack-growth retardation. In contrast to former work, in which synchrotron x-ray diffraction (XRD) was used, this investigation was performed by using a calibrated magnetic Barkhausen noise microscope in combination with digital image correlation based on in situ scanning electron microscope imaging. The underlying mechanisms, residual stress effects in front of the crack tip and plasticity-induced crack closure caused by the plastic wake, have been studied. Specifically, a crack in S960Q steel has been followed through the overload (OL) region while examining measurements at distinctive overload points: before OL, after OL, at maximum retardation, and at recovery. We observe a strong correlation of the local fatigue-crack-growth rate with the local residual stress distribution obtained from magnetic Barkhausen noise, which remains nearly unchanged after the crack has passed by. Digital image correlation results reveal the influence of these residual stresses on crack-tip opening reactions and strain fields under external loads. Although strain fields show a strong decrease because of the OL event, differences in crack opening stresses remain rather low at first, but prevail in the second part of the OL region. The applicability of new measurement methods and their results regarding the dominating retardation mechanism are discussed. These indicate that the residual stress effect on the strain fields can be associated to be more significant than plasticity-induced crack closure at maximum retardation with a change of mechanisms on reacceleration. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDigital image correlation. =650 \0$aFatigue. =650 \0$aMagnetic Barkhausen noise. =650 \0$aOverload effect. =650 \0$aPlasticity-induced crack closure. =650 \0$aResidual stress. =650 \0$aResidual stresses$vHandbooks, manuals, etc. =650 \0$aSteel$xFatigue$vHandbooks, manuals, etc. =650 \0$aVariable-amplitude loading. =650 14$aVariable-amplitude loading. =650 24$aDigital image correlation. =650 24$aFatigue. =650 24$aMagnetic Barkhausen noise. =650 24$aOverload effect. =650 24$aPlasticity-induced crack closure. =650 24$aResidual stress. =700 1\$aBoller, C.,$eauthor. =700 1\$aMarx, M.,$eauthor. =700 1\$aMotz, C.,$eauthor. =700 1\$aSheikh-Amiri, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150059.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150058 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150058$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP983 =082 04$a668/.5$223 =100 1\$aIslam, M.,$eauthor. =245 10$aStudy of Ligament Length Effect on Mode Mix of a Modified In-Plane Shear Test Specimen /$cM. Islam, S. Kao-Walter, G. Yang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aShear fracture toughness is an important material behavior that needs to be determined and considered in many industrial fields. At the same time, shear testing is one of the complex material testing areas where available methods are few, often need special arrangements, and most of the methods do not strictly satisfy the definition of pure shear. In this study, a modified shear test specimen was proposed to measure the shear fracture toughness by uniaxial loading in a tensile testing machine. High density polyethylene (HDPE) was used as test material for the experiments. The specimen was created in order to suit the most common used tensile test machine. The specimen was then optimized by using finite element analysis (FEA) to find the geometry and the size of the pre-notch to avoid the mixed mode loading and minimize effects of normal stresses. For the specimen in discussion, an upper and lower limit of usable ligament length can be found. A method for determining the fracture toughness was discussed according to the essential work of fracture. Finally, an example of a special application of the proposed specimen was presented where the variation of shear strength of controlled delamination material (CDM) was measured. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCosmetics. =650 \0$aFinite element simulation. =650 \0$aFracture toughness. =650 \0$aPolymers. =650 \0$aShear test specimen. =650 \0$aToilet preparations. =650 14$aShear test specimen. =650 24$aFinite element simulation. =650 24$aFracture toughness. =650 24$aPolymers. =700 1\$aKao-Walter, S.,$eauthor. =700 1\$aYang, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150058.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150061 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150061$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.E6 =082 04$a668.4/226$223 =100 1\$aFord, K.,$eauthor. =245 10$aCracking in a Flame-Sprayed Epoxy /$cK. Ford, M. Stavig, R. Chambers. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b11 =520 3\$aThe objective of this work was to understand the cracking of aluminum flame spray on an epoxy thermoset. In the experiments presented here, epoxy cylinders were uniformly coated with flame spray. The cylinders were put into a state of tensile stress by taking them to elevated temperatures and similarly put into a state of compression by taking them down to cold temperatures. Surface cracks on the outside of the cylinders were photographed and compared. The cylinders were cross-sectioned at room temperature to study how the aluminum surface cracks propagate into the epoxy. It was shown that thicker aluminum generates observable surface cracks at a lower temperature than a thinner coating does. The surface cracks cannot be seen at room temperature. However, some of the coating cracks propagate into the substrate and can be seen at room temperature when the cylinder is cross-sectioned. The substrate cracks tend to be deeper with a larger coating thickness. Similarly, cracks are deeper when the substrate with a given thickness is taken to higher temperature. Supplementary examples that contain the addition of a hard inclusion (copper strip) between the aluminum and epoxy substrate at elevated temperatures were discussed, as well as delamination of the aluminum film at cold temperature. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCoating. =650 \0$aCrack. =650 \0$aEpoxy. =650 \0$aFireproofing agents. =650 \0$aFlame spray. =650 \0$aproperties. =650 \0$aThermal spray. =650 14$aThermal spray. =650 24$aCoating. =650 24$aCrack. =650 24$aEpoxy. =650 24$aFlame spray. =700 1\$aChambers, R.,$eauthor. =700 1\$aStavig, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150061.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150057 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150057$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA473 =082 04$a620.1/76$223 =100 1\$aRonevich, J.,$eauthor. =245 10$aAssessing Gaseous Hydrogen Assisted Fatigue Crack Growth Susceptibility of Pipeline Steel Weld Fusion Zones and Heat Affected Zones /$cJ. Ronevich, B. Somerday. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b19 =520 3\$aThe objective of this work was twofold: (1) measure reliable fatigue crack growth relationships for X65 steel and its girth weld in high-pressure hydrogen gas to enable structural integrity assessments of hydrogen pipelines, and (2) evaluate the hydrogen accelerated fatigue crack growth susceptibility of the weld fusion zone and heat-affected zone relative to the base metal. Fatigue crack growth relationships (da/dN versus ?K) were measured for girth welded X65 pipeline steel in high pressure hydrogen gas (21 MPa) and in air. Hydrogen assisted fatigue crack growth was observed for the base metal (BM), fusion zone (FZ), and heat-affected zone (HAZ), and was manifested through crack growth rates reaching nearly an order of magnitude acceleration over rates in air. At higher ?K values, crack growth rates of BM, FZ, and HAZ were coincident; however, at lower ?K, the fatigue crack growth relationships exhibited some divergence with the fusion zone having the highest crack growth rates. These relative fatigue crack growth rates in the BM, FZ, and HAZ were provisional, however, since both crack closure and residual stress contributed to the crack-tip driving force in specimens extracted from the HAZ. Despite the relatively high applied R-ratio (R = 0.5), crack closure was detected in the heat affected zone tests, in contrast to the absence of crack closure in the base metal tests. Crack closure corrections were performed using the adjusted compliance ratio method and the effect of residual stress on Kmax was determined by the crack-compliance method. Crack-tip driving forces that account for closure and residual stress effects were quantified as a weighted function of ?K and Kmax (i.e., Knorm), and the resulting da/dN versus Knorm relationships showed that the HAZ exhibited higher hydrogen accelerated fatigue crack growth rates than the BM at lower Knorm values. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aEmbrittlement. =650 \0$aFatigue crack growth. =650 \0$aHydrogen. =650 \0$aPipeline steel. =650 \0$aResidual stress. =650 \0$aResidual stresses$vHandbooks, manuals, etc. =650 \0$aSteel$xFatigue$vHandbooks, manuals, etc. =650 \0$aWeld. =650 14$aFatigue crack growth. =650 24$aEmbrittlement. =650 24$aHydrogen. =650 24$aPipeline steel. =650 24$aResidual stress. =650 24$aWeld. =700 1\$aSomerday, B.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150057.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150050 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150050$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA409 =082 04$a620.1/26$223 =100 1\$aMayer, U.,$eauthor. =245 10$aConsidering the Statistical Distribution of Dynamic Fracture Toughness Data and the Actual Loading Rate at Fracture Initiation When Applying ASTM E1921 at Elevated Loading Rates /$cU. Mayer. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b15 =520 3\$aASTM E1921-15a describes the determination of the reference temperature T0,X for the loading rate X for ferritic steels in the transition range, where X is the order of magnitude of the average loading rate of the tests evaluated. Because this rate is defined for the linear-elastic part of a test only, the definition of the loading rate, valid for tests showing not only linear-elastic but also plastic behavior, is important. In a research project investigating the correlation of dynamic crack initiation and crack arrest funded by the German government, tests at –20°C on specimens of 22 NiMoCr 3 7 steel (A 508 Cl.2) were performed with different specimen geometry and loading devices in the range from 105 MPa?m s–1 to 3 x 106 MPa?m s–1. Evaluation according to ASTM E1921 shows differences of up to 30 K in T0,X obtained from linear-elastic test series and T0,X obtained from elastic-plastic test series with comparable dK/dt. New results were obtained in the current follow-up joint IWM-MPA project from test series at a loading rate of 5 x 105 MPa?m s–1. Results from tests with 1T C(T)-specimen at various test temperatures in the transition region are presented, analyzed, and reference temperature T0,5 is evaluated. The statistical distribution of the determined dynamic fracture toughness values KId resp., KJc,d and the determination of the characteristic loading rate in the case of elastic-plastic tests is discussed. This analysis shows the need of modifications of the standard evaluation method in ASTM E1921, if used for tests at elevated loading rate. The assumed statistical distribution has to be adapted and the actual loading rate at fracture initiation has to be taken into account. Suggestions for the considerations and requirements for the evaluation of data determined at elevated loading rates are presented. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCompact tension specimen. =650 \0$aDuctile to brittle transition. =650 \0$aDynamic fracture. =650 \0$aElevated loading rate. =650 \0$aFracture mechanics. =650 \0$aMaster curve. =650 \0$aStructural dynamics. =650 14$aASTM E1921. =650 24$aCompact tension specimen. =650 24$aDuctile to brittle transition. =650 24$aDynamic fracture. =650 24$aElevated loading rate. =650 24$aFracture mechanics. =650 24$aMaster curve. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150050.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150063 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150063$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA473 =082 04$a620.1/76$223 =100 1\$aKoechlin, Samuel,$eauthor. =245 10$aHigh Cycle Fatigue Strength of Punched Thin Fe-Si Steel Sheets /$cHelmi Dehmani, Charles Brugger, Thierry Palin-Luc, Charles Mareau, Samuel Koechlin. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aSome parts of electrical machines are built from stacks of thin steel sheets, for which the coarse grain microstructure allows for minimizing magnetic losses. The fabrication process of these parts usually involves punching operations that generate important defects on the edges. Since these alterations may result in a degradation of the fatigue strength, this study aims at elaborating on a fatigue design strategy for such punched parts. To reach this objective, high cycle fatigue tests are performed on different specimens with either punched or polished edges. The results show a significant decrease of the fatigue strength for punched specimens. Scanning electron microscope observations of specimen facture surfaces reveal that defects on punched edges are at the origin of the fatigue cracks. The influence of temperature is also investigated. Fatigue tests are performed at ambient temperature (20°C) and at 180°C. According to the experimental results, no significant influence on the median fatigue strength is observed. Since crack initiation always occur on the edges, additional investigations are performed to characterize how edges are altered by punching operations. Residual stresses are determined on punched edges using x-ray diffraction techniques. As a consequence of punching, important tensile residual stresses exist along the loading direction. In association with the stress concentration caused by geometrical defects, residual stresses promote crack initiation and fast crack propagation. For a better understanding of crack initiation, edge geometries are scanned with a 3D optical profilometer, allowing us to identify the critical defect. It is found that the typical defect size is comparable to the grain size. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDefect. =650 \0$aFe-Si steel sheet. =650 \0$aHCF fatigue. =650 \0$aPunching effect. =650 \0$aResidual stress. =650 \0$aResidual stresses$vHandbooks, manuals, etc. =650 \0$aSteel$xFatigue$vHandbooks, manuals, etc. =650 \0$aTemperature effect. =650 14$aFe-Si steel sheet. =650 24$aDefect. =650 24$aHCF fatigue. =650 24$aPunching effect. =650 24$aResidual stress. =650 24$aTemperature effect. =700 1\$aBrugger, Charles,$eauthor. =700 1\$aKoechlin, Samuel,$eauthor. =700 1\$aMareau, Charles,$eauthor. =700 1\$aPalin-Luc, Thierry,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150063.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150076 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150076$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC377 =082 04$a616.8/34$223 =100 1\$aRabbolini, S.,$eauthor. =245 10$aCrack-Closure Measurements in Low-Cycle Fatigue With Digital Image Correlation /$cS. Rabbolini, S. Beretta, S. Foletti, L. Rusconi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b34 =520 3\$aIn this work, an experimental campaign devoted to measure closure levels onto specimens subjected to low-cycle fatigue (LCF) conditions is described. Two different straining conditions were investigated (i.e., R = –1 and R = 0.5). The measurements of ?op, crack-opening stresses, were carried out by adopting the concept of “crack-tip opening displacements” and “local strain cycles.” However, instead of the original strain gauges measurements above the plane of the propagating crack, the strain cycles were measured by DIC in proximity of the crack tip. Experimental results were compared to those provided by the analytical model proposed by Newman. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCrack closure. =650 \0$aCrack-tip strains. =650 \0$aDigital image correlation. =650 \0$aLow-cycle fatigue. =650 \0$aMultiple sclerosis$xExercise therapy. =650 \0$aMultiple sclerosis. =650 \0$aShort-crack propagation. =650 14$aLow-cycle fatigue. =650 24$aCrack closure. =650 24$aCrack-tip strains. =650 24$aDigital image correlation. =650 24$aShort-crack propagation. =700 1\$aBeretta, S.,$eauthor. =700 1\$aFoletti, S.,$eauthor. =700 1\$aRusconi, L.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150076.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160006 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1603-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160006$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA409 =082 04$a620.1/26$223 =100 1\$aMcClung, R.,$eauthor. =245 10$aIntegrating Fracture Mechanics Into the Material and Structural Design Process /$cR. McClung. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b26 =520 3\$aA new paradigm is now emerging that has the potential to transform fracture control and, in fact, to transform the entire material and structural design process. In a nutshell, the new paradigm is to design and virtually evaluate the material, the manufacturing process, and the structure in an integrated manner for the specific purpose of meeting structural reliability goals in a fraction of the currently required time. The engine of the new paradigm is a set of robust computational models for fatigue crack growth (FCG) and fracture that are fully integrated with computational models for material microstructure and properties, manufacturing processes, and structural response. Efficient methods for calculating stress intensity factors are linked directly with 2D and 3D finite-element models for stress and thermal analysis to perform automated FCG life analysis, next incorporating advanced probabilistic models to calculate fracture risk. The initial conditions for these calculations are informed by direct links to manufacturing process simulation software to determine bulk residual stress fields and location-specific microstructure and properties. Crack origins are linked to specific quantified threats, such as inherent material anomalies, induced manufacturing or maintenance anomalies, or naturally occurring fatigue damage. The entire calculation process is performed in an appropriate probabilistic framework to quantify significant uncertainty and variability. Several specific examples of recent efforts to build and extend this integrated framework are cited, and several suggestions are offered for future work. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAnomalies. =650 \0$aDesign. =650 \0$aFatigue crack growth. =650 \0$aFracture mechanics. =650 \0$aFracture. =650 \0$aLife prediction. =650 \0$aManufacturing. =650 \0$aProbabilistic. =650 \0$aReliability. =650 \0$aSoftware. =650 \0$aStructural dynamics. =650 14$aFracture. =650 24$aAnomalies. =650 24$aDesign. =650 24$aFatigue crack growth. =650 24$aICME. =650 24$aLife prediction. =650 24$aManufacturing. =650 24$aProbabilistic. =650 24$aReliability. =650 24$aSoftware. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 3 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160006.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130043 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130043$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130043$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.T54 =082 04$a669/.96142$223 =100 1\$aFernandez-Zelaia, P.,$eauthor. =245 10$aInfluence of Control Mode on Thermomechanical Fatigue Testing of Circumferentially-Notched Specimens /$cP. Fernandez-Zelaia, R. Neu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aThe aim of this study is to understand the influence of experimentally applied boundary conditions on circumferentially-notched specimens under thermomechanical fatigue loadings (TMF) in two Ni-base superalloys, one equiaxed polycrystalline, and one directionally-solidified. TMF experiments were performed under both force-controlled and displacement-controlled conditions. Notch severities ranged from kt = 1.3 to kt = 2. The notch response was evaluated by finite element analysis using temperature-dependent viscoplasticity. The experiments and analyses are used to assess the impact of the applied boundary conditions on calculated and observed fatigue crack initiation lives. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBoundary conditions. =650 \0$aMetals$xThermomechanical treatment. =650 \0$aNi-base superalloy. =650 \0$aNotch analysis. =650 \0$aNotched specimens. =650 \0$aSteel$xMetallurgy. =650 \0$aThermomechanical fatigue. =650 14$aNotched specimens. =650 24$aBoundary conditions. =650 24$aNi-base superalloy. =650 24$aNotch analysis. =650 24$aThermomechanical fatigue. =700 1\$aNeu, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130043.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130060 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130060$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130060$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aKalyanasundaram, Valliappa,$eauthor. =245 12$aA Recent Development in Creep-Fatigue Testing /$cValliappa Kalyanasundaram, Stuart Holdsworth, Ashok Saxena. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b48 =520 3\$aProcedures for the assessment of components subject to cyclic loading at high temperatures require material property input data that characterize the creep-fatigue deformation response and resistance to cracking. For many years, there was no testing standard or code of practice to ensure that such information was generated in a uniform way. This was mainly because the creep-fatigue test data requirements for organizations in various industrial sectors appeared to be so different that the need for standardization was questioned. In the mid-2000s, it was recognized that even though it would make no sense to be prescriptive about such details as cycle shape, there were many aspects of creep-fatigue testing for which guidance would be beneficial to ensure acceptable uniformity in deformation and endurance data generation. In response to this realization, the state of the art relating to creep-fatigue interaction was extensively reviewed by an international group of specialists, and the generated knowledge base was used to underpin a new ASTM testing standard, ASTM E2714-09. The gathered knowledge is reviewed. There is a requirement for all ASTM standards to include a precision and bias statement, and an international interlaboratory creep-fatigue test comparison activity was facilitated to form the basis of this section of ASTM E2714-09. An integral part of the guidance given in the new standard is the recommendation for post-test metallurgical inspection and the way in which this information can be used to give added value to creep-fatigue crack initiation endurance results. The evidence gathered from this study is also examined. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCreep-fatigue testing. =650 \0$aInterlaboratory study. =650 \0$aPost-test inspection. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 \0$aSteel. =650 14$aCreep-fatigue testing. =650 24$aInterlaboratory study. =650 24$aP91 steel. =650 24$aPost-test inspection. =700 1\$aHoldsworth, Stuart,$eauthor. =700 1\$aSaxena, Ashok,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130060.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130054 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130054$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130054$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aHolmström, Stefan,$eauthor. =245 10$aCreep-Fatigue Interaction Models for Grade 91 Steel /$cStefan Holmström, Rami Pohja, Warwick Payten. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (26 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b28 =520 3\$aDifferent approaches for modelling creep-fatigue (CF) interaction are used on strain controlled creep fatigue data of 9Cr-1Mo-VNb (P91) steel and assessed with the target of finding suitable candidates for use in design rules. The assessed models include time, ductility, and strain energy-based creep-fatigue interaction methods and two simplified models. For the interaction diagram-based models, the challenge of acquiring representative creep damage fractions from the dynamic material response, i.e., cyclic softening with changing relaxation behaviour is addressed. In addition, the interaction diagram approaches are discussed in the light of known (fatigue) material scatter and defining representative cycles for CF data. The performance of the model are presented and also compared against the RCC-MR design code methodology. It is shown that the fitting accuracy of the complex interaction models vary significantly and that modified ductility based models seem to be less susceptible to changes in supporting creep and relaxation models. Successful and also superior prediction of the CF number of cycles to failure for Grade 91 steel was accomplished by simplified methods with much less fitting parameters. The practicality in using interaction diagram methods for design purposes, where simplicity is a key issue, is questioned. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 \0$aSteel. =700 1\$aPayten, Warwick,$eauthor. =700 1\$aPohja, Rami,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130054.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130049 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130049$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130049$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aBF720.C63 =082 04$a155.42/23$223 =100 1\$aAmaro, Robert,$eauthor. =245 10$aTowards the Development of a Physics-Based Thermo-Mechanical Fatigue Life Prediction Model for a Single Crystalline Ni-Base Superalloy /$cRobert Amaro, Stephen Antolovich, Richard Neu, Benjamin Adair, Michael Hirsch, Patxi Fernandez-Zelaia, Matthew O'Rourke, Alexander Staroselsky. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b19 =520 3\$aA long term effort has been underway to develop a mechanism-based model for life prediction under thermo-mechanical fatigue (TMF) cycling. A model has been developed which is based upon the impingement of slip bands upon oxidized regions and subsequent initiation of a crack due to stress concentration. The concept of an effective cycle temperature, Teff, and the dynamic nature of the material are critical components of the model and result in the ability to produce very accurate life predictions. It has also been shown that the model is capable of addressing complexities such as imposed high cycle fatigue (HCF) while still producing excellent agreement with the experiment. However, given the fact that this material is used for jet engine turbine blades and that such blades have cooling holes which act as notches, the next step in the development of this model is to incorporate it into a notched environment. The principal features of the TMF model are reviewed and a strategy for full integration into notched fatigue life prediction is discussed. Recent experimental results are presented which are based upon simulating smooth bar conditions at the notch root and a first approach to numerical simulation (called Q fit) is presented. Suggestions for further research are discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aIndividual differences in infants$xTesting. =650 \0$aIntelligence Tests$xin infancy & childhood. =650 \0$aLife prediction. =650 \0$aNi-base superalloys. =650 \0$aNotches. =650 \0$aPrediction (Psychology) =650 \0$aThermo-mechanical fatigue. =650 14$aNi-base superalloys. =650 24$aLife prediction. =650 24$aNotches. =650 24$aThermo-mechanical fatigue. =700 1\$aAdair, Benjamin,$eauthor. =700 1\$aAntolovich, Stephen,$eauthor. =700 1\$aFernandez-Zelaia, Patxi,$eauthor. =700 1\$aHirsch, Michael,$eauthor. =700 1\$aNeu, Richard,$eauthor. =700 1\$aO'Rourke, Matthew,$eauthor. =700 1\$aStaroselsky, Alexander,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130049.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130070 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130070$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130070$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.22 =082 04$a620.1/1233$223 =100 1\$aBouchenot, Thomas,$eauthor. =245 10$aApproach for Stabilized Peak/Valley Stress Modeling of Non-Isothermal Fatigue of a DS Ni-Base Superalloy /$cThomas Bouchenot, Ali Gordon, Sachin Shinde, Phillip Gravett. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (28 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aTurbine blades derived from directionally solidified (DS) Ni-base superalloys are increasingly employed in the first and second stages of gas turbine engines, where thermal and mechanical cycling facilitate cyclic plasticity and creep. The elongated grains, which are aligned with the primary stress axis of the component, provide (1) greater creep ductility, and (2) lower minimum creep rate in solidification direction compared to other directions. Tracking the evolution of deformation in these structures necessitates a constitutive model having the functionality to capture rate, temperature, history, and orientation dependence. Historically, models rooted in microstructurally based viscoplasticity simulate the response of long-crystal, dual-phase, Ni-base superalloys with extraordinary fidelity; however, a macroscopic approach having reduced order is leveraged to simulate low-cycle fatigue (LCF), creep, and creep-fatigue responses with equally high accuracy. This study applies uncoupled creep and plasticity models to predict the thermomechanical fatigue (TMF) of a generic DS Ni-base, and an anisotropic yield theory accounts for transversely isotropic strength. The microstructure of the subject material contains ?-matrix (FCC Ni) and γ-particles (cuboidal Ni3Al). Because of the fully analytic determination of material constants from mechanical test data, the model can be readily tuned for materials in either peak- or base-loaded units. Application of the model via a parametric study reveals trends in the stabilized hysteresis response of under isothermal fatigue, creep fatigue, idealized thermomechanical fatigue, and conditions representative of in-service components. Though frequently considered in design and maintenance of turbine materials, non-isothermal fatigue has yet to be accurately predicted for a generalized set of loading conditions. The formulations presented in this study address this knowledge gap using extensions of traditional Ramberg-Osgood and Masing models. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCast-nickel-base alloy. =650 \0$aColumnar grained. =650 \0$aContinuum damage mechanics. =650 \0$aRheology. =650 \0$aViscoelastic materials$xThermomechanical properties. =650 \0$aViscoplasticity. =650 14$aColumnar grained. =650 24$aCast-nickel-base alloy. =650 24$aViscoplasticity. =700 1\$aGordon, Ali,$eauthor. =700 1\$aGravett, Phillip,$eauthor. =700 1\$aShinde, Sachin,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130070.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130075 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130075$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130075$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.T54 =082 04$a669/.96142$223 =100 1\$aTorres-Garza, A.,$eauthor. =245 14$aThe Design of a Laboratory Test Machine to Simulate Thermal Fatigue in Hot-Working Tool Steels /$cA. Torres-Garza, M. Quiñones-Salinas, I. Barragan-Serna, R. Mercado-Solis. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aA laboratory-scale thermal fatigue simulator has been designed, constructed, and commissioned by the authors for studying thermal fatigue of hot-working tool steels by means of rapid alternated heating and cooling. The basic design features, construction characteristics, and test capabilities of the thermal fatigue simulator are presented in this paper. Thermal fatigue simulations were run on hardened and tempered AISI H13 hot-working tool steel specimens in time-control with heating and cooling times of 15 and 10 s, respectively, and a total number of 500 and 2000 thermal fatigue cycles. The experimental results have demonstrated that the simulator is capable of producing thermal fatigue cracks with the same characteristics of those seen in real industrial hot-working tools. Based on their size and the extent of propagation, a clear distinction between primary, secondary, and craze cracks could be established at the failed surfaces. Additionally, a thermo-mechanical finite element model of the first 10 thermal fatigue cycles was developed to compute the transient temperatures, stresses, and strains distributions within the test specimen during thermal cycling. Based on the model results, the low cycle fatigue life was estimated using the Coffin-Manson equation, which relates the number of cycles to crack initiation to the plastic strain range per cycle. The experimentally obtained fatigue lives were appreciably shorter than the calculated ones, arguably due to surface roughness and oxidation effects. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCracking. =650 \0$aFE modelling. =650 \0$aLaboratory simulation. =650 \0$aMetals$xThermomechanical treatment. =650 \0$aSteel$xMetallurgy. =650 \0$aThermal cycling. =650 \0$aThermal fatigue. =650 14$aThermal fatigue. =650 24$aCracking. =650 24$aFE modelling. =650 24$aLaboratory simulation. =650 24$aThermal cycling. =700 1\$aBarragan-Serna, I.,$eauthor. =700 1\$aMercado-Solis, R.,$eauthor. =700 1\$aQuiñones-Salinas, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130075.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130081 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130081$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130081$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA409 =082 04$a620.1/126$223 =100 1\$aYan, Wentao,$eauthor. =245 10$aShort Creep-Fatigue Crack Growth in an Advanced 9 %Cr Steel /$cWentao Yan, Stuart Holdsworth, Ingo Kühn, Edoardo Mazza. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b47 =520 3\$aWhile the development of short cracks due to cyclic elastic loading has been relatively widely studied, in particular at room temperature, their consideration for cyclic inelastic loading at high temperatures and lower frequencies is not so common. Short creep-fatigue crack growth rates may be correlated in terms of cyclic strain range, cyclic J-integral or strain energy density factor, with appropriate allowance for associated creep damage accumulation. Candidate approaches are evaluated with reference to test results generated for an advanced 9 %Cr turbine rotor steel. This paper promotes the use of cyclic strain range and strain energy density factor relative to other candidate correlating parameters in relation to the results of a series of 30 min hold time creep-fatigue tests performed using fully instrumented uniaxial specimens with short crack starters. The focus of the testing campaign is an advanced 9 %Cr turbine rotor steel at temperatures of 600 and 625°C. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aJ-integral. =650 \0$aMaterials$xCreep. =650 \0$aMaterials$xFatigue. =650 \0$aShort creep-fatigue crack growth. =650 \0$aStrain energy density factor. =650 \0$aStress corrosion. =650 14$aShort creep-fatigue crack growth. =650 24$a9 %Cr steel. =650 24$aJ-integral. =650 24$aStrain energy density factor. =700 1\$aHoldsworth, Stuart,$eauthor. =700 1\$aKühn, Ingo,$eauthor. =700 1\$aMazza, Edoardo,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130081.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130059 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130059$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130059$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA347.F5 =082 04$a620.00151825$223 =100 1\$aOkrajni, Jerzy,$eauthor. =245 10$aLocal Strains That Lead to the Thermo-mechanical Fatigue of Thick-walled Pressure Vessels /$cJerzy Okrajni, Mariusz Twardawa. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b20 =520 3\$aThis paper discusses the issue of the modeling of strains and stresses resulting from the heating and cooling processes of components in power plants. The main purpose of this work was to determine the mechanical behavior of power plant components operating under mechanical and thermal loading. The finite element method has been used to evaluate the temperature and stress changes in components as a function of time. The temperature fields in the components of power plants are dependent, apart from other relevant parameters, on variable heat-transfer conditions between these components and the fluid medium (which may change its state) flowing inside them. For this reason an evaluation of the temperature field and the consequent stress fields requires the consideration of heat-transfer coefficients as time-dependent variables, which in turn calls for suitable techniques for the determination of appropriate values for these coefficients. Methodology that combines computer modeling of the temperature fields with temperature measurements performed at selected points of the pipelines may be used in this case. It is readily apparent from the stress-versus-time graphs that under unsteady operating conditions the components analyzed in this study, especially in the case of boiler restarts, may operate with transient thermal stresses that sometimes reach values higher than a yield point. Consequently, a thermo-mechanical fatigue process takes place in the materials of the components in question. Local stress-strain diagrams for the selected points of the plant components describe this kind of fatigue. These diagrams characterize the intensity of the process and are necessary when the fatigue life is predicted. Such diagrams are part of thermo-mechanical fatigue life prediction methods. The problem of their description is important in the development of a new design methodology for highly reliable pressure vessels. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aComponent temperature measurements. =650 \0$aFinite element method. =650 \0$aHeat transfer. =650 \0$aPower plant components. =650 \0$aStress-strain curves. =650 \0$aThermo-mechanical fatigue. =650 14$aThermo-mechanical fatigue. =650 24$aComponent temperature measurements. =650 24$aFinite element method. =650 24$aHeat transfer. =650 24$aPower plant components. =650 24$aStress-strain curves. =700 1\$aTwardawa, Mariusz,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130059.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130055 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130055$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130055$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.T54 =082 04$a669/.96142$223 =100 1\$aNani Babu, M.,$eauthor. =245 10$aFatigue Crack Growth Behavior of Ferritic and Austenitic Steels at Elevated Temperatures /$cM. Nani Babu, G. Sasikala. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (28 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b46 =520 3\$aFor the integrity assessment and damage-tolerant design of components operating at elevated temperatures under cyclic loading conditions, evaluation of fatigue crack growth (FCG) properties in the threshold and Paris regimes is important. The FCG behaviors of a modified 9Cr-1Mo steel (P91) and SS 316L(N) for applications in the prototype fast breeder reactor to be commissioned shortly at Kalpakkam, India have been studied extensively in our laboratory over a wide range of temperatures. Some aspects of high-temperature FCG observed in these investigations will be reviewed in this paper. It has been observed that for many engineering alloys, dynamic strain aging plays an important role in the temperature-dependent variations in deformation and fracture behavior, including the FCG parameters. Another important aspect in deciding the FCG behavior is the crack closure behavior, the mechanisms of which may vary with temperature. Effect of crack closure and DSA on the FCG properties of P91 steel and SS 316L(N) welds will be discussed. The DSA mechanism has been identified from the activation energy for the process determined from the temperature dependence of the crack tip strain rates. During FCG of engineering materials, there can be stress shielding at the crack tip because of various factors, like crack bridging, branching, closure, etc. Effect of stress shielding at the crack tip at different conditions was quantified using a procedure incorporating the inter relations between compliance, crack length, and stress intensity factor. The paper will summarize the results of the above studies. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCrack closure. =650 \0$aCrack tip shielding. =650 \0$aDynamic strain aging. =650 \0$aFatigue crack growth. =650 \0$aMetals$xThermomechanical treatment. =650 \0$aSteel$xMetallurgy. =650 14$aFatigue crack growth. =650 24$aCrack closure. =650 24$aCrack tip shielding. =650 24$aDynamic strain aging. =650 24$aP91 steel. =650 24$aRAFM steel. =650 24$aSS 316(N) weld. =700 1\$aSasikala, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130055.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130039 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130039$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130039$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTD898.8.C67 =082 04$a628.5/4$223 =100 1\$aPrakash, Raghu,$eauthor. =245 10$aFatigue Behavior of Nickel Based Super Alloy 718 in a Hot Corrosive Environment /$cRaghu Prakash, Sampath Dhinakaran, Jeyar Venkata Ramakanth, Neeta Paulose, S. Narendrababu, S. Mannan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b23 =520 3\$aNickel based super-alloys when exposed to a combination of high temperature and low melting point fused corrosion products, result in early fatigue failure compared to their response in high temperature benign environment. The high cycle fatigue (HCF) (at 550 and 625°C) as well as fatigue crack growth (at 550°C) behavior of a nickel based super alloy 718 in hot corrosive environment (Na2SO4+NaCl salt coating), typical of marine engine environment, is presented in this paper. At least an order of magnitude decrease in fatigue life is noticed when the temperature is changed from 550 to 625°C at stress levels below 450 MPa. The statistical analysis of scatter in fatigue lives at different stress levels is performed and a Weibull-Inverse power law model is fitted to the stress-fatigue life data of alloy 718 in hot corrosive environment. Fracture surface examination of hot corrosion fatigue failures showed higher crack growth rates compared to uncoated high temperature HCF fracture surfaces. Fatigue crack growth rate at 550°C in a hot corrosive environment increases by an order of magnitude at 0.5 Hz in the Paris region compared to crack growth kinetics at 2 Hz in lab air environment at the same temperature. The fracture surface shows a mix of transgranular and intergranular mode of crack in the propagation region at 0.5 Hz. A fatigue failure diagram is proposed combining the thresholds of maximum stress level from endurance tests and maximum stress intensity factor from fatigue crack growth tests to demarcate the regions of propagating and non-propagating cracks during hot corrosion fatigue. The complexities in incorporating the effect of loading frequency in fatigue failure diagram are highlighted. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCorrosive wastes. =650 \0$acorrosive. =650 \0$aFactory and trade waste. =650 \0$aFatigue crack growth. =650 \0$aFatigue failure diagram. =650 \0$aHigh cycle fatigue behavior. =650 \0$aHot corrosive environment. =650 14$aHigh cycle fatigue behavior. =650 24$aFatigue crack growth. =650 24$aFatigue failure diagram. =650 24$aHot corrosive environment. =700 1\$aDhinakaran, Sampath,$eauthor. =700 1\$aMannan, S.,$eauthor. =700 1\$aNarendrababu, S.,$eauthor. =700 1\$aPaulose, Neeta,$eauthor. =700 1\$aVenkata Ramakanth, Jeyar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130039.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130038 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130038$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130038$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC963.48 =082 04$a155.9/042$223 =100 1\$aKeller, Scott,$eauthor. =245 10$aCoupled Fatigue Crack Initiation and Propagation Model Utilizing a Single Blunt Notch Compact Tension Specimen /$cScott Keller, Ali Gordon. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (27 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b28 =520 3\$aMany power generation facilities equipped with turbomachinery are designed to provide electric energy on an as-needed basis and, as a consequence, impart a mixture of fatigue and creep damage to high-value components at elevated temperatures. Cracks are often initiated on free surfaces of these parts near stress-raising features and propagate under thermal-mechanical cycling until the component is removed from service. Whether the emphasis is on creep or fatigue failure, most conventional structural life prediction approaches decouple crack initiation from crack propagation. Turbine designers are in need of approaches that span the full life cycle of components in which both initiation and propagation are the consequences of a variety of mechanical failure modes. Although recent fracture mechanics methods have been developed to account for fatigue- and creep-crack growth, a tacit assumption is that a precrack exists. Another main limitation of these approaches is the small scale yielding assumption, associated with linear elastic fracture mechanics, in which extensive plasticity invalidates such analyses. In this study, utilizing a blunt notch compact tensile specimen, experimental routines involving crack initiation and propagation within a single specimen at elevated temperatures with plastic-inducing loads and hold periods were conducted. Founded on existing elastic and elastic-plastic fracture mechanics (EPFM), a coupled crack initiation and propagation model is presented. Through the use of the EPFM parameter J, the proposed models are observed to accurately predict crack initiation and replicate crack propagation rates based on the imposed experimental conditions. The model is demonstrated on an austenitic stainless steel, type 304, subjected to moderate temperatures in air. Mechanical testing, metallurgical analysis, and analytical modeling allow for a simplified phenomenological life prediction model capable of predicting crack initiation and propagation at elevated temperatures. Consequently, structural analysis of critical locations of components can span the gamut of crack initiation, crack growth, and instability (i.e., total life assessment) =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCyclic J-integral. =650 \0$aElevated temperature testing. =650 \0$aFatigue crack growth. =650 \0$aFatigue crack initiation. =650 \0$aFatigue. =650 \0$aWork Schedule Tolerance$xpsychology. =650 \0$aWorkload. =650 14$aFatigue crack initiation. =650 24$aCyclic J-integral. =650 24$aElevated temperature testing. =650 24$aFatigue crack growth. =700 1\$aGordon, Ali,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130038.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130026 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130026$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130026$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC685.H8 =082 04$a616.1/32$223 =100 1\$aEvans, Jeffrey,$eauthor. =245 10$aCreep-Fatigue-Environment Crack Tip Kinetics of Ni-Base Superalloys /$cJeffrey Evans. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b15 =520 3\$aSeveral time-dependent damage mechanisms can operate during creep-fatigue loading. In the crack tip region, creep deformation, stress relaxation, oxygen diffusion along grain boundaries, and grain boundary oxidation are all occurring during the hold period of a creep-fatigue cycle. These conditions can lead to grain boundary embrittlement; however, it depends on the rates of the different processes. A comparison of the kinetics can determine which mechanisms are operational and which mechanism is the rate limiting step in the time-dependent damage process during creep-fatigue crack growth. This paper presents results for intergranular embrittlement occurring within a 10 s hold period and compares the kinetics of the processes. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCrack tip. =650 \0$aCreep-fatigue. =650 \0$aOxygen diffusion. =650 \0$aRelaxation. =650 \0$aStress (Psychology)$xPrevention. =650 \0$aStress management. =650 \0$aStress relaxation. =650 \0$aSuperalloys. =650 14$aSuperalloys. =650 24$aCrack tip. =650 24$aCreep-fatigue. =650 24$aOxygen diffusion. =650 24$aStress relaxation. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130026.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130037 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130037$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130037$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA473 =082 04$a620.1/76$223 =100 1\$aGabb, T.,$eauthor. =245 10$aEffects of Long Term Exposures on Fatigue of PM Disk Superalloys /$cT. Gabb, C. Sudbrack, S. Draper, R. MacKay, J. Telesman. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aTurbine disks in some advanced engine applications may be exposed to temperatures above 700°C for extended periods of time, approaching 1000 h. These exposures could affect near-surface composition and microstructure through formation of damaged and often embrittled layers. The creation of such damaged layers could significantly affect local mechanical properties. Powder metal disk superalloys LSHR and ME3 were exposed at temperatures of 704, 760, and 815°C for times up to 2020 h, and the types and depths of environmental attacked were measured. Fatigue tests were performed for selected cases at 704 and 760°C, to determine the impacts of these exposures on properties. Fatigue resistance was reduced up to 98 % in both superalloys for some exposure conditions. The changes in surface composition and phases, depths of these changed layers, failure responses, and failure initiation modes were compared. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aExposure. =650 \0$aFatigue. =650 \0$aMetais. =650 \0$aResidual stresses. =650 \0$aSteel$xFatigue. =650 \0$aSuperalloy. =650 14$aSuperalloy. =650 24$aExposure. =650 24$aFatigue. =700 1\$aDraper, S.,$eauthor. =700 1\$aMacKay, R.,$eauthor. =700 1\$aSudbrack, C.,$eauthor. =700 1\$aTelesman, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 2 Special Issue on High Temperature Fatigue.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130037.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140044 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140044$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140044$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.1/7$223 =100 1\$aGianforcaro, Richard,$eauthor. =245 10$aHigh Cycle Fatigue Behavior of Precipitation Hardened Stainless Steel Alloys in Multiphase Environments /$cRichard Gianforcaro, James Ault. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b8 =520 3\$aStainless steels are often used in marine applications due to their superior corrosion resistance and mechanical properties. However, stainless steels are susceptible to stress corrosion cracking (SCC) and corrosion fatigue. Fatigue occurs when cracks, which initiate as the result of cyclic loading, grow and eventually lead to fracture and component failure. For this reason, it is important to include fatigue in design considerations. Unfortunately, there is little data available for corrosion fatigue in marine environments. Most fatigue studies for materials in marine environments are conducted in aqueous solutions at ambient temperatures. In reality, marine environments can include periods of cyclic wetting and drying and variations in temperature. Furthermore, components often include design parameters that can shorten fatigue life such as crevices and mating surfaces. To better understand the behavior of stainless alloys in realistic marine environments, a series of high cycle fatigue tests were conducted on several alloys. Precipitation hardened and nickel alloys have been tested in environments including ambient air, immersion in solutions of 3.5 % sodium chloride (NaCl), and cyclic wetting environments at both ambient and elevated temperatures. Studies validated the importance of testing alloys in conditions representative of the actual service environment. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBuilding materials. =650 \0$aEngineering design. =650 \0$aFatigue. =650 \0$aHigh cycle fatigue. =650 \0$aImmersion. =650 \0$aMarine. =650 \0$aPrecipitation hardened. =650 \0$aStainless steel. =650 \0$aStress corrosion cracking. =650 14$aFatigue. =650 24$aHigh cycle fatigue. =650 24$aImmersion. =650 24$aMarine. =650 24$aPrecipitation hardened. =650 24$aStainless steel. =650 24$aStress corrosion cracking. =700 1\$aAult, James,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140044.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140017 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140017$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140017$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC100 =082 04$a602/.18 s$223 =100 1\$aSorich, Andreas,$eauthor. =245 10$aFatigue Monitoring of Austenitic Steels with Electromagnetic Acoustic Transducers (EMATs) /$cAndreas Sorich, Marek Smaga, Dietmar Eifler. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b9 =520 3\$aEarly detection of fatigue processes in the cyclically loaded metastable austenitic steel AISI 347 was performed by electromagnetic acoustic transducer measurements in total strain-controlled low-cycle fatigue tests at ambient and elevated temperature. The changes in the physical data were interpreted via microstructural changes observed by scanning- and transmission-electron microscopy, as well as x-ray investigations. The application of physically based measurement data, e.g., time-of-flight from electromagnetically activated ultrasonic signals in austenitic fatigue specimens and total strain, enables measurements of a new hysteresis relationship. In analogy to the common stress-strain hysteresis, this hysteresis gives information about the actual state of fatigue and shows significant changes in shape before specimen failure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAustenite$xStandards. =650 \0$aAustenitic steel$xStandards$zUnited States. =650 \0$aDeformation-induced martensite. =650 \0$aFatigue. =650 \0$aMetastable austenitic steel. =650 \0$aX ray. =650 \0$aX-ray diffractometer$xCalibration. =650 14$aFatigue. =650 24$aDeformation-induced martensite. =650 24$aEBSD. =650 24$aEMAT. =650 24$aMetastable austenitic steel. =650 24$aSEM. =650 24$aTEM. =650 24$aX ray. =700 1\$aEifler, Dietmar,$eauthor. =700 1\$aSmaga, Marek,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140017.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140032 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140032$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140032$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.58 =082 04$a620.1/121$223 =100 1\$aWei, Zhigang,$eauthor. =245 10$aHold-Time Effect on Thermo-Mechanical Fatigue Life and its Implications in Durability Analysis of Components and Systems /$cZhigang Wei, Limin Luo, Burt Lin, Fulun Yang, Dmitri Konson, Kay Ellinghaus, Markus Pieszkalla, Katherine Avery, Jwo Pan, Carlos Engler-Pinto. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b28 =520 3\$aThermo-mechanical fatigue (TMF) resistance of engineering materials is extremely important for the durability and reliability of components and systems subjected to combined thermal and mechanical loadings. However, TMF testing, modeling, simulation, validation, and the subsequent implementation of the findings into product design are challenging tasks because of the difficulties not only in testing but also in results interpretation and in the identification of the deformation and failure mechanisms. Under combined high-temperature and severe mechanical loading conditions, creep and oxidation mechanisms are activated and time-dependent failure mechanisms are superimposed to cycle-dependent fatigue, making the life assessment very complex. In this paper, the testing procedures and results for high-temperature fatigue testing using flat specimens and thermal-fatigue testing using V-shape specimens are reported; emphasis is given to hold-time effects and the possible underlying mechanisms. The uncertainty nature and the probabilistic characteristics of the V-shape specimen test data are also presented. Finally, the impact of hold-time effect on current product design and validation procedure is discussed in terms of virtual life assessment. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aHigh-temperature fatigue. =650 \0$aHold-time effect. =650 \0$aInduction heating. =650 \0$aMaterials$xthermal fatigue. =650 \0$aStrength of materials. =650 \0$aThermal energy. =650 \0$aThermal-fatigue. =650 \0$aV-shape specimen. =650 14$aHigh-temperature fatigue. =650 24$aHold-time effect. =650 24$aInduction heating. =650 24$aThermal-fatigue. =650 24$aV-shape specimen. =700 1\$aAvery, Katherine,$eauthor. =700 1\$aEllinghaus, Kay,$eauthor. =700 1\$aEngler-Pinto, Carlos,$eauthor. =700 1\$aKonson, Dmitri,$eauthor. =700 1\$aLin, Burt,$eauthor. =700 1\$aLuo, Limin,$eauthor. =700 1\$aPan, Jwo,$eauthor. =700 1\$aPieszkalla, Markus,$eauthor. =700 1\$aYang, Fulun,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140032.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130098 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130098$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130098$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA459 =082 04$a620.1/6$223 =100 1\$aLucon, E.,$eauthor. =245 10$aFracture Toughness Characterization of High-Pressure Pipe Girth Welds Using Single-Edge Notched Tension [SE(T)] Specimens /$cE. Lucon, T. Weeks, J. Gianetto, W. Tyson, D. Park. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b12 =520 3\$aThe safety and reliability of large-diameter pipelines for the transport of fluid hydrocarbons is being improved by the development of high-strength steels, advanced weld technologies, and strain-based design (SBD) methodologies. In SBD, a limit is imposed on the applied strains rather than the applied stresses. For high-pressure pipelines, SBD requires an assured strength overmatch for the weld metal as compared to the base material, in order to avoid strain localization in the weldment during service. Achieving the required level of strength overmatch, as well as acceptable ductility and low-temperature fracture toughness, is a challenge as the pipe strength increases. Published studies show that low constraint geometries such as single-edge tension [SE(T)] or shallow-notched single-edge bend [SE(B)] specimens represent a better match to the constraint conditions of surface-breaking circumferential cracks in large-diameter pipelines during service (Shen, G., Bouchard, R., Gianetto, J. A., and Tyson, W. R., “Fracture Toughness Evaluation of High Strength Steel Pipe,” Proceedings of PVP2008, ASME Pressure Vessel and Piping Division Conference, Chicago, IL, July 27-31, ASME, New York, 2008). However, the SE(T) geometry is not included in any of the most widely used elastic-plastic fracture mechanics (EPFM) test standards. A procedure has been developed for performing and analyzing SE(T) toughness tests using a single-specimen technique that includes formulas for calculating the J-integral and crack-tip opening displacement, as well as for estimating crack size using rotation-corrected elastic unloading compliance. Here, crack-resistance curves and critical toughness values obtained from shallow-crack SE(T) specimens (a0/W ? 0.25) are compared to shallow-crack (a0/W ? 0.25) SE(B) specimens. We believe that the SE(T) methodology is mature enough to be considered for inclusion in future revisions of EPFM standards such as ASTM E1820 and ISO 12135, although additional work is needed to establish validity limits for SE(T) specimens. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCrack resistance curves. =650 \0$aElastic compliance. =650 \0$aElastic-plastic fracture toughness. =650 \0$aHigh-strength steels. =650 \0$aLarge-diameter pipelines. =650 \0$aShallow cracks. =650 \0$aStrain-based design. =650 \0$aStrength overmatch. =650 14$aLarge-diameter pipelines. =650 24$aCrack resistance curves. =650 24$aElastic compliance. =650 24$aElastic-plastic fracture toughness. =650 24$aHigh-strength steels. =650 24$aSE(T) specimen. =650 24$aShallow cracks. =650 24$aStrain-based design. =650 24$aStrength overmatch. =700 1\$aGianetto, J.,$eauthor. =700 1\$aPark, D.,$eauthor. =700 1\$aTyson, W.,$eauthor. =700 1\$aWeeks, T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130098.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140037 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1502-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140037$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aU21.2 =082 04$a172/.42$223 =100 1\$aSunder, R.,$eauthor. =245 10$aCharacterization of Threshold Stress Intensity as a Function of Near-Tip Residual Stress :$bTheory, Experiment, and Applications /$cR. Sunder. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (26 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b31 =520 3\$aThreshold stress intensity, ?Kth, is not a material constant, but a variable that is extremely sensitive to load history. This effect has nothing to do with crack closure. It is associated with the influence of near-tip residual stress, ?*, on instantaneous resistance of crack tip surface layers to failure under atmospheric conditions. An analytical procedure is proposed to estimate ?* under constant amplitude loading as well as after tensile or compressive overloads. An experimental procedure is proposed to determine ?Kth under these loading conditions. ?Kth estimates obtained under a variety of overloads and underloads as well as under constant amplitude loading show an excellent correlation with computed ?*. The proposed experimental procedure and analytical relationships appear suitable for adoption as standard practice for an engineering application of threshold stress intensity under variable amplitude loading. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$acrack closure. =650 \0$aresidual stress. =650 \0$athreshold stress intensity. =650 \0$aVariable-amplitude loading. =650 14$aThreshold stress intensity. =650 24$aCrack closure. =650 24$aResidual stress. =650 24$aVariable-amplitude loading. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140037.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140030 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140030$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140030$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA409 =082 04$a620.1/26$223 =100 1\$ade Souza, Rodolfo,$eauthor. =245 10$aRevised ?-Factors and J-CTOD Relationships for SE(B) Fracture Specimens Including 3D Effects and Implications for Fracture Toughness Measurements /$cRodolfo de Souza, Claudio Ruggieri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b36 =520 3\$aThis work provides revised ?-factors derived from CMOD records and J-CTOD relationships applicable to estimate the J-integral and CTOD in SE(B) specimens with varying crack size and specimen configuration. Very detailed non-linear finite element analyses for plane-strain and 3D models provide the evolution of load with increased crack mouth opening displacement, which is required for the estimation procedure. The analysis matrix considers SE(B) specimens with W=2B and W=B configurations with and without side grooves covering a wide range of specimen thickness, including a precracked Charpy (PCVN) specimen. Overall, the present results provide validation of the J and CTOD evaluation procedure currently adopted by ASTM E1820-11, while at the same time giving improved estimation equations for J and CTOD incorporating 3D effects which enter directly into more accurate testing protocols for experimental measurements of fracture toughness values using 3P SE(B) specimens. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFracture mechanics. =650 \0$aJ-integral. =650 \0$aStructural dynamics. =650 14$aJ-integral. =650 24$aCTOD. =650 24$aEta-factor. =650 24$aSE(B) specimen. =700 1\$aRuggieri, Claudio,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140030.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140026 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140026$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140026$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA478 =082 04$a620.17$223 =100 1\$aHassan, Mobbassar Sk,$eauthor. =245 10$aMicrostructurally Mediated Changes in Fracture Characteristics for Electrochemically Hydrogenated 4340 Steel /$cMobbassar Sk Hassan, Ruel Overfelt. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aThe effect of hydrogen on the fracture characteristics of low alloy 4340 steel was studied using double-notched tensile samples electrochemically charged in situ with hydrogen in 1 N H2SO4 + 5 mg/l As2O3 solution. Fracture behaviors of samples with prior austenitic grain sizes of 10 and 40 ?m and martensitic hardness of 43-52 HRC (Rockwell hardness, C scale) were examined after hydrogen charging times of 0-40 min. As expected, increases in hydrogen charging time and hardness resulted in decreased failure strains and decreased evidence of ductile fracture. Harder samples showed predominant intergranular fracture close to the notch and a combination of ductile and flat surfaces away from the notch. Softer samples showed mixed mode intergranular and quasi-cleavage fracture close to the notch and predominant ductile fracture as distance from the notch increased. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aElectrolytic hydrogen charging. =650 \0$aFracture mode change. =650 \0$aHydrogen embrittlement. =650 \0$aHydrogen sulfide$xIndustrial applications. =650 \0$aIntergranular fracture. =650 \0$aPrior austenitic grain size. =650 \0$aQuasi-cleavage. =650 \0$aSteel alloys$xCracking. =650 \0$aSteel alloys$xHydrogen embrittlement. =650 14$aHydrogen embrittlement. =650 24$a4340 steel. =650 24$aElectrolytic hydrogen charging. =650 24$aFracture mode change. =650 24$aIntergranular fracture. =650 24$aPrior austenitic grain size. =650 24$aQuasi-cleavage. =700 1\$aOverfelt, Ruel,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140026.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140029 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140029$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140029$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA690 =082 04$a620.186$223 =100 1\$aJames, M.,$eauthor. =245 10$aTest Development and Materials Characterization Capability for High-Strength Aluminum Alloy Fatigue Crack Growth Response Under Mixed-Mode Loading Conditions /$cM. James, J. Bely, R. Bucci. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aTo meet operational efficiency and productivity demands of the 21st century marketplace, aerospace and transportation sector platforms are being driven to incorporate increasingly larger and more highly stressed unitized structural components. This recent trend has prompted the need for improved fatigue crack growth characterization methodologies to understand impact of relevant mixed-mode loading conditions on crack growth direction and life estimation. This paper describes the development of an Alcoa capability to study and model fatigue crack growth behavior under combined mode I and mode II loading in high-strength aluminum products. The objective is to demonstrate the experimental capability necessary to improve the basic understanding of the roles and synergistic effects of mixed-mode loading (modes I and II) and microstructural resistance, as they relate to fatigue crack growth direction and life estimation. The particular alloy selected for this study is aluminum alloy (AA) 7050-T7651 thick plate taken to be representative of a widely used material for aircraft thick structural parts. The specimens chosen for this capability study are based on the compact tension shear (CTS) specimen documented in the literature. Results are presented to demonstrate the development of stress-intensity factor and compliance solutions to automate the fatigue precracking step. Full-field strain measurements for a notched specimen are used to further validate the finite element analysis. In addition, preliminary results are presented to explore the feasibility of a Keq approach based on total strain-energy release rate to evaluate similitude in the fatigue crack growth rate relationship for the mixed-mode loading case. Preliminary fatigue crack growth test results show that under combined modes I and II loading, the fatigue crack growth rate and direction depend strongly on the competition between the mixed-mode crack-tip driving force and microstructural planes offering the weakest crack growth resistance. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum alloy. =650 \0$aAluminum, Structural. =650 \0$aMixed-mode fatigue-crack growth. =650 \0$auilding materials, Aluminum alloy. =650 14$aMixed-mode fatigue-crack growth. =650 24$aAluminum alloy 7050-T7651. =700 1\$aBely, J.,$eauthor. =700 1\$aBucci, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140029.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140028 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140028$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140028$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.C43 =082 04$a620.14$223 =100 1\$aKalluri, Sreeramesh,$eauthor. =245 10$aMultiaxial and Thermomechanical Fatigue of Materials :$bA Historical Perspective and Some Future ChallengesThis invited manuscript for the ASTM International's Materials Performance and Characterization Journal is based on the Swedlow Memorial Lecture delivered by the author at the 13th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics (39th National Symposium on Fatigue and Fracture Mechanics), held during Nov. 13-15, 2013 in Jacksonville, FL. /$cSreeramesh Kalluri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (34 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b68 =520 3\$aMany engineering components in aircraft gas turbine engines, reusable space propulsion systems, and automotive engines must endure cyclic mechanical forces and deformations in multiple directions and non-isothermal conditions. For the design and safety of such engineering components, durability needs to be estimated with robust multiaxial fatigue life prediction models that are validated under such non-isothermal conditions. In this paper, a historical review is presented on the evolution of uniaxial fatigue (thermal, isothermal, bithermal, and thermomechanical) and isothermal, multiaxial fatigue leading to multiaxial, thermomechanical fatigue with several examples on testing techniques and fatigue life prediction methodologies. The necessity for multiaxial, thermomechanical fatigue testing of structural and engine materials, additional cyclic hardening and reduction in fatigue life observed under such service conditions, and ramifications of estimating multiaxial, thermomechanical fatigue life with isothermal multiaxial fatigue data at the greatest temperature of the cycle are discussed. Finally, some of the potential future challenges associated with experimental characterization of materials and fatigue life estimation under these complex but realistic service conditions are highlighted. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBithermal fatigue. =650 \0$aBuilding Materials. =650 \0$aCeramics, Glass, Composites, Natural Methods. =650 \0$aChemistry. =650 \0$aCyclic hardening. =650 \0$aIsothermal fatigue. =650 \0$aLife prediction. =650 \0$aMultiaxial fatigue. =650 \0$aStructural materials. =650 \0$aThermomechanical fatigue. =650 14$aMultiaxial fatigue. =650 24$aBithermal fatigue. =650 24$aCyclic hardening. =650 24$aIsothermal fatigue. =650 24$aLife prediction. =650 24$aStructural materials. =650 24$aThermomechanical fatigue. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140028.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140018 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140018$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140018$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA462 =082 04$a665.5$223 =100 1\$aPrakash, Raghu,$eauthor. =245 10$aUnderstanding Fatigue Crack Growth Behavior at Low Frequencies for a Mn-Ni-Cr Steel in 3.5 % NaCl Solution Under Controlled Cathodic Potential /$cRaghu Prakash, Sampath Dhinakaran. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b17 =520 3\$aFatigue crack growth behavior at low loading frequencies for a Mn-Ni-Cr steel immersed in 3.5 % NaCl solution, with and without cathodic polarization, is investigated and presented in this paper. Frequency shedding method is used to estimate fatigue crack growth rate over a range of frequencies between 0.01 and 5 Hz at a constant stress intensity factor range of 15 MPa ?m. The effectiveness of cathodic potential of –900 mV SCE in containing corrosion contribution to crack growth is estimated by comparing with published data on fatigue crack growth rate in lab air and 3.5 % NaCl solution without cathodic polarization. It is noted that there are three regions of crack growth rate as a function of applied frequencies when the data is plotted in log-log scale: linear crack growth rate, plateau crack growth rate, and high crack growth rate. The crack growth rate of steel in 3.5 % NaCl solution at 15 MPa ?m is scanned for different cathodic potentials between –760 mV SCE and 1150 mV SCE at 0.01 and 0.1 Hz. The potentials at which the crack growth rates are the maximum and the minimum are found to be –760 and –950 mV, respectively. The optimum cathodic protection potential for the minimum corrosion fatigue crack growth rate ranges between –900 and –950 mV. This optimum potential for the minimum corrosion crack growth rate is more negative than the cathodic potential required for restraining the corrosion effects on fatigue strength of steel to normal ambient air behavior. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCathodic polarization. =650 \0$aChemical engineering. =650 \0$aCivil engineering. =650 \0$aCorrosion fatigue. =650 \0$aCrack growth. =650 \0$aFrequency shedding. =650 \0$aMetals$xCorrosion fatigue. =650 \0$aMn-Ni-Cr steel. =650 14$aCorrosion fatigue. =650 24$a3.5 % NaCl solution. =650 24$aCathodic polarization. =650 24$aCrack growth. =650 24$aFrequency shedding. =650 24$aMn-Ni-Cr steel. =700 1\$aDhinakaran, Sampath,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140018.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140031 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140031$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140031$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC377 =082 04$a616.8/34$223 =100 1\$aBorz, Meghan,$eauthor. =245 10$aFatigue Crack Growth from Compression Pre-Cracks /$cMeghan Borz, Michael Chadwick, Andrew Branin, William Riddell. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aThe compression pre-crack method can be used to develop near-threshold fatigue crack growth rates much quicker than the ASTM standard load shed method. The compression pre-crack method is faster than the standard method and eliminates load history effects that are of concern when the standard method is used. However, crack growth developed using the compression pre-cracking approach is susceptible to different load history effects. A suite of tests using the compression pre-crack method that were performed on AISI 9310 steel are presented in this paper. An approach for identifying the critical crack growth increments required to develop valid data is presented, and the effects of three potential mechanisms are evaluated. For these tests, the residual stress field resulting from the initial compression field appears to be the more important effect on crack growth behavior. Crack growth increments measured from the notch tip that are 2.5 times larger than the size of the plastic zone resulting from the compression pre-cracking are required in order to develop valid data on the fatigue crack growth rate. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCompression pre-crack. =650 \0$aFatigue. =650 \0$aMultiple sclerosis$xExercise therapy. =650 \0$aMultiple sclerosis. =650 \0$aThreshold. =650 14$aCompression pre-crack. =650 24$aFatigue. =650 24$aThreshold. =700 1\$aBranin, Andrew,$eauthor. =700 1\$aChadwick, Michael,$eauthor. =700 1\$aRiddell, William,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140031.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140033 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140033$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140033$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aPZ4.M379 =082 04$a823.914$223 =100 1\$aBeretta, Stefano,$eauthor. =245 10$aLoad Interaction Effects in a Medium Strength Steel for Railway Axles /$cStefano Beretta, Michele Carboni, Daniele Regazzi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b28 =520 3\$aAs is well known, an interaction effect arises on crack propagation when a specimen or a component is subjected to variable amplitude fatigue loading. Depending on the applied load sequence, a certain amount of retardation or acceleration can then be observed, on the fatigue crack growth rate, with respect to the constant amplitude case. In the case of structural ductile materials, the interaction phenomenon is mainly addressed by the local plasticity at the crack tip and can be explained, from a global point of view, by adopting the crack closure concept. From this point of view, in the present research, load interaction effects in a medium strength steel for railway axles are analyzed. An experimental campaign was carried on this material, using SE(T) specimens, in order to understand and quantify the interaction effects arising from relevant load sequences derived from service. The experimental outcomes were then modeled adopting both a simple no-interaction approach and a more sophisticated strip-yield model in order to quantify the possible interaction effects. The modeling was carried out considering different experimental techniques for deriving the crack growth and threshold behaviors of the material, i.e., the traditional ?K-decreasing technique and the compression pre-cracking one. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCompression pre-cracking. =650 \0$aCrack propagation. =650 \0$aRailroad travel. =650 \0$aRailway axles. =650 \0$aRailway mail service. =650 \0$aTrain robberies. =650 \0$aVariable amplitude loading. =650 14$aCrack propagation. =650 24$aCompression pre-cracking. =650 24$aEA4T steel. =650 24$aRailway axles. =650 24$aVariable amplitude loading. =700 1\$aCarboni, Michele,$eauthor. =700 1\$aRegazzi, Daniele,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140033.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140011 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140011$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140011$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.52 =082 04$a620.1/1296$223 =100 1\$aBrueckner-Foit, A.,$eauthor. =245 10$aExtension of Fatigue Cracks in a Low-Alloy Steel After Massive Plastic Deformation /$cA. Brueckner-Foit, M. Besel, T. Stein, F. Zeismann. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b9 =520 3\$aFatigue crack extension was studied in a ferritic-pearlitic steel in two different material conditions. The first one was the virgin state with a typical pearlitic microstructure containing comparatively large stacks of cementite lamellae. The second material contained predominantly globular cementite and stacks of very fine cementite lamellae and was found after massive plastic deformation during a thermo-mechanical forming process. These differences in the microstructure lead to significantly different mechanisms in the damage accumulation process under fatigue loading. Stacks of cementite lamellae pearlite were both crack initiation sites and microstructural barriers for small cracks in the virgin material, whereas the fine lamellae in the plastically deformed (cold-worked) material could cause crack deviation, but no crack initiation and no significant crack arrest or crack retardation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCrack path. =650 \0$aFatigue crack. =650 \0$aFerritic-pearlitic steel. =650 \0$aMaterials$xThermal properties. =650 \0$aMicrostructure. =650 \0$aThermodynamics. =650 14$aFatigue crack. =650 24$aCrack path. =650 24$aFerritic-pearlitic steel. =650 24$aMicrostructure. =700 1\$aBesel, M.,$eauthor. =700 1\$aStein, T.,$eauthor. =700 1\$aZeismann, F.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140011.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140041 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140041$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140041$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA459 =082 04$a620.1623$223 =100 1\$aGupta, Vipul,$eauthor. =245 10$aMicrostructure-Scale In-Situ Image Correlation-Based Study of Grain Deformation and Crack Tip Displacements in Al-Cu Alloys /$cVipul Gupta, Scott Willard, Jacob Hochhalter, Stephen Smith. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (27 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b60 =520 3\$aMechanistic understanding based on experimental measurements of grain and crack tip deformation at relevant length scales is critical for improvement of physics-based modeling of microstructurally-sensitive fatigue crack propagation and for the computationally-assisted design of more durable materials. In this study, single-crystal, bi-crystal, and large-grain multi-crystal specimens of Al-Cu alloys are fabricated, characterized using electron backscattered diffraction (EBSD), and mechanically tested. In addition to conventional optic al-imaging based 3D image correlation (IC), scanning electron microscope (SEM) based high-resolution 2D IC is used to measure displacements within grain interiors, near crack tips, and grain boundaries. The use of micro-scale IC and EBSD-based experiments is discussed as they relate to the development of crystal-plasticity-based finite element models (CP-FEMs). This article specifically highlights experimental methods that have been developed to obtain the relevant data needed for CP-FEM calibration and validation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAlloys$xCorrosion. =650 \0$aAluminum-copper alloy. =650 \0$aCorrosion and anti-corrosives. =650 \0$aCrack closure. =650 \0$aCrystal plasticity. =650 \0$aElectron backscattered diffraction. =650 \0$aFatigue crack growth. =650 \0$aImage correlation. =650 \0$aStrain localization. =650 14$aStrain localization. =650 24$aAluminum-copper alloy. =650 24$aCrack closure. =650 24$aCrystal plasticity. =650 24$aElectron backscattered diffraction. =650 24$aFatigue crack growth. =650 24$aImage correlation. =700 1\$aHochhalter, Jacob,$eauthor. =700 1\$aSmith, Stephen,$eauthor. =700 1\$aWillard, Scott,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140041.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140027 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140027$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140027$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHV5278 =082 04$a362.29/886$223 =100 1\$aDing, Ping,$eauthor. =245 10$aElastic-Plastic Finite Element Analyses of 3D Constraint Effects in Single Edge Cracked Plate Specimens /$cPing Ding, Xin Wang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b20 =520 3\$aExtensive finite element analyses have been conducted to obtain numerical solutions of the constraint parameter A, which is the second parameter in a three-term elastic-plastic asymptotic expansion for the crack-tip field for thin three-dimensional (3D) single edge cracked plate specimens under uniaxial and biaxial loading. The 3D crack geometries analyzed included shallow to deep cracks, and the biaxial loading ratios analyzed were 0.0 (uniaxial loading) and 1.0 (biaxial loading). Solutions for the parameter A were obtained for materials following the Ramberg-Osgood power law with hardening exponents of n = 3, 5, and 10. Remote tension loading was applied covering the deformation range from small-scale to large-scale yielding. Crack-front constraint effects for 3D cracked specimens under uniaxial and biaxial loading are analyzed and discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAddicts$xRehabilitation. =650 \0$aCocaine abuse. =650 \0$aConstraint parameter. =650 \0$aElastic-plastic fracture. =650 \0$aSolutions. =650 \0$aUniaxial and biaxial loading. =650 14$aElastic-plastic fracture. =650 24$a3D constraint effect. =650 24$a3D crack. =650 24$aConstraint parameter. =650 24$aSolutions. =650 24$aUniaxial and biaxial loading. =700 1\$aWang, Xin,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140027.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140025 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140025$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140025$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC377 =082 04$a616.8/34$223 =100 1\$aCarpinteri, Andrea,$eauthor. =245 10$aAnalysis of Cracked and Notched Round Bars Under Rotary Bending /$cAndrea Carpinteri, Camilla Ronchei, Sabrina Vantadori. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aThe fatigue growth of surface flaws in both smooth and notched round bars subjected to rotary bending was numerically simulated by means of a two-parameter theoretical model proposed by the first author. The stress intensity factor distribution along the crack front was needed in order to apply the model. Therefore, finite element analyses and the superposition principle were used to determine such a distribution for a wide range of crack configurations and any position of the flaw with respect to the bending moment axis. The results related to rotary bending are compared to those related to pulsating cyclic bending, and a qualitative comparison is made with some data reported in the literature. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFatigue. =650 \0$aMultiple sclerosis$xExercise therapy. =650 \0$aMultiple sclerosis. =650 \0$aNotched round bars. =650 \0$aRotary bending. =650 14$aFatigue. =650 24$aNotched round bars. =650 24$aRotary bending. =700 1\$aRonchei, Camilla,$eauthor. =700 1\$aVantadori, Sabrina,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140025.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140036 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20140036$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140036$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC377 =082 04$a616.8/34$223 =100 1\$aFoletti, S.,$eauthor. =245 10$aFatigue Crack Growth in Blade Attachment of Turbine Disks :$bExperimental Tests and Life Prediction /$cS. Foletti, S. Beretta, F. Scaccabarozzi, S. Rabbolini, L. Traversone. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b27 =520 3\$aTo assess residual life for those component parts where low cycle fatigue (LCF) design is adopted, especially for those critical regions where high stress concentrations cause cyclic yielding of the material, it is necessary to consider the presence of potential defects and their propagation during service. In order to represent the high stress concentration at the root of blade attachments in a gas turbine and the typical elastic-shakedown conditions, a notched specimen has been designed and tested. A series of experimental tests in three regimes have been carried out with the presence of small semi-circular micronotches and crack growth rates have been measured with plastic replicas. The results have shown that the initial over-load impressed by the spinning tests is able to double the propagation lifetime. The experimental results have then been successfully analyzed with Newman's crack growth model applied to the elastic shakedown stress fields at the notch root. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aGrowth rate. =650 \0$aMultiple sclerosis$xExercise therapy. =650 \0$aMultiple sclerosis. =650 \0$aNotches. =650 \0$aSmall cracks. =650 14$aSmall cracks. =650 24$aGrowth rate. =650 24$aLCF. =650 24$aNotches. =700 1\$aBeretta, S.,$eauthor. =700 1\$aRabbolini, S.,$eauthor. =700 1\$aScaccabarozzi, F.,$eauthor. =700 1\$aTraversone, L.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140036.htm =LDR 03762nab 2200553 i 4500 =001 MPC104374 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104374$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104374$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA347.F5 =082 04$a620.00151825$223 =100 1\$aSchwenk, Maximilian,$eauthor. =245 10$aProcess Simulation of Single and Dual Frequency Induction Surface Hardening Considering Magnetic Nonlinearity /$cMaximilian Schwenk, Martin Fisk, Tord Cedell, Jürgen Hoffmeister, Volker Schulze, Lars-Erik Lindgren. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b26 =520 3\$aA 2D computational model of single and simultaneous dual frequency induction hardening has been developed. Process specific aspects such as the nonlinear magnetic material behavior and phase transformation kinetics of quenched and tempered AISI 4140 are considered. Induction surface hardening experiments have been conducted for validation purposes. The measuring methodologies used to extract input data such as the magnetic material behavior, the current, and the effective heating time are presented. Metallurgical characterization and hardness profiles are compared with the results obtained from simulations. The temperature history, hardness depth profile, and hardness distribution are in good agreement. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFinite element analysis. =650 \0$aFinite element method. =650 \0$aHysteresis curve. =650 \0$aInduction hardening. =650 \0$aProcess simulation. =650 14$aInduction hardening. =650 24$aFinite element analysis. =650 24$aHysteresis curve. =650 24$aProcess simulation. =700 1\$aCedell, Tord,$eauthor. =700 1\$aFisk, Martin,$eauthor. =700 1\$aHoffmeister, Jürgen,$eauthor. =700 1\$aLindgren, Lars-Erik,$eauthor. =700 1\$aSchulze, Volker,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104374.htm =LDR 03762nab 2200553 i 4500 =001 MPC104382 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104382$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104382$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN697.A47 =082 04$a669.722$223 =100 1\$aAhlström, Johan,$eauthor. =245 10$aModeling of Distortion during Casting and Machining of Aluminum Engine Blocks With Cast-in Gray Iron Liners /$cJohan Ahlström, Ragnar Larsson. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b5 =520 3\$aA method for quantifying distortions arising in engine blocks of aluminum with liners of gray iron has been developed based on virtual finite element-based simulation tools. The key processing steps comprise the convection cooling step, associated with shrinkage and residual stress build-up, and the machining step. The engine block has been modeled using the finite element method and machining has been simulated using the element-removal technique. The mechanical behavior of aluminum has been characterized by tensile tests at different temperatures and strain rates. The results were used for calibration of a material model capturing the viscoplastic behavior at higher temperatures. Finally, to illustrate the key process steps, results from a complete process analysis are reported comprising the initial stress build-up during cooling and the initial out-of-roundness and out-of-roundness of the liners after various machining operations. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum alloys. =650 \0$aAluminum$xMetallurgy. =650 \0$aDistortion. =650 \0$aFE-simulation. =650 \0$aMechanical alloying. =650 \0$aOut-of-roundness. =650 \0$aProcess simulation. =650 \0$aResidual stresses. =650 14$aProcess simulation. =650 24$aDistortion. =650 24$aFE-simulation. =650 24$aOut-of-roundness. =650 24$aResidual stresses. =700 1\$aLarsson, Ragnar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104382.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120006 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120006$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120006$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA478 =082 04$a620.17$223 =100 1\$aLuo, Xinmin,$eauthor. =245 10$aFast Primary Cooling :$bAlternative to Lead Baths for High-Carbon Steel Wire Patenting /$cXinmin Luo, Kangmin Chen, George Totten. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b32 =520 3\$aUsing non-toxic cooling media for patenting high-carbon steel wire is of industrial importance in view of current regulations related to human toxicity and environmental pollution problems presented by conventional molten lead bath patenting processes. The cooling behavior of 0.70 % carbon steel wire upon patenting using a lead bath and aqueous solutions of CMC (carboxyl methyl cellulose) polymer were investigated previously. The cooling process and the transformation behavior of the wire were interpreted using curve analyses. The experimental results showed that the high-carbon steel wire can complete the sorbite-pearlite transformation in the aqueous 0.25 % CMC solution, but the transformation temperature is higher and the transformation time is longer than that observed for lead patenting because of the continuous cooling transformation process in the fluid used as an alternative to molten lead. In accordance with the cooling requirement of the patenting process and the cooling characteristics of aqueous polymer solutions, a key point in the adoption of alternatives to molten lead is that the cooling process should be controlled to accelerate the cooling rate during the primary cooling stage and maintain the steady transformation temperature for austenitized steel wires. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCarbon steel$xCracking. =650 \0$aCarbon steel$xHydrogen embrittlement. =650 \0$aCatalytic cracking. =650 \0$aCMC polymer. =650 \0$aCooling curve. =650 \0$aHigh-carbon steel wire. =650 \0$aLead bath. =650 \0$aPatenting. =650 \0$aPhase transformation. =650 14$aHigh-carbon steel wire. =650 24$aCMC polymer. =650 24$aCooling curve. =650 24$aLead bath. =650 24$aPatenting. =650 24$aPhase transformation. =700 1\$aChen, Kangmin,$eauthor. =700 1\$aTotten, George,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120006.htm =LDR 03762nab 2200553 i 4500 =001 MPC104384 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104384$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104384$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN719.5 =082 04$a669.1413$223 =100 1\$aVázquez-Gómez, O.,$eauthor. =245 10$aMathematical Model of Thermal and Microstructural Evolution during Austempering of Ductile Iron /$cO. Vázquez-Gómez, J. Barrera-Godínez, B. Hernández-Morales, H. Vergara-Hernández, E. López-Martínez. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b30 =520 3\$aAustempering of ductile iron is a heat treating process designed to improve the mechanical properties of ductile iron: Increasing its strength and wear resistance while maintaining the tenacity and ductility associated with the untreated condition. This task is achieved by rapidly cooling the part from the austenitizing temperature to the austempering temperature and holding it during a specific time. Austempering promotes the formation of an ausferrite matrix, i.e., a mixture of bainitic ferrite and retained austenite, along with graphite nodules. In order to achieve the required microstructural control, a detailed knowledge of the phase transformation evolution coupled with a heat transfer analysis is required. Thus a thermostructural model has been developed to simulate the phase transformations during austempering of a ductile iron cylindrical probe. The thermal and microstructural submodels were coupled within the Abaqus software. The predictions were validated by austempering ductile iron probes from an austenitizing temperature of 920°C to an austempering temperature of 300°C in a molten salt bath and comparing predictions versus experimental data. It was concluded that the model is suitable to predict the thermal behavior and the final microstructure of the austempered ductile iron. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDuctile iron. =650 \0$aFundicao. =650 \0$aIron, Nodular. =650 \0$aModeling. =650 \0$aThermostructural. =650 14$aADI. =650 24$aModeling. =650 24$aThermostructural. =700 1\$aBarrera-Godínez, J.,$eauthor. =700 1\$aHernández-Morales, B.,$eauthor. =700 1\$aLópez-Martínez, E.,$eauthor. =700 1\$aVergara-Hernández, H.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104384.htm =LDR 03762nab 2200553 i 4500 =001 MPC104376 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104376$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104376$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ246 =082 04$a621.8/85$223 =100 1\$aKoundé, Ludovic,$eauthor. =245 10$aThermo-mechanical Modeling of Laser-MAG Hybrid Welding and Consequences on Large Structure /$cLudovic Koundé, Thierry Engel, Jean-Michel Bergheau, Didier Boisselier. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aWelding induces local residual stress and strain in workpiece joining. These local phenomena lead to distortions in the workpieces and aspect defaults. The consequence is aspect defaults (distortions), which can be corrected by heating and hammering. When the assembled elements have large dimensions and need many joints executed by welding sequences, the aspect defaults can be created by non-optimized sequences. The focus of this study is the optimization of joint sequences (through the numerical simulation of sequences) to minimize distortions induced in wall train shell car manufacturing. The parts are assembled with hybrid laser-MAG welding technology. The metallurgical transformations of the material microstructure are taken into account. A new analytical function called “diaboloïd” has been developed to reproduce the morphology of the molten zone and the heat affected zone created by the laser welding. This analytical function is associated with the double ellipsoid analytical function in order to model the laser-arc hybrid welding process. The material thermo-physical properties according to temperature and phase transformation are taken into account in the numerical model. Experimental measurements (cooling rate, residual stresses) have been done in order to correlate numerical and experimental results. The effects of clamping conditions and tack welds are also considered in the numerical model. All these developments made it possible to reduce the displacement of large structures by a factor of 5. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aClamping conditions. =650 \0$aGlobal model. =650 \0$aLaser-arc hybrid welding. =650 \0$aLocal model. =650 \0$aMorphology of fusion zone. =650 \0$aSealing (Technology) =650 \0$aWelding. =650 14$aLaser-arc hybrid welding. =650 24$aClamping conditions. =650 24$aGlobal model. =650 24$aLocal model. =650 24$aMorphology of fusion zone. =650 24$aTack weld. =700 1\$aBergheau, Jean-Michel,$eauthor. =700 1\$aBoisselier, Didier,$eauthor. =700 1\$aEngel, Thierry,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104376.htm =LDR 03762nab 2200553 i 4500 =001 MPC104397 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104397$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104397$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA347.F5 =082 04$a620.00151825$223 =100 1\$aLi, Zhichao (Charlie),$eauthor. =245 10$aOptimization of an Induction Hardening Process for a Steel Gear Component /$cZhichao (Charlie) Li, B. Ferguson. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b11 =520 3\$aComputer simulation of heat treatment processes has improved significantly over the past two decades, relating to both the material models and the database accuracy. Simulations are being used more aggressively in part and process design rather than just as a trouble shooting agent, meaning heat treat simulation is maturing as an accepted technology. In this paper, an induction heating and spray quenching process of a steel gear is optimized using the commercial heat treatment software DANTE. As a hardening process, induction hardening of steel parts is gaining popularity due to: (1) the process is consistent on a part-to-part basis, making it easier for quality control; (2) the process is more environmentally friendly than oil or polymer immersion quenching because a water spray is the typical cooling agent; and (3) fatigue life can be improved due to higher and deeper residual compression in the hardened surface. Two steel grades, AISI 5120 and AISI 5130, may be used in a thin-walled spur gear. The simplified heat treatment process includes vacuum carburization, controlled cooling to ambient, induction heating, and spray quenching. During induction heating, the internal heat generated by eddy currents is used as direct input to drive the thermal model. A sensitivity based optimization method is combined with heat treatment simulation to optimize the delay and spray quenching practice after induction heating. The objective function is defined to minimize the distortion of the gear tooth while satisfying the residual stress, gear surface temperature, and final microstructure requirements. The results of a two-dimensional (2D) plane strain single tooth model are evaluated during the optimization process, the quenching practice variables are adjusted, and the quenching model is re-run until the optimization function is satisfied. The residual stresses predicted after induction hardening are then mapped to a three-dimensional (3D) whole gear model as the initial stress state of a tooth loading model for predicting gear stresses. The significant effect on fatigue behavior due to residual stresses from heat treatment is addressed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDistortion. =650 \0$aFinite element method. =650 \0$aInduction hardening. =650 \0$aOptimization. =650 \0$aPhase transformation. =650 \0$aResidual stress. =650 14$aInduction hardening. =650 24$aDistortion. =650 24$aFinite element method. =650 24$aOptimization. =650 24$aPhase transformation. =650 24$aResidual stress. =700 1\$aFerguson, B.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104397.htm =LDR 03762nab 2200553 i 4500 =001 MPC104351 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104351$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104351$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTT298 =082 04$a748.2028$223 =100 1\$aHai Do, Duc,$eauthor. =245 10$aMeasurement and Simulation of Lime Calcination in Normal Shaft Kiln /$cDuc Hai Do, Eckehard Specht. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aThis article presents a one-dimensional mathematical model to simulate the lime-burning process in normal shaft kilns. The model comprises ordinary differential equations derived from the principal conservations of mass and energy. A shrinking core approach is employed to describe the mechanisms and to calculate the decomposition rate of limestone particles. The model is used to simulate the temperature of the gas and the solid, the lime-burning degree, the pressure drop, and the heat loss by kiln shell. Operating conditions, such as kiln throughput, energy consumption, and stone size, are also investigated by the model. Experiments were carried out to measure temperatures in industrial kilns. Maximum temperatures were observed in the region of 1.0-2.0 m above the burner level. The kiln temperature is about 1600°C. Comparisons of the experiments and simulations show that the temperatures measured in the kilns are very close to the solid temperatures predicted by simulations. The results of simulations and those of experiments are in good agreement. The results of this study can be direct utility for the regulation and optimization of industrial lime shaft kilns. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aGlass blowing and working. =650 \0$aGlass craft. =650 \0$aKiln-formed glass. =650 \0$aLime calcination. =650 \0$aMeasurement and simulation. =650 \0$aTemperature profile. =650 14$aShaft kiln. =650 24$aLime calcination. =650 24$aMeasurement and simulation. =650 24$aTemperature profile. =700 1\$aSpecht, Eckehard,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104351.htm =LDR 03762nab 2200553 i 4500 =001 MPC104359 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104359$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104359$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA465 =082 04$a620.1/76$223 =100 1\$aLi, Huiping,$eauthor. =245 10$aOptimization of Heat Treatment Parameters of Boron Steel B1500HS Using Response Surface Methodology /$cHuiping Li, Lianfang He, Guoqun Zhao, Lei Zhang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aHeat treatment parameters play important roles in hot stamping of boron steel. In order to optimize the heat treatment parameters of boron steel B1500HS, aResponse Surface Methodology (RSM) with two-factor and five-level experimental project is used, and austenitizing temperature and holding time are the two factors in the experimental project. The heat treatment experiments are performed according to the designed results. The hardness, tensile strength, and ductility of cooled specimens are measured using the Rockwell hardness tester and the tensile testing machine. According to the measuring results and experimental project, the cubic response surface models of hardness, tensile strength, and ductility are gained using the regression method. The austenitizing temperature and holding time are optimized according to the cubic response surface model. The results of parameter optimization show that, when the austenitizing temperature is in the range of 916°C-921°C and holding time is 0 min, with steel die cooling, the cooled parts of B1500HS have the properties of high tensile strength, good abrasion resistance, and energy absorption performance. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCooling. =650 \0$aHeat treatment. =650 \0$aParameter optimization. =650 \0$aResponse surface methodology. =650 \0$aSteel$xFracture. =650 \0$aSteel$xHeat treatment. =650 14$aHeat treatment. =650 24$aCooling. =650 24$aParameter optimization. =650 24$aResponse surface methodology. =700 1\$aHe, Lianfang,$eauthor. =700 1\$aZhang, Lei,$eauthor. =700 1\$aZhao, Guoqun,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104359.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120022 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120022$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120022$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK4058 =082 04$a621.46$223 =100 1\$aHamdoon, Muhsin,$eauthor. =245 10$aEffect of Cyclic Strain on Mechanical Behavior of Structural Steels in Room and Low Temperatures /$cMuhsin Hamdoon, Sreekanta Das, Nader Zamani. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aThe mechanical behavior of fatigue damaged material is expected to differ from that of damage free ones. In this study, three different load histories were applied on round specimens made of AISI 1022 HR and CSA G40.21 350WT steels. Axial loading was applied using a strain controlled mode to determine the effect of cyclic strain on the linear-nonlinear behavior of steels. The experimental results show a significant effect of strain cycles on the linear-nonlinear behavior of steels used in this study. The hysteresis indicates stress relaxation for all loading histories. However, rates of stress relaxation were different depending on the applied mean strain value. Furthermore, specimens tested at low temperatures exhibited different linear-nonlinear behavior than those tested at room temperature. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aChaotic behavior in systems. =650 \0$aCyclic softening. =650 \0$aElectric driving$xAutomatic control. =650 \0$aMechanical behavior. =650 \0$aNonlinearity. =650 \0$aStrain hardening. =650 \0$aTensile properties. =650 14$aMechanical behavior. =650 24$aCyclic softening. =650 24$aNonlinearity. =650 24$aStrain hardening. =650 24$aTensile properties. =700 1\$aDas, Sreekanta,$eauthor. =700 1\$aZamani, Nader,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120022.htm =LDR 03762nab 2200553 i 4500 =001 MPC104533 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104533$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104533$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.Q4 =082 04$a672.36$223 =100 1\$aKobasko, N.,$eauthor. =245 10$aLocal Film Boiling and Its Impact on Distortion of Spur Gears During Batch Quenching /$cN. Kobasko, M. Aronov, B. Ferguson, Z. Li. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b10 =520 3\$aThe paper discusses results of computer simulation connected with the double distortion during batch quenching of spur gears caused by a local film boiling between teeth. A carburized gear, outside diameter 2.5 in., was intensively quenched in conditions that provided heat transfer coefficient (HTC) equal to 25 000 Wm–2K–1. In some places between teeth local film boiling took place where HTC was 800 Wm–2K–1. Computer simulation showed that maximum displacement is observed between teeth where local film boiling took place. The authors came to the conclusion that increasing critical heat flux densities and elimination of local film boiling can result in decreasing distortion of spur gear. That is true for different sizes of gear during their quenching when using the second type of intensive quenching process (IQ-2) technique (a two or three-step quenching process). It is underlined that critical heat flux densities have a great effect on distortion during batch quenching. The authors also came to the conclusion that a small amount of special additives can decrease significantly distortion during quenching of gears. That is why a global database on cooling capacity of quenchants should be available which must contain critical heat flux densities of different kinds of quenchants. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAdditives. =650 \0$aComputer simulation. =650 \0$aCritical heat flux density. =650 \0$aDisplacement. =650 \0$aIQ-2 process. =650 \0$aLocal film boiling. =650 \0$aMetals$xHardenability. =650 \0$aMetals$xHeat treatment. =650 \0$aMetals$xQuenching. =650 \0$aOptimization. =650 \0$aSpur gear. =650 14$aComputer simulation. =650 24$aAdditives. =650 24$aCritical heat flux density. =650 24$aDisplacement. =650 24$aIQ-2 process. =650 24$aLocal film boiling. =650 24$aOptimization. =650 24$aSpur gear. =700 1\$aAronov, M.,$eauthor. =700 1\$aFerguson, B.,$eauthor. =700 1\$aLi, Z.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104533.htm =LDR 03762nab 2200553 i 4500 =001 MPC104541 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104541$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104541$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP810.5 =082 04$a620.1/4$223 =100 1\$aKanematsu, Wataru,$eauthor. =245 10$aCrack Propagation Behavior of Silicon Nitride Using a Ball-on-Flat Rolling Fatigue Bench Test Methodology /$cWataru Kanematsu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aCrack propagation behavior prior to flaking in rolling contact fatigue (RCF) tests has been analyzed by microscopic observation to gain insight into the mechanism for final spall of specimen. Balls-on-flat RCF tests under constant and stepwise load were carried out for three bearing grade silicon nitrides and one general purpose one at several stress levels. Detailed observations of crack propagation on a contact track during tests under constant load reveal that a linear crack, which shows up just outside of the track, grows at both ends of the crack with an increase in stress cycles. This growth, opposite to the rolling direction, eventually leads to the formation of hook-like cracks. Immediately before spalling, a major hook-like crack and associated arc-like cracks are formed. From the surface and section views of spalled regions of the specimens tested under stepwise load, we found supporting evidence for the hypothesis that major crack growth inclined toward the rolling direction forming at the bottom surface of the spall, with subsequent upward crack growths from the major crack and associated arc-like ones on the specimen surface, eventually developing into a crack network leading to the dislodging of fragments. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBalls-on-flat. =650 \0$aCeramics. =650 \0$aConstant loading. =650 \0$aMean effective load. =650 \0$aNanosilicon. =650 \0$aRolling contact fatigue. =650 \0$aSilicon nitride. =650 \0$aSpall. =650 \0$aStepwise loading. =650 14$aRolling contact fatigue. =650 24$aBalls-on-flat. =650 24$aConstant loading. =650 24$aMean effective load. =650 24$aSilicon nitride. =650 24$aSpall. =650 24$aStepwise loading. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104541.htm =LDR 03762nab 2200553 i 4500 =001 MPC104556 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104556$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104556$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA465 =082 04$a620.1/76$223 =100 1\$aSimsir, Caner,$eauthor. =245 10$aAnisotropic Transformation Strain and Its Consequences on Distortion during Austenitization /$cCaner Simsir, Thomas Lübben, Martin Hunkel, Franz Hoffmann, Hans-Werner Zoch. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b33 =520 3\$aThe distribution of segregations, which is introduced in the continuous casting process and modified during succeeding manufacturing steps, is considered as an important “distortion potential carrier” for chemically banded steels. This article presents a recently developed mathematical model for integration of the effect of prior forming and cutting operations into heat-treatment simulations by considering “anisotropic transformation strain (ATS).” The model was justified experimentally by simulating the heating and austenitization of dilatometer specimens machined from the forged discs with distinct orientations with respect to the banded microstructure. After the verification, it is used in conjunction with former experimental work to demonstrate that the distribution of fiber flow is one of the important reasons of the dishing of carburized discs. The model provides promising results for process chain simulation to predict the heat-treatment distortion that cannot be predicted with currently available models. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAnisotropic transformation strain. =650 \0$aDistortion. =650 \0$aHeat-treatment simulation. =650 \0$aProcess chain simulation. =650 \0$aSteel$xFracture. =650 \0$aSteel$xHeat treatment. =650 14$aAnisotropic transformation strain. =650 24$aDistortion. =650 24$aHeat-treatment simulation. =650 24$aProcess chain simulation. =650 24$aSAE 5120. =700 1\$aHoffmann, Franz,$eauthor. =700 1\$aHunkel, Martin,$eauthor. =700 1\$aLübben, Thomas,$eauthor. =700 1\$aZoch, Hans-Werner,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104556.htm =LDR 03762nab 2200553 i 4500 =001 MPC104479 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104479$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104479$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.Q4 =082 04$a672.36$223 =100 1\$aGür, C.,$eauthor. =245 10$aSimulation of Quenching :$bA Review /$cC. Gür, Caner Simsir. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (37 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b226 =520 3\$aQuenching is an important part of the production chain of steel components. The final properties of the product are largely determined during this stage, and this renders quenching as one of the most critical stages of production, requiring design and optimization specific to the product. The simulation of quenching requires the solution of a multi-scale/multi-physics problem with complex boundary conditions because of the simultaneously occurring heat transfer, phase transformation, and mechanical interactions. The aim of this paper is to provide an updated review of research studies on the simulation of quenching. The subject is covered from the pioneering work up to very recent advances in the field, with special emphasis on future research needs for improving the industrial usage of heat treatment simulations. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDistortion. =650 \0$aMetals$xHardenability. =650 \0$aMetals$xHeat treatment. =650 \0$aMetals$xQuenching. =650 \0$aMicrostructure. =650 \0$aQuenching. =650 \0$aResidual stress. =650 \0$aSimulation. =650 14$aQuenching. =650 24$aDistortion. =650 24$aMicrostructure. =650 24$aResidual stress. =650 24$aSimulation. =700 1\$aSimsir, Caner,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104479.htm =LDR 03762nab 2200553 i 4500 =001 MPC103926 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC103926$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC103926$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD9705.5.B434 =082 04$a338.7/669142/0973$223 =100 1\$aDong, J.,$eauthor. =245 10$aInfluence of CO or CO2 as Carbon Donator on the Development of the Compound Layer during Nitrocarburizing of Alloyed Steels /$cJ. Dong, F. Hoffmann, H. Kluemper-Westkamp, Hans Zoch. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b20 =520 3\$aGaseous nitrocarburizing improves wear and corrosion resistance of machine components. This is primarily based on the compound layer that consists of carbonitrides. The composition and the porosity of the compound layer are the principal influencing factors of the properties of the surface layer. They are influenced by the nitriding, carburizing, and oxidation potentials (KN, KCB, and KO) of the process atmosphere. Until now, there is insufficient information about the influence of CO and CO2 and the ratio between them on the relevant potentials and, therefore, on the white layer development. This issue is addressed in the present work. The gaseous nitrocarburizing was carried out on alloyed steels (AISI 4142, AISI H13, and AISI 420) with the addition of CO or CO2 as carbon donator. The resulted potentials (KN, KCB, and KO) were detected using oxygen and hydrogen sensors and the generated surface layers were characterized by means of optical microscope and glow discharge optical emission spectroscopy (GDOS). The investigation proved that CO2 leads to lower carburizing but higher oxidation potential than CO. The typical potential KCB was 0.1 and KO was 0.11 in the nitrocarburizing atmosphere by supplying 4.8 % CO2 in the input gas mixture, whereas the potential KCB was 0.4 and KO was 0.015 by supplying 2.4 % CO. It was recognized that the carburizing reaction of the nitrocarburizing proceeds via CO as in the case of the pure carburizing process, and CO as an essential carbon donator increases carbon concentration in the compound layer effectively. Consequently, the growth and the porosity of the layer are influenced differently by CO and CO2. The degree of this influence depends on the chemical composition of the steels additionally. With the findings of the present investigation possible mechanisms of the pore formation are discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAlloy steel. =650 \0$aMachine parts industry. =650 \0$aNitrocarburizing. =650 \0$aPorosity. =650 \0$aRoller bearings. =650 \0$aSteel alloy industry. =650 \0$aWhite layer. =650 14$aNitrocarburizing. =650 24$aAlloy steel. =650 24$aPorosity. =650 24$aWhite layer. =700 1\$aHoffmann, F.,$eauthor. =700 1\$aKluemper-Westkamp, H.,$eauthor. =700 1\$aZoch, Hans,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC103926.htm =LDR 03762nab 2200553 i 4500 =001 MPC104423 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104423$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104423$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC151.7 =082 04$a532.05$223 =100 1\$aGu, Jianfeng,$eauthor. =245 10$aNumerical Simulation of Heat Treatment Based on the Model With Expanded Solution Domain /$cJianfeng Gu, Jing Wang, Jiansheng Pan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aThe heat treating of metals is a very complicated process in which multiple physical variables nonlinearly couple with each other. The heat transfer at gas-solid and liquid-solid interfaces is the most important problem to be solved in the numerical simulation of heat treatment, which is also the basis for the process design and equipment design of heat treatment. The traditional way in which one takes the parts as investigation objects and sets the heat transfer coefficient on the interface directly inevitably brings significant inaccuracy to simulation results. A series of research achievements in fluid mechanics and heat transfer theory have provided effective ways of dealing with this problem in heat treatment modeling. In this paper, a heat treatment model with an expanded solution domain is proposed after a brief summary of related research results for coupled heat transfer. In this model, the solution domain has been expanded to the surroundings of the heat treating parts. Taking the heating process in an industry furnace as an example, not only the parts and fixture but also the furnace body, furnace chamber, heating units, and all other components in the furnace are modeled as a whole. The virtual equipment design for a novel bell-type gas nitriding furnace has been successfully fulfilled based on the heat treatment simulation and demonstrates the giant advantage of this new model. It is necessary to emphasize that as an important step in the numerical simulation of heat treatment, this new model is far from mature, and a series of key problems still remain. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDifferential equations, Partial$xMathematical models. =650 \0$aHeat transfer. =650 \0$aModel with expanded solution domain. =650 \0$aNumerical analysis$xSimulation methods. =650 \0$aNumerical simulation of heat treatment. =650 14$aNumerical simulation of heat treatment. =650 24$aHeat transfer. =650 24$aModel with expanded solution domain. =700 1\$aPan, Jiansheng,$eauthor. =700 1\$aWang, Jing,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104423.htm =LDR 03762nab 2200553 i 4500 =001 MPC103549 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC103549$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC103549$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD9705.5.B434 =082 04$a338.7/669142/0973$223 =100 1\$aDong, J.,$eauthor. =245 10$aInfluence of Hydrogen, Carbon Dioxide, and Alloy Content on Pore Formation in the White Layer of Alloyed Steels /$cJ. Dong, F. Hoffmann, H. Kluemper-Westkamp, Hans Zoch. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b15 =520 3\$aGaseous nitriding and nitrocarburizing of steel have found new applications in the area of ultra-precision machining of steel with mono-crystalline diamond tools. Steel is normally not diamond machinable because serious chemical reactive wear of diamond tool occurs. The wear can be reduced significantly if the machining is carried out in the white layer of nitrided or nitrocarburized steel, since the chemical reactivity of the white layer is lower compared to the steel substrate. For this application a thick white layer with low porosity is desirable. To produce such white layers the nitriding and nitrocarburizing processes should be specifically adapted. In the present work the influence of hydrogen and carbon dioxide in the process atmosphere on pore formation in the white layer during nitriding and nitrocarburizing was investigated experimentally. The experiments of gaseous nitriding and nitrocarburizing were carried out with varied process atmosphere on alloy steel grades. The generated surface layers were characterized by glow discharge optical emission spectroscopy (GDOS) and by optical microscopy. The results showed that low partial pressure of hydrogen in the nitriding atmosphere and strong nitride-forming elements in the steel are positive in suppressing pore formation, while carbon dioxide promoted pore formation in nitrocarburized white layer. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAlloy steel. =650 \0$aMachine parts industry. =650 \0$aMicromachining. =650 \0$aNitriding. =650 \0$aNitrocarburizing. =650 \0$aPores. =650 \0$aRoller bearings. =650 \0$aSteel alloy industry. =650 \0$aWhite layer. =650 14$aNitriding. =650 24$aAlloy steel. =650 24$aMicromachining. =650 24$aNitrocarburizing. =650 24$aPores. =650 24$aWhite layer. =700 1\$aHoffmann, F.,$eauthor. =700 1\$aKluemper-Westkamp, H.,$eauthor. =700 1\$aZoch, Hans,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC103549.htm =LDR 03762nab 2200553 i 4500 =001 MPC104390 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104390$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104390$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aDS706 =082 04$a628.1$223 =100 1\$aYang, M.,$eauthor. =245 10$aModeling the Nitriding of Steel by Compound Layer Growth Model /$cM. Yang, R. Sisson. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b12 =520 3\$aThe effort to simulate the nitriding process has been ongoing for the last 20 years. Most of the work has been done to simulate the nitriding process of pure iron. In the present work, the compound layer growth model has been developed to simulate the nitriding process of AISI 4140 steel. In this paper, the fundamentals of the model are presented and discussed including the kinetics of compound layer growth and the determination of the boundary conditions. The experimental verification of the model is also presented. It proves the concept of utilizing the compound layer growth model in other steels. The nitriding process of various steels can thus be modeled and predicted in the future. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCarbonitriding. =650 \0$aLehrer diagram. =650 \0$aModeling. =650 \0$aNitriding process. =650 \0$aNitriding$xCongresses. =650 \0$aNitriding. =650 14$aNitriding process. =650 24$aCALPHAD. =650 24$aLehrer diagram. =650 24$aModeling. =700 1\$aSisson, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104390.htm =LDR 03762nab 2200553 i 4500 =001 MPC104551 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104551$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104551$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN697.A47 =082 04$a669.722$223 =100 1\$aSanders, Matthew,$eauthor. =245 10$aTribological Evaluation of Titanium and Aluminum Alloys Exposed to Hydrogen in Wet Conditions /$cMatthew Sanders, Sukbae Joo, Frank Di Bella, Hong Liang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b48 =520 3\$aThe manufacturing processes of titanium and aluminum alloys involve hydrogen wet conditions. The current research investigates the effect of such hydrogen on the mechanical and tribological performance of these alloys. Experimental approaches include the development of a hydrogen charging method, mechanical testing using a small punch tester, and the testing of friction and wear behavior using a tribometer. The results show that for both alloys, no hydride was formed. The molecular hydrogen did not have any visible effects on aluminum; however, the titanium alloy showed profound effects in its mechanical properties, with a reduction in strength. The hydrogen had no significant effect on the tribological properties of titanium or aluminum specimens. The current research shows a novel way to test for the effects of hydrogen in wet conditions on the mechanical strength of materials. The research outcome could aid design engineers in their selection of materials in hydrogen environments. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum$xMetallurgy. =650 \0$aHydrogen embrittlement. =650 \0$aMaterial characterization. =650 \0$aMechanical alloying. =650 \0$aSmall punch test. =650 \0$aWear. =650 14$aSmall punch test. =650 24$aHydrogen embrittlement. =650 24$aMaterial characterization. =650 24$aTi-6Al-4V. =650 24$aWear. =700 1\$aDi Bella, Frank,$eauthor. =700 1\$aJoo, Sukbae,$eauthor. =700 1\$aLiang, Hong,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104551.htm =LDR 03762nab 2200553 i 4500 =001 MPC104632 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104632$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104632$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN697.A47 =082 04$a669.722$223 =100 1\$aReich, Michael,$eauthor. =245 10$aQuenching Simulation of Aluminum Alloys Including Mechanical Properties of the Undercooled States /$cMichael Reich, Olaf Kessler. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b27 =520 3\$aAge hardening is the most important heat treatment to strengthen aluminum alloys. It consists of solution annealing, quenching, and aging. During quenching, a supersaturated solid solution is formed which is necessary for the following precipitation of strengthening particles. During quenching, thermal gradients occur in components, which can generate residual stresses and distortion. The finite element method (FEM) has become a very efficient tool in understanding the complex mechanisms of thermal stresses and distortions during heat treatment. Reliable numerical simulations require accurate material properties and realistic constitutive laws. In the case of quenched aluminum alloys, material properties mean the behavior of the undercooled states depending on temperature and microstructure respectively cooling rate. The mechanical properties of these non-equilibrium microstructures are not available yet. Therefore, compression tests and also tension/compression tests of undercooled aluminum alloy EN-AW A6082 (AlSi1MgMn) were performed in a quenching and deformation dilatometer. Samples have been solution annealed and quenched in the dilatometer to varying temperatures with varying cooling rates. Immediately after quenching, deformation tests on quenching temperature have been performed. The results were implemented in the material model of the FEM-Software SYSWELD. Quenching in warm water of an extruded 6082 L-profile with different legs was simulated to understand and predict residual stress and distortion generation. Using the presented model enables to simulate this complex geometry and inhomogeneous heat transfer. The experimental results of quenched 6082 L-profiles verified the above simulations. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAge hardening. =650 \0$aAluminum$xMetallurgy. =650 \0$aAluminum. =650 \0$aBauschinger effect. =650 \0$aDilatometer. =650 \0$aDistortion. =650 \0$aMechanical alloying. =650 \0$aMechanical properties. =650 \0$aQuenching. =650 \0$aResidual stress. =650 \0$aSimulation. =650 14$aAluminum. =650 24$aAge hardening. =650 24$aBauschinger effect. =650 24$aDilatometer. =650 24$aDistortion. =650 24$aMechanical properties. =650 24$aQuenching. =650 24$aResidual stress. =650 24$aSimulation. =700 1\$aKessler, Olaf,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104632.htm =LDR 03762nab 2200553 i 4500 =001 MPC104417 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104417$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104417$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.Q4 =082 04$a672.36$223 =100 1\$aFelde, Imre,$eauthor. =245 10$aDetermination of Thermal Boundary Conditions During Immersion Quenching by Optimization Algorithms /$cImre Felde. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b15 =520 3\$aThe estimation of thermal boundary conditions occurring during heat treatment processes is an essential requirement for characterization of heat transfer phenomena. In this work, the performance of four optimization techniques is studied. These models are the conjugate gradient method, the Levenberg-Marquardt method, the simplex method, and the non-dominated sorting genetic algorithm (NSGA II) algorithm. The models are used to estimate the heat transfer coefficient in 1D and 2D axis symmetrical cases during transient heat transfer. The performance of the optimization methods is demonstrated using numerical experiments. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aConjugate gradient. =650 \0$aHeat transfer coefficient. =650 \0$aInverse heat conduction problems (IHCP) =650 \0$aLevenberg-Marquardt. =650 \0$aMetals$xHardenability. =650 \0$aMetals$xHeat treatment. =650 \0$aMetals$xQuenching. =650 \0$aNon-dominated sorting genetic algorithm (NSGA II) =650 \0$aQuenching. =650 \0$aSimplex method. =650 14$aQuenching. =650 24$aConjugate gradient. =650 24$aHeat transfer coefficient. =650 24$aInverse heat conduction problems (IHCP) =650 24$aLevenberg-Marquardt. =650 24$aNon-dominated sorting genetic algorithm (NSGA II) =650 24$aSimplex method. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104417.htm =LDR 03762nab 2200553 i 4500 =001 MPC104531 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104531$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104531$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD9579.M4 =082 04$a333.82330973$223 =100 1\$aGao, Weimin,$eauthor. =245 10$aComputational Simulation of the Influence of Inert Particles on Incomplete Combustion of Methane at a Low Air Factor /$cWeimin Gao, Lingxue Kong, Peter Hodgson. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b26 =520 3\$aIt is well known that the gas-solid system plays a significant role in many industrial processes. It is a complex physical and chemical process, generally consisting of heat transfer, mass transfer, species diffusion, and chemical reactions. In this paper, the reaction of methane with air at a low air factor and the gas flow in a fluidized bed with 0.1 mm solid particles are computationally simulated to enable the study of the effect of the inert particles on the species diffusion and the chemical reactions. The reaction of methane and air is modeled by a two-step reaction mechanism that produces a continuous fluid phase composed of six gases (CH4, CO, O2, CO2, H2O, and N2) and discrete solid particles in the reactor. The simulation results are compared with experiment and show that the finite rate model and the eddy dissipation model can well describe the reactions of gases in high-density gas-solid systems. The distribution of each gas and the particle behaviors are analyzed for incomplete combustion at different concentrations of loaded solid particles. The inert particles change the reactions by enhancing both the chemical kinetics and the species diffusion dynamics. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aChemical reaction. =650 \0$aComputational fluid dynamics. =650 \0$aGas-solid flow. =650 \0$aHydrates. =650 \0$aNatural gas. =650 \0$aResearch and development projects. =650 \0$aSolid particle. =650 \0$aSpecies diffusion. =650 14$aGas-solid flow. =650 24$aCFD. =650 24$aChemical reaction. =650 24$aComputational fluid dynamics. =650 24$aSolid particle. =650 24$aSpecies diffusion. =700 1\$aHodgson, Peter,$eauthor. =700 1\$aKong, Lingxue,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104531.htm =LDR 03762nab 2200553 i 4500 =001 MPC104350 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104350$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104350$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA684 =082 04$a624.1/82$223 =100 1\$aGhosh, Abhijit,$eauthor. =245 10$aOptimization of Stability of Retained Austenite in TRIP-Aided Steel Using Data-Driven Models and Multi-Objective Genetic Algorithms /$cAbhijit Ghosh, Shiv Singh, Nirupam Chakraborti. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b11 =520 3\$aThe important parameters that determine the properties of transformation-induced-plasticity (TRIP) -aided steel are the amount of retained austenite phase present in its initial microstructure and its stability. A large value of carbon equivalent leads to a high amount of retained austenite in the initial microstructure of these steels at room temperature. Looking at it from another angle, a high value of carbon equivalent is undesirable, as it adversely affects the weldability. In this study, we have attempted to resolve this conflict by bringing in the notion of Pareto optimality. Through an evolutionary neural network that evolved through multi-objective genetic algorithms, data-driven models were constructed for both carbon equivalent and fraction transformed. The effect of individual variables on the extent of austenite transformation as inferred by the model was found to be consistent with the principles of physical metallurgy of TRIP-aided steel. Next, using a predator-prey genetic algorithm, a bi-objective optimization task was conducted for simultaneous minimization of carbon equivalent and the extent of transformation. The resulting Pareto frontier was carefully analyzed, and the transformation behavior of different TRIP-assisted steels was also predicted for different straining conditions. Further need for optimizing the heat-treatment schedule is highlighted through selective experimentation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aComputer-aided design$xaCongresses. =650 \0$aEngineering design$xData processing. =650 \0$aMulti-objective optimization. =650 \0$aRetained austenite. =650 \0$aTRIP aided steel. =650 \0$aWeldability. =650 \0$aWelded steel structures$xDesign and construction. =650 14$aTRIP aided steel. =650 24$aMulti-objective optimization. =650 24$aRetained austenite (RA) =650 24$aTransformation of RA, genetic algorithms. =650 24$aWeldability. =700 1\$aChakraborti, Nirupam,$eauthor. =700 1\$aSingh, Shiv,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104350.htm =LDR 03762nab 2200553 i 4500 =001 MPC104430 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104430$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104430$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA347.F5 =082 04$a620.00151825$223 =100 1\$aKulkarni, N.,$eauthor. =245 10$aOrdinal-Optimization-Based Framework for Optimization of Cooling Conditions for Reducing Distortion in Hot-Rolled Asymmetric Sections /$cN. Kulkarni, B. Gautham, N. Singhal, P. Zagade. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b33 =520 3\$aModeling and simulation tools are used increasingly to model thermo-mechanical processing of materials. Often these simulations are computationally expensive, and use of formal optimization tools to enhance product or process performance, or both, is practically infeasible in view of the large search space (variables), leading to a large number of function evaluations. Ordinal optimization (OO) adopts a different strategy compared to traditional optimization algorithms. It uses the “order” in the performances among designs, rather than the “value” and provides set of “good enough” solutions with a guarantee, instead of a unique best solution. It has been successfully applied to optimization of such computationally intensive problems. OO can be easily integrated with other optimization algorithms. OO's integration with genetic algorithms (GA) leads to a hybrid algorithm called “genetic ordinal optimization” (GOO). It has better stopping criteria, along with a high probability of finding truly “good enough” design compared to the traditional GA. Cooling of asymmetric sections, post hot rolling, leads to a large distortion because of thermal gradients and phase transformations. Lengthwise distortions pose operational difficulties and challenges for post-rolling operations, including straightening. Here, a possible scheme of a sequence of forced convection cooling stages is considered in place of the traditionally used free convection on the cooling bed. In this work OO, GOO, and GA are applied to optimize the sequence of forced cooling for minimal distortion. A simplified regression model for distortion, built using results of a detailed thermo-mechanical simulation model, is used in the optimization loop. Results obtained show reduction in the distortion by a significant amount as compared to the natural convection cooling on the cooling bed. Besides providing a possible solution, this work also shows the efficacy of OO and GOO for application to industrial problems. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFinite element method. =650 \0$aFinite-element modeling. =650 \0$aGenetic algorithm. =650 \0$aGenetic ordinal optimization. =650 \0$aOrdinal optimization. =650 \0$aThermo-mechanical analysis. =650 14$aOrdinal optimization. =650 24$aFinite-element modeling. =650 24$aGenetic algorithm. =650 24$aGenetic ordinal optimization. =650 24$aThermo-mechanical analysis. =700 1\$aGautham, B.,$eauthor. =700 1\$aSinghal, N.,$eauthor. =700 1\$aZagade, P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104430.htm =LDR 03762nab 2200553 i 4500 =001 MPC104385 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104385$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104385$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS227.2 =082 04$a671.5/2$223 =100 1\$aDoley, J.,$eauthor. =245 10$aStudies on Temperature Distribution in Electromagnetic Welding Process /$cJ. Doley, S. Kore. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b7 =520 3\$aElectromagnetic welding (EMW) is a solid state impact welding technique which uses pulsed electromagnetic field for welding electrically conductive work pieces like aluminum. High velocity of impact created by the electromagnetic force causes the removal of oxide layer from the weld interface. A fully coupled numerical analysis, incorporating the equivalent electric circuit of EMW, electromagnetic field propagation, heat transfer, and dynamic elasto-plastic deformation, has been carried out using LS-DYNA EM module. The numerical simulation results for the EM weld feasibility, deformation pattern, temperature distribution and velocity of impact are reported here and corroborated with the previously published literature. It is observed that the temperature rise is not significant to cause the melting of Al sheets indicating there will not be any intermetallics. Hence, present paper is important for welding dissimilar metals for automobile components. Metallographic studies have also revealed absence of any coarse or columnar grain structures at the weld interface. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aElectromagnetic. =650 \0$aSteel, Structural$xCorrosion. =650 \0$aSteel, Structural$xWelding. =650 \0$aTemperature. =650 \0$aVelocity and deformation. =650 \0$aWelded joints. =650 \0$aWelding. =650 14$aElectromagnetic. =650 24$aTemperature. =650 24$aVelocity and deformation. =650 24$aWelding. =700 1\$aKore, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104385.htm =LDR 03762nab 2200553 i 4500 =001 MPC104367 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104367$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104367$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC173.7 =082 04$a550.14$223 =100 1\$aDas, Subrat,$eauthor. =245 10$aConvection in Fluid Overlying Porous Layer :$bAn Application to Hall-Héroult Cell /$cSubrat Das. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b36 =520 3\$aFinite-element method is used to predict the buoyancy-driven convection in a horizontal layer of fluid (aluminum melt) overlying a porous layer (cathode) saturated with the same fluid. This work aims to compare the Hall-Héroult process in electrolytic cell, where a layer of molten aluminum is reduced over the porous cathode surface. In this study, the physical system of the aluminum melt (fluid) and cathode (porous) together is considered as a composite system of fluid overlying porous layer. The main objective of this study to analyse the velocity components in thin fluid layer and its impact on a porous cathode surface if there is any. In addition, an externally imposed time-independent uniform magnetic field is used to analyse its influence on natural convective forces. The physical system of fluid overlying porous layer is analysed at different Hartmann, Darcy, and fluid-Rayleigh numbers for a fixed Prandtl number (Pr = 0.014). The predicted data show that the convective forces, caused by buoyancy-driven flow, are significant. It is shown that the velocity peaks moves toward the solid wall because of the presence of a magnetic field creating a stronger boundary-layer growth over the permeable cathode surface. The predicted results are plotted in terms of average Nusselt number and Darcy number to indicate the influence of pores and permeability on overall convective heat-transfer characteristics. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBrinkman-Forchheimer extended Darcy model. =650 \0$aElectric fields. =650 \0$aField theory (Physics) =650 \0$aGravitational fields. =650 \0$aMagnetic field. =650 \0$aNatural convection. =650 14$aHall-Héroult cell. =650 24$aBrinkman-Forchheimer extended Darcy model. =650 24$aMagnetic field. =650 24$aNatural convection. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104367.htm =LDR 03762nab 2200553 i 4500 =001 MPC104389 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104389$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104389$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.C3 =082 04$a672.3/6$223 =100 1\$aHe, Liang,$eauthor. =245 10$aModeling the Carbonitriding of Steel /$cLiang He, Yuan Xu, Richard Sisson. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aA software model, CarbNitrideTool, has been developed to simulate the carbonitriding process. In this paper the fundamentals of the model will be presented and discussed including the experimental determination of the surface boundary conditions and the diffusivities of carbon and nitrogen as a function of alloy composition and temperature. The need for accurate databases is emphasized. The experimental verification of the model is also presented. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCarbonitriding$xCongresses. =650 \0$aCarbonitriding. =650 \0$aConcentration profile. =650 \0$aDiffusivity. =650 \0$aNitriding$xCongresses. =650 \0$aNitriding. =650 \0$aNumerical simulation. =650 14$aCarbonitriding. =650 24$aConcentration profile. =650 24$aDiffusivity. =650 24$aNumerical simulation. =700 1\$aSisson, Richard,$eauthor. =700 1\$aXu, Yuan,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104389.htm =LDR 03762nab 2200553 i 4500 =001 MPC104386 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104386$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104386$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA465 =082 04$a620.1/76$223 =100 1\$aElmaryami, Abdlmanam,$eauthor. =245 10$aModeling the Lowest Hardness Point in a Steel Bar During Quenching /$cAbdlmanam Elmaryami, Badrul Omar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b20 =520 3\$aThe modeling of an axisymmetric industrial-quenched low-carbon steel bar based on the finite-element method has been produced to investigate the impact of process history on metallurgical and material properties. Mathematical modeling of a one-dimensional line (radius) element axisymmetric model has been adopted to predict temperature history and, consequently, the hardness of the quenched steel bar at any point (node). The lowest hardness point (LHP) is determined. In this paper, hardness in specimen points was calculated by the conversion of calculated characteristic cooling time for phase transformation t8/5 to hardness. The model can be employed as a guideline to the design cooling approach to achieve desired microstructure and mechanical properties, such as hardness. The developed mathematical model converted to a computer program. This program can be used independently or incorporated into a temperature history calculator to continuously calculate and display temperature history of the industrial-quenched steel bar and thereby calculate LHP. The developed program from the mathematical model has been verified and validated by comparing its hardness results with 2D mathematical model and with commercial finite-element software results. The comparison indicates reliability of the proposed model. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAxisymmetric steel bar. =650 \0$aFinite element. =650 \0$aHeat treatment. =650 \0$aMathematical modeling. =650 \0$aQuenching. =650 \0$aSteel$xFracture. =650 \0$aSteel$xHeat treatment. =650 \0$aUnsteady state heat transfer. =650 14$aHeat treatment. =650 24$aAxisymmetric steel bar. =650 24$aFinite element. =650 24$aMathematical modeling. =650 24$aQuenching. =650 24$aUnsteady state heat transfer. =700 1\$aOmar, Badrul,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104386.htm =LDR 03762nab 2200553 i 4500 =001 MPC104477 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104477$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104477$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA478 =082 04$a620.17$223 =100 1\$aPrasanna Kumar, T.,$eauthor. =245 10$aCoupled Analysis of Surface Heat Flux, Microstructure Evolution, and Hardness during Immersion Quenching of a Medium Carbon Steel in Plant Conditions /$cT. Prasanna Kumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b30 =520 3\$aImmersion quenching is one of the most widely used processes for achieving martensitic and bainitic steels. A comprehensive modeling treatment of quenching requires a description of the surface heat flux or heat transfer coefficient. Generally, the heat transfer coefficients obtained during the quenching of a material not undergoing a phase change, such as austenitic stainless steel, are used for calculating the phase change in an alloy steel also. In order to accurately model phase transformation, one must characterize the heat transfer process specific to the quenchant-steel combination in question. This work reports the development of numerical models for the simultaneous estimation of surface heat flux, austenite decomposition, and hardness during the immersion quenching of carbon and alloy steels in plant conditions. The algorithm couples non-linear transient inverse heat transfer with phase transformation, resulting in heat flux values specific to the steel grade-quenchant combination in actual practice. The effects of the soaking temperature, component surface conditions, quenchant conditions, plant operating practices, and so on can be addressed satisfactorily with this method. The austenite decomposition models use a unique approach consistent with both the time-temperature-transformation diagram of the steel and Fe-C equilibrium phase diagrams. Portable and self-contained handheld equipment was designed for testing in the plant. The equipment was used for computing the surface heat flux at the mid-section of a cylindrical specimen of medium carbon 1050 grade steel (25 mm in diameter by 100 mm in length) quenched in an aqueous solution of a polymer. Using the transient heat flux values, the microstructure evolution and hardness across the cross section of the specimen were simultaneously computed. The hardness profile and the microstructure distribution across the specimen section are presented and are corroborated by laboratory measurements. It was found that in this specific case of polymer quenching, the surface hardness was lower than the core hardness due to an anomalous heat transfer condition, which is explained via the use of the models developed in this article. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAnomalous quenching in 1050 grade. =650 \0$aCarbon steel$xCracking. =650 \0$aCarbon steel$xHydrogen embrittlement. =650 \0$aCatalytic cracking. =650 \0$aInverse Modeling. =650 \0$aMicrostructure evolution. =650 \0$aQuenching heat flux. =650 14$aInverse Modeling. =650 24$aAnomalous quenching in 1050 grade. =650 24$aIn-situ testing. =650 24$aMicrostructure evolution. =650 24$aQuenching heat flux. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104477.htm =LDR 03762nab 2200553 i 4500 =001 MPC104392 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104392$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104392$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA347.F5 =082 04$a620.00151825$223 =100 1\$aHernández-Morales, B.,$eauthor. =245 10$aMathematical Modeling of Steel Heat Treating Using CCT Diagrams /$cB. Hernández-Morales, J. Téllez-Martínez, A. Dueñas-Pérez, M. Díaz-Cruz. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b23 =520 3\$aMathematical modeling is a powerful tool to design, control and optimize heat-treating processes. However, the complex interactions occurring between the thermal, microstructural, and stress fields inside the part during those processes (which must be taken into account in detailed modeling work) precludes its use in many instances-especially in a production environment. Thus, it is desirable to find methodologies that can speed up the simulations while maintaining the mathematical model close to reality. In this work, the evolution of the microstructural field was estimated from fraction-transformed-temperature correlations derived directly from a published continuous-cooling-transformation (CCT) diagram, which uses the cooling rate at 750°C as the x-axis. This approach “softens” the coupling between the thermal and fraction-transformed fields resulting in an efficient algorithm. The thermal field evolution was computed using standard procedures embedded in the commercially available code Abaqus, whereas empirical equations describing the fraction transformed-temperature relationships were programmed through user subroutines. The mathematical model was validated by comparing measured and model-predicted thermal response and final microstructure. In the experiments, austenitized AISI 4140 steel cylindrical probes (0.5-in. diameter x 2-in. length) were cooled in: (1) still air, and (2) a fluidized bed reactor, both at room temperature. The thermal response was measured during the cooling process by inserting two thermocouples: one at the geometrical center of the probe and the other near the probe surface, at mid-length. The latter was input to a code developed in-house to estimate the surface heat flux history, which constitutes the active boundary condition for the direct heat conduction problem and was, in turn, fed to the computational model. Once heat treated, the probes were prepared for metallographic observation using standard techniques. The results indicate that the proposed methodology can be used for predicting the thermo-microstructural evolution during a heat-treating process. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCoupled. =650 \0$aFinite element method. =650 \0$aFinite element. =650 \0$aMultiphysics. =650 \0$aNumerical. =650 \0$aQuench. =650 14$aFinite element. =650 24$aCoupled. =650 24$aMultiphysics. =650 24$aNumerical. =650 24$aQuench. =700 1\$aDíaz-Cruz, M.,$eauthor. =700 1\$aDueñas-Pérez, A.,$eauthor. =700 1\$aTéllez-Martínez, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104392.htm =LDR 03762nab 2200553 i 4500 =001 MPC104656 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104656$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104656$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.Q4 =082 04$a672.36$223 =100 1\$aKobasko, Nikolai.,$eauthor. =245 10$aReal and Effective Heat Transfer Coefficients (HTCs) Used for Computer Simulation of Transient Nucleate Boiling Processes during Quenching /$cNikolai Kobasko. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b26 =520 3\$aIn this paper, real and effective heat transfer coefficients (HTCs) are considered. The real HTC is determined by dividing the heat flux density by the superheat of the liquid. The effective HTC is obtained by dividing the heat flux density by the underheat of the liquid plus the superheat of the boundary layer. In practice, especially in the heat treating industry, effective HTCs and their average values are widely used. In many cases that is not correct, because bubble formation (critical diameter) depends on the superheat ?T = T – TS only and does not depend on the bath temperature. It is shown that due to this incorrectness, many problems arise, and misunderstanding of the quenching process often exists. So as to understand correctly the involved thermo-physical processes and receive correct data for computer simulation, in this paper, the real and effective HTCs are compared with each other. Several contradictions are shown between real and effective HTCs, such as the fact that the real HTCs do not depend on the size of a steel part and the thermal properties of a material. The effective HTC depends proportionally on the thermal properties of a material and is inversely proportional to the size of steel parts that contradict each other. In order to solve this problem, in this paper it is shown that the effective HTC is a mathematical value that can be used only for simplified cooling rate and cooling time calculations at the core of steel parts, and it cannot be used for temperature field calculations and residual stress prediction. The results of this paper can be used for computer simulation of the process of quenching and for the development of new intensive quenching technologies. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aComputer simulation. =650 \0$aEnvironment. =650 \0$aIncorrectness. =650 \0$aMetals$xHardenability. =650 \0$aMetals$xHeat treatment. =650 \0$aMetals$xQuenching. =650 \0$aNew approach in designing. =650 \0$aQuenching technologies. =650 \0$aReal and effective HTCs. =650 \0$aResidual stresses. =650 14$aReal and effective HTCs. =650 24$aComputer simulation. =650 24$aEnvironment. =650 24$aIncorrectness. =650 24$aNew approach in designing. =650 24$aQuenching technologies. =650 24$aResidual stresses. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104656.htm =LDR 03762nab 2200553 i 4500 =001 MPC104378 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104378$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104378$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD5658.I52 =082 04$a338.7/669142/0975412$223 =100 1\$aTalukdar, Tushar,$eauthor. =245 10$aThermo-mechanical Modeling of Laser Deposited Bimetallic Components /$cTushar Talukdar, Liang Wang, Sergio Felicelli. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b26 =520 3\$aA thermo-mechanical three-dimensional finite element model is developed for use in determining the temperature history and residual stress in a Cu-H13 thin wall plate deposited by means of the laser engineered net shaping process. The same model is also applied to an H13-H13 sample in order to compare the results. The input laser power is adjusted for each layer and three different scanning speeds so as to maintain a steady molten pool size and a predefined pool depth of one and a half layers in thickness. It is observed that for a constant scanning speed, the required laser power decreases with the addition of more layers, and with an increase in the scanning speed the laser power needs to be increased. During the deposition of the first two layers, the required input laser power is significantly higher for the H13-H13 sample than for the Cu-H13 one because of the high heat conduction rate through the Cu substrate. The z-component (growth direction) of the residual stresses is found to be dominant over the other components and is compressive near the center of the wall and tensile at the free edges, which is consistent with the experimental results presented in the literature. The residual stress levels near the free edges are found to be higher in the Cu-H13 sample than in the H13-H13 sample. In these regions, the unidirectional scanning strategy results in a higher stress accumulation than the alternative scanning strategy. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBimetallic material. =650 \0$aEmployee ownership. =650 \0$aModeling. =650 \0$aResidual stress. =650 \0$aSteel industry. =650 14$aBimetallic material. =650 24$aCu-H13. =650 24$aH13 tool steel. =650 24$aLENS. =650 24$aModeling. =650 24$aResidual stress. =700 1\$aFelicelli, Sergio,$eauthor. =700 1\$aWang, Liang,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104378.htm =LDR 03762nab 2200553 i 4500 =001 MPC104365 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC104365$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC104365$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357 =082 04$a620.1/06$223 =100 1\$aPrabhu, K.,$eauthor. =245 10$aEffect of Boundary Heat Transfer Coefficient and Probe Section Size on Cooling Curves During Quenching /$cG. Ramesh, K. Prabhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b9 =520 3\$aIn the present work the effect of boundary heat transfer coefficient and section size of quench probe material on cooling curves was investigated by using finite difference heat transfer based SolidCast software. Simulations were carried out at different combinations of heat transfer coefficient and quench probe diameter and thermal history at the geometric center of the probe was estimated to generate cooling curves. Simulation results show that both boundary heat transfer coefficient and quench probe diameter had a significant effect on the average cooling rate. A relationship between Grossmann quench severity (H), thermal conductivity of material, size of the probe, and average cooling rate was established. By using this model, for a known quench medium, probe size, and material it is possible to predict the average cooling rate of the probe. On the other-hand, for a given material and required cooling rate, cooling severity required from the quench media could be predicted and accordingly an appropriate quench medium can be selected. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCooling curve. =650 \0$aFluid dynamics. =650 \0$aHeat transfer coefficient. =650 \0$aHeat$xTransmission. =650 \0$aProbe size. =650 \0$aQuench severity. =650 \0$aTurbulence. =650 14$aHeat transfer coefficient. =650 24$aCooling curve. =650 24$aProbe size. =650 24$aQuench severity. =700 1\$aPrabhu, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC104365.htm =LDR 03762nab 2200553 i 4500 =001 MPC103963 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC103963$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC103963$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC182 =082 04$a541.3453$223 =100 1\$aLopez, Guido,$eauthor. =245 10$aGas-Adsorption Indicator Method for NDT and Surface-Defect Characterization /$cGuido Lopez, Nadezda Berezkina, Ilya Leipunsky. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b19 =520 3\$aThe gas-adsorption indicator method (GAIM) is a relatively unknown yet reliable technique for nondestructive testing (NDT) of engineering materials, and component parts. Invented in Russia, GAIM is a spin-off from the BURAN space program in the former Soviet Union. GAIM is inspired on a highly effective method to detect defects on the tiles of the thermal protection system (TPS) of BURAN and leakages through seals in compartment hatches of the spacecraft. This method involved the capture of gas molecules by a chemically treated sheet. Based on this technique, GAIM was derived and developed into an innovative penetrant technique (PT) for NDT and NDE of surfaces. GAIM offers clear advantages over more conventional PT methods and other techniques for surface NDT and NDE. GAIM proves to be more versatile, adaptable, considerably less expensive, safer, and more reliable. It allows fast inspections, detections, and characterization of surface anomalies, such as cracks, corrosion, and micro-porosity. The technique can be used in a wide variety of materials, including metals, ceramics, specialized coatings, and composites. The applicability of GAIM for NDE and NDT is ample, ranging from simple lab tests to field inspections of spacecraft, aircraft, and nuclear and conventional power plants. The underlying physical phenomena and researched theory behind the technique are presented and explained. The technique is also illustrated with graphical documentation, and application examples. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAdsorptie. =650 \0$aAdsorption. =650 \0$aCrack detection. =650 \0$aGas. =650 \0$aGases$xAbsorption and adsorption. =650 \0$aPenetrant testing. =650 \0$aPhysisorption. =650 14$aPenetrant testing. =650 24$aAdsorption. =650 24$aCrack detection. =650 24$aPhysisorption. =650 24$aTPS shuttle. =700 1\$aBerezkina, Nadezda,$eauthor. =700 1\$aLeipunsky, Ilya,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC103963.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120021 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120021$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120021$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQL430.4 =082 04$a594.3$223 =100 1\$aZhou, Yan,$eauthor. =245 10$aLubrication Behavior of Slug Mucus /$cYan Zhou, David Huitink, Hong Liang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aCrawling worms such as slugs are natural tribological species able to deal with varied surface textures as they crawl. Slug mucus has the ability to act as both an adhesive and a lubricant. In order to understand the principles behind slugs' crawling motion, the frictional behavior of slug mucus was studied, as well as its rheological and morphological properties. The solid constituents of the mucus were confirmed by means of nuclear magnetic resonance. A shear thinning behavior was observed using a rheometer. Slug mucus has a low friction coefficient, and the presence of water enhanced its capacity as a lubricant. The nano-scale physical structure of the solid constituents of the slug mucus was determined by means of atomic force microscopy. It was found that the macro-scale shear thinning behavior works in conjunction with the slug's method of locomotion to provide lubrication for sliding and gel-like adhesion. This overlooked animal might offer a world of intelligent design in engineering biomimetic systems that can both adhere and slide simultaneously. Furthermore, biodegradable and water-compatible features of slug mucus shed light on the formulation of a new generation of lubricants. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFriction. =650 \0$aLubricant. =650 \0$aSlugs (Mollusks) =650 \0$aSlugs. =650 \0$aSnails. =650 14$aLubricant. =650 24$aAFM. =650 24$aFriction. =650 24$aSlugs. =700 1\$aHuitink, David,$eauthor. =700 1\$aLiang, Hong,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120021.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120017 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2012\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120017$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120017$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC176.8.E9 =082 04$a530.414$223 =100 1\$aGueijman, Sergio,$eauthor. =245 10$aTracking Interphases in Directionally Solidified Zn-Al Binary Alloys /$cSergio Gueijman, Carlos Schvezov, Alicia Ares. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b12 =520 3\$aIn the present work, we investigated the movement of [liquid/(solid + liquid)] interphases [L/(S + L)], [(solid + liquid)/(eutectic + solid + liquid)] interphases [(S + L)/(E + L)], [(eutectic + solid+ liquid)/solid] interphases [(E + L)/S], and [(solid + liquid)/solid] interphases [(S + L)/S], running in a binary Zn-Al alloy system from the chilled ends of a hemicylindrical sample. We found that under specific solidification conditions, new [(S + L)/(E + L)] and [(S + L)/S] interphases can be created in the center of the sample, and then move toward the ends of the probe and collide with the solidification advancing fronts. In a horizontal setup with chilled ends we determined the speeds and accelerations of the four imposed interphases, two of which moved from left to right and two of which moved from right to left. We were also able to detect the creation of new [(S + L)/(E + L)] and [(E + L)/S] or [(S + L)/S] interphases created near the center of the sample, and to calculate their speeds and accelerations from the near beginning of the creation to the instant in which they collided with the imposed solidification fronts. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCharge transfer$xResearch. =650 \0$aDirectional solidification. =650 \0$aHigh spin physics. =650 \0$aInterphase boundary dynamics. =650 \0$aInterphases of solidification. =650 \0$aIonic crystals$zSpectra. =650 \0$aPhase transformations. =650 \0$aZinc-aluminum alloys. =650 14$aDirectional solidification. =650 24$aInterphase boundary dynamics. =650 24$aInterphases of solidification. =650 24$aPhase transformations. =650 24$aZinc-aluminum alloys. =700 1\$aAres, Alicia,$eauthor. =700 1\$aSchvezov, Carlos,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 1, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2012$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120017.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150006 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1503-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150006$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS225 =082 04$a671.3/32$223 =100 1\$aBereczki, P.,$eauthor. =245 10$aDifferent Applications of the Gleeble® Thermal-Mechanical Simulator in Material Testing, Technology Optimization, and Process Modeling /$cP. Bereczki, B. Fekete, V. Szombathelyi, F. Misjak. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b22 =520 3\$aIn this study, our aim is to present a compilation about different applications of the Gleeble® thermal-mechanical system concerning material testing, characterization of advanced thermomechanically controlled processes and modeling the multiaxial forging technique. The first topic aims to provide an accurate input dataset for developing an energy-based fatigue model for 15Ch2MFA reactor steel. The process characterization intends to quantify the effect of deformation-stored energy on the start temperature and kinetic of the austenite-ferrite transformation. The modeling topic purposes to predict the evolution of the flow stress and the hardening behavior during processing a mild steel by multiaxial forging. All of these experiments were carried out on a Gleeble® 3800 simulator using different mobile conversion units. The fatigue tests were conducted under uniaxial tension-compression loading with in-phase thermal cycles. To develop a new energy-based low-cycle fatigue (LCF) model, the energy balance of the plastic deformation was also investigated. Moreover, the evolution of the microstructure was observed by transmission electron microscopy (TEM) studies at the different stages of the nominal failure lifetime. The deformation-induced ferrite transformation (DIFT) effect was characterized by a high-resolution dilatometer under uniaxial hot compression tests. An advanced simulation program and experimental setup have been developed for the calculation of reliable flow curve from the data, sampled during the multiaxial forging simulation. Concerning the thermomechanical fatigue tests, the experimental results correspond to the Coffin-Manson curve. Furthermore, temperature evolution measurements were performed to provide input data to the calculation of the plastic strain energy partition converted to heat. Finally, the effect of the deformation stored energy on the start and finish temperature of austenite transformation was obtained and quantified. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAdvanced thermomechanical processes. =650 \0$alow-cycle fatigue. =650 \0$amultiaxial forging. =650 \0$aPhysical simulation. =650 \0$aplastic work into heat. =650 14$aGleeble® thermal-mechanical simulator. =650 24$aAdvanced thermomechanical processes. =650 24$aDIFT effect. =650 24$aLow-cycle fatigue. =650 24$aMultiaxial forging. =650 24$aPhysical simulation. =650 24$aPlastic work into heat. =700 1\$aFekete, B.,$eauthor. =700 1\$aMisjak, F.,$eauthor. =700 1\$aSzombathelyi, V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 3 Special Issue on Acceleration of Alloy Design via Physical Process Simulation.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150006.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150002 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1503-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150002$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN756 =082 04$a672.32$223 =100 1\$aHomsher, C.,$eauthor. =245 10$aComparison of Two Physical Simulation Tests to Determine the No-Recrystallization Temperature in Hot Rolled Steel Plates /$cC. Homsher, C. Van Tyne. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b29 =520 3\$aTwo rolling simulations were conducted using a Gleeble 3500 to determine the no-recrystallization temperature, TNR on six microalloyed plate steels. Double hit deformation tests and multistep torsion tests were performed on steels containing varying amounts of Nb, V, and Ti. TNR for the double hit deformation tests were determined by finding fractional softening using the 5 % true-strain method and the intersection of the sigmoidal fractional softening curve with 20 % fractional softening. TNR for the multistep hot torsion test were determined using a mean flow stress method and finding the intersection of the two linear regions. TNR values following multistep hot torsion testing were lower than values measured after double hit deformation testing. The decrease in measured TNR values for the torsion tests occurs from the inherent multiple deformations, resulting in refined grains and an increase in nucleation sites for recrystallization during the subsequent deformation steps; thus recrystallization can continue to occur at lower temperatures. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$amicroalloy. =650 \0$aMultistep hot torsion tests. =650 \0$aNo recrystallization temperature. =650 \0$aRolling (Metal-work) =650 \0$asteel rolling. =650 14$aSteel rolling. =650 24$aDouble hit compression tests. =650 24$aMicroalloy. =650 24$aMultistep hot torsion tests. =650 24$aNo recrystallization temperature. =700 1\$aVan Tyne, C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 3 Special Issue on Acceleration of Alloy Design via Physical Process Simulation.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150002.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150007 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1503-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150007$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a620.17$223 =100 1\$aKumar, Sanjeev,$eauthor. =245 10$aEffect of Single and Multiple Thermal Cycles on Microstructure and Mechanical Properties of Simulated HAZ in Low Carbon Bainitic Steel /$cSanjeev Kumar, S. Nath, Vinod Kumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b28 =520 3\$aThe correlation of microstructure and mechanical properties in simulated heat affected zone (HAZ) of a low carbon bainitic steel plate of thickness 28 mm using single and multiple thermal cycles was investigated in the Gleeble 3800 Thermo Mechanical Simulator. Optical microscopy, field emission scanning electron microscopy, hardness, and impact strength measurements were done to characterize the weld HAZ simulated steel samples. Peak temperatures (Tp) of 1300, 1150, 1000, 900, 800, 700, and 600°C with heat input 50 kJ/cm were used for single pass weld. In two pass weld cycles, peak temperature (Tp1) 1300°C, and (Tp2) of 1100, 1000, 900, 800, and 700°C were used. This heat input is in line with the submerged arc welding (SAW) process extensively used in the fabrication of ship building industries. The impact toughness of weld HAZ simulated specimens was determined at –50°C by using a Charpy impact tester. Best impact toughness values (minimum 75 J) in weld HAZ simulated specimen were observed at the peak temperatures from 600 to 1150°C in single pass weld and from 1000 to 1100°C in two pass weld HAZ thermal cycles. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBainite. =650 \0$abainitic steel. =650 \0$aHigh heat input. =650 \0$aImpact toughness. =650 \0$aNaval ship steel. =650 \0$aThick plate. =650 14$aWeld simulated HAZ. =650 24$aBainitic steel. =650 24$aHigh heat input. =650 24$aImpact toughness. =650 24$aNaval ship steel. =650 24$aThick plate. =700 1\$aKumar, Vinod,$eauthor. =700 1\$aNath, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 3 Special Issue on Acceleration of Alloy Design via Physical Process Simulation.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150007.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150008 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1503-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150008$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQA402.5 =082 04$a519$223 =100 1\$aKumar, Vinod,$eauthor. =245 10$aImproving Steel Processing Through Thermo-Mechanical Simulation Studies /$cVinod Kumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b11 =520 3\$aThermo-mechanical simulation studies can be effectively utilized for optimization of processing parameters apart from development of new alloys, quality/yield improvement and material characterization. Physical simulation, being very close to the real world process, can be very helpful in near exact reproduction of the process, and in turn, better results. Thermo-mechanical simulation studies using Gleeble System found extensive applications in steel research and its processing. It can help in careful design of alloy chemistry, proper continuous casting operation to produce defect-free casting, and optimization of hot rolling and post-cooling parameters to produce the desired microstructure and annealing process after cold rolling to achieve the desired microstructure and properties, welding for easy fabrication, etc. Each of these steps needs to be fine-tuned and optimized to achieve the maximum benefit towards reduction in alloy additions, as well as quality and yield improvement during steel processing. A number of studies like continuous casting simulation for production of Cr-alloyed rail steel, hot deformation simulation and phase transformation behavior to optimize hot rolling of difficult to process high boron steel, and hot deformation simulation to bring down the rolling load and annealing simulation to achieve the desired hardness in low nickel stainless steel, etc. undertaken, helped to improve the processing of these steels. Details of these studies, results obtained, and the way to improve processing were discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAnnealing. =650 \0$aContinuous casting. =650 \0$aHot rolling. =650 \0$aMachine theory. =650 \0$aNeural computers. =650 \0$aPhysical simulation. =650 \0$aSimulated annealing (Mathematics) =650 \0$aThermo-mechanical simulation. =650 14$aThermo-mechanical simulation. =650 24$aAnnealing. =650 24$aContinuous casting. =650 24$aHot rolling. =650 24$aPhysical simulation. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 3 Special Issue on Acceleration of Alloy Design via Physical Process Simulation.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150008.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150001 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1503-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150001$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.42 =082 04$a620.1/126$223 =100 1\$aSomani, M.,$eauthor. =245 10$aInfluence of Composition and Prior Deformation on Phase Transformation Temperatures and Hardness in Direct Quenching Using Physical Simulation /$cM. Somani, J. Pyykkönen, D. Porter, L. Karjalainen, J. Kömi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aFor conventional reheated and quenched (RQ) steels, the level of alloying necessary to achieve a given hardenability and hardness can be estimated from calculated Jominy curves or ideal critical diameters (DI) given in ASTM A255-10(2014). However, for thermomechanically rolled direct quenched (DQ) steels, little data are available. In this study, the accuracy of the ASTM approach was estimated by designing an experiment to study the main effects of seven alloying elements (C, Mn, Cr, Ni, Mo, Nb, and V) at two levels with eight boron steels based on an eight-run resolution III partial factorial designed experiment. Continuous cooling transformation (CCT) diagrams covering cooling rates of 1.5°C/s-48°C/s were determined using Gleeble simulations with or without controlled deformation below Tnr. The effects of deformation below Tnr and the alloying elements were clearly revealed. In general, low temperature straining of the austenite led to higher levels of hardness than quenching from unstrained austenite. The start of the bainite transformation Ar3 (bainite) was modelled as a function of chemical composition and cooling rate. The data in the CCT diagrams were used to derive equivalent ideal critical diameters (DIB) for strained and unstrained prior austenite. The hardenability index DIB calculated from experimental Jominy curves generally agreed well with those of CCT data for unstrained austenite. In order to apply the ASTM A255 approach to the calculation of DIB, boron factors (BF) for steels with alloy factors (AFs) greater than 26 were estimated by extrapolating the ASTM data. However, this approach did not give satisfactory predictions for either strained or unstrained austenite. Preliminary analysis indicated that Cr, Mo, and V might be less effective at increasing hardenability than implied from their AFs. New formulae were given to allow estimations of the hardness to be expected in connection with direct quenching. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCCT diagram. =650 \0$aDilatation curves. =650 \0$adirect quenching. =650 \0$ahardenability. =650 \0$aHardness. =650 \0$aIdeal critical diameter. =650 \0$aJominy curves. =650 \0$aMartensite. =650 \0$aPhase transformation. =650 \0$aRegression modelling. =650 14$aDirect quenching. =650 24$aCCT diagram. =650 24$aDilatation curves. =650 24$aHardenability. =650 24$aIdeal critical diameter. =650 24$aJominy curves. =650 24$aMartensite. =650 24$aPhase transformation. =650 24$aRegression modelling. =700 1\$aKömi, J.,$eauthor. =700 1\$aKarjalainen, L.,$eauthor. =700 1\$aPorter, D.,$eauthor. =700 1\$aPyykkönen, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 3 Special Issue on Acceleration of Alloy Design via Physical Process Simulation.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150001.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150010 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1503-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150010$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA478 =082 04$a620.17$223 =100 1\$aWeyand, Stephan,$eauthor. =245 10$aInvestigation of Austenite Evolution in Low-Carbon Steel by Combining Thermo-Mechanical Simulation and EBSD Data /$cStephan Weyand, Dominik Britz, Daniel Rupp, Frank Mücklich. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b30 =520 3\$aThe thermo-mechanical simulator Gleeble 3800 was used in combination with the electron backscattered diffraction (EBSD) technique to analyze the austenite microstructure evolution during hot deformation in a low-carbon, microalloyed steel. The parent austenite grain structure was automatically reconstructed from EBSD datasets by applying the commercially available ARPGE software [Cayron, C., Artaud, B., and Briottet, L., “Reconstruction of Parent Grains from EBSD Data,” Mater. Charact., Volume 57, Nos. 4-5, 2006, pp. 386-401]. The work aims at two aspects: the ability to quantify the austenite evolution depending on different process parameters, and the validation of the EBSD reconstruction software ARPGE to evaluate the accuracy of reconstruction and demonstrating the application in low-carbon steels. For these steels, the conventional metallographic methods like Bechet-Beaujard [Bechet, S. and Beaujard, L., “Nouveau réactif pour la mise en évidence micrographique du grain austénitique des aciers trempés ou trempés-revenus,” Rev. Met., 1955] are limited and not reproducible in determining the former austenite. The presented approach provides an attractive alternative. In this context, hot compression tests were performed on cylindrical samples using a Gleeble 3800 simulator to create defined austenite conditions. The samples were rapidly quenched after processing to preserve the austenite microstructure. The obtained bainitic/martensitic microstructure is an essential precondition for the reconstruction procedure. For the validation of the results, correlative measurements using classical metallographic techniques and ARPGE data were performed to check the reliability of the reconstruction. The results obtained in this study provide a direct correlation of the microstructure simulation by Gleeble and the austenite microstructure evolution during processing of low-carbon steels. Especially, austenite grain-growth phenomena and grain refinement could be successfully observed and quantified. Furthermore, the measurements show that even on large EBSD maps (1000 ?m x 1000 ?m), the shape of the austenite grains are calculated with good accuracy. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCarbon steel$xCracking. =650 \0$aCatalytic cracking. =650 \0$aGleeble. =650 \0$aHot rolling. =650 \0$aLow-carbon steel. =650 \0$aPhysical simulation. =650 \0$aPrior austenite grain size. =650 \0$aReconstruction. =650 \0$aSteel alloys$xCracking. =650 \0$aThermo-mechanical. =650 14$aGleeble. =650 24$aARPGE. =650 24$aEBSD. =650 24$aHot rolling. =650 24$aLow-carbon steel. =650 24$aPhysical simulation. =650 24$aPrior austenite grain size. =650 24$aReconstruction. =650 24$aThermo-mechanical. =700 1\$aBritz, Dominik,$eauthor. =700 1\$aMücklich, Frank,$eauthor. =700 1\$aRupp, Daniel,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 3 Special Issue on Acceleration of Alloy Design via Physical Process Simulation.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150010.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150012 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1503-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150012$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.T54 =082 04$a671.3$223 =100 1\$aWhitley, B.,$eauthor. =245 10$aAnalysis of Microstructure in Hot Torsion Simulation /$cB. Whitley, A. Araujo, J. Speer, K. Findley, D. Matlock. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b28 =520 3\$aHot torsion is frequently employed to simulate multipass thermomechanical rolling. While flow behavior, observed through shear stress versus shear strain, is typically used to characterize hot deformation and softening behaviors, the resulting microstructures can also provide significant insight into microstructural evolution and strain accumulation during the hot deformation process. A preferred approach for the analysis of microstructural features resulting from hot torsion is presented. Torsional strain paths are reviewed and compared with traditional hot rolling deformations. A tangential sectioning technique, combined with supporting fundamentals, is also presented. Microstructural observation of steels thermomechanically deformed in hot torsion verified the ability to reasonably quantify strain from microstructural analysis. This approach offers a new method for assessing shear strain accumulation within local regions of a body plastically deformed in torsion, and should provide a useful complement to the assessment of mechanical responses in hot deformation studies. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAccumulated Shear Strain. =650 \0$aHot Torsion. =650 \0$aMateriais metalicos. =650 \0$aMetals$xThermomechanical treatment. =650 \0$aMicrostructural Analysis. =650 \0$aNonequilibrium thermodynamics. =650 \0$aPancaking. =650 \0$aThermomechanical Processing. =650 14$aHot Torsion. =650 24$aAccumulated Shear Strain. =650 24$aMicrostructural Analysis. =650 24$aPancaking. =650 24$aThermomechanical Processing. =700 1\$aAraujo, A.,$eauthor. =700 1\$aFindley, K.,$eauthor. =700 1\$aMatlock, D.,$eauthor. =700 1\$aSpeer, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 3 Special Issue on Acceleration of Alloy Design via Physical Process Simulation.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150012.htm =LDR 03762nab 2200553 i 4500 =001 MPC20140065 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2015\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC1503-EB$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20140065$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL875 =082 04$a620.419$223 =100 1\$aRahul, M.,$eauthor. =245 10$aCorrelation of Microstructure With HAZ Welding Cycles Simulated in Ti-15-3 Alloy Using Gleeble® 3800 and SYSWELD® /$cM. Rahul, G. Phanikumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2015. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aMetastable ?-titanium alloys are finding increasingly wider applications in structural components in aerospace, energy, and chemical industries because of their formability and heat-treatment possibilites. Components from these alloys are usually welded by processes, such as gas tungsten arc welding (GTAW), electron beam welding (EBW), and laser beam welding (LBW). Post-weld heat treatment improves the strength of the weld because of the precipitation of ? phase and TiCr2 particles. In ?-titanium alloys, the location, distribution and morphology of ? precipitates in ? matrix plays an important role in the performance of the welded components. In this work, we simulate different welding processes using SYSWELD® software and obtain realistic thermal cycles after calibrating the fusion zone dimensions with known experimental data. These cycles are then used to program the heat-affected zone (HAZ) cycles in Gleeble® 3800 to study their effect on the microstructure of the ?-titanium alloy. Both continuous and pulsed welding conditions are used for the welding process. Microstructure characterization was performed using scanning electron microscopy (SEM), electron back-scattered diffraction (EBSD), and transmission electron microscopy (TEM). Precipitates of ? phase below 0.2?m are seen to be uniform across the ? grain but the number density is not uniform across different grains of ?. We discuss the characterization results in light of existing models in the literature. The ? precipitation and hardness variation are correlated with welding cycles. A combination of computational and physical simulation tools is proposed to reduce the cycle to find optimal choice in the fabrication process design space. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFEM simulation. =650 \0$aphysical simulation. =650 \0$aPrecipitation. =650 \0$aWelding. =650 14$aFEM simulation. =650 24$aPhysical simulation. =650 24$aPrecipitation. =700 1\$aPhanikumar, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 4, Issue 3 Special Issue on Acceleration of Alloy Design via Physical Process Simulation.$dWest Conshohocken, Pa. :$bASTM International, 2015$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20140065.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120039 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120039$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120039$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD5658.I52 =082 04$a338.7/669142/0975412$223 =100 1\$aParker, Jonathan,$eauthor. =245 10$aAssessment of the Tempering Behavior of Grade 91 Steel /$cJonathan Parker, John Siefert, Kent Coleman. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b12 =520 3\$aAt any point in the fabrication and installation of Grade 91 components, undesirable metallurgical conditions can develop as a result of incorrect heat treatment. Industry techniques for locating and evaluating these microstructures using nondestructive methods are necessary. Field hardness testing is commonly utilized to characterize Grade 91 steel installed in plants. However, it is apparent that there are numerous variables that can affect the results of field hardness testing. Thus, the results can vary significantly depending on the equipment and procedures used. The present study has been undertaken to identify the accuracy of hardness measurements made under controlled laboratory conditions. Measurements were performed on samples that had been subjected to a range of different tempering conditions. The trend in these data provides information relevant to understanding the metallurgical behavior of this steel. Comparison of the data also indicates how measurements made using different hardness testers and methods can be used to assess component condition. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aComposition. =650 \0$aEmployee ownership. =650 \0$aHardness. =650 \0$aSteel industry. =650 14$aGrade 91 steel. =650 24$aComposition. =650 24$aHardness. =700 1\$aColeman, Kent,$eauthor. =700 1\$aSiefert, John,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120039.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130008 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130008$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130008$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.1/7$223 =100 1\$aChimbli, Sri,$eauthor. =245 10$aFailure Analysis on 410 Stainless Square-Head Bolts Failing Wedge Tensile Test /$cSri Chimbli. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b14 =520 3\$aASTM A193-12, grade B6 (Gr.B6), 3/4 in. (19.05 mm) in diameter by 4 in. (101.6 mm) in length, square-head bolts were breaking at the head to shank juncture during wedge tensile testing. Specimens from the same lot did meet the requirements of Gr.B6 for tensile strength, hardness, reduction of area, and elongation. Failure analysis was performed on the lot to indicate whether the discrepancy is with integrity of steel, forging or heading process, or the heat treatment. The investigation was carried out by dimensional inspection, visual inspection, chemical analysis, hardness and tensile test, scanning electron microscopy (SEM) analysis, and microstructure evaluation. SEM analysis indicated that the cause of fracture is because of embrittlement. The microstructure evaluation had showed the presence of tempered martensite in the core and needle martensite with retained austenite on the surface. Failure analysis concluded that cause of failure was because of the formation of unstable microstructure during heat treatment. The retained austenite with needle martensite structure had an average Vickers hardness (HV) of 301 at the surface and the tempered martensite structure had an average Vickers hardness of 262 HV at the core that led to a brittle failure on wedge tensile test. The lot was recommended to be re-tempered at 1180°F (637°C) with a holding time of 2.0 h to meet the requirements of wedge tensile testing. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aB6 bolt-head failures. =650 \0$aB6 bolts temper embrittlement. =650 \0$aB6 temper embrittlement. =650 \0$aBolt-head failures. =650 \0$aBuilding materials. =650 \0$aEngineering design. =650 \0$aNeedle martensite in 410 SS. =650 \0$aRetained austenite. =650 \0$aStainless steel. =650 \0$aWedge tensile test. =650 \0$aWedge tensile testing bolt. =650 14$aWedge tensile test. =650 24$a410 stainless steel. =650 24$aB6 bolt-head failures. =650 24$aB6 bolts temper embrittlement. =650 24$aB6 temper embrittlement. =650 24$aBolt-head failures. =650 24$aNeedle martensite in 410 SS. =650 24$aRetained austenite in 410 SS. =650 24$aWedge tensile testing bolt. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130008.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120044 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120044$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120044$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC175.16.P5 =082 04$a536/.401$223 =100 1\$aSurkialiabad, Roohallah,$eauthor. =245 10$aSimilar Tendency to Strain-Induced Martensite Transformation in Different Austenitic Stainless Steels /$cRoohallah Surkialiabad, Ali Hedayati. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b23 =520 3\$aThe formation of strain-induced martensite in metastable austenitic stainless steels depends on many parameters; the most well known and highly investigated of these is temperature. In this work, we suggest a new relationship between Md30/50, deformation temperature (DT), and martensite content based on data gathered from other studies and our experimental findings. For this purpose we rolled an AISI 304L stainless steel in different strains at 25°C, 0°C, and –15°C; then we characterized the steel via x-ray diffraction and Ferritescope studies to identify different phases and calculate their contents. According to the results, the relationship is as follows: If the delta value (DT – Md30/50) is the same for different austenitic stainless steels, they will form equal amounts of martensite under similar strain conditions. Moreover, both the delta value and the true strain have a strong effect on the formation of martensite. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAustenitic stainless steel. =650 \0$aCold deformation. =650 \0$aCritical phenomena (Physics) =650 \0$aEquilibrio E Transicoes De Fase. =650 \0$aPhase transformation. =650 \0$aPhase transformations (Statistical physics) =650 \0$aStrain-induced martensite. =650 14$aAustenitic stainless steel. =650 24$aCold deformation. =650 24$aPhase transformation. =650 24$aStrain-induced martensite. =700 1\$aHedayati, Ali,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120044.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130010 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130010$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130010$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD172.T6 =082 04$a546.6$223 =100 1\$aHayasi, M.,$eauthor. =245 10$aOptimizing the Brazing Variables for the Fully Dense Freeform Fabrication Process by Design of Experiments /$cM. Hayasi, B. Asiabanpour. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b11 =520 3\$aFully dense freeform fabrication (FDFF) is a process based on thin line cutting processes, variable thickness layering, slicing in different orientations, and bulk layer attachment. The combination of these capabilities enables the production of good quality complex parts from practically any material at a very fast pace. To improve the quality of the fabricated functioning products, multiple design and operational factors affecting the response value are required to be optimized. In this research, affecting factors (e.g., types of bonding materials, a range of heating temperatures, types of metal sheets, etc.) on the quality of the fabricated prototypes using a statistical design of experiments are investigated. Following the statistical analysis, the feasible bonding process in terms of optimal response value (tensile strength) that is achieved in regard with the most influential single or combined factors are presented. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDesign of experiments. =650 \0$aFully dense freeform fabrication. =650 \0$aMetal bonding. =650 \0$aMetal. =650 \0$aSoldering. =650 \0$aTransition metals. =650 14$aFully dense freeform fabrication. =650 24$aDesign of experiments. =650 24$aDOE. =650 24$aFDFF. =650 24$aMetal bonding. =650 24$aSoldering. =700 1\$aAsiabanpour, B.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130010.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120035 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120035$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120035$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC754.2.S75 =082 04$a538/.3$223 =100 1\$aSu, Fei,$eauthor. =245 10$aStudy of Magnetization Behavior of Glass-Coated Amorphous Ferromagnetic Microwires /$cFei Su, Xiaoyan Wang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b20 =520 3\$aIn this paper, two relevant problems are investigated. First, the residual stresses within glass-coated amorphous ferromagnetic microwires (AFMWs) subjected to thermal expansion mismatch and magnetostriction effect are analyzed using the finite element method; the effects of various design parameters (e.g., the thickness of the glass cover) on the residual stress are discussed as well. Then, based on the theory of micromagnetics, the magnetization states of AFMWs under the collective effects of stress and external axial magnetic field are analyzed. It has been found that the magnetization of AFMWs with negative saturation magnetostriction from –0.1 x 10–6 to –0.3 x 10–6 is sensitive to stress change, and external magnetic field of the proper amplitude can help to increase this sensitivity. This study should provide guidance on the optimal design of glass-coated AFMWs and their potential applications in tunable microwave composites and stress sensors. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFerromagnetism. =650 \0$aGlass-coated amorphous ferromagnetic microwires. =650 \0$aMagnetization. =650 \0$aMagnetostriction. =650 \0$aMicromagnetics. =650 \0$aRotational motion. =650 \0$aSpin waves. =650 \0$aStress. =650 14$aGlass-coated amorphous ferromagnetic microwires. =650 24$aMagnetization. =650 24$aMagnetostriction. =650 24$aMicromagnetics. =650 24$aStress. =700 1\$aWang, Xiaoyan,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120035.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120023 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120023$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120023$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.1/7$223 =100 1\$aMirzaev, D.,$eauthor. =245 10$aAnalytical Solution of the Problem of Diffusional Transformation Under Continuous Cooling Condition Based on Isothermal Transformation Diagram Data /$cD. Mirzaev, K. Okishev, K. Mirzaeva. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aThis paper is devoted to theoretical analysis of the critical cooling rate necessary to suppress the diffusional transformation of austenite. The transition from isothermal conditions to continuous cooling conditions was accomplished in two ways: by means of the traditional integral of Scheil and Steinberg (often called the additivity rule), and via direct integration of the Avrami equation. The resulting equations for both the cooling rate and a coefficient in Grange and Kiefer's formula are presented. It was found that the theoretical value of the Grange-Kiefer coefficient almost never reached the value of 1.5 that they proposed. A method for determining the parameters in kinetic equations describing isothermal and continuous cooling transformations from an experimental time-temperature transformation diagram is also outlined. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAustenite transformation. =650 \0$aAustenite. =650 \0$aAvrami equation. =650 \0$aContinuous cooling transformation. =650 \0$aCritical cooling rate. =650 \0$aGrange-Kiefer formula. =650 \0$aScheil-Steinberg integral. =650 \0$aStainless steel. =650 \0$aTTT diagram. =650 14$aAustenite transformation. =650 24$aAvrami equation. =650 24$aContinuous cooling transformation. =650 24$aCritical cooling rate. =650 24$aGrange-Kiefer formula. =650 24$aScheil-Steinberg integral. =650 24$aTTT diagram. =700 1\$aMirzaeva, K.,$eauthor. =700 1\$aOkishev, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120023.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120009 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120009$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120009$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.23 =082 04$a548.028$223 =100 1\$aFernandes, F.,$eauthor. =245 10$aWear Evaluation of Pack Boronized AISI 1060 Steel /$cF. Fernandes, S. Heck, G. Totten, L. Casteletti. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b14 =520 3\$aBoronizing is used to obtain very high hardness and wear resistance on ferrous and non-ferrous materials and some super alloys. The process can be carried out in solid, liquid, or gaseous medium. In this work, samples of AISI 1060 steel were treated by the pack boriding method during 2 and 4 h at 900 and 1000°C. Optical microscopy, x-ray diffraction, and micro-hardness analyses were conducted and wear tests were performed using a micro-wear machine with a fixed-ball configuration. The pack boriding resulted in the formation of layers with high hardness and wear resistance. All the borided layers presented top hardness around 2000 HV (Vickers pyramid number). Raising time and temperature of treatment increased the layer thickness. X-ray diffraction patterns showed the presence of only Fe2B for samples treated at 900°C for 2 and 4 h. The samples borided at 1000°C for 2 and 4 h presented layers composed by a mixture of Fe2B and FeB. The wear resistance of the samples borided at 1000°C was higher than that borided at 900°C, probably because of the difference in chemical composition. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aOptical microscopy. =650 \0$aPack boronizing. =650 \0$aTransmission electron microscopy. =650 \0$aWear. =650 \0$aX-ray crystallography. =650 \0$aX-ray diffraction. =650 \0$aX-rays$xDiffraction. =650 14$aPack boronizing. =650 24$aOptical microscopy. =650 24$aWear. =650 24$aX-ray diffraction. =700 1\$aCasteletti, L.,$eauthor. =700 1\$aHeck, S.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120009.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130024 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130024$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130024$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA478 =082 04$a620.17$223 =100 1\$aManigandan, K.,$eauthor. =245 10$aInvestigating and Understanding the Bending Fatigue Response and Fracture Behavior of Two High Strength Steels /$cK. Manigandan, T. Srivatsan, T. Quick. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b26 =520 3\$aIn this paper, the results of a recent study aimed at understanding the bending fatigue response of two carbon steels is presented and discussed. The two carbon steels chosen are the ones preferred and used for a spectrum of industrial applications. Bend test specimens of the two carbon steels were prepared and conformed to specifications used in several earlier studies. The machined test specimens were deformed in bending fatigue over a range of maximum load, at a positive load ratio of 0.1, and the number of cycles to failure was recorded. The specific influence of chemical composition on bending fatigue life of the carbon steels is presented. The fracture surfaces of the deformed and failed specimens were examined in a scanning electron microscope to establish the macroscopic mode of fracture and to concurrently characterize the intrinsic features and establish the microscopic mechanisms governing fracture. The influence of nature of loading and maximum load on bending fatigue life is discussed in light of chemical composition and intrinsic microstructural features of the chosen carbon steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBending fatigue. =650 \0$aCarbon steel$xCracking. =650 \0$aCarbon steel$xHydrogen embrittlement. =650 \0$aCarbon steel. =650 \0$aCatalytic cracking. =650 \0$aFracture. =650 \0$aMechanisms. =650 \0$aMicrostructure. =650 14$aCarbon steel. =650 24$aBending fatigue. =650 24$aFracture. =650 24$aMechanisms. =650 24$aMicrostructure. =700 1\$aQuick, T.,$eauthor. =700 1\$aSrivatsan, T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130024.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130018 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130018$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130018$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQA273.6 =082 04$a519.2/4$223 =100 1\$aZhao, Yubo,$eauthor. =245 10$aIRI Estimation Using Probabilistic Analysis of Acoustic Measurements /$cYubo Zhao, J. McDaniel, Ming Wang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aThe United States is facing a challenge on repairing aging civil infrastructures because of limited resources allocation. The international roughness index (IRI) is a key quantity of road inspection data to aid officials in prioritizing road maintenance decisions, which allows them to be efficient with their resources. IRI measures both the road roughness and riders' comfort level. This paper introduces a probabilistic method that analyzes probability density function (PDF) of acoustic data collected from a vehicle-mounted microphone to estimate IRI. An analysis of noise source is conducted to support the accuracy of the approach. Compared to existing approaches, the present method is more economical, easier to install, and requires less space. Curves of probability density function (PDF), which show the probability of each sound pressure occurring over a stretch of road, are used to estimate IRI based on the principle that a probability distribution concentrates at low sound pressures over smooth roads and at high sound pressures over rough roads. This method is validated using data collected by a test vehicle that was driven around an engineered test track. Primary conclusions are: (1) the Weibull distribution performs better than normal and lognormal distributions; (2) the optimal Weibull distribution parameter is identified; and (3) the method performs well when applied to different pavement designs, namely, Superpave, Stone Matrix Asphalt (SMA), and Open Grade Friction Coarse (OGFC) =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAcoustic. =650 \0$aInternational roughness index. =650 \0$aProbabilistic analysis. =650 \0$aProbabilities. =650 \0$aRoad roughness. =650 \0$aWeibull distribution$vTextbooks. =650 \0$aWeibull distribution. =650 14$aRoad roughness. =650 24$aAcoustic. =650 24$aInternational roughness index. =650 24$aProbabilistic analysis. =650 24$aWeibull distribution. =700 1\$aMcDaniel, J.,$eauthor. =700 1\$aWang, Ming,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130018.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120007 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120007$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120007$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN690 =082 04$a669/.94$223 =100 1\$aVijeesh, V.,$eauthor. =245 14$aThe Effect of the Addition of Strontium and Cerium Modifiers on Microstructure and Mechanical Properties of Hypereutectic Al-Si (LM30) Alloy /$cV. Vijeesh, M. Ravi, K. Prabhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b39 =520 3\$aThe present work deals with the melt treatment of LM30 hypereutectic Al-Si alloy using cerium and strontium and the assessment of its effect on microstructure and properties of the alloy. The addition of cerium simultaneously modified both primary and eutectic silicon, leading to an increase in ultimate tensile strength, as well as the wear resistance of the alloy. It was found that the coefficient of thermal expansion of the alloy decreased on modification of the microstructure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCoefficient of thermal expansion (CTE) =650 \0$aEutectic alloys. =650 \0$aEutectic silicon. =650 \0$aGermanium. =650 \0$aMechanical properties. =650 \0$aPrimary silicon. =650 \0$aSilicon. =650 14$aAl-Si hypereutectic alloy. =650 24$aCoefficient of thermal expansion (CTE) =650 24$aEutectic silicon. =650 24$aMechanical properties. =650 24$aPrimary silicon. =700 1\$aPrabhu, K.,$eauthor. =700 1\$aRavi, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120007.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120003 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120003$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120003$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1087 =082 04$a668.9/2$223 =100 1\$aBerube, Keith,$eauthor. =245 10$aEffect of Resin Cure Recipe and Ambient Processing Temperature on the Material Properties of Marine Grade Polymer Matrix Composite Materials /$cKeith Berube, Roberto Lopez-Anido. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (29 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b97 =520 3\$aThe effects of the resin curing recipe and ambient processing temperature on the mechanical properties of composite laminates were investigated. Woven roving E-glass/vinyl-ester composite plates were fabricated with a pliable-bag vacuum assisted resin transfer molding process over a range of ambient temperatures and resin gel times commonly encountered when fabricating polymer composite parts for the marine industry. Standardized tests for Mode-I interlaminar fracture toughness, compression, constituent volume fraction, and Barcol hardness were conducted. Interlaminar fracture toughness exhibited the most variability among the measured properties. Although there were few direct correlations between the measured properties and the parameters in the study, there were several statistically significant differences that could not be discarded as random, as they were consistent among the replicate panels fabricated for each combination of parameters in the study. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aMaterial processing. =650 \0$aMaterial properties. =650 \0$aPolymer engineering. =650 \0$aPolymer matrix composites. =650 \0$aPolymerization. =650 14$aPolymer matrix composites. =650 24$aMaterial processing. =650 24$aMaterial properties. =700 1\$aLopez-Anido, Roberto,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120003.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130009 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130009$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130009$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN690 =082 04$a620.1/1299$223 =100 1\$aNeu, R.,$eauthor. =245 10$aPerformance and Characterization of TWIP Steels for Automotive Applications /$cR. Neu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (41 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b140 =520 3\$aThis article reviews the current state of the art in understanding twinning-induced plasticity (TWIP) steels with an emphasis on linking microstructure to mechanical behavior by means of microstructure-aware constitutive models. A materials selection exercise is conducted to substantiate that TWIP steels are more desirable than most other materials for use in structural and safety components of automobiles. Gaps in the knowledge of TWIP steels that are hindering their adoption for automotive applications are identified. This review concludes by suggesting fundamental research needs for promoting the design of TWIP steels with improved properties and performance for structural components in automotive applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aConstitutive models. =650 \0$aDislocations in crystals$xCongresses. =650 \0$aDislocations in crystals. =650 \0$aMaterials selection. =650 \0$aStructure-property relationship. =650 \0$aTwinning (Crystallography) =650 \0$aTwinning deformation. =650 \0$aTWIP steels. =650 14$aTWIP steels. =650 24$aConstitutive models. =650 24$aMaterials selection. =650 24$aStructure-property relationship. =650 24$aTwinning deformation. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130009.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130003 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130003$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130003$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK2960 =082 04$a621.3815/42$223 =100 1\$aGerosa, R.,$eauthor. =245 10$aMechanical Characterization of Single-Crystal Silicon PV Cells /$cR. Gerosa, M. Mauri, B. Rivolta, P. Silva. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b14 =520 3\$aThis paper describes standard and innovative methods for characterizing the mechanical properties of single-crystal silicon cells [orientation (100)] for photovoltaic applications. The knowledge of their mechanical properties is not completely known in the technical literature and this knowledge could enhance the results of modern simulation softwares. The silicon cells were investigated before and after an aging at 100°C for 100 h. In the technical literature, an annealing at temperatures ranging from 70°C up to 180°C is proposed as a possible way to reverse the degradation of such components caused by long-time exposure to daylight (light-induced degradation, LID), and to obtain a recovery of the efficiency. Nevertheless, little information about the influence of such an annealing on the panel mechanical performances is available. Universal instrumented hardness tests were carried out to estimate the Young's modulus; the fracture toughness was calculated by measuring the lengths of the cracks originated from the imprint corners. Moreover, the threshold load under which no cracks appear was estimated. Finally, bending tests were performed to evaluate the mechanical resistance. Such tests were carried out on a tensile testing machine after the design and the realization of suitable devices assembled on the machine standard fixtures. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aMechanical properties. =650 \0$aPhotovoltaic cells$xMaterials. =650 \0$aPV cells. =650 \0$aSilicon cells. =650 \0$aSilicon solar cells. =650 14$aPV cells. =650 24$aMechanical properties. =650 24$aSilicon cells. =700 1\$aMauri, M.,$eauthor. =700 1\$aRivolta, B.,$eauthor. =700 1\$aSilva, P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130003.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120020 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120020$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120020$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQA402.5 =082 04$a518/.282$223 =100 1\$aMahesh, K.,$eauthor. =245 10$aFormability and Microstructural Characterization of Sintered Powder Metallurgical Preforms of Dual-Phase Steel /$cK. Mahesh, S. Sankaran, P. Venugopal. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aIn an attempt to improve mechanical properties of powder metallurgical (P/M) preforms of ferrite-pearlite steel, a ferrite-martensite dual-phase P/M steel was produced through intercritical annealing. In the present paper, the densification characteristics and formability of sintered preforms of dual-phase P/M steel and its comparison with preforms of ferrite-pearlite P/M steel are presented. The elemental powders of required composition were thoroughly mixed and steel compacts with different preform densities were produced by applying recommended pressures. The sintered preform consisted of ferrite-pearlite microstructure whereas intercritically annealed preform contained fine martensite distributed in ferrite matrix. The variation in porosity for different preform densities was approximately in the range of 5 %-28 % for both the steels. Stage wise upsetting was performed to obtain the densification curves, and compression tests were carried out to estimate the apparent strength coefficient (Ka) and apparent strain-hardening exponent (na), to generate the forming limit diagram (FLD) for both the steels. With increasing mean preform density, the Ka values were increasing, whereas the na values were decreasing for both sintered and dual-phase steels. In FLD, the transition of Ka and na values was at critical transition density (CTD) of 6.43 g/cm3 and 6.15 g/cm3 for sintered and dual-phase steel, respectively. Thus, an increase of 4.5 % of safe zone limit in FLD was observed in dual-phase steel, which facilitates the selection of lower preform density for forming process. Interestingly, the contiguity ratio of the martensite phase was increasing with increase in the mean preform density, which changes significantly after CTD of 6.15 g/cm3 in dual-phase P/M steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aannealing. =650 \0$aContiguity ratio. =650 \0$aDensification. =650 \0$aDual-phase steel. =650 \0$aForming limit diagram. =650 \0$aIntercritical annealing. =650 \0$aSimulated annealing (Mathematics) =650 14$aDual-phase steel. =650 24$aContiguity ratio. =650 24$aDensification. =650 24$aForming limit diagram. =650 24$aIntercritical annealing. =700 1\$aSankaran, S.,$eauthor. =700 1\$aVenugopal, P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120020.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120028 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120028$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120028$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA347.F5 =082 04$a620.00151825$223 =100 1\$aSieber, T.,$eauthor. =245 14$aThe Influence of Varying Cell Sizes on the Tensile Behaviour of Open-Cell Foams /$cT. Sieber, T. Liedke, U. Mühlich, F. Ballani. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b47 =520 3\$aThe aim of this paper is to study the mechanical tensile properties of open-cell foam structures on the cell size variation by numerical simulations. For this purpose, random Laguerre tessellations were used, which allow the creation of foam structures with strongly varying cell sizes. First, a model was fitted to real open-cell foams based on x-ray computed tomography (XCT) scans by parameter optimization. Two more virtual foam models with different cell size variations were produced according to the first fitted one. Tensile properties of the model realizations were computed by finite-element analysis using beam elements. The numerical results were presented and discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFinite element method. =650 \0$aFinite elements. =650 \0$aMicrostructure. =650 \0$aNumerical simulation. =650 \0$aOpen-cell foam model. =650 \0$aRandom Laguerre tessellation. =650 \0$aTensile behaviour. =650 14$aMicrostructure. =650 24$aFinite elements. =650 24$aNumerical simulation. =650 24$aOpen-cell foam model. =650 24$aRandom Laguerre tessellation. =650 24$aTensile behaviour. =700 1\$aBallani, F.,$eauthor. =700 1\$aLiedke, T.,$eauthor. =700 1\$aMühlich, U.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120028.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130006 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130006$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130006$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.C43 =082 04$a620.1/404292$223 =100 1\$aEl-Labban, Hashem,$eauthor. =245 10$aPrediction of Mechanical Properties of Nano-Composites Using Vibration Modal Analysis :$bApplication to Aluminum Piston Alloys /$cHashem El-Labban, M. Abdelaziz, Mostafa Yakout, A. Elkhatib. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b36 =520 3\$aIn this work, aluminum piston alloy-based nano-composites of high strength and ductility with large damping capacity were produced. Ni particles and Al2O3 particles were used as reinforcing agents to produce three nano-composites by adding three mixtures of these particles to the melt of Al-Si piston alloy at 700°C and application of stirring and squeeze casting. In addition, three micro-composites were produced by adding Ni particles of different percentages to the melt of the same matrix alloy and application of mechanical stirring and squeeze casting with the same conditions. The microstructures of the different materials were investigated using optical and scanning electron microscopes. Energy-dispersive x-ray analysis was carried out to analyze the elements of the reinforcing and matrix materials. Ultimate tensile strengths and engineering strains of the unreinforced and reinforced materials were evaluated by carrying out tension tests at room temperature. Modal tests were also carried out to evaluate the dynamic characteristics: natural frequency and damping ratio. The tests showed that the ultimate tensile strengths, ductility, and damping capacity of these composites were improved by the increase of both Ni and/or Al2O3 contents. A dynamic life indicator (damping ratio divided by natural frequency) is calculated for each material and showed a significant increase with the increase of nano-particles and/or micro-particles. By carrying out the experiments at different conditions, the mechanical properties, modal characteristics (such as natural frequency and damping ratio), and life indicator can be correlated. By constructing relationships between these properties and dynamic characteristics, the vibration modal analysis can be used for prediction of these properties and characteristics non-destructively. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAl piston alloy. =650 \0$aCeramic materials$xMechanical properties. =650 \0$aCeramic-matrix composites$xMechanical properties. =650 \0$aComposite materials$xMechanical properties. =650 \0$aDynamic properties of composites. =650 \0$aMicro-structured materials. =650 \0$aNano-structured materials. =650 \0$aVibration modal analysis. =650 14$aAl piston alloy. =650 24$aDynamic properties of composites. =650 24$aMicro-structured materials. =650 24$aNano-structured materials. =650 24$aVibration modal analysis. =700 1\$aAbdelaziz, M.,$eauthor. =700 1\$aElkhatib, A.,$eauthor. =700 1\$aYakout, Mostafa,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130006.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120033 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120033$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120033$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a624.1/8$223 =100 1\$aSingh, R.,$eauthor. =245 10$aDevelopment and Characterization of Microstructure and Mechanical Properties of Heat-Treated Zr-2.5Nb Alloy for AHWR Pressure Tubes /$cR. Singh, A. Bind, J. Singh, J. Chakravartty, V. Thomas Paul, K. Madhusoodnan, Satyam Suwas, S. Saroja, A. Suri, S. Banerjee. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b26 =520 3\$aZr-2.5Nb Alloy is used in a cold-worked and stress-relieved (CWSR) condition as pressure tubes in Indian pressurized heavy water reactors (IPHWR). The life-limiting factor for pressure tubes is in-reactor dimensional changes caused by irradiation growth and creep resulting in diametral expansion and axial elongation. Recent work has indicated that heat-treated Zr-2.5Nb alloy may exhibit lower in-reactor dimensional changes vis-à-vis CWSR pressure tubes. The advanced heavy water reactor (AHWR) specification demands more stringent operating condition for the pressure tubes and it was decided to develop a new fabrication route for heat-treated Zr-2.5Nb alloy for possible application as pressure tubes in AHWR. In this work, the microstructural characterization and tensile properties evaluation was carried out using samples obtained from various stage of fabrication of water-quenched and aged Zr-2.5Nb alloy following a route similar to Fugen pressure tubes is discussed. The microstructure was characterized using optical and transmission electron microscopy. The chemical composition, morphology, and location of the precipitates formed during aging were studied using thin-foil electron microscopy and carbon extraction replica. Samples with its axes parallel to longitudinal (L) or transverse (T) direction of rolled plate were machined from quenched, cold-rolled, and aged material and were tested in tension at 25°C and 300°C. The microstructure and the tensile strength of the alloy processed in the present investigation were comparable to that of heat-treated pressure tubes used in Reaktor Bolshoy Moshchnosti Kanalniy (RBMK) and Fugen reactors. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAdvanced heavy water reactor. =650 \0$aComposite materials$xMechanical properties. =650 \0$aMicrostructure. =650 \0$aTensile properties. =650 14$aHeat-treated Zr-2.5Nb alloy. =650 24$aAdvanced heavy water reactor. =650 24$aMicrostructure. =650 24$aTensile properties. =700 1\$aBanerjee, S.,$eauthor. =700 1\$aBind, A.,$eauthor. =700 1\$aChakravartty, J.,$eauthor. =700 1\$aMadhusoodnan, K.,$eauthor. =700 1\$aSaroja, S.,$eauthor. =700 1\$aSingh, J.,$eauthor. =700 1\$aSuri, A.,$eauthor. =700 1\$aSuwas, Satyam,$eauthor. =700 1\$aThomas Paul, V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120033.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120032 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120032$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120032$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357.5.C38 =082 04$a620.1064$223 =100 1\$aMeged, Y.,$eauthor. =245 10$aCatastrophic Failure in Cavitation Erosion Testing /$cY. Meged. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b9 =520 3\$aCatastrophic failure of metallic test specimens under cavitation erosion conditions is evidenced by an increasing rate of material loss. The typical cumulative erosion-time curve for this type of failure is denoted as type C. This type of failure depends on the characteristics of the test material, the test method, and the severity of the test conditions. A review of 264 cavitation erosion-time curves, produced via seven test methods, reveals that type C curves are found with 18 % of the specimens and 58 % of the tests performed via the rotating disc test method. This study shows that type C erosion-time curves can be modeled, analyzed, and extrapolated by means of the transient response erosion model. The two main conclusions from this study are that (i) ductile metallic materials are vulnerable to catastrophic erosion failure under severe cavitation erosion conditions, and (ii) the most effective erosion test method for the detection and classification of these materials and conditions is the rotating disc method. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAnomalous erosion curve. =650 \0$aAstronomie. =650 \0$aCatastrophic failure. =650 \0$aCavitation erosion. =650 \0$aCavitation. =650 \0$aNominal erosion curve. =650 \0$aTime constant. =650 \0$aTime lag. =650 \0$aTransient response model. =650 \0$aUpper time limit. =650 14$aCatastrophic failure. =650 24$aAnomalous erosion curve. =650 24$aNominal erosion curve. =650 24$aTime constant. =650 24$aTime lag. =650 24$aTransient response model. =650 24$aUpper time limit. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120032.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120031 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120031$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120031$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQH61 =082 04$a579/.6$223 =100 1\$aLucon, Enrico,$eauthor. =245 10$aCertified Miniaturized Charpy Specimens for the Indirect Verification of Small-Size Impact Machines*Contribution of the National Institute of Standards and Technology (NIST), an agency of the U.S. government; not subject to copyright in the United States. /$cEnrico Lucon. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b19 =520 3\$aSmall specimen test techniques are becoming ever more popular as the need increases to characterize mechanical properties by the use of the smallest possible amount of material, because of various restrictions on material availability, irradiation, testing space, and other factors. The National Institute of Standards and Technology (NIST) is currently developing certified miniaturized Charpy V-notch (MCVN) specimens for the indirect verification of small-scale impact testing machines. The same materials used for NIST standard verification specimens are being evaluated at three energy levels (low, high, and super-high). Two specimen types are being investigated, denominated KLST (from the German Kleinstprobe, or “small specimen”) and RHS (reduced half-size). Several instrumented impact tests on miniaturized KLST and RHS specimens of low, high, and super-high energy have been performed and analyzed. The variability of MCVN data has been compared to that of full-size Charpy data from the same lots of test specimens. Although this can be considered as just the preliminary phase of this project, the results indicate that MCVN verification specimens can be used for the indirect verification of small-scale instrumented impact testers, both in terms of absorbed energy and maximum force. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aHorticulture. =650 \0$aIndirect verification. =650 \0$aMiniaturized Charpy specimens. =650 \0$aSmall animal culture. =650 \0$aSmall specimens. =650 \0$aSmall-scale impact tester. =650 \0$aZoological specimens$xCollection and preservation. =650 14$aIndirect verification. =650 24$aKLST. =650 24$aMCVN. =650 24$aMiniaturized Charpy specimens. =650 24$aRHS. =650 24$aSmall specimens. =650 24$aSmall-scale impact tester. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120031.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120026 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120026$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120026$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a624.1/8$223 =100 1\$aVillalón, Néstor,$eauthor. =245 10$aHeat Treating of a 718Plus Superalloy /$cNéstor Villalón, Octavio Covarrubias, Rafael Colás. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b28 =520 3\$aHot rolled rings made from nickel-based superalloys are used for the manufacture of rotating components in jet engines and land-based turbines. Contoured rings are attractive to manufacturers because they can simplify and improve manufacturing operations by reducing machining times and, in some cases, eliminating welding operations. ATI 718Plus is a nickel-based superalloy designed to achieve high strength and thermal stability at elevated temperatures while exhibiting good formability during forging operations, characteristics that making it a suitable alloy for the manufacture of contoured rings. This work presents the results of a series of solution and precipitation heat treatments of rings made from ATI 718Plus with the goal of optimizing their processing and mechanical behavior. Microstructural characteristics and mechanical properties are reported, including the results of tensile tests conducted at room temperature and at high temperature and of hardness and stress-rupture testing. The results of this work were implemented at a local factory to ensure the required mechanical properties of heat-treated parts. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aComposite materials$xMechanical properties. =650 \0$aHeat treating. =650 \0$aMechanical properties. =650 \0$aMicrostructure. =650 \0$aRing rolling. =650 14$aMicrostructure. =650 24$aATI 718Plus superalloy. =650 24$aHeat treating. =650 24$aMechanical properties. =650 24$aRing rolling. =700 1\$aColás, Rafael,$eauthor. =700 1\$aCovarrubias, Octavio,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120026.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130007 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130007$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130007$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTG416 =082 04$a624/.25$223 =100 1\$aKenno, Sara,$eauthor. =245 10$aResidual Stresses in Welded Stiffened Steel Plates-An Experimental Comparative Study /$cSara Kenno, Sreekanta Das, Ronald Rogge, Michael Gharghouri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b10 =520 3\$aThis paper examines the residual stress distributions at selected depths in three stiffened 350WT steel plates representing typical stiffened steel plates used in modern ship construction. Residual stresses can develop from the welding process, and the magnitude of these stresses can be high enough to cause an early onset of yielding. Therefore, fatigue or other failures can also occur when welding-induced residual stresses are combined with service-load-induced stresses. In this study, the welding-induced residual stresses of these stiffened steel plate specimens were quantified at the near surface using the X-Ray diffraction method and at various depths using the neutron diffraction method. Transverse and longitudinal stress components for all three specimens were collected and analyzed. The residual stress profiles determined from both methods were found to be similar. However, some disagreement was found within the heat-affected zone of the weld bead. This paper discusses the residual stress distributions found in the three specimens and compares the two methods of measurement. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDiffraction. =650 \0$aExperimental methods. =650 \0$aResidual stresses. =650 \0$aSteel plate deck bridges$xDesign and construction. =650 \0$asteel plate. =650 \0$asteel. =650 \0$aStiffened steel plate. =650 \0$aWelding-induced residual stresses. =650 14$aExperimental methods. =650 24$aDiffraction. =650 24$aResidual stresses. =650 24$aStiffened steel plate. =650 24$aWelding-induced residual stresses. =700 1\$aDas, Sreekanta,$eauthor. =700 1\$aGharghouri, Michael,$eauthor. =700 1\$aRogge, Ronald,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130007.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130016 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130016$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130016$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.F55 =082 04$a363.72/88$223 =100 1\$aJha, Bhagwanjee,$eauthor. =245 10$aSynthesis of Higher Grade Fly Ash Zeolite X From Fly Ash via Three-Step Fusion /$cBhagwanjee Jha, D. Singh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aSeveral researchers have established the fusion of fly ash-NaOH mixtures at 450°C to 900°C. The fly ash gets partially converted to zeolite X when the fused ash is further treated in a hydrothermal system. However, such a solid residue (the end product) exhibits a low cation-exchange capacity. A culprit of such a deficiency in zeolite is improper contact between the NaOH and the fly ash particles during their fusion. To enhance the degree of fusion, in the present study we attempted to demonstrate a three-step fusion technique that does not favor any further treatment in a hydrothermal system. Observed changes in the characteristics (cation exchange capacity, pore volume, pore area, mineralogy, and thermal stability) of the end product of three-step fusion corresponding to an NaOH/fly ash ratio equal to 1.0 proves the suitability of this fusion technique for the synthesis of a better grade of zeolite X (viz., Na-X and Na-Y) =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCation exchange capacity. =650 \0$aFly ash zeolite. =650 \0$aFly ash$xEnvironmental aspects. =650 \0$aFly ash$xIndustrial applications. =650 \0$aFly ash. =650 \0$aFusion. =650 \0$aPores. =650 14$aFly ash. =650 24$aCation exchange capacity. =650 24$aFly ash zeolite. =650 24$aFusion. =650 24$aPores. =700 1\$aSingh, D.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130016.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130013 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130013$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130013$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA484 =082 04$a620.1/66$223 =100 1\$aYanase, K.,$eauthor. =245 12$aA Study on the Multiaxial Fatigue Failure Criterion with Small Defects /$cK. Yanase. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aThis paper reexamines a multiaxial fatigue failure criterion in the presence of small defects. The criterion is based on the assumption that a Mode-I crack on a specified plane, termed a critical plane, plays a dominant role in the determination of fatigue strength. The present study extends previous research to propose a modified failure criterion in conjunction with a systematic computational scheme, and to conduct a detailed analysis of its predictive capability. Using the proposed computational scheme, the applied stress level for the multiaxial fatigue failure can be efficiently predicted for both in-phase and out-of-phase loadings. Additionally, a series of parametric studies was conducted to examine the material's sensitivity to the biaxial stress state with respect to the fatigue strength. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFatigue limit. =650 \0$afatigue. =650 \0$aLight metal alloys$xFatigue. =650 \0$aMetal fatigue. =650 \0$aMultiaxial fatigue. =650 \0$aSmall defect. =650 14$aMultiaxial fatigue. =650 24$a?area-parameter model. =650 24$aFatigue limit. =650 24$aMetal fatigue. =650 24$aSmall defect. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130013.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120042 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120042$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120042$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQ295 =082 04$a620.1126$223 =100 1\$aMcKeighan, Peter,$eauthor. =245 10$aNonlinear Load-Displacement Behavior Observed During Fracture Toughness Testing of Aluminum-Beryllium Material /$cPeter McKeighan, J. Donald, Mark Svilar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aIn fracture toughness testing on beryllium and aluminum-beryllium materials, the load-displacement response exhibits a significant amount of nonlinearity that requires special, nontraditional methods for analysis. This work is directed toward determining what causes this nonlinearity, focusing on plasticity and subcritical crack extension. Plasticity was indirectly assessed by varying the size of the fracture toughness specimen, whereas crack advance was monitored with unloading compliance during the fracture toughness tests. Neither of these influences appears to be the primary contributor to the nonlinearity. Rather, the range of loading employed during precracking influences the load-displacement response of the material. The central, more linear portion of the load-displacement response appears bounded at the low end by the crack opening load and at the high end by the maximum load applied during the terminal stage of precracking. This region of the load-displacement curve represents an alternative to the standard 20 % to 80 % maximum load analysis region. Although using this region for analysis offers the advantage of representing the portion of the curve where the crack is fully open and behaving in an elastic manner, it will likely increase the number of invalid tests as a result of violation of the Pmax/PQ < 1.1 criterion. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum-beryllium. =650 \0$aFracture mechanics. =650 \0$aFracture toughness. =650 \0$aLoad displacement. =650 \0$aMetals$xFracture. =650 \0$aNonlinear. =650 14$aAluminum-beryllium. =650 24$aAlBeMet162. =650 24$aFracture toughness. =650 24$aLoad displacement. =650 24$aNonlinear. =700 1\$aDonald, J.,$eauthor. =700 1\$aSvilar, Mark,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120042.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130001 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130001$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130001$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK5981 =082 04$a621.3818$223 =100 1\$aHasan, M.,$eauthor. =245 10$aStructure and Dielectric Properties of Pure and Zinc Oxide-Doped Barium Titanate /$cM. Hasan, K. Shorowordi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aThe effects of zinc oxide addition and sintering parameters on the structure and dielectric properties of barium titanate are observed. Different percentage of ZnO ranging from 0.30 to 1 wt. % is doped in barium titanate. Both the doped and undoped samples are sintered at temperatures ranging from 1250°C to 1325°C at different soaking times. The amount of densification of the doped and undoped samples is measured in terms of percentage theoretical density. Grain size and microstructural analysis is performed by a scanning electron microscope (SEM). Lattice parameters and tetragonality of doped and undoped barium titanate are calculated from x-ray diffraction pattern obtained from x-ray diffractometer (XRD) test. Dielectric properties of the samples are measured by an impedance analyzer. It is found that all the doped samples obtain their maximum percentage theoretical density at a lower sintering temperature compared to the undoped sample. SEM study reveals that the doped samples always show smaller grains compared to the undoped sample. Significant grain growth is observed in all of the samples at sintering temperatures above 1300°C. The evidence of surface melting is observed in 1 wt. % ZnO-doped sample soaked at 1325°C for 2 h. The presence of liquid at that sintering condition is explained by the doping mechanism of Zn2+ in BaTiO3. Correlation among the grain size, tetragonality, and dielectric properties of the doped and undoped samples are also discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBarium titanate. =650 \0$aCurie temperature. =650 \0$aDielectric properties. =650 \0$aElectro-acoustics. =650 \0$aPiezoelectricity. =650 \0$aPyroelectricity. =650 14$aBarium titanate. =650 24$aCurie temperature. =650 24$aDielectric properties. =650 24$aSEM. =650 24$aXRD. =650 24$aZnO dopant. =700 1\$aShorowordi, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130001.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120034 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120034$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120034$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN719.5 =082 04$a669.1413$223 =100 1\$aAtanda, P.,$eauthor. =245 10$aEffect of Ca-Mg and MgFeSi Graphite Nodularizers on the Nodular Graphite Characteristics of Ductile Cast Irons /$cP. Atanda, O. Olorunniwo, B. Imasogie. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b17 =520 3\$aThe study investigated the effect of a series of Ca-Mg and a commercial grade MgFeSi graphite nodularizers, Fe75Si, and NiFeSi inoculants on the nodular characteristics (particle size, excursion ratio, degree of sphroidization, nodule count, and shape factor/nodularity) of ductile cast irons produced using a 100 kg diesel fired rotary furnace. This was with a view to controlling the volatile and fading effects of magnesium as a graphite nodularizer in the cast iron melt. Heats of the rotary furnace melts were pre-desulphurized with a pre-determined amount of CaC2:Fe45%Si in ratio 3:1. Subsequently, each melt was treated with different ratios of Ca-Mg based master alloys and the cast irons produced were compared with a commercial grade MgFeSi treated cast iron produced under the same conditions. Post-treatment inoculation in each case was carried out using Fe-75-Si. Microstructural characterization was carried out to determine the graphite nodularity and distribution characteristics. The results showed that the cast iron treated with 1:4 ratio of Ca:Mg combination master alloy yielded the optimum graphite nodularity with ASTM type 1 graphite nodule features, which are comparable to cast irons produced using the commercial grade MgFeSi nodularizer. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDuctile iron. =650 \0$aExcursion ratio. =650 \0$aFundicao. =650 \0$aGraphite nodularizer. =650 \0$aIron, Nodular$xCongresses. =650 \0$aIron, Nodular. =650 \0$aMaster alloy. =650 \0$aNodularity. =650 \0$aNodule count. =650 \0$aShape factor. =650 14$aMaster alloy. =650 24$aDuctile iron. =650 24$aExcursion ratio. =650 24$aGraphite nodularizer. =650 24$aNodularity. =650 24$aNodule count. =650 24$aShape factor. =700 1\$aImasogie, B.,$eauthor. =700 1\$aOlorunniwo, O.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120034.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120016 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120016$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120016$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA459 =082 04$a620.1623$223 =100 1\$aSaeed, Adil,$eauthor. =245 10$aCorrosion Damage Analysis and Material Characterization of Sherman and Centaur-The Historic Military Tanks /$cAdil Saeed, Zulfiqar Khan, Eliza Montgomery. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b53 =520 3\$aA study of corrosion damage and material characterization of two historic military tanks, the Sherman and Centaur is reported. Experiments were conducted to analyse surface corrosion and corrosion propagation from surface to sub-surface. Significant surface corrosion was found, and this phenomenon was further facilitated by delamination failure mechanisms. Corrosion depth for the Sherman was approximately 110 ?m, where sulphide inclusions were detected in the sub-surface analysis. The Centaur's analysis showed corrosion pits at 100 ?m depth. These pits possess random geometrical configurations with evidence of sulphur, sodium, and calcium. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAlloys$xCorrosion. =650 \0$aCorrosion and anti-corrosives. =650 \0$aCorrosion. =650 \0$aMaterial characterization. =650 \0$aMetals. =650 \0$aMilitary vehicles. =650 \0$aMuseum environment. =650 \0$aSulphide inclusions. =650 14$aCorrosion. =650 24$aMaterial characterization. =650 24$aMilitary vehicles. =650 24$aMuseum environment. =650 24$aSulphide inclusions. =700 1\$aKhan, Zulfiqar,$eauthor. =700 1\$aMontgomery, Eliza,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120016.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130004 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130004$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130004$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC320.36 =082 04$a532$223 =100 1\$aKobasko, N.,$eauthor. =245 10$aCooling Capacity of Petroleum Oil Quenchants as a Function of Bath Temperature /$cN. Kobasko, Adriana Marques, L. Canale, G. Totten, V. Dobryvechir. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b37 =520 3\$aOther than water, the most common quenchants used for hardening steel are based on petroleum oil base stock. Cooling capacity is dependent on a number of variables including oil viscosity and additives, agitation, and bath temperature and is characterized by critical heat flux densities and heat transfer coefficients. It is shown here that there is an optimal quench oil temperature at which the critical heat flux density reaches its maximum value. Computational results are compared with results from earlier reports. These data show that the optimal quenching temperature for petroleum oils may be used to reduce the distortion of hardened steel parts. Different methods of determining critical heat flux densities and heat transfer coefficients were considered, and the most accurate results were obtained when proprietary software was used to solve an inverse problem that simultaneously yields the current and critical heat flux densities and heat transfer coefficients versus the surface temperature. The computational approach used to determine the cooling capacity of a quench oil as a function of bath temperature is discussed here. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCooling capacity. =650 \0$aCritical heat flux density. =650 \0$aDistortion. =650 \0$aFluid mechanics. =650 \0$aHeat flux$xResearch. =650 \0$aHeat transfer coefficient. =650 \0$aHeat$xTransmission. =650 \0$aOptimal temperature. =650 14$aCooling capacity. =650 24$aCritical heat flux density. =650 24$aDistortion. =650 24$aHeat transfer coefficient. =650 24$aOptimal temperature. =700 1\$aCanale, L.,$eauthor. =700 1\$aDobryvechir, V.,$eauthor. =700 1\$aMarques, Adriana,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130004.htm =LDR 03762nab 2200553 i 4500 =001 MPC20120048 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2013\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20120048$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20120048$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aBF432.A1 =082 04$a153.9/3$223 =100 1\$aVander Voort, George,$eauthor. =245 10$aIs There Possible Bias in ASTM E112 Planimetric Grain Size Measurements? /$cGeorge Vander Voort. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2013. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aThe claim made by Li in 1995 and 2011 publications that the Jeffries planimetric method of determining grain size presented in ASTM E112, as well as in DIN 50601 (it is the standard for every national and international grain size test method and is described in every textbook on quantitative metallography), is wrong and produces biased grain size ratings when the counts are low is incorrect. Li based this statement upon theoretical considerations described by Saltykov, who proposed using rectangles for the planimetric method, rather than circles, to minimize bias at low counts of the number of grains inside the circle. Saltykov, however, did not publish actual test data to back up this proposition. The count levels mentioned are far below those recommended by ASTM E112 for these methods, but they could be encountered in manual measurements of the size of very coarse grains (which might be performed but is rarely done). Actual grain size measurements using both test circles and rectangles, with a very wide range of grains within the test figures and intersecting their borders, showed that the ASTM Jeffries planimetric and Hilliard single-circle intercept methods produced statistically identical measures of the ASTM grain size G down to count levels far below what is recommended-down to 30 for (ninside + 0.5nintercepted) for the planimetric method and down to 20 grain boundary intersections (Pintersections) for the intercept method (well below the recommended minimums of 50 and 35, respectively). At levels below these limits, bias was small-mainly data scatter was observed at counts less than 10 for both methods. The Saltykov planimetric method using rectangles gave the best data, identical to the ASTM E112 data, with statistically identical grain size values down to 10, and it was bias free, but it also exhibited data scatter at counts less than 10. Li's counting method, however, produced more bias at low counts than any other method. His claims have no validity. His model did not evaluate the effect of varying the counting conditions, which was the basis of his claim about the creation of bias. Also, he did not do actual tests to prove that his model was valid and that his claim was correct. Models do not have any validity if they do not test the actual conditions and are not verified by actual experimental data. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBias in measurements. =650 \0$aBias. =650 \0$aGrain size. =650 \0$aJeffries planimetric method. =650 \0$aMinorities$xPsychological testing. =650 \0$aTest bias. =650 14$aGrain size. =650 24$aASTM E112. =650 24$aBias in measurements. =650 24$aHilliard single-circle intercept method. =650 24$aJeffries planimetric method. =650 24$aSaltykov planimetric method with rectangles. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 2, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2013$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20120048.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150068 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150068$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150068$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTD491 =082 04$a363.6/1/0973$223 =100 1\$aRêgo, G.,$eauthor. =245 10$aProduction of Aluminide Layers on Copper and Copper Alloy /$cG. Rêgo, G. Takeya, A. Neto, G. Totten, L. Casteletti. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b23 =520 3\$aIntermetallic coatings were produced on pure copper and aluminum-bronze substrates using the powder aluminizing process. The treatments were carried out at 550°C and 600°C during 30, 60, 120, and 180 min. The layers were characterized by optical and scanning electron microscopy (SEM) associated with energy dispersive spectroscopy (EDS), X-ray diffraction (XRD), and wear and hardness testing. The treatments performed at 600°C resulted in larger layer thicknesses compared to those produced at 550°C for both copper and bronze substrates. XRD analysis indicated the presence of intermetallic phases FeAl, FeAl3, and CuAl on aluminum-bronze. The layers produced on the Cu and aluminum-bronze substrates exhibited maximum hardness of approximately 750 HV and 870 HV, respectively. The adhesive wear resistance of all formed layers was higher than those of low-hardness substrates (100 HV in the case of copper and 300 HV for the aluminum-bronze). There were no significant differences in the wear resistances of the layers produced on the same substrate. The abrasion resistance of the aluminum-bronze layers were higher than those of the copper layers, because of the greater hardness of the layers formed on the aluminum-bronze. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum-bronze. =650 \0$aCopper$xMetabolism$xDisorders. =650 \0$aCopper$xToxicology. =650 \0$aCopper. =650 \0$aDrinking water$xCopper content. =650 \0$aIntermetallic coatings. =650 \0$aPack aluminized. =650 14$aCopper. =650 24$aAluminum-bronze. =650 24$aIntermetallic coatings. =650 24$aPack aluminized. =700 1\$aCasteletti, L.,$eauthor. =700 1\$aNeto, A.,$eauthor. =700 1\$aTakeya, G.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150068.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150069 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150069$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150069$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN799.C5 =082 04$a669/.734$223 =100 1\$aKasprzycka, E.,$eauthor. =245 10$aStructure and Properties of Duplex Layers Composed of Chromium and Titanium Carbides /$cE. Kasprzycka, J. Tacikowski, B. Bogdanski. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aThe structures and properties of the CrC-TiC type duplex layers with an intermediate chromium carbide sublayer and an outer one of titanium carbide, as well as of the TiC-CrC type layers with an intermediate titanium carbide sublayer and an outer one of chromium carbide, produced on steels, were investigated. The structure of the duplex layers produced on plain carbon and alloy steel was compared with the single layers. The microstructure and chemical composition of these layers was determined by means of optical and transmission electron microscopy and X-ray phase analysis. A spectral linear analysis of the Cr, Fe, and Ti concentration in the diffusion zone was performed by means of an X-ray microanalyzer. Proof was presented that the thickness of the outer TiC layer depends on the thickness of the intermediate chromium carbide sublayer. This sublayer slows down the formation of the outer TiC layer. The structure of the chromium carbide sublayer undergoes changes during the process formation of the titanium carbide layer. The hardness and tribological properties of the layers have been determined. A comparison of CrC-TiC and TiC-CrC duplex layers with the CrC and TiC single carbide layers was performed. It was shown that the tribological properties of the CrC-TiC duplex layers are better than those of the TiC-CrC duplex layers, and those of the CrC and TiC type single carbide layers. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aChromium alloys$xMetallurgy. =650 \0$aDiffusion chromizing/titanizing. =650 \0$aDiffusion/duplex carbide layers. =650 \0$aThermo-chemical treatment. =650 \0$aWear resistance. =650 14$aDiffusion chromizing/titanizing. =650 24$aDiffusion/duplex carbide layers. =650 24$aThermo-chemical treatment. =650 24$aWear resistance. =700 1\$aBogdanski, B.,$eauthor. =700 1\$aTacikowski, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150069.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150065 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150065$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150065$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.1/7$223 =100 1\$aMariani, F.,$eauthor. =245 10$aProduction and Characterization of Boride Coatings on Flame-Sprayed Martensitic Stainless Steel /$cF. Mariani, G. Takeya, Amadeu Lombardi, G. Totten, L. Casteletti. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b25 =520 3\$aThermal spray is a process with many industrial applications in surface protection against wear and corrosion. The benefits of these processes include increased component life and decreased equipment downtime. However, sometimes an even greater wear resistance is required for optimal results. In such cases, a secondary treatment may be performed to produce a duplex coating. The objective of this work is to evaluate the wear resistance of a borided flame-sprayed duplex coating using an AISI 410 martensitic stainless steel alloy and a flame-spray process. The boriding treatment was performed at 950°C with 2- and 4-h treatment time in liquid borax in which 10 wt. % of aluminum was added. Optical microscopy, scanning electron microscopy, energy-dispersive x-ray spectroscopy, x-ray diffraction, and Vickers micro-hardness were used to analyze the samples. Micro-adhesive wear tests were performed to evaluate the wear resistance of the coatings using the fixed-ball method. The duplex coating exhibited superior wear resistance and hardness. The flame-sprayed coating layer exhibited a base hardness of about 450 HV, which was increased four times to about 1950 HV by including the boriding treatment. The thickness of the borided layer was approximately 50 ?m. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBoriding. =650 \0$aBuilding materials. =650 \0$aDuplex coatings. =650 \0$aEngineering design. =650 \0$aFlame spray. =650 \0$aMartensitic stainless steel. =650 \0$aMicro-adhesive wear. =650 14$aFlame spray. =650 24$aBoriding. =650 24$aDuplex coatings. =650 24$aMartensitic stainless steel. =650 24$aMicro-adhesive wear. =700 1\$aCasteletti, L.,$eauthor. =700 1\$aLombardi, Amadeu,$eauthor. =700 1\$aTakeya, G.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150065.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150043 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150043$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150043$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.C3 =082 04$a671.3/6$223 =100 1\$aKikuchi, Y.,$eauthor. =245 10$aDLC Duplex Coating on High-Speed Tool-Steel Substrates Using Plasma Nitrocarburizing After Radical Nitriding /$cY. Kikuchi, R. Hanai, T. Shiroya, Y. Sakamoto. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b24 =520 3\$aDiamond-like carbon (DLC) is applied to a wide variety of fields in the industry because of its tribological properties and hardness. However, one of the major issues is the adhesion strength between DLC films and the metal substrate. Many efforts have been made to obtain a higher adhesion strength, such as the formation of an interlayer and the modification of the surface layer. In contrast, radical nitriding is one of the most suitable methods for the pretreatment of duplex coatings, because it makes it possible to increase the surface hardness while maintaining the roughness of the original surface. According to this process, a diffusion layer is formed in the surface region using state plasma control. In the present investigation, we used existing hot-wall plasma nitriding equipment to treat high-speed tool steel using both plasma nitrocarburizing and radical nitriding to form a DLC film. Our results indicated that radical nitriding formed a nitrogen-diffusion layer, followed by the formation of a carbon layer by nitrocarburizing without the formation of a brittle compound layer. It maintained surface roughness compared with the untreated substrate. Although the hardness of the steel did not improve, the resulting DLC films exhibited better adhesion to the treated-steel substrates than to the untreated ones. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAdhesion. =650 \0$aCase hardening. =650 \0$aDuplex coating. =650 \0$aNitriding. =650 \0$aPlasma nitrocarburizing. =650 \0$aSteel$xHeat treatment. =650 14$aDuplex coating. =650 24$aAdhesion. =650 24$aDLC. =650 24$aNitriding. =650 24$aPlasma nitrocarburizing. =700 1\$aHanai, R.,$eauthor. =700 1\$aSakamoto, Y.,$eauthor. =700 1\$aShiroya, T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150043.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150067 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150067$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150067$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aPereira, R.,$eauthor. =245 10$aCharacterization of Layers Produced by Boriding and Boriding-PVD on AISI D2 Tool Steel /$cR. Pereira, F. Mariani, A. Neto, G. Totten, L. Casteletti. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b17 =520 3\$aBoride layers with high hardness and wear resistance were produced on AISI D2 tool steel by thermo-reactive treatment using borax with the addition of 10 wt. % aluminum. Subsequently, PVD treatments were performed on the borided layer. The samples were characterized using optical microscopy, scanning electron microscopy, X-ray diffraction, micro-hardness testing, and free-ball micro-abrasive wear test. The boriding treatment time was 4 h, followed by cooling in oil or air. The average thickness of the borided layers was 120 ?m with a hardness ranging from 1400 to 1700 HV. The micro-abrasive wear tests were performed using an abrasive solution of silicon carbide. All layers produced exhibited a wear resistance much higher than that of the substrate. Samples with duplex PVD plus boriding treatments yielded the best wear performance, followed by the borided steel samples, and finally, the untreated quenched and tempered samples. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBoriding. =650 \0$aDuplex coating. =650 \0$aMicro-abrasive wear. =650 \0$aPVD. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 14$aAISI D2. =650 24$aBoriding. =650 24$aDuplex coating. =650 24$aMicro-abrasive wear. =650 24$aPVD. =700 1\$aCasteletti, L.,$eauthor. =700 1\$aMariani, F.,$eauthor. =700 1\$aNeto, A.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150067.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150066 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150066$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150066$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aTakeya, Gustavo,$eauthor. =245 10$aCharacterization of Coatings Obtained by Boriding Niobizing Treatment of an AISI H13 Steel /$cGustavo Takeya, Fábio Mariani, Amadeu Neto, George Totten, Luiz Casteletti. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aWear is responsible for numerous industrial problems leading to increased maintenance costs due to the necessity of replacing worn components or due to equipment failure and manufacturing process downtime. Surface treatments can improve performance because the component maintains its ductile interior but with significantly improved surface wear resistance while using a minimal amount of material. Niobizing the surface of tool steel leads to the formation of very hard coatings, in the range of 2300 HV, composed of niobium carbide but with limited thickness. Boriding also produces very hard coatings, on order of 2000 HV, but with a much thicker layer than attainable by the niobizing treatment. If both were applied to the same material they could potentially complement each other by forming a duplex coating with a thin, but very hard, surface coating supported by an inner layer with slightly lower hardness but substantially thicker. The objective of this work was to evaluate the wear resistance of a coating formed by the niobizing and boriding diffusion treatments. Boron and niobium coatings were prepared on AISI H13 tool steel by thermo-reactive diffusion treatment in molten borax with 10 wt% aluminum followed by the niobium carbide pack process. The boriding treatment was performed at 900°C for 2 h, followed by a pack process at 1000°C for 2, 4, and 6 h. Optical microscopy, scanning electron microscopy, energy-dispersive X-ray spectroscopy, X-ray diffraction, micro-adhesive wear test, and Vickers micro-hardness were used to analyze the samples. The boriding and niobium carbide pack process produced coatings with thicknesses above 45 and 4 ?m, respectively. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBoriding. =650 \0$aBoriding-niobizing. =650 \0$aDuplex coatings. =650 \0$aMicro-adhesive wear. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 14$aAISI H13 steel. =650 24$aBoriding. =650 24$aBoriding-niobizing. =650 24$aDuplex coatings. =650 24$aMicro-adhesive wear. =700 1\$aCasteletti, Luiz,$eauthor. =700 1\$aMariani, Fábio,$eauthor. =700 1\$aNeto, Amadeu,$eauthor. =700 1\$aTotten, George,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150066.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150071 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150071$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150071$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD181.F1 =082 04$a546/.7312$223 =100 1\$aJasinski, J.,$eauthor. =245 10$aDuplex Titanium Oxide Layers for Biomedical Applications /$cJ. Jasinski, L. Kurpaska, M. Lubas, J. Jasinski, M. Sitarz. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aThis article presented the results of Ti Grade 2 oxidation with the duplex/hybrid method, which combined fluidized bed atmospheric diffusive treatment (FADT) and treatment with plasma methods (PVD). The process was realized to form a titanium diffusive layer saturated with oxygen in the diffusion process and to produce a tight homogeneous oxide coating on Ti substrate, deposited with the magnetron spraying technique. The techniques applied made it possible to combine the synergetic effects of the layers generated and to reduce the stresses in the area of the PVD coating/oxidized Ti substrate interface. In addition, the processes influenced the decrease in the surface roughness parameter and the increase in substrate bio-compatibility, which resulted in easier hydroxyapatite clusters deposition. The diffusion process was realized in Al2O3 fluidized bed reactor, at 913 K for 8 h with air atmosphere, while the deposition of the oxide coatings was realized with magnetron sputtering, with the use of TiO2 target at a pressure of 3 x 10–2mbars. In order to assess the effects of Ti hybrid oxidation, microscopic (AFM, SEM, TEM-EFTEM), spectroscopic (GDOS), and X-ray tests (XRD, sin2?) were performed. The coatings formed had structure, with a Ti?(O) diffusion zone and a TiO2 rutile and anatase oxide zone deposited on the substrate. It was concluded that hybrid method of duplex coatings formation (FADT + PVD) leads to reducing oxide layer defects after fluidized bed heat treatment and to generating a tight homogeneous layer with a favorable state of stress, which results in improving the bio-compatibility of the generated substrate, important from the biomedical applications point of view. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBioactivity. =650 \0$aDuplex layer. =650 \0$aFluorine compounds. =650 \0$aGases, Rare. =650 \0$aHybrid treatment. =650 \0$aHydroxyapatite. =650 \0$aOxidation. =650 \0$aSCIENCE$xChemistry$xInorganic. =650 14$aTi grade 2. =650 24$aBioactivity. =650 24$aDuplex layer. =650 24$aHybrid treatment. =650 24$aHydroxyapatite. =650 24$aOxidation. =700 1\$aJasinski, J.,$eauthor. =700 1\$aKurpaska, L.,$eauthor. =700 1\$aLubas, M.,$eauthor. =700 1\$aSitarz, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150071.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160042 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160042$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160042$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ1075 =082 04$a621.8/9$223 =100 1\$aOrtega-Saenz, J.,$eauthor. =245 10$aMicro-Abrasive Wear Testing of Surface Engineered Surgical Grade CoCrMo Alloy for Biotribological Applications /$cJ. Ortega-Saenz, M. Hernandez-Rodriguez, R. Michalczewski. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aWear of metal-on-metal hip joints is a concern due to the toxicity and biological reaction of wear debris. Retrieved CoCrMo hip implants have shown that abrasive wear is the predominant failure mechanism in such joints. There have been some efforts to improve the wear resistance of joint implants through the application of hard biocompatible ceramic coatings. However, the adhesion of the coatings has been a concern. The aim of the present work was to study the wear resistance of surface engineered CoCrMo alloy intended for biotribological applications by means of an abrasive wear test, based on the ball-crater technique. Different surface conditions were obtained on surgical grade wrought CoCrMo alloy: plasma nitrided, physical vapor deposition (PVD) coated (monolayer CrN and multilayer (TiN/CrN)x3) and modified using duplex surface engineering technology (a combination of the two previous approaches: plasma nitriding followed by plasma assisted PVD). The engineered surfaces were characterized by scanning electron microscopy, nanoindentation and, atomic force microscopy (AFM). Scratch test was used to determine the influence of the duplex technology on the adhesion of the coatings to substrate. The wear resistance of the different surface conditions was determined using a slurry abrasive micro-abrasion testing device. It was found that the duplex engineering technology enables a significant rise in the resistance of surfaces against concentrated loading modes, improving the adhesion of the coatings to the substrate; however, it has no significant influence improving the wear resistance of the samples during the abrasive wear tests. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCoCrMo alloy. =650 \0$aDuplex system. =650 \0$aMicro-abrasion. =650 \0$aPhysical vapor deposition (PVD) coatings. =650 \0$aTribology. =650 14$aMicro-abrasion. =650 24$aCoCrMo alloy. =650 24$aDuplex system. =650 24$aPhysical vapor deposition (PVD) coatings. =650 24$aTribology. =700 1\$aHernandez-Rodriguez, M.,$eauthor. =700 1\$aMichalczewski, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160042.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150052 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150052$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150052$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN757 =082 04$a672.823$223 =100 1\$aNishimoto, A.,$eauthor. =245 10$aEffect of Surface Deposited Layer on Active Screen Plasma Nitriding /$cA. Nishimoto, T. Tanaka, T. Matsukawa. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b36 =520 3\$aThe nitriding process is widely used to improve the tribological properties and wear resistance of metal surfaces. An “edge effect” occurs due to distortions of the electric field around the corners and edges of the components, although the components are well heated. This results in nonuniformity in properties such as the hardness and thickness of the surface layer. Recently, there has been considerable interest in active screen plasma nitriding (ASPN). In this process, the edge effect is completely eliminated because the plasma is produced on the cage and not directly on the samples, and sputtering of material from screen is important for ASPN. In this study, austenitic stainless steel AISI 316L and silicon (Si) were nitrided by ASPN to investigate the effect of surface deposits from the screen. ASPN experiments were carried out using a DC plasma-nitriding unit. The sample was placed on the sample stage in a floating potential and isolated from the cathodic screen and the anode. The screen, which was AISI 316L expanded metal with 38 % open area ratio, was mounted on the cathodic stage around the sample stage. ASPN was performed in 25 % N2 + 75 % H2 atmosphere for 7.2-90 ks at 673 K under 200 Pa. After nitriding, the nitrided samples were examined using scanning electron microscopy, X-ray diffraction, Vickers microhardness, and glow discharge optical emission spectroscopy. The nitrogen-expanded austenite (S phase) was formed on the surface of both samples. Additionally, γ-Fe4N and CrN were also formed on the Si surface. The thickness of the surface deposited layer increased linearly with increasing nitriding time. That of the nitriding layer of S phase also increased, whereas the deviation from parabolic law was observed. This result suggested that the surface deposited layer suppressed the formation of a nitriding layer. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aActive screen plasma nitriding. =650 \0$aAustenitic stainless steel. =650 \0$aDeposited layer. =650 \0$aExpanded austenite. =650 \0$aIron nitride. =650 \0$aSurface modification. =650 14$aSurface modification. =650 24$aActive screen plasma nitriding. =650 24$aAustenitic stainless steel. =650 24$aDeposited layer. =650 24$aExpanded austenite. =650 24$aIron nitride. =700 1\$aMatsukawa, T.,$eauthor. =700 1\$aTanaka, T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150052.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150074 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150074$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150074$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQP372 =082 04$a152.8$223 =100 1\$aKasprzycka, E.,$eauthor. =245 10$aProperties of CrC+(Ni-W) Duplex Layers Produced in Vacuum Chromizing Process Combined With Galvanic Treatment /$cE. Kasprzycka, B. Bogdanski. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aDiffusion chromizing was applied to increase the durability of tools, which operate under wear conditions. Vacuum chromizing, as opposed to other known methods, i.e., powder pack, gas, and molten salt baths, is ecological on account of non-toxic substrates, as well as absence of harmful wastes. Vacuum chromizing of tool steel results in hard and wear resistant chromium carbide coatings. However, the obtained carbide layers exhibited rather poor corrosion resistance in chloride media. To improve their corrosion resistance, Ni-W alloy was deposited electrolytically on the steel surface before the chromizing process. This resulted in the formation of CrC+(Ni-W) type duplex layers with modified characteristics. The objective of this paper was to determine the structure of these duplex layers on tool steel surface, their tribological properties and corrosion resistance in chloride solutions. Investigations of layers' thickness, their morphology, phase composition, hardness, and depth profiles of elements in the layer diffusion zone have been carried out. The chemical composition and distribution of the phases formed in the surface region of the samples were examined by a SEM microscope, equipped with a BSE detector and an EDS spectrometer. Wear resistance tests were carried out by the three-cylinder-cone method. Electrochemical corrosion measurements of obtained layers were performed in a 0.5 M NaCl solution. The tests proved that the wear resistance of duplex layers of the CrC+(Ni-W) type, produced by vacuum chromizing of electrolytically coated steel, is as good as that of carbide layers of the CrC type, produced on bare steel surface, but their corrosion resistance is higher. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCorrosion resistance. =650 \0$aDuplex layers. =650 \0$aGalvanic Skin Response. =650 \0$aGalvanic treatment. =650 \0$aPsychology. =650 \0$aPsychophysiology. =650 \0$aVacuum chromizing. =650 \0$aWear resistance. =650 14$aVacuum chromizing. =650 24$aCorrosion resistance. =650 24$aDuplex layers. =650 24$aGalvanic treatment. =650 24$aWear resistance. =700 1\$aBogdanski, B.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150074.htm =LDR 03762nab 2200553 i 4500 =001 MPC20150064 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2016\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20150064$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20150064$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD9539.N52 =082 04$a307.7/66/095984$223 =100 1\$aMariani, F.,$eauthor. =245 10$aWear Behavior of a Borided Nickel-Based Self-Fluxing Thermal Spray Coating /$cF. Mariani, G. Rêgo, A. Neto, G. Totten, L. Casteletti. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2016. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b22 =520 3\$aIncreasing the hardness of materials used in machines can lead to a longer useful life while decreasing maintenance downtime. However, high hardness usually results in an increase in brittleness of the material, which can be avoided by surface treatments, such as thermal spray coatings that are largely used to produce coatings with high resistance to wear and corrosion. This method has advantages, such as easy application, relatively inexpensive in comparison with other methods, and does not increase the brittleness of the base material. However, in some applications, the wear resistance may not be sufficient. To further improve the wear resistance of these coatings, a thermochemical boriding treatment can be subsequently applied to produce a duplex coating. In this work, an SAE 1020 steel was used as the substrate for the application of a thermal sprayed surface coating. The alloy applied is nickel based and self-fluxing with composition NiCrBSiC. The boriding treatment was subsequently performed at 850°C for 2 h. Optical microscopy, scanning electron microscopy, energy-dispersive X-ray spectroscopy, X-ray diffraction, and Vickers micro-hardness and micro-abrasive wear tests were used to characterize the samples. The flame spray produced coatings of approximately 900 HV, which was increased to 1600 HV after the boriding treatment. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBoriding. =650 \0$aDuplex coatings. =650 \0$aEconomic anthropology. =650 \0$aEconomic history. =650 \0$aFlame spray. =650 \0$aMicro-abrasive wear. =650 \0$aNi-based self-fluxing alloy. =650 \0$aThermal spray. =650 14$aThermal spray. =650 24$aBoriding. =650 24$aDuplex coatings. =650 24$aFlame spray. =650 24$aMicro-abrasive wear. =650 24$aNi-based self-fluxing alloy. =700 1\$aCasteletti, L.,$eauthor. =700 1\$aNeto, A.,$eauthor. =700 1\$aRêgo, G.,$eauthor. =700 1\$aTotten, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 5, Issue 4 Special Issue on Duplex and Multiplex Coatings.$dWest Conshohocken, Pa. :$bASTM International, 2016$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20150064.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130056 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130056$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130056$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQ295 =082 04$a620.1126$223 =100 1\$aKourkoulis, S.,$eauthor. =245 10$aFracture Toughness Determined by the Centrally Cracked Brazilian-Disc Test :$bSome Critical Issues in the Light of an Alternative Analytic Solution /$cS. Kourkoulis, C. Markides. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (42 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b70 =520 3\$aThe centrally cracked Brazilian-disc test is among the configurations proposed for the experimental determination of fracture toughness of brittle rock-like materials. In spite of its wide use and the fact that the test is already standardized by the International Society for Rock Mechanics (ISRM), quite a few issues are still open related especially to the exact expressions of the respective stress intensity factors (SIFs) and the actual shape of the crack during loading. The latter is crucial since for specific crack inclinations, the crack lips are coming in contact and contact stresses appear which alter the boundary conditions, rendering analytic solutions erroneous. In this context, an alternative analytic approach is here introduced assuming that the cracked disc is under uniform pressure along two finite symmetric arcs of its periphery. The main advantage of the present approach is that it provides physically acceptable results independently of whether the crack is under opening- or closing-mode. The results of the analysis are validated against experimental data obtained using the method of Caustics and the Digital Image Correlation (DIC) technique. Based on the analytic solution, some critical practical aspects of the cracked Brazilian-disc test are explored including the influence of the loading type and the length of the loaded arc, the role of the specimen's thickness, the range of crack inclination angles for which generation of contact stress is unavoidable, and the rotation of the crack axis. Moreover, a redefinition of the SIFs in case of Mixed Fundamental problems is proposed. The limitations of the analysis are critically considered and finally some thoughts about the future steps concerning the fracture toughness determination using the cracked Brazilian-disc test are discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aClosing cracks. =650 \0$aComplex potentials. =650 \0$aCracked Brazilian disc. =650 \0$aFracture mechanics. =650 \0$aFracture toughness. =650 \0$aLinear elasticity. =650 \0$aMetals$xFracture. =650 \0$aRock-like materials. =650 14$aCracked Brazilian disc. =650 24$a“overlapping”. =650 24$aClosing cracks. =650 24$aComplex potentials. =650 24$aFracture toughness. =650 24$aLinear elasticity. =650 24$aRock-like materials. =650 24$aStress intensity factors (SIFs) =700 1\$aMarkides, C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130056.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130082 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130082$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130082$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD1 =082 04$a543.081$223 =100 1\$aGhidini, A.,$eauthor. =245 10$aSteels for Plastic Molding :$bRelationship between Mechanical and Microstructural Properties /$cA. Ghidini, B. Rivolta, G. Silva, R. Gerosa. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aIn the automotive world, many components are produced by polymer injection using steel molds with very large sizes, up to 1 m x 1 m sections or even larger. These steels should have good thermal conductivity, good weldability, high machinability, and good disposition to polishing and photoengraving. Moreover, high toughness and high mechanical properties across the whole mold thickness are strongly desired and appreciated. To satisfy these demands, chemical composition and heat-treatment cycles shall be properly designed and optimized. The traditional tensile and impact tests are useful for a basic characterization of the material, whereas the fracture toughness is related to an advanced and deeper analysis. Nevertheless, traditional tests are easier to be carried out and, hence, they are often preferred instead of the more complicated fracture-toughness tests. In this paper, the authors considered different mold steels as an attempt to correlate the fundamental mechanical parameters (i.e., the yield stress, the UTS, the elongation at rupture, and the absorbed impact energy) and the microstructures to the fracture toughness. Surface and core sampling position will be considered. The analysis of the available data resulted in very good correlations among the impact energy and the mechanical properties and among the fracture toughness and the impact energy. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBiomedical research. =650 \0$aFracture toughness. =650 \0$aMechanical properties. =650 \0$aMicro Engineering. =650 \0$aMicrostructures. =650 \0$aSteels for plastic molds. =650 14$aSteels for plastic molds. =650 24$aFracture toughness. =650 24$aMechanical properties. =650 24$aMicrostructures. =700 1\$aGerosa, R.,$eauthor. =700 1\$aRivolta, B.,$eauthor. =700 1\$aSilva, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130082.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130084 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130084$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130084$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.170287$223 =100 1\$aMourad, A-H.,$eauthor. =245 10$aNovel Technique for Normalizing Load-Displacement Curves in Fracture Testing /$cA-H. Mourad, Aladdin Abu-Assi, Fahmy Haggag, Yuh Chao. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b33 =520 3\$aFracture experiments conducted as part of research on stable crack behavior in low alloy steel (EN 34NiCrMo6) are analyzed and presented. CT specimens of low constraint (section slenderness ratio, b0/B ~ 6), with various crack depth and different loading angles, ?, were investigated. Analysis of the load displacement curves revealed that the initiation load is found to be the same when normalized to the maximum load, Pmax. The load-line displacement ?LL at Pmax (?Pmax) was also found to have a single value. Hence the load displacement curves were presented as a unique normalized P-?LL curve. These normalized curves demonstrate having a single “representative/trend” curve that characterises the stable crack growth behavior. The proposed normalization technique was also applied to additional literature data on different materials with various specimen configurations and loading modes with success. This technique could also be useful in studying the fracture of low constraint specimens and contributing to the transferability issue for structural application. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aComposite materials$xFracture. =650 \0$aComposite materials$xTesting. =650 \0$aDuctile crack growth. =650 \0$aLow constraint specimens. =650 \0$aMixed-mode fracture. =650 \0$aNormalized load displacement curves. =650 \0$aThickness-independent load displacement curve. =650 14$aDuctile crack growth. =650 24$aLow constraint specimens. =650 24$aMixed-mode fracture. =650 24$aNormalized load displacement curves. =650 24$aThickness-independent load displacement curve. =700 1\$aAbu-Assi, Aladdin,$eauthor. =700 1\$aChao, Yuh,$eauthor. =700 1\$aHaggag, Fahmy,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130084.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130071 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130071$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130071$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQ111 =082 04$a508 s$223 =100 1\$aCzerner, M.,$eauthor. =245 10$aWire Cutting Method to Assess Fracture Toughness of Gelatin Gels :$bPhenomenological Analysis and Limitations of Methodology /$cM. Czerner, L. Fasce, P. Frontini. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b30 =520 3\$aIn this work the performance of the wire cutting method for determining the fracture toughness, Gc, of gelatin hydrogels is assessed. In this method, wires of different diameters are pushed into a sample while the force and displacement are continuously recorded. The cutting action reaches a steady state, in which fracture propagation, deformation, and friction occur simultaneously. The method implies a linear relationship between the steady-state cutting force per unit sample width and the wire diameter, of which the y-intercept is Gc. Several gel samples differing in gelatin concentration, source (bovine or porcine), solvent (water or water-glycerol mixture), and crosslink type (physical or chemical induced by glutaraldehyde) were tested at different rates. Post-mortem fracture surfaces examined via optical microscopy displayed four different morphologies depending on the gel formulation, cutting rate, and wire diameter: I, striated; II, with one or two oblique straight lines; III, with rhombus-like figures; and IV, with material pull-out. A direct relationship between the developed fracture surface morphology and the method performance existed. One necessary condition for obtaining the linear relationship is a unique fracture surface morphology remaining for all of the wires utilized in the determination. The method is invalid if the fracture surface morphology changes with changing wire diameter, abnormal crack path deflection takes place, or material pull-out occurs as a result of adhesion effects. The applicability of the method seems to be not constrained to physical gels. An appropriate cutting rate and wire diameter have to be selected in order for a unique fracture surface morphology to be achieved. In such cases, reasonable Gc values were obtained from the y-intercept of the best linear fit of experimental data. Gc increased with increasing gelatin concentration, Bloom number, and solvent viscosity. Moreover, Gc was greater when a rhombus-like pattern was induced rather than other morphology due to greater crack path tortuosity. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFracture toughness. =650 \0$aGelatin gels. =650 \0$aGelatin. =650 \0$aLipids. =650 \0$aSoft materials. =650 \0$aWire cutting method. =650 14$aSoft materials. =650 24$aFracture toughness. =650 24$aGelatin gels. =650 24$aWire cutting method. =700 1\$aFasce, L.,$eauthor. =700 1\$aFrontini, P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130071.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130072 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130072$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130072$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS225 =082 04$a682$223 =100 1\$aBind, A.,$eauthor. =245 10$aFracture Toughness Evaluation of Zr-2.5Nb Pressure Tubes Manufactured Employing Double Forging for PHWR700 /$cA. Bind, R. Singh, H. Khandelwal, S. Sunil, J. Chakravartty, A. Ghosh, P. Dhandharia, D. Bachawat, S. Vijayakumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b33 =520 3\$aThe need for improvement of the in-reactor performance of Zr-2.5 % Nb pressure tubes arose because of the higher than expected diametral creep rates and variability in axial elongation observed in some of the pressure tubes of 220 MWe Indian pressurized heavy water reactors (IPHWR220). A systematic study revealed that the pressure tubes used in various IPHWR220 had variations in microstructure, mechanical properties, texture, and chemical composition. The forthcoming PHWR700 is expected to operate at a higher temperature than that of IPHWR220 pressure tubes coupled with ~3 % partial boiling toward the outlet end. The IPHWR220 pressure tubes were manufactured by NFC (Hyderabad, India) using the combination of extrusion-double pilgering with intermediate annealing and with 20 % final cold work. PHWR700 pressure tubes have been manufactured using a combination of forging-extrusion-single pilgering routes. The fracture behavior of cold-worked and stress-relieved Zr-2.5Nb pressure tube material manufactured employing a forging route for PHWR700 is described in this work as a function of hydrogen content (4 and 60 wppm), temperature (25°C-300°C), and sample location. Fracture toughness tests were carried out as per ASTM E1820-06 [ASTM E1820-06: Standard Test Method for Measurement of Fracture Toughness-Designation, Annual Book of ASTM Standards, ASTM International, West Conshohocken, PA] using curved compact tension specimens of 17 mm width. The crack growth was along the axial direction of the tube and was measured using the direct current potential drop (DCPD) technique. The fracture toughness of as-received samples show weak dependency on test temperature, whereas samples having 50 ppm hydrogen show typical S curve behavior and regain toughness above 150°C. The variation in fracture toughness across tube length was within scatter band. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aForging industry$vPeriodicals. =650 \0$aForging industry. =650 \0$aForging$vPeriodicals. =650 \0$aForging. =650 \0$aFracture toughness. =650 \0$aPressure tubes. =650 14$aZr-2.5Nb alloy. =650 24$aForging. =650 24$aFracture toughness. =650 24$aPressure tubes. =700 1\$aBachawat, D.,$eauthor. =700 1\$aChakravartty, J.,$eauthor. =700 1\$aDhandharia, P.,$eauthor. =700 1\$aGhosh, A.,$eauthor. =700 1\$aKhandelwal, H.,$eauthor. =700 1\$aSingh, R.,$eauthor. =700 1\$aSunil, S.,$eauthor. =700 1\$aVijayakumar, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130072.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130073 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130073$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130073$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQ295 =082 04$a620.1126$223 =100 1\$aHosseini, Ali,$eauthor. =245 10$aEvaluation of Cracks in Thin-Walled Pipe Using JQ /$cAli Hosseini, Duane Cronin, Alan Plumtree. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b29 =520 3\$aFracture toughness measurements on small samples are often considered valid (size independent) for a limited range of toughness and sample dimensions. In the present work, it is demonstrated that standard toughness tests are transferrable to thin-walled pipe provided the specimen width and pipe wall thickness are the same. Fracture toughness and tensile tests were undertaken on 508 mm (20 in.) diameter Grade API-5L X52 line pipe with a wall thickness of 5.7 mm. J tests were conducted on samples containing surface flaws to evaluate the fracture toughness of the thin-walled line pipe steel using the ASTM E1820 procedure. Owing to geometry limitations, JQ was determined from the resistance curves (J versus crack extension). The average measured JQ was 197 kJ/m2 for 5.3 mm wide samples. A series of full-scale rupture tests with crack and crack-in-corrosion flaws were conducted and the failure pressures were predicted using API 579 and the JQ results. The average difference between the predicted and experimental failure pressures was 21.4 % for the cracks and 11.0 % for the crack-in-corrosion flaws, demonstrating that the FAD method can be used with toughness characterized using specimens of similar thickness to the pipe, although the toughness results are not geometry independent. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCrack evaluation. =650 \0$aCrack-in-corrosion. =650 \0$aFracture mechanics. =650 \0$aFracture toughness. =650 \0$aMetals$xFracture. =650 \0$aThin-walled pipe. =650 14$aFracture toughness. =650 24$aCrack evaluation. =650 24$aCrack-in-corrosion. =650 24$aThin-walled pipe. =700 1\$aCronin, Duane,$eauthor. =700 1\$aPlumtree, Alan,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130073.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130066 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130066$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130066$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC963.48 =082 04$a155.9/042$223 =100 1\$aBogdanov, S.,$eauthor. =245 10$aProbabilistic Analysis of the Fatigue Crack Growth Based on the Application of the Monte-Carlo Method to Unigrow Model /$cS. Bogdanov, S. Mikheevskiy, G. Glinka. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b23 =520 3\$aThis paper presents results obtained from the combination of the UniGrow fatigue crack growth model with Monte-Carlo simulation method. Four sets of available statistical fatigue crack growth data were used for the analysis. The material resistance to the fatigue crack propagation was modelled as a random input parameter while the geometry and loading conditions were kept deterministic. The measure of comparison was chosen to be the distribution of the number of cycles required to propagate the crack from a certain initial to the desired deterministic size. The difference between the “within specimen” and “from specimen to specimen” variability is assessed. Influence of the former on fatigue crack growth predictions is demonstrated to be negligible. It is shown that the probability distributions obtained from the numerical analysis closely resemble distributions obtained from the available experimental data. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFatigue crack growth. =650 \0$aFatigue. =650 \0$aMonte-Carlo simulation. =650 \0$aUnigrow. =650 \0$aWork Schedule Tolerance$xpsychology. =650 \0$aWorkload. =650 14$aFatigue crack growth. =650 24$aAl 2024-T3, Al 7075-T6. =650 24$aMonte-Carlo simulation. =650 24$aUnigrow. =700 1\$aGlinka, G.,$eauthor. =700 1\$aMikheevskiy, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130066.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130053 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130053$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130053$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQ295 =082 04$a620.1126$223 =100 1\$aGintalas, Marius,$eauthor. =245 10$aNew Equation for the Plastic Correction Factor ? for J-Integral Determination from Test Results of Three-Point-Bend Specimens /$cMarius Gintalas, Antanas Ziliukas, Robert Ainsworth. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b53 =520 3\$aWhen material yielding occurs, the stress intensity factor, K, no longer correctly characterizes the magnitude of the stress field around the crack tip. For significant amounts of yielding, the J-integral approach is applied as an advanced tool. In practice, for many engineering applications, the non-linear plasticity effects are of importance and therefore material behavior beyond yield needs an accurate description for input to tools for assessment. This work presents J-integral values of two different steel grades (1006 and 4340) using a newly developed analytical approach for the correction factors ?pl, which takes into account the elastic-plastic properties of the material. The evaluation approach is based on absorbed energies in a Charpy-sized specimen during the elastic and plastic deformation phases. Values of these energy terms were obtained via numerical simulation of 1006 and 4340 steel Charpy-sized specimens loaded in three-point-bending. This work highlights the effect of materials plastic properties on the J-integral. Different steel grades show different amounts of plasticity defined by the strain-hardening exponent and the strain-hardening constant and these influence the fracture parameters. Application of the plastic correction factor ?pl to Charpy-sized specimens, considering the respective plastic properties of the materials, leads to values of ?pl equal to 2.286 for 1006 steel and 2.621 for 4340 steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFracture mechanics. =650 \0$aFracture toughness. =650 \0$aLoad-line displacement. =650 \0$aMetals$xFracture. =650 \0$aThree-point-bend test. =650 14$aThree-point-bend test. =650 24$aFracture toughness. =650 24$aLoad-line displacement. =700 1\$aAinsworth, Robert,$eauthor. =700 1\$aZiliukas, Antanas,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130053.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130078 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130078$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130078$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7895.M4 =082 04$a621.39/732$223 =100 1\$aKuleshova, E.,$eauthor. =245 10$aEffect of Neutron Irradiation on Brittle Fracture Initiation in VVER-1000 Reactor Pressure Vessel Materials /$cE. Kuleshova, M. Artamonov, A. Erak. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aThis work contains fractographic analysis of base metal and weld metal specimens of a VVER-1000 reactor pressure vessel (RPV) in initial state and after neutron irradiation. In this work, two main types of brittle fracture origins were discovered for VVER-1000 RPV materials in different states-non-metallic inclusions and grain or subgrain boundaries, as well as the correlation between the cleavage initiation distance and critical stress-intensity factor KJc values for each type of fracture origin. In this paper, evolution of relative proportion between these two types of origins under neutron irradiation was also studied. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBrittle fracture. =650 \0$aCleavage initiation distance. =650 \0$aCritical stress-intensity factor KJc. =650 \0$aFracture origin. =650 \0$aFracture toughness. =650 \0$aNeutron irradiation. =650 \0$aNuclear physics. =650 \0$aRadiation dosimetry. =650 \0$aReactor pressure vessel steel. =650 \0$aSemiconductor storage devices. =650 14$aReactor pressure vessel steel. =650 24$aBrittle fracture. =650 24$aCleavage initiation distance. =650 24$aCritical stress-intensity factor KJc. =650 24$aFracture origin. =650 24$aFracture toughness. =650 24$aNeutron irradiation. =700 1\$aArtamonov, M.,$eauthor. =700 1\$aErak, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130078.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130068 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130068$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130068$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA347.F5 =082 04$a620.00151825$223 =100 1\$aKanerva, M.,$eauthor. =245 10$aApparent Fracture Toughness Versus Micro-Scale Fracture Toughness of Interfaces-The Challenge of Critical Values /$cM. Kanerva, J. Jokinen, E. Sarlin, O. Saarela. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b32 =520 3\$aThis study aims to shed light on the conflict between macroscopic fracture toughness and small-scale measures of interface strength when the interface is simulated with an increasing resolution. In the design of practical structures, crack initiation is the critical, limiting phase of material behavior and needs to be defined by lucid means. In this study, we model an example structure, namely a fracture test specimen, including a bi-material interface having micro-roughness and thermal residual stresses. The initiation of secondary cracks, which is one of the microscopic mechanisms leading to crack coalescence, is studied. The work focuses on the effects of the bi-material's Young's modulus, residual stresses, and flaws. The simulation of crack propagation shows that the overall crack tip loading mode mixity distribution is not essentially affected when the Young's modulus of the bi-material's coating is doubled. The analysis of the secondary crack initiation due to interfacial flaws in turn showed that increasing the Young's modulus of either the bi-materials substrate or coating resulted in immediate interface collapse via an elongated 'damage region' along the interface. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCrack growth. =650 \0$aFinite element method. =650 \0$aFinite element simulation. =650 \0$aInterface fracture toughness. =650 14$aInterface fracture toughness. =650 24$aCrack growth. =650 24$aFinite element simulation. =700 1\$aJokinen, J.,$eauthor. =700 1\$aSaarela, O.,$eauthor. =700 1\$aSarlin, E.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130068.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130034 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130034$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130034$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA680 =082 04$a624.1/8341$223 =100 1\$aBelay, Tsegay,$eauthor. =245 10$aInternal Notched Flexure (INF) Test for Measurement of Mode II Interlaminar Fracture Toughness of Fiber Composites /$cTsegay Belay, P.-Y. Jar, J.-J. Cheng. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b13 =520 3\$aA revised analysis to derive the expression for the mode II interlaminar fracture toughness of fiber-reinforced polymers from internal notched flexure (INF) testing in small deformation is presented here. The approach adopted for the derivation takes into account the interlaminar shear load in the overhanging section outside the span. This improves the prediction accuracy for the initial specimen compliance, as evident from a finite element (FE) model of the INF specimen. The FE model also suggests that extensive damage develops at the crack tip before the delamination growth. Therefore, rather than using the physical crack length to calculate the interlaminar fracture toughness, one should use the effective crack length, which can be determined based on the measured specimen stiffness from experimental testing. With that, the analytical expression yields an inerlaminar fracture toughness that is consistent with the input value for the cohesive elements of the FE model. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDelamination. =650 \0$aFiber composites. =650 \0$aFiber-reinforced concrete. =650 \0$aFibrous composites. =650 \0$aFracture toughness. =650 \0$aPolymers. =650 14$aDelamination. =650 24$aFiber composites. =650 24$aFracture toughness. =650 24$aINF test. =700 1\$aCheng, J.-J.,$eauthor. =700 1\$aJar, P.-Y.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130034.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130032 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130032$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130032$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQE369.P49 =082 04$a553.6$223 =100 1\$aHan, Wei,$eauthor. =245 10$aNano-Halloysite Concentration Effects on Fracture Toughness of Diverse Epoxy Nanocomposites /$cWei Han, Yang Yu, Youhong Tang, Karl Sammut. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b17 =520 3\$aWe experimentally report material design of halloysite nanotube (HNT)/epoxy composites, focusing on the effects of HNT concentration on thermal and mechanical properties, especially fracture toughness, of diverse epoxy composites with as-received and phenylphosphonic-acid (PPA)-treated HNTs prepared by mechanical mixing or ball-milling homogenization. It is demonstrated that, with HNT added in the region of 0.0-10.0 wt. %, significantly reinforced fracture toughness of the epoxy composites can be achieved. The epoxy composites prepared by ball-milling homogenization have much more uniform HNT size and dispersion than those prepared by simple mechanical mixing, enhancing their fracture toughness. The morphology of treated HNTs changes from nanotubes to nanoplatelets; as a result, with a substantial increase in the total contact area between HNT and epoxy and enhancing the fracture toughness of epoxy composites. This higher HNT concentration and the higher fracture toughness are achieved for various epoxy composites. However, the optimal concentration of HNT is 5.0 wt. % in this study. The addition of further HNT achieves only marginal fracture toughness enhancement and more negative effects appear, such as HNT concentration gradient in cured epoxy composites, high potential decrease in glass transition temperature (Tg), and potential immature tensile failure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aConcentration. =650 \0$aEpoxy. =650 \0$aFracture toughness. =650 \0$aHalloysite. =650 \0$aMineralogy. =650 \0$aNanocomposites. =650 \0$aNanostructures. =650 \0$aNanotubes. =650 14$aHalloysite. =650 24$aConcentration. =650 24$aEpoxy. =650 24$aFracture toughness. =650 24$aNanocomposites. =700 1\$aSammut, Karl,$eauthor. =700 1\$aTang, Youhong,$eauthor. =700 1\$aYu, Yang,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130032.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130076 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130076$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130076$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD921 =082 04$a548.5$223 =100 1\$aSherman, Dov,$eauthor. =245 10$aEvaluating the Cleavage Energy of Brittle Single Crystals /$cDov Sherman, Anna Gleizer. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b45 =520 3\$aEvaluating the cleavage energy of brittle crystals is challenging due to the need to generate a controlled deformation of only a few microns; to introduce a straight and planar, atomistic thick precrack, perfectly aligned with the plane of propagation; to align the external loading with that plane; and above all, to grip the specimen while avoiding premature cleavage. In addition, achieving a relatively slow crack upon initiation is another requirement that needs special treatment. Consequently, we designed an experimental method that fulfills the above requirements. It consists in gluing a thin, rectangular specimen, with an atomistic sharp precrack, inside a rectangular hole in an aluminum loading frame, using thin layers of epoxy resin. Crack initiation and propagation occur upon heating the assembly on top of an electrical heating stage by only a few °C, due to the coefficients of thermal expansion mismatch between the specimen and the aluminum frame. Finite element analysis is used to evaluate the strain energy release rate. We describe it in full through cleavage experiments of two low energy cleavage systems of silicon crystal under pure Mode I, under room conditions and argon gas at atmospheric pressure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBrittle crystals. =650 \0$aCleavage energy. =650 \0$aCleavage experiments. =650 \0$aEnvironmental effect. =650 \0$aLithium niobate$xAnalysis. =650 \0$aMetal crystals$xElectric properties. =650 \0$aMetal crystals$xGrowth. =650 14$aCleavage energy. =650 24$aBrittle crystals. =650 24$aCleavage experiments. =650 24$aEnvironmental effect. =700 1\$aGleizer, Anna,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130076.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130062 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130062$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130062$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.P68 =082 04$a668.4234$223 =100 1\$aFarhang, L.,$eauthor. =245 10$aInvestigation of Toughening Micro-Mechanisms in Polypropylene/Ethylene-Propylene-Diene Rubber Blends at Crack and Notch Tips /$cL. Farhang, R. Bagheri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b37 =520 3\$aPolypropylene (PP) has the highest growth rate among commodity thermoplastics and is widely used in many applications including packaging, auto, and pipe industries. The relatively low impact strength of this polymer has led to the production of rubber-modified polypropylene with higher impact strength. To promote the applications of these blends, it is necessary to establish the relationship between the mechanical performance and fracture micro-mechanism(s). Fracture behavior is different depending on the application where either crack or notch might be present. In this study, a systematic approach is taken with the aim of understanding the toughening micro-mechanisms of polypropylene/ethylene-propylene-diene monomer (PP/EPDM) blends at both crack and notch tip using different microscopy techniques. Rubber-modified blends were prepared using a twin screw extruder. The samples were exposed to different mechanical, physical, and microscopic examinations. X-ray diffractometer (XRD) and differential scanning calorimetry (DSC) techniques were used to study the crystalline structure. Impact and fracture toughness (JIC) tests were conducted to evaluate toughness of blends. Morphology and fracture behavior of the blends were investigated via transmission optical microscopy (TOM) and scanning electron microscopy (SEM). Results indicate that both impact strength and fracture toughness (JIC) increase with increasing EPDM content. The two parameters, however, do not follow the same trend. The microscopic evaluations reveal that massive crazing coupled with particle cavitation is the dominant toughening mechanism in PP/EPDM blends under quasi-static and impact loading. Morphological features of the damage zone are different in these two loading conditions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFracture behavior. =650 \0$aJ-integral method. =650 \0$aManufacturing processes. =650 \0$aPlastics. =650 \0$aPolypropylene. =650 \0$aRubber-modified polypropylene. =650 \0$aToughening mechanism. =650 14$aRubber-modified polypropylene. =650 24$aFracture behavior. =650 24$aJ-integral method. =650 24$aToughening mechanism. =700 1\$aBagheri, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130062.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130064 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130064$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130064$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQ295 =082 04$a620.1126$223 =100 1\$aLi, Yan,$eauthor. =245 12$aA Multiscale Framework for Predicting Fracture Toughness of Polycrystalline Metals /$cYan Li, D. McDowell, Min Zhou. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b30 =520 3\$aMicrostructure has a strong influence on fracture toughness of materials through the activation of different fracture mechanisms. To tailor the fracture resistance through microstructure design, it is important to establish relations between microstructure and fracture toughness. A multiscale computational framework based on the Cohesive Finite Element Method (CFEM) is introduced to facilitate relations between microstructure and the fracture toughness of ductile polycrystalline materials. This material design framework includes 3D image based microstructure reconstruction, 3D meshing, and finite element implementation. It allows the material fracture toughness to be predicted through explicit simulation of fracture processes involving arbitrary crack paths, crack tip microcracking, and branching. Cohesive elements are embedded both within the grains and along the grain boundaries to resolve the different material separation processes. The calculations carried out concern Ti-6Al-4V alloy and focused on the two primary fracture mechanisms which are correlated with microstructure characteristics, constituent properties, and deformation behaviors. The methodology is potentially useful for both the selection of materials and tailoring of microstructure to improve fracture resistance. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCohesive finite element method. =650 \0$aCrystal plasticity. =650 \0$aFracture mechanics. =650 \0$aMetals$xFracture. =650 \0$aMicrostructure-fracture toughness. =650 \0$aMultiscale framework. =650 14$aMultiscale framework. =650 24$aCohesive finite element method. =650 24$aCrystal plasticity. =650 24$aMicrostructure-fracture toughness. =700 1\$aMcDowell, D.,$eauthor. =700 1\$aZhou, Min,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130064.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130065 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130065$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130065$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA465 =082 04$a620.1/76$223 =100 1\$aBind, A.,$eauthor. =245 10$aComparative Study of Basic Test and Resistance Curve Methods for Fracture Toughness Evaluation of Heat-Treated Zr-2.5Nb Alloy /$cH. Khandelwal, R. Singh, A. Bind, Saurav Sunil, J. Chakravartty. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b45 =520 3\$aASTM E1820-11, the most widely adopted standard for the determination of fracture toughness parameters, recommends two ductile crack growth correction methods for the evaluation of the J-integral parameter, viz., the basic test (BT) method and the resistance curve test (RC) method. In the present work, a comparison between the fracture toughness parameters obtained using these two methods for heat-treated Zr-2.5Nb alloy at 25°C and 300°C is presented. In order to examine the influence of a material's microstructural condition on the fracture toughness results obtained via these two methods, Zr-2.5Nb alloy was investigated under six solution heat-treated conditions after getting soaked at 850°C, 870°C, or 890°C for either 15 min or 30 min followed by water quenching. The BT method predicted a higher J parameter than the RC method for a given crack length. This deviation in the magnitude of J increased with increasing crack length and was found to be almost twice as much at room temperature as the deviation observed at 300°C. For smaller crack lengths (i.e., up to a/W < 0.54), the J parameters determined using the two methods showed insignificant deviation (<5 %). However, such deviation reached ~20 %, corresponding to ~0.63 a/W. Values of fracture toughness parameters such as JQ, Jmax, and dJ/da evaluated using the BT method were found to be higher than those obtained using the RC method. However, deviations in the JQ and Jmax parameters determined by the two methods were insignificant (less than ~6 %), whereas the deviation in the dJ/da parameter was ~15 %. The RC method, in contrast to the BT method, provides a marginally conservative estimation of the fracture toughness. The parameter ? used in the BT method was observed to control the extent of deviation in the J-R curves derived using these methods. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBasic test method. =650 \0$aDuctile crack growth. =650 \0$aFracture toughness. =650 \0$aResistance curve test method. =650 \0$aSolution heat treatment. =650 \0$aSteel$xFracture. =650 \0$aSteel$xHeat treatment. =650 14$aFracture toughness. =650 24$aBasic test method. =650 24$aDuctile crack growth. =650 24$aResistance curve test method. =650 24$aSolution heat treatment. =650 24$aZr-2.5Nb alloy. =700 1\$aBind, A.,$eauthor. =700 1\$aChakravartty, J.,$eauthor. =700 1\$aSingh, R.,$eauthor. =700 1\$aSunil, Saurav,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130065.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130058 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130058$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130058$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA401.3 =082 04$a620.1/12$223 =100 1\$aAli, Muhammad,$eauthor. =245 10$aEffect of Notch Orientation on Fracture Toughness of a Submerged Arc Weld /$cMuhammad Ali, Henryk Pisarski. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b20 =520 3\$aThis paper reports the effect of notch orientation on the fracture toughness of a submerged arc weld as determined by performing standard fracture mechanics tests using single edge notched bend specimens having through-thickness and surface notches. The notch orientations used were NP (through-thickness notch at weld centerline running parallel to the weld direction), NQ (surface notch at weld centerline with the notch plane parallel to the weld but running perpendicular to the weld direction from the cap toward the root), and PQ (a surface notch where the notch plane is transverse to the weld and propagating from the cap toward the root). Testing was carried out over a range of temperatures. It was found that the NP notch orientation led to less scatter in fracture toughness, and the greatest amount of scatter was shown for NQ and PQ notch orientations. The test data for each notch orientation were used to determine the reference temperature T0 using ASTM E1921-13 and FITNET procedures. Values of T0 were subsequently used to define the temperature-versus-toughness transition curve (master curve) for each notch orientation. The fracture toughness predicted by the master curve analyses showed differences among the three notch orientations. As the FITNET procedure is more conservative for highly scattered data than the ASTM procedure, the predicted fracture toughness for the PQ and NQ notch orientations was significantly less than that for the NP notch orientation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFracture toughness. =650 \0$aMaster curve. =650 \0$aMaterials$xEffect of temperature on$xResearch$xCongresses. =650 \0$aNotch orientation. =650 \0$aReference temperature. =650 \0$aSubmerged arc weld. =650 14$aFracture toughness. =650 24$aMaster curve. =650 24$aNotch orientation. =650 24$aReference temperature. =650 24$aSubmerged arc weld. =700 1\$aPisarski, Henryk,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130058.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130031 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130031$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130031$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aK3611.G46 =082 04$a344.04196$223 =100 1\$aWallin, Kim,$eauthor. =245 10$aRotation and Bending Corrections for the SE(B) Specimen /$cKim Wallin. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b11 =520 3\$aStandard tests with single-edge (bend) [SE(B)] specimens do not apply a rotation or bending correction. The load-line displacement (LLD) is generally used only for the estimation of the J integral. The compliance is preferably measured from the crack mouth opening displacement (CMOD). However, the standard equations assume that the measuring point lies at the specimen front face. With small specimens this is impractical, because the necessary cutout will decrease the effective crack length of specimen, thus reducing the constraint. If the CMOD measurement is above the front face, a special geometric rotation correction is required. Even in the case of front face measurements, a rotation correction is needed if the rotation of the specimen is large. When the LLD is used, an additional bending correction may be needed. The correction is needed because, with bending, both the effective span width, as well as the specimen cross-section dimensions will change. Bending makes the specimen appear stiffer than a straight specimen. If bend specimens are tested with the unloading compliance technique, the true crack extension will generally be underestimated, unless the measured compliance is corrected for rotation and bending. The underestimation will be a function of specimen dimensions and degree of bending, but it can, for smaller specimens, be as much as 35 %. Here new analytical rotation and bending corrections for the SE(B) specimen are proposed and validated. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBending correction. =650 \0$aBiological Specimen Banks$xethics. =650 \0$aBiological Specimen Banks$xlegislation & jurisprudence. =650 \0$aRotation correction. =650 \0$aspecimens. =650 14$aSE(B) specimens. =650 24$aBending correction. =650 24$aRotation correction. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130031.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130090 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130090$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130090$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN731 =082 04$a669/.142$223 =100 1\$aSubramanian, Rohit,$eauthor. =245 12$aA Multi-Body Numerical Modeling Approach to Investigate the Role of Inclusions in the Fracture Toughness of Bearing Steels /$cRohit Subramanian, Rajiv Shivpuri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b44 =520 3\$aAntifriction bearings often fail from inclusion initiated surface and/or subsurface cracks that propagate in a hard tempered-martensite matrix that contains a certain amount of retained austenite, especially for case carburized surfaces. The primary inclusions present are carbides, sulfides, nitrides, and oxides that are characterized by distinct morphology, frequency, and constitutive behavior. Consequently, the fracture toughness of the inclusion-matrix system depends on the interactions between the inclusions themselves and their surrounding matrix. This paper presents a numerical framework for investigating the fracture response of the inclusions and the multiphase tempered martensite matrix. In this multibody approach, the inclusions are modeled as discrete bodies embedded in a plastic matrix with their distinct constitutive behavior. The plastic response of the polycrystalline matrix is modeled using a micromechanics approach for heterogeneous materials based on the original works of Eshelby and Hill. Finally, the mechanics of inclusion-matrix interface is included in the sliding surface description for the contacting bodies. This fracture model used in this study is based on the energy adsorption in the initiation of cracks and their subsequent propagation during tensile loading. The multibody model is calibrated and validated by comparison to experimental results reported in literature. Subsequently, the effect of phases surrounding the inclusion and the composition of the matrix are evaluated using the model. The constitutive behavior of the transition layer surrounding the inclusion is found to have a profound impact on the fracture toughness properties. The volume fraction of retained austenite in the matrix is also found to influence the fracture toughness of the material and cracking instability. Key results of this investigation are included in this paper. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBearing steels. =650 \0$aCrack propagation. =650 \0$aFracture toughness. =650 \0$aInclusions. =650 \0$aMulti-body modeling. =650 \0$aRotors$xMaterials. =650 \0$aSteel$xInclusions. =650 \0$aSteel$xRefining. =650 14$aFracture toughness. =650 24$aBearing steels. =650 24$aCrack propagation. =650 24$aInclusions. =650 24$aMulti-body modeling. =700 1\$aShivpuri, Rajiv,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130090.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130042 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130042$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130042$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA347.F5 =082 04$a620.00151825$223 =100 1\$aMartínez-Figueroa, J.,$eauthor. =245 10$aDynamic Fracture Toughness of a Plain Weave Carbon-Epoxy Composite :$bValidation of Test Results with Finite Element Analyses /$cJ. Martínez-Figueroa, C. Rubio-Gonzalez, F. Velasco-Reyes, N. Benseddiq. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b17 =520 3\$aThis document presents the Dynamic Fracture Toughness (KID) measurement for a plain weave carbon-epoxy composite material. An instrumented Hopkinson bar arrangement is used to perform the tests with pre-cracked specimens loaded on a three point bending configuration. The material behavior obtained by the experimental results is compared with Finite Element simulation of static and idealized Hopkinson bars events. A number of important aspects are approached. Among them, the Stress Intensity Factor (SIF) for fiber-epoxy composites considered as transversely isotropic media, the formulae to obtain this parameter compared with isotropic materials, and the precise follow of the SIF evolution during these events. The Finite Element Analyses (FEAs) suggest loss of contact phenomena not only in the transmitted but also with the incident bar, and according to this, a specimen FEA is used to verify the influence of this loss of contact in the SIF evolution and KID calculations. Accordingly, a novel approach using the incident pulse as input for a FEA of the complete arrangement including contact elements is proposed and implemented, so the new revealed phenomena are taken into account. The experimental results using this approach show that the dynamic fracture toughness varies from 15.45 to 25.6 MPa*m0.5 in the projectile speed range between 10 and 20 m/s. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDynamic fracture toughness. =650 \0$aDynamic stress intensity factor. =650 \0$aFinite element method. =650 \0$aHopkinson bars. =650 \0$aPlain weave carbon-epoxy composite. =650 14$aDynamic stress intensity factor. =650 24$aDynamic fracture toughness. =650 24$aHopkinson bars. =650 24$aPlain weave carbon-epoxy composite. =700 1\$aBenseddiq, N.,$eauthor. =700 1\$aRubio-Gonzalez, C.,$eauthor. =700 1\$aVelasco-Reyes, F.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130042.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130041 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130041$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130041$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.C3 =082 04$a620.1/93$223 =100 1\$aTorabi, A.,$eauthor. =245 10$aNotch Fracture Toughness Evaluation for a Brittle Graphite Material /$cA. Torabi, F. Berto. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b41 =520 3\$aFirst, several disc-type test samples weakened by a central bean-shaped slit with two U-shaped ends, called U-notched Brazilian disc (UNBD) specimens, made of commercial graphite, were prepared. Four notch tip radii were considered in the tests. Then, a monotonic compressive load was diametrally applied to each sample along the slit, resulting in pure mode I loading. After sudden fracture, the fracture loads were recorded and converted into the corresponding values of the notch fracture toughness (NFT) KI?,c. The main advantage of the UNBD specimen is that the NTF test can be easily conducted without using complicated fixtures. The well-established brittle fracture model, namely the strain energy density (SED) over a specified control volume, which embraces the notch edge, was employed to estimate the fracture loads theoretically. A good agreement was found between experimental and theoretical results. Under Mode I loading, the SED and the NFT are linked by a simple relationship providing a powerful tool for the fracture assessment of different specimens and structural components weakened by notches. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBrittle fracture. =650 \0$aCarbon composites. =650 \0$aCarbon. =650 \0$aGraphite material. =650 \0$aGraphite. =650 \0$aMode I loading. =650 \0$aNotch fracture toughness. =650 \0$aU-notched Brazilian disc. =650 14$aNotch fracture toughness. =650 24$aBrittle fracture. =650 24$aGraphite material. =650 24$aMode I loading. =650 24$aU-notch. =650 24$aU-notched Brazilian disc. =700 1\$aBerto, F.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130041.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130047 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130047$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130047$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQ295 =082 04$a620.1126$223 =100 1\$aDiener, M.,$eauthor. =245 10$aFracture Toughness :$bA Quality Index for Railway Solid Wheels /$cM. Diener, A. Ghidini. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b11 =520 3\$aAbout 10 years ago, the European Standard EN13262 was introduced, and, for the first time in railways, the toughness characteristic of the rim has to be proofed for tread-braked solid wheels. For wheels of steel grade ER7 the average fracture toughness obtained from six test pieces shall be greater than or equal to 80 MPa m1/2 and no single value shall be less than 70 MPa m1/2. The present paper focuses on the efforts in research and, of course, application of fracture mechanics to railway solid wheels. The obtained results demonstrate that the capability to measure fracture toughness of materials and a proper collection of the related metallurgical parameters help to develop the manufacturing process of wheels. The main challenge is to improve toughness in parallel with yield strength by maintaining a desired microstructure of the material. Some important correlations between structure and fracture toughness are specified and document how the toughness can be tuned. The properties on the production of solid wheels, monitored over a long period, have confirmed the ability to guarantee both high and uniform values of mechanical characteristics and toughness. This is an important result concerning product quality and safety of railway wheels. Fracture toughness and yield strength represent an appropriate quality index for any material and steel grade. A production index (PI), which is the product of yield strength and fracture toughness, is introduced to trace the quality of a material in production. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFracture mechanics. =650 \0$aFracture toughness. =650 \0$aMetals$xFracture. =650 \0$aProduction index. =650 \0$aQuality index. =650 \0$aSolid wheel. =650 \0$aSteel quality ER7. =650 \0$aYield strength. =650 14$aEuropean standard EN13262. =650 24$aFracture toughness. =650 24$aProduction index. =650 24$aQuality index. =650 24$aSolid wheel. =650 24$aSteel quality ER7. =650 24$aYield strength. =700 1\$aGhidini, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130047.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130069 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130069$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130069$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQ295 =082 04$a620.1126$223 =100 1\$aSharma, N.,$eauthor. =245 10$aApplication of Elastic-Plastic Fracture Mechanics to Determine the Locational Variation in Fracture Properties of Cortical Bone /$cN. Sharma, Ruchita Pal, D. Sehgal, R. Pandey. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b46 =520 3\$aThe complex nature of bone material results in a locational variation of fracture and mechanical properties. The heterogeneity associated with bone material and complex hierarchical assembly results in several toughening mechanisms, such as plasticity, micro-cracking, viscoplasticity, etc. These toughening mechanisms and presence of water in bone material makes the linear elastic fracture mechanics (LEFM) inapplicable in such materials. The present work is focused on the elastic-plastic fracture mechanics (EPFM) approach to estimate the locational variation in fracture properties of buffalo cortical bone for longitudinal, as well as transverse orientation of cracking. Samples from upper, middle, and lower locations of bone diaphysis were tested using compact tension and single-edge notch-bending testing methods for longitudinal and transverse orientation of cracking, respectively. The crack-tip opening displacement (CTOD) approach was applied to determine fracture properties, such as CTOD toughness (?c), J integral (Jc?), and equivalent fracture toughness (K?c) at different locations of bone diaphysis. The effect of orientation and location on mechanical properties of cortical bone, such as elastic modulus (E) and yield strength (?ys), was also analyzed with the help of tensile testing. The equivalent fracture toughness values (K?c) obtained in the present work were found to be three times higher than the corresponding values reported in the previous reports where the LEFM approach was applied favoring the application of EPFM for bone materials. The mechanical properties, as well as the fracture properties, were found to be maximum at middle location and minimum at lower location of bone diaphysis. The locational variation in fracture and mechanical properties observed in the present work are considered to be because of locational distribution of collagen fibrils, minerals, porosity, and density at different locations of bone diaphysis. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBone. =650 \0$aCrack-tip-opening displacement. =650 \0$aElastic-plastic fracture mechanics. =650 \0$aFracture mechanics. =650 \0$aFracture toughness. =650 \0$aLinear-elastic fracture mechanics. =650 \0$aMetals$xFracture. =650 14$aBone. =650 24$aCrack-tip-opening displacement. =650 24$aElastic-plastic fracture mechanics. =650 24$aFracture toughness. =650 24$aLinear-elastic fracture mechanics. =700 1\$aPal, Ruchita,$eauthor. =700 1\$aPandey, R.,$eauthor. =700 1\$aSehgal, D.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130069.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130094 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130094$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130094$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aHD9539.A63.A3842012 =082 04$a338.1092348$223 =100 1\$aRobinson, J.,$eauthor. =245 14$aThe Influence of Quenching and Aging on Fracture Toughness of the Al-Zn-Mg-Cu Alloy 7449 /$cJ. Robinson, G. Higgins. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b32 =520 3\$aThis investigation characterises the fracture toughness of the very high strength Aluminium alloy 7449. This Al-Zn-Mg-Cu alloy is heat treatable and relies on rapid quenching from the solution heat treatment temperature to promote subsequent artificial aging. While the influence of quench paths on strength is well understood and can be predicted using techniques like quench factor analysis, the influence of quench rate on fracture toughness is more challenging. The rate of quenching can influence the fracture toughness through complex precipitation reactions occurring during cooling. The precipitate locations dictate the magnitude of the detrimental effect on the fracture toughness. In this investigation, the fracture toughness of 7449 in two product forms was measured using compact tension specimens cut from forged blocks and rolled plate. These plane strain (KIC) results were also augmented with Charpy impact tests. Various quench conditions were investigated, including water at three different temperatures and poly oxyethylene glycol (PAG) in two concentrations. The influence of standard and novel aging procedures including retrogression and reaging was also determined. The combinations of strength and toughness have been related to the prevailing microstructural condition. Fracture toughness magnitudes were found to vary most significantly with rapidity of cooling from the solution treatment temperature, with the subsequent aging treatments having a much smaller effect. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminium alloy. =650 \0$aAluminum casting. =650 \0$aAluminum industry and trade. =650 \0$aCompact tension fracture toughness. =650 \0$aForgings and rolled plate. =650 \0$aHeat treated aluminium alloy. =650 \0$aImpact tests. =650 \0$aPAG synthetic quenchant. =650 14$aCompact tension fracture toughness. =650 24$aForgings and rolled plate. =650 24$aHeat treated aluminium alloy. =650 24$aImpact tests. =650 24$aPAG synthetic quenchant. =700 1\$aHiggins, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130094.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130046 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130046$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130046$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aMoitra, A.,$eauthor. =245 10$aEvaluation of Ductile-to-Brittle Transition Temperature by Reference Temperature (T0) Approach at Higher Loading Rates for a Mod.9Cr-1Mo Steel /$cA. Moitra, S. Sathyanarayanan, G. Sasikala, A. Bhaduri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b18 =520 3\$aTo evaluate the ductile-to-brittle transition temperature of ferritic-martensitic steels, the ASTM E1921-based reference temperature (T0) approach has now been widely recognized; however, until now, the standard restricts itself to static/quasi-static loading rates. It is well recognized that the flow stress of rate-sensitive material increases with the strain rate, and thus it is imperative that the increase in loading rate would lead to limited plasticity-induced brittleness, reflected in higher T0. There have been efforts in the literature for developing empirical correlations to derive T0 at higher loading rates from T0 at quasi-static loading rates or vice versa. However, there is a need to experimentally evaluate the T0 at higher loading rates, especially for the 9Cr-1Mo family of steels, proposed to be used as wrapper material in the upcoming commercial liquid-sodium-cooled fast breeder reactors in India. The present study is directed toward determining T0 for Mod.9Cr-1Mo steel at loading rates of 1.12, 3, and 5 m/s. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aDynamic loading. =650 \0$aReference temperature. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 \0$aSteel. =650 14$aDBTT. =650 24$aASTM E 1921. =650 24$aDynamic loading. =650 24$aReference temperature. =700 1\$aBhaduri, A.,$eauthor. =700 1\$aSasikala, G.,$eauthor. =700 1\$aSathyanarayanan, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130046.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130044 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130044$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130044$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD257.7 =082 04$a546$223 =100 1\$aWong, W.,$eauthor. =245 10$aRole of Vapor Pressure on Popcorn Cracking in IC Packages /$cW. Wong, T. Guo, L. Cheng. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b37 =520 3\$aThe strength and fracture toughness of polymer/silicon interfaces are sensitive to the porosity and moisture content of the interface as well as the yield strain of the polymer. Moisture degrades the strength of polymer/silicon interfaces. Rapidly expanding water vapor introduces high internal pressure within cavities thereby accelerating interface delamination by void growth and coalescence. The latter can cause a ten-fold decrease in the toughness of the interface. Vapor pressure acting on the delaminated surfaces contributes a mode I component to the crack driving force. This component increases as delamination progresses, changing the nature of the driving force from mode II to mode I dominant. The synergistic nature of intrinsic and extrinsic effects transforms an initially stable delamination under a rising R-curve to fast-running delamination exhibiting brittle-like cracking characteristics. The yield strains of polymers span a wide range. High yield strain lowers the macroscopic yield strength of porous polymers as well as decreases the toughness of polymer-silicon interfaces considerably. Vapor pressure and large yield strain effects on interface delamination are most pronounced at high mode mixities, thereby negating the beneficial effect of the latter on interface toughness. The approach adopted in this computational study is micromechanics-based wherein the cell model employs a Gurson constitutive relation augmented by vapor pressure as an internal variable. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aInterface toughness. =650 \0$aOrganic compounds. =650 \0$aPopcorn failure. =650 \0$aResidual stress. =650 \0$aVapor pressure$xTables. =650 \0$aVapor pressure. =650 \0$aVoid growth. =650 14$aInterface toughness. =650 24$aPopcorn failure. =650 24$aResidual stress. =650 24$aVapor pressure. =650 24$aVoid growth. =700 1\$aCheng, L.,$eauthor. =700 1\$aGuo, T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130044.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130077 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130077$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130077$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP261.G7 =082 04$a662/.92$223 =100 1\$aMorrison, Craig,$eauthor. =245 10$aDiscrete Lattice Model of Quasi-Brittle Fracture in Porous Graphite /$cCraig Morrison, Mingzhong Zhang, Andrey Jivkov, John Yates. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b35 =520 3\$aLattice models allow the incorporation of length-scale-dependent microstructural features and damage mechanisms into analyses of the mechanical behavior of materials. We describe our 3D lattice implementation and its use in fracture simulations. The method is particularly suitable for modeling fractures of nuclear graphite. This is a quasi-brittle material in which there is considerable non-linearity prior to final fracture caused by the inherent porosity, which triggers a field of local distributed failures upon mechanical and thermal loading. Microstructure representative models are generated with experimentally measured particle and pore size distributions and volume densities in two graphite grades. The results illustrate the effect of distributed porosity on the emerging stress-strain response and damage evolution. It is shown how the failure mode shifts from graceful, plastic-like behavior associated with substantial energy dissipation via distributed damage at lower porosities, to glass-like behavior with negligible energy dissipation at higher porosities. Thus, the work proposes a microstructure-informed methodology for integrity assessment of aging structures, where porosity increase is driven by environmental factors, such as radiation of nuclear graphite components. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aBrittle-ligament lattice. =650 \0$aDamage evolution. =650 \0$aGraphene. =650 \0$aGraphitization. =650 \0$aNuclear graphite. =650 \0$aPorosity. =650 \0$aQuasi-brittle behavior. =650 14$aNuclear graphite. =650 24$aBrittle-ligament lattice. =650 24$aDamage evolution. =650 24$aPorosity. =650 24$aQuasi-brittle behavior. =700 1\$aJivkov, Andrey,$eauthor. =700 1\$aYates, John,$eauthor. =700 1\$aZhang, Mingzhong,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130077.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130083 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130083$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130083$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669/.96142$223 =100 1\$aMourad, A-H.,$eauthor. =245 10$aFracture Toughness Measurements From Circumferentially-Notched Pipes Tests /$cA-H. Mourad, J. Altarawneha, A. Domiaty, Y. Chao, F. Haggag. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b22 =520 3\$aFracture toughness for full scale steel pipe of API 5L grade X65 PSL1 (ASTM A694) medium strength grade pipeline steel has been measured by a new test specimen utilizing the same procedures of the standard test methods ASTM E399-90 and ASTM E1820-01. Full scale pipe sections with circumferentially machined notches were pulled axially by tensile loads until fracture. An external circumferential sharp notch was machined in the wall of the pipe to simulate the crack. In addition to testing a plain pipe, a well lubricated and axially free loaded plug was mounted inside the pipe to provide plane strain condition for notch failure. Ductile dimple fracture was observed on fractured surfaces of plain pipes, while evidences of cleavage fractures have been observed when the internal plug was used. The measured value of the fracture toughness has been found to be in good agreement with the values measured according to the standard tests for steel plates of similar grade and with the with those measured using in situ Automated Ball Indentation (ABI) tests conducted on the same pipe section. The new testing method for full scale pipe can be used regardless of pipe dimensions since it appears to provide plane strain conditions around the crack. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aCircumferentially-notched pipe. =650 \0$aFracture toughness measurements. =650 \0$aSteel$xMetallography. =650 \0$aSteel$xMetallurgy. =650 14$aFracture toughness measurements. =650 24$aAPI X65 steel. =650 24$aCircumferentially-notched pipe. =700 1\$aAltarawneha, J.,$eauthor. =700 1\$aChao, Y.,$eauthor. =700 1\$aDomiaty, A.,$eauthor. =700 1\$aHaggag, F.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130083.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130045 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130045$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130045$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.P58 =082 04$a620.1/9204292$223 =100 1\$aPodgornik, Bojan,$eauthor. =245 10$aExperimental Evaluation of Tool Steel Fracture Toughness Using Circumferentially Notched and Precracked Tension Bar Specimen /$cBojan Podgornik, Borut Žužek, Vojteh Leskovšek. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b30 =520 3\$aDies and tools used in hot metal forming (extrusion, forging, rolling, etc.) are exposed to elevated temperatures and high contact pressures. As the automotive industry increasingly moves toward use of advanced high-strength steels, requirements on the wear and fatigue properties of tools and dies are constantly growing. This requires high-strength high-hardness materials where reliable determination of fracture toughness is crucial. However, for proper selection, optimization, and heat treatment of tool steel, fracture toughness data and especially its scatter are very important and need to be precisely determined and supported by other material properties. Therefore, the aim of the presented research work was to investigate the suitability of Circumferentially Notched and Precracked Tension Bar specimen (CNPTB) for evaluating fracture toughness of tool steels and to correlate fracture toughness properties of hot work tool steel to the local variation in microstructure, microhardness, and composition. Results of the work show that CNPTB specimen allows simultaneously assessment of basic properties such as hardness, fracture toughness, compressive strength, etc., which can be directly correlated to the vacuum heat treatment parameters and microstructure. Furthermore, presence of any weak point, either in a form of non-metallic inclusions, large undissolved eutectic carbide clusters, and bands, or their combination, especially if located in the region of positive segregation and close to the fatigue crack tip, will lead to considerable reduction in hot work tool steel fracture toughness. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aFracture toughness. =650 \0$aHot work tool steel. =650 \0$aMicrohardness. =650 \0$aMicrostructure. =650 \0$aPolymeres. =650 \0$aPolymers$xMechanical properties. =650 \0$aPolymers$xTesting. =650 14$aHot work tool steel. =650 24$aFracture toughness. =650 24$aMicrohardness. =650 24$aMicrostructure. =700 1\$aŽužek, Borut,$eauthor. =700 1\$aLeskovšek, Vojteh,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130045.htm =LDR 03762nab 2200553 i 4500 =001 MPC20130036 =003 IN-ChSCO =005 20161219061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 161219s2014\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20130036$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20130036$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN697.A47 =082 04$a669.722$223 =100 1\$aMilan, M.,$eauthor. =245 10$aFatigue Crack Growth Behavior of Friction Stir Welded 2024-T3 Aluminum Alloy Tested under Accelerated Salt Fog Exposure /$cM. Milan, W. Bose Filho, J. Tarpani. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2014. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b46 =520 3\$aFatigue crack growth properties of friction stir welded joints of 2024-T3 aluminum alloy were studied via constant amplitude load (increasing ?K) testing under open air and accelerated salt fog exposure conditions. For low ?K values, longitudinal crack growth in the weld line center was slower under corrosion fatigue than by air because of the prevalence of corrosion-induced crack closure. On the other hand, growth rates of transverse crack crossing the weld nugget were not affected by the environment aggressiveness because of a balance between hydrogen embrittlement and corrosion inducing crack closure along with welding compressive residual stresses. For intermediate ?K values, propagation rates 5 times faster were observed for both longitudinal and transverse cracks under salt fog ambient as a result of hydrogen-induced embrittlement, which is favored by larger crack tip openings allowing local corrosive medium access. As the final catastrophic fracture approaches, longitudinal and transversal crack propagation rates under corrosion fatigue approximated the values observed in air testing, as time, under the 30-Hz loading frequency applied, was scarce for an effective interaction between crack tip fresh material and the hostile environment. For longitudinal cracks, precracking in air resulted in fatigue-corrosion limit factor ?Kth slightly lower than that obtained in salt fog precracked specimens, as the corrosive role played by the salt fog environment along the precrack introduction contributed to crack-closure effect, so increasing the apparent value of ?Kth. On the other hand, the environment in which a transverse precrack was created had a negligible effect on ?Kth because of the establishment of an equilibrium condition between corrosion-induced precrack closure and hydrogen embrittlement. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed December 19, 2016. =650 \0$aAluminum alloy. =650 \0$aAluminum$xMetallurgy. =650 \0$aCorrosion fatigue. =650 \0$aFatigue crack growth rate. =650 \0$aFriction stir welding. =650 \0$aMechanical alloying. =650 \0$aResidual stress. =650 14$aAluminum alloy. =650 24$aCorrosion fatigue. =650 24$aFatigue crack growth rate. =650 24$aFriction stir welding. =650 24$aResidual stress. =700 1\$aBose Filho, W.,$eauthor. =700 1\$aTarpani, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 3, Issue 3 Special Issue on Fracture Toughness.$dWest Conshohocken, Pa. :$bASTM International, 2014$x2165-3992$yMPCACD =856 40$uhttp://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20130036.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170022 =003 IN-ChSCO =005 20160410061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 160410s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170022$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170022$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS227 =082 04$a624.2$223 =100 1\$aKandavel, T. K.,$eauthor. =245 10$aExperimental Investigations on Welding and Mechanical Characteristics of Sintered-Forged Plain Carbon Steel under Autogenous TIG Welding /$cT. K. Kandavel, D. Vijay. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b21 =520 3\$aThe present research work embraces the experimental studies on mechanical and metallurgical properties of powder metallurgy (P/M) plain carbon steel (Fe-0.5 %C) welded autogenously with various modes of current, namely, alternate current, direct current, mixed mode current, and pulse current (PC) using autogenous Tungsten Inert Gas (TIG) welding. The sintered specimens of rectangular shape synthesized through the P/M route were densified by cold upsetting to obtain maximum density. A pair of specimens were welded, and the weld quality was checked by standard nondestructive testing methods. Various mechanical tests were conducted using standard size specimens as per the ASTM standards. It is found from the results of various mechanical tests that the welded joint made by PC TIG welding exhibits the greatest tensile and impact strengths among the other modes of welded joint. Scanning Electron Microscopy (SEM) fractography of the tensile fractured surfaces reveal the brittle mode of fracture irrespective of the mode of welding currents, which are being used for joining the specimens. Optical microscopy, Energy Dispersive Spectroscopy (EDS), and X-ray Diffraction (XRD) analyses have been carried out to investigate microstructural changes and phase transformation of chemical constituents at the welded region. The hardness at the fusion zone is found to be higher because of pore-free microstructure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed April 10, 2016. =650 \0$aWelding. =650 14$aPowder metallurgy. =650 24$aCarbon steel. =650 24$aMicrostructure. =650 24$aScanning electron microscopy. =650 24$aSintering. =650 24$aWelding. =700 1\$aVijay, D.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170022.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170056 =003 IN-ChSCO =005 20160410061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 160410s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170056$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170056$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.1/86$223 =100 1\$aNarayana Murty, S. V. S.,$eauthor. =245 10$aDevelopment of Processing Map and Constitutive Relationship for Thermomechanical Processing of Aluminum Alloy AA2014 /$cS. V. S. Narayana Murty, Aditya Sarkar, P. Ramesh Narayanan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b30 =520 3\$aIsothermal hot compression tests were performed on aluminum alloy 2014 (AA2014) to study the evolution of microstructure over a wide range of temperatures (300°C–500°C) and strain rates (0.001–100 s–1). The true stress–true strain curves obtained at all deformation temperatures and strain rates showed gradual flow softening, which is typical of a dynamic recovery-type material such as aluminum. Processing maps that delineate the stable and unstable regions during hot working were developed and validated by comparing the microstructures recorded in the deformed specimens. Optimum processing conditions (temperature > 450°C, strain rate < 0.1 s–1) for the hot deformation of AA2014 were proposed based on contour maps of efficiency of power dissipation and strain-rate sensitivity parameter. The activation energy value (Qavg) for the hot working of AA2014 was calculated to be 181 kJ/mol–1. Finally, the constitutive equation for the hot working of AA2014 was established. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed April 10, 2016. =650 \0$aAluminum alloys$xThermomechanical treatment. =650 \0$aAluminum alloys. =650 14$aAluminum alloy AA2014. =650 24$aActivation energy. =650 24$aConstitutive equation. =650 24$aHot workability. =650 24$aProcessing maps. =700 1\$aRamesh Narayanan, P.,$eauthor. =700 1\$aSarkar, Aditya,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170056.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170058 =003 IN-ChSCO =005 20160410061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 160410s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170058$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170058$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA7 =082 04$a620$223 =100 1\$aLi, Jianfang,$eauthor. =245 10$aEffect of Nitriding on Antibacterial Performance of 8Cr17 and 4Cr13 Martensitic Stainless Steel /$cJianfang Li, Xiaojing He, Guannan Zhang, Xiangyu Zhang, Bin Tang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b19 =520 3\$aMartensitic stainless steel is widely used for medical apparatus, but it can carry a large number of bacteria and cause a potential risk of infection because it has no antimicrobial ability. In this paper, nitriding of 4Cr13 and 8Cr17 martensitic stainless steel was conducted to improve the antibacterial activity. The surface morphology and phase constituents of nitrided 4Cr13 and 8Cr17 specimens were characterized using scanning electron microscopy and X-ray diffraction. Nitrogen concentration profiles in the cross sections of the nitrided specimens were obtained by glow discharge spectroscopy. The antibacterial properties of this nitrided layer were evaluated by a plate-counting method. The antimicrobial ratios of nitrided 4Cr13 and 8Cr17 martensite stainless steel against Staphylococcus aureus were 98.13 % and 99.22 %, respectively, after 12 h. The results showed that the formations of chromium nitride (CrN) and two iron nitrides (Fe3N and Fe4N) are of vital importance to the antibacterial properties of martensitic stainless steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed April 10, 2016. =650 \0$aAcier martensitique$xMicrostructure. =650 \0$aMaterials Science. =650 14$aAntibacterial perform. =650 24$a4Cr13 and 8Cr17 martensitic stainless steel. =650 24$aNitriding process. =700 1\$aHe, Xiaojing,$eauthor. =700 1\$aTang, Bin,$eauthor. =700 1\$aZhang, Guannan,$eauthor. =700 1\$aZhang, Xiangyu,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170058.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170087 =003 IN-ChSCO =005 20160410061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 160410s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170087$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170087$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.C7 =082 04$a620.1/82$223 =100 1\$aDing, T.,$eauthor. =245 10$aHigh Temperature Characteristics of a Carbon Strip Sliding against Copper with Electrical Current /$cT. Ding, Q. D. He, Yi. Yang, Y. J. Fan, J. Yuan, S. Q. Wang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b22 =520 3\$aHigh temperature and arc discharge are two important phenomena that occur in the electrical sliding processes. The extensive adhesive wear, due to high temperature, and arc erosive wear are two mechanisms that potentially cause severe wear of copper-carbon strips with electrical current. Herein, we describe a series of experiments done to better understand the high-temperature characteristics of a carbon strip rubbing against copper with electrical current passing from one to the other. During the experiments, the temperature of the copper-carbon strips was recorded and the wear volumes of carbon strips were measured. The results show that the carbon strip wear volumes are larger when electrical currents pass through the strips. To study how the temperature affects the wear of carbon strips, several wear tests were conducted at an elevated temperature both with and without electrical currents. The results show that adhesive wear is the main mechanism to cause severe wear of carbon strips. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed April 10, 2016. =650 \0$aCarbon Strip. =650 \0$aCopper. =650 14$aHigh temperature. =650 24$aAdhesive wear. =650 24$aElectrical current. =650 24$aWear volume. =700 1\$aFan, Y. J.,$eauthor. =700 1\$aHe, Q. D.,$eauthor. =700 1\$aWang, S. Q.,$eauthor. =700 1\$aYang, Yi.,$eauthor. =700 1\$aYuan, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170087.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170117 =003 IN-ChSCO =005 20160410061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 160410s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170117$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170117$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.F5 =082 04$a620.1/97$223 =100 1\$aLiu, Leibo,$eauthor. =245 10$aOn the Oxidative Ablation and Mechanical Properties of T300 Carbon Fibers at Elevated Temperatures /$cLeibo Liu, Pengfei Huang, Min Miao, Qiqige Wuyun, Tenghui Li, Fei Su. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b15 =520 3\$aCarbon fibers are the main component and load carrier within many high-temperature composites. Oxidative ablation of carbon fibers is the main failure mechanism of high-temperature composites and significantly affects the mechanical properties of the composites. The effects of the ablation of carbon fiber at high temperatures on carbon fiber mechanical properties, nevertheless, have not been systematically studied in the available literature. In the present investigation, the oxidative ablation behavior of carbon fibers from room temperature to 900°C has been systematically investigated by employing a thermogravimetric analyzer and in situ video detection. Detectable carbon fiber weight loss was initiated when the temperature was elevated to 600°C within the air environment. The video images showed that the color of the carbon fiber surfaces changed dramatically and then the fibers disappeared gradually, indicating that the carbon fibers underwent a chemical reaction, i.e., oxidative ablation. The static mechanical strength of carbon fiber at various temperatures was investigated and was found to start decreasing significantly at temperatures above 500°C, even though no obvious oxidative ablation occurred. X-ray photoelectron spectroscopy (XPS) and Raman spectrum reveal that the microstructure transition from graphite to nongraphite carbon is the main reason for strength reduction. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed April 10, 2016. =650 \0$aCarbon fibers. =650 14$aConstitutivearbon fiber. =650 24$aMechanical behavior. =650 24$aOxidative ablation. =700 1\$aHuang, Pengfei,$eauthor. =700 1\$aLi, Tenghui,$eauthor. =700 1\$aMiao, Min,$eauthor. =700 1\$aSu, Fei,$eauthor. =700 1\$aWuyun, Qiqige,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170117.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170129 =003 IN-ChSCO =005 20160410061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 160410s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170129$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170129$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA462 =082 04$a620.1$223 =100 1\$aKolawole, S. K.,$eauthor. =245 10$aTransitions from Pits to Cracks during Stress Corrosion Cracking in a Low-Carbon Steel /$cS. K. Kolawole, J. D. Obayemi, F. O. Kolawole, A. B. O. Soboyejo, W. O. Soboyejo. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aThis article presents the results of a combined experimental and analytical/computational study of the transition from corrosion pits to stress corrosion cracks during the exposure of low-carbon steel to environments with different pH levels (pH of 3, 5, 8, and 11). The transition from pits to cracks is elucidated via confocal microscopy and scanning electron microscopy. The stress concentrations associated with possible pit sizes and configurations are also modeled using finite element analyses and fracture mechanics models. Finally, the implications of the results are discussed for the modeling of the transition from pitting to stress corrosion cracking in low-carbon steels. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed April 10, 2016. =650 \0$aAlloys$xStress corrosion. =650 \0$aCorrosion sous tension. =650 \0$aStress corrosion. =650 14$aLow-carbon steel. =650 24$aCorrosion pits. =650 24$aFinite element and fracture mechanics models. =650 24$aStress corrosion cracking. =700 1\$aKolawole, F. O.,$eauthor. =700 1\$aObayemi, J. D.,$eauthor. =700 1\$aSoboyejo, A. B. O.,$eauthor. =700 1\$aSoboyejo, W. O.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170129.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170141 =003 IN-ChSCO =005 20160410061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 160410s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170141$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170141$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ288 =082 04$a621.1/83$223 =100 1\$aSun, Zhiwei,$eauthor. =245 10$aFailure Analysis of Superheater Tubes Cracking of a Boiler in a Power Plant /$cZhiwei Sun, Yuling Fan, Shugen Xu, Mingda Song, Yuan Zhang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references$b16 =520 3\$aA failure analysis was performed on a power plant's boiler superheater tubes that had burst. The macromorphology, chemical composition, microstructure, and mechanical properties were analyzed by experimental testing. Results showed that the superheater tube bursts can be classified as creep ductile cracks because the two tubes operated in overtemperature and low heat transfer efficiency conditions for a long time, and one of the tubes did not meet the material requirements. Finally, preventative measures were put forward. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed April 10, 2016. =650 \0$aSteam power plants. =650 \0$aSteam-boilers. =650 14$aSuperheater. =650 24$aCreep fracture. =650 24$aTube cracking. =700 1\$aFan, Yuling,$eauthor. =700 1\$aSong, Mingda,$eauthor. =700 1\$aXu, Shugen,$eauthor. =700 1\$aZhang, Yuan,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170141.htm =LDR 03762nab 2200553 i 4500 =001 MPC20160100 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20160100$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20160100$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC320 =082 04$a536.2$223 =100 1\$aAkinluwade, K. J.,$eauthor. =245 10$aModeling of Heat Transfer in Rotary Furnaces Using Finite Element Approach /$cK. J. Akinluwade, F. P. Ibitoye, D. A. Isadare, M. O. Adeoye, A. R. Adetunji. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe pattern of heat flow in a 100-kg capacity rotary furnace was studied at transient state using finite element technique. The study combined volumetric analysis of combusting fuel with finite element analytical computation of heat transfer within the furnace hearth. A parabolic partial differential equation was used in combination with the results of volumetric analysis of combusting fuel, which is applicable to transient heat transfer. The results provide a finite element approach to computational modeling of medium-sized diesel-fired melting furnaces in the metallurgical industry. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aHeat$xTransmission. =700 1\$aAdeoye, M. O.,$eauthor. =700 1\$aAdetunji, A. R.,$eauthor. =700 1\$aIbitoye, F. P.,$eauthor. =700 1\$aIsadare, D. A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20160100.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170053 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170053$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170053$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS176 =082 04$a621.3815/284$223 =100 1\$aDave, Divyeshkumar P.,$eauthor. =245 10$aAssessment of Sputtered Chromium Oxide-Nitride Coatings /$cDivyeshkumar P. Dave, Nicky P. Patel, Kamlesh V. Chauhan, Sushant K. Rawal. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe main purpose of this research work is to explore the formation of chromium oxide-nitride coatings by radio frequency (RF) magnetron sputtering using chromium as a target, oxygen and nitrogen as reactive gases, along with helium as an inert gas. The consequence of temperature variation on the formation of chromium oxide-nitride coatings and their properties is reported in this paper. The identification of respective oxide/nitride phases of chromium was done by X-ray diffraction. A wettability study of chromium oxide-nitride coatings was done using a contact angle–measuring system. Initially, at a lower deposition temperature of 200°C, the deposited films were amorphous. However, when the temperature was increased from 200°C to 600°C, the formation of crystalline films was observed, and its wettability behavior was transmuted from hydrophilic to hydrophobic. The influence of temperature variation on the tribological properties of mixed chromium oxide-nitride coatings is examined. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aMetal oxide semiconductors. =650 \0$aTransistors. =700 1\$aChauhan, Kamlesh V.,$eauthor. =700 1\$aPatel, Nicky P.,$eauthor. =700 1\$aRawal, Sushant K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170053.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170077 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170077$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170077$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA409 =082 04$a620.166$223 =100 1\$aPatra, A.,$eauthor. =245 10$aEvaluation of Thermal, Fracture, and High Temperature Behavior of Mechanically Alloyed and Spark Plasma Sintered Nano-Y2O3 Dispersed W-Ni-Mo and W-Ni-Ti-Nb Alloys /$cA. Patra, R. Saxena, R. R. Sahoo, S. K. Karak, T. Laha. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTungsten (W), Nickel (Ni), Molybdenum (Mo), Niobium (Nb), Titanium (Ti) based W-Ni-Mo and W-Ni-Ti-Nb alloys with nano-yttrium oxide (Y2O3) dispersion and nominal compositions of W79Ni10Mo10(Y2O3)1 (Alloy A) and W74Ni10Ti5Nb10(Y2O3)1 (Alloy B) (all in weight percent) were fabricated by mechanical alloying and spark plasma sintering (SPS) at 1,000°C, 1,200°C, and 1,400°C for 5 min with 75 MPa pressure. The thermal behavior of milled powders and microstructure evolution of milled and consolidated products were examined by scanning electron microscopy, energy-dispersive spectroscopy, and high-resolution transmission electron microscopy. The activation energy of recrystallization for Alloy B is higher as compared to the recently investigated oxide dispersion-strengthened tungsten alloys. The mode of fracture is predominantly intergranular with a titanium addition. Alloy A SPS at 1,400°C shows superior oxidation resistance at 1,000°C as compared to Alloy B at the identical SPS temperature (1,400°C), owing to a higher intensity of the protective nickel tungsten tetroxide, yttrium tungstate oxide scale formation, and less variation in the molar volume of formed oxides. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aAlloys$xFatigue. =650 \0$aAlloys$xFracture. =650 \0$aAlloys. =650 \0$aFracture mechanics. =650 \0$aMetals$xFracture. =700 1\$aKarak, S. K.,$eauthor. =700 1\$aLaha, T.,$eauthor. =700 1\$aSahoo, R. R.,$eauthor. =700 1\$aSaxena, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170077.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170100 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170100$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170100$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.7 =082 04$a620.1122$223 =100 1\$aCrawford, Bruce R.,$eauthor. =245 10$aThe Development of Retrogression and Re-aging to Manage Environmental Degradation in Australian Defence Force Aircraft /$cBruce R. Crawford, Alexandra Shekhter, Chris Loader. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article describes a project in which the Retrogression and Re-aging (RRA) heat treatment was demonstrated to be a viable means of improving the corrosion resistance of 7075-T651 components of the Royal Australian Air Force AP-3C and C-130J-30 aircraft while maintaining the mechanical properties above the material's A-Basis and preserving component functionality. This was achieved by a phased development process starting with the determination of the mechanical properties of the RRA-treated material and culminating in technology demonstrators on thick-section C-130J-30 lower ring segment components and a thin-section AP-3C component. This article describes the results obtained and the lessons learned during the process. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCorrosion and anti-corrosives. =650 \0$aEnvironmental degradation. =650 \0$aMaterials$xDeterioration. =700 1\$aLoader, Chris,$eauthor. =700 1\$aShekhter, Alexandra,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170100.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170126 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170126$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170126$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA460 =082 04$a620.16$223 =100 1\$aHu, Kuanhui,$eauthor. =245 10$aEffects of Austenitizing and Quenching Parameters on Microstructures and Mechanical Properties of Press Hardened WHT1500HF Steel /$cKuanhui Hu, Guifeng Zhou, Jing Liu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe effect of austenitizing temperature and the cooling rate during quenching on the microstructure and mechanical properties of press hardening steel were investigated. The as-quenched microstructure and prior austenite grain size were characterized by optical microscopy and transmission electron microscopy. The mechanical properties were evaluated by uniaxial tensile tests. The results showed that the ultimate tensile strength and yield strength values were the highest and the formability index value was excellent for the water-quenched samples compared to the oil-quenched samples or the die-quenched samples. After quenching at different cooling rates, the microstructure was fully martensite, in which the martensite exhibited lath morphology. As the cooling rate increased, the martensite laths became finer and the martensite packets size decreased. The martensite laths for the specimens with the highest cooling rate were finer than for those of specimens with lower cooling rates, and there was a larger number of fine needle-like ?-Fe2C in the matrix of martensite laths. For the WHT1500HF steel, the optimum austenitizing temperature is 900°C, which resulted in a mean austenitic grain size of 9.4 ?m. Therefore, the properties of the hot stamping steel can be improved through using an optimal austenitizing temperature and increasing the quenching rates by changing the physical die design. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aMetals$xMechanical properties. =700 1\$aLiu, Jing,$eauthor. =700 1\$aZhou, Guifeng,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170126.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170138 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170138$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170138$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC476.6 =082 04$a535.355$223 =100 1\$aPosavec, T.,$eauthor. =245 10$aLow Temperature Photoluminescence in Some Common Polymers /$cT. Posavec, S. Nepal, S. V. Dordevic. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aWe have studied the temperature dependence of photoluminescence (PL) in several common polymers, such as low-density polyethylene, polycarbonate, acrylic, polypropylene, polystyrene, and polyurethane. We found a pronounced temperature dependence of the photoluminescence peak in all polymers. Emission intensity was found to increase as temperature decreased but at different rates for different polymers. Acrylic was found to have the strongest increase, and its temperature range was extended down to 5 K. Below 77 K, its PL intensity was found to saturate to a constant value. The analysis of the data indicates that in all studied polymers the PL intensity at all measured temperatures can be described with the Arrhenius formula. From the best fits of the data, the activation energy was extracted for all studied polymers. Our results might have implications for the low temperature applications of these common polymers. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aPhotoluminescence. =700 1\$aDordevic, S. V.,$eauthor. =700 1\$aNepal, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170138.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170139 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170139$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170139$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS325 =082 04$a672.36$223 =100 1\$aRomano-Acosta, L. F.,$eauthor. =245 10$aOptimization of Heating Cycles Prior Forging for Large Steel Ingots Based on a Simulation Model /$cL. F. Romano-Acosta, I. Álvarez-Elcoro, O. Zapata-Hernandez, L. Leduc-Lezama. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA simulation model has been used to calculate temperature distribution and internal stresses of steel ingots. The aim of this study is to optimize the heating cycles without compromising the mechanical integrity of the ingots, which ideally will result in a reduction in energy consumption and an increase in furnace productivity. The heating cycles of three ingots of different materials (ASTM A105, AISI 4330, and AISI 8630) and sizes (1.60, 1.75 and 1.32 m) are optimized. The optimization procedure of the heating cycle is based on a time reduction at each step of the set point. The phase transformation temperature at the ingot center was taken as a reference because this is where the higher stresses are developed. A sample of a 1 m Ø AISI 8630 ingot was characterized with a Scanning Electron Microscope, Energy-dispersive X-ray Spectroscopy, X-Ray Diffraction, and Differential Scanning Calorimetry. Results show precipitates in the as-cast condition, which will eventually be dissolved after a complete heating cycle. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aHardness. =650 \0$aMetals$xHardenability. =650 \0$aSteel$xHeat treatment. =650 \0$aSteel$xHeating. =650 \0$aSteel. =650 \0$aTempering. =700 1\$aÁlvarez-Elcoro, I.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170139.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170143 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170143$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170143$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ241 =082 04$a621.8/15$223 =100 1\$aGanesh, K. C.,$eauthor. =245 10$aThermo-Mechanical Analysis of Activated Tungsten Inert Gas Welding (A-TIG) of Type 316LN Stainless Steel Thin Plates /$cK. C. Ganesh, M. Vasudevan, K. R. Balasubramanian, P. Vasantharaja, N. Chandrasekhar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present study, thermo-mechanical behavior of 316LN stainless steel thin plates during activated tungsten inert gas (A-TIG) welding was investigated using SYSWELD®. A-TIG welding was carried out with more reduced heat input for fabricating 3-mm-thick 316LN stainless steel plates than that of the conventional TIG welding process. Induced transient temperature during welding was measured using a K-type thermocouple. A pulse-echo ultrasonic test was carried out using a 2-MHz probe employing critically refracted longitudinal waves for measuring residual stresses across the weld joint. A digital height gauge was used to quantify the distortion caused during welding. There was a good agreement between the predicted and measured thermal cycles, residual stresses, and distortion. The concentrated heat intensity of A-TIG welding induced higher surface temperature in the weld center, produced a narrow weld bead, and exhibited a sharp temperature gradient at the weld/base metal interface. Peak residual stress and distortion of the A-TIG weld joint were found to be less than that of the TIG weld joint. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aStainless steel. =700 1\$aBalasubramanian, K. R.,$eauthor. =700 1\$aChandrasekhar, N.,$eauthor. =700 1\$aVasantharaja, P.,$eauthor. =700 1\$aVasudevan, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170143.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170148 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170148$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170148$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1101 =082 04$a668.405$223 =100 1\$aBauer, Benjamin,$eauthor. =245 10$aCrack-Size Measurement of Additive Manufactured Plastics Based on the DCPD Method /$cBenjamin Bauer, Wadim Reschetnik, Gunter Kullmer, Hans Albert Richard. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAdditive manufacturing offers the possibility of producing novel plastic products, which can be unique and complex, especially when the use of load-bearing components leads to a periodic load. Therefore, plastic components must also be examined for a sufficient service life. The aspects of crack initiation and crack propagation are particularly important. In this regard, a significant parameter is the crack propagation curve, for whose determination a continuous crack-size measurement is required. This article addresses how far the Direct Current Potential Drop (DCPD) method can be applied on additive manufactured plastics in order to make a statement about the fracture mechanical behavior of the materials. For this reason, the surfaces of compact tension (CT) specimens were coated with an electrically conductive layer using two different coating methods. Referring to this, experimental investigations were carried out in regard to the applicability of the DCPD method. Overall, two different coating methods were tested with experimental investigations. The experiments showed that the methods of galvanization and specimen coating enabled the application of the DCPD method to additive manufactured plastics. Furthermore, fracture mechanical investigations were carried out. In this context, crack propagation curves were determined by using both methods, and typical fracture mechanics parameters, e.g., threshold value, ?KI,th, and stress-intensity factor at unstable crack propagation, ?KIC, were identified. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aPlastics. =700 1\$aKullmer, Gunter,$eauthor. =700 1\$aReschetnik, Wadim,$eauthor. =700 1\$aRichard, Hans Albert,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170148.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170150 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170150$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170150$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.N5 =082 04$a620.18$223 =100 1\$aHack, Harvey,$eauthor. =245 10$aFatigue and Corrosion Fatigue Properties of Additive-Manufactured Nickel Alloy 625 and Ti-6Al-4V /$cHarvey Hack, Scott Olig, Erik Knudsen, Richard Link, Adelina Beckwith, Attilio Arcari. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSpecimen blanks of additive-manufactured nickel Alloy 625 and Ti-6Al-4V were produced by the laser powder-bed-fusion process (L-PBF) with the principal test axis in both the Z direction (parallel to the build direction) and the X-Y direction (perpendicular to the build direction). The high cycle fatigue and corrosion fatigue properties of these metals were measured using R. R. Moore rotating cantilever fatigue tests, both in air and with a salt water drip on the test sections. Testing was conducted in order to determine the fatigue and corrosion fatigue limits of these materials at 108 cycles. The fatigue limit for L-PBF Alloy 625 material at 108 cycles in air was roughly 48 ksi (331 MPa), independent of build orientation. This is similar to the air fatigue limit of wrought material. The corrosion fatigue limit for L-PBF Alloy 625 material at 108 cycles in salt water was roughly 39 ksi (269 MPa), which was also independent of build orientation and slightly below the values for wrought material and values obtained by other investigators. The fatigue limit for hot isostatic pressed L-PBF Ti-6Al-4V material at 108 cycles in air was roughly 90 ksi (620 MPa), independent of build orientation. This is significantly better than the air fatigue limit of wrought material. The corrosion fatigue limit for L-PBF Ti-6Al-4V material at 108cycles in salt water was roughly 78 ksi (540 MPa), which was also independent of build orientation, better than values for wrought material, and comparable to values obtained by other investigators. The fatigue crack growth rate behavior in air was characterized and compared with information available in the literature. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aNickel alloys. =700 1\$aArcari, Attilio,$eauthor. =700 1\$aBeckwith, Adelina,$eauthor. =700 1\$aKnudsen, Erik,$eauthor. =700 1\$aLink, Richard,$eauthor. =700 1\$aOlig, Scott,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170150.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170157 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170157$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170157$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP990 =082 04$a668.14$223 =100 1\$aBridge, J. W.,$eauthor. =245 10$aDetermining the Water Holding Capacity of Synthetic Track Materials for Thoroughbred Horse Racing /$cJ. W. Bridge, H. Rubin, K. M. Dempsey, M. L. Peterson. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aWax-coated sand, fiber, and rubber surfaces have been in use for more than a decade at a number of North American Thoroughbred racetracks. These synthetic, all-weather racing surfaces were designed to allow races on wet surfaces without impacting performance. As these tracks have aged, some have areas that no longer drain properly. A number of approaches have been taken to refresh the surfaces including re-waxing, adding fiber, and even turning over the surfaces. The results have shown mixed success, with water pooling on top of some tracks and more water retained in the depth profile on other tracks. A gravity-based water holding capacity (WHC) test has been developed to determine the amount of water retained in these surfaces. Traditional permeability measurements are also used in this study. Samples of new and six-year-old synthetic surfaces are taken from four North American Thoroughbred racetracks to examine both the drainage and water holding of the material. These surfaces were identified as having both adequate and inadequate track performances during wet weather. Control samples were also prepared with and without the wax binder. Measuring the WHC at different surface locations may help racetrack superintendents identify problem areas and quantify material changes over time. Test results generally showed that a certain amount of wax binder is necessary to minimize water holding in synthetic surfaces, but too much wax is detrimental. The amount and size of the polymer fiber and rubber constituents, as well as organic material and particulates present, also affects the WHC. Developing threshold values for an “acceptable” WHC for specific synthetic racetracks, as well as understanding primary factors that affect water holding, will allow researchers to set a performance standard to determine the timing and type of renovations that are needed to maintain safe and consistent synthetic track surfaces. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSynthetic product$xTesting. =650 \0$aSynthetic products. =700 1\$aDempsey, K. M.,$eauthor. =700 1\$aPeterson, M. L.,$eauthor. =700 1\$aRubin, H.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170157.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170158 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170158$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170158$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA660.C6 =082 04$a624.17725$223 =100 1\$aZureick, Abdul-Hamid,$eauthor. =245 10$aStructural Engineering Test for Determining the Circumferential Modulus of Circular Pipes and Tubes /$cAbdul-Hamid Zureick, Andrew J. Bechtel. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article proposes a structural engineering test method for determining the transverse flexural modulus of circular tubes and pipes made from fiber-reinforced polymer composite. The computed modulus from the proposed test can be used both in the design and in the qualification and acceptance procedures of these structural components. To validate the proposed test method, experiments were conducted on 23 metallic and 4 carbon fiber-reinforced polymer composite rings having different material properties, diameters, and thicknesses. In addition, three different test setups and measurement techniques were used where each ring was subjected to two collinear tension forces while recording both the force and the change-in-diameter along the line of action of the two forces. The recorded data was then used to compute the transverse moduli of the circular tubes. The transverse modulus values determined from the proposed test were compared with those obtained from material tensile and flexural coupon tests carried out on the same tube materials. The three test setups and measurement techniques yielded satisfactory results, suggesting that the proposed test method is viable for adoption in both laboratory and field testing while balancing its ease of use and cost. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aStructural engineering. =700 1\$aBechtel, Andrew J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170158.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170160 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170160$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170160$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.34 =082 04$a620.112$223 =100 1\$aLucon, Enrico,$eauthor. =245 10$aInstrumented Impact Testing of Miniaturized Charpy Specimens of AM Ti-6Al-4V /$cEnrico Lucon, Nikolas Hrabe. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAn investigation on the impact toughness properties of wrought and additively manufactured (AM) Ti-6Al-4V was conducted at National Institute for Standards and Technology (NIST) Boulder by means of instrumented impact tests on miniaturized Charpy specimens. Full transition curves for absorbed energy and lateral expansion were obtained by performing tests in the temperature range between –196°C and 700°C. The effect of various parameters was investigated for AM specimens, namely specimen orientation, hot isostatic pressing (HIPing), and notch configuration (printed or machined). Our results indicate that AM specimens exhibit equivalent or better impact toughness than wrought material after HIPing and that the material is more resistant to cracks growing in the plane perpendicular to the build direction than in the plane containing the build direction. HIPing has a significantly beneficial effect for the AM material, while no effect of notch configuration was observed from the results obtained. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aImpact$xTesting. =700 1\$aHrabe, Nikolas,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170160.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170161 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170161$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170161$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.P5 =082 04$a620.19236$223 =100 1\$aBrailo, M.,$eauthor. =245 10$aThe Investigation of Tribological Properties of Epoxy-Polyether Composite Materials for Using in the Friction Units of Means of Sea Transport /$cM. Brailo, A. Buketov, S. Yakushchenko, O. Sapronov, V. Vynar, O. Kobelnik. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe tribological properties of composite materials with microdispersed proportions, based on the epoxy-polyether matrix, were investigated. The specimens were tested during dry friction and in the conditions of a corrosive environment. It was determined that at dry friction, the coefficient of friction is f = 0.33–0.35, and the contact temperature of the experimental specimen in the area of mechanical interaction of surfaces is T = 366–369 ?. It was proved that composites, which were tested in the conditions of a corrosive environment, differ with improved antifriction properties and increased durability. In this case, the coefficient of friction is f = 0.08–0.09, and the contact temperature in the friction area is T = 295–298 ?. It was stated that the wetting of the surface of the friction and heat removal from its area significantly affects the properties of the polymer during friction. In particular, the work surface of the source material and polymer, after testing in different conditions, was analyzed with the methods of optical and electron microscopy. The presence of lines of friction and microcracking of specimens at elevated temperatures was revealed. The elemental composition of the surfaces of materials in different areas was investigated with the help of X-ray microanalysis. The presence of selective transfer effect during the testing was ascertained as a result of analysis of the elemental composition. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aTribology. =700 1\$aBuketov, A.,$eauthor. =700 1\$aKobelnik, O.,$eauthor. =700 1\$aSapronov, O.,$eauthor. =700 1\$aVynar, V.,$eauthor. =700 1\$aYakushchenko, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170161.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170162 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170162$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170162$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.2 =082 04$a620.1127$223 =100 1\$aFarrell, Shannon P.,$eauthor. =245 10$aAnalysis of Seeded Defects in Laser Additive Manufactured 300M Steel /$cShannon P. Farrell, Joseph Deering. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis research activity was initiated to better assess the capacity for traditional nondestructive testing (NDT) approaches to ascertain the defects inherent to materials fabricated through a directed energy laser additive manufacturing (LAM) process. A methodology was developed to intentionally seed defects in 300M steel specimens through intermittent modification of fabrication parameters. Several 300M steel specimens were fabricated and the concentration of defects or bulk density was characterized using optical microscopy and variations of the Archimedes' principle. Specimens were then evaluated using NDT (radiographic testing, ultrasonic testing). Results show that by using n-hexane as the displacement liquid, the Archimedes' principle was found to have repeatability in density values of 0.1 ± 0.1 %. The results reveal the unique defects produced through the LAM process and the limitations for conventional NDT techniques to adequately detect defects in LAM materials. Ultrasonic testing was found to be a promising tool for assessing the LAM defect distribution. Future work will focus on LAM alloys with higher densities and relate microstructure and defects to overall material performance. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aNondestructive testing. =700 1\$aDeering, Joseph,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170162.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170166 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170166$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170166$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.F6 =082 04$a668.493$223 =100 1\$aAshrith, Hiriyalu Shivegowda,$eauthor. =245 10$aInfluence of Materials and Machining Parameters on Drilling Performance of Syntactic Foams /$cHiriyalu Shivegowda Ashrith, Mrityunjay Doddamani, Vinayak Neelakanth Gaitonde, Nikhil Gupta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe effects of drilling parameters and material properties are investigated on epoxy matrix syntactic foams reinforced with 20, 40, and 60 volume percent glass microballoon. The influences of cutting speed, feed, drill diameter, and filler content on drilling performance are studied based on the full factorial design of experiments using tungsten carbide twist drills. Based on experimental results, machinability aspects within the range of the chosen input parameters are predicted using response surface methodology-based models, which can guide industrial practitioners for choosing the appropriate process parameters. Microscopy is conducted on the drilled specimens to understand crack initiation and propagation mechanisms. The thrust force and specific cutting coefficient of syntactic foam are 40 % lower as compared to those of neat epoxy. The surface roughness of syntactic foams is higher than that of neat epoxy. The micrographs of drill bits show negligible tool wear. These results show the possibility of using syntactic foams in industrial applications in which the drilling of material is required for reasons such as joining using bolts. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCeramic-matrix composites. =650 \0$aFoamed materials. =700 1\$aDoddamani, Mrityunjay,$eauthor. =700 1\$aGaitonde, Vinayak Neelakanth,$eauthor. =700 1\$aGupta, Nikhil,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170166.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170167 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170167$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170167$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.11830724$223 =100 1\$aAbbas, Saqlain,$eauthor. =245 10$aA Review on SHM Techniques and Current Challenges for Characteristic Investigation of Damage in Composite Material Components of Aviation Industry /$cSaqlain Abbas, Fucai Li, Jianxi Qiu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (35 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIntroduction of composites for aircraft fabrication has given the opportunity to all researchers and original equipment manufacturers to design a lightweight structure that will reduce both fuel consumption and harmful emissions. Reliability and cost of implementing structural health monitoring (SHM) systems are two critical parameters for the utilization of composite materials in the aviation industry. SHM of composite material components in the aviation industry not only lessens the downtime of aircraft but also enhances the possibility of damage detection in order to avoid severe failure. This article presents a case study of SHM systems that has been developed from research and implemented for the inspection and safety of recent aircraft structures. Compulsory components required for proper working of an SHM system and the basis and classification of defects in composite material components of aircraft are thoroughly explained in this article. Furthermore, characterization of SHM techniques (on the basis of functioning, advantages, and limitations) for crack detection and challenges of SHM systems are also part of this case study. An experimental work and its results have been well expressed regarding guided wave inspection using two different types of fiber-optic sensors for quasi-isotropic carbon fiber–reinforced plastic laminate. The ultimate goal of this article is to highlight the current challenges of SHM and promote the concept that SHM has great potential for research in the aviation industry. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aComposite materials$xTesting. =700 1\$aLi, Fucai,$eauthor. =700 1\$aQiu, Jianxi,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170167.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170171 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170171$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170171$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.38 =082 04$a620.1123$223 =100 1\$aManikandan, P.,$eauthor. =245 10$aResidual Strength and Fracture Toughness of 0.3C-CrMoV(ESR) Ultrahigh-Strength Steel Used for Solid Booster Motor Cases /$cP. Manikandan, G. Sudarsana Rao, S. V. S. Narayana Murty, Goutam Nayak, A. K. Mishra, P. Ramesh Narayanan, P. Ramkumar, P. V. Venkitakrishnan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$a0.3C-CrMoV(ESR) steel is an ultrahigh-strength low-alloy steel developed primarily for use as a cost-effective material for aerospace pressure vessel applications. These large-sized (Ø 2,800 mm) pressure vessels are manufactured by auto Tungsten Inert Gas (TIG) welding of plates/end domes. During the welding process, defects are likely to be generated, which will reduce the strength of the material. Therefore, residual strength in the presence of a possible missed defect has to be analyzed to qualify the pressure vessel for aerospace applications. In order to evaluate the residual strength and fracture toughness of welded specimens using surface crack tension specimens, mechanical tests were conducted as per the ASTM E740/E740M-03(2010) standard, Standard Practice for Fracture Testing with Surface-Crack Tension Specimens. Plates of 7.6 mm were TIG welded with filler wire matching the chemical composition of the base metal. The welded plates were hardened at 920 ± 10°C and tempered at 505 ± 5°C. The material exhibited a 0.2 % proof strength of 1,417 MPa, ultimate strength of 1,466 MPa, residual strength (?r) of 1,301 MPa, and apparent fracture toughness (KIe) of 86.5 MPa?m in the presence of a surface crack, sized 6 by 2 mm. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aFatigue$xTesting. =700 1\$aMishra, A. K.,$eauthor. =700 1\$aMurty, S. V. S. Narayana,$eauthor. =700 1\$aNarayanan, P. Ramesh,$eauthor. =700 1\$aNayak, Goutam,$eauthor. =700 1\$aRamkumar, P.,$eauthor. =700 1\$aRao, G. Sudarsana,$eauthor. =700 1\$aVenkitakrishnan, P. V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170171.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180006 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180006$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180006$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP968 =082 04$a338.476683$223 =100 1\$aRavichandran, G.,$eauthor. =245 10$aTaguchi-Based ANN Predictions to Analyze the Tensile Strength of Adhesive-Bonded Single Lap Joints /$cG. Ravichandran, G. Rathnakar, Pinto Ratan, John Joshy, Suresh Vishal. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe adhesive bonding method is commonly used in various industries to join different materials because of its benefits, which include a high strength-to-weight ratio, low cost, and high efficiency properties. Automotive, aerospace, marine, and construction industries are increasingly using adhesively bonded joints because the hand layup techniques involve simpler fabrication methodologies, maintenance procedures, and controllable stress distribution parameters in the overlap region, which ultimately lead to easier production of automobile, aircraft, and ship components. The objective of the present work is primarily to assess the overlap length in conjunction with the adhesive strength of glass-epoxy adherends bonded with epoxy resin. In this article, the experiments are performed on single lap-bonded joints. The parameters considered for the current work involve the length of overlap, which is maintained at 15, 25, and 35 mm, and adhesive bonding thickness that is maintained at 0.2, 0.3, and 0.5 mm, respectively. The strength of the adhesively bonded lap joint is determined using a Universal Testing Machine (Lloyd Instruments Ltd., West Sussex, United Kingdom) with a 1–20 kN capacity. The investigational outcome reveals that, as the overlap length of the adhesively bonded single lap joint increases, a substantial increase in the joint strength is observed; additionally, it is noted that, with the increase in adhesive thickness, the joint strength decreases. It was observed that the artificial neural network–predicted values from the analysis were extremely close to the experimental values, and the difference between the experimental and predicted values was very small. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aAdhesives. =700 1\$aJoshy, John,$eauthor. =700 1\$aRatan, Pinto,$eauthor. =700 1\$aRathnakar, G.,$eauthor. =700 1\$aVishal, Suresh,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180006.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180014 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180014$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180014$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC766.M36 =082 04$a620.1064$223 =100 1\$aZhang, Hansong,$eauthor. =245 10$aThe Magnetorheological Performance of MRFs Based on Different Types of Carbonyl Irons /$cHansong Zhang, Zhide Hu, Hua Yan, Jianjian Yang, Fanghao Niu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMagnetorheological fluid (MRF) is a kind of promising smart functional material with significant magnetorheological (MR) performance. MRFs are typically fabricated by mixing magnetizable microparticles into a base oil. As the most important part of MRFs, magnetizable carbonyl iron (CI) particles show an obvious impact on the performance of MRFs. In this work, MRFs based on six types of CI particles were fabricated, and their MR performance was tested under both rotational and oscillatory modes by a parallel plate rheometer coupled with an MR device. The results indicate that MRFs based on big particles with high iron content present more significant MR performance in both rotational and oscillatory modes. Conversely, small particles were likely to form weaker structures that displayed lower shear stress and storage modulus. Meanwhile, silicon dioxide–coated CI particles led to decreased shear stress and storage modulus but dilated the linear viscoelastic range of MRFs. MRFs based on phosphate-modified CI particles presented a high storage modulus but low shear stress. Moreover, the normal force test results also suggest that big particles with high iron content are likely to form stronger microstructures that macroscopically present relatively higher normal forces. The suspension stability of MRFs was measured by direct observation. The results indicate that MRFs based on surface-modified and small particles have better suspension stability. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aMagnetorheological fluids. =700 1\$aHu, Zhide,$eauthor. =700 1\$aNiu, Fanghao,$eauthor. =700 1\$aYan, Hua,$eauthor. =700 1\$aYang, Jianjian,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180014.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180026 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180026$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180026$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN948.S7 =082 04$a549.75$223 =100 1\$aAbdel-Karim, R.,$eauthor. =245 10$aCorrosion Characteristics of ASTM A106 Grade B Carbon Steel Pipelines Exposed to Sodium Sulfate Solutions /$cR. Abdel-Karim, M. Nabil, Y. Reda, S. El-Raghy. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCarbon steel is used in large-tonnage petroleum production and refining. In this work, the corrosion behavior of ASTM A106 Grade B carbon steel subjected to sodium sulfate (Na2SO4) environments was studied in a range of sulfate concentrations and different working temperatures. Increasing the sulfate ion content had an inhibiting effect on the corrosion behavior of carbon steel. The highest corrosion rate was detected for electrolytes containing 0.5 M Na2SO4. The influence of temperature was significant on the oxide layer density and stability, while there was the appearance of thick cracked layer as the temperature and the sulfate concentration increased. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSodium sulfate. =700 1\$aEl-Raghy, S.,$eauthor. =700 1\$aNabil, M.,$eauthor. =700 1\$aReda, Y.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180026.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180039 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180039$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180039$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.118$223 =100 1\$aSadeghi, B.,$eauthor. =245 10$aWear Behavior of Al-Based Nanocomposites Reinforced with Bimodal Micro- and Nano-Sized Al2O3 Particles Produced by Spark Plasma Sintering /$cB. Sadeghi, M. Shamanian, F. Ashrafizadeh, P. Cavaliere, A. Rizzo. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSpark Plasma Sintering (SPS) has been recognized, in the recent past, as a very useful method to produce metal matrix composites with enhanced mechanical and wear properties. Obviously, the material's final properties are strongly related to the reinforcement types and percentages and the particles' distribution, as well as to the processing parameters employed during synthesis. The present article analyzes the effect of microscopic and nanometric alumina particles, blended to pure aluminum in different combinations, on the final properties of metal matrix composites produced via SPS. A strong variation in the microstructural behavior, mechanical, and wear properties has been observed by varying the nano- to micro-alumina particles' percentage and the distribution of the ceramic particles blended with aluminum ones. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aNanocomposites (Materials) =700 1\$aAshrafizadeh, F.,$eauthor. =700 1\$aCavaliere, P.,$eauthor. =700 1\$aRizzo, A.,$eauthor. =700 1\$aShamanian, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180039.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180053 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180053$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180053$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.T5 =082 04$a620.189322$223 =100 1\$aYadav, Ravindra Nath,$eauthor. =245 10$aAn Experimental Study and Parameters Optimization on Duplex Turning of Titanium Alloy /$cRavindra Nath Yadav. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe present article focuses on analyzing the cutting behavior of the duplex turning process for turn-cut machining of aerospace material, especially for titanium alloy. The experiments are conducted on a homemade setup that was mounted on a lathe machine. Each experiment was replicated twice to avoid variability, and a total of 31 experimental data are collected according to the Central Composite Rotating Design matrix. The feed rate, cutting velocity, and depth of cuts (primary and secondary) are taken as control parameters, while the average surface roughness, primary cutting force, and secondary cutting force are taken as response parameters. The experimental data are used to develop an empirical model using Response Surface Methodology (RSM). The developed RSM model has been experimentally tested and used to generate the response surfaces for parametric studies. Finally, the responses are optimized using D-optimality criteria, and the optimal results are experimentally validated. The result shows that RSM models are well fitted with experimental values with percentage errors of 5.03, 4.77, and 4.87 % for the Fp, Fs, and Ra, respectively. Furthermore, the optimal cutting condition shows significant improvement in the responses, i.e., 4.22, 3.72, and 2.85 % for the Fp, Fs, and Ra, respectively. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aTitanium alloys. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180053.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180068 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180068$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180068$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS300 =082 04$a658.969105$223 =100 1\$aLowrie, F.,$eauthor. =245 10$aStrain Rate Sensitivity Effect Measured in 316 Steel by the Small Punch Testing Method /$cF. Lowrie, M. Gorley, E. Surrey, B. Wynne, D. Wilkes. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAn investigation has been carried out to verify if the strain rate sensitivity effect of 316 steel material can be measured using the small punch test method. It was found that the effect was observed during small punch testing over a displacement rate range of 0.0125–1.25 mm/min, with maximum load increasing as the rate increased, and the strain rate sensitivity exponent m was calculated as 0.018. This result highlights the importance of specifying the strain rate conditions when using the small punch test method. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSteel. =700 1\$aGorley, M.,$eauthor. =700 1\$aSurrey, E.,$eauthor. =700 1\$aWilkes, D.,$eauthor. =700 1\$aWynne, B.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180068.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180073 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180073$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180073$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN23 =082 04$a333.76/5/0973$223 =100 1\$aMariswamy, Madhusudhan,$eauthor. =245 10$aProcessing and Characterization of Zirconium Dioxide Dispersion–Strengthened Al7068 Composites /$cMadhusudhan Mariswamy, Mahesha Kumbeshwar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAluminum metal matrix composites are a class of advanced engineering materials that have major applications in aerospace, automobile, and marine engineering domains because of their mechanical properties. The aluminum matrix is dispersion strengthened with hard ceramic particles like zirconia (ZrO2), silicon carbide, alumina, boron carbide, and so forth bringing about better wear protection and enhanced strength-to-weight ratios. In light of the advances in the size and morphology of the reinforcements, it is indeed a sensitive task to process the aluminum composite materials. Among the various processing methodologies, the traditional stir casting technique is an important fabrication methodology for delivering aluminum matrix composites, since it is generally reasonable and offers an extensive variety of material processing conditions. An endeavor has been made to manufacture Aluminum Matrix Composites (AMCs) with the Al7068 alloy as the matrix phase and ZrO2of a generalized particulate size of 25–40 ?m as the reinforcement phase dispersed with varying weight proportions in the range of 0 to 12 wt. % in intervals of 2 wt. % utilizing an indigenously created stir casting process. The homogeneous scattering of ZrO2 particles in the AMCs is distinctly observed from the optical micrographs. Mechanical characterization is effectively done, and the tensile, compression, hardness properties of the composites are taken into account, which gives major evidence that the characteristics of the AMCs improve with the addition of reinforcement particulates attributed to the fact that ZrO2 forms a solid solution with the Al7068 eutectic phases, resulting in improved densification and better toughness and load-bearing capabilities. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aZirconium oxide. =700 1\$aKumbeshwar, Mahesha,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180073.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180078 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180078$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180078$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA472 =082 04$a669.142$223 =100 1\$aSharma, Jagdeep,$eauthor. =245 10$aEffects of Arcor Nitrocarburizing Process on the Case Chemistry and Morphology of AISI 1018 Low-Carbon Steel /$cJagdeep Sharma, Balwinder Singh Sidhu, Rajesh Gupta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIndustrial modern machinery components, such as gears, bolts, and shafts, are always subjected to continuous frictional wear. The wear resistance and cost of material are the two most important factors while selecting a material for such components. The conventional materials are costly, and there is always a quest for inexpensive materials. The designers mostly choose the low-cost, low-carbon steels. AISI 1018 is one such low-cost, low-carbon grade, which has been used extensively in high-volume screw machine parts applications and is commonly employed in spindles, pins, rods, sprocket assemblies, axles, bolts, connecting rods, motor shafts, hydraulic shafts, pump shafts, and machinery parts. However, the wider applications are restrained by their relatively poor wear and surface properties. This necessitates the need for research on these low-carbon, low-cost materials to address the problem. For decades, surface treatments have been performed to enhance the tribological properties of these components. Salt bath nitrocarburizing is one of the oldest methods and an economical method to improve the tribological properties, as well as the mechanical properties of materials. Unfortunately, in the present literatures, there is not much attention paid on treating AISI 1018 low-carbon steel. A nontoxic salt bath surface modification process nitrocarburizing (Arcor) in ferritic state is investigated on AISI 1018 low-carbon steel. It has been observed that with the increase in nitrocarburizing time and nitrocarburizing temperature, a significant enhancement in mechanical properties, like the hardness of the work material, has been found. Field Emission Scanning Electron Microscope (FESEM) investigations identified compound and diffusion regions on the surface of steel along with line scan elemental intensities. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCarbon steel. =700 1\$aGupta, Rajesh,$eauthor. =700 1\$aSidhu, Balwinder Singh,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180078.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180079 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180079$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180079$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP990 =082 04$a668.14$223 =100 1\$aWaddar, Sunil,$eauthor. =245 10$aBuckling and Free Vibration Behavior of Cenosphere/Epoxy Syntactic Foams under Axial Compressive Loading /$cSunil Waddar, Jeyaraj Pitchaimani, Mrityunjay Doddamani, Nikhil Gupta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe buckling and free vibration behavior of cenosphere/epoxy syntactic foams under axial compressive loading are investigated experimentally in this work. The buckling load is obtained from the load-deflection curve based on the Double Tangent Method (DTM) and Modified Budiansky Criteria (MBC). Furthermore, the influence of an axial compression load on the natural frequencies associated with the first three transverse bending modes is analyzed. Finally, the buckling loads predicted using DTM and MBC are compared to the buckling load calculated based on the vibration correlation technique. It is observed that the buckling loads predicted through the three different methods are in close agreement. The experimental results revealed that the buckling load and natural frequency of the syntactic foams increase with the cenosphere volume fraction. It is observed that the natural frequencies reduce with increases in the axial compression load for all the modes. However, a rapid increase in the fundamental frequency is observed when the compressive load is near and beyond the critical buckling load. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSynthetic products. =700 1\$aDoddamani, Mrityunjay,$eauthor. =700 1\$aGupta, Nikhil,$eauthor. =700 1\$aPitchaimani, Jeyaraj,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180079.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180082 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180082$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180082$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C7 =082 04$a620.11299$223 =100 1\$aChakravarthi, K. V. A.,$eauthor. =245 10$aOptimization of Hot Workability and Control of Microstructure in 18Ni (M250 Grade) Maraging Steel Using Processing Maps /$cK. V. A. Chakravarthi, N. T. B. N. Koundinya, Aditya Sarkar, S. V. S. Narayana Murty, B. Nageswara Rao. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article examines the hot working characteristics of M250 grade maraging steel by performing isothermal compression tests varying the temperatures and strain rates. A processing map has been developed, indicating microstructurally “stable” and “unstable” regions during hot working. At strain rates (?, ?,,,,, ) above 0.1 s–1 and temperatures (T) below 1,000°C, stress–strain curves show strain hardening behavior, whereas steady-state behavior is shown at strain rates below 0.01 s–1 and temperatures above 1,050°C. Above 1,150°C, flow softening is observed at 0.001 and 0.01 s–1. In the processing map, two distinct microstructurally stable domains are observed: one is at T = 1,150–1,200°C and ?, ?,,,,, = 0.001–0.01 s–1, and another is at T = 1,000–1,150°C and ?, ?,,,,, = 0.001–0.1 s–1. Based on microstructural observations, electron backscattered diffraction results, and the high efficiency of power dissipation, dynamic recrystallization is the softening mechanism. A constitutive relation useful in computer modeling is developed, using the generated flow stress data. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aMicrostructure. =700 1\$aKoundinya, N. T. B. N.,$eauthor. =700 1\$aNageswara Rao, B.,$eauthor. =700 1\$aNarayana Murty, S. V. S.,$eauthor. =700 1\$aSarkar, Aditya,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180082.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180084 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180084$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180084$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC320 =082 04$a536.2$223 =100 1\$aNayak, U. V.,$eauthor. =245 10$aEffect of Section Thickness on Heat Transfer during Quenching in Vegetable Oils /$cU. V. Nayak, K. N. Prabhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present work, mineral, sunflower, karanja, and neem oil were used as quench media. 304 stainless steel probes with diameters of 25 mm and 50 mm were quenched in these oils to assess the effect of section diameter on heat transfer during quenching. Cooling curve analysis was carried out by instrumenting the probes at various locations with thermocouples. The heat extraction ability of oil quench media was quantified using an inverse heat conduction method. Thermal data and the predicted hardness values showed the suitability of nonedible vegetable oils as potential quenchants to heat treat steels. The predicted hardness was higher during quenching in karanja oil compared to other oil media. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aHeat$xTransmission. =700 1\$aPrabhu, K. N.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180084.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180094 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180094$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180094$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN667 =082 04$a669$223 =100 1\$aPandey, Chandan,$eauthor. =245 10$aGrain Refinement of P91 Steel Using Double Austenitization Treatment /$cChandan Pandey, M. M. Mahapatra, Pradeep Kumar, N. Saini, J. G. Thakre, Prakash Kumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe effect of conventional normalizing and tempering (CNT) and double austenitization–based normalizing and tempering (DNT) heat treatments on the microstructure evolution and mechanical properties of creep strength–enhanced ferritic P91 steel were studied. CNT treatment was performed at 1,050°C and air cooled for 1 h and also at 760°C and air cooled for 2 h. In double austenitization–based normalizing heat treatment, steel was austenitized at 1,050°C and air cooled for 1 h and then normalized in a temperature range of 950°C –1,150°C for 1 h followed by water quenching. After the double normalizing, tempering is performed at 760°C for 2 h. A DNT treatment resulted in homogeneous microstructure formation that led to improved mechanical properties as compared to CNT treatment. The incomplete dissolution of precipitates in single-stage tempering resulted in incomplete martensitic structure formation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSteel$xHeat treatment. =700 1\$aKumar, Pradeep,$eauthor. =700 1\$aKumar, Prakash,$eauthor. =700 1\$aMahapatra, M. M.,$eauthor. =700 1\$aSaini, N.,$eauthor. =700 1\$aThakre, J. G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180094.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180099 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180099$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180099$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aKF26 =082 04$a343.730875669142$223 =100 1\$aKumar, Ravindra,$eauthor. =245 10$aCharacterization of Hot Corrosion Behavior of Different Regions of Tungsten Inert Gas Weldment in ASTM SA 210 GrA1 Boiler Tube Steel /$cRavindra Kumar, V. K. Tewari, Satya Prakash. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHot corrosion is a serious problem in fired tube boiler materials. The deposition of oxalates from the water side does not allow the proper transfer of heat, resulting in overheating. This leads to catastrophic failures of boiler materials. In this study, GrA1 boiler tube steel was selected as a candidate material because it is used in several thermal power plants. Hot corrosion studies were conducted on different regions, i.e., base metal, weld metal, and heat-affected zone (HAZ) of tungsten inert gas (TIG) weldment in GrA1 steel in a molten salt (Na2SO4-60 % V2O5) environment at 900°C under cyclic conditions. The thermogravimetric technique was used to establish the kinetics of corrosion. The corrosion products formed on different regions of TIG welded steel were characterized by scanning electron microscopy with energy-dispersive X-ray analysis and X-ray diffraction pattern. Base metal was found to oxidize at much higher rates than those of weld metal and HAZ. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aTubes, Steel. =700 1\$aPrakash, Satya,$eauthor. =700 1\$aTewari, V. K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180099.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180119 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180119$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180119$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a669.142$223 =100 1\$aMann, B. S.,$eauthor. =245 10$aEnergy-Based Water Droplet Impact Erosion Studies of Laser-Treated Austenitic and Martensitic Steels and their Applications /$cB. S. Mann. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHigh-power diode laser (HPDL) surface treatments of high-manganese austenitic and high-chromium martensitic steel round specimens have been carried out, and their resistance to water droplet impact erosion (WDIE) in air was evaluated as per ASTM G73-10, Standard Test Method for Liquid Impingement Erosion Using Rotating Apparatus. This is because the water droplets always travel along with a fluid medium, either steam or air, and these are influenced by inertial, Coriolis, and centrifugal forces, which are missing in a vacuum. Because of these forces, the water droplets elongate and may break before hitting a target, resulting in WDIE damages entirely different from those in a vacuum. The WDIE damages on the test specimens were observed on the leading edge towards the suction side, where the boundary layer is attached, and the pressure gradients are high. These are similar to those occurring on the blades of an axial flow compressor of a gas turbine, a low-pressure steam turbine, and a helicopter rotor, because their leading edges are round. The WDIE testing is based on water droplet kinetic energy (KEd) and kinetic energy flux (KEfd). It has been proved experimentally that the product of KEd and KEfd can predict WDIE damages in a material, and this product can be used to compare the WDIE test results of different materials received from different laboratories. It is observed from the test results that the resistance to WDIE of HPDL-treated high-manganese austenitic steel (Hadfield's steel) has reduced drastically, whereas that of high-chromium martensitic stainless steel has improved manifold. Fine microstructure and increased martensitic contents in high-chromium martensitic stainless steel after HPDL treatment are the main reasons for its improved performance, whereas the coarse microstructure having microcracks in HPDL-treated Hadfield's steel is responsible for poor performance. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aAustenitic steel. =650 \0$aStainless steel. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180119.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170151 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170151$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170151$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC191 =082 04$a6531.38$223 =100 1\$aWells, Douglas N.,$eauthor. =245 10$aA Review of the Proposed KIsi Offset-Secant Method for Size-Insensitive Linear-Elastic Fracture Toughness Evaluation /$cDouglas N. Wells, Mark A. James, Phillip A. Allen, Kim R. W. Wallin. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aRecently proposed modifications to ASTM E399, Standard Test Method for Linear-Elastic Plane-Strain Fracture Toughness KIc of Metallic Materials, would provide a new size-insensitive approach to analyzing the force-displacement test record. The proposed size-insensitive linear-elastic fracture toughness, KIsi, targets a consistent 0.5-mm crack extension for all specimen sizes by using an offset secant that is a function of the specimen ligament length. With intent to increase flexibility in the test method, the KIsi evaluation method removes the Pmax/PQ criterion, which can penalize materials with rising tearing resistance curves, and increases the limits on specimen deformation, which allows more plasticity at the crack tip at the onset of crack extension. The primary motivation for this investigation is to confirm the validity of this new interpretation of the force-displacement test record in regard to the increase in acceptable specimen deformation. This article summarizes a finite element study of the effects of increased crack tip plasticity on the KIsi evaluation method, with two primary points of investigation: the continued validity of linear-elastic fracture mechanics (LEFM) to describe the crack front conditions and the effect of crack tip plasticity on compliance change in the force-displacement record. The analytical study illustrates that LEFM assumptions remain valid at the increased deformation limit; however, the influence of plasticity on the compliance change in the test record is problematic. A proposed revision to the validity criteria for the KIsi test method is described. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aElastic solids$xTesting. =700 1\$aAllen, Phillip A.,$eauthor. =700 1\$aJames, Mark A.,$eauthor. =700 1\$aWallin, Kim R. W.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170151.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170128 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170128$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170128$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA460 =082 04$a620.11223$223 =100 1\$aLucon, E.,$eauthor. =245 10$aASTM E08.07.09 Analytical Round-Robin on the Use of DC Electrical Potential Difference for the Measurement of Crack Size in Ductile Fracture Testing /$cE. Lucon. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe Direct Current Electrical Potential Difference (DCEPD) technique has been used for many years in fatigue and fracture testing for monitoring crack propagation in metallic materials. The principle of DCEPD methods is that when a constant current flows through a cracked specimen, the voltage change measured across the crack plane can be analytically related, empirically related, or both, to the change in crack size. In fatigue testing, performed within the limits of Linear Elastic Fracture Mechanics, crack propagation is the sole source of potential change. In ductile fracture testing, additional contributions from specimen dimension changes and crack-tip plastic deformation (blunting) have to be accounted for and distinguished from the DCEPD increase caused by crack growth. The ASTM E08.07.09 Task Group, formed in 2013 and chaired by the author, has been developing an annex for ASTM E1820, Standard Test Method for Measurement of Fracture Toughness, which focuses on the use of DCEPD measurements for the prediction of crack size and crack extension in ductile fracture toughness tests. This article presents the analysis of an analytical round-robin, in which 8 participants analyzed 24 existing fracture toughness data sets using two different approaches, based on the analysis of the displacement versus DCEPD and force versus DCEPD, respectively. The comparison between these two approaches and the implications for the ASTM E1820 annex being developed are the focus of this article. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aMetals$xFracture$xTesting. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170128.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170118 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170118$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170118$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$a TA409 =082 04$a620.1/126$223 =100 1\$aBrazill, Richard L.,$eauthor. =245 10$aBias in Linear Regression Analysis of Compliance Measurements in Fatigue Crack Growth and Fracture Toughness Tests /$cRichard L. Brazill, J. Keith Donald. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aWhen compliance methods are used to determine specimen crack size in fracture mechanics testing, accurate and unbiased determination of the slope of the linear region of the force versus the crack opening displacement (COD) curve is required. Often, the region of interest is isolated by truncation of data that lie outside either force or COD limits. Two decisions are required: which parameter to use for the truncation and which to use as the independent variable in the linear regression analysis. This article will demonstrate that the incorrect choice of independent variable for truncated data sets can lead to a systematic bias in the determination of the linear regression slope and intercept. It will be shown with Monte Carlo simulations that the independent variable for linear regression should always be the same as the truncation variable, and in this case the variation in slope will be random, with a zero mean. The magnitude of the slope bias is related to the relative noise in each variable. Not only will this lead to a bias in determining crack size, but large errors can occur when determining nonlinearity associated with crack-opening force and in the crack-compliance method for determining the crack driving force due to residual stress, Kres. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aFracture mechanics. =700 1\$aDonald, J. Keith,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170118.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170094 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170094$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170094$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA460 =082 04$a620.1/66$223 =100 1\$aDonald, J. Keith,$eauthor. =245 10$aCrack Size and Shape Considerations Related to Near-Threshold Fatigue Crack Growth Rate Behavior /$cJ. Keith Donald, Mark A. James, Richard G. Pettit. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIt is well recognized that crack size or load history or both have an important influence on near-threshold fatigue crack rate behavior at a low stress ratio. This investigation will compare the behavior of a radial crack, such as a surface flaw or a corner crack, to that of a linear crack to see if crack shape plays a role in physically small crack to long crack behavior. Recent research has unveiled a methodology to experimentally partition plasticity from roughness- and oxide-induced crack closure, showing that nonplasticity-induced closure mechanisms have a greater influence at low Kmax by orders of magnitude. Knowledge of this is key to understanding differences between long crack and physically small crack behavior in the near-threshold regime. In this study, the well behaved 2024-T351 aluminum alloy was used to generate threshold data using numerous specimen geometries, flaw geometries, crack sizes, and test procedures to highlight not only the significance of crack size but also the role of crack shape. It will be shown both experimentally and analytically that a radial crack (surface flaw, corner crack) has significantly less remote closure and, therefore, a lower threshold than a through crack (compact tension, middle crack tension), even if the crack size is the same. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aMetals$xCracking. =650 \0$aMetals$xFatigue. =700 1\$aJames, Mark A.,$eauthor. =700 1\$aPettit, Richard G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170094.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170086 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170086$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170086$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA462 =082 04$a620.166$223 =100 1\$aBombardier, Yan,$eauthor. =245 10$aDevelopment of an Optimization Tool for Calibrating Crack Growth Material Models /$cYan Bombardier. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCrack growth models are typically calibrated using experimental data prior to conducting damage tolerance analyses of aircraft structures. This process can be trivial for crack growth models that only have a few fitting parameters. However, other models, such as the FASTRAN crack growth equation with the analytical crack-closure model, include several model parameters that make calibration challenging. To simplify the calibration process and improve the accuracy of crack growth simulations, an automated crack growth model optimization tool was developed. This tool also aims at improving the robustness of crack growth models by reducing their dependency on loading spectra and specimen geometries. To achieve this, numerical optimization is used to minimize the discrepancy between experimental data and analytical crack growth. To demonstrate this approach, material model parameters were calibrated for P-3/CP-140 aircraft applications using the FASTRAN crack growth equation with the analytical crack-closure model. The optimization tool was found to be very effective at fitting crack growth simulation results to experimental data by changing the values of selected parameters. It was, however, observed that the automated calibration process could find multiple sets of FASTRAN parameter values that provide equivalent correlations with experimental data. In an attempt to develop a more robust material model, multiple test configurations with different geometries and loading spectra were used to determine an optimal trade-off model that maximizes the correlation for multiple test configurations. The conducted tests demonstrated that this approach is viable and could be used to improve the robustness of crack growth simulations. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aMetals$xCracking. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170086.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170152 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170152$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170152$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.T54 =082 04$a669.96142$223 =100 1\$aBarbosa, Vitor Scarabeli,$eauthor. =245 10$aExperimental Measurements of Jc-Values for a Low Alloy Structural Steel Using Nonstandard Bend Specimens and Evaluation of the Reference Temperature, T0 /$cVitor Scarabeli Barbosa, Claudio Ruggieri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (26 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis work experimentally investigates the cleavage fracture behavior of a high strength, low alloy structural steel using standard and nonstandard single-edge notched bend specimens, including nonstandard precracked Charpy-type configurations tested under three-point bending. The primary purpose of this study is to investigate the effects of geometry and loading mode on fracture toughness using nonstandard bend specimens under three-point and four-point loading. Fracture toughness testing conducted on various bend specimen geometries extracted from an ASTM A572, Standard Specification for High-Strength Low Alloy Columbium-Vanadium Structural Steel, Grade 50 steel plate provides the cleavage fracture resistance data in terms of the J-integral at cleavage instability, Jc. The experimental results show potential effects of specimen geometry and loading mode on Jc-values that can help to mitigate the effects of constraint loss often observed in smaller fracture specimens. An exploratory application derived from the master curve methodology to determine the reference temperature, T0, also provides additional support for using nonstandard bend specimens in routine fracture applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSteel, Structural. =700 1\$aRuggieri, Claudio,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170152.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170073 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170073$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170073$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.4 =082 04$a620.165$223 =100 1\$aHuang, Chuanshi,$eauthor. =245 10$aModeling the Effect of Hydrogen on Ductile Fracture /$cChuanshi Huang, Tuo Luo, Xiaosheng Gao, Stephen M. Graham. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHydrogen-enhanced localized plasticity (HELP) is a major cause of material ductility reduction. In this study, the effect of hydrogen on ductile fracture is demonstrated by its influence on the process of void growth and coalescence. Assuming an initially uniform hydrogen distribution and a periodic array of spherical voids present in the material, a series of finite element analyses of a representative material volume subjected to various stress states was carried out. The evolution of local stress and deformation states results in hydrogen redistribution in the material, which in turn changes the material's flow property because of the HELP effect. The results show that hydrogen reduces the ductility of the material by accelerating void growth and coalescence, and the effect of hydrogen on ductile fracture is strongly influenced by the stress state experienced by the material, as characterized by the stress triaxiality and the Lode parameter. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aMaterials$xDuctility. =700 1\$aGao, Xiaosheng,$eauthor. =700 1\$aGraham, Stephen M.,$eauthor. =700 1\$aLuo, Tuo,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170073.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170144 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170144$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170144$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC242.2 =082 04$a620.25$223 =100 1\$aAllen, Phillip A.,$eauthor. =245 10$aPhase II Results of an Analytical Round Robin for Elastic-Plastic Analysis of Surface Cracked Plates /$cPhillip A. Allen, Douglas N. Wells. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe second phase of an analytical round robin for the elastic-plastic analysis of surface cracks in flat plates was conducted under the auspices of ASTM Interlaboratory Study 732. The interlaboratory study (ILS) had ten participants with a broad range of expertise and experience, and experimental results from a surface crack tension test in 4142 steel plate loaded well into the elastic-plastic regime provided the basis for the study. The participants were asked to evaluate a surface crack tension test according to the version of the surface crack initiation toughness testing standard published at the time of the ILS, ASTM E2899, -13, Standard Test Method for Measurement of Initiation Toughness in Surface Cracks under Tension and Bending. Data were provided to each participant that represented the fundamental information that would be provided by a mechanical test laboratory prior to evaluating the test result. Participants were asked to interpret the test according to E2899, including evaluation of crack-front constraint, determination of a critical initiation angle along the crack front, determination of the deformation regime of the test, and determination of the critical J-integral value. The choice of finite element analysis constitutive models and treatment of the stress-strain data was left to the discretion of the participants. The hope was that this process would familiarize participants with the standard and provide the task group with very helpful feedback regarding the interpretation of the requirements as they are written. Overall the participants' test analysis results were in good agreement and constructive feedback was received that has resulted in an improved published version of the standard E2899-15. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aElastic analysis (Engineering) =700 1\$aWells, Douglas N.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170144.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170079 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170079$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170079$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.38 =082 04$a620.1123$223 =100 1\$aRao, Harish M.,$eauthor. =245 10$aStudy on the Role of Casting Defects and Surface Finish on Fatigue Life in Die-cast AM60B Magnesium Alloy Using X-Ray Computed Tomography /$cHarish M. Rao, Jidong Kang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMagnesium alloy has attracted considerable attention from the automotive industry because of its low density and high specific strength combined with excellent casting capabilities. However, the role of casting defects and surface finish on the fatigue life emerges as a major concern. To study the role of surface finish, the die-cast skin was removed from the selected test specimens by hand polishing. No major difference in surface roughness was observed between the die-cast and polished surface. To characterize the casting defects in each test specimen, prior to the fatigue test, X-ray computed tomography (XCT) scans were performed on a desktop micro-XCT scanner. The preliminary XCT scans revealed a large number of gas and shrinkage pores concentrated in the center sections of the test specimens and a few scattered close to the free surface. In addition to gas and shrinkage pores, in unpolished specimens, small microcracks and notch-like surface imperfections were also observed on the edge of the test specimens. Strain controlled fatigue tests were performed on polished and unpolished test specimens at a 0.3 % strain amplitude. After every 2,000 fatigue cycles, the test was interrupted and XCT was performed to study the crack initiation and propagation in the respective test specimens. The fatigue test exhibited no major difference in fatigue life between the unpolished and polished specimens. However, XCT scans revealed the dominant fatigue crack initiated from the surface imperfections in unpolished specimens and from casting pores closer to the free surface in polished specimens. The fatigue test results and spatial distribution of casting pores were compared with the specimens extracted from a die-cast shock-tower structure from a previous study. Although a difference in spatial distribution of the casting pores was observed, it had no major impact on the fatigue life between the two sets of specimens. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aFatigue--Testing. =700 1\$aKang, Jidong,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170079.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170127 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170127$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170127$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.1/86$223 =100 1\$aLeitner, Martin,$eauthor. =245 10$aSurface Topography Effects on the Fatigue Strength of Cast Aluminum Alloy AlSi8Cu3 /$cMartin Leitner, Michael Stoschka, Jürgen Fröschl, Jens Wiebesiek. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article investigates the effect of the cast surface topography on the fatigue strength of the cast aluminum alloy AlSi8Cu3, which is equivalent to EN AC-46200 and A380 according to ASTM. Fatigue tests utilizing small-scale specimens under bending at a load stress ratio of R = 0 reveal a significant influence of the cast surface layer, leading to a reduction of the nominal fatigue strength at ten million load cycles by about one half. Fracture surface analysis highlights that crack initiation occurs because of both surface roughness and micropores within the cast surface layer. A numerical simulation procedure to assess the influence of the surface roughness on the fatigue strength is presented. Thereby, a three-dimensional mesh of an optically scanned surface topography is set up and a local fatigue strength reduction factor is numerically computed based on the critical distance approach by Taylor. The results reveal that the presented method slightly overestimates the fatigue strength compared to the experiments; however, the determined values lead to a sound accordance if the scatter of the fatigue test data points is considered. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aAluminum alloys. =700 1\$aFröschl, Jürgen,$eauthor. =700 1\$aStoschka, Michael,$eauthor. =700 1\$aWiebesiek, Jens,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170127.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170115 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170115$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170115$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.T54 =082 04$a671.32$223 =100 1\$aNguyen, Kien,$eauthor. =245 10$aThermomechanical Modeling of Welding and Galvanizing a Steel Beam Connection Detail to Examine Susceptibility to Cracking /$cKien Nguyen, Reza Nasouri, Caroline R. Bennett, Adolfo Matamoros, Jian Li, Arturo H. Montoya. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (26 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHot-dip galvanizing is the process of submerging steel elements into molten zinc to form a metallurgically bonded zinc coating that serves as corrosion protection for the steel substrate. Used with great success on an industrial scale for many decades, hot-dip galvanizing is a ubiquitous process. On occasion, cracks in steel members develop during galvanizing. While such cracking remains a poorly understood phenomenon, previous research has attributed the formation of cracks to the combined effects of residual strains introduced by welding and temperature-induced deformations caused by the hot-dip galvanizing process. This article presents thermomechanical analyses of a structural steel beam with a welded double-angle connection detail where cracking occurred during hot-dip galvanizing. Three-dimensional finite element models of the beam and connection detail were analyzed using the finite element analysis software Abaqus (Dassault Systèmes, Vélizy-Villacoublay, France). The welding process was simulated using the Abaqus Welding Interface, maintaining the welding sequence of the connection. After welding, the entire beam was subjected to a temperature field that was specified through a user subroutine in Abaqus, simulating the hot-dip galvanizing process. The temperature field had a bath temperature of 450°C and a thermal cycle that included dipping, dwell time, and removal from the bath. Material properties used in the simulation were nonlinear and temperature dependent. The parameters of the study were the welding sequences, heat input during welding, and the depth of the double-angle connection. It was observed that strain demands due to welding and hot-dip galvanizing were high magnitude at the cracked location in the beam. The relative significance of strain demands due to welding and of hot-dip galvanizing on the propensity for the beam to develop cracks are discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSteel$xThermomechanical treatment. =700 1\$aBennett, Caroline R.,$eauthor. =700 1\$aLi, Jian,$eauthor. =700 1\$aMatamoros, Adolfo,$eauthor. =700 1\$aMontoya, Arturo H.,$eauthor. =700 1\$aNasouri, Reza,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 2 Special Issue on Advances in Fatigue and Fracture Mechanics.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170115.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170067 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170067$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170067$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ1077 =082 04$a621.43$223 =100 1\$aPape, Florian,$eauthor. =245 10$aZDDP Containing Tribofilms Generated under Sliding Micro Contact and Bearing Test Rig Conditions /$cFlorian Pape, Christian Muhmann, David Pahl, Dieter Lipinsky, Heinrich F. Arlinghaus, Gerhard Poll. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aFor machine elements in relative motion (like bearings), lubrication is mandatory to prevent wear or premature fatigue and to reduce friction. Oils and greases typically contain additives to protect against wear and oxidation by building up a tribofilm with a thickness of a few ten nanometers. There is the suspicion that under some critical compositions and under specific test conditions, the resulting tribofilm can cause early bearing failure because of subsurface damages like white etching cracks (WECs). One component relevant for tribofilm formation is zinc dialkyldithiophosphate (ZDDP), which forms protective phosphate glass-based tribofilms. With the aim of detecting critical lubricant compositions and test parameters, experiments on an FE8 test rig were performed. To investigate the formation of tribofilms, tests were also executed using a modified Center for Tribology (CETR, now Bruker Corporation, Billerica, MA) Olympus HDI reliability spin-stand. This device was originally developed to investigate the head-to-disk interface of a hard disk drive (HDD). During the test cycles, the coefficient of friction was recorded. In order to determine the effect of the operation conditions, the microtribological properties of the boundary layers were analyzed. The boundary layers were investigated by means of nanoindentations and nanoscratches on the raceways. Additionally, time-of-flight-secondary ion mass spectrometry (ToF-SIMS) with depth profiling was used to analyze the adhering lubricant, as well as the composition of the boundary layers. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aLubricating oils. =700 1\$aArlinghaus, Heinrich F.,$eauthor. =700 1\$aLipinsky, Dieter,$eauthor. =700 1\$aMuhmann, Christian,$eauthor. =700 1\$aPahl, David,$eauthor. =700 1\$aPol, Gerhard,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170067.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170078 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170078$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170078$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ1075 =082 04$a621.89$223 =100 1\$aWoydt, Mathias,$eauthor. =245 10$aGeneration of Defined Tribofilms and Their Stability under Slip-Rolling in a 2Disk Test Rig /$cMathias Woydt, John-Theodore Burbank, Dirk Spaltmann. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTribofilms formed by additives in lubricants represent a key mechanism for preventing wear but are difficult to investigate because of the complexity of the composition of lubricants, their small thickness, and their amorphous nature. The tribological profile of such tribofilms can be established based on a new test methodology described here. For a large range of additives, the corresponding chemically reactive tribofilms were generated in 2Disk test rigs on widely used reference steels, such as 100Cr6 (SAE52100), Cronidur 30 (AMS 5898), or 20MnCr5 Quenched & Tempered (Q&T) (SAE4820/SAE5120), during slip-rolling in the mixed/boundary lubrication regime at 120°C. The performance of the created tribofilms is compared to those created on alternative steels, such as 36NiCrMoV1-5-7, 45SiCrMo6, or even Diamond-Like Coating (DLC)-coated steels, using the same additives. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aLubrication and lubricants. =700 1\$aBurbank, John-Theodore,$eauthor. =700 1\$aSpaltmann, Dirk,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170078.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170064 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170064$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170064$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.18922$223 =100 1\$aAlves, Salete Martins,$eauthor. =245 10$aNanolubrication Mechanisms: Influence of Size and Concentration of CuO Nanoparticles /$cSalete Martins Alves, Valdicleide Silva e Mello, Amilton Sinatora. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn nanolubrication, friction-reduction and anti-wear behaviors are dependent on the characteristics of nanoparticles, such as size, shape, and concentration. Some mechanisms of friction-reduction and anti-wear of NNP in lubricant have been reported as protective film, rolling effect, polishing or smoothing effect, mending effect, and the third body. Thus, this work studied differences in nanolubrication mechanism as functions of size and concentration of CuO NNP added in synthetic oil. Three levels of concentration and size were evaluated: 0.1, 0.25, and 0.5 % wt., and 2.5, 4.4, and 8.7 nm, respectively. The methodology was divided into three steps: first, the preparation of CuO NNP from an alcohol-thermal method. These were characterized by XRD (X-ray diffraction) and TEM (Transmission electron microscopy). The second part was constituted by evaluation of lubricant with NNP by a tribological test, which was carried out under boundary lubrication conditions in high frequency reciprocating rig (HFRR) equipment. The last step was the characterization of the wear mechanism; scanning electron microscopy (SEM) and Raman spectroscopy aided to identify tribochemistry interactions between nanolubricant and steel surface. The results showed that the concentration of NNP influenced wear: low concentration decreased the wear and promoted a smooth surface, while more plastic deformation was observed in high concentration. For the NNP size, the smallest size corresponded to the lowest friction coefficient. The best results were obtained for nanolubricant with a concentration of 0.1 % wt. and a NNP size of 2.5 nm. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aNanoparticles. =700 1\$aMello, aldicleide Silva e,$eauthor. =700 1\$aSinatora, Amilton,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170064.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170061 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170061$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170061$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ1075 =082 04$a621.89$223 =100 1\$aKornienko, E. E.,$eauthor. =245 10$aResearch of Structure and Properties of NiCrSiB Sintered Materials Additionally Alloyed with Nb /$cE. E. Kornienko, A. S. Ivashutenko, A. S. Saigash, E. A. Drobyaz, M. K. Tutunkova. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSelf-fluxing nickel-base alloys containing chromium, silicon, boron, and carbon (NiCrSiB) are widely used in industry because of their unique properties. In this study, various amounts of niobium (Nb) powder (2, 4, 6, and 8 wt. %) were added to the self-fluxing powder of an NiCrSiB system in order to obtain more wear-resistant and dense material by using the technology of spark plasma sintering (SPS). SPS of the powder blends was carried out by the SPS 10-4 apparatus (Advanced Technologies, Newport News, VA). The structure and phase composition of the sintered materials were investigated by optical microscopy, scanning electron microscopy, and X-ray diffractometry. This study gives details of porosity and microhardness measurements as well as tribological tests under the friction on the fixed abrasive particles' conditions. This study demonstrates that phases (the central region of which is niobium carbide) are formed at the interfaces and in the junctions between the self-fluxing powder particles. The addition of Nb contributes to the decrease of porosity and the increase of wear resistance. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aTribology. =700 1\$aDrobyaz, E. A.,$eauthor. =700 1\$aIvashutenko, A. S.,$eauthor. =700 1\$aSaigash, A. S.,$eauthor. =700 1\$aTutunkova, M. K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170061.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170074 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170074$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170074$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS325 =082 04$a672/.3/6$223 =100 1\$aMishigdorzhiyn, Undrakh,$eauthor. =245 10$aThe Influence of Boroaluminizing Temperature on Microstructure and Wear Resistance in Low-Carbon Steels /$cUndrakh Mishigdorzhiyn, Igor Sizov. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article investigates the possibility of improving the wear resistance of carbon steel 30 by means of boroaluminizing in treatment pastes. Boroaluminizing was conducted in sodium fluoride (as an activator), boron carbide, and aluminum at furnace heating (the latter two components were taken in a ratio of 4 to 1). The treatment was administered for 4 hours in four temperature modes between 950°C and 1,100°C with a 50°C difference between modes. The microstructure, microhardness, and elemental and phase compositions of the boroaluminized layers were investigated. In addition, the wear resistance of the boroaluminized steels was tested. It was established that treatment temperatures of 1,000°C and lower lead to the formation of layered structures consisting of iron aluminides that are mainly located on top of the diffusion layer and iron borides adjacent to the base metal. Moreover, the use of boroaluminizing temperatures over 1,000°C results in the formation of a heterogeneous structure with iron borides FeB and Fe2B evenly distributed in the matrix of aluminum solid solution in iron. This contributes significantly to the mechanical properties of the layer; in particular, it enhances its wear resistance. It was established that the wear resistance of steel 30 significantly improves after treatment at 1,100°C in comparison with temperature modes of 950°C and 1,000°C. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCarbon steel$xHeat treatment. =700 1\$aSizov, Igor,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170074.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170084 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170084$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170084$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK2901 =082 04$a621.31242$223 =100 1\$aMa, Lian,$eauthor. =245 10$aElectrochemical Characterization of a Nickel-Phosphorus Coating on Diamond Grits /$cLian Ma, Xihua He, Alex Fang, Hong Liang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMachining tools electroplated with coated diamond abrasives are widely used because of their high wear resistance. However, the inconsistent quality caused by coating failure has hindered tools' performances and service lives. In the present work, experimental investigation through electrochemical approach was conducted on a coating electrolessly plated on diamond grits. A newly designed working electrode with nickel-phosphorus alloy coating was fabricated. Subsequently, immersion test, potentiodynamic polarization, and linear polarization resistance (LPR) and open circuit potential (OCP) monitoring were performed on this electrode, in order to reveal insight from the failure mechanisms of coatings. Morphological characterization was carried out before and after both the potentiodynamic polarization experiments and immersion test. The results showed that, in a low-concentration (60 g/L nickel sulfamate) bath, the coating cracked and stripped off because of the current assisted breakthrough of pinholes, while the coating has less damage in the high-concentration (300 g/L nickel sulfamate) bath because of an extra passivation stage at lower potential (–0.30 V versus OCP). The increase in OCP and decrease in corrosion rate over time indicated the continuous coating cracking and exposure of the nobler diamond substrate. LPR and OCP monitoring is an effective approach to evaluate the coating durability before the coated diamond grits are actually used in wire saw manufacturing. The electrochemical characterization methods used in this work can be applied to other core-shell systems with metal coatings and particulate substrates. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aElectrochemistry. =700 1\$aFang, Alex,$eauthor. =700 1\$aHe, Xihua,$eauthor. =700 1\$aLiang, Hong,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170084.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170085 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170085$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170085$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.17$223 =100 1\$aNirmal, Umar,$eauthor. =245 10$aSurface Roughness Analysis of Stainless Steel Counterface (AISI-304) Subjected to Treated Betelnut Fiber–Reinforced Polyester (T-BFRP) Composites Aged in Different Solutions with Different Kinematic Viscosity /$cUmar Nirmal, Jamil Hashim, M. M. H. Megat Ahmad, M. Y. Yuhazri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (39 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe current research aims to study the surface roughness (Ra) analysis of stainless steel counterface type AISI-304 subjected to Treated Betelnut Fiber–Reinforced Polyester (T-BFRP) composites that are aged for a period of 3 years in different solutions with different kinematic viscosity. The test was conducted with a pin-on-disk wear test rig, which was designed and fabricated in-house according to ASTM G99-05, Standard Test Method for Wear Testing with a Pin-on-Disk Apparatus (Superseded). Different sliding distances (0–3.36 km) at a fixed applied normal load of 30 N subjected to a smooth stainless steel (60 HB) counterface at a sliding velocity of 2.83 m/s were used as the experimental parameters. Different orientations (O) of the betelnut fiber mats with respect to the sliding direction of the counterface were investigated, i.e., antiparallel (AP) and parallel (P) directions. The worn surface morphology was studied using a metallurgical microscope. Results revealed that the aged T-BFRP composite in a R134a solution demonstrated the lowest Ra values after the sliding wear test and after the counterface was cleaned. This result is due to the lowest absorption rate (i.e., highest kinematic viscosity) incurred by the aged AP and P test specimens as compared to the other types of aging solutions. As such, the improvement in Ra values of the samples aged in R134a solution were 87.8 and 99.9 % for the aged AP and P test samples, respectively, as compared to the aged neat polyester (NP) samples. It was also noted that the fibers had low absorption rates when they were aged in solutions with high kinematic viscosity; in other words, the aged T-BFRP composite demonstrated the lowest absorption rate (?0.0085 %) when it was aged in the R134a solution. Aged NP did not show any remarkable absorption into the test samples mainly because of the absence of fibers. All in all, this work reveals a possible method that can be used to lower the damage on abrasiveness to processing equipment by means of aging the composite in various solutions with different kinematic viscosities. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aStainless steel. =700 1\$aAhmad, M. M. H. Megat,$eauthor. =700 1\$aHashim, Jamil,$eauthor. =700 1\$aYuhazri, M. Y.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170085.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170035 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170035$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170035$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS250 =082 04$a671.8/23$223 =100 1\$aSivarajan, S.,$eauthor. =245 10$aImprovement of Tribology in Sheet Metal Forming of High-Strength Steel Sheets by PVD-Coated Dies /$cS. Sivarajan, R. Padmanabhan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDuring sheet metal formation, the high strength of sheet material leads to high contact stress between the die and blank material, which results in increased die wear. Moreover, the reduction in the use of lubricants because of environmental concerns has led to greater wear of sheet metal–forming dies. It is important to understand the tribological behavior of the blank die contact so that steps can be taken to reduce the die wear to an acceptable level. Die wear reduction is possible by using alternative die materials, modifying die geometry, or by creating a wear-resistant surface on sheet metal–forming dies using Physical Vapor Deposition (PVD) coatings. PVD coatings have a thickness in the micro range and greatly improve the tribological properties of the die material. In this work, three pins made of AISI D2 steel were coated with Titanium Nitride, Titanium Aluminum Nitride (TiAlN), and Aluminum Chromium Nitride using the PVD process. Friction and wear tests were conducted on the pin-on-disk testing machine as per ASTM G99, Standard Test Method for Wear Testing with a Pin-on-Disk Apparatus. The pins had diameters measuring 10 mm and lengths measuring 35 mm. They were heat treated until they reached 55 HRC and ground to a Ra value of 0.1 µm. A 5-mm-radius tip was provided on one end of the pin. D3 steel was used as counter material (disk). The normal load was 30 N, and the sliding speed was 0.3 m/s. The experiments were conducted in dry contact conditions. Based on the results, it was concluded that TiAlN coatings are an excellent choice to modify friction behavior and improve wear resistance of die material. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSheet-metal work. =650 \0$aTECHNOLOGY & ENGINEERING$xTechnical & Manufacturing Industries & Trades. =700 1\$aPadmanabhan, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170035.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170065 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170065$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170065$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.F7 =082 04$a621.89$223 =100 1\$aBataev, A. A.,$eauthor. =245 10$aA Novel Device for Quasi In Situ Studies of Materials Microstructure during Friction /$cA. A. Bataev, V. G. Burov, A. A. Nikulina, I. A. Bataev, D. V. Lazurenko, A. I. Popelukh, D. A. Ivanov. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe friction of metallic materials leads to the evolution of the microstructure of surface layers. The structural evolution is a way of the surface adaptation to mechanical stresses that occur as the conditions of the local temperature increase and physical and chemical interact with the material of the counterbody and the environment. Only a few methods have been developed to dynamically observe the structural changes in the friction process. Microbeam synchrotron X-ray diffraction is one of them. It allows monitoring of the peak profile changes with a high time resolution, depending on pressure, velocity, material of indenter, type of lubrication, and other parameters. This article describes the friction testers that are designed to study the structure of the surface layers, the temperature in the friction zone, and the friction coefficient using synchrotron radiation in situ (directly at the friction zone) or quasi in situ (i.e., at some distance from the friction zone). The in situ measurements obtain the most complete information about the structural evolution directly in the process of friction. However, this type of research may be difficult when metals and alloys are used as the indenters as they strongly scatter the X-rays. The quasi in situ scheme developed by our group has no restrictions regarding the material of the indenter. However, the structural changes are recorded with a delay of 100–300 ms. The results of preliminary experiments using the newly developed apparatus are described herein. The peak broadening and decrease in intensity of the peaks due to refinement and straining of the lattice was observed in steel, titanium alloy, and copper specimens. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aFriction materials. =650 \0$aTECHNOLOGY & ENGINEERING$xMetallurgy. =700 1\$aBataev, I. A.,$eauthor. =700 1\$aBurov, V. G.,$eauthor. =700 1\$aIvanov, D. A.,$eauthor. =700 1\$aLazurenko, D. V.,$eauthor. =700 1\$aNikulina, A. A.,$eauthor. =700 1\$aPopelukh, A. I.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170065.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170107 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170107$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170107$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ1075 =082 04$a665.5385$223 =100 1\$aPatzer, Gregor,$eauthor. =245 10$aEvaluation of High Performance Lubricating Greases on the Translatory Oscillation Tribometer (SRV®) /$cGregor Patzer. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe diversity of lubricating grease species, each with their own complexity and philosophy, raises the demand for the diversification of existing screening methods even in model testing. This article presents an overview of existing standard methods as well as application-oriented testing procedures, which can be used for evaluating friction, wear, and extreme pressure properties of lubricating greases in a model tribometer. For lubricant developers, the SRV® technology platform offers not only testing according to the established test methods and relevant standards, but also the possibility of testing new products in application-oriented load situations. The testing according to standards can be used as a screening test for the grease chemistry and the flow properties of the grease sample. However, it reflects the potential real-life operating conditions of a product in only a very limited way. This article will present test scenarios for such application-oriented friction and wear tests through a few selected examples: Effect of wear particles on the lubricity of a lubricating grease,, High temperature fretting behavior of industrial greases,, Simplified examination of rolling/sliding friction of high performance greases. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aLubricating oils. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170107.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170063 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170063$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170063$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTC160 =082 04$a627$223 =100 1\$aKazama, Toshiharu,$eauthor. =245 10$aExperimental Study of Jet Cavitation Erosion Applicable to Oil and Water-Hydraulic Equipment /$cToshiharu Kazama. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHydraulic components, such as valves, pumps, and actuators, include many narrow passages in the form of nozzles, orifices, and gaps. Cavitation can occur when jets flow from high to low pressure through such sections, making it unavoidable for jets containing cavitation bubbles to impinge on the inner walls of hydraulic components. This report summarizes a series of experiments involving erosion tests, flow visualization, and pressure measurements with hydraulic oils and municipal water. For the erosion tests, the ASTM G134, Standard Test Method for Erosion of Solid Materials by a Cavitating Liquid Jet, method of jet cavitation erosion is used to evaluate the eroded mass loss and the specimen's surface damage. The experimental apparatus consists of a stainless steel cylindrical chamber, a high-pressure hydraulic pump, and auxiliary hydraulic components. The main test parameters are the standoff distance, cavitation number, nozzle outlet geometry, specimen surface shape, and liquid type. The specimen mass is measured, and the eroded surfaces are recorded at specific intervals. For the visualization tests, an acrylic chamber and a digital video camera are used. Video frames are extracted as pictures and are processed by superposition. For the pressure measurements, pressure-sensitive films are used to estimate the pressure distributions on the impinged surfaces. The films are bonded on the specimen surface beforehand, exposed to the cavitating jets for a short period, and then analyzed using an image analysis system. Overall, by comparing the mass loss, surface damage, visualization pictures, and pressure mapping, the effects of the experimental parameters on the erosion characteristics are examined. Moreover, design approaches that are applicable to both oil and water-hydraulic components are proposed in order to reduce erosion by cavitating jets. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aHydraulics. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170063.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170070 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170070$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170070$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP343 =082 04$a662$223 =100 1\$aHansen, Gregory A. T.,$eauthor. =245 10$aDetermining the Sensitivity of Fuel Lubricity Additive Concentration on HFRR Test Parameters /$cGregory A. T. Hansen, Peter M. Lee, Steven R. Westbrook, George R. Wilson. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn diesel engines, fuel pumps and injectors are subjected to tremendous pressures that can reach upward of 200 MPa in modern systems. In order to generate and maintain this level of pressure, the internal pump and injector components are made to an exacting standard. The drawback is that the moving components are largely lubricated with just the diesel fuel. If the diesel fuel has insufficient lubricating quality, catastrophic wear and subsequent failures can occur., The US Army currently utilizes aviation turbine fuel in all of its diesel-powered ground vehicles. The current specifications outlined in MIL-DTL-83133, Turbine Fuel, Aviation, Kerosene Type, JP-8 (NATO F-34), NATO F-35, and JP-8 + 100 (NATO F-37), and ASTM D1655, Standard Specification for Aviation Turbine Fuels, allow specific synthetic fuel components that can exacerbate the lubricity issue (having both low viscosity and no aromatic content). With these synthetics, the High-Frequency Reciprocating Rig (HFRR) can have a wear scar diameter as high as 900 ?m, which, if run unadditized in an engine, will cause immediate hardware failure. The military requires the use of an approved lubricity additive in the fuel it acquires. If treated with an approved additive at a rate between 20 and 30 mg/kg, even these poor lubricity fuels will be able to operate in Army equipment for the life of the engine. Unfortunately, the HFRR wear result does not discriminate between these neat and additized fuels. This work was undertaken in an attempt to improve the correlation of HFRR-type wear scar results with pump test results for a series of fuels with varying levels of lubricity additive. The effects of varying test conditions are reported and conclusions drawn on how improvements could be made to the current lubricity testing standards. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aLubrication and lubricants$xAdditives$xTesting. =650 \0$aStandards, Engineering. =700 1\$aLee, Peter M.,$eauthor. =700 1\$aWestbrook, Steven R.,$eauthor. =700 1\$aWilson, George R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170070.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170033 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170033$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170033$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ1075 =082 04$a621.89$223 =100 1\$aShah, Raj,$eauthor. =245 10$aTemperature Estimations in Elastohydrodynamic Contacts of Tribochemical Processes: A Comparative Study Using Modeling by Mechanical/Wear Process Mechanisms and Chemical Kinetic Modeling /$cRaj Shah, Cindy Klager, Jesse Kelly. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article deals with the subject of thermal Elastohydrodynamic Lubrication (EHL) and how temperatures can be estimated in elastohydrodynamic contacts. An attempt has been made to explain why it is essential to study temperature effects in EHL, and the process of thermal EHL modeling has been elucidated by solving a simple thermal EHL model. The temperatures obtained from this simple model seem to agree well with published literature. A comprehensive literature review of the numerous studies in thermal EHL modeling with particular emphasis on recent developments in this field has been presented. The second part of this comprehensive study includes a comparison between temperatures in the EHL contact as obtained by mechanical models and a chemical model, which will be discussed. The contact temperature required to consume the lubricant by oxidation during a microsample wear test is determined by a chemical kinetic model. Finally, the discrepancy between the temperatures obtained by both the chemical kinetic model and the mechanical model is discussed, presenting various plausible explanations to account for the temperature difference. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aElastohydrodynamic lubrication. =700 1\$aKelly, Jesse,$eauthor. =700 1\$aKlager, Cindy,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 3 Special Issue on Tribometry and Tribochemistry.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170033.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170111 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170111$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170111$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS250 =082 04$a669.95$223 =100 1\$aSimon, Nicola,$eauthor. =245 10$aReliable Residual Stress Analysis for Thin Metal Sheets by Incremental Hole Drilling /$cNicola Simon, Tobias Mrotzek, Jens Gibmeier. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSheet metal–forming processes induce characteristic residual stress-depth gradients into technical components. Regarding thin metal sheets with thicknesses of only a few millimeters, or those in the sub-mm range, surface finishing processes, e.g., machining processes like grinding, polishing, lapping, or mechanical post–surface treatments, might cause significant distortions. These may result from intentionally induced one-sided residual stress distributions or residual stress redistributions through one-sided materials removal. For process assessment and control, accurate residual stress analysis is indispensable. However, in sheet metal formation, the residual stress state is often accompanied by pronounced crystallographic textures, which usually cause failure of the standard laboratory procedures. As an example, X-ray residual stress analysis according to the standard sin2?-method is not feasible for markedly textured material states because of curved 2?-sin2? distributions. On the contrary, we have already shown that the incremental hole drilling method that uses case-specific calibration data and considers specimen thickness and crystallographic texture provides reliable stress evaluation. Hereby, for thin metal sheets, the appropriate support condition is very important since improper support can lead to significant restraints, i.e., the specimen fixture hinders the strain relaxation on the specimen's surface during the hole drilling process, and, for nonflat sheets, even assembling stresses can be superimposed. Consequently, stress calculation based on the measured strain relaxation data leads to erroneous residual stress results in application of the incremental hole drilling method. This work is derived from the necessity of measuring residual stress-depth gradients in thin molybdenum sheets. Thereby, an appropriate specimen support strategy for hole drilling application on thin metal sheets is proposed based on a systematic parametric study using 3-D finite element modeling that considers different sheet thicknesses. Based on the simulation results, a support ring with an adequate inner diameter is proposed as the most suitable specimen support. The numerical findings were verified by experimental residual stress analyses with the use of two different specimen supports. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSheet-metal work. =700 1\$aGibmeier, Jens,$eauthor. =700 1\$aMrotzek, Tobias,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170111.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170044 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170044$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170044$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aGA140 =082 04$a912.0148$223 =100 1\$aOlson, Mitchell D.,$eauthor. =245 10$aRepeatability of Contour Method Residual Stress Measurements for a Range of Materials, Processes, and Geometries /$cMitchell D. Olson, Adrian T. DeWald, Michael R. Hill. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article examines the precision of the contour method using five residual stress measurement repeatability studies. The test specimens evaluated include the following: an aluminum T-section, a stainless steel plate with a dissimilar metal slot-filled weld, a stainless steel forging, a titanium plate with an electron beam slot-filled weld, and a nickel disk forging. These specimens were selected to encompass a range of typical materials and residual stress distributions. Each repeatability study included contour method measurements on five to ten similar specimens. Following completion of the residual stress measurements, an analysis was performed to determine the repeatability standard deviation of each population. In general, the results of the various repeatability studies are similar. The repeatability standard deviation tends to be relatively small throughout the part interior, and there are localized regions of higher repeatability standard deviations along the part perimeter. The repeatability standard deviations over much of the cross section range from 5 MPa for the aluminum T-section to 25 MPa for the nickel disk forging. There is a strong correlation between the elastic modulus of the material and the repeatability standard deviation. These results demonstrate the precision of the contour method over a broad range of specimen geometries, materials, and stress states. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aContours (Cartography) =700 1\$aDeWald, Adrian T.,$eauthor. =700 1\$aHill, Michael R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170044.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170123 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170123$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170123$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA473 =082 04$a620.176$223 =100 1\$aValentini, Emilio,$eauthor. =245 10$aImprovements in the Hole-Drilling Test Method for Determining Residual Stresses in Polymeric Materials /$cEmilio Valentini, Lorenzo Bertelli, Alessio Benincasa. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article describes some improvements of the hole-drilling test method to increase the accuracy in determining residual stresses in polymeric materials. Unlike traditional applications of the hole-drilling technique to metals, when applied to polymers, it is essential to take into account important aspects such as the influence of ambient temperature, local heating, and thermal and mechanical effects generated by drilling operations. Unfilled polymers have a great coefficient of linear thermal expansion range, but the strain gauges for residual stresses available on the market are self-compensated only for some metallic materials. Furthermore, their low thermal diffusivity and the strong temperature dependence of their mechanical properties, notably, elastic modulus, creep, and relaxation, could determine local heating problems. The article investigates the hole-drilling technology on these materials and presents a testing procedure suitable for minimizing sources of error. The tests are carried out in a temperature-controlled test environment, and drilling is performed using the automatic drilling technique with a remote control, rather than a manual, drilling technique. Selections of the drilling rotational speed, feed rate, and type of drilling cutter are examined in detail. In order to validate the measurement approach, the experimental results obtained with a bending test bench on a polyethylene terephthalate sample are shown. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aResidual stresses. =700 1\$aBenincasa, Alessio,$eauthor. =700 1\$aBertelli, Lorenzo,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170123.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170135 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170135$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170135$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC482.D5 =082 04$a537.53$223 =100 1\$aMeixner, Matthias,$eauthor. =245 10$aAnalysis of Multiaxial Near-Surface Residual Stress Fields by Energy- and Angle-Dispersive X-ray Diffraction: Semi- Versus Nondestructive Techniques /$cMatthias Meixner, Manuela Klaus, Wolfgang Zinn, Daniel Apel, Alexander Liehr, Christoph Genzel, Berthold Scholtes. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aUnder laboratory conditions while applying angle-dispersive X-ray diffraction, the information depth in steel is usually restricted to less than 10 ?m. Access to residual stresses induced by mechanical, chemical, or both types of surface treatment in deeper regions requires either the application of the layer removal method or an analysis with highly penetrating X rays and synchrotron radiation, respectively. Successive layer removal yields the actual residual stress depth profiles ?ij(z) up to any depth below the surface, but this is time consuming and semidestructive. High-energy X-ray diffraction performed in the energy-dispersive mode avoids these drawbacks, but it provides only the Laplace stresses, ?ij(?), which have to be transformed back into the real space in order to obtain the actual stress-depth profile ?ij(z). Using an example of a uniaxially ground steel specimen, it is shown that the layer removal method and the energy-dispersive diffraction method for X-ray stress analysis when performed in reflection geometry yield comparable results in the case of the in-plane stress components ?11 and ?22. However, significant differences were observed concerning the out-of-plane stresses, which can be attributed to the boundary conditions that the ?i3 components must satisfy at the free surface. It is demonstrated that stress redistribution at the newly generated surfaces after successive layer removal leads to an underestimation of the shear stresses ?13. The analysis of the out-of-plane normal stress component ?33 is shown to require nondestructive measurements. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aX-rays$xDiffraction. =700 1\$aApel, Daniel,$eauthor. =700 1\$aGenzel, Christoph,$eauthor. =700 1\$aKlaus, Manuela,$eauthor. =700 1\$aLiehr, Alexander,$eauthor. =700 1\$aScholtes, Berthold,$eauthor. =700 1\$aZinn, Wolfgang,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170135.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170114 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170114$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170114$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC721 =082 04$a548.8$223 =100 1\$aWimpory, Robert C.,$eauthor. =245 10$aPrecise Measurement of Steep Residual Strain Gradients Using Neutron Diffraction in Strongly Absorbing Materials with Chemical Compositional Gradients /$cRobert C. Wimpory, Michael Hofmann, Vasileios Akrivos, Mike C. Smith, Thilo Pirling, Carsten Ohms. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA round robin benchmark weldment, denoted TG6, from the European Network on Neutron Techniques Standardization for Structural Integrity (NeT), offers the ability to test the technique of residual stress determination using neutron diffraction to an extreme. This test component comprises a 200 mm by 150 mm by 12 mm rectangular base plate made from Inconel 600 with three passes of Alloy 82 weld metal deposited in a slot of length 76 mm. This not only has large grain issues in the weld region but a large interplanar spacing variation caused by high strain gradients and a change in material composition. Because of the high absorption of neutrons in the Inconel 600 within the gauge volume, there is a large difference between the instrumental gauge volume IGV (which is the volume of space defined by the neutron beam paths through the defining apertures, taking into account properties of the beam) compared with the sampled gauge volume SGV (which is the intersection of the IGV with the sample that takes into account the absorption of the neutrons). The relative shift in position of the center of gravity of measurement (when the gauge volume is fully immersed in the sample) has been observed to be significant, for example, ~0.3 mm, using 1 by 1 by 5 mm3 defining optics (where 5 mm is the gauge volume height) and increases approximately proportionally with larger gauge volumes dimensions in the horizontal plane. The magnitude of this shift depends upon many parameters. Measuring the sample and rotating 180° and measuring again, taking the average is another way one can eliminate this absorption effect. This novel approach is compared with three neutrons instruments on the same sample. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aNeutrons$xDiffraction. =700 1\$aAkrivos, Vasileios,$eauthor. =700 1\$aHofmann, Michael,$eauthor. =700 1\$aOhms, Carsten,$eauthor. =700 1\$aPirling, Thilo,$eauthor. =700 1\$aSmith, Mike C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170114.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170080 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170080$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170080$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA473 =082 04$a620.176$223 =100 1\$aGur, C. Hakan,$eauthor. =245 10$aReview of Residual Stress Measurement by Magnetic Barkhausen Noise Technique /$cC. Hakan Gur. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDetermination of residual stress state is important for quality, integrity, and service performance of the components and structures. Almost all manufacturing processes cause considerable amounts of residual stress; thus, any process or product design ignoring it involves a risk for distortion or early failure. Among the existing methods, the magnetic Barkhausen noise method has been gaining attention for measuring residual stresses nondestructively in ferromagnetic materials. It is sensitive to the interactions between the magnetic structure and microstructure or residual stress fields. So far, successful qualitative results have been obtained for monitoring the residual stress variations on the surfaces of the components manufactured by various processes. However, some challenging tasks exist, such as obtaining reliable quantitative results when residual stresses and microstructure change at the same time or extracting depth-specific information. This article reviews the studies for the measurement of residual stress by magnetic Barkhausen noise method, particularly focusing on the processes widely used in industry, namely shot peening and welding. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aResidual stresses. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170080.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170050 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170050$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170050$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA648.3 =082 04$a620.1123$223 =100 1\$aShimov, G. V.,$eauthor. =245 10$aRapid Method for Determining the Distribution of Residual Stresses in Pipes /$cG. V. Shimov. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis paper describes the method of longitudinal residual stress measurement on inner and outer pipe surface layers, which is used for calculation of the distribution of all residual stresses over the wall thickness. The method proposed is applicable in cases of stresses that are opposite in sign and exist inside and outside the pipe. Moreover, in accordance with the hypothesis of a parabolic circumferential and longitudinal distribution of residual stresses, this paper proposes the calculation method of stress distribution by measured ultimate stresses of the same sign inside and outside the pipe. The method is suitable for use in the express laboratory of a workshop that produces cold-formed seamless pipes. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aResidual stresses$xMeasurement. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170050.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170097 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170097$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170097$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK9166 =082 04$a621.48/071/173$223 =100 1\$aCristea, Mihaela E.,$eauthor. =245 10$aResidual Stress Profile in Tubular Components /$cMihaela E. Cristea, Mirco D'Incau, Paolo Scardi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe precise manufacturing of seamless steel pipes requires postprocess straightening treatments that lead to rather complex and not easily predictable residual stress fields. In this work, we combine blind hole drilling (BHD) and X-ray diffraction (XRD) techniques to determine the most relevant component, the circumferential (hoop) stress: BHD is used on the outer surface of the steel pipe and XRD is used on the inside; the results from both techniques are combined with a progressive layer removal procedure to determine the stress profile across the pipe wall. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aPipe, Steel$xTesting. =700 1\$aD'Incau, Mirco,$eauthor. =700 1\$aScardi, Paolo,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170097.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170110 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170110$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170110$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA4755.P58 =082 04$a620.192$223 =100 1\$aVollert, Florian,$eauthor. =245 10$aTwo-Dimensional Residual Stress Mapping of Multilayer LTT Weld Joints Using the Contour Method /$cFlorian Vollert, Jens Gibmeier, Joana Rebelo-Kornmeier, Jonny Dixneit, Thilo Pirling. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aLow transformation temperature (LTT) weld filler materials offer an attractive alternative to cost intensive postweld treatments as they can mitigate detrimental welding residual stresses during the welding process. Compared to conventional weld filler materials, LTT alloys are characterized by a delayed martensite transformation at low temperatures, which can result in compressive residual stresses in the weld. The high strength of these filler materials makes them potentially applicable to high-strength steels as well as for a large amount of requested repair works in steel structures. The focus of the study is on the confirmation of the LTT idea with regard to the residual stress state for multipass weld lines processed by metal active gas welding. It is demonstrated that the contour method is a well-suited technique for measuring the residual stress in the weld joint as it gives an entire two-dimensional map of the residual stress state in the weld line, heat affected zone (HAZ), and base material. The technique was applied at different LTT alloys with varying chemical compositions. Additionally, the results are compared to residual stress maps that were determined by neutron diffraction using the Strain Analyzer for Large Scale Engineering Applications, an instrument referred to as SALSA, at the Institut Laue-Langevin in Grenoble. For all investigated specimens, compressive residual stress distributions were determined in the area of the weld joint and the HAZ. They are balanced by tensile residual stresses in the surrounding base material. However, it is shown that the size of the region exhibiting compressive residual stresses and the absolute values of the compressive residual stresses depend on the chemical composition of the weld filler material. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aFillers (Materials) =700 1\$aDixneit, Jonny,$eauthor. =700 1\$aGibmeier, Jens,$eauthor. =700 1\$aPirling, Thilo,$eauthor. =700 1\$aRebelo-Kornmeier, Joana,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170110.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170089 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170089$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170089$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS227.A1 =082 04$a671.52$223 =100 1\$aOkano, Shigetaka,$eauthor. =245 10$aCoupling Computation between Weld Mechanics and Arc Plasma Process for Residual Stress Analysis /$cShigetaka Okano, Hitoshi Tsuji, Ryohei Ihara, Masahito Mochizuki. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article presents an advanced computational framework to accurately simulate weld residual stress, which is generated as a result of thermomechanical behavior during welding. The basis of the framework is coupled process–mechanics modeling and analysis of gas tungsten arc welding (GTAW). In the developed modeling and analysis, a heat source model dependent on the welding heat input condition was constructed by considering the physics of the welding arc. Formation of the weld pool and temperature field was calculated through a combined conductive and convective heat transfer analysis with the constructed heat source model. Transient temperature fields obtained were used for large-deformation thermal elastic–plastic analysis of residual stress induced by welding. The modeling and analysis were applied to calculate the welding thermomechanical problems of low-carbon austenitic stainless steel. The calculated weld penetration, temperature profiles, and distribution of residual stress in the welds were compared with the experimental measurements to validate the accuracy of the modeling and analysis. The effect of convective heat transfer on weld pool formation was further investigated in relation to a parameter derived from welding thermal conduction theory for a moving point heat source. The dimensions of weld penetration and the convective heat transfer effect were estimated by the parameter. Thus, it was concluded that the developed modeling and analysis techniques successfully achieved an accurate weld residual stress analysis and provided a more detailed understanding of the convective heat transfer effect on weld pool formation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aWelding. =700 1\$aIhara, Ryohei,$eauthor. =700 1\$aMochizuki, Masahito,$eauthor. =700 1\$aTsuji, Hitoshi,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170089.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170103 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170103$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170103$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS227.A1 =082 04$a671.52$223 =100 1\$aKromm, Arne,$eauthor. =245 10$aFrom the Field to the Lab: Real Scale Assessment of Stresses in Welded Components /$cArne Kromm, Thomas Lausch, Dirk Schröpfer, Jonny Dixneit, Andreas Hannemann, Thomas Kannengiesser. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aResidual stresses are crucial when assessing the performance of welded components. The present work deals with the possibilities of transferring the real-life boundary conditions of welding, which influence the residual stress, into the laboratory. The possibilities of a test system specifically developed for this purpose, with a maximum capacity of 2 MN, are shown, because the structural design, global process, geometry, and material-dependent stresses are induced, which can be simulated and quantified within the system. Additionally, X-ray diffraction can be applied to determine the resulting local stress distribution precisely with high spatial resolution. Two examples are presented to show how the conditions to be found during production are simulated in the laboratory. It is shown how welding stresses in high-strength steels are affected by the heat control. It was possible to clarify why elevated working temperatures significantly increase the bending stresses in the welded joint and therefore the tensile stresses in the heat-affected zone. The effect of heat treatment applied under stresses resulting from welding is demonstrated by the example of a creep-resistant steel. Reheat cracking is significantly increased in this case, as compared to small-scale laboratory-based tests. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aWelding. =700 1\$aDixneit, Jonny,$eauthor. =700 1\$aHannemann, Andreas,$eauthor. =700 1\$aKannengiesser, Thomas,$eauthor. =700 1\$aLausch, Thomas,$eauthor. =700 1\$aSchröpfer, Dirk,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170103.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170125 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170125$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170125$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA648.3 =082 04$a620.1123$223 =100 1\$aMaestri, N.,$eauthor. =245 10$aExperimental Measurement of Residual Stresses in Cr-Mo-V Steel Restrained Welds with High Thickness /$cN. Maestri, P. Marangoni, D. Pettene, B. Rivolta, R. Gerosa. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis experimental work is focused on the residual stresses induced by multi-pass welding of thick components. Two samples were produced, inspired by the nozzle-vessel geometry, with Submerged Arc Welding buttwelding, performed according to the standard welding procedures employed by Belleli Energy CPE. The components were characterized by different sizes and groove positions. Measurements of residual stresses were carried out by hole drilling according to ASTM E837-13a, Standard Test Method for Determining Residual Stresses by the Hole-Drilling Strain-Gage Method, in different positions of the samples. The measurements were performed on welded, and Dehydrogenation Heat Treatment (350°C, 4h), and Intermediate Stress Relieving treatments. The obtained results allowed a discussion of the influence of the component size on the residual stresses and the effectiveness of an intermediate heat treatment for reducing the stress state. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aResidual stresses$xMeasurement. =700 1\$aGerosa, R.,$eauthor. =700 1\$aMarangoni, P.,$eauthor. =700 1\$aPettene, D.,$eauthor. =700 1\$aRivolta, B.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170125.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170091 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170091$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170091$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA648.3 =082 04$a620.1123$223 =100 1\$aBenghalia, G.,$eauthor. =245 10$aMultiscale Measurements of Residual Stress in a Low-Alloy Carbon Steel Weld Clad with IN625 Superalloy /$cG. Benghalia, S. Rahimi, J. Wood, H. Coules, S. Paddea. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aFatigue fracture is one of the major degradation mechanisms in the low-alloy 4330 carbon steel pumps that are utilized in the hydraulic fracturing process operating under cyclic loading conditions. A weld cladding technology has been developed to improve the ability of these components to resist fatigue crack initiation by cladding them with a secondary material. This process introduces a residual stress profile into the component that can be potentially detrimental for fatigue performance. The cladding technology under examination is a low-alloy 4330 carbon steel substrate weld that is clad with the nickel-chromium–based superalloy IN625 and is investigated herein using several experimental residual stress measurement techniques. Understanding the magnitude and distribution of residual stress in weld clad components is of the utmost importance to accurately assess the performance of the component in service. This study summarizes the results of residual stress measurements that were determined using X-ray diffraction, i.e., hole drilling based on electronic speckle pattern interferometry, deep-hole drilling, and the contour method, to obtain the residual stress distributions from the surface of the weld clad, through the clad layer, and into the substrate material. The results of deep-hole drilling and the contour method show large-scale tensile residual stress in the clad layer and compressive residual stress in the majority of the substrate. However, the X-ray diffraction and hole drilling methods indicate the presence of short-scale compressive residual stress on the surface and near the surface of the clad layer. It was shown that these measurement techniques are complementary in assessing the residual stress profile throughout the entire component. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aResidual stresses$xMeasurement. =700 1\$aCoules, H.,$eauthor. =700 1\$aPaddea, S.,$eauthor. =700 1\$aRahimi, S.,$eauthor. =700 1\$aWood, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170091.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170113 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170113$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170113$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA473 =082 04$a624.182$223 =100 1\$aHensel, Jonas,$eauthor. =245 10$aResidual Stress–Based Fatigue Design of Welded Structures /$cJonas Hensel, Thomas Nitschke-Pagel, Klaus Dilger. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aFatigue design concepts for welded structures generally consider residual stresses as a factor affecting the mean stress influence. Residual stresses are mostly interpreted as mean stresses. In addition, high tensile residual stresses are conservatively assumed, resulting in maximum effective load stresses from fatigue loading in the order of the yield strength. The consequence of this is that additional static load stresses may have no influence on the resulting fatigue strength because the local effective mean stress (residual stresses and load mean stresses) is always high. The related evaluation concepts neither distinguish between different steel grades nor between different origins and amounts of possible residual stresses in welded joints. The real magnitude of existing residual stresses is also usually not considered, because in practice, usually no explicit knowledge of the residual stresses at critical sites of a construction is available because residual stress measurements are not state of the art in welding practice. For an explicit consideration of residual stresses in design concepts, the sign, the initial amount, and especially the amount of the residual stresses after a load induced relaxation must be considered. Therefore, the steel grade and the condition of the material are of great importance, as well as the local stress condition influenced by welding-induced notch geometry. The article shall give an overview about the state of the art of consideration of residual stresses in fatigue design concepts for welded structures and the background of their development. Finally, a new approach shall offer a possibility for an enhanced consideration of residual stresses in design concepts based on the explicit knowledge about the effective residual stresses that can actually be observed with different measurement concepts. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aResidual stresses. =700 1\$aDilger, Klaus,$eauthor. =700 1\$aNitschke-Pagel, Thomas,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170113.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170093 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170093$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170093$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN757.C5 =082 04$a672.36$223 =100 1\$aO'Sullivan, D.,$eauthor. =245 10$aAn Investigation into the Reverse Transformation Mechanisms in the Heat Treatment of Austenitic Stainless Steel /$cD. O'Sullivan, R. Raghavendra, M. Cotterell, I. Mészáros, D. A. Tanner. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCold working of austenitic stainless steel results in the formation of α′-martensite (ferromagnetic) within the host material (paramagnetic). The role of α′-martensite and carbide precipitation in the reverse transformation mechanism during the heat treatment of AISI 304 is presented. A magnetic Barkhausen noise (MBN) measurement technique was employed to characterize the transformation mechanisms. MBN was found to be an effective tool for studying the transformation mechanisms of austenite to α′-martensite during material deformation as MBN and the ferromagnetic phase showed a good correlation. AISI 304 specimens plastically strained to 51 % were subjected to annealing heat treatment (from 100°C to 1,100°C) for 30 minutes. The α′-martensite to austenite reversion mechanisms were found to have a significant effect on residual stress and materials magnetic properties, thus limiting MBN effectiveness in studying the reverse transformation process. Residual stresses go from tensile to compressive between 500°C and 600°C as a result of the transformation mechanisms, as the austenitic phase is larger than α′-martensite and therefore compresses the remaining α′-martensite. It is suggested that ?-martensite has a significant role in the dislocation structural mechanisms in the heat treatment of AISI 304. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aAustenitic stainless steel. =700 1\$aCotterell, M.,$eauthor. =700 1\$aMészáros, I.,$eauthor. =700 1\$aRaghavendra, R.,$eauthor. =700 1\$aTanner, D. A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170093.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170083 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170083$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170083$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA492.P7 =082 04$a669.142$223 =100 1\$aJokiaho, Tuomas,$eauthor. =245 10$aEffect of Microstructural Characteristics of Thick Steel Plates on Residual Stress Formation and Cracking during Flame Cutting /$cTuomas Jokiaho, Suvi Santa-aho, Henri Järvinen, Mari Honkanen, Pasi Peura, Minnamari Vippola. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThick wear-resistant steel plates are commonly used in demanding conditions, such as in the mining industry. In harsh environments, a high degree of both toughness and hardness is required, which extends the service life of the components but also makes the production of the plates difficult. Flame cutting is a generally applied cutting method in the heavy steel industry since it enables the cutting of thick steel plates at high production rates. However, flame cutting may cause cracks in the cut edge of the steel plates, leading to rejects for the steel industry and end-users. In addition, cutting generates a heat-affected zone at the cut edge, where volumetric and microstructural changes and hardness variations take place. A steep thermal gradient, generated during flame cutting, also produces high residual stresses on the cut edge. The goal of this study is to examine how microstructural features contribute to the residual stress formation and cracking probability of thick steel plates. Specific microstructural features can make the plates prone to cracking and tend to produce undesired stresses during the cutting process. The residual stress profiles of flame-cut specimens were measured using the X-ray diffraction method. In addition, the mechanical properties of steel plates were evaluated. The microstructures of the cut edge and the base material were characterized by electron microscopy. Results indicate that the shape of the prior austenite grains has an effect on both the cracking probability and residual stress formation. Longitudinally oriented prior austenite grain boundaries combined with a high residual tensile stress state provide potential sites for cracking. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aPlates, Iron and steel. =700 1\$aHonkanen, Mari,$eauthor. =700 1\$aJärvinen, Henri,$eauthor. =700 1\$aPeura, Pasi,$eauthor. =700 1\$aSanta-aho, Suvi,$eauthor. =700 1\$aVippola, Minnamari,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170083.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180018 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180018$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180018$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.186$223 =100 1\$aAbburi Venkata, K.,$eauthor. =245 10$aExamining Stress Relaxation in a Dissimilar Metal Weld Subjected to Postweld Heat Treatment /$cK. Abburi Venkata, S. Khayatzadeh, A. Achouri, J. Araujo de Oliveira, A. N. Forsey, S. Gungor, P. J. Bouchard, C. E. Truman. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDissimilar metal welds are often required in nuclear power plants to join components made from austenitic steels to those from ferritic steels, particularly in fast breeder reactor plants, in order to join the intermediate heat exchanger to the steam generator. The process of welding alters the microstructure of the base materials and causes residual stresses to form, both because of the change in the microstructure and the differing thermal histories in various regions. Postweld heat treatment (PWHT) is required to relieve the residual stresses and achieve preferable microstructural gradients across the weld joint. Therefore, in order to arrive at the optimal PWHT process, it is necessary to investigate the effects of heat treatment on the joint integrity, microstructure, and residual stress relaxation in the welds. To investigate the effect of PWHT on the residual stress relaxation and corresponding alteration of microstructure across a welded joint, a dissimilar weld between modified 9Cr-1Mo steel and austenitic stainless steel AISI 316LN was made using autogenous electron beam welding. To achieve this, the welding process was first modeled numerically using finite element analysis, and the residual stress predictions were validated by experimental investigation using neutron diffraction. The validated model was then used to study the residual stress relaxation through the simulation of PWHT. The predicted stress relaxation was compared with contour method measurement of residual stresses in the actual welded plate subjected to PWHT. The results indicate that, although some relaxation of residual stresses occurred during PWHT, there is still a significant portion of highly localized residual stresses left in the specimen. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aMetals$xHeat treatment. =700 1\$aAchouri, A.,$eauthor. =700 1\$aBouchard, P. J.,$eauthor. =700 1\$ade Oliveira, J. Araujo,$eauthor. =700 1\$aForsey, A. N.,$eauthor. =700 1\$aGungor, S.,$eauthor. =700 1\$aKhayatzadeh, S.,$eauthor. =700 1\$aTruman, C. E.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180018.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170145 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170145$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170145$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN757.C5 =082 04$a672.36$223 =100 1\$aSomers, Marcel A. J.,$eauthor. =245 10$aResidual Stress in Expanded Austenite on Stainless Steel; Origin, Measurement, and Prediction /$cMarcel A. J. Somers, Ömer C. Kücükyildiz, Casper A. Ormstrup, Hossein Alimadadi, Jesper H. Hattel, Thomas L. Christiansen, Grethe Winther. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aExpanded austenite is a supersaturated solid solution of nitrogen/carbon in austenite that forms as a case by the diffusion of nitrogen/carbon into austenitic stainless steel. Expanded austenite has a high level of hardness that provides resistance against galling and wear, superior resistance against localized corrosion, and contributes to improvement of the fatigue performance. This latter characteristic is a consequence of the huge compressive residual stresses in the expanded austenite case. Such stresses are induced by the high interstitial content in the austenite lattice and are accommodated elasto-plastically. The experimental assessment of the elastic lattice strains is complicated by the presence of steep composition-depth and stress-depth profiles, which necessitate special measurement or correction procedures to unravel the influence of composition and stress on the lattice spacing and avoid artifacts arising from (steep) lattice-spacing gradients. In the present work the sin2? method was combined with grazing incidence X-ray diffraction to keep the information depth during measurement shallow, independent of the (effective) tilt angle ?. The plastic strains in the expanded austenite 27 zone were estimated from the lattice rotations, as determined with electron backscatter diffraction. It is demonstrated that the level of elastic lattice strains in expanded austenite can be adjusted by retracting part of the dissolved nitrogen. The experimental results for elastic and plastic strains are compared to those predicted by a comprehensive numerical model that simulates the time-dependent development of composition-depth and stress-depth profiles in expanded austenite. The work described in this manuscript is a combination of a review of previously achieved and published results as well as the newest results of ongoing research activities. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aAustenitic stainless steel. =700 1\$aAlimadadi, Hossein,$eauthor. =700 1\$aChristiansen, Thomas L.,$eauthor. =700 1\$aHattel, Jesper H.,$eauthor. =700 1\$aKücükyildiz, Ömer C.,$eauthor. =700 1\$aOrmstrup, Casper A.,$eauthor. =700 1\$aWinther, Grethe,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170145.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170119 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170119$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170119$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC482.D5 =082 04$a537.53$223 =100 1\$aThiede, Tobias,$eauthor. =245 10$aResidual Stress in Selective Laser Melted Inconel 718: Influence of the Removal from Base Plate and Deposition Hatch Length /$cTA479.A88 . =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe residual stress distribution in IN718 elongated prisms produced by selective laser melting was studied by means of neutron (bulk) and laboratory X-ray (surface) diffraction. Two deposition hatch lengths were considered. A horizontal plane near the top surface (perpendicular to the building direction) and a vertical plane near the lateral surface (parallel to the building direction) were investigated. Samples both in as-built (AB) condition and removed from the base plate (RE) were characterized. While surface stress fields seem constant for the AB condition, X-ray diffraction shows stress gradients along the hatch direction in the RE condition. The stress profiles correlate with the distortion maps obtained by tactile probe measurements. Neutron diffraction shows bulk stress gradients for all principal components along the main sample directions. We correlate the observed stress patterns with the hatch length, i.e., with its effect on temperature gradients and heat flow. The bulk stress gradients partially disappear after removal from the base plate. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aX-rays$xDiffraction. =700 1\$aBode, Johannes,$eauthor. =700 1\$aBruno, Giovanni,$eauthor. =700 1\$aHaberland, Christoph,$eauthor. =700 1\$aKromm, Arne,$eauthor. =700 1\$aNadammal, Naresh,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170119.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170133 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170133$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170133$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS213 =082 04$a571.36$223 =100 1\$aCoratella, Stefano,$eauthor. =245 10$aResidual Stress Field of a Single Edge Notch Specimen after Laser Shock Peening and Shot Peening Treatment /$cStefano Coratella, T. J. Spradlin, Kristina Langer, Michael A. Gharghouri, U. C. Heckenberger, E. Hombergsmeier. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aLaser shock peening (LSP) is a reliable, repeatable, and successful surface technique for introducing high magnitude, deep compressive residual stresses that can significantly increase the fatigue life of metallic components. However, depending upon how the LSP treatment is applied, the induced residual stresses can result in the undesirable deformation of the part. In this work, traditional shot peening has been applied over LSP as a means to optimize the stress distribution at the surface of a part while constraining deformation. A single edge notch test specimen of AA7075 was laser peened local to the notch region and then shot peened over the entire central region. The resulting residual stress distribution has been characterized using neutron diffraction to measure the stress distribution in the bulk, and it was compared with (1) incremental center hole drilling to measure the stress distribution up to depths of ~1 mm and (2) near-surface stresses obtained in a previous X-ray diffraction (XRD) study on nominally identical specimens subjected to the same surface treatments. For regions where the two techniques overlap, the residual stresses are in good agreement (within uncertainty). Comparing the bulk stresses obtained from neutron diffraction in this study and XRD data published elsewhere, it can be shown that shot peening applied after LSP has a profound effect on near-surface stresses; however, these effects disappear at depths of ~0.7 mm or more. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aShot peening. =700 1\$aGharghouri, Michael A.,$eauthor. =700 1\$aHeckenberger, U. C.,$eauthor. =700 1\$aHombergsmeier, E.,$eauthor. =700 1\$aLanger, Kristina,$eauthor. =700 1\$aSpradlin, T. J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170133.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170108 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170108$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170108$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA472 =082 04$a672$223 =100 1\$aMiao, Shan,$eauthor. =245 10$aResidual Stress Modification and Mechanisms of Bearing Steel with Different Microstructures during Water-Jet Cavitation Peening /$cShan Miao, Dong-Ying Ju, Hui-Jun Zhao. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aWater-jet cavitation peening (WCP) is used to increase the hardness and induce the formation of a compressive residual stress layer on the surface through the shock wave pressure, which is produced by the collapse of small bubbles of a cavitation jet at the surface of materials. In this article, a pressure sensitive paper is applied to determine the pressure field distribution of WCP. WCP is carried out on the bearing steel 100Cr6 with different microstructures, which are heat-treated differently. The hardness, residual stress distribution, and microstructure of bearing steels at the same observation points are compared, respectively, before and after WCP. The research indicates that both the hardness and residual stress are increased with the peening time. It also proves that this method has different strengthening limits for materials with different microstructures because of the different mechanisms of WCP. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSteel, Bearing. =700 1\$aJu, Dong-Ying,$eauthor. =700 1\$aZhao, Hui-Jun,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170108.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170134 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170134$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170134$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS213 =082 04$a571.36$223 =100 1\$aEisensmith, David L. A.,$eauthor. =245 10$aEffects of Laser Shock Peening over Minimally Detectable Partial Through-Thickness Surface Cracks /$cDavid L. A. Eisensmith, Anthony N. Palazotto, Kristina Langer, Michael A. Gharghouri, Stefano Coratella. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aLaser shock peening (LSP) has evolved as a viable alternative to other surface treatments (shot peening, burnishing, etc.) that induce beneficial residual stress in structural components. While fatigue life improvements have been recognized by the aerospace industry, in-service components may have surface flaws with sizes below current inspection limits. A concern is that the application of LSP over an existing crack may cause unintended detrimental consequences. To address this concern, two different LSP processes were applied over a 0.25 in. (6.35 mm) partial through-thickness surface fatigue crack in 7075-T651 aluminum. The resulting residual stresses were measured using combinations of included X-ray diffraction with layer removal, incremental center-hole drilling, and neutron diffraction. Both LSP processes resulted in a through-thickness residual stress profile in which compressive stresses at either surface were balanced by tensile stresses in a band centered in the mid-thickness of the specimen. Peened and unpeened (baseline) specimens were then tested under constant-amplitude cyclic loading to assess the fatigue response. The average fatigue life of the baseline specimens was about 49,000 cycles. The peened specimens (both treatments) survived to runout, exhibiting no crack growth when examined with an optical microscope even when the crack tip was either very close to or inside the region of tensile residual stress. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aShot peening. =700 1\$aCoratella, Stefano,$eauthor. =700 1\$aGharghouri, Michael A.,$eauthor. =700 1\$aLanger, Kristina,$eauthor. =700 1\$aPalazotto, Anthony N.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170134.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170106 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170106$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170106$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.186$223 =100 1\$aCarlson, Scott,$eauthor. =245 10$aUsing a Beta (?) Correction to Improve the Life Predictions of Cold-Expanded Holes in 2024-T3 & 7075-T6 Aluminum Alloys /$cScott Carlson, Robert T. Pilarczyk. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (28 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aFastener holes represent the most common fatigue details found in airframe structures. In order to minimize the impact fastener holes have on the fatigue behavior of critical aircraft components, many are processed by cold expansion (Cx). Cx imposes a residual compressive stress field around a hole that retards fatigue crack growth (FCG) and increases the fatigue life of the component. In order to take analytical advantage of the Cx process, a “one size fits all” method of reducing the initial flaw size to a minimum of a 0.005 in. (0.127 mm) symmetric corner crack is often employed. This approach leads to predictions that do not represent the physics of crack growth behavior within materials that have been processed using Cx. A physics-based approach was investigated to take analytical advantage of the Cx process. The authors developed an empirical-based factor (?) to characterize the effect of Cx on the FCG behavior within 2024-T351 and 7075-T651 aluminum alloys. This method takes into account the interaction of the fatigue crack and the residual stress field. This ? can be used in FCG analysis to provide an accurate model of the crack growth behavior at Cx holes. In order to develop accurate da/dN versus ?K plots for the Cx configuration, finite element modeling was used to calculate stress intensities along the crack front. By using the fracture-mechanics-based similitude principle, the nonCx and Cx da/dN versus ?K data were compared and ? corrections representing the residual stress field in the body were calculated. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aAluminum alloys. =700 1\$aPilarczyk, Robert T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170106.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170169 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170169$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170169$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS213 =082 04$a571.36$223 =100 1\$aSanta-aho, Suvi,$eauthor. =245 10$aSurface Layer Characterization of Shot Peened Gear Specimens /$cSuvi Santa-aho, Aki Sorsa, Jukka Wartiainen, Per Lundin, Lasse Suominen, Tuomas Jokiaho, Mari Honkanen, Kauko Leiviskä, Minnamari Vippola. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe production of gear components includes numerous manufacturing operations, which are carried out to ensure proper surface characteristics. Shot peening is one of the surface finishing processes used for transmission components like gears to improve their fatigue behavior. Shot peening increases the compressive residual stresses on the surface, and the procedure also reduces the amount of retained austenite in the surface layer. In addition, shot peening has an influence on other mechanical properties, such as surface roughness and surface hardness. An experimental design was conducted with varying shot peening process parameters, like coverage density and intensity, to alter the surface layer of 13 transmission gear specimens. The correlation between shot peening parameters, Barkhausen noise (BN) features, and X-ray diffraction residual stress measurement was studied. Linear correlation was found between residual stress and shot peening parameters. The relationship between residual stress and BN root-mean-square was not evident but was revealed by taking the ratio of BN measurements at different frequencies. Additionally, BN features, such as peak position, coercivity, and integral area, were found to have a linear trend with the intensity. Along with the aforementioned measurements, other material characterization measurements were also taken. The shot peening coverage density was observed to have a linear relationship with surface roughness values, while an intensity of over 0.6 mm A was noticed to affect the surface hardness. The results obtained can be used in the determination of suitable shot peening parameters to achieve a surface with desired residual stress. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aShot peening. =700 1\$aHonkanen, Mari,$eauthor. =700 1\$aJokiaho, Tuomas,$eauthor. =700 1\$aLeiviskä, Kauko,$eauthor. =700 1\$aLundin, Per,$eauthor. =700 1\$aSorsa, Aki,$eauthor. =700 1\$aSuominen, Lasse,$eauthor. =700 1\$aVippola, Minnamari,$eauthor. =700 1\$aWartiainen, Jukka,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170169.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170099 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170099$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170099$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL671.6 =082 04$a629.13431$223 =100 1\$aBall, Dale L.,$eauthor. =245 10$aAn Update on the Impact of Forging Residual Stress in Airframe Component Design /$cDale L. Ball. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (35 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn a recently concluded study, the effects of forging process–induced bulk residual stresses on fatigue life were evaluated at both the coupon and large component level. During this program, it was demonstrated that the extraction of confounding residual stress effects from material property data (especially fatigue crack growth rate data), coupled with the explicit inclusion of forging residual stresses in subsequent fatigue analyses, resulted in a significant improvement in the fidelity of those analyses. In the first phase of the program, coupon-level tests were carefully designed, executed, and analyzed, and it was shown that the newly developed methods resulted in analysis versus test life correlation ratios that were either within the United States Air Force (USAF) required scatter factor of 2, or were conservative. This is in contrast to a much broader scatter band (5x) for calculations made using traditional (non–residual-stress-informed) methods. The explicit residual stress method was incorporated into an integrated structural design/analysis tool suite that allows zoning of parts into residual stress–specific regions, automated generation of location-specific fatigue spectra, automated execution of fatigue crack initiation, fatigue crack growth, and residual strength analyses, and automated generation of fatigue-based design, allowable stresses, and margins of safety. In the second phase of the program, the residual stress design procedure was applied (to the furthest extent possible) to the design and manufacture of a large, fighter aircraft bulkhead. The objective of this phase of the program was to demonstrate, by way of two large component fatigue tests, that the technology would scale to the structural level, and that its use would result in components that are either lighter or more durable (or both) than their traditionally designed counterparts. In this article, we compare and contrast the traditional versus residual stress–informed design procedures, and we describe in detail the resulting baseline and “optimized” test articles. A full description of the fatigue tests, along with comparisons between detailed fatigue calculations and test findings, are given. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aAirframes$xFatigue$xTesting. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170099.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170105 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170105$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170105$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.1/86$223 =100 1\$aOlson, Mitchell D.,$eauthor. =245 10$aMulti-Technique Residual Stress Measurements to Quantify Stress Relief of 7085-T7452 Aluminum Die Forgings /$cMitchell D. Olson, Thomas J. Spradlin, Adrian T. DeWald, Michael R. Hill. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article describes the use of complementary residual stress measurements to quantify cold-work stress relief in die forgings used for monolithic unitized aerospace components. Two specimens were used, being nominally identical, but measured at different processing stages: one that was die forged and quenched (high residual stress state) and one having a post-quench, cold-work stress relief (low residual stress state). Multi-component residual stress maps were developed using multiple techniques along a single measurement plane (axes of this plane run parallel to the nominal long-transverse [x-direction] and short-transverse directions [y-direction]). The measurement techniques were energy dispersive X-ray diffraction (EDXRD), neutron diffraction (ND), and primary slice removal (PSR) biaxial mapping. Good agreement was found between the EDXRD and PSR biaxial mapping measurements. In the high-stress specimen, measured stress normal to the measurement plane (z-direction [L]) is highly compressive along the part exterior (–300 MPa) and highly tensile toward the center (250 MPa), as typical of quenched aluminum. Stress along the x-direction has a similar spatial distribution but smaller magnitude (–200 MPa to 130 MPa). The measured stresses in the cold-worked, low-stress specimen are significantly lower, with z-direction and x-direction stresses ranging between –130 MPa and 75 MPa. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aAluminum alloys. =650 \0$aDie-casting. =700 1\$aDeWald, Adrian T.,$eauthor. =700 1\$aHill, Michael R.,$eauthor. =700 1\$aSpradlin, Thomas J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170105.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170132 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170132$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170132$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC721 =082 04$a548.8$223 =100 1\$aMeyer, Heiner,$eauthor. =245 10$aIn Situ Investigations of Elastic Strain State in Deep Rolled 4140H Steel by Neutron Diffraction Method /$cHeiner Meyer, Jérémy Epp, Thilo Pirling, Hans-Werner Zoch. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA deep rolling process was applied on 4140H steel specimens with a self-built loading frame and investigated in situ with neutron radiation using the SALSA instrument at the Institut Laue-Langevin (ILL). A neutron diffraction stress imaging approach was developed and used to determine material changes from the surface up to several millimeters inside the material by single expositions. The strains could be evaluated as deviations of the diffraction signal along the height of an area detector, and the theoretical maximum depth resolution was given by geometrical magnification together with the detector pixel size. The results of these experiments together with complementary post-process investigations could be used to link the internal load during the process with resulting material modifications such as the generated residual strains. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aNeutrons$xDiffraction. =700 1\$aEpp, Jeremy,$eauthor. =700 1\$aPirling, Thilo,$eauthor. =700 1\$aZoch, Hans-Werner,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170132.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170130 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170130$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170130$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC721 =082 04$a548.8$223 =100 1\$aRobinson, J. S.,$eauthor. =245 10$aCold Compression of 7075 and Factors Influencing Stress Relief /$cJ. S. Robinson, R. C. Wimpory, D. A. Tanner, B. Mooney, C. E. Truman, T. Panzner. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe residual stresses in heat-treated 7075 aluminum alloy blocks have been characterized using neutron diffraction, X-ray diffraction, and incremental center-hole drilling. Specimens were quenched to induce high-magnitude residual stresses, which were then stress relieved by the controlled application of plastic deformation using a cold compression technique. The experimental variables investigated were the quench water temperature and the postquench delay. This delay is considered to influence the final residual stress magnitudes because of hardening precipitation occurring by natural aging during the period between quenching and the application of plastic deformation. Cold compression significantly lowered the residual stresses in all specimens. Neutron diffraction measurements demonstrated a benefit to applying plastic deformation as soon as possible after quenching. However, this beneficial effect was not evident when characterizing surface residual stresses using hole drilling or X-ray diffraction. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aNeutrons$xDiffraction. =700 1\$aMooney, B.,$eauthor. =700 1\$aPanzner, T.,$eauthor. =700 1\$aTanner, D. A.,$eauthor. =700 1\$aTruman, C. E.,$eauthor. =700 1\$aWimpory, R. C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170130.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170156 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170156$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170156$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ853 =082 04$a620.106$223 =100 1\$aBehera, A. R.,$eauthor. =245 10$aAn Experimental Study of Residual Stress Induced Modulation of Vibration Characteristics in 1-D MEMS Resonators /$cA. R. Behera, A. Dangi, R. Pratap. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aWe experimentally study test structures of more than 100 microelectromechanical systems (MEMS) beam resonators with clamped ends and residual stresses varying from highly tensile to compressive loads beyond buckling and provide experimental verification of some key theoretical results reported in the literature. We compare the theoretically predicted natural frequencies over a large range of residual stresses that make the one-dimensional micro-mechanical resonators behave like beams or strings, depending on the relative magnitude of the effective axial load and the flexural stiffness. In particular, we measure the natural frequencies of the first four modes of buckled beams to show the drastically different behavior of beams under post critical buckling load from those under tension and, for the first time, present experimental evidence of invariance of even modes to compressive residual stresses in microscale beams. We then derive the sensitivity of these modes to residual stresses and discuss the consequences of such sensitivity on sensing applications along with recommendations on how to engineer the required level of residual stresses. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aMicroelectromechanical systems. =700 1\$aDangi, A.,$eauthor. =700 1\$aPratap, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170156.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170102 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170102$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170102$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1007 =082 04$a624.15136$223 =100 1\$aPazdanowski, Michal,$eauthor. =245 10$aA Simple Method to Estimate Numerically the Residual Stresses in Bodies Subjected to Cyclic Loads /$cMichal Pazdanowski. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aResidual stresses in metallic materials may arise during the manufacturing process as a byproduct of the process itself, or they may be introduced on purpose to enhance the behavior of the product in service (for instance the compressive hoop stress in railroad vehicle wheels). Depending on the service regimen, the residual stresses in a body subjected to cyclic loads may either attain the stable (time-independent) state, thus leading to elasto-plastic shakedown of the body to the given loading program, or may not stabilize, resulting in the destruction of the body because of the ratcheting (alternating plasticity). The residual stresses in a considered body may be calculated using the standard incremental approach, where the final state is found through following step by step the actual loading program, or they may be estimated by the application of plastic shakedown theorems. The first approach, although yielding precise information on body behavior, may be extremely time consuming in the case of cyclic loads. The second approach, although yielding only an estimate of the final residual stress distributions, is much more time efficient. The numerical approach discussed in this article is based on Melan's theorem and allows for a reasonably accurate estimate of residual stresses induced in an elastic plastic body made of strain hardening material as long as an upper bound of the loading program is known. The tests performed on an autofrettage problem exhibit excellent agreement with an exact analytical solution. The results for the calculations of the residual stresses in railroad rails subjected to simulated service loads are provided. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aEngineering. =650 \0$aLoads (Mechanics) =650 \0$aMaterials. =650 \0$aSoil mechanics. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170102.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170092 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170092$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170092$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC631 =082 04$a537.6$223 =100 1\$aLobanov, Leonid M.,$eauthor. =245 10$aDevelopment of Post-weld Electrodynamic Treatment Using Electric Current Pulses for Control of Stress-Strain States and Improvement of Life of Welded Structures /$cLeonid M. Lobanov, Igor P. Kondratenko, Andriy V. Zhiltsov, Nikolai A. Pashchin, Olha L. Mikhodui. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe present work was aimed at the development of a new technological process: a post-weld electrodynamic treatment of welded joints by pulses of a high-density current. Generators of the pulse current and electrode devices, realizing the preset parameters of electrodynamic effects at single- and two-channel schemes, were designed and manufactured. The results of experimental investigations, carried out on specimens of base metal and welded joints, showed that the electrodynamic treatment has a positive effect on the structure of the treated metal and allows the residual stresses in welded joints to decrease gently, increasing their resistance to fatigue and brittle fracture as well as eliminating the distortion deformations in thin-walled elements of structures. The developed technologies and equipment gave an opportunity to perform the electrodynamic treatment of welded joints of hull structures of ships of aluminum alloy AMg6 and repair welds of an intermediate casing of the aircraft engine of heat-resistant magnesium alloy ML10, thus promoting an increase in their service reliability and life. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aElectrodynamics. =700 1\$aKondratenko, Igor P.,$eauthor. =700 1\$aMikhodui, Olha L.,$eauthor. =700 1\$aPashchin, Nikolai A.,$eauthor. =700 1\$aZhiltsov, Andriy V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170092.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170109 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170109$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170109$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA492.R6 =082 04$a621.884$223 =100 1\$aHaque, Rezwanul,$eauthor. =245 10$aResidual Stress in Self-Piercing Riveting (SPR) Joints—A Review /$cRezwanul Haque. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSelf-piercing riveting (SPR) is a high-speed method of joining sheet materials by creating a mechanical interlock between the sheets. Unlike conventional riveting, SPR does not require predrilling. Automobile industries adopted this joining technique because of its suitability in joining dissimilar materials and doing so at high-volume production. However, in SPR, the rivet plastically deforms and residual stress develops in the joint. The deformation behavior of the rivet and the residual stress distribution in SPR joints are poorly understood. This leads to difficulties in developing new product and optimizing the process. Development of new rivet and die geometries are also limited since the residual stress state in SPR joints are not fully described. Several key issues in modeling and measuring residual stress in SPR joints are discussed. How the plastically induced residual stress can be linked to the different phases of the riveting process is also described. This is an area of SPR with numerous prospects for research. It is expected that advancement will be achieved by a combination of techniques, including laboratory recreation, finite element modeling and manufacturing trials. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aRivets and riveting. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170109.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170098 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170098$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170098$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ828 =082 04$a621.45$223 =100 1\$aSmit, D. A.,$eauthor. =245 10$aThe Influence of Uneven Temperature Distributions on Local Shear and Interlaminar Fracture Toughness Properties of a Thick Composite Laminate /$cD. A. Smit, F. Lahuerta, M. Borst, R. P. L. Nijssen. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aBecause wind turbine blade length has increased over the years, so have the root and spar cap thicknesses. Temperature gradients and residual strains related to the manufacturing process of thick laminates are factors that determine the final laminate mechanical properties. The aim of this study is to investigate the manufacturing process influence on shear and fracture toughness properties for an epoxy glass fiber-reinforced polymer. Epoxy-infused laminates of 84 layers (55–60 mm) thick were manufactured. The laminate was manufactured using vacuum infusion on a single-sided mold. Thermocouples and strain gauges were embedded at different thickness positions to monitor temperature and residual strain during the curing process. The laminate was manufactured using the sublaminate technique: with the help of peel plies at different thickness positions, sublaminates were extracted and separately tested as standard coupons. Shear coupons were tested according to ASTM D7078-12, Standard Test Method for Shear Properties of Composite Materials by V-Notched Rail Shear Method, and fracture toughness double-cantilever beam coupons were tested in Mode I according to ASTM D5528-13, Standard Test Method for Mode I Interlaminar Fracture Toughness of Unidirectional Fiber-Reinforced Polymer Matrix Composites. Based on the extracted sublaminates, the relations between local curing cycles, residual strains, and the influence on the shear and fracture toughness were studied. This work reports temperature profiles and residual strain measurements that were monitored during thick laminate manufacturing. In addition, experimental data from shear and fracture toughness tests (static and fatigue) are correlated with the local residual strains and temperature measurements. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aTurbines$xBlades. =700 1\$aBorst, M.,$eauthor. =700 1\$aLahuerta, F.,$eauthor. =700 1\$aNijssen, R. P. L.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 4 Special Issue on Residual Stresses.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170098.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180038 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180038$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180038$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC183 =082 04$a530.427$223 =100 1\$aSagar, Hemant J.,$eauthor. =245 10$aExperimental and Numerical Investigation of Damage on an Aluminum Surface by Single-Bubble Cavitation /$cHemant J. Sagar, Stefanie Hanke, Martin Underberg, Chaojie Feng, Ould el Moctar, Sebastian A. Kaiser. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aFor a better understanding and modeling of cavitation, investigations of isolated single-bubble events are useful. They allow for describing and quantifying the physics of the bubble collapse and its interaction with surrounding material. The generation of such single bubbles in a liquid using an electric spark or focused laser beam is well described in the literature, and sophisticated analyses of bubble dynamics near surfaces exist. However, only a few studies addressed the material damage induced by single-bubble collapse. This article presents experiments in water, generating single bubbles with 3-mm diameters at various defined distances to the polished surface of a commercially pure aluminum specimen. The collapse of each laser-induced bubble was captured by high-speed imaging. A detailed quantitative analysis of the surface damage was performed using 3-D profilometry. A single bubble created a shallow pit with a typical depth of 1 to 2 ?m. The overall statistics of the damage parameters, such as pit depth and volume, are consistent with previous investigations. Outliers with unusually small or multiple pits can be explained by the high-speed images of the corresponding bubble collapse. The image sequences also help identify effects of the edge of the specimen surface. In addition, a complementary numerical investigation of single bubbles based on the Navier-Stokes equations was used to obtain flow characteristics near the surface, such as microjet impact and pressure. For the commercially pure aluminum used in this study, simulation and measured surface damage correlate well. The methods developed here provide a basis for studies on more complex engineering materials. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCavitation. =700 1\$aFeng, Chaojie,$eauthor. =700 1\$aHanke, tefanie,$eauthor. =700 1\$aKaiser, Sebastian A.,$eauthor. =700 1\$aMoctar, Ould el,$eauthor. =700 1\$aUnderberg, Martin,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 5 Special Issue on Cavitation.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180038.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180041 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180041$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180041$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC476.5 =082 04$a535.35$223 =100 1\$aWhitfield, Claire M. F.,$eauthor. =245 10$aCavitating Flow Luminescence as a Potential Source for Analytical Spectroscopy /$cClaire M. F. Whitfield, Michael E. Foulkes, E. Hywel Evans. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCavitating flow luminescence (CFL) has been observed for the first time at the microscale in fluid flow through a Venturi orifice. Water and mixtures of dimethyl sulfoxide and water were pumped through a Venturi orifice with a 220-?m inside diameter at flow rates between 60–100 mL min–1 to generate cavitation bubbles downstream of the Venturi restriction. Cavitation inception was observed to occur at a flow rate of 35 mL min–1 and a cavitation inception number of ?i ? 0.83. The onset of CFL emission occurred at a flow rate of 60 mL min–1 and increased with increasing flow rate through the orifice. CFL also increased with decreasing temperature and decreasing vapor pressure of the cavitating fluid. The intensity of CFL also increased when argon was present as a dissolved gas compared to untreated fluids. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aLuminescence spectroscopy. =650 \0$aSCIENCE$xSpectroscopy & Spectrum Analysis. =700 1\$aEvans, E. Hywel,$eauthor. =700 1\$aFoulkes, Michael E.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 5 Special Issue on Cavitation.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180041.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180021 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180021$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180021$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTC7 =082 04$a627$223 =100 1\$aMarcon, Andrea,$eauthor. =245 10$aAnalysis of Co-Flow Water Cavitation Peening of Al7075-T651 Alloy Using High-Speed Imaging and Surface Pitting Tests /$cAndrea Marcon, Shreyes N. Melkote, Minami Yoda, Daniel Sanders. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIt has been recently demonstrated that co-flow water cavitation peening introduces beneficial compressive residual stresses in aerospace materials. In this process, cavitation is produced in the shear layer between two concentric co-flowing water jets with a large velocity difference. Although prior studies have shown that material response is greatly influenced by the jet velocities and standoff distances used, no effort has been made to explain the observed trends by correlating the salient features of the cavitating flow with the resultant process performance. This article investigates the effect of jet velocities in co-flow water cavitation peening through high-speed imaging and surface-pitting tests on Al 7075-T651 alloy. High-speed imaging is used to determine the cavitation cloud width as a function of the inner and outer jet velocities. Results show that the observed increase in mass loss with inner jet velocity (Vin) is due to a corresponding increase in cloud width. The high-speed imaging results also highlight the trade-off between the cloud width and the cloud occurrence probability at different outer jet velocities Vout. While a lower Vout yields a larger cavitation cloud width, a higher outer flow velocity sustains the cavitation for a larger distance, resulting in more cavitation impacts on the material surface. As a result, for the range of inner jet velocities considered, an optimum value for the outer flow velocity (Vout = 11.0 m/s) is shown to exist, which is confirmed by mass loss and strip curvature measurements. Surface micropitting analysis is used to evaluate the cavitation intensities at different flow conditions. The combined pitting and high-speed imaging results explain why higher cavitation loads are produced at the optimum flow conditions of Vin = 150 m/s, Vout = 11.0 m/s, and sn = 45. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCavitation--Testing. =700 1\$aMelkote, Shreyes N.,$eauthor. =700 1\$aSanders, Daniel,$eauthor. =700 1\$aYoda, Minami,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 5 Special Issue on Cavitation.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180021.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180024 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180024$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180024$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL697.H9 =082 04$a629.135$223 =100 1\$aKazama, Toshiharu,$eauthor. =245 10$aJet Cavitation Erosion in Chamfered and Tapered Cylindrical Passages: Comparison with Visualization and Simulation /$cToshiharu Kazama, Tatsuya Noda. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn hydraulic equipment, a jet cavitation occurs frequently at points wherein oil flows through an orifice and a gap that is due to a high pressure and large pressure difference. These jets typically erode equipment surfaces when the cavitation bubbles collapse. Although the erosion characteristics have been studied for cases wherein jets impinge on surfaces at normal or oblique angles, cavitation erosion has not been studied in cases wherein jets flow parallel to the wall surfaces. This study uses the method outlined in ASTM G134-17, Standard Test Method for Erosion of Solid Materials by Cavitating Liquid Jet, to perform 8-hour-long erosion tests on aluminum specimens and to visualize cavitation jets in transparent acrylic specimens. We test specimens with chamfers and tapers in different orientations and compare the results with numerical simulations to better understand the mechanisms behind cavitation erosion. The inner walls of the chamfered specimens were partially eroded near the downstream chamfered edge, regardless of the chamfer location. During the testing time, the chamfered surfaces and outer surfaces on both ends were not eroded. Erosion pits were visible locally along the convergent and straight paths in the tapered specimen, but the pits did not appear in the divergent-tapered specimen. Visualization and numerical results offer some insights into the pressure dynamics that explain why divergent tapers seem to be effective countermeasures against cavitation erosion in hydraulic equipment. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aAirplanes$xHydraulic equipment. =700 1\$aNoda, Tatsuya,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 5 Special Issue on Cavitation.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180024.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180086 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180086$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180086$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357.5.C38 =082 04$a620.1064$223 =100 1\$aChahine, Georges L.,$eauthor. =245 10$aRecommended Procedures to Test the Resistance of Materials to Cavitation Erosion /$cGeorges L. Chahine. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (35 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPredicting cavitation erosion under full-scale operating conditions is difficult and relies on laboratory testing using accelerated methods such as ASTM G32-09, Standard Test Method for Cavitation Erosion Using Vibratory Apparatus, and ASTM G134-95, Standard Test Method for Erosion of Solid Materials by a Cavitating Liquid Jet. The main difficulty is that full-scale cavitation intensity is often unknown, and correlating cavitation field characteristics of the accelerated method and the full scale is not obvious. The problem is more acute for compliant polymeric coatings, used for protection or repair of parts subject to cavitation. Extensive testing of such materials shows that, unlike metallic surfaces, they are highly resistant to low-intensity cavitation but fail catastrophically when the intensity exceeds a certain threshold. Such behavior creates the risk of accepting a candidate coating for its resistance to cavitation if the coating was tested at a low cavitation intensity not representative of the application field conditions. This highlights the need to conduct tests with a range of cavitation intensities rather than a single intensity. This article uses results from extensive tests under various forms of cavitation to propose a generalized definition of cavitation intensity. It then presents data on the response of both metals and polymeric coatings to various levels of accelerated cavitation. A new method to test the coatings at varying cavitation intensities is then presented. Such tests provide maps of material resistance to different levels of cavitation and are helpful to make an informed decision. The tests also show that during cavitation exposure, the coatings are subjected not only to mechanical stress but also to significant heating, which dynamically modifies their properties during the exposure. Temperature rise in the coating when exposed to cavitation is directly connected to the cavitation intensity to which it is exposed, and this interaction needs to be considered. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCavitation erosion. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 5 Special Issue on Cavitation.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180086.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180027 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180027$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180027$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357.5.C38 =082 04$a620.1064$223 =100 1\$aCourt, Spencer,$eauthor. =245 10$aCavitation Erosion Performance of Steel, Ceramics, Carbide, and Victrex PEEK Materials /$cSpencer Court, Ilaria Corni, Nicola Symonds. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCavitation erosion has to be taken into consideration during material selection in many industrial sectors, e.g., offshore, marine, and oil and gas, in which components operate under severe working conditions. The cavitation erosion equipment, located at the University of Southampton, uses a vibratory apparatus to compare, rank, and characterize the cavitation erosion performance of materials. This article highlights some of the results obtained from industrial research (consultancy) work employing a Hielscher UIP1000hd 20 kHz ultrasonic transducer (Hielscher Ultrasonics GmbH, Teltow, Germany). The transducer is attached to a titanium horn to induce the formation and collapse of cavities in a liquid, creating erosion (material loss) of the specimen undergoing testing. The results from erosion cavitation testing (in accordance with ASTM G32-16, Standard Test Method for Cavitation Erosion Using Vibratory Apparatus (Superseded)) of two commercially available steels are presented herein and are shown to have less resistance to cavitation when compared to polyether(ether ketone), ceramic, and carbide materials. These materials are presented, along with Nickel 200, which was used to normalize the results. A plot of cumulative erosion versus exposure time was determined by periodic interruption of the test. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCavitation erosion. =700 1\$aCorni, Ilaria,$eauthor. =700 1\$aSymonds, Nicola,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 5 Special Issue on Cavitation.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180027.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180015 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180015$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180015$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357.5.C38 =082 04$a620.1064$223 =100 1\$aYlönen, Markku,$eauthor. =245 10$aCavitation Erosion Resistance Assessment and Comparison of Three Francis Turbine Runner Materials /$cMarkku Ylönen, Pentti Saarenrinne, Juha Miettinen, Jean-Pierre Franc, Marc Fivel, Tuomo Nyyssönen. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCavitation erosion is the most important erosion mechanism in Francis turbine runner blades. For this reason, knowledge of a material's ability to resist cavitation is important in defining how suitable it is for use in a Francis turbine. In this study, three Francis turbine materials were subjected to cavitation erosion in a high-speed cavitation tunnel. One of the materials was a low-alloy steel, and the other two were stainless steels. The cavitation tunnel produced an annular cavitation field on one face of a cylindrical specimen. The test specimens underwent cavitation erosion until the erosion had reached a maximum penetration depth of about 0.5 mm. The material surface profiles were measured at regular intervals to calculate volume and mass loss. These losses were compared to those of several other materials that had undergone the same tests with the same setup and operational parameters. The materials were compared according to their steady-state erosion rates. The steady-state erosion rate represents a material's ability to resist cavitation erosion once cavitation damage has already started to develop. The low-alloy steel eroded four times faster than the two stainless steels. One of the stainless steels tested here (Stainless steel 1) had the lowest erosion rate, along with another previously tested stainless steel. The other stainless steel (Stainless steel 2) had a slightly greater erosion rate than the first, falling into the same class as other lower-grade stainless steels and a nickel aluminum bronze alloy. The results show that in choosing a turbine blade material, stainless steels outperform nonstainless ones. The choice of which type of stainless steel to use is significant in turbines with cavitation problems. The eroded surfaces were analyzed with scanning electron microscopy in order to study the erosion mechanisms, and these studies showed that most of the damage is probably due to low-cycle fatigue. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCavitation erosion. =700 1\$aJean-Pierre Franc,$eauthor. =700 1\$aJuha Miettinen,$eauthor. =700 1\$aMarc Fivel,$eauthor. =700 1\$aPentti Saarenrinne,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 5 Special Issue on Cavitation.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180015.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180010 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180010$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180010$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA357.5.C38 =082 04$a620.1064$223 =100 1\$aSyamsundar, C.,$eauthor. =245 10$aImproved Resistance of Nanoparticle-Laden Polymer Coatings Subjected to Combined Silt and Cavitation /$cC. Syamsundar, Dhiman Chatterjee, M. Kamaraj. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHydropower generation, particularly in the Himalayan region during monsoons, suffers because of the erosion of turbine components, which is due to the high concentration of silt present in water. These high-power machines also suffer from cavitation, especially at off-design conditions. However, erosion caused by the synergistic effects of silt and cavitation can cause more serious degradation, is more complex, and remains an unsolved problem in hydraulic machines. The present work addresses this concern through the systematic study of different polymeric coatings under a controlled silt and cavitation environment. This article discusses the design and development of an experimental facility, where a specimen can be subjected to combined submerged slurry jet along with acoustic cavitation produced by a focused ultrasonic transducer. Novel polymeric coatings made of polyurethane (PU) reinforced with hard nanoparticles (B4C and SiC) of varying concentrations (from 1 to 75 weight percentage [wt. %] being defined with respect to polymer weight) are used in this work. These coatings show erosion resistance superior to the base material (16Cr-5Ni martensitic stainless steel) commonly used to make hydroturbine blades. Results are divided into three divisions. At first, we present erosion kinetics and discuss possible erosion wear mechanisms based on pure silt erosion experiments. Afterwards, pure cavitation erosion and synergistic studies of silt and cavitation studies under different experimental conditions are presented. Base material showed the maximum mass loss rate of ~22 mg/h, pure PU suffered ~9 mg/h, while nanoparticle-reinforced PU (10 wt. % B4C or 2 wt. % SiC) has a loss of ~1.5 mg/h. This shows the tremendous potential that this approach of using polymer laden with hard nanoparticles has in combating the synergetic effects of silt and erosion. The results are well-supported by detailed scanning electron microscope images and analyses to explain the reason behind the successful performance of the coatings. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCavitation erosion. =700 1\$aChatterjee, Dhiman,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 5 Special Issue on Cavitation.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180010.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170155 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170155$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170155$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTT603 =082 04$a646.2$223 =100 1\$aWang, Li-li,$eauthor. =245 10$aAnalysis of Oil Film Characteristics of Two-Axial Groove Sleeve Bearings /$cLi-li Wang, Yu-liang Wei, Guo-teng Yuan, Xing-tang Zhao, Huan Geng. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aBased on the finite finite difference method, the Reynolds equation, the flow equilibrium relationship of oil film gradient, and the oil film thickness equation are solved for different groove locations and depths in two-axial groove sleeve bearings. The oil film pressure, extent of the cavitation zone, and carrying capacity of two-axial groove sleeve bearings are computed at different oil groove locations and depths. With the increase of oil groove depth, the oil film pressure of two-axial groove sleeve bearings decreases noticeably, and the bearing capacity decreases gradually. It can be concluded that the maximum oil film pressure and bearing capacity of two-axial groove sleeve bearings are lower than that of the common sleeve bearing. With the groove position moving along the circumferential direction, the oil film pressure peak heights and bearing capacities decrease and then increase. The oil film pressure peak heights and load capacities reach maximum when the position of the two-axial oil groove is about 20° and 200°. It has been proven that different positions of oil grooves show different influences on the extent of the cavitation zone. The first oil groove is always located in the full oil film region, and the second oil groove may be located in the full oil film region or the cavitation region because of the change of distance from the convergent wedge of the bearing. The cavitation area firstly decreases and then increases with the movement of the groove in the circumferential direction. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aSleeves. =700 1\$aGeng, Huan,$eauthor. =700 1\$aWei, Yu-liang,$eauthor. =700 1\$aYuan, Guo-teng,$eauthor. =700 1\$aZhao, Xing-tang,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 5 Special Issue on Cavitation.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170155.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180008 =003 IN-ChSCO =005 20190211061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190211s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180008$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180008$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQE471.15.S25 =082 04$a552.5$223 =100 1\$aXie, Fei,$eauthor. =245 10$aNovel Pack Cementations: Alternating Current Field Enhanced Pack Cementations /$cFei Xie, Shaoqiang Xu, Jianwei Pan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2018. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThermal chemical treatments can effectively improve the surface properties of steels to resist wear, erosion, fretting, and oxidation. Among the various types of thermo-chemical treatment, pack cementation is most often employed for diffusing boron, aluminum, chromium, or silicon into the surface of steel. Pack cementation is superior to other thermo-chemical treatments in process simplicity and flexibility. However, like many other thermo-chemical treatments, conventional pack cementation (CPC) has the disadvantages of a high processing temperature and a long processing duration for obtaining a thick case. A novel approach is presented to enhance pack cementations by applying an alternating current field (ACF) on specimens and pack media. An adjustable 50 Hz alternating current power source was connected to a pair of parallel electrodes set in pack media. Investigations were conducted into the influences of the ACF on pack boriding, aluminizing, chromizing, and silicon-aluminizing. Cases' thicknesses, structures, phases, hardness distributions, and oxidation resistances were characterized with optical microscopy, X-ray diffraction, Vickers' hardness testing, and oxidation testing. These treatments can be carried out effectively at temperatures much lower than temperatures for CPC. The ACF can optimize cases' structures and phases as well as accelerate cases' growth. Brittle phases, such as iron boride and Al5Fe2, formed on a steel surface by CPC can be easily and economically avoided. The new technology can endow steels with properties that are much better than those provided by CPC. It is suggested that the ACF can enhance chemical reactions among pack agents by heating pack media and intensifying vibrations of active species. The formation, activity, and diffusion of active species containing required elements are promoted. The electromagnetic effect and the heating effect of the ACF increase vacancy concentrations in specimens, which greatly enhance diffusion in treated specimens. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed February 11, 2019. =650 \0$aCementation (Petrology) =700 1\$aPan, Jianwei,$eauthor. =700 1\$aXu, Shaoqiang,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 7, Issue 5 Special Issue on Cavitation.$dWest Conshohocken, Pa. :$bASTM International, 2018$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180008.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180030 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180030$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180030$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aLD2411.4 =082 04$a378.7543$223 =100 1\$aHernández-Morales, B.,$eauthor. =245 10$aMathematical Modeling of the Thermal Response of Laboratory-Scale Probes /$cB. Hernandez-Morales, R. Cruces-Resendez, H. J. Vergara-Hernandez. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aExperiments for cooling curve analysis of laboratory-scale quenched probes produce a wetting front that advances at a finite velocity along the longitudinal axis of the probe as cooling progresses. The wetting front velocity depends on probe material and geometry as well as the type of quenchant, its temperature, and agitation. Because of the wetting front, the mathematical model of the direct heat conduction problem to compute the evolution of the thermal field within the probe may be characterized as a moving front boundary problem. In this work, cooling curves at three subsurface locations along the length of conical-end cylindrical probes, fabricated with AISI 304 stainless steel, during quenching from 850°C with water at 60°C flowing parallel to the probe's longitudinal axis were measured. A fourth thermocouple located at the geometrical center of the probe was used to validate the model. Two values of free-stream water velocity (0.2 and 0.6 m/s) were studied. As a first approximation, the measured cooling curves were used to estimate the corresponding surface heat flux histories by solving three separate 1-D inverse heat conduction problems. Then, the thermal field evolution within the probe was computed by solving a 2-D axis-symmetrical heat transfer model. The boundary condition at the probe surface was modeled with a composite mapping of the surface heat flux histories. The surface heat flux history estimated for the lower section of the cylindrical part of the probe was applied as a boundary condition for the probe tip. It was found that the cooling curve at the lowest thermocouple position was overestimated; thus, the surface heat flux history for the probe tip was divided by 1.2 to correctly model the thermal response. The model was successfully validated by comparing measured and computed cooling curves for the thermocouple located at the probe's geometrical center. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aThermal analysis$xMathematical models. =650 \0$aThermal stresses$xMathematical models. =700 1\$aCruces-Reséndez, R.,$eauthor. =700 1\$aVergara-Hernández, H. J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180030.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180040 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180040$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180040$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.T54 =082 04$a620.1610113$223 =100 1\$aSmoljan, B.,$eauthor. =245 10$aMathematical Modeling and Computer Simulation of Steel Quenching /$cB. Smoljan, D. Iljkic, S. Smokvina Hanza, M. Jokic, L. Štic, A. Boric. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe purpose of this research is to upgrade the mathematical modeling and computer simulation of steel quenching. Based on theoretical analyses of physical processes that exist in quenching systems, the mathematical model for steel quenching is established and computer software is developed. The mathematical model of steel quenching is focused on physical phenomena, such as heat transfer, phase transformations, mechanical properties, and generation of stresses and distortions. The numerical procedure of computer simulation of steel quenching is divided into three parts: numerical calculation of transient temperature field, numerical calculation of phase change, and numerical calculation of the mechanical behaviors of steel during quenching. The numerical procedure is based on the finite volume method. Physical properties that were included in the model, such as heat conductivity coefficient, heat capacity, and surface heat transfer coefficient, were obtained by the inversion method based on the Jominy test results. By the completed algorithm, 3-D situation problems, such as the quenching of complex cylinders, cones, spheres, etc., can be simulated. The established model of steel quenching can be successfully applied in the practical usage of quenching. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aMetals$xThermomechanical treatment$xComputer simulation. =650 \0$aMetals. =650 \0$aThermal analysis$xComputer simulation. =650 \0$aThermal analysis. =650 \0$aThermochemistry. =700 1\$aŠtic, L.,$eauthor. =700 1\$aBoric, A.,$eauthor. =700 1\$aIljkic, D.,$eauthor. =700 1\$aJokic, M.,$eauthor. =700 1\$aSmokvina Hanza, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180040.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180023 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180023$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180023$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD117.T4 =082 04$a543.086$223 =100 1\$aSugimoto, Tsuyoshi,$eauthor. =245 10$aResearch for Utility of Combination Calculation Method between Heat Treatment Simulation and Computer Fluid Dynamics /$cTsuyoshi Sugimoto, Kouichi Taniguchi, Shigenori Yamada, Toshiyuki Matsuno, Masaru Sonobe, Dong-Ying Ju. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aFor vehicle drivetrain system parts such as gears, case hardening heat treatment with carburizing is well used to improve wear and rolling contact fatigue properties. However, distortion would occur during heat treatment processes, which may be a problem in improving the precision of the gear shape. Predicting distortion behavior accurately by heat treatment simulation method could help us achieve a good heat treatment quality and parts' shape accuracy. In this article, heat treatment simulation that is the predicting method from cooling situation to heat treatment distortion and computer fluid dynamics that is the predicting method from flow condition to cooling phenomena are combined. This combined method can estimate heat treatment quality on mass production treatment, especially in stable flow condition or some cooling conditions. However, especially for a continuously variable transmission pulley quenched in high-speed flow oil condition, the accuracy of heat treatment simulation is lower than other conditions. We estimated this to be the effect of turbulence generated in the flow. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aThermal analysis$xResearch. =700 1\$aJu, Dong-Ying,$eauthor. =700 1\$aMatsuno, Toshiyuki,$eauthor. =700 1\$aSonobe, Masaru,$eauthor. =700 1\$aTaniguchi, Kouichi,$eauthor. =700 1\$aYamada, Shigenori,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180023.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180012 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180012$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180012$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS183 =082 04$a670$223 =100 1\$aMaisuradze, M. V.,$eauthor. =245 10$aInvestigation and Numerical Simulation of the High Strength Silicon Steel Phase Transformations and Microstructure /$cM. V. Maisuradze, M. A. Ryzhkov. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHigh strength silicon steel implemented for manufacturing engineering products, such as aircraft components and various mining equipment, was under consideration. To obtain data for the numerical simulation of the studied steel heat treatment, the following investigations were conducted: (1) plotting of the continuous cooling transformation diagram; (2) identification of the steel microstructure constituents and the temperature ranges of their formation; (3) determination of the heat transfer coefficients of the industrial cooling media for the heat treatment (oil and still air) by the analysis of the cooling curves. The algorithm was developed for quantifying the amount of the microstructure constituents after continuous cooling to the room temperature at the rates 0.025°C/s–75°C/s. The obtained experimental data was implemented in the commercial software package to simulate the heat treatment process of the steel parts. The simulated data (microstructure distribution over the cross-section of the steel parts) was verified using the microstructure investigation of the heat-treated steel parts. A good agreement of the data was obtained. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aManufacturing processes. =650 \0$aMaterials. =650 \0$aMetal-work. =700 1\$aRyzhkov, M. A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180012.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180019 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180019$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180019$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN751 =082 04$a672.36$223 =100 1\$aMiao, Shan,$eauthor. =245 10$aOptimization Based on Orthogonal Experiment Design and Numerical Simulation for Carburizing Quenching Process of Helical Gear /$cShan Miao, Dong-Ying Ju, Yong Chen, Yi-qi Liu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPredictions of distortion and hardness after heat treatment by numerical simulation are very useful for determining the optimum condition and for controlling the distortion of machinery parts. In this article, the combination method of orthogonal experiment and numerical simulation is used to optimize the standard heat treatment condition by reducing the distortion after carburizing quenching. A helical gear made of carburizing steel 20MnCrS5 is simulated using three-dimensional coupled analysis that is based on thermo-mechanical theory. The good agreement between the experiment and simulation is verified by the comparison between the experimental data and the simulated data. Firstly, the influencing factors of distortion after carburizing quenching are investigated and discussed. Four influence factors of heat treatment are selected as follows: carburizing time, the cooling time before 860°C, the holding time at 860°C, and the gear orientation during quenching. Next, selection of the optimal case is then determined by comparing the distortions. Finally, a new optimization method of minimum distortion after carburizing quenching is provided. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aSteel$xHeat treatment. =700 1\$aChen, Yong,$eauthor. =700 1\$aJu, Dong-Ying,$eauthor. =700 1\$aLiu, Yi-qi,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180019.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170168 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170168$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170168$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN751 =082 04$a672.36$223 =100 1\$aMaisuradze, M. V.,$eauthor. =245 10$aA Novel Approach for Analytical Description of the Isothermal Bainite Transformation in Alloyed Steels /$cM. V. Maisuradze, Y. V. Yudin, A. A. Kuklina. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA novel approach for modeling the bainite transformation in alloyed steels during isothermal quenching is presented. The approach is based on the application of the logistic function with the logarithmic argument of the isothermal holding time. The proposed model involves two time-independent fitting parameters, a and b, where are specified for the given isothermal quenching temperature and other conditions (e.g., steel grade, austenite grain size, etc.). The adequacy of the modeling results is estimated using the sum of squared differences between the experimental and calculated bainite fraction formed at every time step ?? during isothermal quenching. The logistic function was found to provide a fit between the experimental and calculated bainite transformation kinetics that was up to ten times better than that of the conventionally applied Kolmogorov–Johnson–Mehl–Avrami equation. An excellent agreement is achieved between the modeling results and the experimental data for commercially produced high-strength alloyed steels 300M, HY-TUF, and D6AC isothermally quenched in the temperature range of the bainite transformation. The obtained temperature dependences of the model parameters a and b reveal the potential for further theoretical investigation and verification of their physical meaning. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aPhysical metallurgy. =650 \0$aSteel alloys$xHeat treatment. =700 1\$aKuklina, A. A.,$eauthor. =700 1\$aYudin, Y. V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170168.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180049 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180049$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180049$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ260 =082 04$a621.402205$223 =100 1\$aFried, Zoltán,$eauthor. =245 10$aParallelized Particle Swarm Optimization to Estimate the Heat Transfer Coefficients of Palm Oil, Canola Oil, Conventional, and Accelerated Petroleum Oil Quenchants /$cZoltán Fried, Imre Felde, Rosa L. Simencio Otero, Jônatas M. Viscaino, George E. Totten, Lauralice C. F. Canale. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAn inverse solver for the estimation of the temporal-spatial heat transfer coefficients (HTC), without using prior information of the thermal boundary conditions, was used for immersion quenching into palm oil, canola oil, and two commercial petroleum oil quenchants. The particle swarm optimization (PSO) method was used on near-surface temperature-time cooling curve data obtained with the so-called Tensi multithermocouple, and a 12.5 by 45 mm Inconel 600 probe. The fitness function to be minimized by a PSO approach is defined by the deviation of the measured and calculated cooling curves. The PSO algorithm was parallelized and implemented on a graphics accelerator architecture. This article describes, in detail, the PSO methodology used to compare and differentiate the potential quenching properties attainable with vegetable oils versus those attainable with accelerated and conventional petroleum oil quenchant. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aHeat$xTransmission$xMeasurement. =700 1\$aCanale, Lauralice C. F.,$eauthor. =700 1\$aFelde, Imre,$eauthor. =700 1\$aSimencio Otero, Rosa L.,$eauthor. =700 1\$aTotten, George E.,$eauthor. =700 1\$aViscaino, Jônatas M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180049.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170170 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170170$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170170$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7871.85 =082 04$a621.38152$223 =100 1\$aKobasko, Nikolai I.,$eauthor. =245 10$aPhenomena of Physics Taking Place During Hardening of Steel Parts in Liquid Media That Can Be Investigated by Lišcic/Petrofer Probe /$cNikolai I. Kobasko. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article discusses some phenomena of physics taking place during the quenching of steel parts in liquid media, such as the formation of a double surface electrical layer, poker effect, the existence of the second spike of the cooling rate during the quenching of the standard probe in salt water and alkali water solutions, and the self-regulation of the part surface temperature during the transient nucleate boiling process. A double electrical layer is conceived around the steel part surface during quenching in salt water or alkali water solutions. This layer prevents the film boiling during quenching because of electrical forces arising in it. This is a reason for maximizing critical heat flux densities. When immersing the quench probe into a salt (alkali) water solution, the probe surface temperature drops almost instantly (within 1–2 s) to the liquid boiling point and remains at this level for a relatively long time. A so-called self-regulated thermal process takes place; such a process is possible because of a significant difference between boiling and convection Biot numbers. A new quenching technology that allows for the austempering process to be performed in cold liquids is discussed in the article. It is shown that a Lišcic/Petrofer probe can be successfully used for investigations of the discovered phenomena and for controlling austempering processes in cold liquids. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aRapid thermal processing. =650 \0$aSemiconductors$xHeat treatment. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170170.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180046 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180046$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180046$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ260 =082 04$a621.402205$223 =100 1\$aMeekisho, Lemmy,$eauthor. =245 10$aAssessment of Cooling and Heat Transfer Properties of Quenchants with MATLAB /$cLemmy Meekisho, Rosa L. Simencio Otero, Jônatas M. Viscaino, D. Scott MacKenzie, George E. Totten, Lauralice C. F. Canale. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThere is ongoing interest for evaluating the potential of renewable base stocks, such as vegetable oils, to replace petroleum oils as metal quenchants. Perhaps the most critical part of this process is characterizing and comparing the cooling and heat transfer performance of potential quenchant candidates. In this work, cooling curves of two vegetable oils, palm oil and canola oil, were obtained along with a commercially available conventional and an accelerated petroleum quenchant using the so-called Tensi multiple thermocouple probe, with emphasis on the center probe emulating a small probe concept. The lumped-parameter approach was implemented in the MATLAB environment (Mathworks Inc., Natick, MA). Experimental quenching data along with temperature-dependent thermal properties for the Inconel probe material were used to quantify the cooling characteristics and heat transfer properties of two typical vegetable and petroleum oil quenchants. The results obtained exhibited a fundamental difference in the cooling characteristics between the vegetable oils and also between both vegetable oils and the petroleum oil quenchants evaluated. The focus of this article will be on the development of the computational codes and the use of MATLAB to perform these analyses. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aHeat$xTransmission$xMeasurement. =700 1\$aCanale, Lauralice C. F.,$eauthor. =700 1\$aScott MacKenzie, D.,$eauthor. =700 1\$aSimencio Otero, Rosa L.,$eauthor. =700 1\$aTotten, George E.,$eauthor. =700 1\$aViscaino, Jônatas M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180046.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180042 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180042$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180042$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC274 =082 04$a536.52$223 =100 1\$aSimencio Otero, Rosa L.,$eauthor. =245 10$aQuenchant Cooling Curves, Rewetting, and Surface Heat Flux Properties of Vegetable Oils /$cRosa L. Simencio Otero, Jônatas M. Viscaino, Jun Xu, Jianfeng Gu, George E. Totten, Lauralice C. F. Canale. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (27 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aVegetable oils are currently used for biodegradable and renewable base stocks for quenchant formulation. However, there are relatively few references relating to their true equivalency, or lack thereof, comparative to the quenching performance of petroleum oil-based quenchant formulations. To obtain an overview of the variability vegetable oil quenching performance, the cooling curves and rewetting properties were determined, and the surface heat flux properties were calculated. The vegetable oils that were studied included canola, coconut, corn, cottonseed, palm, peanut, soybean, and sunflower oils. Cooling curves were obtained using the Tensi multiple-surface thermocouple 15 mm diameter by 45 mm cylindrical Inconel 600 probe (Note: The multiple thermocouple probe was custom manufactured to conform to a drawing provided by: Heattec located at Seglaregatan 1C, 302 90 Halmstad, Sweden). For comparison, similar data was obtained with Houghto-Quench H100, a conventional (slow) petroleum quenchant oil, and Houghto-Quench HKM, an accelerated (fast) petroleum oil quenchant (Houghton International Inc., Valley Forge, PA). The results of this work will be discussed here. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aTemperature measurements. =650 \0$aThermocouples. =700 1\$aCanale, Lauralice C. F.,$eauthor. =700 1\$aGu, Jianfeng,$eauthor. =700 1\$aTotten, George E.,$eauthor. =700 1\$aViscaino, Jônatas M.,$eauthor. =700 1\$aXu, Jun,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180042.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180031 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180031$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180031$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC274 =082 04$a536.52$223 =100 1\$aHernández-Morales, B.,$eauthor. =245 10$aRevisiting the Temperature Gradient Method /$cB. Hernández-Morales, R. Cruces-Reséndez, J. S. Téllez-Martínez. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCooling curve analysis has emerged as a preferred method to characterize the cooling power of quenching media. This methodology is based on measuring the local cooling curve in a laboratory-scale probe using thermocouples. Several methods have been proposed to analyze cooling curves. Among them, the temperature gradient method (TGM) developed by Professor Lišcic uses cooling curves measured at the surface and 1.5 mm below the surface of a cylindrical probe (the Lišcic-Nanmac probe) to calculate the surface heat flux during quenching. In this work, we measured the thermal response at a location near the surface of cylindrical probes, fabricated with AISI 304 stainless steel, with two different geometries (conical- and hemispherical-end) during quenching from 850°C with water at 60°C, flowing parallel to the probe's longitudinal axis. Together with the probe geometry, the experimental matrix included two values of water velocity (0.2 and 0.6 m/s). The data was used to estimate the surface heat flux and thermal response at the probe surface by solving a one-dimensional inverse heat conduction problem (IHCP) without phase change. The TGM was then applied to re-estimate the surface heat flux using the cooling curves at the subsurface (measured) and at the surface (estimated by solving the IHCP). The surface thermal gradient computed solving the IHCP is higher and, therefore, the surface heat flux estimated solving the IHCP is also higher than the value calculated with the TGM. The hemispherical-end probe delays the rupture of the vapor film, producing low values of the surface temperature at the time of maximum heat extraction; this results in extremely high values of the heat-transfer coefficient, which precludes the use of this geometry in conjunction with the TGM. The thermal profiles are parabolic, which restricts the maximum depth at which a subsurface thermocouple may be placed to use the TGM confidently. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aTemperature measurements. =650 \0$aThermocouples. =700 1\$aCruces-Reséndez, R.,$eauthor. =700 1\$aTéllez-Martínez, J. S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180031.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180016 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180016$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180016$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS320 =082 04$a669.142$223 =100 1\$aArimoto, Kyozo,$eauthor. =245 10$aModified Prototypes of Rotary Arm–Type Test System Using a Small Ball Probe for Determination of Cooling Characteristics of Quenchants /$cKyozo Arimoto, Mitsuyoshi Shimaoka, Fumiaki Ikuta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPerformances of quenchants have been enhanced and maintained based on their cooling characteristics as determined by specific test systems. A rotary arm–type test system with a small ball probe has been developed for this purpose by making prototypes. The unique concept, derived mainly from a circular motion of a small ball probe in quenchants, was proposed by Tawara in 1941. The prototypes have been realized by current heating, measuring, and mechatronic techniques. The material used for the probe has changed from nickel alloy to platinum to resolve the discoloration and thermal aging problems on the probe surface. The performance of the prototypes has been verified by systematic tests using specific quenchants under some cooling conditions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aPlates, Iron and steel$xCooling. =650 \0$aSteelwork. =700 1\$aIkuta, Fumiaki,$eauthor. =700 1\$aShimaoka, Mitsuyoshi,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180016.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180017 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180017$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180017$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS320 =082 04$a669.142$223 =100 1\$aOuld El Moctar, Ahmed,$eauthor. =245 10$aTransient Cooling of Metallic Piece during a Quenching Process: Effect of Bath Agitation /$cAhmed Ould El Moctar, Brahim Bourouga, Benjamin Guenerie. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDuring the quenching process, metallurgical transformations and residual stress fields are controlled by the metallic piece cooling speed. It is a fact that the agitation of the bath matters, and this is why all the industrial processes use agitated baths in the quenching process. The first role of agitation is to remove the vacuum film from the vicinity of the metallic piece. This agitation should contribute to the enhancement of convective heat coefficient, but the effect of such an increase of the convection heat transfer depends on the size and properties of the metallic piece. It was shown that the cooling process is predominated by convection in the cases of massive, resistive, or massive and resistive metallic pieces (mean Biot number higher than 10). In contrast, in the cases of thin, very conductive, or thin and very conductive pieces, boiling is the main cooling phenomenon. This study will focus on the characterization of the fluid flow depending on the agitation system—a pump or a turbine. It has been observed that the flows are dramatically different in terms of velocity field and energy dissipated. The results of this study could help in the design of an agitation system, considering the metallic piece to be treated. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aPlates, Iron and steel$xCooling. =650 \0$aSteelwork. =700 1\$aBourouga, Brahim,$eauthor. =700 1\$aGuenerie, Benjamin,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180017.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180028 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180028$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180028$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS320 =082 04$a669.142$223 =100 1\$aLuo, Xinmin,$eauthor. =245 10$aEvolution from Cooling Modeling to Cooling Engineering of the Steel Quenching Process: A Technology Overview /$cXinmin Luo, George E. Totten. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (28 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe type of heat treatment process used is mainly determined by its cooling mode. Hardening is a metal heat treatment during which the most critical operation is cooling. Most quenchants used for steel hardening are vaporizable liquids, such as water, petroleum oils, emulsions, aqueous polymer solutions, or brines. Testing methodologies that include ISO 9950, Industrial Quenching Oils-determination of Cooling Characteristics-Nickel-alloy Probe Test Method, and ASTM Standards: D6200, Standard Test Method for Determination of Cooling Characteristics of Quench Oils by Cooling Curve Analysis, D6482, Standard Test Method for Determination of Cooling Characteristics of Aqueous Polymer Quenchants by Cooling Curve Analysis with Agitation (Tensi Method), D6549, Standard Test Method for Determination of Cooling Characteristics of Quenchants by Cooling Curve Analysis with Agitation (Drayton Unit), and D7646, Standard Test Method for Determination of Cooling Characteristics of Aqueous Polymer Quenchants for Aluminum Alloys by Cooling Curve Analysis, are typically used to evaluate the cooling characteristics of these quenchants or processes. The cooling time–temperature curves obtained by these methodologies traditionally involve three stages of cooling. However, the relationship between this model and heat treatment, especially between hardening theory and practice, has not been satisfactory. Therefore, it is necessary to better understand the relationship between cooling theory and metallurgical behavior to create a new cooling model that achieves zero distortion, zero dispersion of quality, and zero pollution, which are concepts proposed in the “Heat Treating Industry Vision 2020 “and the “Heat Treating Technology Roadmap 2004” by the ASM Heat Treating Society and Materials Treating Institute. The relationship between the physical metallurgical phenomenon of phase transformation of a steel workpiece during quenching after being austenitized and the actual cooling conditions in engineering practice were analyzed and discussed in this report. Additionally, the development of advanced cooling technologies and related quenching equipment are discussed. The evolution from cooling model research to cooling engineering construction represents important progress in heat treatment practice. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aPlates, Iron and steel$xCooling. =650 \0$aSteelwork. =700 1\$aTotten, George E.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180028.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180002 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180002$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180002$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS320 =082 04$a669.142$223 =100 1\$aZhang, Ke Jian,$eauthor. =245 10$aTwo New Factors Having Influence on Surface Cooling Rate of Quenched Workpiece /$cKe Jian Zhang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe cooling processes of standard probes are observed directly, and it is found that all of the measured cooling characteristic curves cannot reflect the actual cooling condition of the probe surface. To know how the surface of a workpiece is cooled, the actual cooling process of the workpiece must be observed. The quench cooling processes of samples in different shapes and sizes are directly observed and video is recorded; the causes for the observed phenomena are discussed. Then, it is found that the flow of gas in the vapor blanket and the order of transition from vapor blanket cooling to boiling cooling at different parts have considerable influences on the surface cooling rate of the workpiece and cooling uniformity of the entire workpiece, in addition to the cooling capacity of the quenching medium and effective thickness of the workpiece. The fundamental rules of these two factors are tentatively revealed. Utilizing these rules, we can aspire to regulate and control the cooling rates on different surfaces of the same workpiece in the quench cooling process. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aPlates, Iron and steel$xCooling. =650 \0$aSteelwork. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180002.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180022 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180022$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180022$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN751 =082 04$a672.36$223 =100 1\$aGarmeh, Behdad,$eauthor. =245 10$aA Study on the Effect of Austempering Temperature on Microstructure and Mechanical Properties of DIN 36CrNiMo4 Carbide-Free Nano Bainitic Steel /$cBehdad Garmeh, Masoud Kasiri-Asgarani, Kamran Amini, Hamid Ghayour. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, the effects of the austempering temperature on the microstructure and mechanical properties of carbide-free nano bainitic steel (CFB) were discussed. For the achievement of CFB 2 wt. %, silicon was added to DIN 36CrNiMo4 steel, austempered at 450°C and 300°C for 1.5 hours and 10 hours, respectively, and then quenched in oil. The microstructure was studied by optical microscope, scanning electron microscope, and X-ray crystallography. The results showed that the 300°C austempered samples contained the ferrite phase to a greater degree than the martensitic phase. The higher amounts of martensite in the 450°C austempered samples were due to the higher amounts of initial retaining austenite that transformed to martensite in oil quenching. Also, in the samples where carbide participated, there were lower degrees of the martensitic phase, and no carbides afford higher impact toughness and lower hardness for the 300°C austempered sample. As a result of the higher impact toughness in the ball mill wear test, the 300°C austempered sample has a lower weight loss than the 450°C austempered sample. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aSteel$xHeat treatment. =700 1\$aAmini, Kamran,$eauthor. =700 1\$aGhayour, Hamid,$eauthor. =700 1\$aKasiri-Asgarani, Masoud,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180022.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180007 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180007$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180007$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669.96142$223 =100 1\$aChen, Kangmin,$eauthor. =245 10$aUsing Sodium Polyacrylate Aqueous Solution to Replace Lead Bath for Patenting High-Strength Steel Rope Wire of Automobile Industry /$cKangmin Chen, Yongdong Qi, Honghong Shao, Zongke Li, Xinmin Luo. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn order to eventually eliminate the lead toxicity in the steel wire making industry and to protect our environment from pollution, a polymer quenchant, aqueous sodium polyacrylate (SPA) solution, was selected to replace the lead bath and used as a substitution quenchant in patenting of high strength and precise steel rope wire for a car window auto lifter. A series of different concentrations of aqueous SPA solution were made up, cooling curves of these solutions at different temperatures were measured, and the cooling characteristics of the quenchant were evaluated according to the requirements for high strength steel wire patenting treatment. The cooling mechanism of patenting treatment and the cooling behavior of steel wires in the different concentrations of SPA solution bath at different temperatures were systematically explored and analyzed. Then, the cold-drawn KSC72A (0.72 % carbon) steel wires were subjected to patenting treatment in the optimized concentration of the SPA solution bath. The effect of the staying time in the water bath treatment on the microstructure and mechanical properties of the steel wire was investigated by means of a scanning electron microscope, a transmission electronic microscope, and material testing machines. The results show that when the SPA solution concentration is between 5–20 %, both the cooling rate at the high temperature range and the vapor blanket breaking the temperature decrease with the bath temperature increasing. When the temperature of the SPA aqueous solution bath is between 70°C~95°C, the concentration has a barely significant effect on the cooling rate at a higher temperature range, which is needed for the sorbite transformation; however, the higher bath temperatures can make the vapor blanket stage (A-stage) maintain at 400°C. The patenting test results show that, within the designed length of the patenting bed, both the sorbite colony size and the lamella space decrease with the extension of processing time in the solution bath, and the mechanical properties (tensile strength, percentage of elongation, and reduction of area) of the steel wires do increase as the sorbite colony size and the lamella space decrease. When the KSC72A (0.72 % carbon) steel rope wires with diameters of 0.8 mm are subjected to the patenting treatment in the SPA solution bath at 90°C with the concentration of 10 %, the satisfactory metallurgical results and mechanical properties can be obtained by using a wire feed speed of 50 cm/min within the 50-cm length of the solution bath. The sorbite lamellae space and the sorbite colony size of the steel rope wires are about 82.76 nm and 2.86 ?m, respectively. The tensile strength, elongation percentage, area reduction, and micro-hardness reach 1,266 MPa, 6.4 %, 54.5 %, and 340 HV, correspondingly. This excellent combination of the mechanical properties completely meets the technical requirements of the high strength steel rope wire. Hence, the SPA aqueous solution bath can replace the traditional lead bath to be used for the patenting process of high strength steel rope wires. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aSteel, High strength. =700 1\$aLi, Zongke,$eauthor. =700 1\$aLuo, XinmiN,$eauthor. =700 1\$aQi, Yongdong,$eauthor. =700 1\$aShao, Honghong,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180007.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180033 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180033$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180033$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN775 =082 04$a669.722$223 =100 1\$aFlores, Francisco J.,$eauthor. =245 10$aAssessment of a Mist Cooling System for Aluminum Alloys /$cFrancisco J. Flores, Alberto Cantú, Imre Felde, Rafael Colás. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aWrought aluminum alloys can be heat treatable following a three-stage cycle that consists of solution, cooling, and aging. The cooling rate at which the heat-treated parts are subjected to is a critical parameter; if the rate is slow, the dissolved elements will have enough time to precipitate during cooling, affecting the mechanical properties after aging, whereas with a high cooling rate, it will be possible for pieces of the complex geometry to exhibit distortion or, in some cases, fracture. A mist cooling system prototype is presented in this work. The system was developed by mixing forced air that is produced by a blower with atomized water within. The cooling rate was measured in 6061-T6 aluminum alloy cylinders by varying the air velocity and volume of atomized water; the results were compared to cooling in still air. The temperature profiles during cooling were obtained using K-type thermocouples that gathered data from the inside and from surface locations. Cooling rates were determined by a first-order derivative of the measured temperatures, and the heat transfer coefficients (HTC) were calculated by the inverse method using 2-D transient axial symmetrical analysis with commercial software. HTC values were found in a range of 250 to 590 W/m2.K. The results showed that the HTC increased with the amount of atomized water. The HTC does not seem to be affected by the higher range values when plotted against surface temperature. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aAluminum alloys$xHeat treatment. =650 \0$aAluminum alloys. =650 \0$aMetals$xHeat treatment. =700 1\$aCantú, Alberto,$eauthor. =700 1\$aColás, Rafael,$eauthor. =700 1\$aFelde, Imre,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180033.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180070 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180070$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180070$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN672 =082 04$a671.36$223 =100 1\$aGarmeh, Behdad,$eauthor. =245 10$aComparison between Quench Tempering and Quasi Quench Partitioning Treatment on Structure and Mechanical Properties of Cr-Mo Steel /$cBehdad Garmeh, Kamran Amini. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, the microstructure and mechanical properties of chromium-molybdenum steel, which is used in mining mills as a liner, were compared after quench and tempering (QT) and quenching and partitioning (QP). Quasi QP was performed by austenitizing and quenching to the exact martensite start temperature (Ms), with the partitioning procedure at an upper temperature Ms in a furnace (common QP is done in a salt bath, so this process is called quasi QP). The procedure was characterized by optical microscopy, scanning electron microscopy, and X-ray diffraction. During the QP procedure, the bainitic ferrite is shaped, and carbon diffuses from the martensite and ferrite to the remaining austenite, but the microstructure of QT is a mixture of martensite and lower bainite. The mechanical properties were measured by a tensile test and Charpy impact test. Samples treated by QP had much higher strength and ductility than those treated by QT. The hardness and wearing weight loss of the QP process was less than QT, but the difference was not great. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aMetals$xHeat treatment. =650 \0$aMetals$xQuenching. =700 1\$aAmini, Kamran,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180070.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180051 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180051$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180051$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN672 =082 04$a671.36$223 =100 1\$aArimoto, Kyozo,$eauthor. =245 10$aStudy on Blade Curving Caused by Quenching of the Japanese Sword /$cKyozo Arimoto, Muneyoshi Iyota. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aBlade curving caused by quenching of the Japanese sword has been recognized by swordsmiths through the ages. In the late 1920s, Denzaburo Hattori noted that, based on his experimental results using cylindrical specimens, sword curving is induced not only by martensitic transformation expansion in the near-edge region but also nonuniform elastic and plastic strains distributed in this section. The presented research is an updated explanation on the subject of prepared Japanese sword (JS)-type specimens made of the same steel and by the same process as the Japanese sword, and model JS-type specimens with almost the same shape as JS-type specimens, which were machined from commercial carbon steel and austenite stainless steel bars. All specimens quenched by a swordsmith using the traditional way showed a usual curved shape with different curvatures. The curving, temperature, hardness, microstructure, and residual stress of the specimens were examined to prepare future simulation works. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aMetals$xHeat treatment. =650 \0$aMetals$xQuenching. =700 1\$aIyota, Muneyoshi,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180051.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170159 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170159$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170159$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN672 =082 04$a671.36$223 =100 1\$aPustovoit, Viktor Nikolaevich,$eauthor. =245 10$aDistortion-Free Heat Treatment of Thin Rods in Magnetic Field /$cViktor Nikolaevich Pustovoit, Yuri Vychislavovich Dolgachev. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (5 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe problem of distortion during the quenching of thin rods (shafts, rollers, sewing needles, etc.) is serious, making vital the need for straightening (often by hand). The device for the heat treatment of thin rods was developed. The use of the device avoids distortion of the rods and improves their structural characteristics. A distinctive feature of the device is the use of a constant magnetic field (intensity up to 800 kA/m). The magnetic field performs an orienting function. When the part is immersed in the hardening liquid, the magnetic field of the solenoid orients the rod vertically. This ensures the magnetic fixation of the part. In addition, the magnetic field controls the heating temperature for quenching. The device was used for heat treatment of sewing needles made of U10A (UNS T72301) steel. The needles are held vertically in the upper part of the tube furnace by means of a magnetic field. When heated to a temperature of 740°C–750°C, the steel parts lose their ferromagnetic properties and fall vertically downwards. During the fall, they are further heated to a quenching temperature of 780°C. For this purpose, the height of the furnace (in this case 1,000 mm) is specially calculated. In the quench tank, the needles are in a strictly vertical position. In addition, the effect of the magnetic field on quenching leads to an enhancement of the martensitic transformation. The dispersity of individual crystals and laths of martensite increases. The volume fraction of lath martensite in alloys with a mixed morphology is increasing. The degree of self-tempering increases. The preferential arrangement of martensite crystals in the direction of the magnetic field lines is present. Thus, the device improves the structural characteristics of thin rods and excludes their distortion. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aMetals$xHeat treatment. =700 1\$aDolgachev, Yuri Vychislavovich,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170159.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180020 =003 IN-ChSCO =005 20190525061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 190525s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180020$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180020$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN672 =082 04$a671.36$223 =100 1\$aDores, A. C. L.,$eauthor. =245 10$aDistortion Prediction in Quenching Seamless Pipes of Low-Carbon Steel /$cA. C. L. Dores, P. R. Cetlin, A. D. da Silva, P. M. A. Stemler, L. N. Soares, L. Machado. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aQuenching is an important pipe production step that can also be responsible for geometric distortions in steel parts, depending on cooling heterogeneities, thermal contractions, and changes in the steel microstructure. The quenching stage generally leads to an increase in the outside diameter (OD) of the pipes, and the prediction of the final size becomes key to assuring the quality and dimensional requirements of the product. The objective of this study was to apply simulations based on the finite element method (FEM) to water quenching in tanks to estimate the final OD of a seamless low-carbon steel pipe. This work is a first approach to developing a methodology for predicting quenched pipe distortion that depends on the process parameters used during quenching, e.g., internal and external water jets. In the available scientific literature, there are some approaches to the problem, but a consistent approach was not found, especially concerning the experimental validation of the simulation results, which is always a challenge under industrial conditions. The present research was developed in three stages: temperature measurement at several points of the pipe during the quenching process, heat transfer coefficient (HTC) calculation, and distortion calculation. The first stage was performed on an industrial scale to determine the pipe temperature distribution. Afterwards, a finite element (FE) model was set to conduct the second and third stages. The former covered the HTC prediction for inner and outer pipe surfaces using inverse analysis. Pipe distortions were predicted while taking phase transformations and deformations into account. Finally, experimental temperature profiles during heat treatment were used to predict the HTC and OD growth in the low-carbon pipes. The results of the simulations were compared with the industrial data of a quenched pipe in order to validate the methodology that was used. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 25, 2019. =650 \0$aMetals$xHeat treatment. =650 \0$aMetals$xQuenching. =700 1\$aCetlin, P. R.,$eauthor. =700 1\$ada Silva, A. D.,$eauthor. =700 1\$aMachado, L.,$eauthor. =700 1\$aSoares, L. N.,$eauthor. =700 1\$aStemler, P. M. A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 2 Special Issue in Honor of Prof. Božidar Liščić on Quenching and Control of Distortion.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180020.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180147 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180147$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180147$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP159.C3 =082 04$a620.135$223 =100 1\$aMeduri, Kavita,$eauthor. =245 10$aA Comparative Study of Carbon Supports for Pd/Au Nanoparticle-Based Catalysts /$cKavita Meduri, Arianna Rahimian, Riley Ann Humbert, Graham OBrien Johnson, Paul G. Tratnyek, Jun Jiao. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCarbon materials are promising supports for heterogeneous catalysis compared to oxide supports, such as titania, alumina, mesoporous silica, and hydrotalcite, because of their stability and relative chemical inertness. Additionally, the unique surface structures of carbon supports help control the growth, aggregation, and uniformity of the catalytic nanoparticles (NPs) hybridized with them. However, the effect of carbon supports on these NP catalysts is not well understood, affecting the optimization of this type of catalysts. In this study, palladium-gold (Pd/Au) carbon composites were systematically investigated, and the most favorable carbon support was identified. Carbon-supported Pd/Au NPs have often been favored for catalytic hydrodehalogenation (HDH) of volatile organic compounds. Hence, this study uses trichloroethylene (TCE) as model contaminant to investigate the effects of four types of carbon supportsgranular activated carbon (GAC), carbon black, graphite, and graphite nanoplateson the formation of catalytic Pd/Au NPs and their correlations to HDH reactions. Each support was chosen based on a desirable quality: GAC has a large surface area and substantial absorption capabilities, carbon black has a high surface-area-to-volume ratio and good chemical stability, graphite is the most stable form of carbon with a layered structure and thermal stability, and graphite nanoplates have large surface areas with structural stability. Characterizations of these Pd/Au-carbon composites show different NP sizes on each support, with GAC and carbon black generating smaller NPs. The HDH results suggest GAC, carbon black, and graphite nanoplates composites generate fast reaction rates. However, when comparing particle size and surface area, Pd/Au-GAC composites generate the fastest TCE degradation, providing a bigger boost to HDH rates than other types of carbon supports. More advantageously, GAC is widely available commercially with relatively low cost, and its high surface area is enabled by its high porosity, making GAC the preferred carbon support for Pd/Au NP catalyst mass production. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aCatalysts. =700 1\$aHumbert, Riley Ann,$eauthor. =700 1\$aJiao, Jun,$eauthor. =700 1\$aOBrien Johnson, Graham,$eauthor. =700 1\$aRahimian, Arianna,$eauthor. =700 1\$aTratnyek, Paul G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180147.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190089 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190089$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190089$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA685 =082 04$a691.7$223 =100 1\$aKingklang, S.,$eauthor. =245 10$aA Comparative Study of Forming and Crash Behavior of High Strength Steels /$cS. Kingklang, W. Julsri, T. Chiyatan, V. Uthaisangsuk. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAdvanced high strength (AHS) steel sheets of various grades have been increasingly used in the automotive industries because of their advantageous mechanical properties. High strength and great energy absorption are desired for a structural component design. On the other hand, large formability and strain hardening are necessary for achieving an effective forming process. To apply eligible steel grades, precise understanding of their forming and crash characteristics is needed. In this work, AHS steels with varying strengths, namely grades 780, 980, and 1180, were investigated. First, tensile tests were performed, and mechanical properties, including r -values, of the examined steels were obtained for different loading directions. The forming limit curves (FLCs) and respective forming limit stress curves (FLSCs) were determined by means of a Nakajima forming test and finite element simulation. The cyclic tension-compression tests were conducted to characterize the elastic recovery and Bauschinger effect of steels. Afterward, forming processes of an automotive part were performed, and the forming and springback behaviors of steels were evaluated by using simulations coupled with Hill48 and Yoshida-Uemori models, determined material parameters, FLCs, and FLSCs. In addition, crashworthiness of steels was numerically studied by means of a crash rectangle profile and simplified side impact pole test. The mechanical, forming, and crash performances of all the investigated AHS steels were evaluated and discussed so that the results can be applied for part design and manufacturing. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMaterials$xDynamic testing. =650 \0$aSteel, Structural. =700 1\$aChiyatan, T.,$eauthor. =700 1\$aJulsri, W.,$eauthor. =700 1\$aUthaisangsuk, V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190089.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180189 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180189$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180189$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.11$223 =100 1\$aSalari, O.,$eauthor. =245 10$aA New Criterion for Construction of Instability Maps in Hot Deformation /$cO. Salari, A. Abdi, M. Aghaie-Khafri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA new instability criterion has been developed to identify safe and unsafe regions in hot deformation of metals. The instability function takes into account both the material variable ( m ) and process variable (?, ?, , , , ) as well as the efficiency of power dissipation ( ? ). The proposed instability function is based on Narayana Murtys efficiency of power dissipation expression and can be used for a wide range of materials, including materials in which the stress-strain curve does not obey the power law. Different criteria as well as the new one were used for construction of the instability maps for the Mg-4Sn alloy, single-phase brass, and aluminum alloy AFNOR 7020. Concerning the Mg-4Sn alloy, compression tests were conducted at the temperature range of 300C500C and strain rates of 0.0011 s -1 . It has been shown that the prediction of Prasad and Narayana Murty instability criteria is more conservative than the new presented criterion. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMaterials. =700 1\$aAbdi, A.,$eauthor. =700 1\$aAghaie-Khafri, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180189.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180095 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180095$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180095$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1677 =082 04$a621.366$223 =100 1\$aBarath, V. R.,$eauthor. =245 10$aAdaptive Process Control for Uniform Laser Hardening of Complex Geometries Using Iterative Numerical Simulation /$cV. R. Barath, Manish Tak, R. Padmanaban, G. Padmanabham. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aLaser surface hardening, when applied to complex geometries, poses a challenge in the terms of obtaining uniform hardness throughout the hardened area because of variable heat sink effects. In this work, an iterative numerical approach was used to estimate the required modulation in laser power to achieve a uniform surface temperature throughout the process zone. Firstly, a transient thermal model for the lasermaterial interaction was developed using the finite element method for a rectangular spot of 85 mm. The temperature-dependent material properties were used to bring in nonlinear effects in the analysis so as to predict the hardened zone dimensions more precisely. The numerical model was validated by carrying out laser hardening experiments using a 6-kW diode laser. The validated numerical model was used with an iterative technique aided by conditional looping to achieve a uniform surface temperature during the laser hardening of the complex geometry with a variable heat sink. The developed iterative approach can be effectively used on any geometry with a variable heat sink to obtain a constant surface temperature throughout the process zone. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aLasers$xIndustrial applications. =700 1\$aPadmanaban, R.,$eauthor. =700 1\$aPadmanabham, G.,$eauthor. =700 1\$aTak, Manish,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180095.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180143 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180143$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180143$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA472 =082 04$a669.142$223 =100 1\$aGupta, G.,$eauthor. =245 10$aAn Experimental Evaluation of Mechanical Properties and Microstructure Change on Thin-FilmCoated AISI-1020 Steel /$cG. Gupta, R. K. Tyagi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aLow carbon steel AISI1020, which is a widely accepted material for industrial applications, was surface coated, and its role in enhancing endurance strength and other mechanical properties was investigated for improving performance. In this work, an experimental investigation on the effect of different types of coating processes on surface roughness, surface hardness, and endurance strength was conducted. Thin films were deposited over the surface of standard specimens by galvanizing, electroplating, and spraying techniques. Chromium, zinc, nickel, and tin were used as the coating material. It was found that optimum surface roughness, hardness, and endurance strength exist for zinc coating compared with the others under investigation. The surface roughness, hardness, and endurance strength are associated by bonding strength and a chemical bond between parent metal and coated surface. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aCarbon steel$xMetallurgy. =650 \0$aCarbon steel. =700 1\$aTyagi, R. K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180143.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180139 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180139$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180139$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA660.J64 =082 04$a671.5$223 =100 1\$aZamora Rangel, L.,$eauthor. =245 10$aAn Investigation of Dissimilar Metal Weld Joints: SB166Alloy 82/182SA182 /$cL. Zamora Rangel, J. A. Aguilar Torres, A. R. Sandoval, C. R. Arganis Jurez, L. Daz Prez, J. C. Zenteno Surez. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe alloys 82 and 182 have been widely used as filler metal to join austenitic stainless steel with alloy 600 by a shielded metal arc welding process in the reactor pressure vessel and pressure vessel nozzles, which are both components in boiling water reactors. These components are affected by interdendritic/intergranular stress corrosion cracking, usually confined to the welding metal of alloys 82 and 182. For better understanding of this effect, the heat-affected zones (HAZ) were studied. Usually, the damages are present in dissimilar metal welds along the fusion lines; this zone is susceptible to cracking. This is an important reason to research the microstructural behavior in the transition regions. For this study, specimens for dissimilar welding SB166Alloy 82/182SA182 were prepared; the physical dimensions of the specimens were 2.0 by 1.0 by 0.375 in. (5.08 by 5.54 by 0.95 cm). The welding metals were prepared as multilayer by shielded metal arc welding process using electrodes ERNiCr3 and ENiCrFe3. The microstructural characterization was realized by optical and scanning electron microscopy, including electron backscattering diffraction technique. Additionally, the Vickers microhardness profile was recorded using a Shimadzu Model HMV-G-20DT. The measurements were from the base metal and HAZ as well as the welding. The microscopy analysis shows that austenite phase is present in both base metals. The chemical compositions of different materials indicate that they correspond to the joints of alloy 600 and stainless steel (SS) 304L with alloy 82 and 182. The values of microhardness are interesting results of these joining welding. They show a slight increase in the hardness value as the measurements approached the fusion line, with the exception of the SA182 alloy. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aJoints (Engineering) =650 \0$aStructural analysis (Engineering) =700 1\$aAguilar Torres, J. A.,$eauthor. =700 1\$aArganis Jurez, C. R.,$eauthor. =700 1\$aDaz Prez, L.,$eauthor. =700 1\$aSandoval, A. R.,$eauthor. =700 1\$aZenteno Surez, J. C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180139.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180061 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180061$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180061$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA439 =082 04$a620.135$223 =100 1\$aPachideh, Ghasem,$eauthor. =245 10$aAn Investigation on the Effect of High Temperatures on the Mechanical Properties and Microstructure of Concrete Containing Multiwalled Carbon Nanotubes /$cGhasem Pachideh, Majid Gholhaki, Amin Moshtagh, Mohammadali Kafi Felaverjani. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this article, the effect of multiwalled carbon nanotubes on the properties of concrete was evaluated in the postheat-treated condition. For this, a number of cylindrical specimens (10 by 20 cm), including multiwalled carbon nanotubes in different percentages of 0.5, 1, and 1.5 % by weight of cement, were cast. Then, the concrete specimens were exposed to temperatures of 25C, 100C, 250C, 500C, and 700C in an electric furnace, and after they cooled down, compressive and tensile strength tests were carried out on them. The results show that by increasing the number of multiwalled carbon nanotubes in concrete, the compressive and tensile strengths of concrete increase up to 138 and 88 %, respectively. In addition, the dissipation of energy and modulus of elasticity of the concrete specimens were up to two times greater than those of the control specimens. The scanning electron microscope test results indicated that a strong bond between concrete particles exists at room temperature and above. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aConcrete. =700 1\$aGholhaki, Majid,$eauthor. =700 1\$aKafi Felaverjani, Mohammadali,$eauthor. =700 1\$aMoshtagh, Amin,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180061.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180164 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180164$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180164$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP986.A1 =082 04$a668.9$223 =100 1\$aShuvho, Bengir Ahmed,$eauthor. =245 10$aAnalysis of Artificial Neural Network for Predicting Erosive Wear of Nylon-12 Polymer /$cBengir Ahmed Shuvho, Mohammad Asaduzzaman Chowdhury, Uttam Kumar Debnath. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, artificial neural network (ANN) is applied to predict the erosion rate of nylon-12 polymer to ensure the accuracy of soft computing. The ANN model was developed with 4 neurons in the input layer, 10 neurons in the hidden layer, and 1 neuron in the output layer. A backpropagation algorithm was utilized in a multilayered perception. The inputs include impact velocity (m/s), impingement angle (), erodent size (?m), and stand-off distance (mm). Experimental data were used to predict the erosion rate in relation to the input parameters. The size of the erosive element of randomly shaped sand particles (silicon dioxide) is set between 300 and 600 ?m, the impact velocity between 30 and 50 m/s, the impingement angle between 30 and 90, and the stand-off distance between 15 and 25 mm. The consistency between the experimental and ANN model values, with an accuracy of 94.428 % and root mean square error of 9.729, signifies that the proposed ANN model is suitable for predicting the erosion rate of nylon-12 polymer. The prediction made using the ANN model was in good agreement with the experimental results. The ANN model can be used to estimate the maximum and total erosion rate of nylon-12 with high reliability. Therefore, this model can be applied for practical purposes. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aPolymer engineering. =650 \0$aPolymers. =700 1\$aChowdhury, Mohammad Asaduzzaman,$eauthor. =700 1\$aDebnath, Uttam Kumar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180164.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190203 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190203$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190203$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1677 =082 04$a621.366$223 =100 1\$aDobrzanski, Leszek A.,$eauthor. =245 10$aApplications of Laser Processing of Materials in Surface Engineering in the Industry 4.0 Stage of the Industrial Revolution /$cLeszek A. Dobrzanski, Anna D. Dobrzanska-Danikiewicz. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (39 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article presents a comprehensive literature study showing contemporary industrial applications of laser processing of materials in the area of surface engineering. Laser remelting, alloying, feathering, and cladding are discussed. The results of our own research on the application of laser technologies for surface treatment, including hot work tool alloy steels, high-speed steels, magnesium and aluminum alloys, are presented. The production of porous titanium microskeletons prepared using the additive selective laser sintering (SLS) method for the production of original biological engineering materials and implants-scaffolds is presented. The laser texturing of polycrystalline silicon is also presented after texturing requiring etching in alkaline solutions and preferably also after applying antireflective coatings. The article also presents the use of SLS for the application of electrical contacts on photovoltaic cells. Identification of the critical surface of engineering technologies has been presented. Attention was paid to select 21 technologies, which were included in the group of laser processing of materials, from 500 critical technologies of surface engineering that were analyzed with our own methodology of technological foresight. In order to determine the strategic position of individual groups of critical technologies, an original set of context matrices was developed, including the dendrological matrix of technology values and the meteorological matrix of environmental impact, and the results were summarized in a sixteen-field strategy matrix for technologies. A 20-year time horizon of heuristic research was established. It has been shown that the analyzed technologies of laser processing of materials are finding wider and wider application in modern technology so that their significant development in the next two decades should be expected. It has been pointed out that laser surface technologies, because of their high development potential demonstrated by the performed foresight research, are some of the important elements of the development of the Industry 4.0 idea. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aLasers$xIndustrial applications. =700 1\$aDobrzanska-Danikiewicz, Anna D.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190203.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190146 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190146$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190146$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.135$223 =100 1\$aRane, Ajay Vasudeo,$eauthor. =245 10$aAttenuated Total Reflectance Fourier Transform Infrared Spectroscopy: A Tool to Determine Reinforcement of Carbon Black in Polylactic Acid Composites /$cAjay Vasudeo Rane, Lithu Mathew, Krishnan Kanny, Sixberth Mlowe, Neerish Revaprasadu, Sabu Thomas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aInfrared spectroscopy helps in investigating the relationship existing between the structure of polymer composites and their structure-sensitive properties by determining molecular interactions. Neat polylactic acid and carbon black (0.5, 1.0, 1.5, 2.0, and 2.5 wt.%) filled polylactic acid composites were fabricated via dissolution dispersion solution casting. Composites filled with 2.5 wt.% of carbon black showed increased mechanical properties in tensile mode, in comparison to its neat and filled polylactic acid. Hence, an interest in analyzing the structure and property dependence via attenuated total reflectanceFourier transform infrared (ATR-FTIR) spectroscopy for neat polylactic acid and carbon black filled composites was felt. Analyzing ATR-FTIR spectrographs for neat polylactic acid and filled polylactic acid composites confirms strong interactions with the addition of carbon black; these interactions are at a maximum for 2.5 wt.% of carbon black. Displacement (i.e., shift), percent transmittance, and area of absorption peak in infrared spectra, confirm the strength of molecular interaction in polylactic acid composites, and are corroborated with the numerical values of the mechanical properties in tensile mode. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aPolymeric composites. =700 1\$aKanny, Krishnan,$eauthor. =700 1\$aMathew, Lithu,$eauthor. =700 1\$aMlowe, Sixberth,$eauthor. =700 1\$aRevaprasadu, Neerish,$eauthor. =700 1\$aThomas, Sabu,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190146.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180141 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180141$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180141$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.193$223 =100 1\$aRamos-Galicia, Lourdes,$eauthor. =245 10$aCarbon Nanotubes and Reduced Graphene Oxides Dimensionality Effect on Thermoset Matrix Performance /$cLourdes Ramos-Galicia, Eduardo E. Perez-Ramirez, Rosalba Fuentes-Ramirez, Ana Laura Martinez-Hernandez, Carlos Velasco-Santos. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe mechanical, electrical, thermomechanical, and thermal properties of a thermoset matrix reinforced with pristine carbon nanotubes (1-D) and reduced graphene oxide (2-D) have been evaluated. Epoxy resin was reinforced with 1-D and 2-D nanomaterials in a wide range of load for a detailed study: 0.1, 0.3, 0.5, 0.7, 0.9, and 1.0 wt. %. It is observed that carbon nanomaterials dimensionality influences its ability to transfer their unique properties to the nanocomposites. In this work, carbon nanotubes are more suitable than reduced graphene oxide to improve some properties, even though graphene-related materials have outperformed 1-D nanomaterials in other research. Tensile tests of nanocomposites show the best increment, with loads of 0.7 and 0.1 wt. % carbon nanotubes and reduced graphene oxide, respectively. Tensile strength at these loads is ~120 % higher than epoxy resin, but the load for obtaining the best mechanical performance is different for each nanomaterial. Electrical conductivity measurements show that 1-D nanostructures are able to form conductive paths better than nanosheets. In this work, carbon nanotubes yield up to three magnitude orders higher than reduced graphene oxide. The highest initial storage modulus is achieved by employing 1-D nanomaterials and contributes to improving the thermomechanical stability. Therefore, the dimensionality of carbon nanomaterials impacts the properties of nanocomposites, and each nanostructure is able to improve the matrix at different regions of the load. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aNanostructured materials. =650 \0$aNanotubes. =700 1\$aFuentes-Ramirez, Rosalba,$eauthor. =700 1\$aMartinez-Hernandez, Ana Laura,$eauthor. =700 1\$aPerez-Ramirez, Eduardo E.,$eauthor. =700 1\$aVelasco-Santos, Carlos,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180141.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180152 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180152$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180152$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS225 =082 04$a671.332$223 =100 1\$aChander, Subhash,$eauthor. =245 10$aCharacterization and Industrial Performance Evaluation of Duplex-Treated AISI H21 Die Steel during Hot Forging Process /$cSubhash Chander, Vikas Chawla. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDie/tooling failure during the hot forging process is mainly due to repeated varying mechanical loads, rigorous thermal shocks, as well as strong friction and erosion. These cause different failure mechanisms, such as wear, thermal fatigue, and plastic deformation. The enhancement of die service life for a hot forging industry is necessary now in order to be competitive globally. Four nitride coatingsTiN, TiAlN, TiCrN, and AlCrNwere deposited onto plasma-nitrided AISI H21 hot work die steel using the cathodic arc evaporation physical vapor deposition technique. The coatings were characterized by scanning electron microscope (SEM), SEMenergy dispersive x-ray spectroscopy (EDS), x-ray power diffraction (XRD), line scan EDS, and x-ray mapping tests and microhardness tester. The wear characteristics were examined using a pin-on-disk method at high temperature and speed against EN31 bearing steel disk. It was observed that the AlCrN and CrTiN coatings have lower wear rates than other coatings at high temperature (550C). Also, these coatings performed best during actual industrial practice. The enhancement in die life was reported to be 55 and 76 % in terms of parts being hot forged. The low value of the coefficient of friction for all coatings at 550C can partly be attributed to lower hardness difference between the pins and disks, decreased plastic deformation in the contact, and, consequently, less ploughing (abrasive wear action). Predominately, wear was the main die failure mode there was; when used, dies were observed microscopically. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aForging. =650 \0$aForging machinery. =700 1\$aChawla, Vikas,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180152.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180085 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180085$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180085$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.76 =082 04$a671.7$223 =100 1\$aTomlinson, Scott M.,$eauthor. =245 10$aComparison of Surface Treatments for Secondarily Bonded Joints of Marine Grade Composites /$cScott M. Tomlinson, Roberto A. Lopez-Anido. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSecondarily bonded joints will be required for large,>50 m, modularly constructed composite hull vessels, as opposed to the primary single infusion currently used in smaller hulls. The objective of this study is to characterize the experimental response of and provide documentation for the use of E-glass fiber and epoxy resin composite secondarily bonded joints fabricated using vacuum-assisted resin transfer molding and surface treatment methods common in modular marine construction. Primary single infusion benchmark joints are compared to secondarily bonded joints using four surface treatments: polyamide release-treated peel ply fabric, polyester peel ply fabric, isopropyl alcohol cleaning agent, and acetone cleaning agent. The experimental methods used to compare the surface treatment methods consist of two measuring apparent strength, single lap shear, and cleavage peel experimentation, and one measuring Mode I interlaminar fracture toughness, using the double cantilever beam experimental method. The investigation results concerning the surface treatments indicate the use of polyester peel ply over polyamide peel ply and isopropyl alcohol over acetone as a surface cleaning agent. The investigation concerning the experimentation methods indicates the acceptable use of a single-sided lap shear to determine statistically significant variations between surface treatments. Single primary infusion joints showed less variation and higher characteristic values than secondarily bonded joints. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMetals$xSurfaces. =650 \0$aProtective coatings. =700 1\$aLopez-Anido, Roberto A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180085.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190148 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190148$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190148$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.118$223 =100 1\$aBarat, K.,$eauthor. =245 10$aCompositional Optimization of a Commercially Produced Ferritic Steel Using Microstructural Heterogeneity and Mechanical Properties /$cK. Barat, G. Das, S. Bharathy, M. Ghosh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTitanium- and niobium-added medium-strength ferritic steels find widespread application in automotive industries. Carbon and nitrogen play an important role in controlling microstructure and mechanical properties of these alloys. In this study, five alloys were selected from commercial heats of the same grade. Carbon and nitrogen contents were different for them. The microstructure of steel consisted of polygonal ferrite with a small quantity of cementite. Two types of precipitates were identified. One group was coherent/semicoherent niobium carbide (NbC) of size <20 nm. Other group was incoherent titanium nitride (TiN)-NbC with size >=20 nm. The quantity of NbC precipitates primarily contributed in strengthening the mechanism and the rate of strain hardening. The quantity of complex TiN-NbC was controlled by bulk nitrogen content of steel. These incoherent carbides were responsible for the deterioration of the mechanical properties of the alloy. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aComposite materials. =700 1\$aBharathy, S.,$eauthor. =700 1\$aDas, G.,$eauthor. =700 1\$aGhosh, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190148.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180175 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180175$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180175$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1637 =082 04$a620.82$223 =100 1\$aKhazal, Haider,$eauthor. =245 10$aComputation of Fracture Parameters in Stepwise Functionally Graded Materials Using Digital Image Correlation Technique /$cHaider Khazal, Abdul Kareem F. Hassan, Wafaa Farouq, Hamid Bayesteh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis research reports the computation of the fracture parameters, namely T-stress and stress intensity factors of a stepwise functionally graded material (FGM) by using the digital image correlation technique. A five-layer epoxy/glass FGM with layers varying from pure epoxy to 60 % glass/40 % epoxy was investigated. The effects of the crack-tip positions and crack length on the nonsingular terms were analyzed. In addition, the numerical simulation of the layered FGM was investigated to further evaluate the fracture parameters. The numerical and experimental model results were compared, and good agreement was obtained between the experimental and numerical tests. Accordingly, the numerical models developed with the corresponding material properties can be used for the evaluation of fracture parameters of the developed FGM. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aDigital image correlation. =650 \0$aFinite element method. =700 1\$aBayesteh, Hamid,$eauthor. =700 1\$aFarouq, Wafaa,$eauthor. =700 1\$aHassan, Abdul Kareem F.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180175.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190020 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190020$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190020$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA485 =082 04$a620.16$223 =100 1\$aSaxena, K. K.,$eauthor. =245 10$aConstitutive Analysis of Zr-1Nb Alloy for Different Phase Regions /$cK. K. Saxena, K. Chetan, K. Vaibhav, K. V. Mani Krishna, V. Pancholi, S. K. Jha, D. Srivastava. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe hot deformation behavior of alloys that exhibit allotropy is expected to be dependent on phase/phase mixture present. Therefore, the development of a constitutive equation for finite element method (FEM) simulation of industrial hot deformation processes should consider the effect of phase/phase mixture on parameters of constitutive equation. Hot compression tests of Zr-1Nb alloy were carried out at temperatures covering single ?phase, single ?phase, and two-phase ?+?, for a range of strain rates. The stressstrain data of hot compression test were corrected for adiabatic temperature rise (ATR) at a strain rate of 1 s -1 and above. Constitutive equations were developed based on phase(s) present. Developed constitutive equations were validated by experimental flow stress data and FEM simulation. FEM simulation confirmed that the phase-wise constitutive equation provides better simulation results of the industrial extrusion process. Furthermore, the ram force profile obtained from the simulation was similar to the ram force profile of the physical extrusion experiment. Thus, by using correct phase-wise constitutive parameters in FEM simulation, the ram force for industrial hot processes can be correctly predicted. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aHeat resistant alloys$xResearch. =700 1\$aChetan, K.,$eauthor. =700 1\$aJha, S. K.,$eauthor. =700 1\$aMani Krishna, K. V.,$eauthor. =700 1\$aPancholi, V.,$eauthor. =700 1\$aSrivastava, D.,$eauthor. =700 1\$aVaibhav, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190020.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180090 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180090$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180090$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ1191 =082 04$a621.366$223 =100 1\$aSrin, K. S.,$eauthor. =245 10$aControllable Superhydrophobic Stainless Steel Surfaces Fabrication by Femtosecond Laser /$cK. S. Srin, G. Padmanabham, Ravi Bathe. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aUltrafast laser processing has emerged as important tool for micro- and nanoscale fabrications. It is also used to create self-organized microstructures with nanoscale features on surfaces. Fabrications of superhydrophobic surfaces induced by femtosecond laser have many applications that include anticorrosion, self-cleaning, and drag reduction. We created hydrophobic surfaces on stainless steel surfaces by producing a hierarchical nanomicrostructure with ultrafast laser ablation. Periodic nanomicrostructures with different topographies were fabricated on stainless steel AISI 304 surface using a femtosecond laser with a pulse duration of 100 fs and a wavelength of 800 nm. Ablation was performed in the open air with no subsequent treatment. In this study, a three-level BoxBehnken design of response surface method was used to investigate and optimize the process parameters for hydrophobic surfaces. The laser-machined hierarchical nanomicrostructures were examined using a scanning electron microscope and an opto-digital 3D microscope. The wetting of surfaces was measured in terms of the contact angle of a water droplet using a digitized goniometer. The contact angle of laser-modified surfaces was changed from a hydrophilic behavior to a hydrophobic one without any surface coatings. The effect of pulse energy was found to be significant on the output characterization. The results revealed that the average pulse energy range of 0.0350.05 mJ at 10,000 Hz with a scanning speed of 10100 mm/s and line separation of 1030 ?m produced hydrophobic surfaces with the apparent contact angle of 110135. We demonstrated a simple way to tune hydrophobicity using femtosecond laser surface modification in a single step with no subsequent post treatment. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aFemtosecond lasers. =700 1\$aBathe, Ravi,$eauthor. =700 1\$aPadmanabham, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180090.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180162 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180162$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180162$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL521.3 =082 04$a620$223 =100 1\$aBalasundar, I.,$eauthor. =245 10$aCorrelation between Microstructural Features and Tensile Properties in Near-? Titanium Alloy IMI 834 Processed in the ? + ? Regime /$cI. Balasundar, T. Raghu, B. P. Kashyap. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe mechanical properties of titanium alloys are highly sensitive to the morphology, topology, and dimensions of the ? and ? phases present in the material. An attempt has been made here to systematically evaluate the effect of heat treatment parameters, that is, solution treatment temperature and cooling rate, on the microstructure and room temperature tensile properties of a near-? titanium alloy IMI 834. Seven important microstructural features that affect the mechanical properties of a near-? titanium alloy IMI 834 processed in the ?+? regime were quantified and used to establish a direct microstructure-mechanical property correlation with the aid of artificial neural network. The established neural network has been used to evaluate and understand the effect of each individual microstructural feature on the tensile property of the material. The results obtained are presented and discussed here. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMetals$xMechanical properties. =700 1\$aKashyap, B. P.,$eauthor. =700 1\$aRaghu, T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180162.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190022 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190022$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190022$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.11$223 =100 1\$aKumar, Sumit,$eauthor. =245 10$aCritical Conditions for Dynamic Recrystallization of Hot Deformed 1 wt% Chromium - 1 wt% Molybdenum Rotor Steel /$cSumit Kumar, G. P. Chaudhari, Sumeer K. Nath. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA medium carbon 1 wt% Chromium and 1 wt% Molybdenum low-alloy steel is an important material for making of rotors of turbines. Its hot forging requires precise control of temperature, strain, and strain rate for defect-free forging. In a view of this, this steel was subjected to a hot compression test in a thermomechanical simulator, Gleeble 3800. Hot compression was carried out at temperatures of 900C, 1,000C, and 1,100C. At each temperature four strain rates, i.e., 0.001 s -1 , 0.01 s -1 , 0.1 s -1 and 1 s -1 , were used. Constitutive equations were used to analyze hot flow behavior, material constants, and activation energy. A mathematical model developed by Poliak and Jonas has been used to determine critical condition parameters like critical stress ( ?c ), critical strain (? c ), peak stress ( ?p ), and peak strain (? p ). For dynamic recrystallization (DRX), the variation of strain hardening rate up to steady state stress ( ?ss ), steady state strain (? ss ), and volume fraction of DRX (X, D, R, X, , , , , , ), with the help of Avrami-type models, have been discussed. Zener Hollomon parameters ( Z ) explained in terms of strain rate and steady state that flow stress (? ss ) has been expressed. Microstructures at different hot deformation conditions have been reported and explained. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMaterials. =700 1\$aChaudhari, G. P.,$eauthor. =700 1\$aNath, Sumeer K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190022.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190008 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190008$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190008$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.11$223 =100 1\$aHariharan, Avinash,$eauthor. =245 10$aCrystal Plasticity Study of Heterogeneous Deformation Behavior in ? Matrix Channels during High Temperature Low Stress Creep of Single Crystal Superalloys /$cAvinash Hariharan, Anand K. Kanjarla. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSingle crystal nickel-based superalloys have high temperature creep resistance due to particle strengthening by high volume fraction of coherent ? precipitates distributed within nickel-based solid solution ? matrix. In the high temperature low stress regime, published experimental studies reveal that the creep deformation mechanism during the secondary stage is predominantly by dislocation glide in the ? matrix only, and that there is a preferential motion of dislocations in the matrix, oriented in a direction perpendicular to the stress. In this work, the crystal plasticity finite element method is employed to perform creep simulations on a representative volume element in the high temperature and low stress regime. A sine-hyperbolicbased material creep model was used for the matrix, while the precipitates are assumed to be elastic. A softening model incorporating the evolution of mobile dislocation density was used to capture the transition from secondary to tertiary creep. The predicted creep curves agree well with the published experimental measurements on single crystal superalloy CMSX-4. The simulations predict a higher creep strain distribution in the horizontal channel of the matrix (perpendicular to the applied stress) as compared with the vertical channel (horizontal to the applied stress). Local creep strain distributions in the channels were found to be greater than twice their average creep strain. The results provide key insights into the distribution of macroscopic creep strain in the local channels of the ? matrix to further aid in the microstructural design of creep-resistant superalloys. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMaterials. =700 1\$aKanjarla, Anand K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190008.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190040 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190040$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190040$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.M6 =082 04$a620.18934$223 =100 1\$aBrindley, K. A.,$eauthor. =245 10$aCrystal Viscoplasticity Model of Molybdenum Including the Influence of Silicon in Solid Solution /$cK. A. Brindley, R. W. Neu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMolybdenum (Mo)-based alloys offer higher temperature capability than nickel-based superalloys. The challenge of designing these alloys is tailoring the chemistry and microstructure to achieve high-temperature strength, creep and fatigue resistance, and oxidation resistance while maintaining lower-temperature ductility and damage tolerance. Structure-properties modeling tools can be used to identify optimum microstructures. However, one missing element in this tool set is a constitutive model for the more ductile ? -Mo phase over the entire temperature range from room temperature to 1,400C. A crystal viscoplasticity model is developed for ? -Mo, including the influence of varying amounts of silicon (Si) in solid solution. The temperature, strain rate, and Si dependence of the deformation behavior needed to determine the model parameters are obtained from new compression experiments. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMolybdenum. =700 1\$aNeu, R. W.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190040.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190050 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190050$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190050$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ7 =082 04$a620$223 =100 1\$aSonkar, Suresh,$eauthor. =245 10$aDetermination of Critical Conditions for Dynamic Recrystallization of Commercially Pure Titanium /$cSuresh Sonkar, V. Pancholi, S. V. S. N. Murty. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMicrostructural evolution and mechanical properties are controlled by dynamic recrystallization (DRX) during industrial processing. To identify the critical condition for initiation of DRX, hot isothermal compression tests of commercially pure (CP)-70 titanium were conducted in a temperature range of 750C1,100C and strain rate range of 0.00110 s -1 to a true strain of 0.69. The critical condition for initiation of DRX can be identified from the inflection point on the strain-hardening rate (, ?, =, ?, ?, /, ?, ?, ), , , versus flow stress (, ?, ), , , curve. A third-order polynomial equation was fitted to the experimental ?, -, ?, , , , data to find out the inflection point. The results show that the critical stress (, ?, c, , ), , , for the initiation of DRX can be expressed as ?, c, , =, -, B, /, 3, A, , , , where A and B are the coefficients of the third-order polynomial equation. It was observed that critical stress value depends on the deformation condition. The stress-strain curve was then normalized with respect to the peak stress (, U, =, ?, /, ?, p, , , vs, ., W, =, ?, /, ?, p, , ), , , , leading to a normalized value of critical stress, (, U, c, , ), =, ?, c, , /, ?, p, , =, -, B, , /, 3, A, , , , , where A and B are the coefficients of the normalized third-order equation. The value of U, c, , (, ?, 0.95, ), , , is a constant and independent of deformation conditions. These parameters were then used to calculate the DRX fraction, and the relationship between DRX fraction and processing variables was established. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aStrain hardening$xMathematical models. =650 \0$aStrains and stresses$xMathematical models. =700 1\$aMurty, S. V. S. N.,$eauthor. =700 1\$aPancholi, V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190050.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190108 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190108$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190108$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP371.8 =082 04$a664.0288$223 =100 1\$aSharma, Jagdeep,$eauthor. =245 10$aDevelopment of Applications of Infrared Heating in Ferritic Salt Bath Nitrocarburizing Process /$cJagdeep Sharma, Balwinder Singh Sidhu, Rajesh Gupta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA rapid salt bath nitrocarburizing process technology is primarily developed by providing infrared heating instead of conventional induction heating. Two thermochemical techniques, conventional salt bath nitrocarburizing with induction heating and salt bath nitrocarburizing with infrared heating, were done on AISI 1018 low-carbon steel. The results showed that infrared heating could significantly enhance the nitrocarburizing efficiency and shorten the holding time comparing with the conventional nitrocarburizing process. Nitrocarburizing time has been shortened from 120 min to 90 min in infrared heating technique, and a more intense carbon-enriched compound layer is observed in field emission scanning electron microscope micrographs when compared to the conventional nitrocarburizing process. Energy dispersive X-ray spectroscopy analysis reveals higher weight % (1.18 %) and atomic % (2.85 %) of nitrogen in infrared-heated nitrocarburizing process specimens as compared to weight % (0.96 %) and atomic % (1.92 %) in conventional nitrocarburizing specimens. A line scan mapping of compound layer and diffusion zone was done to find out the elemental intensities and results favored by infrared heating specimens. Furthermore, an increase in microhardness was observed because of the thick and compact compound layer in infrared heating. Also, more profound diffusion zone was observed as compared to the conventional nitrocarburizing process. Further, surface roughness values have been found to be very high because of the highly porous surfaces created by the postoxidation process, and this could also be attributed to higher radiant energies from infrared heating. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aInfrared heating. =700 1\$aGupta, Rajesh,$eauthor. =700 1\$aSidhu, Balwinder Singh,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190108.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190041 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190041$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190041$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a671.52$223 =100 1\$aThirunavukarasu, Gopinath,$eauthor. =245 10$aDiffusion Bonding of Ti6Al4V and SS 304 with Nb Interlayer /$cGopinath Thirunavukarasu, Vivek V. Patel, Sukumar Kundu, Alankar Alankar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this investigation, solid-state indirect diffusion couples (IDCs) were prepared between stainless steel (SS) 304 and Ti6Al4V using a niobium (Nb) interlayer of 200 m thickness from 850C to 950C using uniaxial compressive pressure (~4 MPa) for 60 min under high vacuum of 10 -3 Pa. Microstructural analysis along the NbFOOPIPESS-304 interfaces of IDCs processed at 875C950C revealed layer-wise ironniobium-based intermetallics like Fe 2 Nb and FeNb+(Nb), apart from these reaction layers IDCs processed at 925C revealed a (Nb) reaction layer, and IDCs processed at 950C revealed both (Nb) and ? Fe+ ? reaction layers. IDCs processed at all processing temperatures revealed solid solution behavior along Ti6Al4VFOOPIPENb interfaces. Thermodynamic analysis showed that the diffusion mechanism at the Ti6Al4VFOOPIPENb interface is quite functionally easier than the diffusion mechanism observed at the NbFOOPIPESS-304 interface. Empirical atomic diffusivity ( D ) characteristics of NbFOOPIPESS-304 interface and Ti6Al4VFOOPIPENb interfaces are ~1.95710 -14 m 2 /s and ~9.19710 -14 m 2 /s, respectively, for the IDCs processed at 950C. The observed maximum hardness at the Ti6Al4VFOOPIPENb interface was ~300 HV; whereas hardness at the NbFOOPIPESS-304 interface is found to be ~200 HV and ~650 HV for IDCs processed at 850C and at 875C and above, respectively. A maximum strength of ~372 MPa (tensile) and ~241 MPa (shear), along with ~4.5 % ductility, was noticed for the IDCs processed at 875C. The presence of two reaction layers: FeNb+(Nb) and Fe 2 Nb at the NbFOOPIPESS-304 interfaces improved the strength properties of the IDCs. Strength properties of the IDCs processed at 950C deteriorated because of the presence of ? phase. Using diffraction studies, hardness property, and fracture behavior, it was established that the IDCs failed because of the propagation of crack, apparently along ironniobium-based intermetallic reaction layers at NbFOOPIPESS-304 interfaces. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aDiffusion bonding (Metals) =700 1\$aAlankar, Alankar,$eauthor. =700 1\$aKundu, Sukumar,$eauthor. =700 1\$aPatel, Vivek V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190041.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190012 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190012$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190012$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.A88 =082 04$a672.823$223 =100 1\$aDolzhenko, P.,$eauthor. =245 10$aDynamic Recrystallization in Austenitic Stainless Steel during Hot Working with Decreasing Deformation Temperature /$cP. Dolzhenko, M. Tikhonova, T. Sakai, A. Belyakov, R. Kaibyshev. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe deformation microstructures and the mechanical properties of an advanced austenitic stainless steel subjected to hot forging with a decrease in deformation temperature from 1,323 to 1,073 K were studied. The deformation microstructures were characterized by the development of dynamic recrystallization (DRX), leading to a decrease in the mean grain size from 11 to 1 ?m as temperature decreased. Two DRX mechanisms, i.e., discontinuous and continuous ones, operated concurrently during the hot compressions. Corresponding true flow stress gradually increased approaching a steady-state deformation during each compression. The grain refinement was accompanied by an increase in the dislocation density, resulting in significant strengthening. The yield strength increased from about 600 MPa to almost 1,000 MPa as revealed by tensile tests at room temperature. Both the grain-size strengthening and the dislocation strengthening contributed to the overall strength of the processed steel samples with DRX microstructures. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAustenitic stainless steel. =650 \0$aStainless steel. =700 1\$aBelyakov, A.,$eauthor. =700 1\$aKaibyshev, R.,$eauthor. =700 1\$aSakai, T.,$eauthor. =700 1\$aTikhonova, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190012.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190122 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190122$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190122$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.118$223 =100 1\$aVini, M. Heydari,$eauthor. =245 10$aEffect of Electrically Assisted Accumulative Roll Bonding (EARB) Process on the Mechanical Properties and Microstructure Evolution of AA5083/Al2O3 Composites /$cM. Heydari Vini, S. Daneshmand. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, electrically assisted accumulative roll bonding (EARB) process has been proposed and applied to produce metal matrix composite (MMC: AA5083/-1 % aluminum oxide [Al 2 O 3 ]). This process can be used to fabricate the MMCs needed in various industries such as automobile and aerospace with appropriate mechanical properties. The alloy was deformed in various electricity current levels, i.e., at 0, 100, 200, and 300 A up to six ARB cycles ( ? =4.8). The mechanical properties of the deformed material have been measured by a tensile test, Vickers microhardness test, and scanning electron microscopy. Microstructure evolution during the EARB cycles leads to improvement of the strength and elongation amount of samples. According to the results obtained, uniform dispersion of Al 2 O 3 particles improves both the strength and tensile toughness of the composites. Also, it was established that the electricity current had a significant effect on the mechanical and microstructure properties of the manufactured MMCs. High strength, low elongation, and high average Vickers microhardness were obtained for the material processed at lower current intensities. Whereas, by increasing the electricity current intensity up to 300 A, the tensile toughness and elongation amplitudes improved considerably. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aComposite materials. =700 1\$aDaneshmand, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190122.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180132 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180132$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180132$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.G65 =082 04$a620.135$223 =100 1\$aSabet, Maziyar,$eauthor. =245 10$aEffect of Graphene on Mechanical and Flowability Properties of Low-Density Polyethylene Composites /$cMaziyar Sabet, Hassan Soleimani. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe logical outline and assembly of structuralfunctional materials are progressive tendencies of materials knowledge. In this study, it was found that the homogenous graphene (Gr) spread in low-density polyethylene (LDPE) considerably increases the mechanical properties of LDPE/Gr composites. The high specific surface areas and superior properties of Gr improved thermal strength, conductivity, storage modulus, and mechanical properties of composites. Results display that the inclusion of Gr (03 wt.%) and frequency growth enhanced the viscosity, loss modulus, and storage modulus of LDPE/Gr composites significantly. The addition of Gr also augmented the Youngs modulus, Youngs strength, tensile modulus, and elongation modulus, but the tensile strength values of LDPE/Gr composites have not changed significantly. The elongation test displayed reduction values with further addition of Gr in LDPE/Gr composites. The effect of temperature rise caused the decrease in the storage modulus with Gr addition; however, further inclusion of Gr mitigated the trend of storage modulus reduction of the composites considerably. This study also presents that Gr inclusion leads to limit polymer chain mobility, which reduces maximum strain and increases the melt flow indexes during material processing. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aGraphene. =700 1\$aSoleimani, Hassan,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180132.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190026 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190026$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190026$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN731 =082 04$a620.11$223 =100 1\$aRodrguez-Calvillo, P.,$eauthor. =245 10$aEffect of Silicon on the Hot Flow Behavior of Ultra-Low Carbon Austenite /$cP. Rodrguez-Calvillo, J. Schneider, Y. Houbaert, J. M. Cabrera, R. Cols. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe influence of silicon on the high-temperature deformation behavior of ultra-low carbon austenite was studied in the range of temperature and strain rate from 1,000 to 1,100C and 0.001 to 0.1 s -1 , respectively. The flow curves of the steels exhibit the classic softening due to dynamic recrystallization. The characteristic pairs of stress-strain values (zero, critical, peak, saturation, and steady state) were determined by the analysis of the work hardening curves. These values were analyzed by applying first the classical Sellars and McTegart approach. Once the apparent stress exponents and activation energies were determined as being in the vicinity of 5 and above 270 kJ/mol, respectively, a modified hyperbolic sine equation was used. The flow curves were characterized by work hardening, dynamic recovery, and recrystallization terms at any processing conditions, showing a direct relationship with the silicon content of the steels. Finally, all the flow curves of studied steels were discussed and modeled as a function of the processing parameters and silicon content. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAustenite. =650 \0$aSilicon steel. =700 1\$aCabrera, J. M.,$eauthor. =700 1\$aCols, R.,$eauthor. =700 1\$aHoubaert, Y.,$eauthor. =700 1\$aSchneider, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190026.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180091 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180091$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180091$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1677 =082 04$a621.366$223 =100 1\$aAhmed Obeidi, M.,$eauthor. =245 10$aEffect of Surface Roughness on CO2 Laser Absorption by 316L Stainless Steel and Aluminum /$cM. Ahmed Obeidi, E. McCarthy, S. I. Ubani, I. Ul Ahad, D. Brabazon. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe roughness of a materials surface is a significant factor affecting the absorption of energy when scanned with laser beam radiation. It is a robust variable affecting the entire laser process cost and the appropriate levels for the laser processing parameters, such as the power applied. It is thus an important factor for many processes, such as laser cutting, welding, roughening, and polishing. As such, an examination of the effect of roughness on laser absorption is desirable to determine how input parameters, such as power, must be adjusted when working with different roughness and the potential power savings of roughening samples, or eliminating polishing or finishing steps, before laser processing. In this study, a comparison of the effect of the surface roughness of flat 316L stainless steel and aluminum samples on the thermal energy absorbed in laser processing was investigated. The aim was to characterize the effect and identify the potential energy savings. Samples were processed as received and either polished or roughened, such that there were five different roughness levels for each material. Individual carbon dioxide laser shots were applied with large unprocessed gaps in order to allow clear investigation of the crater depth dimensions. The width, length, and depth of the craters were measured by both scanning electron microscope and three-dimensional microscope, with larger dimensions indicating a greater absorption of the laser energy. The expected outcome of the study was confirmed, finding a noticeable improvement in the absorbed energy on the rougher surfaces for both materials, with a saving of ~62 % in the laser power applied when the aluminum surface roughness increased from 2.4 ?m to 7.03 ?m. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aLasers$xIndustrial applications. =700 1\$aBrabazon, D.,$eauthor. =700 1\$aMcCarthy, E.,$eauthor. =700 1\$aUbani, S. I.,$eauthor. =700 1\$aUl Ahad, I.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180091.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180013 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180013$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180013$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP363 =082 04$a660$223 =100 1\$aBaykal, B. Aydin,$eauthor. =245 10$aEffect of Viscosity on the Erosion-Corrosion of Steels Exposed to White Liquor Including Abrasives for Extended Time Periods /$cB. Aydin Baykal, Preet M. Singh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aErosion-corrosion is a type of corrosion in which mechanical (erosive) and chemical (corrosive) effects combine to accelerate material loss because of corrosion because of its negative impact on the reformation of a protective oxide layer on a metal surface. Erosion-corrosion has been observed in most industries that utilize alkaline streams such as pulping liquors, including the pulp, paper, nuclear, petrochemical, and pharmaceutical industries. Although erosion-corrosion research has been conducted mainly by studying the effects of changing chemical species and concentrations within the environment and mapping corrosion modes for specific alloys and environments, the mechanical properties of the electrolyte such as its viscosity have been neglected. Erosion-corrosion rate is directly related to flow characteristics such as flow regime, wall shear stress, etc., many of which are directly influenced by viscosity. Furthermore, variable viscosity is a factor in many occurrences of erosion-corrosion, notably black liquor-related corrosion in the pulp and paper industry. To understand such a system, a white liquor electrolyte was spiked with various concentrations of an inert viscosity adjusting additive (agar agar) under alkaline conditions. Corrosion rates were obtained from combinations of white liquor, alumina erodent, and agar agar using mass loss testing over 100 h of C1018 carbon steel, 316L stainless steel, and 2205 duplex stainless steel (DSS) at 60C. The results showed that higher wall shear stress resulting from a higher viscosity tended to increase the corrosion rate. Erosion-corrosion surfaces were observed using profilometry and scanning electron microscopy, revealing that higher viscosity led to more severe damage but with fewer damage sites. This indicated a lower number of critical impacts because of the higher resistance to flow but higher damage to the passive film because of higher shear stress. In the two-phase structure of 2205 DSS, preferential dissolution of ferrite was observed at a viscosity of 14.86 cP. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aEvaporators. =650 \0$aViscosity. =700 1\$aSingh, Preet M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180013.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180118 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180118$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180118$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a620.135$223 =100 1\$aShamsudeen, Shanavas,$eauthor. =245 10$aEffect of Welding on Pitting and Intergranular Corrosion Behavior of Marine Grade Aluminum Alloy /$cShanavas Shamsudeen, Edwin Raja Dhas John. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAA 5052 H32 aluminum alloy is one of the most commonly used materials in the marine environment due to its good formability, good weldability, and better corrosion resistance. Assessment of resistance of welds of the alloy against corrosion is necessary for reliable design. In the present study, pitting and intergranular corrosion behavior of tungsten inert gas (TIG), normal friction stir welding (FSW), and underwater FSW (UFSW) joints of AA 5052 H32 aluminum alloy and parent alloy are investigated. Electrochemical corrosion behavior by Tafel polarization technique and intergranular corrosion susceptibility by mass loss of the specimen in concentrated nitric acid solution are studied as per ASTM standards. The corrosion studies were conducted on welded plates for which welding parameters during TIG welding and FSW were kept optimum for maximum tensile strength. The result shows that corrosion resistance of welded joints is inferior to that of parent metals. Corrosion resistance of the FSW joint and UFSW joint are nearly equal and found to be higher compared with the TIG joint. Density and size of pits formed on the parent metal and welded joints are examined via macro- and microscopic analysis and atomic force microscopic study. Results also show that the specimens welded by FSW and UFSW processes are immune to intergranular corrosion attack. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aDissertations, Academic. =650 \0$aFriction stir welding. =700 1\$aDhas John, Edwin Raja,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180118.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180069 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180069$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180069$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS227 =082 04$a671.52$223 =100 1\$aKorra, Nanda Naik,$eauthor. =245 10$aEffect of Welding Processes on the Microstructure and Mechanical Properties of Duplex Stainless Steel Weld Joints /$cNanda Naik Korra, V. Maduraimuthu, M. Vasudevan, K. R. Balasubramanian. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe objective of the present investigation involves studying the microstructure and mechanical properties of duplex stainless steel (DSS) alloy 2205 and super DSS (SDSS) alloy 2507 weld joints fabricated by tungsten inert gas (TIG) welding and its variant, activated TIG (A-TIG) welding. Square butt weld joints were fabricated from 10-mm-thick plates of DSS and SDSS using single pass A-TIG and multi-pass TIG welding processes. The filler wire ER2209 was used for multi-pass TIG welding of DSS 2205, and ER2594 filler wire was used for multi-pass TIG welding of SDSS 2507. The microstructure in the A-TIG weld metals was found to be coarser, which was caused by high peak temperatures during A-TIG welding. The microstructures exhibited different forms of austenite, including grain boundary allotriomorphs, Widmansttten side plates, and intragranular precipitates in the weld metal. In the A-TIG weld metals, the microstructure exhibited a balanced ferrite-to-austenite ratio. The hardness values of multi-pass TIG weld joints were higher compared to A-TIG weld joints. The tensile and yield strengths of multi-pass TIG weld joints were higher compared to A-TIG weld joints, which was mainly due to higher delta ferrite content and finer microstructure. The toughness values obtained by Charpy impact testing were higher in A-TIG weld joints compared with multi-pass TIG weld joints at room temperature, which was mainly due to the balanced ferrite-to-austenite ratio in the weld microstructure. However, at subzero temperatures, the A-TIG weld joints exhibit lower impact toughness because of their coarser weld metal structure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aWelding. =700 1\$aBalasubramanian, K. R.,$eauthor. =700 1\$aMaduraimuthu, V.,$eauthor. =700 1\$aVasudevan, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180069.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180124 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180124$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180124$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.186$223 =100 1\$aShivaram, Anish,$eauthor. =245 10$aEffects of Laser Marking on Fatigue Strength of Titanium Alloys /$cAnish Shivaram, Ethan Baker, Morgan Ewing, Satya Nambu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (6 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aLaser marking is a requirement for all medical implants in the biomedical industry. The purpose is to provide permanent identification of the details of an implant, such as the part number, size, lot number, etc., in the form of laser engraving. The intent of this practice is mainly to provide the information needed to correctly identify an implant when removed from its package and before its use and, secondly, to provide the necessary information when an implant is surgically removed from a patients body to analyze the cause of removal. However, laser marking can affect the fatigue performance of an implant and create a heat-affected zone, though other factors, such as the positioning of the marking along with the laser marking parameters, can also play a significant role. The improper choice of laser marking parameters can induce high residual stresses on the implant. High tensile residual stresses can result in fracture at the marking region, and hence, compressive or low tensile residual stresses are desired. Therefore, the objective of this study was to evaluate the effect of various laser marking parameters on the residual stresses and fatigue strength of titanium alloy. Laser marking parameters, such as power and pulse speed, were varied and residual stresses were calculated using the X-ray diffraction technique. Heat-affected zones were imaged using a digital microscope. Finally, four-point bend tests were conducted to evaluate the fatigue strength for samples with different laser parameters. The results from the testing demonstrated that laser parameters can have a significant impact on the tensile or compressive residual stresses. Laser-marked samples also showed a reduction in fatigue strength as compared to nonlaser-marked samples. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAluminum alloys$xMechanical properties. =650 \0$aAluminum castings. =700 1\$aBaker, Ethan,$eauthor. =700 1\$aEwing, Morgan,$eauthor. =700 1\$aNambu, Satya,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180124.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190062 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190062$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190062$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL521.3 =082 04$a620$223 =100 1\$aTun, Khin Sandar,$eauthor. =245 10$aEnhanced Tensile Properties and Reversal of Tension-Compression Asymmetry of Magnesium Reinforced with High Entropy Alloy Particles /$cKhin Sandar Tun, Manoj Gupta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, an attempt was made to develop magnesium-based composites containing a new type of reinforcement, ball-milled high entropy alloy (HEA) particles. The presence and variation in the amount of ball-milled HEA particles (2.5 wt. %, 5 wt. %, and 7.5 wt. %) in pure magnesium matrix and their effect on the microstructure and tensile properties of magnesium-HEA composites were investigated. HEA particle reinforcement triggered the particle-stimulated nucleation that effectively led to a significant reduction of matrix grain size in the composites. The yield and ultimate tensile strength were improved in magnesium-HEA composites. The reorientation of basal planes in recrystallized grains provided the random texture in the composites as compared to that of pure magnesium. The outcome of randomization of texture was the reduction in tension-compression yield asymmetry in the range of 0.931 in the case of composites. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMetals$xMechanical properties. =700 1\$aGupta, Manoj,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190062.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190135 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190135$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190135$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.P58 =082 04$a620.192$223 =100 1\$aRaja, Thandavamoorthy,$eauthor. =245 10$aEvaluation of Thermal Stability and Thermal Properties of Neem/Banyan Reinforced Hybrid Polymer Composite /$cThandavamoorthy Raja, Palanivel Anand. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThermal insulation materials are used to increase the efficiency of many structural and heat-resistant applications. A sawdust-filled alkali-treated Neem/Banyan hybrid composite is prepared and its behaviors of thermal stability, short-term heat resistance, thermal expansion, and thermal conductivity are examined by conducting Thermogravimetric Analysis (TGA) and a thermal conductivity test. The hybrid composite is prepared by hand layup technique, using an epoxy matrix blended with sawdust as the matrix and varying the weight fraction of the Neem/Banyan fibers as reinforcement for fabrication of hybrid composites. The weight fractions of five composite samples of Neem/Banyan fibers are 90/45, 90/60, 45/45, 60/90, and 45/90 (in grams), respectively. The mass loss of fabricated composite laminates due to temperature has been investigated through TGA. Sample A gives an initial deformation from a mass of 11 mg to 10.9 mg at a 330C temperature and a maximum working temperature of 427C during mass at 25 % of hybrid composites. The material can withstand up to 25 % of the mass of the hybrid composite after this mass of 2.75 mg moves to degrade hybrid composites. Therefore, the percentage efficiency of the hybrid composite is 75 % of the mass, giving working conditions of hybrid composites. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aComposite materials. =650 \0$aPolymeric composites. =700 1\$aAnand, Palanivel,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190135.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180190 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180190$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180190$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7871.15.S56 =082 04$a621.38152$223 =100 1\$aGao, Chao,$eauthor. =245 10$aExperimental Investigations of Drilling Silicon Carbide Using Brazed Diamond Tools /$cChao Gao, Guangzhao Liu, Hui Wang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article mainly studied the machining efficiency and service life of a brazed diamond tool for drilling silicon carbide (SiC). Firstly, the influence of process parameters (spindle speed [ss], axial pressure [ap], feed rate [fr]) on the drilling efficiency was researched. Then, the orthogonal analysis was carried out to study the influence of tool structural parameters (wall thickness of tools [wtt], diamond grit size [dgs], working layer thickness [wlt], and outer diameter of tools [odt]) on the drilling efficiency and tool life. Eventually the effects of solder composition on the drilling performance were investigated. The results show the following: (1) the optimal drilling efficiency can be obtained under the condition of ss of 83? rad/s, ap of 800 N, and fr of 4/100? mm/rad. (2) The influence degree of tool structure on the drilling performance is wtt>dgs>wlt>odt; the optimal tool structural parameters are wtt of 1 mm, dgs of 250 ?m, odt of 10 mm, and wlt of 0.8 mm. (3) For SiC ceramics prepared by hot pressing and hot isostatic pressure sintering, diamond tools with nickel-chromium alloy solder should be chosen; whereas for SiC ceramics prepared by pressure-free and reactive sintering, diamond tools with copper-based solder should be chosen. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aSilicon carbide. =700 1\$aLiu, Guangzhao,$eauthor. =700 1\$aWang, Hui,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180190.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180134 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180134$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180134$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.95 =082 04$a671$223 =100 1\$aAndreassen, Michael Joachim,$eauthor. =245 10$aExperimental Study of Residual Stresses in Hybrid Laser Arc and Submerged Arc-Welded 10-mm-Thick Low-Carbon Steel Plates /$cMichael Joachim Andreassen, Zhenzhen Yu, Jeffrey R. Bunn, Jens Henrik Nielsen. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aOffshore structures are constantly exposed to a multihazard marine environment that threatens their structural integrity. This imposes a high risk for extensive structural failures while various deterioration mechanisms may degrade the available capacity of the structures. Thus, no reliable decisions can be reached regarding design, operation, and survivability of the structures unless a deep comprehension of their fatigue performance is available, including welding-induced residual stresses. In particular, the continuous increase in size of the weldments for the offshore wind industry needs special attention with regard to welding-induced residual stresses, as they can reduce fatigue life, promote distortion, and contribute to stress corrosion cracking. Thus, the current design methods and increased structural dimensions as well as new design and manufacturing methods need to be inspected, understood, and optimized. Related to this, there is a growing need for evaluation of the effect of welding methods with various heat input density distributions. This article deals with the influence of welding method on the welding-induced residual stresses in 10-mm-thick low-carbon structural steel plates. The residual stresses are investigated in hybrid laser-arc welded and submerged arc butt-welded steel plates by means of experimental temperature profile measurements and neutron diffraction measurements and in accordance with existing production procedures. The residual stresses were measured at three different depths in the plates. The goal of the analysis is to gain a comprehensive understanding of the distribution and development of residual stresses in relation to the welding method for better control of the residual stresses and distortion. The repeatability of the neutron diffraction measurements is also investigated and reported in this article. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aElectric welding. =650 \0$aLaser arc welding. =700 1\$aBunn, Jeffrey R.,$eauthor. =700 1\$aNielsen, Jens Henrik,$eauthor. =700 1\$aYu, Zhenzhen,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180134.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180165 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180165$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180165$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP965 =082 04$a664.26$223 =100 1\$aGunasekaran, Harish,$eauthor. =245 10$aFabrication and Characterization of Gelatin/Carbon BlackBased Scaffolds for Neural Tissue Engineering Applications /$cHarish Gunasekaran, Aurora De Acutis, Francesca Montemurro, Carmelo De Maria, Giovanni Vozzi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aNeural tissue engineering has recently emerged as an alternative strategy to repair nerve damage and promote nerve regeneration. It involves the fabrication of scaffolds with properties mimicking those of the natural extracellular matrix for guiding a three-dimensional (3D) neural regeneration. These engineered constructs, in addition to mechanical support, should be also capable of providing proper chemical and electrical stimuli for adhesion, migration, and proliferation of the neural cells. In this study, we developed conductive composite hydrogel films based on gelatin and carbon black (CB) as scaffolds for neural tissue engineering applications. The presented hydrogel constructs were fabricated in the form of films using the solvent casting method after dispersing several concentrations of CB in a 5 % (w/v) gelatin solution along with (3-glycidoxypropyl)trimethoxysilane (GPTMS) as the crosslinking agent at a concentration of 1.84 % (v/v). The CB concentrations of 0.3 %, 0.5 %, 0.7 %, and 0.9 % (w/w) with respect to the gelatin amount were chosen. The morphological, compositional, swelling, dissolution, electrical, mechanical, and wettability properties together were characterized as function of CB content and compared with those of pure gelatin-based hydrogel. Results demonstrated that the incorporation of different quantities of CB relatively reduced the water uptake capability of the films and increased the stability in water of the gelatin matrix. Findings from the mechanical tests revealed that composite hydrogels have a lower elastic modulus with respect to the pure gelatin matrix. Moreover, it was found that the incorporation of incremental CB concentrations kept the wettability surface property unchanged while the electrical characterization of the proposed structures showed a reduction of the electrical impedance. Overall, the study suggests that the composite structures could be used as a potential candidate for fabrication of scaffolds for neural regeneration with tunable electrical and mechanical properties by varying the CB concentration in a finite range. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aGelatin industry. =700 1\$aDe Acutis, Aurora,$eauthor. =700 1\$aDe Maria, Carmelo,$eauthor. =700 1\$aMontemurro, Francesca,$eauthor. =700 1\$aVozzi, Giovanni,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180165.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180171 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180171$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180171$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL521 =082 04$a620.82$223 =100 1\$aBere, Paul,$eauthor. =245 10$aFabrication and Mechanical Characterization of Short Fiber-Glass Epoxy Composites /$cPaul Bere, Mircea Dudescu, Calin Neamtu, Ovidiu Nemes, Catalin Moldovan, Mihaela Simion. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this article, the epoxy-based composites were developed by combining the short E-glass fibers into epoxy matrix. The fiber content in the composite was varied from 0.05 to 0.40 by weight fraction, and the variation of mechanical properties, such as tensile, flexural, impact, and hardness properties, in each case, were investigated. Chemical analyses of the constituents by X-ray spectroscopy and a microstructural analysis of the fracture area complete the mechanical tests. The obtained results show that although ultimate tensile strength and flexural strength of the composites decreased with increasing fiber content, Youngs and flexural moduli increased. The reduction in the failure strain is caused by an embrittlement effect as the stiffness of the composites is improved when the fiber weight fraction is increased. In the investigated glass fiber volume fraction range, the notched Charpy impact energy of composites increases with an increase of the glass fiber volume fraction. The morphological analysis of the tensile fracture surfaces of the composites observed using scanning electron microscopy brings an important clarification that explains the obtained behavior. The micromechanics analysis of behavior of epoxy composites reinforced with short glass fibers was performed using Digimat 6.0 software, and the obtained results of Youngs modulus revealed a good convergence of the calculated and measured values. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aFibrous composites$xTesting. =700 1\$aDudescu, Mircea,$eauthor. =700 1\$aMoldovan, Catalin,$eauthor. =700 1\$aNeamtu, Calin,$eauthor. =700 1\$aNemes, Ovidiu,$eauthor. =700 1\$aSimion, Mihaela,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180171.htm =LDR 03762nab 2200553 i 4500 =001 MPC20170136 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20170136$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20170136$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.38 =082 04$a620.166$223 =100 1\$aSharma, Rahul,$eauthor. =245 10$aFatigue and Static Properties of Built-up Friction Stir Welded Ti-6Al-4V I-Beams /$cRahul Sharma, Damon R. Fick, Michael K. West, Bharat K. Jasthi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aModern aircraft systems use high-strength alloys, such as Ti-6Al-4V (Ti-6-4), for their components. The advantage of using Ti-6-4 is its high corrosion resistance and low weight to strength ratio when compared with other metals. The downside of using titanium is its high cost and lead time associated with procurement in addition to the material wastage that occurs with machining different cross-sectional geometries. Built-up titanium beams fabricated using friction stir welding (FSW) and readily available titanium plates may be a viable alternative that reduces these expenses. This study investigates the fatigue and static strengths of built-up titanium I-beams using FSW and 7-mm-thick Ti-6-4 plate material and compares the results with strengths of representative coupon specimens. Coupons in the transverse and longitudinal directions of the FSW were evaluated for both polished and as-welded FSW surfaces. The results of the investigation showed that the static flexural strength of the built-up I-beam reached 57 % of the yield strength of the Ti-6-4 plate material. The fatigue strengths of the two I-beams tested reached 87 and 63 % of comparable coupon-level specimens with as-welded and polished finishes, respectively. Failures in these beams initiated at discontinuities in the welded fillet region, which suggests that strength and fatigue performance of built-up titanium I-beams can be improved through more consistent FSW methods for Ti-6-4 plate materials. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMetals$xEffect of high temperatures on. =650 \0$aMetals$xFatigue. =700 1\$aFick, Damon R.,$eauthor. =700 1\$aJasthi, Bharat K.,$eauthor. =700 1\$aWest, Michael K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20170136.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180148 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180148$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180148$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA356 =082 04$a624.176$223 =100 1\$aGolpayegani, Iman Fakhari,$eauthor. =245 10$aFinite Element Vibration Analysis of Variable Thickness Thin Cylindrical FGM Shells under Various Boundary Conditions /$cIman Fakhari Golpayegani, Ehsan Mohammadi Arani, Ali Asghar Foroughifar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis research aimed to study the analysis of free vibrations of cylindrical shells made of functionally graded materials (FGMs). The studied shells were thin and had been selected in a way that their thickness varies linearly along the length. A combination of different boundary conditions was applied, and vibrational analysis was performed through finite element method. Then, the effects of different parameters, including varying thickness along the length, shell length, and radius, on the frequency behavior of the shell were extracted. Afterward, the frequency behaviors of the shells made of different materials were compared. The numerical results obtained in this article have been verified by the results derived from the analytical relations of previous research, which indicated the high accuracy of the finite element method for the vibrational analysis of the shells with variable thickness. The analysis indicated significant effects of thickness changes and boundary conditions on the natural frequencies. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aFinite element method. =650 \0$aVibration. =700 1\$aArani, Ehsan Mohammadi,$eauthor. =700 1\$aForoughifar, Ali Asghar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180148.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180179 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180179$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180179$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a671.52$223 =100 1\$aDragatogiannis, Dimitrios A.,$eauthor. =245 10$aFriction Stir Welding between 6082 and 7075 Aluminum Alloys Thermal Treated for Automotive Applications /$cDimitrios A. Dragatogiannis, Dimitrios Kollaros, Panagiotis Karakizis, Dimitrios Pantelis, Jianguo Lin, Costas Charitidis. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe automotive industry demands ecofriendly manufacturing processes and lightweight structures and materials to reduce CO 2 emissions and decrease weight and fuel consumption while optimizing overall performance. Aluminum alloys in the 7xxx and 6xxx series offer high potential for weight reduction in automotive and other transportation industries. 7xxx aluminum alloys have the best strength performance among all commercial aluminum alloys. Alloys in the 6xxx series generally have medium-to-high strength, high corrosion resistance, and good formability. Alloys in both the 7xxx and 6xxx series are strengthened by heat treatment. The increased strength-to-weight ratio and the thermal treatment processing open the possibility to use these alloys as possible alternative materials instead of steel in the automotive industry for the fabrication of car body parts. However, their poor formability and weldability are the main drawbacks when these alloys are considered as substitutes of steel and other dissimilar joints during the fabrication of car body parts and the production chain. Recently, Hot Forming and in-die Quenching (HFQ), a patented hot stamping process, has been introduced to manufacture complex-shaped high-strength heat-treatable aluminum alloys. The work described in this article is an experimental investigation of the weldability between AA6082 and AA7075 by Friction Stir Welding (FSW) that considers thermal treatments used during HFQ for automotive applications. The aforementioned FSW base metals, 6082 and 7075, are heat treated according to the solution heat treatment adopted during HFQ to evaluate the effect of the HFQ thermal cycle on the quality of the produced joints. Optical microscopy has been used to characterize the microstructure of the produced joints. The defect-free welded joints are characterized by good mechanical mixing between the joined materials as well as by grain refinement. The mechanical behavior of the produced welded joints was studied and compared with the parent materials, whereas the measured mechanical properties are correlated with the microstructure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aFriction welding. =650 \0$aPressure welding. =700 1\$aCharitidis, Costas,$eauthor. =700 1\$aKarakizis, Panagiotis,$eauthor. =700 1\$aKollaros, Dimitrios,$eauthor. =700 1\$aLin, Jianguo,$eauthor. =700 1\$aPantelis, Dimitrios,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180179.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180116 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180116$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180116$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a671.52$223 =100 1\$aShashi Kumar, S.,$eauthor. =245 10$aFriction Stir Welding of AISI 316L Stainless Steel in a 3.5 NaCl Aqueous Solution: Metallurgical and Mechanical Characterization /$cS. Shashi Kumar, N. Murugan, K. K. Ramachandran. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSubmerged friction stir welding (SFSW) was employed for joining AISI 316L stainless steel sheets. The effect of submerged friction stir welding on the metallurgical and mechanical properties of the weld joints was studied by varying tool rotational speed from 600 to 1,400 r/min, in steps of 400 r/min with other constant process parameters (welding speed of 55 mm/min, axial force of 12 kN, and tool tilt of 1.5) in an artificially prepared 3.5 sodium chloride aqueous solution chamber. Characterization studies, such as scanning electron microscopy and electron backscattered diffraction, were used for studying the microstructural studies of the weld zone. The results of the experimental analysis reveal that the SFSW joints exhibited overall better joint strength, and the weld made at 1,000 r/min was superior in terms of strength and microstructural features to that of the base steel. The pitting corrosion behavior of the base steel and the weld joints depicts a stable pitting potential with no active passive behavior, in which the pitting corrosion resistance of all weld joints was marginally higher, especially the weld joint made at 1,000 r/min, which was superior to that of the base steel. The existence of the secondary precipitates was ruled out in all the cases, owing to lower peak temperatures and continuous (fast) cooling of the weld zone. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aFriction welding. =650 \0$aPressure welding. =700 1\$aMurugan, N.,$eauthor. =700 1\$aRamachandran, K. K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180116.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190084 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190084$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190084$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN672 =082 04$a671.36$223 =100 1\$aZhang, Kejian,$eauthor. =245 10$aHolistic Problem of Cooling Effect of Vertically Oil-Quenched Shaft-Type Workpiece /$cKejian Zhang, Shui Wang, Xuezhi Hao. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDuring the process of vertical oil quenching, the sides of a shaft with the same effective thickness often do not obtain the same quench cooling effect. Therefore, the quench cooling effect of such workpieces can only be described with the distribution of measured values on the whole surface instead of measured values at individual spots. This is the holistic problem of the quenching effect of such workpieces. The main hazard caused by this type of holistic phenomenon is the creation of serious and regular uneven longitudinal quenching hardness, from inside out on the shaft. The holistic problem is caused by two factors: (1) the gas flow within the vapor blanket and (2) the order of the transition of vapor blanket to nucleate boiling on the surface of the workpiece. Through experimental observation, analysis, and inference, a general model is summarized for the holistic problem of workpieces with shafts of different lengths in the quenching process. By using the general model and the law disclosed by it, a new technique is developed to solve the holistic problem of the workpieces. With the new technique, higher and more uniform quenching hardness can be achieved, the quenching period of the workpiece can be shortened substantially, and steels with lower hardenability can be used to make the workpieces and achieve the same hardening effect. Moreover, oil quenching can replace induction quenching and achieve the same case hardening effect. By comparing the characteristics of the holistic problem and the distortion problem of workpieces in quenching, we arrived at two inferences: (1) quenching distortion and the holistic phenomenon have the same driving factors and (2) quenching distortion is just one of the detriments caused by the holistic problem. Therefore, the quenching distortion problem of most workpieces can be solved by the angle of their holistic problems. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMetals$xQuenching. =700 1\$aHao, Xuezhi,$eauthor. =700 1\$aWang, Shui,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190084.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190014 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190014$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190014$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.11$223 =100 1\$aRahul, M. R.,$eauthor. =245 10$aHot Deformation Behavior and Microstructural Characterization of CoCrFeNiNb0.45 Eutectic High Entropy Alloy /$cM. R. Rahul, Sumanta Samal, Gandham Phanikumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn recent years, several multicomponent alloys of near equiatomic composition (also known as high-entropy alloys) with excellent mechanical properties have been developed. In this study, a eutectic high entropy alloy, CoCrFeNiNb 0.45 , was chosen for a hot deformation study. The alloy consists of a primary face-centered cubic (FCC) phase (CoCrFeNi rich) and a eutectic region between the FCC and Laves phase (Co 2 Nb type). The combination of FCC and eutectic region is expected to provide better strength and ductility. Hot compression tests were carried out at different strain rates of 0.001, 0.1, 1, and 10 s -1 with varying temperatures of 1,073, 1,173, 1,273, and 1,323 K. The optimum processing window was identified by plotting processing maps, and the instability region was verified using multiple parameters. Constitutive equation relating stress, strain rate, and temperature is established. The optimum processing condition was correlated with the microstructural characterization, and instability was characterized with cracks on the specimen. Finite element simulation was carried out, taking the flow curve as input and correlating the strain field distribution with the microhardness variation. These studies are intended to contribute to an integrated computational materials engineering approach to developing these alloys toward a product. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMaterials. =700 1\$aPhanikumar, Gandham,$eauthor. =700 1\$aSamal, Sumanta,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190014.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190019 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190019$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190019$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.11$223 =100 1\$aPramanik, Sudipta,$eauthor. =245 10$aHot Deformation Behavior of Fe-6.8Al Low-Density and AISI 1040 Steels /$cSudipta Pramanik, Tushar S. Pund, G. S. Avadhani, Satyam Suwas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSteels are the traditional choice for automobile bodies due to their low cost and good combination of strength, ductility, and formability. Aluminum-containing low-density steels have recently been materials of immense attention due to the quest for a weight reduction of automobiles. For these applications, steel parts are produced by casting, followed by forming operations at an elevated temperature. Furthermore, the application of low-density steels is highly envisaged in automobile applications. Therefore, in the present investigation, the hot deformation behavior of single phase Fe-6.8Al low-density steel, and American Iron and Steel Institute (AISI) 1040 dual phase steel has been evaluated by developing strain rate sensitivity maps. Hot compression tests were carried out at temperatures ranging between 500 and 900C and 650 and 900C for the Fe-6.8Al and AISI 1040 steels, respectively, at strain rates between 0.001 and 10 s -1 . Microstructural features have been evaluated for both the steels and correlated to the deformation behavior. For the Fe-6.8Al steel, strain localization in the form of shear bands is detected during deformation below 600C in the strain rate range between 1 and 10 s -1 . The dynamic recrystallization of ferrite in Fe-6.8Al steel is also noted during compression at 800 and 900C for strain rates 0.01 and 0.001 s -1 . For the AISI 1040 steel, based on the microstructural features, dynamic recovery and dynamic recrystallization is reported to occur at 700 and 850C, respectively. The optimized deformation conditions (temperature and strain rate) for the Fe-6.8Al and AISI 1040 steels are determined to be 900C, 0.001 s -1 and 850C, 0.001 s -1 , respectively. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMaterials. =700 1\$aAvadhani, G. S.,$eauthor. =700 1\$aPund, Tushar S.,$eauthor. =700 1\$aSuwas, Satyam,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190019.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190027 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190027$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190027$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.N6 =082 04$a671.5$223 =100 1\$aNageswara Rao, M.,$eauthor. =245 10$aHot Deformation of 18 % Ni Maraging Steels: A Review /$cM. Nageswara Rao, S. V. S. Narayana Murty. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe published literature makes reference to the excellent hot workability of 18 % nickel maraging steels. However, production of large cross-sectioned products of 18 % nickel maraging steels by hot deformation can lead to different types of quality problems, such as (i) inadequate recrystallization and grain structure aligned in working direction, resulting in directionality of mechanical properties; (ii) thermal embrittlement that leads to poor values of ductility and fracture toughness; and (iii) sharp increase in flow stress with decreasing hot working temperature, necessitating the application of high loads for deformation at relatively low temperatures. To overcome these problems, primarily two sets of studies have been carried out by researchers. One set of studies was centered around the development of an optimum posthot work solution treatment. Two-stage solution treatments, as opposed to standard single-stage solution treatment at 820C, have been developed and are shown to lead to a fine-grained microstructure and an excellent combination of strength and fracture toughness with a high degree of isotropy. It has been documented that such heat treatments can also rejuvenate the quality of the products produced through a nonoptimum hot deformation schedule. The other set of studies was focused on establishing deformation processing maps using hot isothermal uniaxial compression testing. Different grades of 18 % nickel maraging steels have been the subject of investigation. Based on these studies, regimes of strain rate and temperature have been identified for optimum processing. Regimes in which flow localization occurs and hence need to be avoided have been identified. Processing regimes for obtaining fine-grained microstructures have been identified; regimes that lead to coarse grains, which need to be avoided, have been established. Constitutive equations have been developed to predict the deformation behavior as an aid to the design of the hot deformation process. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aNickel alloys. =650 \0$aNickel. =700 1\$aNarayana Murty, S. V. S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190027.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190030 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190030$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190030$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.11$223 =100 1\$aSyed Ansari, S.,$eauthor. =245 10$aHot Workability and Microstructure Control through the Analysis of StressStrain Curves during Hot Deformation of M350 Grade Maraging Steel /$cS. Syed Ansari, K. V. A. Chakravarthi, S. V. S. Narayana Murty, B. Nageswara Rao, J. Mukhopadhyay. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe ultrahigh strength (2,400 MPa) 18Ni maraging steel (M350 grade) is widely used for critical structural applications, such as aircraft landing gears, in which the strengthtoughness balance is the essential criterion for material selection. Microstructure control during thermomechanical processing is the key to obtain the desired mechanical properties on a repeatable basis in a manufacturing environment. This involves thorough understanding of the hot deformation behavior under a wide range of temperatures and strain rates to map the microstructural evolution as a function of process parameters to obtain defect-free products. Towards achieving this goal of optimization of hot workability with a view to control microstructure for M350 grade maraging steel, hot deformation processing maps have been developed and correlated to the microstructure evolved. Further, analysis of stressstrain curves was carried out to obtain fine prior austenite grain (PAG) size via discontinuous dynamic recrystallization, and the same was verified experimentally by the microstructures evolved through hot isothermal compression tests on cylindrical specimens subjected to different strain levels. A single peak DRX type ? - ? curve was selected for analyses. The theoretically determined critical strain value was verified experimentally for initiation of DRX (DRXI) and transition from DRX dominant region to grain growth dominant region (DRXT). Hot isothermal compression tests have been conducted at T =950C and ?, ?, , =, 0.01, , s, -, 1, , , , , , and obtained PAG size of 3.14 m in the specimen deformed to theoretically determined optimum strain of 0.74, thereby validating the used models. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMaterials. =700 1\$aChakravarthi, K. V. A.,$eauthor. =700 1\$aMukhopadhyay, J.,$eauthor. =700 1\$aNageswara Rao, B.,$eauthor. =700 1\$aNarayana Murty, S. V. S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190030.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180156 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180156$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180156$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA485 =082 04$a620.16$223 =100 1\$aGangolu, Srinu,$eauthor. =245 10$aHot Working Flow Behavior of Ti-6242S Alloy /$cSrinu Gangolu, Tomonori Kitashima, Masuo Hagiwara, Satoshi Emura, Kazuhiko Iida. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe hot working behavior of Ti-6242S alloy was investigated over a range of temperatures and strain rates (9731,373 K and 10 -3 1 s -1 , respectively). The flow behavior was dominated by dynamic recovery and flow softening at temperatures above and below 1,223 K, respectively. Processing maps were constructed from the flow curves at a true strain of 0.5 over the temperature ranges 9731,223 K and 1,2231,373 K. In each temperature regime, we compared the flow localization parameter and temperature sensitivity with the instability parameter determined from the processing map. The processing conditions were optimized in the temperature range 1,1731,273 K and strain rate ranges of 5.010 -1 1.0 s -1 and (1.05.0)10 -3 s -1 . The deformation activation energy under a strain rate of 10 -3 s -1 was determined as ~360 kJ/mol and was further reduced when considering the threshold stress. The operating deformation mechanism in the 9731,223 K regime was dislocation climb creep. The microstructural evolution was examined by optical and scanning electron microscopies and was correlated with the stable and unstable regimes of the processing map. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aHeat resistant alloys$xResearch. =700 1\$aEmura, Satoshi,$eauthor. =700 1\$aHagiwara, Masuo,$eauthor. =700 1\$aIida, Kazuhiko,$eauthor. =700 1\$aKitashima, Tomonori,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180156.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190070 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190070$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190070$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTE7 =082 04$a624.176$223 =100 1\$aKurc-Lisiecka, Agnieszka,$eauthor. =245 10$aHybrid Laser-GMA Welding of High-Strength Steel Grades /$cAgnieszka Kurc-Lisiecka, Aleksander Lisiecki. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe results of investigations on hybrid laser+gas metal arc (GMA) welding of butt joints of different fine-grained and thermomechanically rolled steel plates 5.0 mm thick are presented in the article. The hybrid welding tests were carried out on steel grade Domex 700MC, Domex 960, and Domex 1100. The experimental stand for hybrid welding consisted of the laser welding head and also the arc GMA torch. Butt joints of Domex 700MC plates were hybrid welded applying a metal cored wire Stein Megafil 742B (Charpy V: 80 J at -20C). In turn, the butt joints of Domex 960, and Domex 1100 steel plates were hybrid welded applying a metal cored wire Stein Megafil 1100M (Charpy V: 55 J at -20C). The quality of the test joints was analyzed by means of visual inspection and cross-section observation. In turn, the mechanical properties were evaluated by means of a static tensile test of the welded joints and also impact toughness of the weld metal. The results showed that the hybrid welding can provide a proper shape of weld even at altering gap between the butt surfaces of the groove and also at distinct shift of the electric arc to the laser beam spot. Results of tensile tests showed that the hybrid welded joints of Domex 960 and 1100 have the strength at similar levels of approximately 1,140 MPa, which is significantly higher compared to the joints of Domex 700MC at approximately 820 MPa. In turn, the weld metal of the Domex 700MC steel exhibited the highest impact toughness at a mean value of 139 J/cm 2 , whereas the test joints of Domex 960 showed lower impact toughness at approximately 122 J/cm 2 . Surprisingly, the lowest impact toughness was determined for the joints of Domex 1100, despite the same wire being applied for the Domex 960. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aReinforced concrete construction. =650 \0$aStrains and stresses. =700 1\$aLisiecki, Aleksander,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190070.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190017 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190017$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190017$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA490 =082 04$a620.11$223 =100 1\$aBharat Reddy, G.,$eauthor. =245 10$aIdentification of Hot Working Conditions and No-Recrystallization Temperature for a Cr-Mo-V Reactor Pressure Vessel Steel /$cG. Bharat Reddy, Apu Sarkar, Rajeev Kapoor, Harish Kumar, Vivek Shrivastav. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSpecimens of chromium-molybdenum-vanadium steel, commonly used as reactor pressure vessel material, were hot deformed under uniaxial compression in the temperature range of 700C1,200C and strain rate range of 0.00110 s -1 in a Gleeble thermomechanical simulator. The strain rate sensitivity ( m ) map was generated using the flow curves data. The maximum m value of 0.22 was obtained in the temperature range of 1,100C1,200C and strain rate range of 0.010.1 s -1 . Optical micrographs were used to correlate the deformed microstructures with the hot compression parameters. Kinetics analysis within the high m domain yielded the activation energy as 275 kJ mole -1 and the stress exponent as 4.46. Further, a multistep deformation (at constant strain rate with varying temperature) technique, widely used to identify the temperature of no-recrystallization (inhibition of recrystallization), was performed at 0.001, 0.01, 0.1, and 1 s -1 , with temperatures varying from 1,150C800C. The determined value of the temperature of no-recrystallization was approximately 920C, meaning below this value of temperature dynamic recrystallization would be inhibited. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMaterials$xMechanical properties. =650 \0$aPressure vessels. =700 1\$aKapoor, Rajeev,$eauthor. =700 1\$aKumar, Harish,$eauthor. =700 1\$aSarkar, Apu,$eauthor. =700 1\$aShrivastav, Vivek,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190017.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190154 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190154$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190154$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS156 =082 04$a620.82$223 =100 1\$aVishal, R.,$eauthor. =245 10$aImpact on Machining of AISI H13 Steel Using Coated Carbide Tool under Vegetable Oil Minimum Quantity Lubrication /$cR. Vishal, K. Nimel Sworna Ross, G. Manimaran, B. K. Gnanavel. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn machining, final surface quality and dimensional accuracy are the most specified customer requirements. AISI H13 tool steel is used in many fields such as the automotive, aerospace, and defense fields. It is considered to be a hard-to-machine material because of its immense strength. Conventional machining has several negative effects for the environment and human health. It has failed to produce a superior performance on machining of H13 steel. In this study, an eco-friendly minimum quantity lubrication technique is implemented by using a commercially available vegetable-based cutting fluid. An investigation was done on surface characteristics, chip morphology, and intensity of cutting temperature evolved during the machining of H13 steel. Further, wear on the tool of PVD-titanium-aluminum-nitrogen/titanium-nitrogencoated carbide inserts used for milling was observed for the given input cutting speeds of 30, 45, 60, and 75 m/min and feed rates of 0.08, 1, and 1.2 mm/rev for the constant depth of cut of 1 mm. The results obtained from vegetable oilbased minimum quantity lubrication showed a reduction in the cutting temperature by 5257 % and 3845 % and the average surface roughness in the range of 5364 % and 2240 % compared to dry and wet machining. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMetal-cutting tools. =650 \0$aMetal-cutting. =700 1\$aGnanavel, B. K.,$eauthor. =700 1\$aManimaran, G.,$eauthor. =700 1\$aNimel Sworna Ross, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190154.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180110 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180110$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180110$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK4660 =082 04$a671.5212$223 =100 1\$aAlbannai, Abdulaziz I.,$eauthor. =245 10$aImproving Centerline Solidification Crack Resistivity of AA 2024 Using Tandem Side-by-Side GTAW Technique /$cAbdulaziz I. Albannai, Abdulkareem S. Aloraier, Ayman M. Alaskari, Meshal Y. Alawadhi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, four gas tungsten arc welding (GTAW) techniques were employed by varying the travel speed and arc motion to analyze centerline solidification crack resistivity, namely slow (3.6 mm/s), fast (8.4 mm/s), weaving (4.2 mm/s), and tandem side-by-side with alternating working electrodes (3.6 mm/s). Welding high-strength materials like aluminum alloy 2024 (AA 2024) using fusion welding processes may cause centerline solidification cracking due to the wide range of solidification temperatures. AA 2024 was used because of its high susceptibility to centerline solidification cracking; it is mainly used in aerospace industries. This alloy is considered a nonweldable material when fusion welding processes are applied. A GTAW process was used because it has better control over the welding parameters and produces high quality welds. Overall, the tandem technique resulted in thinner axial grain structure surrounded by some equiaxed grains in the weld zone. Moreover, the resistance of centerline solidification cracking was improved by using the tandem technique because of the resulting disordered grain orientation, which reduces crack energy by deflecting the crack path and preventing crack propagation through thickness. In addition, a reduction in the average grain size of 4060 % was achieved by implementing the tandem technique because of its fast cooling rate. The tandem technique also showed better improvement in microhardness in the weld zone compared to the other three techniques. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aGas tungsten arc welding. =700 1\$aAlaskari, Ayman M.,$eauthor. =700 1\$aAlawadhi, Meshal Y.,$eauthor. =700 1\$aAloraier, Abdulkareem S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180110.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180149 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180149$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180149$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.P58 =082 04$a620.135$223 =100 1\$aAgarwal, Charu,$eauthor. =245 10$aIn Situ Green Synthesis and Functionalization of Reduced Graphene Oxide on Cellulose Fibers by Cannabis sativa L. Extract /$cCharu Agarwal, M. N. Singh, R. K. Sharma, Archna Sagdeo, Levente Cska. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe last decade has seen an enormous rise in the use of green reducing agents, such as plant extracts, for the chemical synthesis of several materials in view of the limitations of conventional reducing agents, such as their toxicity and instability. This study reports the green reduction and simultaneous functionalization of graphene oxide on cellulose fibers using the aqueous extract from the inflorescences of Cannabis sativa L. The graphene oxide, synthesized using the modified Hummers method, was reduced in situ on the cellulose matrix in the presence of the extract at elevated temperatures without external stabilizers in order to functionalize the fibers with reduced graphene oxide (RGO). The cellulose fibers not only acted as a flexible, biodegradable, and cost-effective matrix for the anchorage of RGO but also supported in situ reduction on the fiber surface. Different weight fractions of RGO, from 0.1 to 10 wt %, were used to fabricate RGO/cellulose composites by paper-making technique, which were characterized using Fourier transform infrared spectroscopy, scanning electron microscopy, X-ray diffraction, and X-ray photoelectron spectroscopy techniques. The RGO sheets uniformly covered the surface of the cellulose fibers and dispersed well within the fiber matrix. The surface resistivity at 40 V decreased with increasing RGO content from 1.8110 11 ? for 0.1 wt % RGO to 0.1510 11 ? for 10 wt % RGO loading. The presence of air voids between the fibers hindered the physical contact between the RGO layers, thereby preventing the formation of an effective conductive network and significantly affecting the performance of the composites. Likewise, the surface charging capacity of the composites at 40 V dropped from 1.2110 -3 ?mAh for 0.1 wt % RGO to 0.0510 -3 ?mAh for 10 wt % RGO content, indicating a rise in conductivity with RGO loading. These composites show immense potential as sustainable materials for portable energy storage devices, such as capacitors. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aCellulose fibers. =700 1\$aCska, Levente,$eauthor. =700 1\$aSagdeo, Archna,$eauthor. =700 1\$aSharma, R. K.,$eauthor. =700 1\$aSingh, M. N.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180149.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180131 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180131$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180131$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN23 =082 04$a620.118$223 =100 1\$aEngbrecht, Dick C.,$eauthor. =245 10$aInterrelationship of Thermal Effects on Calcium Sulfate Dihydrate Casts Containing Borax and Kaolin: Differential Thermal Analysis (DTA), Thermogravimetric Analysis (TGA), and Contact Dilatometry /$cDick C. Engbrecht, Deidre A. Hirschfeld. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe core composition of gypsum wallboard is calcium sulfate dihydrate (CaSO 4 2H 2 O) with varying impurities, additives, or both. This study compares two commercially calcined sources of hemihydrate (CaSO 4 2H 2 O) from a natural source and a synthetic by-product of flue gas desulfurization and neutralization to reagent grade hemihydrate. Two common ingredients, borax and kaolin, are mixed into a slurry with distilled water. The analysis supports the hypothesis that minor components in the cast have an effect on the high temperature performance of gypsum casts. The analysis is enhanced when the differential thermal analysis, thermogravimetric analysis, and dilatometry data are combined to study the changes in density versus heat flow. Specifically, the thermal performance is affected by (1) the impurities found in hemihydrate sources; (2) during the fluidization phase, the reaction of borax with free Ca ++ ions to form new borate salts that melt at lower temperatures; and (3) the intercalation of these and other ions with kaolin, providing thermal stability by reducing the formation of thermally active salts. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aThermal analysis. =700 1\$aHirschfeld, Deidre A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180131.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190025 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190025$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190025$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.A88 =082 04$a672.823$223 =100 1\$aKumar, Santosh,$eauthor. =245 10$aInvestigation on Grain Boundary Character Distribution During Dynamic Recrystallization of Austenitic Stainless Steel During Hot Deformation /$cSantosh Kumar, B. Aashranth, Dipti Samantaray, M. Arvinth Davinci, Utpal Borah, A. K. Bhaduri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe phenomenon of dynamic recrystallization (DRX) is central to the hot working and thermomechanical processing of austenitic stainless steel. This study aims to relate two distinct parameters that influence DRX: the content of interstitial atoms, such as nitrogen, and character of grain boundaries in the steel. 316LN austenitic stainless steel has been subjected to thermomechanical processing at 1,423 K through uniaxial compression at different strain rates. At these, the microstructure is fully recrystallized. The nature, character, and growth of DRX grains are studied using Electron Backscatter Diffraction (EBSD). EBSD is used to determine grain boundary character distribution and the Effective Grain Boundary Energy (EGBE) parameter. The evolution of EGBE and its relation to grain growth are analyzed. The concomitant development of special low-energy boundaries is correlated with the interstitial content in the steel, thus linking interstitial content to EGBE. The correlations so made are tested by examining the corrosion resistance of different boundaries formed at different deformation conditions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAustenitic stainless steel. =650 \0$aStainless steel. =700 1\$aAashranth, B.,$eauthor. =700 1\$aBhaduri, A. K.,$eauthor. =700 1\$aBorah, Utpal,$eauthor. =700 1\$aDavinci, M. Arvinth,$eauthor. =700 1\$aSamantaray, Dipti,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190025.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190061 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190061$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190061$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1677 =082 04$a621.366$223 =100 1\$aDobrzanski, Leszek A.,$eauthor. =245 10$aLaser Application in Photovoltaics for Surface Texturization of Silicon and Front Electrode Deposition /$cLeszek A. Dobrzanski, Aleksandra Drygala. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe laser technology in the manufacturing of solar cells has become an indispensable element of modern photovoltaic technology. The main reason for taking up such research is because conventional methods used for monocrystalline silicon texturization are ineffective when applied to polycrystalline silicon texturing. This is related to random distribution of grains of different crystalographic orientations on the surface of polycrystalline silicon. Texturing a polycrystalline silicon surface using an Nd:YAG laser makes it possible to increase absorption of the incident solar radiation. The additional technological operation of etching in potassium hydroxide solution introduced into the technology of the photovoltaic cells manufactured from laser-textured wafers allows for improvement in electrical performance compared with cells produced from nontextured wafers. Moreover, this article presents the influence of selective laser sintering of front metallization that was manufactured using paste based on silver nanopowder on contact resistant. The electrodes were formed on monocrystalline silicon solar cells. The microstructures of laser-textured silicon and sintered front metallization were investigated by scanning electron microscope and confocal laser scanning microscope. The reflectance of produced textures was measured by spectrophotometer with an integrating sphere. Current-voltage characteristics of solar cells manufactured from laser-textured polycrystalline silicon wafer were measured under standard AM 1.5 radiation. The contact resistance between the metal and semiconductor was investigated using the transmission line model. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aLasers$xIndustrial applications. =700 1\$aDrygala, Aleksandra,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190061.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180153 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180153$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180153$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.115$223 =100 1\$aAddepally, Uma,$eauthor. =245 10$aLignin-Based Carbon NanomaterialsThe Future Scope /$cUma Addepally, Vani Gandham, Kiran Kumari Palety, Yerra Kanakaraju. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCarbon, a versatile material available in nature, can assume various allotropic forms, which improves its chances of useful exploitation in various applications. The application scope increases for carbon when it is brought to nanosize structures, like fullerenes and related materials, carbon nanotubes, carbon nanofibers, graphene, and carbon nanocomposites with better mechanical, thermal, electronic, and electrical properties, coupled with chemical robustness. Various precursor materials used for carbon nanostructures include hydrocarbons, carbonaceous industrial wastes, carbon blacks, carbon nano-onions etc. The high cost of precursors in particular is caused by petro-based sources, and manufacturing costs are narrowing the applications of carbon materials in high-performance structural materials. One alternative is biobased precursor materials like lignin, a polymeric aromatic compound with various side chain substituents found in plant cell walls. Lignin consists of more than 60 % carbon on a theoretical basis and can be a green carbon source for the production of carbon-based nanomaterials. Worldwide data show that the paper and pulp industry alone produces ~5010 9 kg of lignin per annum. The E20 or E30 norms of biofuel blending shows that each ton of biomass produces ~1525 % (w/w) of lignin as a by-product. Therefore, precursor material limitation can be avoided if lignin-based sources are used for nanomaterial production. In addition to these, animal manure from herbivores can also be considered for the same beause the manure contains significant amounts of microbial, processed lignin in the rumen with decreased degree of polymerization, making it suitable to play with the structure for various applications, particularly with nanocomposites. Some of the applications based on lignin might require preliminary functionalizations to the source material. Lignin-based nanomaterials have various applications in many biocompatible-based applications, such as for cancer diagnosis, drug delivery, optical sensors, tissue engineering, energy storage devices, air filtration, oil-water separation, electronics, and catalysis, etc. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aCarbon. =650 \0$aNanostructured materials. =700 1\$aGandham, Vani,$eauthor. =700 1\$aKanakaraju, Yerra,$eauthor. =700 1\$aPalety, Kiran Kumari,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180153.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190057 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190057$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190057$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTC171 =082 04$a620$223 =100 1\$aYlnen, Markku,$eauthor. =245 10$aMartensitic Steel Microstructure Effects on Cavitation Erosion /$cMarkku Ylnen, Tuomo Nyyssnen, Mari Honkanen, Pasi Peura. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCavitation and cavitation erosion are sometimes unavoidable phenomena in hydro machine operation. For example, operating hydro turbines as regulating power leads to situations in which the risk of cavitation is accepted to some extent. Cavitation-resistant materials are therefore required to reduce machine damage and maintenance. This study characterizes the microstructure of two martensitic stainless steels from Francis turbines. They were already studied for cavitation erosion resistance in a previous study, and this study reveals the reasons behind the other steel having a significantly better resistance, while they had similar chemical compositions. The electron backscatter diffraction (EBSD) method is effective in defining the martensitic microstructure, specifically the block, packet, and prior austenite grain level. In addition, the retained austenite is effectively detected with the method. A fine prior austenite grain size and small packet and block sizes were found to be among the defining factors in cavitation erosion resistance of these steels. In addition, the transformation of retained austenite to martensite was detected in the edge region where cavitation had taken place. This transformation further increases cavitation erosion resistance. The better resistance of Steel 1 against cavitation was attributed to these microstructural differences. According to these findings, the microstructure in Steel 1 would be highly beneficial in building cavitation erosion resistant hydro machines and would be of interest to manufacturers of martensitic stainless steel components. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aCavitation. =650 \0$aMetals$xErosion. =700 1\$aHonkanen, Mari,$eauthor. =700 1\$aNyyssnen, Tuomo,$eauthor. =700 1\$aPeura, Pasi,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190057.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190075 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190075$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190075$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS225 =082 04$a671$223 =100 1\$aKitashima, T.,$eauthor. =245 10$aMeasurement and Prediction of Temperature Increase during Isothermal Forging of Titanium6 Aluminum4 Vanadium /$cT. Kitashima, R. Matsumoto, Y. Yoshida, H. Matsumoto, T. Nishihara, S. Kuroda, N. Motohashi, M. Hagiwara, S. Emura. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTitanium6 aluminum4 vanadium is isothermally forged at 1,0231,223 K (750C950C) at 0.05, 0.1, and 1.0/s using a 1,500-ton forging press simulator. The temperature increase of a workpiece (100 mm in diameter, 50 mm in height) during forging is measured by inserting thermocouples into the workpiece, and this increase is predicted using finite element analysis (FEA). The physical properties necessary for the FEA are determined using the same material as the forged one in order to improve the prediction accuracy. The true stresstrue strain curves and heat transfer coefficient between the workpiece and dies are inversely obtained. The temperature change predicted by FEA using those parameters and curves agreed well with the experimental results. In the FEA, the inelastic heat fraction, which is a conversion factor for plastic deformation energy to heat energy, did not depend on the strain rate, but it remained the same at strain rates of 0.051.0/s. This result suggests that the large heat capacity of the workpiece in this study suppressed the effect of heat transfer between the workpiece and dies/air on the temperature of the workpiece. It is also shown that the prediction accuracy of the workpieces temperature could be degraded unless the appropriate specific heat value is used, especially near the ? transus temperature, which can be affected by the composition of light elements. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aForging machinery. =650 \0$aLubrication and lubricants. =700 1\$aEmura, S.,$eauthor. =700 1\$aHagiwara, M.,$eauthor. =700 1\$aKuroda, S.,$eauthor. =700 1\$aMatsumoto, H.,$eauthor. =700 1\$aMatsumoto, R.,$eauthor. =700 1\$aMotohashi, N.,$eauthor. =700 1\$aNishihara, T.,$eauthor. =700 1\$aYoshida, Y.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190075.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180074 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180074$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180074$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.135$223 =100 1\$aSharma, Sumit,$eauthor. =245 10$aMechanical Properties of Multiwalled Carbon NanotubeReinforced Cement Composites /$cSumit Sharma, Krishan Mohan Dubey, Prince Setia. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCement is a great resource for the construction of buildings, dams, bridges, etc. because of its high compressive strength, but it has low tensile and flexural strength. Thus, to improve its properties, cement has been reinforced with carbon nanotubes (CNTs). Three groups of specimens of cement composites containing multiwalled CNTs (MWCNTs) with different concentrations of MWCNTs (0, 0.2, and 0.3 % by weight of cement) were prepared. From the results, it was observed that the 0.3 wt. % MWCNT-cement composites had higher flexural strength compared to the 0.2 wt. % MWCNT-cement composites at 21 days, but the reverse was the case at the age of 14 days. The 0.2 wt. % MWCNT-cement composites had greater strain-to-failure than the 0.3 % MWCNT-cement composites at 14 as well as 21 days. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aCement composites. =650 \0$aPortland cement$xAdditives. =700 1\$aDubey, Krishan Mohan,$eauthor. =700 1\$aSetia, Prince,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180074.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190232 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190232$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190232$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA4 =082 04$a620.82$223 =100 1\$aLiu, Qingsong,$eauthor. =245 10$aMicrostructure and Properties of the Nitrided Layer of Nodular Cast Iron /$cQingsong Liu, Lei Zhuang, Xu Liu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (5 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe plunger pair is an important part of the plunger pump. It is required to have high wear resistance, self-lubrication, deformation resistance, and sufficient strength and rigidity because of the harsh application environment, thus ductile iron is a common material for large piston pumps because of its excellent overall performance. In order to improve the friction and wear performance of spheroidal graphite cast iron plungers, a nitride layer was prepared on the ductile iron QT600-3 by the ion nitriding technique. The morphology of the permeable layer was observed with a metallographic microscope, and its hardness, friction, and wear properties were analyzed using a Vickers hardness tester and a multifunctional material tester. The results of the article show that the hardness of the nitrided specimens is greatly improved, which is about twice the hardness of the matrix. The friction coefficient is found to be much lower than the friction coefficient of the matrix; the diameter of the wear scar is small, showing a moderate change compared with the matrix; and the performance is about four times. Therefore, the ion nitriding technique can significantly improve the friction and wear resistance of the pump plunger pair. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aSteel alloys. =650 \0$aSteel$xMetallography. =700 1\$aLiu, Xu,$eauthor. =700 1\$aZhuang, Lei,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190232.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190147 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190147$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190147$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.76 =082 04$a620.135$223 =100 1\$aChen, Wen-Long,$eauthor. =245 10$aMicrostructure Evolution and Impedance Analysis of 7YSZ Thermal Barrier Coating during Gas Thermal-Shock /$cWen-Long Chen, Min Liu, Sai-rang Zhuang, Xiao-Ling Xiao. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA gas thermal-shock experiment of thermal barrier coating was carried out in air up to 1,250C in order to simulate the thermal cycling process of the engine blades during the start heating and shut cooling. The growth of thermal growth oxide (TGO) layer and microstructure evolution of YSZ layer during thermal cycling process were investigated systematically by electrochemical impedance spectroscopy testing and scanning electron microscopy. The results show that the thickness of TGO layer increases when increasing the frequency of thermal cycling, and the impedance response of middle frequencies is more and more remarkable. Meanwhile, initiation and growth of microcracks occur in YSZ layer during the gas thermal-shock experiment. The corresponding impedance characterization of YSZ layer after 100 cycles is similar to the as-sprayed sample, indicating that the YSZ microcracks could heal in a short time when sintered at high temperature. But after 300 cycles, the impedance spectroscopy of YSZ layer is quite different from the as-sprayed sample, with the corresponding impedance of YSZ grain boundary becoming more and more remarkable when prolonging the thermal-shock times, indicating that unhealing microcracks form in the YSZ layer, which may be the main reason to induce the failure of YSZ layer. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aCoatings$xThermal properties. =650 \0$aProtective coatings. =700 1\$aLiu, Min,$eauthor. =700 1\$aXiao, Xiao-Ling,$eauthor. =700 1\$aZhuang, Sai-rang,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190147.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180183 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180183$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180183$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA459 =082 04$a620.16$223 =100 1\$aTorres, H.,$eauthor. =245 10$aModeling the Induction Hardening of High-Carbon Saw Blades /$cH. Torres, F. A. Prez-Gonzlez, O. Zapata-Hernndez, N. F. Garza-Montes-deOca, J. H. Ramrez-Ramrez, Z. Fried, I. Felde, M. Rger, R. Cols. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSaws for food processing are designed to exhibit good resistance to corrosion and wear during service; the saws are made from high-carbon steel and are subjected to induction hardening to achieve the required properties. Such process offers good industrial advantages because heating is done at specific regions during very short times without heating all the material. The localized heating allows for the rapid cooling of the heated-up regions that result in transformation to austenite. This work presents the results of the simulation of induction heating using the finite and the boundary element methods to solve the heat transfer and electromagnetic phenomena. The model was coupled to a commercial package that considers the phase transformations occurring during the heating and quenching stages. The results of the simulation were validated with trials carried on site. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMetals$xMechanical properties. =650 \0$aMetals. =700 1\$aCols, R.,$eauthor. =700 1\$aFelde, I.,$eauthor. =700 1\$aFried, Z.,$eauthor. =700 1\$aGarza-Montes-deOca, N. F.,$eauthor. =700 1\$aPrez-Gonzlez, F. A.,$eauthor. =700 1\$aRamrez-Ramrez, J. H.,$eauthor. =700 1\$aRger, M.,$eauthor. =700 1\$aZapata-Hernndez, O.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180183.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180108 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180108$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180108$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.118$223 =100 1\$aVashisth, Aniruddh,$eauthor. =245 10$aMultiscale Characterization and Modeling of Nanosilica-Reinforced Filament Wound Carbon/Epoxy Composite /$cAniruddh Vashisth, Charles E. Bakis. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe addition of nanosilica (NS) particles as secondary reinforcement in the matrix of carbon/epoxy composites is known to improve certain matrix-dominated properties. The current investigation characterizes and models the effects of carbon fiber, NS, and void contents on the full set of lamina-level properties of filament wound compound sites. The properties of interest include the orthotropic elastic properties, strengths, and coefficients of thermal expansion. Multiscale modeling of the lamina properties is validated by comparing predicted and measured properties of multidirectionally reinforced filament wound carbon/epoxy tubes with and without NS. A parametric study is conducted to illustrate the effects of variable fiber and NS contents on the lamina-level thermoelastic and strength properties of filament wound carbon/epoxy composites. Inclusion of NS in the matrix is shown to significantly increase the longitudinal and transverse compressive strengths of the carbon/epoxy material. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aComposite construction. =650 \0$aComposite materials. =700 1\$aBakis, Charles E.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180108.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190178 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190178$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190178$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ853.4.M53 =082 04$a620.82$223 =100 1\$aChen, Yan,$eauthor. =245 10$aNanofluidic Behavior at the Fluid-Solid Interface /$cYan Chen, Yuan Yue, Mojdeh Rasoulzadeh, Hong Liang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe confinement and nature of complexity at the fluid-solid interface pose significant challenges for studying the nanofluidic behavior. Here, we report an approach to probe the rheological performance of three media through dynamic interaction with a harmonic oscillator. A prototype device is developed that is able to vibrate in the range up to hundreds of hertz. Results show that the interfacial viscosity was similar to that of its bulk in terms of amplitude and frequency. However, an additional phase lag appeared when the amplitude was small, and its responsive curve exhibited distortion around the natural frequency. Theoretical analysis indicated that this might be due to fluid memory because the fluid response to the solid motion is not instantaneous. The approach reported here has potential to lead toward new ways of studying dynamic properties of fluid-solid interfaces. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMicrofluidics. =650 \0$aNanofluids. =700 1\$aLiang, Hong,$eauthor. =700 1\$aRasoulzadeh, Mojdeh,$eauthor. =700 1\$aYue, Yuan,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190178.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190052 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190052$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190052$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS694.2 =082 04$a673.722732$223 =100 1\$aKumar, Anil,$eauthor. =245 10$aNanoporous Oxide Surface Obtained on Titanium (Grade 5) Alloy to Analyze Surface Hardness and Anti-Wear Character /$cAnil Kumar, Manoj Kumar Kushwaha. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis research work exhibits a technique to enhance the surface character of nanoporous oxide layer obtained on Ti6Al4V by an anodic oxidation method and by critically analyzing its tribological behavior along with improved surface hardness. The effects of anodizing parameters like electrolytic concentration, anodic voltage, time, current density, etc. were monitored to attain well-ordered porous oxide film on the titanium substrate. Phase analysis and the morphological survey of the anodized surface were performed by an X-Ray diffractometer and scanning electron microscopy (SEM), respectively. Phase analysis revealed that porous structure appeared at 0.4 M of sulfuric acid (H 2 SO 4 ) and anodic voltage at 20 V; the phase transformation from anatase to rutile occurred at 0.5 M of H 2 SO 4 . Wear tests performed on pin-on-disctype tribometer showed accumulated oxide layer (titanium dioxide) significantly enhanced wear-resisting strength, especially abrasive wear. Comparison between the anodized and nontreated/nonanodized surface with SEM micrographs was performed to determine the response of oxide film after wear. This work determines a large range of applications for the treated surface, especially for biomaterial. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAluminum alloys$xAnodic oxidation. =650 \0$aAluminum$xAnodic oxidation. =700 1\$aKushwaha, Manoj Kumar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190052.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190003 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190003$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190003$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN689.2 =082 04$a620.16$223 =100 1\$aShafiei, E.,$eauthor. =245 10$aNew Phenomenological Model to Predict High-Temperature Flow Stress Curves at High Strain Rates /$cE. Shafiei, F. Ostovan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, a new phenomenological equation has been presented to predict high-temperature flow stress curves of metallic materials at industrially relevant deformation conditions with negligible flow softening. To this end, a nonlinear estimation of strain-hardening rate versus strain curves was employed to obtain flow stress as a function of strain. To prove the validity and competency of the presented model, flow stress curves of Alloy 800 H obtained at temperatures from 850C to 1,050C and at strain rates of 5 s -1 and 10 s -1 were used. The evaluation of the mean error of flow stress revealed that the presented model can give a precise estimation of stress-strain curves of Alloy 800 H at high strain rates. The Johnson-Cook and logarithmic power models were also used to show the accuracy of the presented model at different deformation conditions. It was discovered that the presented model can provide a more accurate estimation of flow stress curves for the alloy of this study. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMaterials. =650 \0$aStrains and stresses. =700 1\$aOstovan, F.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190003.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180096 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180096$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180096$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS227 =082 04$a671$223 =100 1\$aSchwarz, Alexander,$eauthor. =245 10$aNew Welding Joint Geometries Manufactured by Powder Bed Fusion from 316L /$cAlexander Schwarz, Andreas Gebhardt, Markus Schleser, Patricia Popoola. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn metal additive manufacturing, an increasing demand for large size parts occurs. However, because of the economics of size, the manufacturing costs for parts do not increase linearly with their volumes. It is often economically unreasonable to directly produce large size components. Instead of directly building parts, technologies like hybrid building are used. To avoid extensive clamping devices for welding, additive manufacturing can be used to design new gap geometries. With these new geometries, the positions of the parts can be defined and the deformations that are due to thermal influences by the welding process can be reduced. Nevertheless, the powder bed fusion process leads to a different microstructure that needs to be taken into account for the welding process. The new microstructure leads to an extensive shrinkage during welding that exceeds the shrinkage of conventionally produced parts. To avoid the shrinkage, the weld gap design not only has to fulfill the requirements of conventional welding but it also needs to avoid the shrinkage of the parts. The resulting shrinkage of the parts is, in one way, a disadvantage, but it can also be used as an advantage for subsequent laser welding processes. If additively manufactured parts should be laser welded to get a smooth weld surface, normally post-processing must be performed to fulfill the necessary gap distance. This can be avoided by combining different welding processes. If the backside of a part is first welded by conventional welding, the resulting shrinkage will close the gap on the structured surface. If laser welding is then applied to a structured surface, it is nearly impossible to see the weld. This article will present new designs for welding joints and show how the different welding behavior can be used to improve the additively manufactured parts for hybrid welding processes. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aWelding. =700 1\$aGebhardt, Andreas,$eauthor. =700 1\$aPopoola, Patricia,$eauthor. =700 1\$aSchleser, Markus,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180096.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180172 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180172$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180172$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA690 =082 04$a624.1826$223 =100 1\$aMukhopadhyay, A. K.,$eauthor. =245 10$aOn the Phases Present in Artificially Aged AA2618 Extrusions /$cA. K. Mukhopadhyay, R. Sarkar, D. Kumar, P. Ghosal. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe aluminum alloy AA2618, based on aluminumcoppermagnesiumsiliconironnickel, is successfully utilized at elevated temperatures, i.e., in the temperature range of 100C300C, for varying durations for critical aerospace applications. The intermetallic compound Al 9 FeNi (having the monoclinic crystal structure) forms early during the solidification process, and this compound is known to assist in stabilizing the grain structure of the alloy. This work shows that during subsequent homogenizing, annealing, and thermo-mechanical processing, the Al 9 FeNi compound becomes unstable and acts as a nucleation site for the stable Al 7 Cu 2 (FeNi) phase (having a tetragonal crystal structure). It is further observed that in the artificially aged condition, both GuinierPrestonBagaryatsky zones and S (Al 2 CuMg) phase co-exist. However, the S phase is found to form copiously parallel to {110} Al crystallographic planes apart from its known habit planes of {210} Al. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAluminum alloys. =650 \0$aAluminum construction. =700 1\$aGhosal, P.,$eauthor. =700 1\$aKumar, D.,$eauthor. =700 1\$aSarkar, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180172.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180112 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180112$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180112$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1677 =082 04$a621.366$223 =100 1\$aBasak, Amrita,$eauthor. =245 10$aOn the Spatial Variation of the Microstructure and Microhardness Properties of Nickel-Based Superalloy Ren 142 Fabricated via Scanning Laser Epitaxy (SLE) /$cAmrita Basak, Yunpei Yang, Suman Das. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article seeks to investigate and characterize the spatial variation of the microstructure and microhardness properties of Ren 142, a high- ? nickel-based superalloy, fabricated through single-pass depositions using scanning laser epitaxy (SLE), a laser powder bed fusion (LPBF)based additive manufacturing (AM) process. Various advanced material characterization techniques such as optical microscopy, scanning electron microscopy, and Vickers microhardness measurements are employed to thoroughly characterize the SLE-fabricated Ren 142 specimens. Whereas optical microscopy analyses reveal that the primary dendritic arm spacing (PDAS) remains relatively constant, scanning electron microscopy investigations demonstrate that the size of the ? precipitates increase as the scan progresses. Microhardness measurements indicate that the hardness values remain unaffected along the scan direction. Through this study, it is demonstrated that the microstructure and the microhardness properties of the AM-fabricated Ren 142 deposits are strong functions of the spatial location. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aLasers$xIndustrial applications. =700 1\$aDas, Suman,$eauthor. =700 1\$aYang, Yunpei,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180112.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180066 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180066$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180066$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK9152 =082 04$a621.4835$223 =100 1\$aMaduraimuthu, V.,$eauthor. =245 10$aOptimization of A-TIG Welding Process Parameters for P92 (9Cr-0.5Mo-1.8W-VNb) Steel by Using Response Surface Methodology /$cV. Maduraimuthu, P. Vasantharaja, M. Vasudevan, B. S. Panigrahi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aResponse surface methodology (RSM) is a mathematical and statistical technique useful for the modeling and optimization of processes in which a response of significance is influenced by a number of process parameters called input variables. The major concern faced by fabrication engineers during activated tungsten inert gas (A-TIG) welding is the selection of the optimum combination of input variables for achieving the desired weld bead geometry. In this research work, the optimization of A-TIG welding process parameters for P92 (9Cr-0.5Mo-1.8W-VNb) steel have been carried out using RSM. The design matrix for conducting experiments was generated using the central composite design of RSM. The four input process variables, such as welding current, torch speed, arc gap, and electrode tip angles, are varied at five levels. A-TIG bead-on-plate welds were made on a 10 mm-thick P92 steel plate as per the combination of input parameters given by the design matrix. Weld bead geometry, such as the depth of penetration, bead width, and width of the heat-affected zone, were measured and recorded as responses. Second-order response surface models were developed for predicting the response for the set of given input process parameters. Moreover, the response optimization was carried out for obtaining the maximum depth of penetration, minimum bead width, and target heat-affected zone width using the desirability approach. The validation experiments were carried out on the determined optimized process parameters, and it was found that there was good agreement between the predicted weld bead dimensions and actual values obtained during the experiments. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aNuclear reactors$xSafety measures$xMathematical models. =650 \0$aResponse surfaces (Statistics) =700 1\$aPanigrahi, B. S.,$eauthor. =700 1\$aVasantharaja, P.,$eauthor. =700 1\$aVasudevan, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180066.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190009 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190009$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190009$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.186$223 =100 1\$aSarkar, Aditya,$eauthor. =245 10$aOptimization of Hot Workability of Cu-Cr-Zr-Ti Alloy Through Development of a Processing Map /$cAditya Sarkar, S. V. S. Narayana Murty, M. J. N. V. Prasad. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aOwing to high thermal conductivity, copper-based alloys are used to fabricate heat transfer elements of rocket engines, such as combustion chambers, nozzle liners, and metal gaskets. One such alloy is the Copper-Chromium-Zirconium-Titanium (Cu-Cr-Zr-Ti) alloy, which possesses a good combination of thermal conductivity and strength at high temperatures. Thermomechanical processing is an important step in the realization of the various aforementioned heat transfer elements from this alloy. Hence, it is imperative to understand the hot deformation behavior of the alloy as a function of the process variables such as temperature and strain rate. An attempt is made to study the hot deformation behavior of the Cu-Cr-Zr-Ti alloy by subjecting it to uniaxial hot compression tests in the temperature range of 600C800C and strain rate range of 0.00110 s -1 . The flow stress measurement tests were conducted up to a true strain of 0.5 using a Gleeble 3800 simulator. The nature of the flow curves obtained at the completion of the tests indicated the occurrence of dynamic recrystallization (DRX) at deformation temperatures greater than 700C and with a strain rate below 1 s -1 . The work hardening rate was plotted as a function of effective flow stress to assess the flow softening behavior due to DRX at different deformation conditions. A processing map delineating the stable and unstable regions during hot working is developed and validated by observing the microstructures in the corresponding domains. Optimum processing parameters (temperature of 750C and strain rate of 0.110 s -1 ) for hot working of the alloy were proposed based on a contour map of efficiency of power dissipation. Two constitutive equations are also established: one using the Hyperbolic sine law as proposed by Sellars and McTegart and the other using Kocks Mecking analysis. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAluminum alloys$xMechanical properties. =650 \0$aAluminum castings. =700 1\$aNarayana Murty, S. V. S.,$eauthor. =700 1\$aPrasad, M. J. N. V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190009.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180115 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180115$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180115$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK4660 =082 04$a671.5212$223 =100 1\$aGonzales, Devon S.,$eauthor. =245 10$aOxygen Effects on Solidification Behavior of Gas Tungsten ArcWelded Laser Powder Bed FusionFabricated 304L Stainless Steel /$cDevon S. Gonzales, Stephen Liu, Daniel Javernick, Robin Pacheco, Michael Brand, Matthew Johnson, David Tung. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe laser powder bed fusion (L-PBF) process inherently accumulates interstitial gas elements during powder fabrication and laser deposition processes. Such elements can lead to localized variations in the weld pool and affect the solidification behavior (when compared with its wrought equivalent), in addition to chemical microsegregation within the fabricated material. This study was conducted to characterize the solidification behavior of gas tungsten arc (GTA) welds made on L-PBF 304L stainless steel. The effect of surface active elements on the local solidification rates was studied. An emphasis was placed on the role local solidification rates and temperature gradients throughout the weld play on the resultant weld solidification structure and microsegregation. It was determined that gas tungsten arc welds on L-PBF 304L stainless steel exhibited a vermicular ferrite solidification structure compared with a mix of vermicular and lathy ferrite structure in wrought 304L. The varying convective thermal gradients in the weld pool affected the solidification modes and partitioning of elements, leading to fluctuations of microsegregation in the L-PBF 304L. Macroscopically, such partitioning affected the surface tension within the weld pool, producing asymmetric weld pool geometries. The compositional differences between wrought and L-PBF fabricated 304L stainless steels resulted in irregular solidification behaviors during welding affecting the final weld microstructure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aGas tungsten arc welding. =700 1\$aBrand, Michael,$eauthor. =700 1\$aJavernick, Daniel,$eauthor. =700 1\$aJohnson, Matthew,$eauthor. =700 1\$aLiu, Stephen,$eauthor. =700 1\$aPacheco, Robin,$eauthor. =700 1\$aTung, David,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180115.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180144 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180144$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180144$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA403.6 =082 04$a620.11$223 =100 1\$aNandee, Rajib,$eauthor. =245 10$aPerformance and Characterization of Two-Dimensional Material Graphene ConductivityA Review /$cRajib Nandee, Mohammad Asaduzzaman Chowdhury, Mohi Uddin Ahmed, Bengir Ahmed Shuvho, Uttam Kumar Debnath. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aGraphene material is made from graphite using different techniques. The development of graphene material is now at a very initial stage even though a lot of research is conducted to analyze the electrical and thermal feature of graphene. Graphene is considered an epoch-making invention that has a two-dimensional single lattice. Hexagonal bonding also exists. The main limitation of graphene is that it cannot form a band gap because of its high attraction of intermolecular atoms, but the researchers main challenges are to find out the processes by which this critical issue can be solved. As a matter of fact, graphene is the hardest material in the earth today. In the research field, researchers are presently trying to make graphene a conductor or semiconductor by forming energy gaps. In this review article, literature is mentioned to understand the thermal and electrical conductivity of graphene in various layers through the process of emissivity, microwave absorption, etc. This article can be considered state of art for future research in the industry. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aGraphene. =650 \0$aMaterials science. =700 1\$aAhmed, Mohi Uddin,$eauthor. =700 1\$aChowdhury, Mohammad Asaduzzaman,$eauthor. =700 1\$aDebnath, Uttam Kumar,$eauthor. =700 1\$aShuvho, Bengir Ahmed,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180144.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190018 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190018$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190018$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.186$223 =100 1\$aRaja, Nitish,$eauthor. =245 10$aPhysical Simulation and Processing Map of Aluminum 7068 Alloy /$cNitish Raja, B. S. S. Daniel. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aElevated temperature deformation of as-cast aluminum 7068 alloy was done to optimize its workability by physical simulation using Gleeble 3800. The microstructural evolution was traced using electron microscopy and electron back-scattered diffraction studies. Hot deformation involving uniaxial isothermal compression was done in the 300C475C temperature range and 10 -3 10 0 s -1 strain rate up to a true strain of 0.69. From the true stresstrue strain plot it is observed that flow stress initially increases sharply because of the multiplication of dislocations during the initial phase of deformation; i.e., only work hardening is predominant during this phase. Subsequently, after attaining the peak value the flow stress increases, decreases, or remains constant. Because of dynamic restoration processes such as dynamic recovery and recrystallization, the flow stress decreases or remains constant. During this phase, the competition between work hardening and dynamic softening governs the slope of true stressstrain curve. The decrease in the Zener-Hollomon parameter with increasing temperature and decreasing strain rate follows the same trend as flow stress. Activation energy for this alloy is calculated as 206 kJ mol -1 . The deformed microstructure shows serrated grains, and also well-formed subgrains are observed mostly inside the grains. Moreover, substructural strengthening is observed in this alloy, due to the presence of the high density of precipitates and subgrains. Microstructural analysis confirms the high power dissipation of the stable region may be mainly due to dynamic recovery. In the unstable region, flow instabilities may be due to adiabatic shear band formation, particle cracking, and debonding. The optimized working region is determined from the developed processing map. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAluminum alloys$xMechanical properties. =650 \0$aAluminum castings. =700 1\$aDaniel, B. S. S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190018.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190004 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190004$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190004$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.11$223 =100 1\$aPrasad, K. S.,$eauthor. =245 10$aPrediction Capability of Constitutive Models for Inconel 718 Sheets Deformed at Various Elevated Temperatures and Strain Rates /$cK. S. Prasad, S. K. Panda, S. K. Kar, S. V. S. N. Murty, S. C. Sharma. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe fabrication of Inconel 718 (IN718) sheet metal components often requires larger deformation loads at room temperature. In this regard, deformation of the material at elevated temperature is a promising approach for reducing the forming load and enhancing the formability. Hence, the flow-stress behavior of IN718 sheets at elevated temperatures within the range of 773973 K over wide ranges of strain rate (from 0.001 to 1 s -1 ) was studied by uniaxial tensile testing. The peak load reduced significantly by 75.6 and 8.5 % at 923 K and 0.001s -1 compared with room temperature and 773 K, respectively. Also, the total elongation improved by 65.4 and 16.5 % at 923 K with respect to room temperature and 773 K, respectively. In addition, a substantial improvement in the total elongation was observed with decrease in strain rate at higher temperatures. Seven different constitutive models, viz., Johnson-Cook (JC), modified-JC (m-JC), modified-Arrhenius equation (m-ARR), mechanical threshold stress (MTS), Rusinek-Klepaczko (RK), modified Zerilli-Armstrong (m-ZA), and the artificial neural network (ANN) were developed to describe the deformation behavior of IN718 sheet material at elevated temperatures and varying strain rates. Furthermore, suitability of these developed models was determined by comparing three standard statistical parameters, namely correlation coefficient (R), average absolute error (?), and standard deviation (SDA). The results showed that m-JC and m-ZA models predicted the flow stress very well in accordance with the experimental data. However, the trained ANN model could predict the flow-stress behavior more accurately throughout the entire testing condition. Though the ANN model was the best among all seven models, it was strongly dependent on an extremely good set of experimental data. Hence, the physical-based m-ZA model was considered to be the suitable model that could precisely predict the flow-stress behavior of IN718 sheet material. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMaterials. =700 1\$aKar, S. K.,$eauthor. =700 1\$aMurty, S. V. S. N.,$eauthor. =700 1\$aPanda, S. K.,$eauthor. =700 1\$aSharma, S. C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190004.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180138 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180138$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180138$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN672 =082 04$a671.36$223 =100 1\$aNayak, U. V.,$eauthor. =245 10$aQuench Cooling PerformanceHardness Correlation for AISI 1045 and 1090 Steels /$cU. V. Nayak, K. N. Prabhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHeat transfer and microstructure evolution during quenching of AISI 1045 and 1090 steels in vegetable oils was investigated. To simulate the industrial quench heat treatment, reference probes made of medium and high carbon steels were quenched, and heat flux transients were estimated by taking into account the phase transformation. The cooling curves obtained with reference probes made from AISI 1045 and AISI 1090 steels showed kinks indicating enthalpy change accompanied with phase transformations during continuous cooling. This was reflected in the estimated heat flux curves. The section thickness effect on heat flux transients was examined by using probes of diameters 25 mm and 50 mm. The cooling rates measured at various locations across the section diameter of reference probes were related to the hardness using the quench factor technique. The heat transfer characteristics of the quench media, the evolved microstructure, and the resulting hardness were in complete agreement. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMetals$xQuenching. =700 1\$aPrabhu, K. N.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180138.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180122 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180122$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180122$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA460 =082 04$a620.16$223 =100 1\$aSarafan, Sheida,$eauthor. =245 10$aResidual Stresses, Microstructure, and Mechanical Properties of EB-Welded 90-mm-Thick UNS S41500 Martensitic Stainless Steel after PWHT /$cSheida Sarafan, Priti Wanjara, Jean-Benot Lvesque, Javad Gholipour, Henri Champliaud, Louis Mathieu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aUNS S41500 is a grade of 13Cr-4Ni martensitic stainless steel utilized in hydroelectric turbine products. In this study, the microstructural characteristics, mechanical properties, and through-thickness residual stresses of electron-beam (EB) welded butt joints in 90-mm-thick UNS S41500, assembled using a single pass autogenous process, were evaluated after post-weld heat treatment (PWHT). The results of the longitudinal residual stresses, measured using the contour method, indicated that the applied PWHT was effective in stress relieving and reducing the hardness of the weldment through tempering of the fresh martensite present in the microstructure after EB welding. The static tensile properties that were evaluated in the directions transverse and longitudinal to the weld seam demonstrated high performance of the joints with conformance to the requirements of not only ASME Section IX, ASME Boiler & Pressure Vessel CodeSection IX: Qualification Standard for Welding and Brazing Procedures, Welders, Brazers, and Welding and Brazing Operators , but also ASTM A240, Standard Specification for Chromium and Chromium-Nickel Stainless Steel Plate, Sheet, and Strip for Pressure Vessels and for General Applications , for unwelded UNS S41500. The Charpy impact energies indicated that the toughness of the welds greatly surpassed the minimum acceptance criteria specified in ASME Section VIII, ASME Boiler & Pressure Vessel CodeSection VIII: Rules for Construction of Pressure Vessels . Also, bend testing of transverse weld cross sections displayed no discontinuities on the tension side of the bent joints. These results provide the essential data for validating a manufacturing process for assembly of high-performance joints in an important hydroelectric turbine material. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMetals$xMechanical properties. =700 1\$aChampliaud, Henri,$eauthor. =700 1\$aGholipour, Javad,$eauthor. =700 1\$aLvesque, Jean-Benot,$eauthor. =700 1\$aMathieu, Louis,$eauthor. =700 1\$aWanjara, Priti,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180122.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190125 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190125$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190125$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA409 =082 04$a620.192$223 =100 1\$aNarasimhachary, Santosh B.,$eauthor. =245 10$aResults of the ASTM Round Robin on Creep-Fatigue Crack Growth Testing of a P91 Steel /$cSantosh B. Narasimhachary, Ashok Saxena. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article summarizes the results of a round robin (RR) study begun in 2013 to evaluate ASTM E2760-10, Standard Method for Creep-Fatigue Crack Growth Testing (Superseded) . Thirteen laboratories from around the world conducted testing and reported results. The test material was a creep-ductile, ASTM Grade P91 9Cr-1Mo steel. All testing was performed using nominally 50-mm-wide compact tension specimens at a test temperature of 625C using trapezoidal waveforms with hold times of 0, 60, and 600 s. The 600-s hold time condition was the primary condition used for assessing interlaboratory variability among crack growth rates. Loading/unloading times were 2 s each. All laboratories tested duplicate specimens that were identical in all respects except for the force amplitude levels. Results from prior studies that included tensile, creep deformation and rupture, and low-cycle fatigue properties were available for the analysis of tests conducted as part of this RR testing. Crack growth rates at 600-s hold time reported by six laboratories fall within a 95 % confidence band (interlaboratory variability) separated by a factor of 6.16 when correlated with ? K , 10.76 when correlated with measured vales of ( Ct ) avg , and 7.17 when correlated with calculated values of ( Ct ) avg. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMaterials$xFatigue$xTesting. =650 \0$aMaterials$xTesting. =700 1\$aSaxena, Ashok,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190125.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180140 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180140$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180140$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.118$223 =100 1\$aThomas, Shijo,$eauthor. =245 10$aReview of Recent Progress in the Development and Properties of Aluminum Metal Matrix Composites Reinforced with Multiwalled Carbon Nanotube by Powder Metallurgy Route /$cShijo Thomas, V. Umasankar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (30 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAluminum and its alloys are finding increasing applications in every sphere of industry with various reinforcements. New reinforcements like graphene and carbon nanotubes (CNTs) are in focus on account of its contribution in mechanical, thermal, and electrical properties. Achieving uniform distribution and selecting the right manufacturing process still remain a challenge. Hence, this review takes into account the contributions by many researchers and attempts to consolidate the findings that may close the gap and identify the scope for future research. In spite of the advantages of aluminum, it requires improvement in strength, wear resistance, heat resistance, conductivity, and thermal expansion. Among the available reinforcements, CNT stands out because of its unique features of thermal conductivity, expansion, and strength. The effect of multiwalled CNT reinforcement in metal on precipitation hardening is also discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aComposite construction. =650 \0$aComposite materials. =700 1\$aUmasankar, V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180140.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190068 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190068$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190068$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1677 =082 04$a621.366$223 =100 1\$aLisiecki, Aleksander,$eauthor. =245 10$aRobotic Fiber Laser Cladding of Steel Substrate with Iron-Based Metallic Powder /$cAleksander Lisiecki, Dawid Slizak, Adrian Kukofka. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe investigations of robotized laser cladding of mild steel by iron-based powder and the study of process parameters on quality and properties of the test surface layers are described. The test surface layers were produced as single stringer beads by means of a laser head coupled with powder-delivering nozzles and mounted on a welding robot arm. The fiber laser emitting at 1.061.07 m with maximum output power 3.0 kW was used in the study. As the substrate for cladding, the mild steel was chosen, while the experimental powder was composed of 7.0 wt. % of molybdenum, 4.0 wt. % of chromium, 2.0 wt. % of tungsten and vanadium, and also 0.81.0 wt. % of carbon. The surface layers were produced at different laser powers and different scanning speeds. The area of the melt pool and the surrounding regions were protected by argon flow. The detailed influence of the heat input of cladding on the geometry of single stringer beads of surface layers was determined. Results of the investigations showed that the microstructure of surface layers is homogeneous and fine-grained with dispersive precipitation of very fine carbides. Hardness of the mild steel substrate is in the range of 120 to 150 HV1, while the hardness in surface layer is significantly increased up to 800 HV1. The produced surface layers are characterized by high quality. No significant imperfections or discontinuity such pores or cracks were found. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aLasers$xIndustrial applications. =700 1\$aKukofka, Adrian,$eauthor. =700 1\$aSlizak, Dawid,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190068.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190069 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190069$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190069$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1677 =082 04$a621.366$223 =100 1\$aLisiecki, Aleksander,$eauthor. =245 10$aRobotized Fiber Laser Cladding of Steel Substrate by Metal Matrix Composite Powder at Cryogenic Conditions /$cAleksander Lisiecki, Dawid Slizak, Adrian Kukofka. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe results of investigations on laser cladding of mild steel plates (0.17 wt.% carbon and 1.4 wt.% manganese) by nickel powder with addition 60 wt.% of tungsten carbides at conditions of forced cooling by liquid nitrogen are presented. To provide reproducible conditions and high accuracy, tests of cladding were carried out on a robotized stand equipped with a fiber laser generator and powder feeding system. The symmetrical circular laser beam with beam spot diameter of 300 ?m was applied as the heat source for cladding of composite single stringer beads at different heat inputs and different cooling conditions. Free cooling of the steel substrate was conducted in the ambient air, while the forced cooling was achieved by partial immersion of the steel plate in liquid nitrogen at approximately -190C. The results showed that the conditions of cooling have a strong influence on the cladding process, mechanism of a bead formation, quality, microstructure, and geometry of the beads. Laser cladding at forced cooling leads to a favorable fine-grained microstructure and increased microhardness of the metal matrix and also, lower dilution. In the case of stringer beads produced at cryogenic conditions, the heat-affected zone in the substrate of the mild steel is hardened with evident traces of bainitic microstructure. However, the heat input of laser cladding must be significantly increased at forced cooling to provide the proper shape of the bead and also to avoid cracks and a lack of fusion the steel substrate. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aLasers$xIndustrial applications. =700 1\$aKukofka, Adrian,$eauthor. =700 1\$aSlizak, Dawid,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190069.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180145 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180145$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180145$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a671.52$223 =100 1\$aVenkataiah, M.,$eauthor. =245 10$aRole of Friction Stir Processing Parameters on the Microstructure and Hardness of ZE41Mg Alloy: A Taguchi Approach /$cM. Venkataiah, T. Anup Kumar, K. Venkata Rao, S. Anand Kumar, B. Ratna Sunil. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present study, the influence of friction stir processing (FSP) tool rotational speed and tool travel speed on achieving higher hardness in ZE41 Mg alloy was investigated by adopting a Taguchi design model using orthogonal array. The extent of grain refinement, hardness enhancement, and achieving defect-free stir zones in FSP completely depend on process parameters. In the present work, FSP parameters such as tool rotation speed and tool traverse speed were varied. The microscopic and macroscopic observations revealed that tool speeds of 1,400 rpm with 25 and 50 mm/min feeds were found to be optimal to develop fine grain size and wide stir zone, respectively, without defect. These results are in good agreement with the design model and help with choosing optimized parameters with a minimum number of experiments in developing grain-refined ZE41 Mg alloy for emerging lightweight technological applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aFriction stir welding. =650 \0$aMetals$xFormability. =700 1\$aKumar, S. Anand,$eauthor. =700 1\$aKumar, T. Anup,$eauthor. =700 1\$aRao, K. Venkata,$eauthor. =700 1\$aSunil, B. Ratna,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180145.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190058 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190058$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190058$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTG380 =082 04$a620.135$223 =100 1\$aZuk, Marcin,$eauthor. =245 10$aSimulated Heat-Affected Zone of Steel 4330V /$cMarcin Zuk, Jacek Grka, Wojciech Jamrozik. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSteel 4330V is a material that contains an addition of vanadium (approximately 0.06 wt. %). The steel is widely used in the mining and petroleum industries. The steel microstructure contains tempered martensite. The high carbon equivalent of the steel makes it difficult to weld. The simulation of the heat-affected zone (HAZ) makes it possible to determine the effect of an increase in temperature on the properties and the structure of the steel. The simulation of heating was performed using a resistive heating device. The specimens were heated between 2 and 8 s at a temperature restricted within the range of 300C1,300C. During the tests, temperature was recorded using a thermal imaging camera. The tests revealed that up to a temperature of approximately 600C, the material did not undergo structural changes. Above a temperature of 600C, the hardness of the specimen increased to 500 HV. As the temperature of the HAZ increases, the grain size changes, which in turn affects the change of mechanical properties. Results of the impact strength tests performed at a temperature of 40C confirmed hardness values and results of micrographic examinations. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aIron and steel bridges$xDesign and construction. =650 \0$aSteel, Structural$xDesign and construction. =700 1\$aGrka, Jacek,$eauthor. =700 1\$aJamrozik, Wojciech,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 4 Special Issue on Advanced Welding Technologies and Weldability.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190058.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180188 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180188$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180188$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN719.5 =082 04$a671.36$223 =100 1\$aPimentel, A. S. O.,$eauthor. =245 10$aSlip-Rolling Behavior of Ductile and Austempered Ductile Iron Containing Niobium or Chromium /$cA. S. O. Pimentel, W. L. Guesser, P. D. Portella, M. Woydt, J. Burbank. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe use of high niobium alloyed cast iron alloys is a relatively new approach in which the niobium addition intends to improve the properties of the material by the precipitation of hard niobium carbides during solidification. Steels can be replaced by ductile cast iron in some rolling applications, such as gears and cams, in order to reduce material costs. The aim of this work is to evaluate ductile iron alloyed with 1 weight percent (wt.%) niobium for the as cast specimens and with 1.8 wt.% and 2.4 wt.% niobium for the austempered specimens under lubricated slip-rolling tests using mixed/boundary conditions in an Amsler-type machine. Austempered ductile iron (ADI) alloyed with 1 wt.% chromium, or Carbidic ADI, was tested for comparison. For the as cast conditions, the niobium addition resulted in an increase of wear resistance owing to the low contact pressure of these tests. However, for the austempered specimens, the best performance was found for unalloyed ADI. The main factor acting in the initiation and propagation of cracks in ductile iron is the presence of the graphite nodules. The coarse carbides also contributed to the initiation of cracks and spalling of the material. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aIron$xDuctility. =650 \0$aTempering. =700 1\$aBurbank, J.,$eauthor. =700 1\$aGuesser, W. L.,$eauthor. =700 1\$aPortella, P. D.,$eauthor. =700 1\$aWoydt, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180188.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180067 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180067$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180067$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.F55 =082 04$a363.7288$223 =100 1\$aSpencer, William Cole,$eauthor. =245 10$aStatistical Analysis of Fly Ash Sampling Frequency /$cWilliam Cole Spencer, Eleazar I. Diaz Loya, Anupam Joshi, Rafic Minkara. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aFly ash is a byproduct of the combustion of pulverized coal, which has found an application as a supplementary cementitious material that offers several benefits such as improved workability, durability, and improved long-term strength to concrete. The requirements for sampling frequency of this material are laid out in ASTM C311, Standard Test Methods for Sampling and Testing Fly Ash or Natural Pozzolans for Use in Portland-Cement Concrete . The article analyzes the composite sampling frequency and provides insight into how changing it would affect the ability to capture changes in fly ash properties. The analysis is based on data collected using the current composite sampling requirements during the calendar year of 2016 from four power plants located in the United States. Fly ash properties included in the analysis are the sum of silica, alumina, iron oxide content, sulfur trioxide content, loss on ignition (LOI), fineness, and the strength activity index at 7-days and 28-days. The statistical analysis shows that reducing the composite sampling frequency to monthly, instead of every 2,900 Mg (3,200 tons), would not affect the ability to properly identify the properties of fly ash. This conclusion is supported by the observation that the parameters show small variability throughout the year and that those dependent on plant operational changes (such as fineness and LOI) are monitored on site at an even higher frequency, daily or every 360 Mg (400 tons) =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aFly ash$xEnvironmental aspects. =650 \0$aFly ash$xIndustrial applications. =700 1\$aDiaz Loya, Eleazar I.,$eauthor. =700 1\$aJoshi, Anupam,$eauthor. =700 1\$aMinkara, Rafic,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180067.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180057 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180057$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180057$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7871.15.C4 =082 04$a621.381$223 =100 1\$aDra, Rafik El Arslene,$eauthor. =245 10$aStructural Study and Electrical Properties of Bi1.5xCaxSb1.5CuO7 Pyrochlore-Type Solid Solution Series /$cRafik El Arslene Dra, Ahmed Bekka, Robert E. Dinnebier, Bounekref Boukerma. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPyrochlore solid solution Bi, , 1.5, -, x, , , Ca, , x, , Sb, , 1.5, , , CuO, , 7, , , , , has been prepared by conventional ceramic solid state reaction with 0<= x <=0.4. The samples were characterized by X-ray powder diffraction (XRPD), scanning electron microscopy, and electrical conductivity measurements. The pyrochlore single phase formation was confirmed for all of the x -fractions. The variation of the electrical resistivity versus x of all samples measured by means of a four-probe device at room temperature indicates that these still remain insulators. High-temperature electrical conductivity measurements at various frequencies using a device with two electrodes allow us to note the maximum electrical conductivity of 4.710 -3 S.cm -1 , which has been reached at x =0.2, generating an activation energy of 0.14 eV. For this fraction, Rietveld refinement of the corresponding XRPD pattern confirmed the typical cubic Fd-3m space group with a cell parameter of a =10.4089(1) =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aPiezoelectric ceramics. =700 1\$aBekka, Ahmed,$eauthor. =700 1\$aBoukerma, Bounekref,$eauthor. =700 1\$aDinnebier, Robert E.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180057.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190059 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190059$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190059$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.186$223 =100 1\$aGrka, Jacek,$eauthor. =245 10$aStructure and Properties of High-Strength Low-Alloy Steel Melted by the Laser Beam /$cJacek Grka, Marek Opiela. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this article, examinations were presented of laser beam remelting of microalloyed high-strength low-alloy steel28MnTiNbVB (UTS=1,600 MPa), 12 mm thick. The remelting process was carried out with variable linear energy in the range from 0.6 to 2.6 kJ/cm. The examinations have shown that remelted zones have a correct geometry but also include gas pores that could be caused by very high cooling rates, resulting in the hindering of gas evacuation from remelted zones. These gas pores are caused by trapping gases dissolved in metal or vaporizing alloying elements. Remelted zone is martensitic with a lath structure and a hardness up to 600 HV10. Laths are smaller, and smaller precipitations are more tightly packed relative to parent material. The examination results show that steel 28MnTiNbVB exhibits limited weldability. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAluminum alloys$xMechanical properties. =700 1\$aOpiela, Marek,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190059.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180137 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180137$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180137$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ1280 =082 04$a621.92$223 =100 1\$aGao, Chao,$eauthor. =245 10$aStudy of Grinding Edge on Tempered Glass Using Electroplated Diamond Abrasive Belts /$cChao Gao, Sheng Wang, Guangzhao Liu, Hui Wang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis study aims at improving the grinding quality and efficiency of the grinding edges on tempered glass using electroplated diamond abrasive belts. Firstly, the most suitable diamond type and composition of metal coating were selected in the first experiment. Secondly, the structure parameters of abrasive belts, such as diamond grain size (dgs), chip clearance (chc), matrix thickness (mt), and coating thickness ratio (ctr), were optimized through an L 9 (3 4 ) orthogonal experiment. Finally, the influences of the process parameters on the grinding effect were investigated, which are optimized by an L 9 (3 3 ) orthogonal experiment. The results show the following: (1) the abrasive belt with the diamond type of SMD40 and metal coating of 90 % nickel, 5 % cobalt, 5 % copper (Ni90%-Co5%-Cu5%) weight percentage (wt.%) of the total weight of the coating metal possesses the best grinding performance for the grinding edges on tempered glass. (2) The best grinding quality can be achieved under the conditions of the 230/270 US mesh (63-53 ?m) in dgs, 1.5 mm in chc, 1.2 mm in mt, and 2/3 in ctr. (3) The roughness decreases first and then increases with the increase of dgs and ctr, decreases with the increase of chc, and increases with the increase of mt. (4) With the increase of the grinding pressure (gp), the roughness increases, and the material removal rate increases first and then decreases; with the increase of belt linear velocity (blv), the roughness first descends and then tends to stability, and the material removal rate increases first and then decreases; with the increase of the belt tensioning force (btf), the roughness decreases, and the material removal rate increases first and then tends to be stable. (5) The best grinding performance can be achieved under gp of 18 N, blv of 30 m/s, and btf of 55 N. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aGrinding and polishing. =700 1\$aLiu, Guangzhao,$eauthor. =700 1\$aWang, Hui,$eauthor. =700 1\$aWang, Sheng,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180137.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180117 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180117$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180117$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA491 =082 04$a620.118$223 =100 1\$aWang, Lili,$eauthor. =245 10$aStudy on Cavitation Behaviors of Spiral Oil Groove Journal Bearing /$cLili Wang, Guoteng Yuan, Guoxiao Yin, Yuliang Wei. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA model of spiral oil wedge hydrodynamic bearing is first established, and a numerical simulation of the fluid region is carried out by Fluent. The influence of inlet pressure and rotation speed on the cavitation area in the oil film divergence region is analyzed, and the cavitation shape, size, and location of the cavitation area are also compared and analyzed; at the same time, the influence of noncondensing gas (NCG) mass fraction on the oil film flow field is studied. The results show that the results of the numerical simulation are in agreement with the experimental results. The change of the inlet pressure and rotational speed can affect the disappearing position of the cavitation, but it has almost no influence on the appearing position of the cavitation. The increase of the inlet pressure can reduce the cavitation effectively, as well as the area of cavitation and number of large volume cavitation. But the increase of the rotational speed promotes the production of cavitation obviously and increases the number and area of cavitation and the possibility of complete cavitation. The NCG content in lubricating oil has a certain influence on the lubrication performance and bearing capacity. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aCavitation. =650 \0$aProtective coatings. =700 1\$aWei, Yuliang,$eauthor. =700 1\$aYin, Guoxiao,$eauthor. =700 1\$aYuan, Guoteng,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180117.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180034 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180034$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180034$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.12$223 =100 1\$aMohamed, Mostafa R.,$eauthor. =245 10$aSurface Activation of Wood Plastic Composites (WPC) for Enhanced Adhesion with Epoxy Coating /$cMostafa R. Mohamed, Hamdy M. Naguib, Rasha A. El-Ghazawy, Nevein O. Shaker, Amer A. Amer, Ahmed M. Soliman, Usama F. Kandil. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis work aims to improve the adhesive force of epoxy coating with a wood-plastic composite (WPC) surface. First, WPC was formulated using the extrusion technique through different percentages of wood flour (WF) with virgin polyethylene (PE) in the presence of a coupling agent. Dynamic mechanical analysis and water percentage gain (WPG%) were performed to find the optimized WF/PE mixing ratio. The optimized formula was subjected to surface treatment by different methods, including chromic acid oxidation, ultraviolet irradiation, and flame and heat treatment. Then the treated surface of WPC was coated with nano-modified epoxy resin using carboxylated carbon nanotube, organically modified nanoclay (Cloisite-30B), and reactive rubber nanoparticles. The surface treatment of the WPC was characterized with contact angle measurement and Fourier Transform Infrared (FTIR), while the interaction between the WPC and epoxy coat was investigated by attenuated total reflection FTIR microscopy analysis. The adhesion strength of the nano-modified epoxy showed significant enhancement when investigated by pull-off method and cross-cut test. Nano-scratching was utilized in exploring the effect of different surface treatments on enhancing adhesion to epoxy. The interfacial morphological behavior of epoxy coating on the WPC surface was investigated by Scanning Electron Microscope. The results indicated that chemical treatments helped for the functionalization of the WPC surface, leading to stronger adhesion with epoxy. These epoxy-coated WPC composites recorded enhanced mechanical properties because of the chemical reaction between the WPC surface and epoxy. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aPlastic-impregnated wood. =650 \0$aStrength of materials. =700 1\$aAmer, Amer A.,$eauthor. =700 1\$aEl-Ghazawy, Rasha A.,$eauthor. =700 1\$aKandil, Usama F.,$eauthor. =700 1\$aNaguib, Hamdy M.,$eauthor. =700 1\$aShaker, Nevein O.,$eauthor. =700 1\$aSoliman, Ahmed M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180034.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190037 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190037$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190037$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA690 =082 04$a624.1826$223 =100 1\$aBalanand, Santhosh,$eauthor. =245 10$aSurface Characteristics of Plasma Treated and Titanium Nitride (TiN) Deposited Aluminum Alloy /$cSanthosh Balanand, Shantanu Bhowmik, Madhav Datta, Ramkrishna Rane, Subrato Mukherjee. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis investigation highlights the rationale of the magnetron sputtering technique to deposit titanium nitride (TiN) coatings on aluminum alloy 2024 (AA 2024). TiN deposition on aluminum was systematically optimized, with nitrogen flow rate (mL/min) as the varying parameter. The developed TiN coatings were compared with the atmospheric pressure plasma treated and raw (uncoated) AA 2024 aluminum substrate surface. The crystalline phase formations of TiN on the alloy surface were studied using X-ray diffractometer technique. The scanning electron microscopy imaging technique was used to study the morphology of the formed ceramic layer. Fine and pore-free grains of TiN on the alloy surface were obtained at 1.5 mL/min nitrogen flow rate (TiN layer thickness ~ 630 nm). X-ray photoelectron spectroscopy analysis was conducted on the surface in order to characterize elemental composition of the surface. Surface characteristic and wettability studies on the developed coatings were conducted using atomic force microscopy (AFM) and by measurement of contact angle, respectively. The roughness parameter ( Ra ) (obtained from AFM) increased by ~72 % with TiN deposition on the AA 2024, while the contact angle value decreased by ~18 %. The adhesion of the coating to the metal substrate (using scratch test) and the Vickers hardness measurements were also performed. Corrosion resistance imparted by the coatings was also confirmed from the electrochemical measurements. A significant positive shift in the corrosion potential ( Ecorr ) value from -0.96 V to -0.75 V was observed from the analysis. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAluminum alloys. =700 1\$aBhowmik, Shantanu,$eauthor. =700 1\$aDatta, Madhav,$eauthor. =700 1\$aMukherjee, Subrato,$eauthor. =700 1\$aRane, Ramkrishna,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190037.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190005 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190005$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190005$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.118$223 =100 1\$aRao, K. P.,$eauthor. =245 10$aTextural Changes in Hot Compression of Disintegrated Melt Deposition (DMD)Processed AZ31-1Ca-1.5 Volume % Nano-Alumina Composite /$cK. P. Rao, C. Dharmendra, Y. V. R. K. Prasad, K. Suresh, M. Gupta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe development of texture in AZ31-1Ca-1.5 volume percent (vol. %) nano-alumina composite subjected to uniaxial compression is studied over large ranges of temperature and strain rate, and correlated with operative slip systems in the various domains of its processing map. The initial rod, synthesized via disintegrated melt deposition and subsequently extruded, has a fine grain size (23 ?m) and basal texture with (0001) planes parallel to the extrusion direction. The processing map exhibits four domains: Domain 1: 250350C and 0.00030.01 s -1 , Domain 1A: 350410C and 0.00030.01 s -1 , Domain 2: 410490C and 0.0020.2 s -1 , and Domain 3: 325410C and 0.610 s -1 . Microstructures in these four domains revealed dynamic recrystallization, although the mechanisms of slip and recovery are different. In Domain 1, basal slip is the dominating mechanism that produced strong basal textures. Recovery occurs via dislocation climb controlled by lattice self-diffusion, which is promoted by the fine grain size in the starting material. In Domain 1A, prismatic slip is the major deformation mechanism and the basal texture is reduced, and the prismatic planes are tilted towards the compression axis. At higher temperatures of Domain 2, in addition to basal and prismatic slip, pyramidal slip occurs, and cross-slip among the multiple intersecting slip planes is the recovery mechanism that destroys the initial basal texture. At higher strain rates, at which Domain 3 occurs, non-basal slip (prismatic and pyramidal) activity is higher than that for basal slip, and the basal texture is reduced, giving way to favorable prismatic slip orientations. The recovery in this domain occurs via dislocation climb, which is controlled by grain boundary self-diffusion. The activation parameters, tensile ductility, and fracture features further support the conclusions on the rate-controlling mechanisms occurring in each domain. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aComposite construction. =650 \0$aComposite materials. =700 1\$aDharmendra, C.,$eauthor. =700 1\$aGupta, M.,$eauthor. =700 1\$aR. K. Prasad, Y. V.,$eauthor. =700 1\$aSuresh, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190005.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180044 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180044$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180044$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aT175.C355 =082 04$a620.5$223 =100 1\$aTikale, Sanjay,$eauthor. =245 10$aThe Effect of Multi-Walled Carbon Nanotubes Reinforcement and Multiple Reflow Cycles on Shear Strength of SAC305 Lead-Free Solder Alloy /$cSanjay Tikale, K. Narayan Prabhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, the effect of multi-walled carbon nanotubes (MWCNT) reinforcement on joint shear strength and microstructural development of tin-3.0silver-0.5copper (SAC305)/copper solder joint subjected to multiple reflow cycles was investigated. The MWCNT-reinforced SAC305 solder systems (SAC305- x MWCNT; x =0.01, 0.05, 0.1, and 0.5 wt.%) were developed by a mechanical dispersion method. The microstructural, mechanical, and melting properties of SAC305 composite solders were evaluated as a function of different wt.% of MWCNT addition. The melting behavior of composite solders was analyzed using differential scanning calorimetry. The morphology and intermetallic compound growth at the solder joint interface were studied using scanning electron microscopy. The copper/solder/copper micro-lap-shear solder joint specimens reflowed for multiple reflow cycles were systematically characterized to evaluate the joint shear strength. The results showed that the reinforcement in the range of 0.010.05 wt.% of MWCNT resulted in the improvement of joint shear strength and better wettability compared to plain SAC305 solder alloy. Amongst all compositions analyzed, SAC305-0.05MWCNT nanocomposite suppressed the intermetallic compound layer growth effectively leading to improvement in the joint shear strength under multiple reflow cycles. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aCoating processes. =650 \0$aTitanium dioxide. =700 1\$aNarayan Prabhu, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180044.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190157 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190157$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190157$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.11$223 =100 1\$aAltay, Pelin,$eauthor. =245 10$aThe Effect of pH, Coagulation Bath, and Reduction on Characteristic Properties of Continuous Graphene Oxide Fiber /$cPelin Altay, zge Alptoga, Aysen nen, Nilgn Karatepe, Nuray Uar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis study focuses on the effect of different process parameters including pH of GO dispersion, hydrazine reduction, number of coagulation bath on the properties of graphene oxide (GO) fibers produced through wet spinning method. Produced GO fibers have been characterized by scanning electron microscopy, Raman, X-ray diffraction methods, and an electrical conductivity meter. Results show that pH3 hydrazine reduction causes an expansion of the fiber volume and formation of porous fiber structure with higher defects. The crystal structure of GO fibers was also observed to be affected by hydrazine reduction, leading to decreased interlayer spacing and increased crystalline size and number of layer as compared to the reference (unreduced) one. Single coagulation bath was found to result in crystal on the fiber surface because of the calcium chloride (CaCI 2 ) salt, which provides higher electrical conductivity than triple coagulation bath. The pH value of GO dispersion was found to influence the crystal structures of the GO fiber, resulting in lower interlayer spacing, lower crystallinity degree, and higher crystallite size in the pH5 sample as compared to that of pH3 for triple coagulation baths. The results obtained in this study are expected to contribute to and shed light for further studies on carbon-based fiber materials such as GO fiber and reduced GO fiber that can have different application fields including electronic smart textiles, graphene-based membranes, gas adsorption, energy application such as lithium ion battery, and ultrafiltration applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aFibrous composites. =650 \0$aOxide coating. =700 1\$aAlptoga, zge,$eauthor. =700 1\$aKaratepe, Nilgn,$eauthor. =700 1\$anen, Aysen,$eauthor. =700 1\$aUar, Nuray,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190157.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180167 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180167$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180167$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC189.5 =082 04$a531.1134$223 =100 1\$aWang, Dawei,$eauthor. =245 10$aThe Oxidation Stability and Magnetorheological Properties of MR Grease Based on Different Kinds of Base Oil /$cDawei Wang, Zhide Hu, Hua Yan, Hansong Zhang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMagnetorheological (MR) grease based on mineral oil, silicon oil, and polyalphaolefi was prepared directly by synchronizing with synthetic grease, respectively. The oxidation stability of each was measured using a pressurized differential scanning calorimeter, whereas sedimentation stability was evaluated by the natural settling process. The effects of base oil and magnetic field strength on MR response of the suspensions were investigated via measurement of the rheological properties, including storage modulus, loss modulus, and MR effect under dynamic oscillation test. It was confirmed that ethyl silicon oilbased MR grease has excellent oxidation stability, good sedimentation stability, and outstanding MR effect. In addition, the MR grease exhibited characteristics of a solid state both with and without magnetic field. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMaterials$xElectric properties. =650 \0$aMaterials$xMagnetic properties. =700 1\$aHu, Zhide,$eauthor. =700 1\$aYan, Hua,$eauthor. =700 1\$aZhang, Hansong,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180167.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190055 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190055$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190055$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA483.R393 =082 04$a671.5$223 =100 1\$aKashyap, B. P.,$eauthor. =245 10$aTreatment of Concurrent Microstructure Evolution and Deviation from Steady-State Flow in Constitutive Relationship for Superplastic Deformation /$cB. P. Kashyap. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSuperplasticity is the ability of certain polycrystalline materials to exhibit exceptionally large elongations by grain boundary sliding and its accommodation by diffusion, dislocation slip, or both. One of the critical requirements for this phenomenon to occur is the fine equiaxed grains, which should be stable during deformation at elevated temperature. Under this condition, there exists a unique relationship between stress and strain rate as a function of temperature and grain size, with the high values of strain rate sensitivity index m of greater than 0.3. However, there is ample evidence of the variation in flow stress with strain along with concurrent microstructural evolution. Often the microstructures are known not to be equiaxed yet exhibit superplasticity by rapid change in morphology and size during early stage of deformation. This leads to flow softening and hardening with strain as a result of the dominance of one type of change over the other. Mechanistically, accommodation of grain boundary sliding by grain boundary migration leads to grain growth, resulting in flow hardening, whereas the absence of the same may cause the formation of cavities because of stress concentration at triple points and at two-phase or particlematrix interphase boundaries. In view of this, the constitutive relationship needs to be modified by incorporating the dependence of stress on strain and concurrent microstructure changes. The present work critically examines the nature of stressstrain curves and microstructure evolution in an attempt to account for the nonsteady-state flow and attain a generalized form of constitutive relationship for superplastic deformation. An attempt is made to quantify the variations in flow stress and microstructures interdependently as well as with strain by exploring the suitable trend lines. These equations can numerically and physically help in correlating the microscopic and macroscopic properties to the mechanisms for superplastic deformation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aStrains and stresses$xMathematical models. =650 \0$aSuperplasticity. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190055.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180092 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180092$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180092$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1677 =082 04$a621.366$223 =100 1\$aNazeer Basha, D.,$eauthor. =245 10$aTribological Behavior of Surface Textured Gray Cast Iron at Different Texture Density by Ultrafast Laser /$cD. Nazeer Basha, G. Padmanabham, Ravi Bathe. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aLaser surface texturing process involves the creation of microfeatures, e.g., tiny dimples, that are usually distributed in a certain pattern, covering only a fraction of the surface of the material that is being treated. This process offers several advantages for tribological applications, including improved load capacity, wear resistance, lubrication lifetime, and reduced friction coefficient. In the present study, surface modification of gray cast iron using femtosecond laser irradiation is adopted in order to establish an optimal geometric pattern with dimple features and dimensions, to improve wear and friction behavior. The surface texturing of gray cast iron was done with the help of an ultrafast laser with a pulse duration of 100 fs and wavelength of 800 nm. The effect of a range of process parameters, such as pulse energy, scan velocity, and textured density, on the performance characteristics of laser-textured samples was investigated. The laser surface textures were examined using an opto-digital 3-D microscope. The friction and wear tests under starved lubrication condition were performed using a ball-on-disk tribometer. The textured surfaces cause a significant reduction in friction coefficient (by 72 %) and wear (by 19 %) over the untextured surfaces. Furthermore, an analysis of wear tracks using a scanning electron microscope and energy-dispersive x-ray spectroscopy show a significant improvement in wear resistance. The wear track of the textured surface exhibited a significant reduction of wear debris and was found to be smoother than the untextured surface. Among various patterns tried, the pattern with 55 % texture density gave the best results. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aFemtosecond lasers. =650 \0$aLasers$xIndustrial applications. =700 1\$aBathe, Ravi,$eauthor. =700 1\$aPadmanabham, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180092.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180123 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180123$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180123$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.118$223 =100 1\$aMallik, B.,$eauthor. =245 10$aTribological Performance of In Situ Reinforced Al-Based Metal Matrix Composite Processed by Spark Plasma Sintering /$cB. Mallik, K. Sikdar, D. Roy. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHigh resistance to material damage from protecting the deterioration of the contacting surfaces is of considerable interest in the design and selection of materials for tribological applications. The present investigation concerns the study of the wear properties of iron aluminide and aluminum oxide (Al 2 O 3 ) reinforced in situ metal matrix nanocomposite, fabricated by mechanical milling followed by spark plasma sintering (SPS), under fretting condition. The wear experiments were carried out in gross slip fretting conditions to investigate the wear performance of the composite against the Al 2 O 3 balls with ambient conditions of temperature (242C) and humidity (505 %) =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aComposite construction. =650 \0$aComposite materials. =700 1\$aRoy, D.,$eauthor. =700 1\$aSikdar, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180123.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190010 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190010$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190010$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN752.T54 =082 04$a672.3$223 =100 1\$aJha, Jyoti S.,$eauthor. =245 10$aUnderstanding Flow Behavior and Microstructure Evolution during Thermomechanical Processing of Mill-Annealed Ti-6Al-4V Titanium Alloy /$cJyoti S. Jha, Suraj P. Toppo, Rajkumar Singh, Asim Tewari, Sushil K. Mishra. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTitanium alloy in the mill-annealed condition has a significant store of energy because it is not fully recrystallized and the grains possess a very high dislocation density. It is well established that the extent of softening mechanisms like dynamic recrystallization/recovery (DRX/DRV) are dependent on the stored energy during hot deformation. In this case, stored energy in the prior worked material may facilitate the softening. The hot deformation behavior of mill-annealed Ti-6Al-4V is studied by hot compression tests in the temperature range of 750C950C and strain rate (?, , ?, , , , , , ) range of 0.00110 s -1 for 60 % deformation. The true stress-strain curve of the compression tests exhibits the variation in flow stress ( ? ) characteristics in a wide range of temperature and strain rate (T, ,, ?, , ?, , , , , , ). The activation energy calculated from the phenomenological constitutive equation is significantly higher than the self-diffusion activation energy, which suggests DRX as the main softening process. However, ? -> ? phase transformation below the ? -transition temperature during hot deformation substantiates the occurrence of a mechanism other than DRX. In the lower temperature regime T (<850C), softening is caused by the DRX process at a lower deformation rate ?, ?, , , , , (<0.01 s -1 ), whereas at a higher deformation rate, the grains are more deformed with very high grain average misorientation. In the high temperature regime, where ? -> ? phase transformation is very pertinent, it subsequently forms the transformed microstructure. The processing map shows the highest efficiency in the lower ?, , ?, , , , , , and temperature regime, whereas the least efficiency with instability is observed at high ?, , ?, , , , , , . Microstructure analyses reveal that the DRX/DRV and phase transformationassisted microstructure evolution in mill-annealed Ti-6Al-4V are the major deformation mechanisms. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aSteel$xThermomechanical treatment. =700 1\$aMishra, Sushil K.,$eauthor. =700 1\$aSingh, Rajkumar,$eauthor. =700 1\$aTewari, Asim,$eauthor. =700 1\$aToppo, Suraj P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190010.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180135 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180135$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180135$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN672 =082 04$a671.36$223 =100 1\$aMatijevic, Bozidar,$eauthor. =245 10$aUsing Thermal Gradient Measurements to Compare Bath Temperature and Agitation Effects on the Quenching Performance of Palm Oil, Canola Oil and a Conventional Petroleum Oil /$cBozidar Matijevic, Bruno F. Canale, Bozidar Liscic, George E. Totten. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (26 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA proprietary Liscic/Petrofer cylindrical Inconel 600 probe of 50-mm diameter and 200-mm length which was instrumented with three thermocouples on the same radius of the cross-section at the middle of the length was used to determine the differences in quenching performance of two vegetable oils, palm oil and canola oil, and they were compared to a locally produced conventional petroleum oil quenchant. The cooling curves and heat transfer performance of these oils were determined at different bath temperatures and agitation rates. The work was performed at the Quenching Research Centre located at the Faculty for Mechanical Engineering, University of Zagreb, Croatia. The results of this comparative study are reported herein. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aMetals$xQuenching. =700 1\$aCanale, Bruno F.,$eauthor. =700 1\$aLiscic, Bozidar,$eauthor. =700 1\$aTotten, George E.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180135.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190023 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190023$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190023$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.118$223 =100 1\$aDwivedi, Shashi Prakash,$eauthor. =245 10$aUtilization of Organic Waste and Inorganic Waste in Development of Green Hybrid Composite Material /$cShashi Prakash Dwivedi, Garima Dwivedi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAir pollution and soil pollution from organic and inorganic wastes are one of the major problems all over the world. Furthermore, disposal of these organic and inorganic wastes is very costly. In the present investigation, the organic waste considered is rice husk ash (RHA). Rice husk was collected from rice mill industries. The inorganic waste considered is fly ash. Fly ash was collected from thermal power plant industries. By utilizing these wastes in the development of composite materials, some environmental problems can be reduced. In this study, an attempt was made to develop AA6061 base composite material reinforced with different weight percentages of RHA and fly ash. Microstructure of RHA- and fly ashreinforced composite shows proper distribution of reinforcements. Maximum tensile strength was found to be 145.5 MPa for AA6061+5 % RHA+10 % fly ash composite. Minimum porosity and maximum hardness was found to be 0.80 % and 88 HRB, respectively, for AA6061+7.5 wt% RHA+7.5 wt% fly ash hybrid metal matrix composite. In the same way, minimum corrosion loss and minimum thermal expansion were 0.12 mg and 20 mm 3 for AA6061+7.5 wt% RHA+7.5 wt% fly ash hybrid metal matrix composite, respectively. Minimum water absorption and minimum soil degradation was also found for AA6061+7.5 wt% RHA+7.5 wt% fly ash hybrid metal matrix composite. However, density of composites continuously decreases by increasing the percentage of RHA and fly ash in the development of composites. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aComposite materials. =700 1\$aDwivedi, Garima,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190023.htm =LDR 03762nab 2200553 i 4500 =001 MPC20180136 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20180136$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20180136$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTE278.2 =082 04$a620.135$223 =100 1\$aSinha, Medhavi,$eauthor. =245 10$aVehicular Light Weighting by Finite Element Simulation of E GlassBased Composite Automotive Seat /$cMedhavi Sinha, R. K. Tyagi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe automobile industry has demonstrated itself to be one of the most quickly growing industries. However, the growth in the automotive industry has direct implications for fossil fuel reserves. The vigorously depleting fossil fuel reserves, the eminently increasing petroleum prices, the constant increase in pollution levels, and the hazardous effects of atmospheric environmental degradation are the driving forces for gravitation toward vehicular light weighting. The current article discuses the process of lightening the weight of front car seats, which is one of the most indispensable components of the automobile. This article demonstrates the feasibility of replacing metal automotive seats with E-Glassbased fiber-reinforced polymer (FRP) composite automotive seats. Various types of investigations and comparative analyses, such as analysis for displacement, force, force-to-weight ratio, maximum and minimum stresses, and unit cost of fiber composites, are performed on the conventional car seat composed of steel alloy 4340 and that composed of FRP composites. It can be demonstrated from the various analyses that a substantial weight reduction of front car seat is obtained with respect to alloy steel when FRPs are used as substitutional materials. The weight of the steel alloy front car seat is reduced by 79.76 % with the utilization of carbon fiber composite as an alternative material, whereas the component weight was reduced by 57.27 and 70.31 % with the utilization of glass fiber composite and Kevlar materials, respectively. A cost analysis is also performed, and it is determined that the costs of carbon fiber composite, glass fiber composite, and Kevlar are quite a bit higher than that of alloy steel. The stress analysis for alloy steel and fiber composites exhibits that the maximum stresses of glass fiber composite, carbon fiber composite, and Kevlar are about 1.95, 2.96, and 2.40 times higher than alloy steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aPavements, Concrete$xJoints. =650 \0$aReinforcing bars. =700 1\$aTyagi, R. K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20180136.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190021 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190021$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190021$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.A88 =082 04$a672.823$223 =100 1\$aAashranth, B.,$eauthor. =245 10$aWarm Working as a Potential Substitute for Hot Working of Austenitic Steel in Selected Applications /$cB. Aashranth, M. Arvinth Davinci, Dipti Samantaray, Utpal Borah. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe conventional manufacturing route for austenitic steels involves casting, ingot breakdown, subsequent hot working, and finally cold working, with numerous intermediate heat treatment stages. In this study, the potential of warm working to substitute some steps of the conventional manufacturing process is examined. A low-carbon austenitic stainless steel, SS304L, is subjected to cold, warm, and hot deformation in light of recent understanding of warm working. The deformation response in these two regimes is compared on the basis of metallurgical, mechanical, and process variables. Metallurgical response is compared on the basis of resultant grain size and stability of microstructure to subsequent heat treatment. The differences in mechanical response in the two regimes are evaluated through analysis of flow curves. Finally, the important but often ignored parameter of process stability is examined by performing nonisothermal deformation and examining the effect on microstructure. The results are used to propose some applications where warm working can substitute hot and cold working. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aAustenitic stainless steel. =650 \0$aStainless steel. =700 1\$aArvinth Davinci, M.,$eauthor. =700 1\$aBorah, Utpal,$eauthor. =700 1\$aSamantaray, Dipti,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 5 Special Issue on Recent Advances in Hot Deformation of Materials, Part 1.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190021.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190071 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190071$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190071$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA660.J64 =082 04$a621.366$223 =100 1\$aKurc-Lisiecka, Agnieszka,$eauthor. =245 10$aWeld Metal Toughness of Autogenous Laser-Welded Joints of High-Strength Steel Domex 960 /$cAgnieszka Kurc-Lisiecka, Aleksander Lisiecki. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe results of investigations on autogenous laser welding of 5.0-mm-thick high-strength steel Domex 960 are presented in this article. The experimental plates delivered directly from the steel manufacturer were used for butt joint welding. The disk laser with maximum output power (maximum capacity of the laser generator) of 3.3 kW, emitting at 1.03 ?m, and with the beam spot diameter of 200 ?m was used for the trails of welding. Initially, the bead-on-plate welding tests were carried out, and then the test butt joints were laser welded. The influences of basic technological welding parameters, especially the energy input of laser welding on the shape of the fusion zone, the microstructure of weld metal and heat affected zone, and the impact toughness were analyzed. Laser welding trials were conducted in a wide range of energy input from 100 to 400 J/mm. Despite the low energy input of the laser welding process and also the short cooling times t 8/5 , tendency to cold crack was found neither in the weld metal nor in the heat affected zone. The carbon equivalent (CET), determined by the chemical analysis of the experimental melt, was just 0.341, indicating moderate tendency to increase hardness after welding because of martensitic transformation. It was found that the energy input has a clear influence on the microstructure and the impact toughness of the weld metal. The weld metal of the test butt joint welded at the energy input of 198 J/mm showed the average impact toughness at approximately 80 % of the base metal, whereas the weld metal of the test butt joint welded at a lower energy input of 132 J/mm showed the average impact toughness at the level of just 60 % of the base metal of Domex 960 steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aStrains and stresses. =650 \0$aStrength of materials. =700 1\$aLisiecki, Aleksander,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 6 Special Issue on Laser Processing of Materials.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190071.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190145 =003 IN-ChSCO =005 20200129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 200129s2018\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190145$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190145$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aT173.8 =082 04$a004.6$223 =100 1\$aDobrzanski, Leszek A.,$eauthor. =245 10$aWhy Are Carbon-Based Materials Important in Civilization Progress and Especially in the Industry 4.0 Stage of the Industrial Revolution /$cLeszek A. Dobrzanski, Anna D. Dobrzanska-Danikiewicz. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2019. =300 \\$a1 online resource (34 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article presents a comprehensive literature study showing that, starting from the emergence of the species of homo sapiens, the progress of human civilization is strongly dependent on the development of materials, and over time this is mainly development of engineering materials and the accompanying increase in productive forces. There is no close correlation between changes, and especially between the development of the brain and technologies sequentially controlled by humans. The materials science appeared as an independent branch of knowledge only in the late 1950s. Technical aspects of the product launch on the market relate to several technical aspects; engineering design is a significant conceptual phase of this activity, and within it, the material design. The expected functional properties of the product will be assured only if the right expected material is used and is produced in a suitably selected expected technological process that will provide both the expected shape and other geometric features of the product, including assembly and the expected structure of the material, ensuring the expected mechanical, physical, and chemical properties of the material, the use of which ensures the expected application of the product. The given rule defines the paradigm of contemporary materials science and engineering. Without the use of engineering materials and without the development of manufacturing processes, it is impossible to manufacture any product and make it available to consumers. The material design process in history has gone through a long period of changes. Initially, for millions of years and almost a century ago, materials were selected based on the trial and error method, which is stage Materials 1.0. Currently, about 80 % of work in the field of engineering materials development and material design is carried out in accordance with the Materials 2.0 protocol. The Materials 2.0 protocol includes more systematic material research, ranging from conceptualization, systematic laboratory experiments to verify the idea, prototyping in the laboratory and real conditions, and testing and validating prototypes and life cycle assessment to use the results of research in product production. Materials 3.0 use computational materials science materials, and materials are computationally designed with a target functionality. Only the idea of Materials 4.0 overcomes human limitations in applying existing knowledge about the theory of materials, processing, and properties through the use of cyber-physical space. In manufacturing processes generally after the era of water and steam and mass production based on the division of labor with the use of electricity, and then the use of electronics and information technology for the automation of production processes, there is a dynamic use of cyber-physical systems, the Internet of objects, machine learning, artificial intelligence, and virtual reality, currently guaranteeing the production progress at the stage of the Industry 4.0 industrial revolution. So far, nine technologies have been designated as determining the change in industrial production at the Industry 4.0 stage. According to the authors of this article, it is necessary to augment this list by manufacturing processes and engineering materials as well as living and bioengineering machines; therefore, in total, there will be 12 technologies determining the changes in production in the Industry 4.0 stage. Omitting these issues would make it impossible to manufacture any products available on the market, and the idea of Industry 4.0 presented would be incomplete. The importance of carbon-based materials is also presented, and several results of our own research on various materials are presented, with an indication of application possibilities. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed January 29, 2020. =650 \0$aIndustries. =650 \0$aManufacturing processes$xAutomation. =700 1\$aDobrzanska-Danikiewicz, Anna D.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 8, Issue 3 Special Issue on Carbon Nanomaterials and Nanocomposites.$dWest Conshohocken, Pa. :$bASTM International, 2019$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190145.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190032 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190032$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190032$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.T5 =082 04$a620.189322$223 =100 1\$aChatterjee, Ritam,$eauthor. =245 10$aDynamic Recrystallization in Titanium Alloys: A Comprehensive Review /$cRitam Chatterjee, S. V. S. Narayana Murty, Alankar Alankar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (42 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article is an attempt at highlighting recent advances made for understanding and modeling the phenomenon of dynamic recrystallization (DRX) prevalent in titanium alloys. Research work in recent years has focused on providing a rigorous description of key factors that influence the DRX process such as the effect of grain size, stacking fault energy, and other microstructural descriptors, thermomechanical processing, etc. The key addition of this work to existing literature is a critical commentary of important experimental as well as modeling efforts in recent years related to observing DRX in hexagonal close-packed (hcp) metals. We have attempted to directly compare, with reference to experiments, the effects of process variables such as strain rate, temperature, and composition on the occurrence of DRX in titanium alloys. A comprehensive review has been made of the experiments that have been carried out specifically to observe DRX in titanium alloys. This can aid modeling and validation efforts to accurately capture different facets of DRX for titanium alloys and other hcp metals. A similar comparison of the drawbacks and insights obtained from applying various modeling strategies, viz., FEM-based, phenomenological, or grid-based numerical methods for various alloys can provide valuable insights to choose appropriate modeling schemes or develop novel techniques to predict aspects of DRX such as preferred nucleation sites and evolution of microstructure, including grain boundaries and primary and secondary phases. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aTitanium alloys. =700 1\$aAlankar, Alankar,$eauthor. =700 1\$aNarayana Murty, S. V. S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190032.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190072 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190072$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190072$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS209.5 =082 04$a673.722$223 =100 1\$aAthreya, C. N.,$eauthor. =245 10$aInfluence of Deformation Mode on Hot Deformation Behavior of CP Titanium /$cC. N. Athreya, S. Suwas, V. Subramanya Sarma. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTo obtain desired properties, the microstructure of metallic materials is tailored by subjecting them to different thermomechanical processing routes. In manufacturing industries, metallic materials are subjected to different hot deformation processes, viz , rolling, extrusion, and forging, during which materials undergo deformation under complex stress state. Therefore, it is important to understand the effect of deformation mode on microstructure evolution during hot deformation. In the present work, we report systematic studies performed on the influence of deformation mode on dynamic recrystallization behavior of titanium. Titanium specimens were deformed through uniaxial compression (UC) and plane strain compression (PSC) at temperatures of 1,023, 1,073, and 1,123 K, and at strain rates of 0.01-1 s -1 to an equivalent strain of 0.5. Hot deformation experiments were conducted in a Gleeble thermomechanical simulator in an argon atmosphere. The specimens were water quenched immediately after the deformation process to arrest microstructure. To understand the deformation behavior of hot deformed specimens, flow curve analysis was performed. The microstructural characterization was performed through electron backscattered diffraction technique. The dynamic recrystallization (DRX) fraction is temperature and strain rate dependent. Significant difference in DRX fraction between PSC and UC is observed at 1,123 K at a strain rate of 0.1 s -1 and 1 s -1 . In both, PSC- and UC-deformed specimens, DRX grains formed preferentially along grain boundaries through grain boundary bulging mechanism. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMetals$xHot working. =700 1\$aSubramanya Sarma, V.,$eauthor. =700 1\$aSuwas, S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190072.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190031 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190031$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190031$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS209.5 =082 04$a673.722$223 =100 1\$aOzturk, Utkudeniz,$eauthor. =245 10$aHigh-Temperature Deformation Behavior of 718Plus: Consideration of y' Effects /$cUtkudeniz Ozturk, Jose Maria Cabrera, Jessica Calvo, Abdelkrim Redjaimia, Jaafar Ghanbaja. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe hot deformation behavior of 718Plus is modeled through a physically based hybrid dislocation density model, which includes the effects of precipitating particles. It is well known that the service performance and hot flow characteristics of this alloy are strongly dependent on the microstructure, particularly the grain size and second-phase particles. Thus, comprehension and modeling of the hot flow behavior is an important task. In precipitation hardening alloys (superalloys, microalloyed steels, etc.), it is particularly challenging to model the microstructural evolution in the processing windows, where material softening and precipitation processes take place concurrently. In this work, the initial stages of the deformation are studied. A model based on dislocation density evolution is presented. As in conventional approaches, the dislocation density is considered as a competition between dislocation generation and dynamic recovery at the early stages of deformation. Recovery is assumed to be driven by glide and climb of dislocations, which are considered to be proportional to the strain rate and damped by the existence of second-phase particles. It is known that under high-temperature deformation conditions, 718Plus may undergo dynamic precipitation. Second-phase particles in the material may impede the grain boundary motion and contribute to an increase in flow stress. To account for the dynamic precipitation, the present model combines experimental results and precipitation models to predict volume fraction and particle size. The effect of aging is studied through transmission electron microscopy (TEM) characterization of the specimens from interrupted tests at the onset of dynamic recrystallization. Stress contribution due to different modes of dislocation precipitation interaction are modeled and integrated to the phenomenological dislocation density-based hardening models. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMetals$xHot working. =700 1\$aCabrera, Jose Maria,$eauthor. =700 1\$aCalvo, Jessica,$eauthor. =700 1\$aGhanbaja, Jaafar,$eauthor. =700 1\$aRedjaimia, Abdelkrim,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190031.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190109 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190109$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190109$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.T5 =082 04$a620.189322$223 =100 1\$aKommel, Lembit,$eauthor. =245 10$aPeculiarities of Microstructure Evolution and Property Changes of Titanium Alloys In Situ during Electric Forging /$cLembit Kommel. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe experimental studies of the parameters of hot electric forging were carried out on industrial heat resistance ( a + β ), (near- a ), and ( a '+ β ) titanium alloys. It was established that simultaneous fast Joule heating with a high-density electric current and an initial temperature of hot intense plastic deformation are important parameters for the electric forging of heat resistance titanium alloys. The heating rate dependence on electric current density and thermophysical properties of metal, as well as deformation temperature dependence on axial compression stress and mechanical strength of heated metal under compression as the main parameters of electric forging, were chosen. To calculate the processing parameters, we investigated the evolution of the thermophysical properties and mechanical strength of selected titanium alloys at a heating rate of 50 degrees -1 at a temperature up to 1,200degree C. Microstructural evolution and the phase transformation temperature were determined using optical and scanning electron microscopes. The results show that the grinding efficiency of the coarse-grained microstructure depends on the increase of the heating rate, and the formation of uniaxial ultrafine alpha-phase grains depends on an increase of the compressive stress or decrease in the deformation temperature. It can be argued that the compressor blades made of titanium alloys for aircraft turbojet engines had increased ductility, stability, and high-cyclic fatigue strength, as well as increased operating life at ambient temperatures. The results can be used to model and calculate the rational parameters of electric forging to improve the operational properties of the final products. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aTitanium alloys. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190109.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190034 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190034$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190034$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669.96142$223 =100 1\$aKumar, Atul,$eauthor. =245 12$aA Study of Recrystallization Behavior of Two Ni-Cu-Containing High-Strength Steels with Different Mn Contents /$cAtul Kumar, T. V. V. S. Vara Prasad, M. Nazeer, K. Gopinath, R. Balamuralikrishnan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe Defence Metallurgical Research Laboratory (DMRL) has been investigating several high-strength and high-toughness steels in the past few decades for various defense applications. As a part of this work, two novel low-carbon steels - each containing 4-6 wt% Ni+Cu of similar strength level, one with high Mn (~1 wt%) and one with low Mn (~0.3 wt%)were investigated. In order to optimize the rolling schedules during production, it is necessary to understand the recrystallization behavior of these two steels during hot deformation. Usually, the recrystallization behavior of materials that do not undergo phase transformations (viz. aluminum, copper, etc.) is commonly studied using microstructural techniques for identification of fraction of recrystallized grains. But, as the steels in the present study undergo phase transformation wherein the austenitic structure at deformation temperature is transformed to martensitic/bainitic structure during cooling, it is challenging to track the recrystallization process directly from the microstructure. Therefore, the recrystallization behavior was investigated by conducting double-hit compression tests (DHCTs) using Gleeble. Fractional softening values were determined from DHCT data using various methods, such as the offset method, back-extrapolation method, and mean flow stress method. The mean flow stress method was found to be more reliable and thus was adopted in this study. The effects of different deformation temperature (850degree C-1,050degree C) and intermediate static recrystallization time (ISRT) (10, 100, and 500 s) on fractional softening were studied. Temperature for 50 % recrystallization ( T 0.5 ), determined as the temperature for 50 % fractional softening, was seen to reduce with an increase in ISRT. Steel with lower manganese content showed relatively lower fractional softening values and thus relatively higher T 0.5 , as compared with that for the steel with higher manganese content, for all three ISRTs. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aSteel, High strength. =700 1\$aBalamuralikrishnan, R.,$eauthor. =700 1\$aGopinath, K.,$eauthor. =700 1\$aNazeer, M.,$eauthor. =700 1\$aVara Prasad, T. V. V. S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190034.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190006 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190006$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190006$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA690 =082 04$a624.1826$223 =100 1\$aSitdikov, O. S.,$eauthor. =245 10$aEffect of Multidirectional Forging with Decreasing Temperature on the Microstructure and Microhardness of the Aluminum-Magnesium-Scandium-Zirconium Alloy /$cO. S. Sitdikov, E. V. Avtokratova, M. A. Murzinova, M. V. Markushev. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aEvolution of the microstructure and microhardness of the cast and homogenized aluminum alloy 1570C (aluminum [Al]-5 magnesium [Mg]-0.18 manganese [Mn]-0.2 scandium [Sc]-0.08 zirconium [Zr], wt. %) were studied under multidirectional forging (MDF) with decreasing the temperature. Sequential compression passes were performed at a strain rate of 10 -2 s -1 with 90 changing of the loading axes from pass to pass; with the strain per pass of ? e =0.7 and the 25Degree C decrease of temperature in each pass, starting from 450Degree C ( T =0.8 Tm ). It has been shown that the alloy ductility was sufficient for straining the samples without cracking up to the total strain of s e =10.5 at 100 degree C (about 0.4 Tm ). In the initial state, the alloy possessed a coarse-grained structure with a grain size of about 25 ?m and a uniform distribution of the Al 3 (Sc,Zr) nanoscale aluminides. MDF led to a continuous grain refinement. At relatively low strains, s e =4.2 (and high temperatures, T =325 Degree C), new grains were evolved mainly in the mantle areas of initial grains, resulting in the formation of a bimodal (sub)grain structure, which persisted up to s e =8.4 ( T =175Degree C). During further MDF, the alloy structure became more homogeneous and fine-grained, and at s e =10.5 ( T =100Degree C), it almost completely transformed into a nanocrystalline grain structure with a crystallite size of 100-150 nm, stabilized by nanodispersed Al 3 (Sc,Zr) precipitates. The average size of the deformation-induced (sub)grains in the whole range of strains (temperatures) studied obeyed a power-law function of the flow stresses with the exponent close to -0.75. The microhardness testing showed that MDF did not lead to the notable alloy hardening in the samples deformed at relatively high temperatures ( T >325Degree C) and low strains (s e <4.2). With further processing, in contrast, a significant (about 1.5 times) hardness increase took place in accordance with the Hall-Petch relationship. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aAluminum alloys. =700 1\$aAvtokratova, E. V.,$eauthor. =700 1\$aMarkushev, M. V.,$eauthor. =700 1\$aMurzinova, M. A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190006.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190036 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190036$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190036$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS209.5 =082 04$a673.722$223 =100 1\$aKumar, Deepak,$eauthor. =245 10$aStudy on Hot Deformation Behavior of High Carbon Low Alloy Steel by Constitutive and ANN Modeling and Development of Processing Maps /$cDeepak Kumar, Sumit Kumar, S. K. Nath. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe hot deformation behavior of high carbon low alloy steel was investigated by isothermal compression tests on Gleeble 3800 thermomechanical simulator in the temperature range of 850Degree C-1,100Degree C and in the strain rate range of 0.01 s -1 to 10 s -1 . The Arrhenius-type constitutive equations model and the artificial neural network (ANN) model were developed to investigate and predict the flow behavior of steel. The result of constitutive modeling showed that the material constants can be represented as a sixth degree polynomial function. The average apparent activation energy for hot deformation decreased from 441 kJ/mol to 350 kJ/mol, and the stress exponent decreased from 5.6 to 4.01, indicating the deformation mechanism to be dislocation glide and climb. The accuracy and effectiveness of the two models were compared using correlation coefficient and mean absolute error. Results showed that the ANN model almost perfectly predicted the flow behavior in terms of flow stress. Mean absolute errors in the Arrhenius-type constitutive equations model and ANN model are 7.2 % and 2.1 %, respectively. This confirms the better predictability of the ANN model over the analytical constitutive equations-based model. Processing maps were constructed using the dynamic material model, modified dynamic material model, and strain rate sensitivity maps at true strains of 0.3 and 0.6, which were correlated with microstructure evolution. It was observed that the instability region shrinks with increasing strain, which can be attributed to the fact that, for longer deformation, the stress value becomes constant and hardening-softening cycles cease to exist. Metallographic investigations showed the variety of instabilities such as cracks, voids, pores, and adiabatic shear bands, confirming the unstable region predicted by the processing maps. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMetals$xHot working. =700 1\$aKumar, Sumit,$eauthor. =700 1\$aNath, S. K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190036.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190013 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190013$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190013$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA684 =082 04$a624.1821$223 =100 1\$aKumar, Sanjeev,$eauthor. =245 10$aUnderstanding Hot Workability and Flow Stress Prediction through Processing Map with Microstructural Correlation for HY85 Steel /$cSanjeev Kumar, S. K. Rajput, Niranjan Kumar, S. K. Nath. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, the hot compression tests of HY85 steel have been experimented by using thermomechanical simulator Gleeble 3800 in hot compression temperature range of 750Degree C-1,100Degree C under strain rates between 0.001-10 s -1 up to true strain 0.7. It is worth noticing from the results that the flow stresses are dependent on the combination of temperature and strain rate. Adiabatic heating corrections of experimental flow stress data were carried out and were used to model stress-strain curves. The predictability of these stress-strain curves was confirmed from experimental results. True stress-true strain curves show the peak stresses followed by softening probability because of the existence of dynamic recrystallization (DRX). The apparent activation energy is calculated to be 360 KJ/mol using the sinh type constitutive equation, and it is observed that its value decreases with increasing strain. Hot compression of HY85 steel is controlled by dislocation climb and glide ( n =6.3). The processing maps are plotted based on different dynamic materials modeled with strain rate versus temperatures. The flow localization is one of the primary factors with resulting instability, which is revealed from the microstructure. Moreover, the partial DRX was noticed besides the grain boundaries and compression bands. Workability regions were identified using processing maps in the domain of strain rate and temperature and verified with microstructures. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aSteel, Structural. =700 1\$aKumar, Niranjan,$eauthor. =700 1\$aNath, S. K.,$eauthor. =700 1\$aRajput, S. K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190013.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190081 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190081$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190081$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS209.5 =082 04$a673.722$223 =100 1\$aAnoop, C. R.,$eauthor. =245 10$aDevelopment and Validation of Processing Maps for Hot Deformation of Modified AISI 321 Austenitic Stainless Steel /$cC. R. Anoop, R. K. Singh, Ravi Ranjan Kumar, Jayalakshmi Miyala, S. V. S. Narayana Murty, K. Thomas Tharian. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHot deformation studies and optimization of hot working parameters and corresponding microstructure evolution were explored in a modified AISI 321 austenitic stainless steel. Hot compression tests were carried out in the temperature range of 800Degree C-1,100Degree C and five different strain rates (0.001-10 s -1 ). Processing maps were developed based on the results of hot compression tests, employing the principles of dynamic materials model and various domains of microstructure evolution were identified. The stable and unstable domains, as well as various domains indicating other microstructural reconstitutive mechanisms, including dynamic recrystallization (DRx), were identified with the aid of a processing map. The domain for DRx was confirmed by microstructural analysis of deformed specimens and also from the inflections in hardening curves. The processing regime for microstructural control was identified, and the results were validated by actual forging trials on a 1,000-T hydraulic forging press. The grain size of laboratory-tested hot-compressed samples and industrially forged billets exhibited excellent correlation. Constitutive equation for hot deformation was also developed for the steel based on hot compression test results. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMetals$xHot working. =700 1\$aKumar, Ravi Ranjan,$eauthor. =700 1\$aMiyala, Jayalakshmi,$eauthor. =700 1\$aMurty, S. V. S. Narayana,$eauthor. =700 1\$aSingh, R. K.,$eauthor. =700 1\$aTharian, K. Thomas,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190081.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190087 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190087$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190087$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS209.5 =082 04$a673.722$223 =100 1\$aAnoop, C. R.,$eauthor. =245 10$aHot Deformation Studies and Optimization of Hot Working Parameters in Custom 465® Martensitic Precipitation Hardenable Stainless Steel /$cC. R. Anoop, R. K. Singh, Ravi Ranjan Kumar, M. Jayalakshmi, S. V. S. Narayana Murty, K. Thomas Tharian. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHot deformation studies and optimization of hot working parameters and corresponding microstructure control were explored in Custom 465® ultrahigh-strength precipitation hardenable martensitic stainless steel. Hot compression tests were carried out in the temperature range of 800Degree C-1,100Degree C and at five different strain rates (0.001-10 s -1 ). Processing maps were developed based on the results of hot compression tests, employing principles of the Dynamic Materials Model, and various domains of microstructure evolution (in the austenite phase) were identified. The stable and unstable domains as well as domains indicating dynamic recrystallization (DRx) were identified from the processing map. The domain for DRx was confirmed by detailed microstructural investigations (prior austenite grains) of the respective water-quenched specimens, as well as from the inflections in hardening curves. The optimum conditions for processing Custom 465 steel were suggested as T =1,075Degree C and ϵ, ?, , =, 10, , -, 3, , , s, -, 1, , , , , , and can be used for initial ingot breakdown (cogging) operations and T =925Degree C and ϵ, ?, , =, 10, , -, 3, , , s, -, 1, , , , , , for finish forging operations to obtain grain size control. The value of the activation energy for hot deformation was calculated to be 543.88 kJ/mol for this steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMetals$xHot working. =700 1\$aJayalakshmi, M.,$eauthor. =700 1\$aKumar, Ravi Ranjan,$eauthor. =700 1\$aNarayana Murty, S. V. S.,$eauthor. =700 1\$aSingh, R. K.,$eauthor. =700 1\$aThomas Tharian, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190087.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190078 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190078$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190078$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS209.5 =082 04$a673.722$223 =100 1\$aPanda, Rajiv,$eauthor. =245 10$aHot Deformation Behavior of AA2024 with and without In Situ Titanium Diboride Dispersoids /$cRajiv Panda, R. K. Gupta, Animesh Mandal, P. Chakravarthy. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAA2024 is known for its good combination of mechanical properties and is widely used in aircraft fuselage and other aerospace applications. However, because of its relatively lower yield strength, it has limited application in high-stress regions. In alloy AA2024, when titanium diboride particulates are embedded uniformly, it is expected to improve the strength of alloy by working as particulate dispersed composite. However, deformation of such metal matrix composite (MMC) is likely to be difficult and different from the base alloy. In this work, the deformation behavior of AA2024 alloy and its composite with titanium diboride particles developed in situ through salt-metal reaction have been studied. Hot deformation behavior was studied through hot isothermal compression tests over a temperature range of 300Degree C-450Degree C and strain rate from 0.01-10 s -1 . The results show that there is an increase in flow stress with an increase in strain rate and a decrease in flow stress with an increase in temperature. Processing maps were generated based on the dynamic material model to identify the stable and unstable regions for hot working. The strain rate sensitivity of the composite has been compared to base alloy AA2024. Deformation parameters were calculated from the stress-strain data, and constitutive equations have been generated. Softening in alloy and in MMC is found to be caused by dynamic recrystallization. Microstructural modifications that are caused by titanium diboride reinforcement and its impact during hot deformation are reported. The safe zones for the hot working of both base alloy and MMC were found to be in the range of 380Degree C to 450Degree C in a strain rate of 0.001-10 s -1. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMetals$xHot working. =700 1\$aChakravarthy, P.,$eauthor. =700 1\$aGupta, R. K.,$eauthor. =700 1\$aMandal, Animesh,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190078.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190024 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190024$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190024$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA462 =082 04$a620.11223$223 =100 1\$aKrishnan, A. Sarath,$eauthor. =245 10$aHot Workability and Microstructure Control of Aluminum-2.5 Copper-1.5 Magnesium Alloy /$cA. Sarath Krishnan, V. Anil Kumar, R. K. Gupta, C. Deepumon, S. V. S. Narayana Murty. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAluminum-2.5 copper-1.5 magnesium alloy is an important aerospace alloy and is extensively used in the fabrication of aerospace and aircraft systems. Hot working parameters for the alloy have been generated through hot isothermal compression testing at different temperatures (673-748 K at an interval of 25 K) and at strain rates of 0.01 to 10 s -1 . Hot workability of alloy has been established by using the instability criteria and validating the same with microstructural evolution. Further, the Holloman parameter was calculated, and the constitutive equation has been derived. Optimum parameters for the hot deformation were evolved avoiding the unstable metal flow regimes of 673-760 K at 0.1 to 1 s -1 . Maximum power efficiency in the dynamic recrystallization domain of the alloy is found to be ~0.6, indicating stable material flow during hot deformation. Strain rate sensitivity ( m ) value of 0.25-0.35 is observed in the stable regime at strain rates of 0.01-0.1 from 698 to 748 K indicating superplastic flow domain. Very fine recrystallized grains can be seen at higher temperatures greater than 723 K and lower strain rates of 0.1 and 0.01 s -1 , which grow further with an increase in temperature, indicating onset of grain growth. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aAlloys$xTesting. =700 1\$aDeepumon, C.,$eauthor. =700 1\$aGupta, R. K.,$eauthor. =700 1\$aKumar, V. Anil,$eauthor. =700 1\$aMurty, S. V. S. Narayana,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190024.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190204 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190204$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190204$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN700 =082 04$a620.1617$223 =100 1\$aKoundinya, N. T. B. N.,$eauthor. =245 10$aExploring the Safe Hot Working Regime of Creep-Resistant Mg-3Ca-2Sn-1Al Alloy /$cN. T. B. N. Koundinya, K. Rangan, S. V. S. Narayana Murty, Ravi Sankar Kottada. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHot workability characteristics of a recently developed rare-earth-free creep-resistant magnesium alloy Mg-3Ca-2Sn-1Al (XTA321) is evaluated using the processing map approach. The processing map is established using the flow stress data from constant strain rate compression tests conducted in the temperature and strain rate range of 300Degree C-500Degree C and 10 -3 -10 s -1 , respectively. The processing map exhibits a hot workability domain between 475Degree C to 500Degree C and in the strain rate range of 10 -2 to 10 -1 s -1 . Correlation of post-deformation microscopy with kinetic analysis is carried out to identify the possible softening mechanism in the hot working domain. The significant portion of the processing map falls in the instability regime, having shear band formation as the prime microstructural feature. The poor workability of the XTA321 vis-a-vis most of the magnesium alloys can be attributed to the presence of a high volume fraction of the strong second phase in the microstructure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aHeat resistant alloys. =700 1\$aKottada, Ravi Sankar,$eauthor. =700 1\$aMurty, S. V. S. Narayana,$eauthor. =700 1\$aRangan, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190204.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190110 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190110$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190110$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS209.5 =082 04$a673.722$223 =100 1\$aKoundinya, N. T. B. N.,$eauthor. =245 10$aUnderstanding the Hot Working Behavior of a Ni-Base Superalloy XH 67 via Processing Map Approach /$cN. T. B. N. Koundinya, K. Sri Bharadwaj, E. Nandha Kumar, S. V. S. Narayana Murty, Ravi Sankar Kottada. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHot deformation behavior of nickel-based superalloy XH 67 (Ni-18.5Cr-4.5Mo-4.5W-3.0Fe-2.5Ti-1.2Al) was investigated in the temperature range of 900Degree C-1,200Degree C and in the strain rate range of 10 -3 -10 s -1 . A processing map was generated from the flow stress data. Detailed postdeformation microscopy was carried out to understand the microstructural evolution during hot deformation. Correlation of the kinetic analysis together with microstructural characterization studies was accomplished to identify the rate controlling mechanism. An increase in the fraction of ∑, 3, , , , boundaries is observed with an increase in the strain rate at 1,150Degree C. In the temperature range of 1,100Degree C-1,200Degree C, discontinued dynamic recrystallization has been identified as the major softening mechanism. Based on the critical analysis of the mechanical data together with microstructural analysis, the safe hot working regime for the XH 67 alloy is established to have a temperature range of 1,100Degree C-1,200Degree C and a strain rate range of 10 -3 to 5-10 -2 s -1. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMetals$xHot working. =700 1\$aKottada, Ravi Sankar,$eauthor. =700 1\$aNandha Kumar, E.,$eauthor. =700 1\$aNarayana Murty, S. V. S.,$eauthor. =700 1\$aSri Bharadwaj, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190110.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190045 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190045$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190045$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS209.5 =082 04$a673.722$223 =100 1\$aNeelima, P.,$eauthor. =245 10$aComparison of Prediction Capabilities of Flow Stress by Various Constitutive Equation Models for Hot Deformation of Aluminum Matrix Composites /$cP. Neelima, S. V. S. Narayana Murty, P. Chakravarthy. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aOne of the important objectives of studies on the hot deformation of materials is the development of constitutive equations that represent the flow stress of the material as a function of strain, strain rate, and temperature useful for the structural designers in finite element analysis. While the constitutive analysis is fairly simple for pure metals and dilute alloys at high temperatures and low strain rates (low flow stresses), it can get complicated at high stresses and with the presence of a second phase, such as those in metal matrix composites. In the present work, the hot deformation behavior of aluminum matrix composites was studied by developing constitutive equations using JohnsonDegree Cook (JC), modified JC (m-JC), Arrhenius, and modified Zerilli and Armstrong (m-ZA) models, and the prediction capability of these models was compared based on average absolute error ( ? ). Further, the effect of reinforcement on activation energy of these composites was studied by varying parameters, viz., nature of reinforcement, volume fraction, and size. Out of the four constitutive models studied, the average absolute error is lowest for m-JC and Arrhenius models, and the flow stress values predicted by these two models compare well with the experimental data. Material constants of all the constitutive models for silicon carbide particulate (SiC p )-reinforced AA2124 composites with various volume fractions (5-30 %) were evaluated and provided as a database for the numerical simulations of hot deformation of these composites. To validate the constitutive equations, power dissipation maps have been developed for AA2124-15 vol % SiC p -reinforced composites, and it was found that the predicted flow stress data obtained from m-JC and Arrhenius equations could successfully reproduce the efficiency of power dissipation, indicating their better predictability of flow stress over JC and m-ZA models. Constitutive equations are quantified for 28 aluminum alloys and their composites, and physical interpretation of the constants of Arrhenius equation was provided. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aDeformations (Mechanics) =650 \0$aMetals$xHot working. =700 1\$aChakravarthy, P.,$eauthor. =700 1\$aNarayana Murty, S. V. S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190045.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190011 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190011$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190011$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a671.52$223 =100 1\$aKar, Amlan,$eauthor. =245 10$aMechanism of Variation in High-Temperature Grain Stability of Aluminum in Dissimilar Friction Stir Welds /$cAmlan Kar, Satish V. Kailas, Satyam Suwas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the dissimilar Friction Stir Welding (FSW) of aluminum to titanium, a large fraction of titanium particles is inhomogeneously distributed in the weld nugget and their distribution is highly complex. Such a distribution can have an immense influence on the grain stability of the weld nugget, which decides its mechanical properties at the high temperatures experienced in critical applications. The present investigation highlights the variation in grain structure at the top surface and center of the weld nugget. The results show that the microstructure at the surface of the weld contains a higher fraction of fine titanium particles, refined grains of aluminum and high-angle grain boundaries, and a lower intensity of shear texture components when compared to the center of the weld nugget. The variation in the grain stability of the weld was correlated with the qualitative variation in the strain rate and temperature in the weld. It is proposed that the formation and distribution of a high fraction of fine titanium particles results in superior grain stability of aluminum at the surface of the weld due to arrest of the grain boundary mobility against grain growth. This mechanism and methodology can be applied in developing metal matrix composites with superior mechanical properties as well. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aFriction stir welding. =700 1\$aKailas, Satish V.,$eauthor. =700 1\$aSuwas, Satyam,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190011.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190095 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190095$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190095$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC880.4.T8 =082 04$a551.55$223 =100 1\$aGupta, Pradeep,$eauthor. =245 10$aHigh Velocity and Temperature Effects on the Bending Behavior of Nickel Nanowire: A Large-Scale Molecular Dynamics Simulation Study /$cPradeep Gupta, Krishna Chaitanya Katakam, Natraj Yedla. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aWe performed classical molecular dynamics (MD) simulation of bending of large-size nickel nanowire (NW) of size 28 a (x-axis) by 284 a (y-axis) by 28 a (z-axis) comprising of 925,965 atoms (where a =3.52 -). Embedded atom method potential is used for modeling the interactions between nickel atoms. Bending studies have been carried out at temperatures in the range of 300 K-1,500 K. A rigid diamond tip is used to apply force on the NW at a velocity of 100 m/s along z-direction [0 0 -1]. The load time results show that as the temperature increases the yield load decreases as expected and is more significant at temperatures higher than 900 K. The structural studies are carried out by centro-symmetry parameter (CSP) and radial distribution function (RDF) analysis. The CSP analysis reveals the formation of stacking faults in the NW regions below the indenter tip, indicating localized plastic deformation. The RDF analysis reveals that with an increase in temperature the regions in the NW below the indenter tip become disordered. Dislocation extraction algorithm analysis carried out for understanding the plastic deformation mechanism reveals that the deformation mechanism is by slip by Shockley partial dislocations. We also observed twins in a few regions of the NW. The fracture features of the NW suggest ductile nature. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aMolecular dynamics. =700 1\$aKatakam, Krishna Chaitanya,$eauthor. =700 1\$aYedla, Natraj,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190095.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190117 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190117$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190117$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1150 =082 04$a668.412$223 =100 1\$aPatil, Jeet P.,$eauthor. =245 10$aContact Analysis for Contact Thermoforming of PMMA Sheet /$cJeet P. Patil, Yogesh S. Gaikhe, Vilas Nandedkar, Sushil K. Mishra, Sandip K. Saha. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe ability to produce products with more uniformity in the wall thickness distribution makes contact thermoforming the most suitable optical product processing method. Among all the process parameters, the contact condition significantly affects the structural strength and the optical properties of the product. Thus, it is imperative to investigate the effect of change in the contact conditions on product thickness. Hence, in this study, experimental investigations on contact conditions were performed considering poly(methyl methacrylate) as the sheet material and stainless steel 304 as the punch material. Experiments were conducted to examine the effect of temperature on the coefficient of friction (mechanical contact condition) and the effect of pressure on the thermal contact conductance (thermal contact condition). It was found that the contact conditions change significantly with changes in the operating conditions. Furthermore, numerical simulations were performed, considering isothermal processing and nonisothermal processing with constant and variable contact conditions to identify the effect of the change in contact condition on the product thickness. It was found that the change in contact condition has a considerable effect on the product thickness distribution. This study shows the importance of incorporation of the change in the contact condition for realistic simulations. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aThermoforming. =700 1\$aGaikhe, Yogesh S.,$eauthor. =700 1\$aMishra, Sushil K.,$eauthor. =700 1\$aNandedkar, Vilas,$eauthor. =700 1\$aSaha, Sandip K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 2 Special Issue on Recent Advances in Hot Deformation of Materials, Part 2.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190117.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190035 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190035$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190035$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD502 =082 04$a541.394$223 =100 1\$aKeddam, M.,$eauthor. =245 10$aModeling of the Kinetics of Boron Diffusion in Dehydrated Paste Pack-Borided AISI M2 Steel Based on Two Mathematical Approaches /$cM. Keddam, M. Kulka. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this work, two mathematical approaches were used in order to determine the values of activation energies in the iron monoboride (FeB) and diiron boride (Fe 2 B) layers on AISI M2 steel. The required experimental data about the boriding kinetics of AISI M2 steel were taken from the literature to estimate the values of boron diffusion coefficients in the FeB and Fe 2 B layers in the range of 1,173 K to 1,273 K produced by the dehydrated paste pack-boriding. The first approach was based on the integral method, whereas the second approach employed the Dybkov model. The estimated values of activation energies for boron diffusion in the FeB and Fe 2 B layers were in the range of 232.77-246.86 kJ mol -1 and 218.58-231.29 kJ mol -1 , respectively. Finally, the experimental thicknesses of FeB and (FeB+Fe 2 B) layers obtained for 1, 3, 5, and 7 h at 1,173, 1,223, and 1,273 K were compared with the predicted thicknesses by using these two approaches. A good concordance was achieved between the experimental data and the simulated results. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aChemical kinetics. =700 1\$aKulka, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 3 Special Issue on Advances in Boronizing and Related Technologies.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190035.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190074 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190074$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190074$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.1866$223 =100 1\$aCampos-Silva, I.,$eauthor. =245 10$aApparent Fracture Toughness of the CoB-Co2B Interface /$cI. Campos-Silva, E. J. Hern-ndez-Ram-rez, H. I. Mondrag-n-Nava, A. Contreras-Hern-ndez, D. Fern-ndez-Vald-s, A. Meneses-Amador, A. M. Delgado-Brito. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, new results for the interfacial fracture toughness of the CoB-Co 2 B layer formed at the surface of the ASTM F1537, Standard Specification for Wrought Cobalt-28Chromium-6Molybdenum Alloys for Surgical Implants (UNS R31537, UNS R31538, and UNS R31539) , alloy were estimated. Initially, the cobalt boride layers were developed by means of the powder-pack boriding process at 1,173 K with 6 h of exposure, and 1,223 K with 8 h of exposure. The depth-sensing Vickers microindentation tests were performed using applied loads ranging between 1 and 2.3 N to generate a crack along the CoB-Co 2 B interface. The apparent fracture toughness (, K, ca, , , ), , , , of the CoB-Co 2 B interface was estimated using a half-penny cracking model and considering the interfacial values of the Young-s modulus, hardness, and the critical point (P, c, , , , , , a, c, , , , , ), in which P, c, , , , , was considered as a criterion of the adhesion between CoB and Co 2 B. To verify the influence of the cobalt boride layer thickness and the magnitude of the residual stresses developed on CoB-Co 2 B interface, the cracking model was extended to estimate the K, ca, , , , , , for the boriding condition at 1,273 K with 6 h of exposure. In addition, the magnitude of the shear stresses on the CoB-Co 2 B interface was analyzed by the finite element method as a function of the indentation loads of 1 and 2.3 N using the boriding conditions of 1,173 K with 6 h of exposure and 1,223 K with 8 h of exposure. The results showed that the interfacial fracture toughness of the CoB-Co 2 B increased as a function of the CoB layer thickness, whereas the magnitude of the compressive residual stresses decreased for the thicker cobalt boride layer formed at 1,273 K with 6 h of exposure. Finally, the distribution of the maximum shear stresses located on the CoB-Co 2 B interface oscillated from 3.9 to 4.4 GPa according to the indentation loads. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aFracture mechanics. =700 1\$aContreras-Hern-ndez, A.,$eauthor. =700 1\$aDelgado-Brito, A. M.,$eauthor. =700 1\$aFern-ndez-Vald-s, D.,$eauthor. =700 1\$aHern-ndez-Ram-rez, E. J.,$eauthor. =700 1\$aMeneses-Amador, A.,$eauthor. =700 1\$aMondrag-n-Nava, H. I.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 3 Special Issue on Advances in Boronizing and Related Technologies.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190074.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190091 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190091$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190091$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA684 =082 04$a624.1821$223 =100 1\$aKrukovich, M. G.,$eauthor. =245 10$aTechnology to Improve the Performance Properties of Heterogeneous Boronized Layers /$cM. G. Krukovich. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe aim of this work is to develop a technology for obtaining heterogeneous boronized layers of considerable thickness on structural steels to ensure higher wear resistance. Typically, boronized layers are obtained at different temperatures (1,150-550Degree C) by the diffusion and diffusion-crystallization mechanisms of mass transfer. The heterogeneous layers with a dispersed distribution of borides in the a-solid solution are obtained by the diffusion-crystallization mechanism, with the liquid-crystalline state of the treated surface. This aim is achieved by stepwise temperature treatment. At the beginning, the borating is carried out in the liquid-crystalline state of the surfaces, and then in the crystalline state. To efficiently determine the processing temperature in the crystalline and liquid crystal states of the surface, for the first time, the five-component scheme diagram of the state iron-chromium-nickel-manganese-boron in the traditional temperature-concentration coordinates was built. At the base of this scheme diagram is a pentagon with a divergent concentration grid. The amount of liquid phase during the processing in the liquid crystal state of the surface should not exceed 20 %. After this treatment, the boronized layers consist on the surface of a compact single-phase structure of iron boride (Fe 2 B) or a two-phase structure (FeB+Fe 2 B). The thickness of this zone is not more than 0.2 mm. Next, there is an extensive zone (0.5-1.5 mm) with a heterogeneous structure (a-solid solution with alloy borides). This structure ensures a smooth distribution of hardness from the surface to the core of the part. The resulting boronized layers provide higher wear resistance. The choice of a particular layer structure depends on the operating conditions. Under the conditions of the experiment performed, the layer with the combination of borides on the surface and the pseudoeutectic structure in the sublayer became the best. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aSteel, Structural. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 3 Special Issue on Advances in Boronizing and Related Technologies.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190091.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190086 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190086$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190086$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS320 =082 04$a672.3$223 =100 1\$aJurci, Peter,$eauthor. =245 10$aCharacterization of Microstructure and Fracture Performance of Boronized H11 Grade Hot-Work Tool Steel /$cPeter Jurci, M-ria Hud-kov-. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aH11 grade hot-work tool steel was subjected to powder boronizing at 1,030Degree C for different processing times. Subsequently, the steel was austenitized, quenched, and tempered to a bulk hardness of 47-48 HRC. The microstructure, phase constitution, and hardness of boronized layers were examined using scanning electron microscopy and microanalysis, glow discharge optical emission spectroscopy, X-ray diffraction, and microhardness measurements. The effect of the boronized region on the material fracture performance was examined using the Charpy impact test, according to the corresponding standard NADCA 202-97, Recommended Procedures for H13 Tool Steel . It was determined that the growth of the boronized layer begins with a boron enriched a-phase. Then, the (Fe,Cr) 2 B boride was developed, and in the case of longer processing time, the (Fe,Cr)B boride was grown. During boronizing, carbon atoms were transported from the surface toward the bulk, forming extra carbides beneath the compound regions. Their amount increased with increasing boronizing duration, which was reflected in the enhanced hardness of the intermediate region beneath the compound boronized layer. The microhardness of (Fe,Cr) 2 B boride layers was around 1,600 HV 0.1, and the microhardness values of (Fe,Cr)B considerably exceeded 2,000 HV 0.1. However, boronizing led to a substantial reduction of the Charpy impact toughness of the material, and this reduction was more pronounced when a thicker compound layer was formed on the steel surface. The reduction in toughness was clearly reflected on the fractured surfaces as they manifested clear cleavage fracture propagation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aSteel$xHot working. =700 1\$aHud-kov-, M-ria,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 3 Special Issue on Advances in Boronizing and Related Technologies.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190086.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190101 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190101$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190101$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS360 =082 04$a671.30287$223 =100 1\$aCampos-Silva, I.,$eauthor. =245 10$aWear and Scratch Resistance of Cobalt Boride Layer Exposed to a Diffusion Annealing Process /$cI. Campos-Silva, A. D. Contla-Pacheco, V. H. Castrej-n-S-nchez, A. M. Delgado-Brito, A. Gardu-o-Alva, D. L-pez-Suero, J. Mart-nez-Trinidad. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis study evaluated the wear (under dry conditions) and scratch resistance of a cobalt boride layer exposed to a diffusion annealing process (DAP). Firstly, the powder-pack boriding process (PPBP) was conducted at 1,223 K with 4 h of exposure to develop a CoB-Co 2 B layer on the surface of the ASTM F1537 alloy, followed by a DAP at 1,273 K with 2 h of exposure in an argon atmosphere. Before the wear and scratch tests, the resulting cobalt boride layers, obtained by the PPBP and PPBP+DAP, were characterized by X-ray diffraction, scanning electron microscopy, energy dispersive spectroscopy, and depth-sensing Vickers microindentation techniques. The wear sliding tests, on the PPBP and PPBP+DAP, were performed using a ball-on-flat configuration comprising an alumina ball as a counterpart using a constant normal force and different relative wear distances (50, 100, and 150 m). In addition, the scratch tests were carried out over the surface of the PPBP and PPBP+DAP using a Rockwell-C diamond indenter with a continuously increasing normal force from 5 to 150 N. Finally, and according to the entire set of experimental conditions, the results showed that the presence of the CoB-Co 2 B layer obtained by the PPBP on the surface of the ASTM F1537 alloy increased the wear resistance compared with the values estimated on the PPBP+DAP. In contrast, the effect of the DAP on the cobalt boride layer enhanced the practical adhesion resistance of the layer-substrate system based on the critical loads obtained during the scratch tests. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aAnnealing of metals$xTesting. =700 1\$aCastrej-n-S-nchez, V. H.,$eauthor. =700 1\$aContla-Pacheco, A. D.,$eauthor. =700 1\$aDelgado-Brito, A. M.,$eauthor. =700 1\$aGardu-o-Alva, A.,$eauthor. =700 1\$aL-pez-Suero, D.,$eauthor. =700 1\$aMart-nez-Trinidad, J.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 3 Special Issue on Advances in Boronizing and Related Technologies.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190101.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190094 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190094$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190094$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.6 =082 04$a620.11228$223 =100 1\$aPolyansky, I.,$eauthor. =245 10$aImpact Study of Electron-Beam Heating on the Structure and Properties of Boroaluminized Layers Aimed at Producing New Composite Coatings with Special Properties /$cI. Polyansky, I. Sizov, O. Lazareva, A. Volkov, B. Maksimov. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aElectron-beam processing is a promising method of surface processing. Electron-beam processing can involve surface melting accompanied by adding alloying elements into the melt (electron-beam alloying), or it can be applied to preliminary obtained diffusion layers on a material-s surface (electron-beam chemical thermal processing). Electron-beam heating both increases the temperature and initiates diffusion processes in the metal. By regulating parameters of electron-beam processing, different types of layers-diffusion, diffusion-crystalized, or liquid phase-are formed. The paper presents the study of the impact of electron-beam heating on the structure and properties of boroaluminized layers in carbon steel 60 (0.6 % carbon), obtained by thermochemical processing (solid-phase boroaluminizing in powder mixture 98 % (70 % aluminum oxide Al 2 O 3 )+10 % boron oxide (B 2 O 3 )+20 % aluminum (Al)+2 % sodium fluoride (NaF) at T =950Degree C, τ =4 h). The authors studied the influence of electron-heat processing modes on the formation of boroaluminized layers- structure. The parameters of electron-beam heating were beam current Ic =20-60 mA and time of impact τ =15-120 s. The authors conducted metallographic and X-ray microscopic analysis and measured microhardness of boroaluminized layers obtained with a combined method (thermochemical processing and electron-beam heating). It was shown that electron-beam heating of boroaluminized layers leads to changes in the structure and properties as well as in the layer-s morphology. Aluminum is spread evenly in the depth of the layer. The layer-s microhardness changes and the brittleness decreases. The obtained results led to the conclusion that electron-beam heating can be recommended to improve properties of boroaluminized layers and used as a foundation for producing new composite coatings with special properties. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aElectron beams. =700 1\$aLazareva, O.,$eauthor. =700 1\$aMaksimov, B.,$eauthor. =700 1\$aSizov, I.,$eauthor. =700 1\$aVolkov, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 3 Special Issue on Advances in Boronizing and Related Technologies.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190094.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190102 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190102$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190102$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA472 =082 04$a620.17$223 =100 1\$aDaas, Amed,$eauthor. =245 10$aPaste Borided Layers Produced on XC38 Steel Using a New Activator /$cAmed Daas, Laid Abdelkrim Allaoui, Sami Zidelmel, Omar Allaoui. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe objective of this work is to study the possibility of producing boride layers on XC38 steel by the slurry coatings technique in a muffle furnace under an ambient atmosphere. The principle of this technique consists in the application of a slurry of about 1-2 mm thickness containing boron carbide as a boron source and sodium fluoroborate (NaBF 4 ) as a new activator on the surface of the sample to be treated and placed in a muffle furnace at 800Degree C for 4 hours. The obtained results show that it is possible to produce boride layers on XC38 steel by the slurry coatings technique with NaBF 4 as an activator. The characterization of the obtained layers by Optical Microscopy, Scaning Electron Microscope (SEM), X-Ray Diffraction (XRD), and microhardness indicates that depending on the proportion of the boron source and the activator, these layers can be single phase (only di-iron boride [Fe 2 B]) at 10 % of NaBF 4 or two phases iron monoboride (FeB) and Fe 2 B when the proportion of NaBF 4 exceeds 10 %. The total thickness of the obtained boride layers is approximately 60 ?m for all the slurries- composition. But it should be pointed out that for the two-phase borided layers, the proportion of FeB boride increases with the increase of the percentage of NaBF 4 . The microhardness of borided layers is relatively similar for all samples and about 2,100 HV for FeB boride and 1,900 HV for Fe 2 B. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aSteel. =700 1\$aAllaoui, Laid Abdelkrim,$eauthor. =700 1\$aAllaoui, Omar,$eauthor. =700 1\$aZidelmel, Sami,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 3 Special Issue on Advances in Boronizing and Related Technologies.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190102.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190162 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190162$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190162$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN695 =082 04$a671.3705$223 =100 1\$aRamakrishnan, P.,$eauthor. =245 10$aPowder Characterization Techniques /$cP. Ramakrishnan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aKnowledge of the characteristics of powders is of paramount importance for the successful development and application of powder metallurgy and particulate materials. Early characterization techniques were related to press and sinter powder metallurgy, dealing with the relatively coarser powders and with the analysis of individual as well as mass of powders. These analyses include structure, chemistry, morphology, size, shape, their distribution, different densities, flow, porosity, compressibility, friction, shear, residual stress, and so on to obtain a defect-free product. The advent of nanopowders and nanotechnology, metal injection molding, and more recent additive manufacturing has to deal with finer powders and different processing steps, which has resulted in the advancement of traditional powder characterization techniques to the next level, evolving newer and more innovative characterization techniques. Consequently, techniques such as x-ray photoelectron spectroscopy, scanning electron microscopy, laser light diffraction, x-ray computed tomography scan, atomic force microscopy, differential thermal analysis, etc., have been used with emphasis on powder cleanliness and internal particle porosity. The widely used industrial additive manufacturing process uses powder bed fusion that bonds successive layers of powders to facilitate the fabrication of parts with complex geometries. Thus, this article also explores the emerging trends in dynamic powder testing using a powder rheometer to measure dynamic flowability from measurement of axial and rotational forces acting on the rotating blade and the study of spreadability and flowability of powders by rotating drum instruments. A judicious selection of relevant and appropriate powder characterization techniques will ensure predictable powder behavior during the manufacturing process, resulting in consistent and reliable products. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aPowder metallurgy. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190162.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190197 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190197$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190197$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS245 =082 04$a620.5$223 =100 1\$aLefebvre, Louis-Philippe,$eauthor. =245 10$aMeasurement of Water Content in Metal Powders /$cLouis-Philippe Lefebvre, Jiajie Dai, Yannig Thomas, Malgosia Daroszewska, Yadienka Martinez-Rubi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIt is recognized that humidity affects the properties of metallic powders (e.g., flowability, density, composition). Although standards exist to evaluate the water content in various materials, there is presently no standard method validated or specifically adapted for the evaluation of the water content in metallic powders. This article evaluates the water content in titanium powders using different techniques (gravimetry, Karl Fischer titration, quantification of volatiles with a relative humidity sensor). The effect of measurement conditions, particle size, and types of powder were investigated. The results showed that the adsorption of water is a function of the relative humidity in the environment and the characteristics of the powders. The relative humidity in the laboratory has, however, limited effect if the exposure of the powder to the environment is limited prior to the measurements. Water adsorption/desorption is a function of the surface area of the powder. The measured values were underestimated as the methods used (i.e., heating at temperature lower than 275Degree C) did not allow recovering all the water from the powders (i.e., chemisorb water is strongly bonded to the surface and cannot be completely desorbed at temperatures lower than 275Degree C). Although some variability has been observed, the measurement of volatiles with the relative humidity sensor allowed discriminating powders with water contents ranging from 0 to 108 ppm. The amount of water measured using the gravimetric technique was not sensitive enough to precisely monitor the small amount of water adsorb/desorb on the powders investigated in this study. Additional studies are needed to assess the variability and reproducibility of the results and evaluate the techniques on other types of metallic powders. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aMetal powders. =700 1\$aDai, Jiajie,$eauthor. =700 1\$aDaroszewska, Malgosia,$eauthor. =700 1\$aMartinez-Rubi, Yadienka,$eauthor. =700 1\$aThomas, Yannig,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190197.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190220 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190220$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190220$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA492.T8 =082 04$a671.8/3$223 =100 1\$aKey, D.,$eauthor. =245 10$aProcessing of Microscale Aluminum Foamed Particles /$cD. Key, Walid M. Daoush, K. Morsi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMetallic foams have been gaining significant interest because of their unique properties. The present study investigates the processing of microscale particles of aluminum-titanium dihydride foaming precursors, together with their foaming characteristics. The external and internal features and dimensions of these precursor particles were found to be highly dependent on the mechanical milling process and the use of a process control agent (methanol) during milling. The effect of the foaming environment on the foaming characteristics was investigated. Foaming in argon was found to yield better foaming characteristics than that in air. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aAluminum foam. =700 1\$aDaoush, Walid M.,$eauthor. =700 1\$aMorsi, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190220.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190205 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190205$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190205$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN695 =082 04$a671.3705$223 =100 1\$aG-linas, Simon,$eauthor. =245 10$aSolidification Structures in Low-Alloyed Powder Metallurgy Steels Obtained through Permanent Liquid Phase Sintering Using a Master Alloy Containing Boron /$cSimon G-linas, Jean-Nicolas Rousseau, Carl Blais. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPowder metallurgy (PM) steels containing boron form an attractive group of alloys because of the important densification that can be achieved through permanent liquid phase sintering (LPS). However, upon solidification, such liquid phase is known to form borides or borocarbides. Recent works have shown that some alloying elements have significant interactions with the LPS of PM steels containing boron. More specifically, it is suspected that the concentration of prealloyed molybdenum influences the formation of boride/borocarbide upon cooling at the end of the sintering cycle. Therefore, the main objective of this work is to describe the relationship that exists between the concentration of prealloyed molybdenum and the crystal structure of the boride/borocarbide eutectic component that typically forms in PM steels containing boron. A master alloy made of iron-manganese-nickel-boron-carbon was utilized to introduce boron, thus providing enhanced sintering through LPS. Characterization in optical and scanning electron microscopy combined with electron-backscattered diffraction and energy-dispersive X-ray spectrometry (EDS) revealed that increasing the prealloyed molybdenum content not only increased the volume fraction of liquid phase but also modified the morphology and the nature of the boron-rich eutectic. Changing the prealloyed molybdenum content from 0.5 to 0.85 wt.% transformed the discontinuous M 2 B boride to a continuous M 23 (C,B) 6 borocarbide phase, causing a drastic decrease in strength despite the higher densification observed at 0.85 wt.% molybdenum. The effect of molybdenum on the LPS process of boron PM steels is undeniable and was found to occur after the initial formation of the liquid phase. Indeed, differential scanning calorimetry revealed no difference in the endothermic melting peaks temperature for both concentration of molybdenum. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aPowder metallurgy. =700 1\$aBlais, Carl,$eauthor. =700 1\$aRousseau, Jean-Nicolas,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190205.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190193 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190193$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190193$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN695 =082 04$a671.3705$223 =100 1\$aMurphy, Thomas F.,$eauthor. =245 10$aMicrostructural Evolution during Sintering and Fracture Behavior of Iron-Copper-Carbon Compacts Made with Elemental Powders /$cThomas F. Murphy, Bruce A. Lindsley. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIron-copper and iron-copper-carbon have been significant alloy compositions in the ferrous powder metallurgy industry for decades. In most applications in which these alloys are used, the copper is mixed into an iron or low-alloy steel base powder as an elemental particulate additive, with alloying accomplished by diffusion during sintering. In this manuscript, the effect of sintering on the development of the microstructure is investigated, where the copper particles melt and flow into the interconnected pore structure, relocate within the iron-base matrix, and create more interfacial area for diffusion. With this combination of enlarged copper-iron contact area and the presence of the liquid phase, diffusion is improved and enhancements in both physical and mechanical properties are realized. The mechanisms for both alloying and the evolution of the microstructure are described through changes in both compact temperature and the time at sintering temperature. It is demonstrated that alloying strengthens not only the surfaces of the particles, but also many of the most vulnerable sites in the compact, i.e., the locations where neighboring particles are forced into contact during compaction. These sintered particle-to-particle contacts are frequently small in cross-sectional area and often the weakest sites in the final microstructure. Fractography is used to show the change in fracture behavior as copper diffusion is affected by sintering times and temperatures. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aPowder metallurgy. =700 1\$aLindsley, Bruce A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190193.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190073 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190073$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190073$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN695 =082 04$a671.3705$223 =100 1\$aToulba, Eman,$eauthor. =245 10$aMicrostructure and Properties of Nickel/Detonated Nanodiamond Composites Fabricated by Powder Metallurgy /$cEman Toulba, Mahmudun N. Chowdhury, Ahmed I. Ali, Ibrahim S. Qassem, Walid M. Daoush. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aNickel/detonated nanodiamond composites were prepared using the powder metallurgy technique. Detonated nanosized diamond particles were reinforced in the nickel matrix. The investigated powder was used to prepare homogenous diamond/nickel composite mixtures with different detonated nanodiamond content of weight percentage (0.2, 0.4, 0.6, and 0.8 wt.%). The produced mixtures were cold pressed into a cylindrical die shape under compaction pressure of 400 MPa followed by sintering at 1,000Degree C for 120 min under a controlled atmosphere of 1:3 hydrogen/nitrogen gas mixture. Phase identification and microstructure of the produced sintered samples were investigated using X-ray diffraction and scanning electron microscope, respectively. The results of the microstructure show a good distribution of the detonated nanodiamond in the nickel matrix, especially in the 0.8 wt% diamond/nickel sintered sample. The densities of the obtained sintered samples were measured by applying the Archimedes principal. As the detonated nanodiamond content was increased in the nickel matrix, the density of the sintered samples was decreased. The thermal expansion, electrical conductivity, and hardness of the produced diamond/nickel composites were measured. The coefficient of thermal expansion and electrical conductivity were decreased, but the hardness was increased by increasing the detonated nanodiamond weight percentage. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aPowder metallurgy. =700 1\$aAli, Ahmed I.,$eauthor. =700 1\$aChowdhury, Mahmudun N.,$eauthor. =700 1\$aDaoush, Walid M.,$eauthor. =700 1\$aQassem, Ibrahim S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190073.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190161 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190161$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190161$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN695 =082 04$a671.3705$223 =100 1\$aWilson, M. F.,$eauthor. =245 10$aHot Extrusion of a Commercial Aluminum Powder Metallurgy Metal Matrix Composite Material /$cM. F. Wilson, G. A. W. Sweet, M. Y. Amegadzie, B. W. Williams, L.-J. B. Smith, A. Taylor, R. L. Hexemer, I. W. Donaldson, D. P. Bishop. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSintered preforms made of an aluminum powder metallurgy (PM) 2000 series metal matrix composite designed for press-and-sinter applications were forward extruded at 450Degree C under displacement rates of 254 mm/min and 2,032 mm/min. The material was highly responsive to extrusion under these conditions and was readily formed into products that included 10-mm and 15-mm solid round bars as well as C-channel and round tubing profiles, wherein extrusion ratios ranged from 11:1 to 76:1. Significant metallurgical improvements were also observed in the seemingly defect-free products. These included gains in tensile yield strength (10 %), ultimate tensile strength (20 %), and tensile ductility (400 %) when compared to the nonextruded T6 counterpart. Such enhancements were attributed to the attenuation of full theoretical density, disruption of the residual oxide network, and the development of a partial duplex fiber texture with strong <111> and moderate <100> fiber components within the extruded PM products. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aPowder metallurgy. =700 1\$aAmegadzie, M. Y.,$eauthor. =700 1\$aBishop, D. P.,$eauthor. =700 1\$aDonaldson, I. W.,$eauthor. =700 1\$aHexemer, R. L.,$eauthor. =700 1\$aSmith, L.-J. B.,$eauthor. =700 1\$aSweet, G. A. W.,$eauthor. =700 1\$aTaylor, A.,$eauthor. =700 1\$aWilliams, B. W.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190161.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190149 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190149$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190149$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS255 =082 04$a668.412$223 =100 1\$aAli, Ghalya,$eauthor. =245 10$aThreshold Concentration of Surfactant Agent in Feedstocks Used for Low-Pressure Powder Injection Molding /$cGhalya Ali, Vincent Demers, Rapha-l C-t-, Nicole R. Demarquette. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this work, 32 different feedstocks formulated from four different stainless steel powders and two wax-based binder systems (paraffin wax and beeswax), for which the proportion of two different surfactant agents was varied from 0 to 5 vol.% (stearic acid and oleic acid), were obtained. The viscosity of the feedstocks according to the shear rate was measured using a rotational rheometer. The moldability of the mixtures was assessed using the injected length following real-scale injections. The results show that the influence of surfactant agents on viscosity depends on the main binder constituent used in the feedstock formulation. The moldability of paraffin wax-based feedstocks was significantly affected by the proportion of the surfactant agents, whereas that of beeswax-based feedstocks was not affected by the presence of stearic acid or oleic acid. It was confirmed that as little as 0.20 vol.% of stearic acid or oleic acid in paraffin wax-based feedstock is enough to produce the surfactant effect, leading to a significant increase in the moldability of feedstocks (e.g., fourfold longer injected length). This threshold concentration of surfactant agent in paraffin wax-based feedstocks was also established with different powder grades, shapes, and sizes. For feedstocks containing paraffin wax and surfactant agents, the presence of a discontinuity in the viscosity profiles was confirmed not to be an experimental artifact because the phenomenon was reproduced using three different measurement approaches. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aPowder injection molding. =700 1\$aC-t-, Rapha-l,$eauthor. =700 1\$aDemarquette, Nicole R.,$eauthor. =700 1\$aDemers, Vincent,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190149.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190160 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190160$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190160$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN695 =082 04$a671.3705$223 =100 1\$aMwema, F. M.,$eauthor. =245 10$aAdvances in Powder-based Technologies for Production of High-Performance Sputtering Targets /$cF. M. Mwema, E. T. Akinlabi, O. P. Oladijo, A. D. Baruwa. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe sputtering method has been extensively adopted for the production of high-performance thin films and coatings. This can be attributed to its versatility and flexibility, which allows easier tailoring of the properties and characteristics of the sputtered films and coatings for the desired application and performance. Contrary to thermal spray and chemical techniques, sputtering can be performed at room temperature for a wide range of targets, thus overcoming the challenges, such as residual stresses and degradation of the substrates, associated with high-temperature processes. The most important aspect of the sputtering is the target from which the thin film material is derived. The quality of the target determines the properties and performance of the resulting film and coating. Published data reveal that the quality of the targets depends mainly on the method of production. Although different manufacturing techniques have been used to produce these targets, consolidation of powders has been shown to provide outstanding results. The production of these targets through powder metallurgy depends on the compaction or sintering methods and associated processing parameters. With the increasing demand for high-performance thin films and coatings, such as high-entropy alloy films, the quality of the targets used for sputtering is crucial for application in various fields that include medical, electronics, and energy. In this article, progress on the powder metallurgy on the manufacturing of sputtering targets is detailed. Advances in various powder technologies, process parameters, and conditions, and their interrelationships with properties and performance of targets and sputtered thin films will be discussed, synthesized, and general/specific trends will be derived. This article will serve as a resource for metallurgists in the optimization and development of advanced targets for industry 4.0. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aPowder metallurgy. =700 1\$aAkinlabi, E. T.,$eauthor. =700 1\$aBaruwa, A. D.,$eauthor. =700 1\$aOladijo, O. P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190160.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190128 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190128$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190128$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN695 =082 04$a671.3705$223 =100 1\$aYehia, Hossam M.,$eauthor. =245 10$aMicrostructure, Hardness, Wear, and Magnetic Properties of (Tantalum, Niobium) Carbide-Nickel-Sintered Composites Fabricated from Blended and Coated Particles /$cHossam M. Yehia, Walid M. Daoush, F. Abdel Mouez, Mohamed H. El-Sayed, Ahmed E. El-Nikhaily. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$a(Tantalum, niobium) carbide-nickel composites were prepared by the powder metallurgy technique. Microsize (tantalum, niobium) carbide particles were reinforced in the nickel matrix. Different nickel contents were added to (tantalum, niobium) carbide powders by two different methods, namely, blending and electroless coating. The results of the microstructure show a good distribution of the (tantalum, niobium) carbide particles in the nickel matrix. The produced (tantalum, niobium) carbide-nickel composite powders were cold compacted at 400 MPa and sintered under vacuum at 1,450Degree C for 90 min. The density of the (tantalum, niobium) carbide-nickel-sintered materials was measured by the Archimedes method. The mechanical properties of the obtained sintered materials were evaluated by measuring the Vickers hardness and the wear rate using a pin-on-ring wear test machine. The microstructure of the sintered (tantalum, niobium) carbide-nickel as well as the microstructure of worn samples were investigated by a scanning electron microscope. The results revealed that the (tantalum, niobium) carbide-nickel-sintered materials, which were prepared by the electroless nickel coating of (tantalum, niobium) carbide particles, have a homogeneous microstructure and exhibit higher relative density, hardness, and low specific wear rate than the samples of the (tantalum, niobium) carbide/nickel-sintered materials prepared by blending of nickel with the (tantalum, niobium) carbide powders. The magnetic properties of the obtained blended and coated (tantalum, niobium) carbide particles as well as the sintered one have been studied. It was observed that the saturation magnetization is increased by increasing the nickel content. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aPowder metallurgy. =700 1\$aAbdel Mouez, F.,$eauthor. =700 1\$aDaoush, Walid M.,$eauthor. =700 1\$aEl-Nikhaily, Ahmed E.,$eauthor. =700 1\$aEl-Sayed, Mohamed H.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190128.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200023 =003 IN-ChSCO =005 20201014061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 201014s2020\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200023$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200023$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS183 =082 04$a670$223 =100 1\$aDobrzanski, Lech B.,$eauthor. =245 10$aComparison of the Structure and Properties of the Solid Co-Cr-W-Mo-Si Alloys Used for Dental Restorations CNC Machined or Selective Laser-Sintered /$cLech B. Dobrzanski, Anna Achtelik-Franczak, Joanna Dobrzanska, Leszek A. Dobrzanski. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2020. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe purpose of this paper is to compare the impact of selective laser-sintering (SLS) technology and computer numerical control (CNC) machining methods on the structure and properties of solid Co-Cr-W-Mo-Si alloys. Structural tests were carried out using x-ray structural analysis; energy-dispersive x-ray spectroscopy chemical composition analysis; metallographic investigations using stereoscopic, light, and scanning electron microscopes using computerized methods of quantitative metallography; and tests of tensile, bending, and compression strength. Individually designed microsamples were used, and the results were statistically processed. It was shown that if optimal conditions of SLS technology are used, it is possible to obtain a structure with a pore content of 0.1 % smaller than in the case of solid cast materials. This ensures better mechanical properties than cast materials. At the same time, it was pointed out that even minor technological errors associated with SLS technology caused a lowering of all strength properties associated with a significant increase in porosity by up to 10 %. Allowing small changes in technological conditions, including the width of the laser spot, the width of the laser beam, the allowance associated with the overlap of the laser beam, disturbances in the flow of inert gas, and uncontrolled changes in the laser power, can cause a significant reduction in strength. A plug and play approach is unacceptable. If even one layer with a thickness of 25 ?m is produced in suboptimal conditions, the manufactured element cannot meet the assumed requirements. The use of SLS additive technology for the production of prosthetic components made of Co-Cr alloys is the best choice among the methods currently used in dentistry. The use of SLS technology together with the digitization of design and manufacturing processes is an important element in implementing the Dentistry 4.0 approach as part of the Industry 4.0 stage of the industrial revolution. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed October 14, 2020. =650 \0$aManufacturing processes. =700 1\$aAchtelik-Franczak, Anna,$eauthor. =700 1\$aDobrzanska, Joanna,$eauthor. =700 1\$aDobrzanski, Leszek A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 4 Special Issue on Advances in Powder Engineering.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200023.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190038 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190038$2doi =037 \\$aMPC20190038$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA481 =082 04$a620.16$223 =100 1\$aGupta, Ashish Kumar,$eauthor. =245 10$aStructure Property Correlation of In Situ Reinforced Al–based Metal Matrix Composite via Stir Casting /$cAshish Kumar Gupta, Banshidhar Mallik, Debdas Roy. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAluminum-based in situ nanocomposites are synthesized by stir casting route. The powder materials used to develop the in situ reinforcement were mechanically milled so as to reduce the powder size in the nanoregime. The as-fabricated nanocomposite aluminum base 20 vol% (Al203 +Fe-aluminide) in situ reinforcement is characterized through X-ray diffraction, field emission scanning electron microscopy (FE-SEM), and energy dispersive spectroscopy analysis, yet its mechanical properties were characterized through microhardness, dry sliding wear, and shear punch test. The tormented surface of the wear out and sheared specimen, investigated through FE-SEM of the as-processed composite, elicits improved tribological and shear properties as compared with pure aluminum. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aMetallic composites. =700 1\$aMallik, Banshidhar,$eauthor. =700 1\$aRoy, Debdas,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190038.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190066 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190066$2doi =037 \\$aMPC20190066$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1177.5.G5 =082 04$a668.4$223 =100 1\$aRajendran, Sundarakannan,$eauthor. =245 10$aMechanical Performance Studies on Composites Using Polyethylene Terephthalate Char Derived from Polyethylene Terephthalate Waste Bottle–Reinforced Polyester Composites /$cSundarakannan Rajendran, Arumugaprabu Veerasimman, Manikandan Vairavan, Vigneshwaran Shanmugam, Deepak Joel Johnson Rajendran. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the modern world, the disposal of wastes and its reusage is always a challenging task. Many researchers have been working toward the reusage of wastes. This research article reports on one such method to reuse the pet bottles that are used worldwide. The pet bottles were crushed, then they underwent a pyrolysis process, and the polyethylene terephthalate (PET) char extracted from it was used as reinforcement for composite production. Waste bottles are collected and chopped into small pieces and packed in a closed container. This container is kept in the furnace and maintained at a temperature of 300°C. After 3 h, the plastic char is taken from the container and ball milled for about 5 h in order to obtain the PET char in fine powder form. The extraction of PET char followed by the mechanical property studies on PET char derived from waste PET bottles has been carried out to know its effectiveness as a primary reinforcement in the polyester matrix and will be discussed in detail. The PET char is reinforced with polyester composites with varying weight percentages of 5, 10, and 15 %. The addition of PET char in the polyester matrix drastically increases the tensile strength and flexural strength by 24 and 20 % compared with pure polyester matrix. From the results, it was noted that 10 % wt. PET char-reinforced composites revealed better mechanical properties, which indicates its potentiality to be used for composite manufacturing. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aComposite materials. =650 \0$aPlastics. =650 \0$aGlass-reinforced plastics. =700 1\$aVeerasimman, Arumugaprabu,$eauthor. =700 1\$aVairavan, Manikandan,$eauthor. =700 1\$aShanmugam, Vigneshwaran,$eauthor. =700 1\$aRajendran, Deepak Joel Johnson,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190066.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190080 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190080$2doi =037 \\$aMPC20190080$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRC78.7.D53 =082 04$a616$223 =100 1\$aLaquai, René,$eauthor. =245 10$aClassification of Defect Types in SLM Ti-6Al-V4 by X-ray Refraction Topography /$cRené Laquai, Bernd Randolf Müller, Galina Kasperovich, Guillermo Requena, Jan Haubrich, Giovanni Bruno. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPorosity in additively manufactured materials, such as laser powder bed fusion Ti-Al6-V4, can play an important role in their mechanical performance. Not only the total porosity but also the shape/morphology of the individual pores need to be considered. Therefore, it is necessary to determine the distributions of different defect types (especially fusing defects and keyhole pores) and their dependence on process parameters. We show that synchrotron X-ray refraction radiography allows analysis of large samples (up to several millimeters) without compromising the detectability of submicrometer defects. Correspondingly, a classification tool is introduced that is able to quantitatively distinguish defects such as keyhole pores and binding defects with a confidence level of 94 %, even when the shape cannot be discerned because of limited spatial resolution. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aRadiotherapy. =700 1\$aMüller, Bernd Randolf,$eauthor. =700 1\$aKasperovich, Galina,$eauthor. =700 1\$aRequena, Guillermo,$eauthor. =700 1\$aHaubrich, Jan,$eauthor. =700 1\$aBruno, Giovanni,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190080.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190111 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190111$2doi =037 \\$aMPC20190111$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS280 =082 04$a621.8672$223 =100 1\$aAzraai, S. N. A.,$eauthor. =245 10$aEffect of Silica Sand Filler on Mechanical Properties of Epoxy Grout for Composite Repair of Steel Pipelines /$cS. N. A. Azraai, K. S. Lim, N. Yahaya, L. Zardasti, M. K. Abu Husain, N. Md. Noor. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aOil and gas pipes are vulnerable to failure initiated by corrosion because of their operating pressure under adverse conditions. A composite repair assembled around the pipe with a small gap that is then infilled with epoxy grout is considered a suitable option for repairing corroded pipelines. This article presents an investigation into the mechanical properties (compressive, tensile, and flexural) of epoxy grout, with and without inclusion of silica sand as a filler. The mechanical tests were carried out in accordance with American Society for Testing and Materials standards. Experimental results on mechanical properties indicate that the strength in tensile and flexural mode for the grout decreases with the inclusion of filler because of a weak interface between the matrix and filler. However, the addition of filler in grout showed an increase in compressive, tensile, and flexural modulus. Based on suggested properties in a previous study, both grouts have the potential to be used on structural rehabilitation, especially for repairing damaged pipeline. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aPipe, Steel$xStandards. =700 1\$aLim, K. S.,$eauthor. =700 1\$aYahaya, N.,$eauthor. =700 1\$aZardasti, L.,$eauthor. =700 1\$aHusain, M. K. Abu,$eauthor. =700 1\$aNoor, N. Md.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190111.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190123 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190123$2doi =037 \\$aMPC20190123$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA690 =082 04$a624.1826$223 =100 1\$aRamaswamy, Addanki,$eauthor. =245 10$aInfluence of Metal Transfer Modes and Postweld Heat Treatment on Tensile Properties of Gas Metal Arc–Welded AA6061-T6 Aluminum Alloy Joints /$cAddanki Ramaswamy, S. Malarvizhi, V. Balasubramanian. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe issues of dissolution or overaging of precipitates in the weld metal or heat-affected zone of aluminum alloy joints welded by conventional or constant-current gas metal arc welding (CC-GMAW) process are the key factors responsible for the formation of softening region, which leads to the degradation of the mechanical properties of the joint. In order to prevent the precipitate dissolution, a low heat input welding process is required. Further, to improve the mechanical properties of the welded joints, reprecipitation is necessary, and this can be achieved by postweld heat treatment (PWHT) The main aim of this investigation is to study the combined effect of metal transfer modes (i.e., CC-GMAW, pulsed-current gas metal arc welding [PC-GMAW], and cold metal transfer gas metal arc welding [CMT-GMAW]) and heat treatment on the tensile properties of gas metal arc–welded AA6061 aluminum alloy joints. This investigation effectively implements the low heat input GMAW variants like PC-GMAW and CMT-GMAW to control the dissolution of precipitates. Moreover, PWHT procedure (solutionizing at 530°C for 1 h, followed by quenching in water and then artificial aging at 170°C for 19 h, and finally cooling in air at an ambient temperature) was imposed on the specimens in order to recover the mechanical properties of the welded joints. It is observed from the tensile properties that PWHT joints exhibited improved mechanical properties compared with the as-welded joints. But the joint welded by CC-GMAW process has shown no improvement in the tensile properties because of the segregation of alloying elements that are observed along the grain boundary. The PWHT CMT-GMAW joint showed huge improvement in tensile properties (i.e., 13 % higher than the CC-GMAW joint and 9 % higher than the PC-GMAW joint) because of the controlled segregation of alloying elements with nucleation of β′ precipitates. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aAluminum alloys. =700 1\$aMalarvizhi, S.,$eauthor. =700 1\$aBalasubramanian, V.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190123.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190130 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190130$2doi =037 \\$aMPC20190130$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.18623$223 =100 1\$aSantra, Sumita,$eauthor. =245 10$aCarbide Faceting in Alloy 690: HRTEM Study /$cSumita Santra, S. V. Ramana Rao, K. Kapoor, D. Srivastava. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (19 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAlloy 690 (Unified Numbering System [UNS] No. 6690) in thermally treated (TT) condition is an advanced steam generator tubing material that offers high corrosion resistance with tailored carbide morphology and chromium concentration adjacent to the grain boundary. The morphology of the intergranular carbides was found to have strong dependence on the grain boundary character distribution (GBCD) from an electron backscattered diffraction (EBSD) study. The effect of thermal aging on crystallography and faceting of carbides was studied with the aid of high-resolution transmission electron microscopy (HRTEM) Carbides formed at 600°C, 700°C, and 800°C were structurally consistent with face centered cubic (fcc) M 23 C 6 . The orientation relationship of the carbides with grain allowing maximum atomic correspondence was found to be (111) C ‖ (111) M and <110> C ‖ <110> M . HRTEM analysis revealed that the carbides were partially faceted with multiple facet initiation at lower temperature and become fully faceted with fewer stable facets at 800°C. The non-faceted parts of carbides had lattice structure discontinuity from the faceted portion creating new energy interface within the carbides. It is suspected that the growth of carbides, formation of facets, and facet transformation takes place via ledge growth and coalescence. Stable, low-energy faceted interfaces of 800°C remain inactive and hold the carbides firmly, preventing dissolution or dislodging in corrosive environments and thus providing superior corrosion resistance. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aCorrosion and anti-corrosives. =700 1\$aRamana Rao, S. V.,$eauthor. =700 1\$aKapoor, K.,$eauthor. =700 1\$aSrivastava, D.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190130.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190139 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190139$2doi =037 \\$aMPC20190139$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a624.1/8$223 =100 1\$aSooraj, V. S.,$eauthor. =245 10$aInvestigations on the Machining Characteristics of Silica-Phenolic Ablative Tiles Bonded to a Metal Substrate /$cV. S. Sooraj, P. Chakravarthy, H. Danish, L. Mohan Kumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThermal protection systems are of great importance to the aerospace industry as they prevent the structural member from being heated up to a great degree, which otherwise may lead to undesired failures. “Silica phenolics” is one such ablative composite that is widely used for rocket nozzle and re-entry applications. Though the composite is fabricated to a near net shape, secondary processing, such as machining, becomes inevitable for maintaining dimensional tolerances. Usually, these composites are bonded to a structural member that needs protection from high temperatures. Subsequently, these composites, after bonding to the substrate, are machined to the required geometries using single-point cutting tools to suit the functional requirements. The present work addresses the single-point machining of ablative tiles bonded to a metallic mandrel to simulate the real-time conditions of machining ablative composites bonded to a rocket nozzle. The present work also adopts a special cutting strategy that varies the uncut thickness on different segments of a circular workpiece during its rotation, which simulates reality. Variation of cutting forces was captured at each of these ablative composite segments for different cutting speeds and depth of cut to understand the influence of uncut thickness and width of cut. Possible hypotheses on the mechanism of material removal were analyzed to understand the defects that would arise out of cutting edge interaction with the ablatives. The study revealed that the cutting forces during machining were much lower, and the debonding of the ablatives from the substrate was not observed. The results of the shear lap test also indicated that the debonding force was comparably higher than the observed cutting forces. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aAblative materials. =700 1\$aChakravarthy, P.,$eauthor. =700 1\$aDanish, H.,$eauthor. =700 1\$aMohan Kumar, L.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190139.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190141 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190141$2doi =037 \\$aMPC20190141$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTE278 =082 04$a625.8/4$223 =100 1\$aNaqvi, Ali Zia,$eauthor. =245 10$aEvaluation of Heat Treatment Effect on Impact Strength of Glass Fiber–Reinforced Composite Material Using NDT Technique /$cAli Zia Naqvi, Tariq Mairaj Rasool Khan, M. Ghazanfar Ali, Muhammad Imran, Aqueel Shah. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aOf late, the frequent use of composite materials merits effective inspection techniques to ensure structural integrity after manufacturing as well as during service. The inspection of composite materials is undertaken using various nondestructive testing (NDT) techniques. Ultrasonic testing (UT) is one of the popular NDT techniques used for testing of composites. The aim of the research is to establish a quantitative relationship between UT signal‘s features and the mechanical property, i.e., impact toughness of the composite material heat treated at different temperatures. Polyester glass fiber–reinforced composite undergone post-cure heat treatment is the composite used in the research work. The glass fiber–reinforced plastic (GFRP) specimens have been heat treated at different temperatures to mimic different levels of thermal aging. The impact toughness of the composite material is determined using the Charpy impact test. Then, variation in attenuation of UT signals is related to the change in impact toughness of GFRP composite material heat treated at different temperatures. A possible classification of UT signals acquired from GFRP specimens in terms of different level of thermal aging has also been investigated through application of Hilbert–Huang transform (HHT) on the acquired UT signals. Hilbert energy frequency distribution-based feature extraction has been successfully used to analyze the effect of post-cure heat treatment on GFRP composite. An empirical relationship is finally obtained between Charpy impact energy and HHT energy. The proposed technique will be useful in prediction of strength and remaining useful life of GFRP composites through analyses of acquired UT-based NDT signals. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aGlass fibers. =650 \0$aPavements, Reinforced concrete$xDesign and construction. =700 1\$aKhan, Tariq Mairaj Rasool,$eauthor. =700 1\$aAli, M. Ghazanfar,$eauthor. =700 1\$aImran, Muhammad,$eauthor. =700 1\$aShah, Aqueel,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190141.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190144 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190144$2doi =037 \\$aMPC20190144$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA690 =082 04$a624.1826$223 =100 1\$aMarigoudar, Rajaneesh N.,$eauthor. =245 10$aComparative Surface Morphology of Machined Hybrid and Unhybrid Zinc-Aluminum Alloy-Based Metal Matrix Composites /$cRajaneesh N. Marigoudar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe present article reveals the surface characteristics of zinc-aluminum alloy (ZA43) reinforced with silicon carbide (SiC) particulate conventional composite and SiC+Graphite dual reinforced hybrid metal matrix composites. Both the composites were prepared using a liquid metallurgy technique. A base alloy of metal matrix composites (MMC) containing zinc—57 %, aluminum—43 % was reinforced with SiC (5 %) with an average particle size of 60 Μm and hybrid composite with 5 % SiC and 5 % graphite. The coated carbide tool SNMG was used to machine the two varieties of composites under dry condition. Machining parameters were considered at three different levels, keeping a constant depth of cut. It was observed from the results that the surface finish was greatly influenced by cutting speed and feed. Unhybridized composites exhibit (without graphite) higher roughness values than composites with graphite during the machining trials. The reasons for higher roughness values include particle pullout, particle fracture, and built-up edge formation on the cutting tool during the machining process. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aAluminum alloys. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190144.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190173 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190173$2doi =037 \\$aMPC20190173$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA481 =082 04$a620.16$223 =100 1\$aVeeresh Kumar, G. B.,$eauthor. =245 10$aInvestigation of Mechanical and Tribological Properties of Al6061–TiB2 Metal Matrix Composites /$cG. B. Veeresh Kumar, D. Gopinath Reddy, C. Vineeth Reddy, Ch Sriteja, R. Pramod. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAluminum alloys are commonly used in transportation, manufacturing, and related production fields for commercial applications because they possess high stiffness, strength-to-weight ratio, design flexibility, corrosion, and crack resistance. For this study, an attempt has been made to fabricate and improve the mechanical and sliding wear behavior of in situ–produced aluminum metal matrix composites (MMCs) with the titanium diboride (TiB 2 ) particulate reinforcements by varying weight percentage from zero to six. The addition of TiB 2 ceramic particle reinforcements to Al6061 matrix leads to an increase in material density and also results in a significant increase in modulus of the composite and specific strength as they have hardness of 86 HRA and high elastic modulus of 560 GPa. The Brinell hardness values of the composites along with the ultimate tensile strength (UTS) values were witnessed to increase with higher content of ceramic TiB 2 because of uniform particle distribution and smaller size of filler at the lower elongation percentage. The microscopic investigations indicated that the change in hardness and UTS with increase in grain boundaries was due to fine interfacial bonding and coarse grain structure. Superior performance in properties was found at 6 wt. % of TiB 2 . The sliding wear tests were carried out at fixed velocity and at different loads. The wear test results of composites with TiB 2 filler showed higher wear resistance because of effective load transfers at matrix ceramic particle interface. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aMetallic composites. =700 1\$aGopinath Reddy, D.,$eauthor. =700 1\$aVineeth Reddy, C.,$eauthor. =700 1\$aSriteja, Ch,$eauthor. =700 1\$aPramod, R.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190173.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190177 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190177$2doi =037 \\$aMPC20190177$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.G65 =082 04$a662.92$223 =100 1\$aKrishnia, Lucky,$eauthor. =245 10$aOptimization of Reducing Agents for Selective Bandgap Manipulation in Visible Region of Graphene Oxide and Its Work Function Estimation /$cLucky Krishnia, Pawan K. Tyagi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (25 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present study, we report an effective way for reduction of graphene oxide (GO) as well as tuning of bandgap using various reducing agents. It is found that sodium borohydride (NaBH 4 ) can be a promising reducing agent, as it can reduce the bandgap to 2.30 eV and has a higher capacity to restore the carbon–carbon bonds compared with other reducing agents. Further bandgap tuning has been obtained by hydrogenation of GO as well as NaBH 4 -reduced GO (NGO) It was observed that after hydrogenation, the bandgap of GO was reduced from 2.48 to 1.95 eV, whereas it reduced from 2.45 to 1.87 eV in NGO. Hydrogenation of GO results in rearranging of C=O functionalities and removal of oxygen-containing groups. Furthermore, transmission electron microscopy observations corroborate the observation that after reduction with NaBH 4 , GO shows a more uniform nature than GO. The intensity ratio (I {1,100} /I {1,200} ) of the {1,200} and {1,100} planes is found to be 1. After reduction with NaBH 4, the ID / IG ratio decreased from 1.05 to 0.92, suggesting a decrease in defect density and better reduction. The intrinsic work function of GO and hydrogenated NGO is determined using electrostatic force microscopy and found to be 5.19±0.1 eV and 4.39±0.1 eV, respectively. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aGraphene. =700 1\$aTyagi, Pawan K.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190177.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190212 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190212$2doi =037 \\$aMPC20190212$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP684.P3 =082 04$a664/.36$223 =100 1\$aDaud, Flora Anak Albert,$eauthor. =245 10$aCharacterization of Alkali-Activated Palm Oil Fuel Ash Pastes as a Function of Calcination Temperatures of Raw Precursor /$cFlora Anak Albert Daud, Idawati Ismail, Raudhah Ahmadi, Nur Amalina Shairah Binti Abdul Samat. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis research investigates the influence of calcination temperatures of palm oil fuel ash (POFA) on the properties of the raw precursor and its hardened binder after alkali activation. The raw POFA obtained from palm oil mill is treated at 500°C, 600°C, and 700°C for approximately 6 h. The treated POFA (TPOFA) is characterized for particle size distributions and chemical compositions by X-ray fluorescence (XRF); microstructural properties by observing through scanning electron microscopy (SEM); and Fourier-transform infrared spectroscopy (FTIR) for molecular functional groups. Pastes of alkali-activated POFA (AAPOFA) are synthesized with 12 M sodium hydroxide (NaOH) as alkali activator where the liquid to binder ratio is 0.4. Calcination temperatures are observed to have some influences on the physical properties (such as color, texture, particle size and fineness) and chemical properties (such as composition and reactivity) of the raw precursor. These properties control microstructural evolution of hardened pastes, compressive strength and capillary sorptivity properties of the hardened pastes. Overall results show 500°C is the optimum calcination temperature for POFA that contributes to comparable strength and lowest permeability of AAPOFA binders. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aPalm oil. =700 1\$aIsmail, Idawati,$eauthor. =700 1\$aAhmadi, Raudhah,$eauthor. =700 1\$aAbdul Samat, Nur Amalina Shairah Binti,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190212.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190219 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190219$2doi =037 \\$aMPC20190219$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA472 =082 04$a629.232$223 =100 1\$aSaliby, F.,$eauthor. =245 10$aEffect of Rolling after Heat Treatment on Hydrogen Embrittlement Susceptibility for High Strength Steel Fasteners /$cF. Saliby, S. Brahimi, S. Rajagopalan, S. Yue. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSteel fasteners comprising two different metallurgical structures were investigated for hydrogen embrittlement (HE) susceptibility by incremental step load testing. The metallurgical structures examined consisted of tempered martensite obtained by quenching and tempering and lower bainite obtained by austempering. It has been shown that lower bainite exhibits marginally lower HE susceptibility when tested under moderate hydrogen charging conditions (e.g., -1.0 V) At the most severe hydrogen charging potential of -1.2 V, both microstructures are equally embrittled. The current paper examines the effect of the sequence of the fabrication process, specifically the effect of rolling the threads before and after heat treatment (i.e., quenching and tempering or austempering) The results show irrespective of the metallurgical structure, rolling the threads after heat treatment causes a significant decrease in HE susceptibility. These findings are attributed to the presence of high dislocation density when thread rolling is performed on hardened parts as a final manufacturing step. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aSteel, High strength. =700 1\$aBrahimi, S.,$eauthor. =700 1\$aRajagopalan, S.,$eauthor. =700 1\$aYue, S.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190219.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190228 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190228$2doi =037 \\$aMPC20190228$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.A88 =082 04$a620.172$223 =100 1\$aKumar, Viranshu,$eauthor. =245 10$aEffect of Warm Forging on the Microstructure and Corrosion Behavior of Austenitic Stainless Steel 316LN /$cViranshu Kumar, Ratnesh Kumar Gupta, Ghanshyam Das. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe as-received as well as deformed microstructure and electrochemical corrosion behavior of warm-forged and annealed 316LN austenitic stainless steel have been investigated by using electron backscatter diffraction (EBSD) and electrochemical corrosion test methods. An attempt has been made to understand the effect of warm forging and annealing on the microstructure and electrochemical corrosion behavior of 316LN stainless steel. As-received and deformed microstructures of a sample were observed by EBSD, and from micrographs, it was observed that the refinement of grain occurs after deformation. Microstructural refinement occurs after appropriate annealing of the forged sample because of the revision of alpha ferrite and strain-induced martensite into austenite, which is formed after forging. Annealing treatment after warm forging gives better mechanical strength and optimum corrosion resistance because of the formation of homogeneous and equiaxed strain-free austenite grains. After warm forging, around 85 % of grains show a low misorientation angle of 2.5°, which shows that a lot of dislocation generation occurred during warm forging deformation and that these dislocations aligned themselves to form subgrain boundaries also known as recovery during annealing dislocation. The corrosion rate drastically increases after deformation but decreases after the annealing of deformed samples, which indicates that after appropriate annealing the corrosion resistance and repassivation capacity of materials improved because of the formation of stable oxide of chromium. The value of corrosion current density ( Ecorr ) shifted toward the passive direction in the Tafel plot after annealing of deformed samples, which indicates that a more protective passive film of Cr 2 O 3 formed on the surface of the annealed sample after warm forging. The surfaces of the samples after an immersion test in the FeCl 3 solution have been observed by scanning electron microscopy, and from micrographs, it has been observed that the number of pits is reduced after the annealing of a warm-deformed sample as compared with undeformed samples. The pitting potential of the samples was calculated in a simulated pressurized water reactor environment using the Tafel potentiodynamic polarization test. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aAustenitic stainless steel. =700 1\$aGupta, Ratnesh Kumar,$eauthor. =700 1\$aDas, Ghanshyam,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190228.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190230 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190230$2doi =037 \\$aMPC20190230$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS610 =082 04$a671.56$223 =100 1\$aPanikar, Ramanandan Santhanu,$eauthor. =245 10$aThe Effect of Reflow Temperature on Time at the End of Gravity Zone (Tgz) of Sn-3.8Ag-0.7Cu Solder Alloy /$cRamanandan Santhanu Panikar, V. Amogha Skanda, Sanjay Tikale, K. Narayan Prabhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe reflow time for solder until the end of the gravity zone ( Tgz ) is considered to be the optimum reflow time for obtaining high mechanical performance from lead-free solders. In the present work, the effect of reflow time and temperature on Tgz of Sn-3.8Ag-0.7Cu (SAC387) lead-free solder alloy reflowed on the copper substrate has been investigated. The evolution of interfacial microstructure and solder bond shear strength under different reflow temperatures and time was assessed. Solder balls weighing 0.08±0.01 g were reflowed at 260°C, 280°C, and 300°C for reflow times of 30 s, 60 s, 120 s, and 240 s. Times at the end of the gravity zone for SAC387 solder were obtained as 110±5 s, 55±5 s, and 23±3 s for reflow temperatures of 260°C, 280°C and 300°C, respectively. The contact angle for SAC387 solder on the copper substrate at Tgz was found to be 25.5°±0.2° for all reflow temperatures. Scanning electron microscopy revealed the formation of a Cu 6 Sn 5 intermetallic compound (IMC) layer at the interface. The IMC layer thickness increased with increase in reflow temperature and time. Maximum solder joint strength was obtained at Tgz reflow times for all reflow temperatures. Microstructures of samples reflowed beyond the gravity zone showed secondary Cu 6 Sn 5 precipitation in the solder bulk. The present investigation reveals a reduction in Tgz reflow time for SAC387 lead-free solder at higher operating reflow temperatures. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aSolder and soldering. =700 1\$aSkanda, V. Amogha,$eauthor. =700 1\$aTikale, Sanjay,$eauthor. =700 1\$aPrabhu, K. Narayan,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190230.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190233 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190233$2doi =037 \\$aMPC20190233$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.17$223 =100 1\$aRivolta, Barbara,$eauthor. =245 10$aHeat Treatment and Impact Toughness of the F55-Grade Steel /$cBarbara Rivolta, Riccardo Gerosa, Francesca Tavasci. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aLow-temperature impact tests are commonly performed to test the quality of industrial forgings in Duplex Stainless Steels (DSS) The F55 grade is a highly alloyed Super DSS characterized by excellent low-temperature toughness in the solution annealed condition. Because of the rich chemical composition, it is very prone to precipitation phenomena during quenching. This research investigates the effect of the material cooling rate on the impact toughness of a water-quenched F55 steel, characterized by the absence of σ-phase. Furthermore, by elaborating the impact test data, the T 45 J [°C] and the KV -46°C [J] parameters have been identified. They are two indicators based on the austenite/ferrite ratio and the material cooling rate, useful for predicting the material impact behavior prior to testing. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aStainless steel. =700 1\$aGerosa, Riccardo,$eauthor. =700 1\$aTavasci, Francesca,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190233.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190245 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190245$2doi =037 \\$aMPC20190245$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ853.4.M53 =082 04$a620.106$223 =100 1\$aPasam, Vamsi Krishna,$eauthor. =245 10$aTesting of Nanofluids and Their Machining Performance Evaluation /$cVamsi Krishna Pasam, Rukmini Srikant Revuru, Parimala Neelam. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis paper is an attempt to evaluate the thermophysical properties and performance of vegetable oil–based nano-cutting fluids while turning American Iron and Steel Institute (AISI) 1040 steel. Nano boric acid particles in different proportions (0.25, 0.5, 0.75, 1, and 1.25 % w/w) are dispersed in coconut oil. The nano-cutting fluids thus formulated are tested for density, thermal conductivity, and dynamic viscosity. Empirical relations are used to evaluate specific heat and heat transfer coefficients. These nanofluids are then applied during machining through minimum quantity lubrication technique. Microbial contamination and biodegradability tests are conducted to assess the quality of nano-cutting fluids. It is observed that the contribution of depth of cut is 46 % and the contribution of nanoparticle inclusions (NPI) is 31.29 % in minimizing the cutting temperatures. Optimum machining performance is influenced mainly by NPI followed by depth of cut, cutting speed, and then feed rate. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aNanofluids. =700 1\$aRevuru, Rukmini Srikant,$eauthor. =700 1\$aNeelam, Parimala,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190245.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190248 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190248$2doi =037 \\$aMPC20190248$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a671.52$223 =100 1\$aAgrawal, Arvind K.,$eauthor. =245 10$aFriction Stir Processing of AA6063-T6 Tubes and End Forming Characterization at Varying Tool Pin Profiles /$cArvind K. Agrawal, R. Ganesh Narayanan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe effect of tool pin profiles on the end forming performance of friction stir processed (FSPed) Al6063-T6 tubes has been studied. FSP is done in the longitudinal direction of the tube. Straight cylindrical pin, tapered cylindrical pin, and stepped cylindrical pin (STP) are selected. End expansion, end reduction, and end beading experiments are conducted. The load-displacement curve and instabilities are evaluated and predicted by finite element simulations and the strain mapping method. The STP generates better ductility and a better strain hardening exponent because of the reduction in dislocation density in the stir zone. This has a considerable effect on load requirement and displacement at failure during end expansion and end beading, whereas it has an insignificant effect during end reduction. The hardness index of FSPed tubes improves during end forming because of strain hardening, which is appropriate for structural applications in industries. FSPed tubes perform equal to that of parent tubes in terms of energy absorption during end beading and end reduction, whereas it is not so in end expansion, highlighting the applicability of FSPed tubes for tube beading and reduction applications. Instabilities in the form of longitudinal crack, wrinkling, and overlap are observed. The predicted instability results agree well with experimental data during end reduction and end beading, and they have reasonable agreement during end expansion. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aMetals$xFormability. =650 \0$aFriction stir welding. =700 1\$aNarayanan, R. Ganesh,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190248.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190249 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190249$2doi =037 \\$aMPC20190249$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.T5 =082 04$a620.1/89322$223 =100 1\$aSu, Sichao,$eauthor. =245 10$aEffect of Ultrasonic Cavitation and Chemical Erosion on TC4 Titanium Alloy in Aluminum Melt /$cSichao Su, Ruiqing Li, Xiaoqian Li. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAn ultrasonic radiation rod made of Ti-6Al-4V (TC4) titanium alloy can be eroded in an aluminum alloy casting, which can also affect the stable transmission of ultrasonic waves. This erosion is a result of complex, multifactor interaction. Therefore, two groups of experiments were designed: one group did not apply ultrasonic treatment (UST), while the other group did. Five titanium alloy samples removed from the radiation rod were ground on the automatic grinding machine to make their surface roughness similar. The four samples were placed in the molten aluminum for 4.5, 9, 13.5, and 18 h, respectively, without UST. The remaining sample was placed in molten aluminum with UST for 4.5 h. The four samples without UST were cooled and cut through the middle position by a wire-cutting machine. The cross sections of the four samples were ground and observed by a scanning electron microscope (SEM) The generated chemical layer was determined to be titanium trialuminide alloy (TiAl 3 ) by energy dispersion spectrum (EDS) analysis, and its thickness was approximately 20–50, 145, 220, and 345 Μm, respectively, corresponding to different processing times. The fifth titanium alloy sample was processed by UST, the residual aluminum on the sample surface was removed by hydrochloric acid, and obvious erosion pits and microcracks were found by SEM. The roughness of the surface was approximately 340 Μm in the LY-WN-YH 3-D system. Therefore, the effect of ultrasonic cavitation on TC4 titanium alloy is much larger than that of a chemical reaction. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aTitanium alloys. =700 1\$aLi, Ruiqing,$eauthor. =700 1\$aLi, Xiaoqian,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190249.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190251 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190251$2doi =037 \\$aMPC20190251$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS1767 =082 04$a677/.02864/0973$223 =100 1\$aRastogi, Shweta,$eauthor. =245 10$aExperimental Response of Nonwoven Waste Cellulose Fabric–Reinforced Epoxy Composites for High Toughness and Coating Applications /$cShweta Rastogi, Akarsh Verma, V. K. Singh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this article, the authors have fabricated (using the manual hand lay-up method) and characterized in detail the nonwoven waste cellulose fabric (with varying weight percentages of 0, 7, 9, and 11) reinforced epoxy resin composites. The methodology to develop in conjunction with various physical (density, water absorption, and thickness swelling), mechanical (tensile, compression, flexural, hardness, and impact), thermal (differential thermal analysis, thermogravimetric analysis, and derivative thermogravimetric analysis), morphological (scanning electron microscopy and X-ray diffraction), and electrical characterization tests were performed to give complete insight into the mechanics of epoxy fabric laminates. It was predicted from these tests that with an increasing weight percentage of fabric, most of the mechanical properties improved and were complemented through the microstructural morphological tests. Enhanced mechanical strength and thermal stability of the developed composite (relative to the neat epoxy resin) pave its way for high toughness and coating applications in various engineering fields. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aComposite materials. =700 1\$aVerma, Akarsh,$eauthor. =700 1\$aSingh, V. K.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190251.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190253 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190253$2doi =037 \\$aMPC20190253$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQA279 =082 04$a519.6$223 =100 1\$aDwivedi, Shashi Prakash,$eauthor. =245 10$aIdentification of Microwave Radiation Effect on Copper Welded Joint with Brass as Filler Material Using Response Surface Methodology /$cShashi Prakash Dwivedi, Satyendra Sharma, Satpal Sharma. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this study, copper plates were welded using the microwave technique, and brass material was used as an interface. The response surface methodology was used to optimize the microwave parameters for maximum joint strength, which resulted in a value of 264 MPa in 350 s. The welding temperature was maintained at 1,100°C for maximum joint strength using a single microwave oscillator with a rated power of 890 W. A Hardness test was carried out, and the tested parameter was 79 BHN, which is a better result compared with traditional welding. The corrosion behavior of the copper welded joint was also observed to be an effect of brass when used as an interfacial material between the copper plates. Weight loss of the heat-affected zone in salt solution (5 % NaCl+95 % water) after 96 hours was found to be zero. This result indicates that brass as a filler material also enhances the corrosion resistance of the welded joint. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aResponse surfaces (Statistics) =650 \0$aExperimental design. =700 1\$aSharma, Satyendra,$eauthor. =700 1\$aSharma, Satpal,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190253.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190254 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190254$2doi =037 \\$aMPC20190254$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.118$223 =100 1\$aSingh, Komal,$eauthor. =245 10$aFunctionalized Graphite–Reinforced Cross-Linked Poly(vinyl Alcohol) Nanocomposites for Vibration Isolator Application: Morphology, Mechanical, and Thermal Assessment /$cKomal Singh, Naman Jain, Akarsh Verma, V. K. Singh, Sakshi Chauhan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present investigation, cross-linking of poly(vinyl alcohol) (PVA) was done to enhance the physical, mechanical, and thermal properties of neat PVA. Furthermore, to specifically enhance the mechanical properties, functionalized graphite (via oxidative acidic treatment) particles were used as reinforcement material with varying weight percentages (0, 0.5, 1, 1.5, and 2) in the PVA domain. Fabricated samples are firstly examined by a water absorption test to confirm the formation of cross-linked bonds. Fourier transform infrared spectroscopy is used to confirm the oxidative acid treatment to functionalize the graphite particles. Scanning electron microscopy of the fractured surface of fabricated composites shows strong interfacial bonding taking place between the functionalized graphite and cross-linked PVA, which results in improved mechanical properties of fabricated composites. The maximum ultimate tensile strength is found at 1 wt. % of functionalized-graphite particle reinforcement, which is about 62.5 % higher than neat PVA. The thermal stability of composites was also enhanced with an increase in functionalized graphite particles weight percentage. Dynamic mechanical analysis results show a high value of damping coefficient (tan δ), which is about 0.573 for cross-linked PVA, which confirms a high damping character. Therefore, these materials could be potentially used to minimize noise transmission as a vibration isolator and shock absorber and in nanocoating applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aNanocomposites (Materials) =700 1\$aJain, Naman,$eauthor. =700 1\$aVerma, Akarsh,$eauthor. =700 1\$aSingh, V. K.,$eauthor. =700 1\$aChauhan, Sakshi,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190254.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190255 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190255$2doi =037 \\$aMPC20190255$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.2 =082 04$a620.11232$223 =100 1\$aHunston, D. L.,$eauthor. =245 10$aEffects of Prestrain on the Nonlinear Viscoelastic Properties of a Model Sealant /$cD. L. Hunston, K. T. Tan, C. C. White. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aElastomeric sealants are nonlinear viscoelastic materials that exhibit the Mullins effect. As a result, the behavior of a sealant depends on the previous history of strains the sample has seen. To deal with this issue, characterization tests like ASTM C1735, Standard Test Method for Measuring the Time Dependent Modulus of Sealants Using Stress Relaxation , subject the specimen to a specific strain history before measuring properties. To gain a better understanding of this history effect, this article studied a model sealant where the nonlinear viscoelastic properties were measured after a variety of strain histories ranging from no exposure to strain before the test to the history specified in ASTM C1735. The results provide insight into how strain history affects properties, supports information for the ASTM characterization test, and adds knowledge on the nature of the Mullins effect. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aViscoelasticity. =700 1\$aTan, K. T.,$eauthor. =700 1\$aWhite, C. C.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190255.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190256 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190256$2doi =037 \\$aMPC20190256$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.G65 =082 04$a662.92$223 =100 1\$aSabet, Maziyar,$eauthor. =245 10$aThe Effect of Graphene Oxide on Flame Retardancy of Polypropylene and Polystyrene /$cMaziyar Sabet, Hassan Soleimani, Erfan Mohammadian, Seyednooroldin Hosseini. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis study discusses how a graphene oxide (GO) has been developed to improve flame resistance, ignitability, and flame threats of polystyrene (PS) and polypropylene (PP) For reasons where high thermal stability alongside fire-resistant parts for vehicles or airships is essential, the manufacture of lightweight products appears to have promising outcomes. Cone calorimeter and limiting oxygen index experiments were used to measure heat and fire experiments of PS and PP nanocompounds. The incorporation of GO into PS and PP structures has reduced the heat release rate as measured through cone calorimeter. The characterization implied that without clear accumulations, the GO nanolayers were properly distributed throughout the PS structure, resulting in an outstanding upgrade of thermal strength and fire safety characteristics. During the ignition period, GO dispersal in PS and PP accelerated the ignition period and lowered the heat release rate. In addition, the incorporation of GOs reduced the PP‘s combustion rate as a result of developing a carbon protective layer that acts as a heat and mass transfer barrier. However, during combustion experiments, nanocompounds PS/GO and PP/GO generate a thermal insulation intumescent that protects the sublayers of the polymer. The peak of the heat release rate was reduced by 23 % for PP/GO and 53 % for PS/GO under flaming circumstances. The maximum thermal release rate indicates a substantial reduction for PP/GO 2.0 weight percent of nanocomposite compared to pure PP. This research shows that even GO inclusion does not change the limiting oxygen index values, but the development of an intumescent char protects the polymer sublayers properly. This feature offers a distinctive modification strategy to enhance GO‘s flame-resistant effectiveness. This research offers excellent insights into PP and PS nanocompounds‘ ignitability behavior with the inclusion of GO filler. This study delivers an appropriate choice to evaluate the potential for fire safety using graphene in polymers and flame-retarded polymers. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aGraphene. =700 1\$aSoleimani, Hassan,$eauthor. =700 1\$aMohammadian, Erfan,$eauthor. =700 1\$aHosseini, Seyednooroldin,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190256.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190257 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190257$2doi =037 \\$aMPC20190257$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA472 =082 04$a629.232$223 =100 1\$aVijayan, Vijeesh,$eauthor. =245 10$aMetallography and Computed Tomography Analysis of the Shrinkage Cavity Formed in Advanced High-Strength Steel Resistance Spot Welds /$cVijeesh Vijayan, Siva Prasad Murugan, Seong-Guk Son, Yeong-Do Park. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAmong various defects formed in resistance spot welds (RSW), voids or cavities formed at the center of the nugget are scarcely studied. However, it is widely accepted that such cavities significantly influence the mechanical properties of the spots, especially in advanced high-strength steels (AHSS) Nonavailability of a proper characterization technique to quantify these cavities is one of the reasons for less research in this area. Although conventional metallographic analysis portrays cavities in the nugget, the associated destructive sampling results in erroneous interpretation. To date, there is no reliable technique to quantify the size, shape, and distribution of the voids in the nugget. In this context, the present study uses a computed tomography (CT) technique to visualize and quantify the cavities in spot-welded AHSS nuggets. The images obtained using a CT scan provide a new insight into the cavity and its characteristics, such as volume and surface topology. According to the CT results, the voids formed in AHSS spots increase with the increase in base metal yield strength. Furthermore, the CT results also reveal that the conventional critical diameter of 4×thickness1/2 to obtain plug failure in RSW is not valid for AHSS spots because of the influence of the cavity in the faying interface. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aSteel, High strength. =700 1\$aMurugan, Siva Prasad,$eauthor. =700 1\$aSon, Seong-Guk,$eauthor. =700 1\$aPark, Yeong-Do,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190257.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190258 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190258$2doi =037 \\$aMPC20190258$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.T54 =082 04$a669.7322$223 =100 1\$aVyas, Vandan V.,$eauthor. =245 10$aWettability Studies of Titanium and Its Oxide-Based Coatings /$cVandan V. Vyas, Kamlesh V. Chauhan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThin films of titanium oxide were deposited on the substrate of corning glass using radio frequency magnetron sputtering, and the films were then annealed at temperature of 500°C, 650°C, and 800°C for 1 h. For the purpose of film characterization, X-ray diffraction technique was used; for the study of surface topography and wettability, atomic force microscope and commercial goniometer were used; and for the study of optical properties, ultraviolet visual light spectra was used. The measurement of wettability was performed after the storage of samples for significant time in a dark room and after sunlight exposure for 5 h in ambient conditions. It was observed that the unannealed sample showed an amorphous phase, whereas samples annealed from 500°C to 650°C showed formation of anatase. At 650°C, the rutile phase appeared, and at 800°C, the conversion of anatase phase to rutile phase was observed. Titanium oxide films, after storage in a dark room, showed a hydrophobic nature, but after white light exposure for 5 h, superhydrophilic properties with a contact angle up to 4° was obtained. The results showed that with an increase in anatase phase, hydrophilicity was enhanced, but with the conversion to rutile phase, a significant increment in the values of the contact angle was observed from 4° to 27°. The films showed a highly transparent surface with around 85 % transparency. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aTitanium. =700 1\$aChauhan, Kamlesh V.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190258.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190259 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190259$2doi =037 \\$aMPC20190259$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.T54 =082 04$a669.7322$223 =100 1\$aVyas, Vandan V.,$eauthor. =245 10$aA Review Paper on Wettability Properties of Titanium and Its Oxide-Based Coatings /$cVandan V. Vyas, Kamlesh V. Chauhan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aNano-coating has become the focus of study in recent years because of its wide range of applications in several fields to obtain superior materials. By depositing a thin film with thickness ranging from nanometer to micrometer, an advanced material is developed. These advanced materials have properties like ultraviolet (UV) protection, self-cleaning properties, photocatalyst properties, and thermal resistance as well as thermal conductivity, higher reflectivity and transparency, wear resistance, and much more. All these properties depend upon the target materials used for the process and the formation of films. By obtaining a proper deposition process of selective target material, an enhanced component in the field of energy optimization, biological implants, mechanical instruments and tools, and thermal resistive surfaces that will have superior properties can be developed. These properties of an advanced material depend upon the chemical characteristic of the target material, the thickness of the film deposited, grain size and grain orientation, and surface morphology as a few of the important factors. In this review paper, the studies carried out by different scientists on titanium oxide as a target material to study the wettability properties, optical properties, and effect of annealing on wettability, effect of the phase of titanium oxide on wettability, and effect of UV irradiation on wettability have been reviewed. Different deposition processes, such as a physical deposition process as well as a chemical deposition process, have been considered. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aTitanium. =700 1\$aChauhan, Kamlesh V.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190259.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190260 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190260$2doi =037 \\$aMPC20190260$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA410 =082 04$a620.1126$223 =100 1\$aBhat, Anirudh,$eauthor. =245 10$aOn the Constraint Factor Relating Uniaxial and Indentation Yield Strength of Polycrystalline Materials Using Spherical Microindentation /$cAnirudh Bhat, R. W. Neu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHigh-throughput (HT) material property characterization has become increasingly important for the rapid and cost-effective development of new material systems. In recent years, spherical indentation using the Pathak-Kalidindi (P-K) protocol has been shown to be a reliable and HT method for capturing the elastic-plastic properties of several different types of materials. However, because of the higher hydrostatic pressure under the indenter tip and the constraint of the surrounding elastically deforming material, the indentation yield strength is higher than the uniaxial yield strength and they can be related by a scaling factor, referred to as the constraint factor. For fully plastic indentation, the constraint factor was found by Tabor to be ~2.8. However, the constraint factor is not well defined for elastic-plastic indentation and depends on the strain induced. In this work, the application of the P-K indentation protocol is demonstrated on a set of aluminum 7050 samples that have undergone different solution and aging treatments. Conventional uniaxial tensile and compression tests were also conducted on the same material. The constraint factor at the 0.2 % offset yield point was determined from the indentation and uniaxial measurements to be ~1.4. Experimental observations from our work and a similar work on aluminum 6061 showed a dependence of the constraint factor at the 0.2 % offset yield point on the uniaxial plastic properties. To explain these experimental observations, further investigation was carried out using finite element simulations of spherical indentation on materials with different yield strengths and hardening parameters. New insights are provided on the constraint factor at the 0.2 % yield point, which show that it increases with the ratio of the plastic to elastic strain. It was also found that the effect of the hardening is much less than that of the yield strength on the constraint factor at the 0.2 % yield point. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aMetallography. =650 \0$aMaterials$xTesting. =700 1\$aNeu, R. W.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190260.htm =LDR 03762nab 2200553 i 4500 =001 MPC20190261 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190261$2doi =037 \\$aMPC20190261$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC151 =082 04$a532.05$223 =100 1\$aWoydt, Mathias,$eauthor. =245 10$aHydrodynamic Fluid Film and Tribofilm Formation—Combining the Friction Signals with Contact Resistance /$cMathias Woydt, Raj Shah. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aUnder unidirectional sliding, the Stribeck-type curve traverses different lubrication regimes. Under mixed/boundary conditions, tribofilms formed by additives in lubricants represent a key mechanism for preventing wear but are difficult to investigate because of the complex composition of lubricants, their small thickness, and their amorphous nature. The formation of a hydrodynamic fluid film depends on the topography and the viscometric fluid properties. Low coefficients of friction do not consequently indicate that hydrodynamic fluid films were formed. The electric contact resistance serves here as a complementary indicator to identify the hydrodynamic fluid film and tribofilm formation under transient or static sliding conditions. The frictional work ( WR ) is a useful quantity to assess the contribution to the frictional losses of all lubrication regimes in a Stribeck-type curve. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aHydrodynamics. =650 \0$aFluctuations (Physics) =700 1\$aShah, Raj,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20190261.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200001 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200001$2doi =037 \\$aMPC20200001$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP951 =082 04$a662.93$223 =100 1\$aTortora, Angela Maria,$eauthor. =245 10$aNovel Insight into Tribology of Carbon Black Soot Particles in Engine Oil /$cAngela Maria Tortora, Gerrit Zijlstra, Deepak Halenahally Veeregowda. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAn investigation into the interaction between soot and steel surfaces can improve the development of soot wear–resistant lubricants. In this study, we have tested the wear response of carbon black (CB; a surrogate for engine soot) on different steel surfaces using the high-frequency reciprocating rig and scanning electron microscopy – energy-dispersive X-ray spectroscopy. Results show that CB in 0W20 reacts to the preconditioned steel surface differently than the nonpreconditioned steel surface. Chemisorption of zinc dialkyldithiophosphates (ZDDP) on the steel surface prior to the wear test resulted in severe wear, but the shear-induced chemisorption of ZDDP on the steel surface showed the least wear. Changes in wear were related to the concentration of zinc and phosphorus, which represent antiwear phosphate film on the surface. Chemisorption of ZDDP prior to the test triggered an aggressive response by CB, as there was a complete removal of antiwear phosphate film. Thus, unprotected steel was exposed to sulfur, a corrosion enhancer in the lubricant that resulted into micropitting and grooves on the disk surface, a representation of the corrosion–abrasion wear mechanism. Shear-induced chemisorption of ZDDP on steel surface allowed retention of antiwear phosphate films. As a result, there were no grooves or severe micropitting on the steel surface, indicating a protection against CB. This study shows that preconditioning the steel can have a profound effect on the soot wear mechanism. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aCarbon-black. =700 1\$aZijlstra, Gerrit,$eauthor. =700 1\$aVeeregowda, Deepak Halenahally,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200001.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200003 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200003$2doi =037 \\$aMPC20200003$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ840.A3 =082 04$a629.24$223 =100 1\$aKazama, Toshiharu,$eauthor. =245 10$aCavitation Erosion Characteristics of High Bulk Modulus Oils: Preliminary Evaluation Experiment for Hydraulic Equipment /$cToshiharu Kazama, Shinji Aoki, Masahiro Kobessho. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA high bulk modulus oil, which promises to enhance the responsibility and efficiency of hydraulic systems, has been developed because of high pressure operation. Although cavitation erosion in the hydraulic components is a serious concern, the phenomena and behaviors of the oils for the erosion have not been examined. This report investigates the characteristics of cavitation erosion caused by a cavitating jet in terms of high bulk modulus oils produced with different compounding agents and molecular weights and mineral oils prepared as a reference. The experiment was conducted in a test rig, applying the jet-cavitation method under an upstream absolute pressure of 10.1 MPa. The diameter and thickness of the aluminum alloy specimens were 15 and 5 mm, respectively. The mass loss was maximized at a specific standoff distance, and the surface erosion was ring-like, as previously reported for general hydraulic oils and municipal water. The mass losses in the high bulk modulus oils and mineral oils increased with increasing liquid temperature and decreasing cavitation number under the test conditions. Although the erosion is intrinsically enhanced because of the high bulk modulus oils with high density, the erosion can be reduced by adding high molecular-weight polymer. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aHydraulic machinery. =700 1\$aAoki, Shinji,$eauthor. =700 1\$aKobessho, Masahiro,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200003.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200008 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200008$2doi =037 \\$aMPC20200008$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.N35 =082 04$a620.118$223 =100 1\$aShinde, Deepak M.,$eauthor. =245 10$aHigh Temperature Tribology of A413/B4C Nanocomposites under Dry Sliding Contact /$cDeepak M. Shinde, Suswagata Poria, Prasanta Sahoo. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this work, boron carbide (B 4 C) particulate (0.5, 1.0, 1.5, and 2.0 weight %) reinforced A413 alloy nanocomposites were fabricated by ultrasonic stir casting method. The prepared aluminum matrix nanocomposites were characterized using optical microscopy and field emission scanning electron microscopy to observe particle dispersion and quantify microstructural features. A high temperature pin-on-disk tribo-tester was employed to investigate the dry sliding tribological behavior of fabricated nanocomposites and unreinforced alloy at a constant speed (0.66 m/s) and different loads (20, 60 N) over the temperature range of 50°C–200°C. Specimens were slid against an AISI SAE 52100 counterface for the fixed duration of 10 minutes. Worn surfaces were examined under the scanning electron microscopy, and energy dispersive spectroscopy analysis was carried out to understand the wear mechanisms. It was revealed that the wear resistance of the alloy improved because of increasing B 4 C content. The wear rate of all specimens was found to increase with increased load and operating temperatures. A shift in the mild oxidative to severe metallic wear of an unreinforced alloy was seen increased by about 50°C–80°C because of particulate reinforcement. The mild abrasive wear mechanism of the base alloy at low temperature was changed to adhesion with heavy plastic deformation at elevated temperature. Increased thermal stability offered by boron carbide particles and oxides and a mechanically mixed transfer layer were key factors enhancing the wear resistance of the nanocomposites. Under the tested experimental conditions A413/B 4 C nanocomposite was found suitable and better than the base alloy for use in wear resistance applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aNanocomposites (Materials) =700 1\$aPoria, Suswagata,$eauthor. =700 1\$aSahoo, Prasanta,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200008.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200010 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200010$2doi =037 \\$aMPC20200010$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ291 =082 04$a621.194$223 =100 1\$aKumar, Ravindra,$eauthor. =245 10$aOxidation Behavior of Microstructurally Different Regions of TIG Weldment in ASTM SA 210 GrA1 Boiler Steel /$cRavindra Kumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aASTM SA 210 GrA1 steel is used for many different applications of steam-generating systems in thermal power plants because of its resistance to corrosion at elevated temperatures and low cost of production. This study examines the oxidation behavior of tungsten inert gas (TIG) weldment in GrA1 boiler steel. Different regions of the weldment were identified by optical microscopy. The oxidation studies were then performed about heat-affected zone (HAZ) and weld metal specimens of TIG weldment after exposure to air at 900°C under cyclic conditions. The thermogravimetric method was applied to observe the kinetics of oxidation. X-ray diffraction and scanning electron microscopy with energy-dispersive X-rays techniques were used to analyze the oxidation product. The HAZ region confirmed the presence of moderately more oxidation (in terms of weight gain of 145.045 mg/cm 2 ) than that of weld metal (139.797 mg/cm 2 ) because the formation of the thick porous oxide scale had internal voids to a high extent. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aSteam-boilers. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200010.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200013 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200013$2doi =037 \\$aMPC20200013$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP691 =082 04$a665$223 =100 1\$aMolina, Gustavo J.,$eauthor. =245 10$aViscosity of Mineral Oil Diluted by Biodiesel Methyl Esters: Methods for Mixture Predictions and Small Samples after Tribometer Testing /$cGustavo J. Molina, Sultana M. Shanta, Emeka F. Onyejizu, Valentin Soloiu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe use of biodiesels in internal combustion engines leads to tribology concerns because significant oil dilution occurs when biodiesels leak into the oil pan. Dilution by biodiesels may substantially alter oil lubricity and lead to reduced viscosity, which produce tribological changes on engine materials. It is also possible that such oil-biodiesel mixtures undergo further viscosity decreases when subjected to the high temperatures and high contact pressures typical of internal combustion engine boundary lubrication. This research presents new methods to test viscosity reductions because of biodiesel addition in mineral oil and to assess prediction of mixture viscosity considering the chemical breakdown of biodiesel. The results of dynamic viscosity versus dilution rates are presented for small after-tribometer-testing samples of SAE 15W40 mineral oil diluted by four biodiesels (from canola, peanut, and soybean and chicken fat oil) The small sample remaining after tribometer-testing required an ad-hoc method, the suitability of which is discussed; large viscosity decreases in a range of about 70 to 95 % were observed for after tribometer testing of the mixtures. Preliminary data of viscosity versus temperature also are presented for the mineral oil diluted by increasing fractions of different biodiesels and by six pure fatty-acid methyl esters (methyl-oleate, -palmitate, -linoleate, -laurate, -myristate, and -stearate, which are typical components of biodiesels), and they are discussed to explain tribological properties of such mixtures. The results suggest that the viscosity of commercial biodiesels blended in oils could not be fully explained by assuming the former as mixtures of pure methyl esters, which is consistent with the previous experimental data on their tribological effects. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aMineral oils. =650 \0$aPetroleum$xTesting. =650 \0$aSteel$xCorrosion. =700 1\$aShanta, Sultana M.,$eauthor. =700 1\$aOnyejizu, Emeka F.,$eauthor. =700 1\$aSoloiu, Valentin,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200013.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200017 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200017$2doi =037 \\$aMPC20200017$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA472 =082 04$a672$223 =100 1\$aDurango, Alexander Zuleta,$eauthor. =245 10$aEffect of Temperature on Friction and Wear Behavior under Reciprocating Dry Sliding of AISI 52100 Steel against AISI H13 Steel /$cAlexander Zuleta Durango, Michell Felipe Cano, Roberto Martins Souza, Amilton Sinatora. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPrevious work about the effect of temperature on friction and wear of dry steel-on-steel sliding tests showed a transition from severe wear to mild wear. Nevertheless, in dissimilar counterpart materials, the mechanical properties and microstructural characteristics generate differences in friction and wear behavior. In this work, experimental tests were conducted in an SRV-4 tribometer using a ball-on-disk configuration (i.e., nonconformal contact) The selected materials were AISI 52100 bearing steel balls and AISI H13 steel disks, which are used in different engineering applications. Frequency, load, and stroke length parameters were fixed, and analyses refer to the effect of different times and temperatures. The results of friction coefficient above 300°C showed 2 friction regimes as a function of test time. In the first friction regime, abrasion of the counterpart was observed, and for the second friction regime, the reduction of friction and wear was related to an oxide tribolayer formation. Tribological tests for the lowest time, of 0.5 h, were not long enough to show two friction regimes, which were observed in other test times (4, 8, and 15 h). =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aSteel, Bearing. =700 1\$aCano, Michell Felipe,$eauthor. =700 1\$aSouza, Roberto Martins,$eauthor. =700 1\$aSinatora, Amilton,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200017.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200018 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200018$2doi =037 \\$aMPC20200018$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.6 =082 04$a624.176$223 =100 1\$aLi, Xin,$eauthor. =245 10$aFatigue Behavior of Bolted Joints: Comparative Analysis for the Effect of Fretting and Stress Concentration /$cXin Li, Jianwei Yang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this paper, a methodology is developed to investigate the combined effect of some main factors (bolt pretension load, shear load, coefficient of friction, and bolted joints structure) on the fatigue performance of bolted joints. A parameter k , which reflects the ratio of bolt pretension load to shear load, is used to evaluate the competition effect of fretting and stress concentration on fatigue damage of bolted joints. The analysis result deduces that as the increase of k , the effect of stress concentration is decreased, while the influence of fretting is increased. At the increase of the bolt pretension load, the fatigue crack formation position will be far away from the hole center. This parameter k can be used as a design or assembly parameter to improve the strength performance of the bolted joints. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aStress concentration. =700 1\$aYang, Jianwei,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200018.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200019 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200019$2doi =037 \\$aMPC20200019$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP884.A3 =082 04$a666.893$223 =100 1\$aSingh, Avtar,$eauthor. =245 10$aWear and Tensile Behavior of Titanium Carbide and Fly Ash–Reinforced Magnesium Matrix Composites /$cAvtar Singh, Niraj Bala, Baljinder Ram. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMetal matrix composites are considered as suitable materials for enhancing the properties of materials used for automobile and aerospace sectors. This research work is about magnesium matrix composites reinforced with 7 wt. % of titanium carbide and fly ash fabricated by stir casting technique. The particle distribution of the reinforcements in matrix material was examined by using optical microscope and scanning electron microscopy technique. The mechanical and microstructural properties of composites were investigated and compared with stir-cast pure magnesium. Titanium carbide and fly ash–reinforced composite showed around a 55.5 % and 33.3 % increase in hardness, respectively. Titanium carbide–reinforced composite displayed more wear resistance as related to fly ash composite and stir-cast pure magnesium. There was also an increase in tensile strength of composites as equated to stir-cast pure magnesium. The fracture behavior of composites showed the presence of surface cracks, voids, and particles of reinforced material in composites. As compared to titanium carbide–based composite, fly ash composite showed wider voids and agglomeration of fly ash particles in fracture surface. However, the fractured surface of pure magnesium showed deep voids as compared to composites along with elongated dimples. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aFly ash. =700 1\$aBala, Niraj,$eauthor. =700 1\$aRam, Baljinder,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200019.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200020 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200020$2doi =037 \\$aMPC20200020$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aRK651 =082 04$a610$223 =100 1\$aDobrzański, Leszek A.,$eauthor. =245 10$aApproach to the Design and Manufacturing of Prosthetic Dental Restorations According to the Rules of Industry 4.0 /$cLeszek A. Dobrzański, Lech B. Dobrzański. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (83 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe paper contains an extensive, richly illustrated literature study, theoretical studies, and practical work on current development trends of technical support for dental prosthetics. Dentistry 4.0 is the concept closely inspired by the highest stage Industry 4.0 of the industrial revolution. An augmented holistic Industry 4.0 model, which takes into account all other aspects, i.e., materials, processes, and technological machines and their development and informatics service, was developed and presented. The basis for consideration is the analysis of the disease in the human stomatognathic system and the possibility of prosthetic treatment in the event of a partial or total loss of natural dentition. In several centers, independent work on the popularization of individual implants manufactured using information obtained using conical beam computed tomography (CBCT) is carried out. The developed procedure requires one to make a three-dimensional bone base model based on the CBCT tomogram and its connection with the three-dimensional model of the dentition and soft tissues in the oral cavity, prepared on the basis of impression material, and most preferably a three-dimensional scan directly from the mouth. The presented and fully digitized approach is a radical turnaround in both clinical procedures and the method of technical implant preparation using Computer-Aided Design/Computer-Aided Manufacturing (CAD/CAM) methods and additive manufacturing technologies (AMT), including mainly Selective Laser Sintering (SLS) and stereolithography (SLA) The concept of hybrid multilayer biological-engineering composites is much more technologically advanced. The application of the principles of the augmented holistic Industry 4.0 model in modern dental engineering, according to the analysis, indicates a change in the traditional relationship between a dentist and dental engineer. The practical application of the Dentistry 4.0 approach is illustrated by projects regarding the manufacturing of a few dental restorations. The general conclusion indicates that the implementation of the ideas of Dentistry 4.0 following the assumptions of the augmented holistic model Industry 4.0 is inevitable and extremely beneficial. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aProsthodontics. =700 1\$aDobrzański, Lech B.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200020.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200026 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200026$2doi =037 \\$aMPC20200026$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.C37 =082 04$a620.17$223 =100 1\$aSondar, Pavankumar R.,$eauthor. =245 10$aDeep Cryogenic Treatment of Plain-Carbon and Low-Alloy Steels /$cPavankumar R. Sondar, Subray R. Hegde. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTo improve the mechanical properties of steels, cryogenic treatment is often carried out as an intermediate step between quenching and tempering. The transformation of retained austenite into martensite is the main objective and principle behind the cryogenic treatment. Generally, high-alloy and high-carbon steels are subjected to cryogenic treatment, as they produce a high fraction of retained austenite during quenching as compared with low- and medium-alloy steels. This work analyses the effect of cryogenic treatment on EN8, a plain-carbon steel, and EN47, a low-alloy steel, through microstructural characterization, hardness measurements, and tensile tests. The work shows that influence of cryogenic treatment carried out after tempering is only marginal, whereas cryogenic treatment carried out before tempering yields much better mechanical properties. Experimental results obtained in this work confirm that EN47 responds slightly better than EN8 suggesting that low-alloying additions influence the cryogenic treatment of steels. This work established that by properly applying cryogenic treatment, the strength and hardness of both EN8 and EN47 steels can be increased by about 50 MPa and 3 HRC, respectively, as compared with conventional hardening and tempering treatment. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aSteel alloys. =700 1\$aHegde, Subray R.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200026.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200029 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200029$2doi =037 \\$aMPC20200029$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP155.2.T45 =082 04$a660.2969$223 =100 1\$aAhmed, Ismaila Idowu,$eauthor. =245 10$aThermochemical Characterization of Horns and Hooves for Carbonitriding Treatment /$cIsmaila Idowu Ahmed, Ajadi Abdulafeez Buhari, Sulaiman Abdulkareem, Taiwo Yahaya, Jeleel Adekunle Adebisi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHorns and hooves are abattoir wastes that have not been fully used and that are sometimes disposed of indiscriminately because of a limited understanding of their thermochemical properties. However, ancient blacksmiths intuitively rub animal horns on hot forging steels in anticipation of better performance. This study therefore conducts a thermochemical characterization of horns and hooves of selected animals, namely cows, sheep, and goats, for a better understanding of their thermochemical properties. A chemical analysis of horns and hooves was conducted using both a scanning electron microscope with energy-dispersive spectroscopy and Raman spectroscopy for quantitative and qualitative analyses of the elements present, respectively. X-ray diffraction was carried out to determine the molecular phases present. The thermal behavior of samples was investigated using thermogravimetric analysis. All the samples analyzed confirmed the presence of carbon and nitrogen in significant quantities. Again, the results of thermal characterization showed cow hooves as the most thermally stable, whereas goat horns and hooves were the least thermally stable at an elevated temperature. The study therefore reinforces the potential of the horns and hooves for carbonitriding treatment of steels and consequently absolves these wastes from underutilization and indiscriminate dumping in the environment. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aThermodynamics. =650 \0$aChemical processes. =700 1\$aBuhari, Ajadi Abdulafeez,$eauthor. =700 1\$aAbdulkareem, Sulaiman,$eauthor. =700 1\$aYahaya, Taiwo,$eauthor. =700 1\$aAdebisi, Jeleel Adekunle,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200029.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200037 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200037$2doi =037 \\$aMPC20200037$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA481 =082 04$a620.16$223 =100 1\$aVeeresh Kumar, G. B.,$eauthor. =245 10$aFabrication and Investigation of Mechanical and Dry Sliding Wear Characteristics of Al6061-Si3N4 Composites /$cG. B. Veeresh Kumar, A. Ulhas Krishna Rao, T. Srinivas Rao. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAluminum based metal matrix composites (MMCs) are excellent grade engineering materials used in high-tech applications like aerospace, automotive, marine, and other applications, owing to their higher specific strength, better physical and mechanical characteristics, coupled with lower density, when compared with pure aluminum and its alloys. The present paper emphasizes experimental work that was carried out on the fabrication of Al6061 alloy reinforced with different weight percentages (wt%) of silicon nitride (Si 3 N 4 ) MMCs. The vacuum-assisted stir casting technique was used to fabricate Al6061-Si 3 N 4 composites. The wt% of Si 3 N 4 reinforcement was varied from 0 to 6 wt% in steps of 2. The optical micrograph (OM), density, energy dispersive spectroscopy, and mechanical characteristics such as resistance to indentation, ultimate tensile strength, percentage elongation, and scanning electron micrographs of the composites before and after tensile and wear tests have been investigated. The tribological studies for the determination of wear properties of developed composites were carried out with respect to volumetric wear loss, sliding distance, and applied load, with increasing Si 3 N 4 reinforcement content in Al6061 alloy. The density of Al6061-Si 3 N 4 composites has improved with increased reinforcement content as compared to monolithic alloy. The OM and scanning electron micrographs reveal a uniform distribution of Si 3 N 4 particulates in the matrix alloy. The mechanical properties along with the resistance to the wear property have improved, and there was a noteworthy loss in the ductility of Al6061-Si 3 N 4 composites in comparison with Al6061 alloy. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aMetallic composites. =700 1\$aUlhas Krishna Rao, A.,$eauthor. =700 1\$aSrinivas Rao, T.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200037.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200041 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200041$2doi =037 \\$aMPC20200041$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.T5 =082 04$a620.1/89322$223 =100 1\$aVenkata Sivareddy, D.,$eauthor. =245 10$aDetermination of Constitutive Material Model Constants for Ti6Al4V Alloy at Near Orthogonal Machining Conditions /$cD. Venkata Sivareddy, P. Vamsi Krishna, A. Venu Gopal. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe accuracy of numerical modeling of a machining process largely depends on material model constants. The Johnson-Cook (J-C) material model constants, i.e., A , B , C , n , and m , describe deformation behavior of material under thermomechanical loading. This paper considers an equivalent strain hardening exponent neq in place of ‘ n ‘ in the J-C constitutive law for accurate prediction of material model constants at near orthogonal machining conditions. The effect of strain on the secondary deformation zone, i.e., the tool-chip interface, is also considered for accurate prediction of material parameters. In the present work, a machining approach based on response surface methodology and particle swarm optimization technique are used to identify J-C material model constants for the Ti6Al4V alloy. The cutting force, feed force, and chip thickness obtained from orthogonal experiments are used to evaluate the physical quantities of Oxley‘s extension theory at different rake angles. It is noted that J-C constants determined from the present approach at a 7° rake angle are more accurate in predicting flow stress than J-C constants determined from other methods. J-C constants identified from a machining approach show less deviation from the measured equivalent flow stresses obtained at similar machining conditions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aTitanium alloys. =700 1\$aVamsi Krishna, P.,$eauthor. =700 1\$aVenu Gopal, A.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200041.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200043 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200043$2doi =037 \\$aMPC20200043$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL521.3 =082 04$a651.8$223 =100 1\$aFeng, Ning,$eauthor. =245 10$aLinear In-Plane Elasticity of a Polygon Honeycomb Core with Zero Poisson’s Ratio /$cNing Feng, Jie Yan, Zhiyong Feng, Xinjian Lin, Tong Zhang, Jian Li. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis paper reports a zero Poisson‘s ratio honeycomb core with a polygon shape. Compared with the traditional hexagonal honeycomb, a unit cell of the proposed polygon honeycomb core was modified. As it turns out, this variation results in great mechanical property diversity of variable in-plane elasticity as compared with the traditional hexagonal honeycomb. The elastic constants were investigated via theoretical approach, and finite element (FE) models were conducted to verify the theoretical results. The developed theoretical models for calculating the in-plane elastic modulus are based on the Euler-Bernoulli beam theorem and energy principle. A topological analysis of the polygon honeycomb core was conducted to classify the changing geometry into three styles. The in-plane elastic modulus derived from the FE results showed a very high similarity to the theoretical calculation in the three changing geometry styles. The theoretical results of the in-plane elastic modulus are able to capture the changing trend in the whole geometry. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aHoneycomb structures$xTesting. =700 1\$aYan, Jie,$eauthor. =700 1\$aFeng, Zhiyong,$eauthor. =700 1\$aLin, Xinjian,$eauthor. =700 1\$aZhang, Tong,$eauthor. =700 1\$aLi, Jian,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200043.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200055 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200055$2doi =037 \\$aMPC20200055$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP884.A3 =082 04$a666.893$223 =100 1\$aNasr, Gamal,$eauthor. =245 10$aDynamic Mechanical and Dielectric Properties of Fly Ash/(Polystyrene/Low-Density Polyethylene) Composites /$cGamal Nasr, Taqwa Mohamed, Rania Khalil. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aBy using the melt mixing method, polystyrene (PS), low-density polyethylene (LDPE), and a PS/LDPE blend have been prepared. Fly ash was used as filler embedded in the PS/LDPE blend to form composites. The dynamic mechanical analysis (DMA) showed that the storage modulus ( E′ ) decreases as the temperature increases. E′ increases clearly with fly ash loading, and the maximum E′ value was found for the composite loaded with 30 % fly ash content. The mean-field theory developed by Kerner was used to predict the dynamic mechanical properties of the composites from their pure components. A good agreement was investigated between the deduced theoretical values via iteration method and the experimental results. The dielectric constant ( ε′ ), dielectric loss, and dielectric loss tangent (tan Δ ) have been measured at different constant frequencies. The ε′ and tan Δ commence to decrease by increasing the applied frequency. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aFly ash. =700 1\$aMohamed, Taqwa,$eauthor. =700 1\$aKhalil, Rania,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200055.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200056 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200056$2doi =037 \\$aMPC20200056$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a668$223 =100 1\$aRane, Ajay Vasudeo,$eauthor. =245 10$aUltraviolet–Visible Spectroscopy: A Qualitative Tool to Predict Dispersion and Interphase Characteristics in Carbon-Based Particulate Filled Poly (Lactic Acid) Composites /$cAjay Vasudeo Rane, Krishnan Kanny, Merlin Biju, Sudhikuttan Akkattil Sudhakaran, Ammu Aravind, Sabu Thomas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aProperties of polymer composites depend to a large extent on the characteristics of dispersion and interphase layers. In this work, poly (lactic acid) composites (PLAC) were prepared via the dissolution–dispersion method (DD) and oligomeric–dispersion method (OD) Ultraviolet–Visible spectroscopy (UV–VIS) was used to determine the dispersion and interphase characteristics within the PLAC. An increase in absorbance at a higher wavelength within the absorbance spectra was observed for PLAC prepared by DD and OD, which can be attributed to the formation of strong adlayers as well as “near to homogenous dispersion” for carbon-based particulate filled composites. An increase in absorbance was observed for PLAC prepared by OD in comparison to DD and can be attributed to modifications occurring at interphase regions. PLAC using carbon black, multiwalled carbon nanotubes in poly (lactic acid) were prepared via DD and OD and further characterized by UV–VIS. To study the “hybrid effect,” composites with 2.5 weight percent of carbon black with varied concentration of multiwalled carbon nanotubes and nanocellulose fibers were prepared via DD and OD, further characterized for UV–VIS. This manuscript portrays the role of UV–VIS to determine dispersion as well as the interphase characteristics for poly (lactic acid) filled carbon composites. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aPolymeric composites. =700 1\$aKanny, Krishnan,$eauthor. =700 1\$aBiju, Merlin,$eauthor. =700 1\$aSudhakaran, Sudhikuttan Akkattil,$eauthor. =700 1\$aAravind, Ammu,$eauthor. =700 1\$aThomas, Sabu,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200056.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200074 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200074$2doi =037 \\$aMPC20200074$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.22 =082 04$a620.1/1233$223 =100 1\$aAhammed, Syed Riyaz,$eauthor. =245 10$aDirect Ink Writing Method for Manufacturing Electronic Circuits Using Multiwalled Carbon Nanotubes and Polyvinyl Alcohol Composites /$cSyed Riyaz Ahammed, Ayyappan Susila Praveen. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aUsage of conductive materials for manufacturing electronic circuits using 3D printing methods plays a prominent role in sensing applications and has achieved significant growth in recent years. This growth has led to the development of stretchable, flexible electronics and wearable electronics that are useful as sensing applications in the fields of real-time health monitoring systems. In this paper, a multiwalled carbon nanotube (MWCNT)-based electronic circuit was developed using the 3D printing technique called direct ink writing (DIW) Polyvinyl alcohol (PVA) was used as the binder material to make the MWCNT ink for printing. Different concentrations of MWCNT ink were prepared using 5, 10, and 15 wt. % PVA solutions. The viscosity of MWCNT inks was measured using a rheometer (cone and plate type) The ink exhibited shear thinning behavior, which is suitable for DIW. Finally, the printing of a designed electronic circuit was carried out using a pneumatic extrusion–based 3D printer. The strain sensor circuit—measuring 20 mm long, 9.2 mm wide, and 0.8 mm thick—is manufactured by the 3D printer. Electrical resistivity of strain sensor circuit is evaluated by adopting a two-probe method; the observed resistivity value was 1.7×10 -2 Ωm for MWCNT ink made with 10 wt. % PVA solution and 1.97×10 -2 Ωm for MWCNT ink made with 15 wt. % PVA solution. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aCarbon nanotubes. =700 1\$aPraveen, Ayyappan Susila,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200074.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200081 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200081$2doi =037 \\$aMPC20200081$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA690 =082 04$a624.1826$223 =100 1\$aGuo, Guannan,$eauthor. =245 10$aModeling the Yield Strength of an A356 Aluminum Alloy during the Aging Process /$cGuannan Guo, Qigui Wang, Yiming Rong, Richard D. Sisson. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe wide applications and continuously developing manufacturing methods of heat-treatable aluminum alloys require accurate and efficient precipitate hardening models to predict the microstructure behaviors response to the aging process. The current article proposed a modified precipitate hardening model of A356 aluminum alloy used for engine block. In terms of the microstructure parameters of β” as the primary strengthening phase, the relative volume fraction is studied and modified because of the phase transformation in aging process. The proposed model successfully predicts the yield strength at underaged aging process in the temperature range of 150°C∼170°C after considering the impact of coexist precipitate phases such as β‘ phase. After the modification, the deviation between the yield strengths at low temperature and high temperature was greatly eliminated. This successful modification draws attention to the precipitate phase volume fraction in the research of the precipitate hardening model. The composition of the precipitate phase and interactive transformation when altering the aging process parameters has a significant impact on the yield strength behaviors in the aging process. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aAluminum alloys. =700 1\$aWang, Qigui,$eauthor. =700 1\$aRong, Yiming,$eauthor. =700 1\$aSisson, Richard D.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200081.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200093 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200093$2doi =037 \\$aMPC20200093$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.S7 =082 04$a668.4233$223 =100 1\$aTsagli, K.,$eauthor. =245 10$aTemperature Dependence of Photoluminescence Spectra in Polystyrene /$cK. Tsagli, S. V. Dordevic. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aOur previous study of low-temperature photoluminescence (PL) in several common polymers revealed that PL intensity is, to different degree, temperature dependent in all of them. Even though polystyrene (PS) showed only moderate temperature dependence, it was the only studied polymer in which the wavelength, and therefore the energy, of the PL peak changed with temperature. In this work, we explored that effect in more detail and found that it is not present in all samples. Therefore, the effect is not intrinsic to PS, and we hypothesize that it is due to impurities. Moreover, our analysis revealed that the shift of the peak is due to a second PL peak, which displays a very strong temperature dependence. These PL results are also supplemented with UV-vis measurements on the same samples. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aPolystyrene. =700 1\$aDordevic, S. V.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200093.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200094 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200094$2doi =037 \\$aMPC20200094$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA690 =082 04$a624.1826$223 =100 1\$aRobinson, J. S.,$eauthor. =245 10$aReduction in Residual Stress during Plastic Deformation of the Aluminum Alloy 7449 /$cJ. S. Robinson, T. Pirling, C. E. Truman. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aRectilinear blocks of the very high-strength aerospace aluminum alloy 7449 were solution treated and cold water quenched. They were then stress relieved immediately by cold compression. The amount of cold compression was systematically varied from 0 to 0.3 %. The amount of plastic strain was limited to well below the industrial standard of ~2 %. The blocks then received a stabilizing aging treatment. The residual stress distribution remaining in the blocks was characterized using neutron diffraction, with the aim of tracking how the through thickness 3-D residual strains and stresses change as cold compression progresses. Stress relief was of the order of 30–50 %, but there was no discernible systematic increase in stress relief as the plastic deformation magnitude was increased. It is suggested that this is mainly due to the differences between the samples being less than the experimental uncertainty of the neutron diffraction strain measurement technique. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aAluminum alloys. =700 1\$aPirling, T.,$eauthor. =700 1\$aTruman, C. E.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200094.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200095 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200095$2doi =037 \\$aMPC20200095$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.B55 =082 04$a620.192323$223 =100 1\$aNithya Priya, C.,$eauthor. =245 10$aStudies on Pectin-Polyvinyl Alcohol–Based Biodegradable Polymer Blend Electrolytes /$cC. Nithya Priya, R. Muruganandham, M. Muthuvinayagam, M. Vahini. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aBiodegradable polymer blend electrolytes based on Pectin–polyvinyl alcohol (PVA) with a constant amount of sodium nitrate (NaNO 3 ) salt are prepared by using a solution casting technique. The complexation between polymers and salt is confirmed by Fourier transform infrared spectroscopy, and the AC impedance technique is implied to analyze the ionic conductivity of the prepared samples. When synthetic polymer PVA is added with pectin, the ionic conductivity increases. Pectin: PVA:NaNO 3 [00.100.04] blend polymer electrolyte shows the higher ionic conductivity of 4.3×10 -6 (S/cm) at room temperature. Further, the dielectric constant and dielectric loss of the polymer electrolytes are also analyzed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aPolymeric composites. =650 \0$aBiodegradable plastics. =700 1\$aMuruganandham, R.,$eauthor. =700 1\$aMuthuvinayagam, M.,$eauthor. =700 1\$aVahini, M.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200095.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200126 =003 IN-ChSCO =005 20210504061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210504s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200126$2doi =037 \\$aMPC20200126$bASTM =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC585.8.E4 =082 04$a547.84$223 =100 1\$aSaxena, Pooja,$eauthor. =245 10$aA Review of Polymer Electrets and Their Applications /$cPooja Saxena, Prashant Shukla. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis research focuses primarily on the uses of polymer electrets as an important class of organic materials finding their use in a variety of electronic and electrical engineering industries and ranging from photovoltaic cells to transducers, dosimeters, and other applications. This paper provides a broad summary about types of electrets and their mechanisms along with better knowledge of the electrical properties and detailed mechanisms involved in the buildup, transport, and storage of charges in organic polar polymers electrets. This work also aims to investigate the conditions favorable for obtaining long-lived electrets. This article highlights early research conducted in the field of electrets and reviews the current trends and applications of electrets in devices. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25. =588 \\$aDescription based on publisher's website, viewed May 04, 2021. =650 \0$aPolymers. =650 \0$aElectrets. =700 1\$aShukla, Prashant,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aASTM International. =773 0\$tMaterials Performance and Characterization.$gVolume 9, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2020$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200126.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200138 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200138$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200138$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA459 =082 04$a669$223 =100 1\$aUmezawa, Osamu,$eauthor. =245 10$aReview of the Mechanical Properties of High-Strength Alloys at Cryogenic Temperatures /$cOsamu Umezawa. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTo advance the understanding of metallic materials for structural components at cryogenic temperatures, a review of previous studies on the mechanical properties of austenitic stainless steels, titanium alloys, aluminum alloys, and copper alloys is presented herein. In particular, the evaluation of strength and toughness balance intends to clarify key differences between these alloys to facilitate better alloy design and potentially bolster further alloy development. Several key points on cryogenic mechanical tests are also introduced. Temperature control, testing tools, and test conditions should be properly calibrated to avoid experimental errors. Furthermore, substantial progress for subsurface crack initiation in high-cycle fatigue at cryogenic temperatures is presented, in which the mechanism of subsurface crack generation is highlighted as a key design consideration in microstructure of high-strength alloys. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aAlloys. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200138.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200193 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200193$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200193$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669.96142$223 =100 1\$aAnoop, C. R.,$eauthor. =245 10$aA Review on Steels for Cryogenic Applications /$cC. R. Anoop, R. K. Singh, Ravi Ranjan Kumar, M. Jayalakshmi, T. Antony Prabhu, K. Thomas Tharian, S. V. S. Narayana Murty. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (73 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCryogenic systems have played a crucial role in almost all of the finest technological achievements of mankind. Cryogenic applications demand materials with a unique combination of properties, which drastically limits the choice of materials. In most other engineering applications, because of wide tailorability of their properties and excellent combination of strength and toughness, coupled with lower cost compared with nonferrous materials, steels have become the preferred/dominant structural material for cryogenic applications. The contradictory requirement of higher strength without compromising toughness at cryogenic temperatures posed considerable challenges and led to the development of large array of steels tailored for specific applications. This review is an attempt to survey the metallurgical aspects, material selection, mechanical property evaluation, and application of various standard and nonstandard steels for cryogenic applications. This review covers the influence of low temperatures on material properties, simulative mechanical tests for property evaluation, metallurgy of steels, and application examples surveying the published literature to date. The review also analyzes the origins of low-temperature toughness, various application requirements, and the work carried out at authors‘ laboratories. The issues pertaining to mechanical tests at low temperatures and status of data generation in international scenario have been critically analyzed. Physical metallurgy aspects have been highlighted in the review, and microstructure-property-processing correlations for various steels have also been covered. One of the recent advances in steels for cryogenic applications, high-entropy alloys, which are proposed as alternatives for the conventional steels, have been reviewed, and mechanical property data have been critically analyzed. The potential of additive manufactured steels for low-temperature applications has been reviewed. Finally, this review article discusses challenges in processing–mechanical properties correlation for various grades of steels for cryogenic applications. It also provides useful information for researchers working on steels for cryogenic applications with a glimpse of recent advances made in this area. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aSteel. =700 1\$aSingh, R. K.,$eauthor. =700 1\$aKumar, Ravi Ranjan,$eauthor. =700 1\$aJayalakshmi, M.,$eauthor. =700 1\$aAntony Prabhu, T.,$eauthor. =700 1\$aThomas Tharian, K.,$eauthor. =700 1\$aNarayana Murty, S. V. S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200193.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200133 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200133$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200133$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.7.H55 =082 04$a620.11217$223 =100 1\$aSonber, J. K.,$eauthor. =245 10$aProcessing of ZrB2- and HfB2-Based Ultra-High Temperature Ceramic Materials: A Review /$cJ. K. Sonber, T. S. R. Ch. Murthy, Sanjib Majumdar, Vivekanand Kain. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (33 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aZrB 2 and HfB 2 are leading materials in the category of ultra-high temperature ceramics (UHTCs). UHTCs are a group of ceramic materials that can withstand ultra-high temperature (>2,000°C) in oxidizing conditions. Such a high temperature will be encountered by future hypersonic reentry vehicles. Future reentry vehicles will have sharp edges to improve aerodynamic performance. The sharp leading edges will cause higher surface temperature than that of the actual blunt-edged vehicles. The sharp edges have less surface area to dissipate heat and thus the temperature gets increased. To withstand the intense heat generated when these vehicles reenter the earth‘s upper atmosphere, UHTC materials are needed. UHTC materials are composed of borides of early transition metals. From the larger list of borides, ZrB2 and HfB2 have received the most attention as potential candidates for leading edge materials because their oxidation resistance is superior to that of other borides because of the stability of the ZrO2 and HfO2 scales that form on these materials at elevated temperatures in oxidizing environments. Processing of these materials is very difficult because these materials are very refractory in nature. Powder synthesis usually involves high-temperature solid state reactions. Dense bodies are generally produced by hot pressing and spark plasma sintering. For coating preparation, plasma spray, chemical vapor deposition, and physical vapor deposition is used. All these processing methods for ZrB 2 and HfB 2 are difficult because of the involvement of very high temperatures. In this review, the present state of the knowledge on processes employed for powder synthesis, fabrication of dense bodies, and coating processes is discussed. The advantages, limitations, and challenges in the different processing methods are addressed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aMaterials at high temperatures. =700 1\$aMurthy, T. S. R. Ch.,$eauthor. =700 1\$aMajumdar, Sanjib,$eauthor. =700 1\$aKain, Vivekanand,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200133.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200183 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200183$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200183$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA459 =082 04$a669$223 =100 1\$aPerepezko, J. H.,$eauthor. =245 10$aMo-Silicide Alloys for High-Temperature Structural Applications /$cJ. H. Perepezko, M. Krüger, M. Heilmaier. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe challenges of a high-temperature environment ( T >1,400°C) impose severe material performance constraints in terms of melting point, oxidation resistance, and structural functionality. A number of ceramic materials, intermetallic compounds, and refractory metals with high melting temperatures are available as material choices. However, in a single-component single-phase form, these materials do not satisfy all the aforementioned requirements. One clear message from the evolutionary development of high-temperature alloys is the importance of developing multicomponent alloys with multiphase microstructures and the capability to control phase fractions and morphologies to satisfy a number of mechanical property requirements. Besides the essential structural requirements, elevated temperatures often also involve aggressive environments that require a material to display an inherent oxidation protection that can be further enhanced by coating. Among the leading candidates to advance beyond the capability of the current nickel (Ni)-base superalloys, the multiphase microstructures that can be developed in the molybdenum-silicon-boron (Mo-Si-B) system involving a high melting temperature (>2,100°C) ternary-based intermetallic Mo 5 SiB 2 (T 2 ) offer an attractive performance. Most of the attention has been on three-phase alloys comprised of Mo(ss), T 2 , and Mo 3 Si that offer high-temperature stability and robust microstructures, but new alloy designs are in development. In this review the recent advances in the development of Mo-silicide alloys are discussed in terms of alloy design, microstructure control, structural performance, environmental resistance, and component analysis. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aAlloys. =700 1\$aKrüger, M.,$eauthor. =700 1\$aHeilmaier, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200183.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200178 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200178$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200178$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.7.H55 =082 04$a620.11217$223 =100 1\$aKulkarni, Anand,$eauthor. =245 10$aAdvanced Materials and Manufacturing Technology Developments for Extreme Environment Gas Turbine Applications /$cAnand Kulkarni, Allister James, Ahmed Kamel. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aElectrical power generation is becoming increasingly reliant on gas turbines with multiple fuel capability, with research advances focusing on increased efficiency/power output and reduced emissions. Increasing gas turbine efficiency primarily requires higher operating temperatures and reduced coolant flow in the turbine flow path, which makes it challenging to increase component performance, as these will encounter high stresses and large temperature gradients. Current nickel-based alloys, which operate at operate at extreme environments, are exposed to stress caused by temperature or static/dynamic loading like creep and fatigue, oxidation and corrosion, wear, and damage due to vibrations. Higher turbine inlet temperatures are currently managed with internal/film cooling and thermal/environmental barrier coatings for hot section parts. Comprehensive solutions are needed to translate to achieve ultrahigh efficiencies, lower parts cost, reduced scrape rate, and life cycle savings. The paper discusses material developments coupled with innovative manufacturing approaches to be married with advanced design strategies to realize the needed improvements for hot gas path components. The case studies for combustion and turbine components will be presented to demonstrate the structure property relationships and improved component performance at lower cost. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aMaterials at high temperatures. =700 1\$aJames, Allister,$eauthor. =700 1\$aKamel, Ahmed,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200178.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200167 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200167$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200167$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA485 =082 04$a620.163$223 =100 1\$aMukherjee, Shreya,$eauthor. =245 10$aCreep-Fatigue Behavior of a Newly Developed Ultra-Supercritical Steam Turbine Grade Nickel-Based Superalloy, HAYNES 282 /$cShreya Mukherjee, Kaustav Barat, Soumitra Tarafder, S. Sivaprasad, Sujoy Kumar Kar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMost engineering components used in gas/steam turbines are exposed to a range of complex loading conditions resulting from startup and shutdown procedures. These loading conditions involve superimposition of time-dependent creep on cyclic fatigue and can be simulated by properly designed high-temperature creep-fatigue tests. Creep-fatigue interaction is a function of duration and position of dwell in the loading waveform, and the material microstructure. The objective of this work is to investigate the creep-fatigue interaction response of a newly developed γ′-strengthened wrought nickel-based superalloy (HAYNES 282), which has a potential application in advanced ultra-supercritical steam turbines. Creep-fatigue tests are conducted at 760°C with strain dwell either at tensile peak or compressive peak or at both tensile and compressive peak positions for different dwell times of 100 and 1,000 s. The test results are analyzed with respect to evolutions of peak stress, stress amplitude, stress relaxation, hysteresis loop, inelastic strain energy density, and degree of softening. Degree of softening is found to increase with dwell position at tensile, compressive, and both peaks in that order. Tests with dwell at both tensile and compressive peak positions are found to be the most damaging, showing the least life. Between tensile dwell and compressive dwell tests, interestingly, those with compressive dwell show a significantly reduced life. Increasing dwell time aggravates the damaging effect manifold. The mechanism of fracture at the end of life is illustrated with fractographic characterization. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aMetals$xCreep. =700 1\$aBarat, Kaustav,$eauthor. =700 1\$aTarafder, Soumitra,$eauthor. =700 1\$aSivaprasad, S.,$eauthor. =700 1\$aKar, Sujoy Kumar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200167.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200146 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200146$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200146$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA459 =082 04$a669$223 =100 1\$aPatel, Vivek,$eauthor. =245 10$aPrediction of Long-Term Creep Properties of Zirconium-2.5 % Niobium Alloy Using Wilshire Method /$cVivek Patel, R. N. Singh, Madangopal Krishnan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aZirconium-2.5 % niobium alloy, used as a pressure tube material in pressurized heavy water reactors, have to experience extreme stress, temperature, and radioactive conditions to serve within the designed dimensional tolerance limit. Prolonged duration under high stress and high temperature causes the creep deformation, ultimately leading to deformation beyond the permitted limit or interference with other components, or both. Hence, a priori using particular material for a specific application, mechanical testing has to be done to investigate its deformation behavior. However, creep tests of material can last from a few hours to several months or even years. The cost of testing the material can eventually impact the cost of the component. Instead of carrying out long-term creep tests, an extrapolation technique named the Wilshire method is applied to predict the creep behavior of the material under any given test conditions. This method is also capable of reconstructing the complete creep curve using the data from accelerated creep tests. Such an approach can drastically scale down the cost and time required for the long-term creep tests. In the present study, zirconium 2.5 % niobium alloy, which is used as pressure tube material in pressurized heavy water reactors, is employed as a test material for the analysis using the Wilshire method. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aAlloys. =700 1\$aSingh, R. N.,$eauthor. =700 1\$aKrishnan, Madangopal,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200146.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200157 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200157$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200157$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.T5 =082 04$a620.189322$223 =100 1\$aThammaiah, B. R.,$eauthor. =245 10$aHigh Strain Rate Behavior of GTM-900 Titanium Alloy /$cB. R. Thammaiah, Chandru D. Fernando, Anuradha Nayak Majila, A. R. Anilchandra, M. S. Nandana, Udaya K. Bhat, C. M. Manjunatha. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aGTM-900 is an α+β alloy of titanium used in low-pressure (LP) compressor blades of gas turbine (GT) engines. The maximum allowable operating temperature of this alloy is 500°C. Silicon is added to enhance the creep resistance at elevated temperatures. The aim of this work is to establish the microstructural stability of this alloy and determine the high strain rate Johnson-Cook (J-C) material parameters such as A , B , and n . The material parameters are subsequently used by designers to simulate the “blade-off” and “casing containment” capability of the LP compressor blade. Split Hopkinson tensile bar was used to conduct high strain rate tests at about 2,000 s -1 , and at three different temperatures, viz., 25°C, 300°C, and 500°C, to simulate critical conditions. Data obtained from these testing were used to construct a J-C model. Flow stress increased with an increase in strain rate and decreased with an increase in temperature because of thermal softening. Characterization, using optical and electron microscopes, indicated that the microstructure was stable even after the deformation at 500°C. The presence of needle-like silicide phase was observed under transmission electron microscopy and the composition was verified with X-ray diffraction results. A high strain hardening rate was observed even at elevated temperatures in this alloy ( n ≈ 0.54 at 2,000 s -1 and 500°C) compared to Ti-6Al-4V titanium alloy ( n ≈ 0.28). Considering good strength and microstructural stability up to 500°C, the present material offers to be an attractive alternate to other contemporary titanium alloys currently used in GT engine applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aTitanium alloys. =700 1\$aFernando, Chandru D.,$eauthor. =700 1\$aMajila, Anuradha Nayak,$eauthor. =700 1\$aAnilchandra, A. R.,$eauthor. =700 1\$aNandana, M. S.,$eauthor. =700 1\$aBhat, Udaya K.,$eauthor. =700 1\$aManjunatha, C. M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200157.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200131 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200131$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200131$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.19204296$223 =100 1\$aHarrison, Shay,$eauthor. =245 10$aHigh-Temperature Performance of Next-Generation Silicon Carbide Fibers for CMCs /$cShay Harrison, John Schneiter, Joseph Pegna, Erik Vaaler, Ramkiran Goduguchinta, Kirk Williams. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSingle-fiber (monofilament, not twisted tow) high-temperature creep performance of refractory ceramic compositions is a fundamental material property that must be examined and understood for the successful deployment of ceramic matrix composite material systems in demanding applications. A novel creep testing approach was devised utilizing an innovative approach to fiber sample attachment and used to evaluate the creep behavior of Free Form Fibers‘ LP-30SC and Nippon Carbon-based Hi-Nicalon Type S (HNS) silicon carbide fiber products. The testing apparatus, analytical basis for the creep calculations, including the sample gage length, and collected data are presented. Test conditions include a range of peak hold temperatures, from 1,300°C to 1,500°C, gas environments, and hold time patterns at the peak temperature. Clear differences in resistance to creep degradation were evident between the LP-30SC and HNS fibers, as the LP-30SC demonstrated strong resiliency to high temperature exposure while the HNS showed performance degradation consistent with oxidation attack. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aComposite materials. =700 1\$aSchneiter, John,$eauthor. =700 1\$aPegna, Joseph,$eauthor. =700 1\$aVaaler, Erik,$eauthor. =700 1\$aGoduguchinta, Ramkiran,$eauthor. =700 1\$aWilliams, Kirk,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200131.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200145 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200145$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200145$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.7.H55 =082 04$a620.11217$223 =100 1\$aVetrivendan, E.,$eauthor. =245 10$aDevelopment of Silicon Carbide Interlayers for Plasma Spray Yttria Topcoat on Graphite for High-Temperature Applications /$cE. Vetrivendan, B. Madhura, Ch. Jagadeeswara Rao, S. Ningshen, U. Kamachi Mudali. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPlasma-sprayed yttria (Y 2 O 3 ) coatings on commercial high-density graphite (HDG) as a chemical barrier coating are presently being explored for uranium-zirconium alloy melting crucibles in pyrochemical reprocessing of spent metallic fuel of future fast breeder reactors. The performance and durability of Y 2 O 3 coatings for high-temperature exposure up to 1,823 K for multiple batch operations are critical to reducing solid active waste generation. However, plasma-sprayed Y 2 O 3 coatings on HDG experience large thermal mismatch stresses due to the difference in the coefficient of thermal expansion (CTE) value of ∼8×10 -6 K -1 for Y 2 O 3 and ∼4×10 -6 K -1 for HDG, combined with partial active oxidation of HDG interface leading to premature cracking and spallation of the coating. Silicon carbide (SiC) coating with intermediate CTE (∼6×10 -6 K -1 ) offers superior oxidation protection for HDG, which can suitably be used as an interlayer to improve the durability of Y 2 O 3 coatings. In the present work, SiC interlayer coating is developed on HDG substrates using conventional coating techniques such as pack cementation and chemical vapor deposition techniques for subsequent deposition of Y 2 O 3 topcoat by plasma spraying. The thermal fatigue studies simulating uranium melting condition by isothermal hold at 1,723, 1,773, and 1,823 K for 1 h showed twofold improvements in the life of Y 2 O 3 coatings with SiC interlayer. The evolution of thermal cycling damage and failure mechanisms are discussed. The role of interfacial microstructure, the stability of phases, and the underlying mechanisms for life enhancement in the presence of SiC interlayer for plasma-sprayed Y 2 O 3 coating for high-temperature applications are highlighted. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aMaterials at high temperatures. =700 1\$aMadhura, B.,$eauthor. =700 1\$aJagadeeswara Rao, Ch.,$eauthor. =700 1\$aNingshen, S.,$eauthor. =700 1\$aKamachi Mudali, U.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200145.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200171 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200171$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200171$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.7.H55 =082 04$a620.11217$223 =100 1\$aSreejith, K. J.,$eauthor. =245 10$aPreparation of Titanium-Aluminum-Carbon MAX Phase via a Simple Precursor Route for High-Temperature Coating Applications /$cK. J. Sreejith, Vipin Vijay, T. Jayalatha. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMAX phase materials are gaining increased research interest because of the unique combination of metallic and ceramic properties. For high-temperature applications, titanium-aluminum-carbon (MAX) phases are extensively investigated. In order to utilize these MAX phase materials as coatings for high-temperature space applications, a pressureless preparation route employing a polymer-based precursor would be advantageous. A cost-effective, pressureless synthetic route using a carbonaceous polymer-based slurry was explored to obtain titanium-alumnium-carbon MAX phase. In continuation of our earlier report on the preliminary investigations on a precursor system, in the present study, an investigation on the effect of (i) heat treatment duration and (ii) nucleating filler on the formation of titanium-aluminum-carbon MAX phase from the precursor was carried out. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aMaterials at high temperatures. =700 1\$aVijay, Vipin,$eauthor. =700 1\$aJayalatha, T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200171.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200161 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200161$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200161$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.7.H55 =082 04$a620.11217$223 =100 1\$aKumar, Shobhit,$eauthor. =245 10$aDevelopment of C/SiC Fasteners for High-Temperature Applications /$cShobhit Kumar, Anil Painuly, Anurag Kamal, Sajimon Kuttappan, Ravi Ranjan Kumar, Shyin Palani Prabhakaran, Renjith Devasia. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aContinuous carbon fiber reinforced silicon carbide (C/SiC) ceramic matrix composites are the candidate materials for high-temperature structural applications owing to their high specific strength, low coefficient of thermal expansion, and moderate thermal conductivity. C/SiC based fasteners provide reliability with oxidation resistance up to 1,650°C for joining such C/SiC structural components used in reusable launch vehicles for space applications. The present study describes the methodology to realize C/SiC based M8 fasteners by isothermal-isobaric chemical vapor infiltration process using 2D-stitched carbon fabric preforms. The realized fasteners exhibited a density of 2.10 g/cm 3 , a tensile strength of 191±3 MPa, a shear strength of 230±69 MPa in non-threaded and 150±86 MPa in threaded regions of shank at room temperature, a high-temperature tensile strength of 170±12 MPa, and a tensile modulus of 70±8 GPa at 1,100°C in the atmospheric conditions. The tensile failure of the C/SiC bolts was observed to depend upon the relative dimensions of fillet radius and thread root radius, wherein a small fillet radius was observed to be detrimental, as it resulted in failure at the head-shank interface of the bolts. The scanning electron microscope images of tensile tested C/SiC bolts indicate extensive fiber pullout, characteristic of quasi-ductile failure of bolts. It is clearly evident from the studies that the C/SiC fasteners are a promising alternative over the currently used molybdenum alloy fasteners. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aMaterials at high temperatures. =700 1\$aPainuly, Anil,$eauthor. =700 1\$aKamal, Anurag,$eauthor. =700 1\$aKuttappan, Sajimon,$eauthor. =700 1\$aKumar, Ravi Ranjan,$eauthor. =700 1\$aPrabhakaran, Shyin Palani,$eauthor. =700 1\$aDevasia, Renjith,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200161.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200166 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200166$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200166$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a671.52$223 =100 1\$aRajendran, Anbukkarasi,$eauthor. =245 10$aEffect of Axial Load-Dependent Deformation Rate on the Grain Size Distribution and Mechanical Properties of Friction Stir Processed Copper /$cAnbukkarasi Rajendran, Naresh Nadammal, Kuldeep Singh, Satish V. Kailas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDuring friction stir processing (FSP), the combination of rotation and movement of the tool leads to frictional heat generation and plastic deformation at the tool-material contact surface, leading to a microstructurally refined formation region. The deformation rate in the material can be altered by varying the axial load by increasing or decreasing the tool‘s plunging depth. In the present study, FSP was carried out on a pure copper plate of 3-mm thickness by varying the plunge depth from 2.3 to 2.6 mm for a tool pin length of 2.4 mm. The microstructure of the processed samples was studied by optical microscopy, and the grain size was measured by the linear intercept method. Tensile testing was carried out perpendicular to the processing direction. The grain size distribution was narrower at low axial loads and wider at the higher axial loads, measured between 1 and 120 µm. At higher axial loads, microstructure consisted of bands indicative of the heterogeneity in the deformation. The formation of bands at higher axial loads leads to improved mechanical properties. The ductility of the processed materials at higher axial loads was 16%, which was four times the increase observed at lower axial loads (4%). The formation of a bi-modal microstructure (alternating layers of fine and coarse grains) at high axial load enhanced the processed materials‘ strength and ductility. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aFriction welding. =700 1\$aNadammal, Naresh,$eauthor. =700 1\$aSingh, Kuldeep,$eauthor. =700 1\$aKailas, Satish V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200166.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200125 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200125$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200125$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.I7 =082 04$a669.96142$223 =100 1\$aNagai, Kotobu,$eauthor. =245 10$aEvaluation of Fire Resistance for a Recycled 0.15 mass% Carbon Steel /$cKotobu Nagai, Satoru Terayama. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA recycled steel with 0.2 % offset stress higher than 295 MPa was verified as a candidate for fire-resistant use, based on an academic standard in Japan. The chemical compositions were 0.15 mass% carbon-0.02 mass% silicon-0.5% mass% manganese and unavoidable alloy elements. The amount of elements inevitably contained in recycling was kept within the regulation, and then the dispersion of tensile properties among hot coils was controlled to be sufficiently small. The recycled steel satisfied the requirements by the academic standard in terms of tensile properties at elevated temperatures. No significant evolution was observed in the ferrite-based microstructure within the temperature and time range tested. The plastic deformation is apparently a strain-controlled one up to 400°C and a strain rate-controlled one at 600°C and 700°C. At 500°C, it is in the middle of the two. In the adopted test method, a constant strain rate was realized over the entire strain range except for the beginning stage of deformation. A peak strain rate occurs at about 0.2 % strain, which brings about the uncertainty in determination of 0.2 % offset stress at elevated temperatures. However, the constant strain rate requirement is satisfied in the determination of 1 % offset stress that the academic standard specifies. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aSteel. =700 1\$aTerayama, Satoru,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200125.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200083 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200083$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200083$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.T5 =082 04$a620.189322$223 =100 1\$aSonar, Tushar,$eauthor. =245 10$aInfluence of InterPulsed TIG Welding Parameters on the Evolution of Microstructure and Tensile Properties of Su-718 Alloy Sheets /$cTushar Sonar, Visvalingam Balasubramanian, Sudersanan Malarvizhi, Thiruvenkatam Venkateswaran, Dhenuvakonda Sivakumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (31 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSuperalloy 718 (Su-718) is a high-performance nickel-based alloy typically employed in high-temperature applications of aero-engine components. It is mostly joined by the Tungsten Inert Gas (TIG) welding process for clean and precise joints. However, the joints are more prone to premature failure owing to the metallurgical problems during solidification, such as constitutional segregation in the fusion zone (FZ) and microfissuring in the heat affected zone (HAZ). To overcome these problems, in this investigation, a recently emerged InterPulsed TIG (IP-TIG) welding process was utilized for joining Su-718 alloy. It is the advanced variant of the TIG welding process principally differentiated by electromagnetic condensation of the arc and high-frequency pulsation up to 20 kHz. The primary objective of this study is to make the potential use of electromagnetic condensation of the arc and pulsation for minimizing the Laves phase growth in FZ and enhancing the tensile strength of joints. To achieve this, the effect of IP-TIG welding parameters on evolution of the microstructure and tensile properties of Su-718 alloy joints is investigated and the results are analyzed in detail in this paper. The analysis of microstructural features was done using optical microscopy, scanning electron microscopy, and Energy Dispersive X-ray Spectroscopy techniques. The influence of Laves phase morphology on the strength and elongation of joints is revealed and correlated to the fracture surface. The principal mechanism responsible for changes in microstructural features and consequential influence on tensile behavior of joints is explained briefly and correlated to the cooling rate and heat input conditions during welding. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aTitanium alloys. =700 1\$aBalasubramanian, Visvalingam,$eauthor. =700 1\$aMalarvizhi, Sudersanan,$eauthor. =700 1\$aVenkateswaran, Thiruvenkatam,$eauthor. =700 1\$aSivakumar, Dhenuvakonda,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200083.htm =LDR 03762nab 2200553 i 4500 =001 MPC20200172 =003 IN-ChSCO =005 20210722061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 210722s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200172$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200172$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.P5 =082 04$a620.19236$223 =100 1\$aEdachery, Vimal,$eauthor. =245 10$aEnhancing Tribological Properties of Inconel X-750 Superalloy through Surface Topography Modification by Shot Blasting /$cVimal Edachery, Aashish John, Anbukkarasi Rajendran, Vivek Srinivasappa, Sribalaji Mathiyalagan, Santosh Kumar, Satish Vasu Kailas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe profound usage of Inconel X-750 in structural and high-pressure conditions mandates improved tribological properties. One of the methods to achieve this is through surface topography modifications. In this work, the viability of the shot blasting technique is explored to enhance the wear resistance of Inconel X-750. For this purpose, aluminum oxide particles with 80 mesh size were shot blasted on the superalloy surface at a constant pressure of 0.6 MPa. The 3D surface topography of Inconel X-750 alloy confirms substantial surface deformation and increased surface roughness after shot blasting. Furthermore, the surface characteristics of shot-blasted superalloy were meticulously examined using a string of techniques: optical profilometer, scanning electron microscope, and electron probe microanalysis. The tribological properties of Inconel X-750 before and after shot blasting were examined using a reciprocating tribometer with a ball-on-flat configuration. Results showed that shot blasting the superalloy has tremendously enhanced the wear resistance by ∼78%, which could be attributed to the reduced sliding contact area, enhanced surface hardness, and the hindrance in the transition of wear mechanism from abrasion tribo-oxidation to adhesion. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25 =588 \\$aDescription based on publisher's website, viewed July 22, 2021. =650 \0$aTribology. =700 1\$aJohn, Aashish,$eauthor. =700 1\$aRajendran, Anbukkarasi,$eauthor. =700 1\$aSrinivasappa, Vivek,$eauthor. =700 1\$aMathiyalagan, Sribalaji,$eauthor. =700 1\$aKumar, Santosh,$eauthor. =700 1\$aKailas, Satish Vasu,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/DIGITAL_LIBRARY/JOURNALS/MPC/PAGES/MPC20200172.htm =LDR 03286nas a2200733 i 4500 =001 MPC1001 =003 IN-ChSCO =005 20220129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220129c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =245 00$aMaterials performance and characterization. =082 04$a620.11$223 =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 10, Issue 1; title from table of contents page (publisher's website, viewed January 29, 2022). =588 \\$aLatest issue consulted: Volume 10, Issue 1 (viewed January 29, 2022). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/journals/volume/listing/coden/MPCACD/issue/1/volume/10/online-issue-date/2021-10-13+00%3A00%3A00 =LDR 03286nas a2200733 i 4500 =001 MPC1002 =003 IN-ChSCO =005 20220129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220129c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =245 00$aMaterials performance and characterization. =082 04$a620.11$223 =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 10, Issue 2; title from table of contents page (publisher's website, viewed January 29, 2022). =588 \\$aLatest issue consulted: Volume 10, Issue 2 (viewed January 29, 2022). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/journals/volume/listing/coden/MPCACD/issue/2/volume/10/online-issue-date/2021-06-24+00%3A00%3A00 =LDR 03286nas a2200733 i 4500 =001 MPC1102 =003 IN-ChSCO =005 20220129061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220129c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =245 00$aMaterials performance and characterization. =082 04$a620.11$223 =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 11, Issue 2; title from table of contents page (publisher's website, viewed January 29, 2022). =588 \\$aLatest issue consulted: Volume 11, Issue 2 (viewed January 29, 2022). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/journals/volume/listing/coden/MPCACD/issue/2/volume/11/online-issue-date/2021-09-20+00%3A00%3A00 =LDR 03762nab 2200553 i 4500 =001 MPC20210045 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210045$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210045$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC176.8.N35 =082 04$a620.1/15$223 =100 1\$aSinha, Brajalal,$eauthor. =245 10$aSonofragmentation Synthesis of Composition-Controlled Iron-Cobalt Nanoparticles with Enhanced Magnetic Properties /$cBrajalal Sinha, Rubayet Tanveer, Palash Kumar Sarker, Md Nazrul Islam. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aNowadays, developing simplistic, low-cost, and environment-friendly ways for the synthesis of nanoparticles (NPs) is very attractive, as reported synthesis processes with use of toxic chemicals are particularly complex. In this report, a facile and one-step approach, i.e., the sonofragmentation method, had been applied for the synthesis of FexCo1−x (x = 0.20, 0.40, and 0.80) NPs with enriched saturation magnetization and coercivity. Morphology and structure of the NPs were observed using a scanning electron microscope (SEM) and X-ray diffraction (XRD) respectively. The energy dispersive spectroscopy analysis was used for the confirmation of elemental composition. The crystalline structure of NPs was confirmed from the XRD patterns, and the crystallite size obtained from the powder XRD peak using the Scherrer equation was approximately 24.5 nm. The accumulation of NPs was observed in SEM analysis. Moreover, the magnetic property was characterized using a vibrating sample magnetometer at room temperature. The saturation magnetization (Ms) value was measured from the magnetization (M)-applied field (H) curve and found to be increased from 107 to 153 emu/g (107 to 153 Am2/kg) and the coercivity (Hc) decreased from 128 to 72 Oe (10.18 to 5.53 kA/m) for increasing the iron content in iron-cobalt NPs. Furthermore, the magnetic properties (i.e., Ms and Hc) of synthesized iron-cobalt NPs were compared with those of other methods of synthesis. The overall findings suggest that the present approach is simple, cost-effective, and environmentally safe for the synthesis of NPs. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMagnetic nanoparticles. =650 \0$aNanostructures$xMagnetic properties. =650 \0$aNanoparticles$xMagnetic properties. =700 1\$aTanveer, Rubayet,$eauthor. =700 1\$aSarker, Palash Kumar,$eauthor. =700 1\$aIslam, Md Nazrul,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210045.html =LDR 03762nab 2200553 i 4500 =001 MPC20210049 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210049$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210049$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a671.52$223 =100 1\$aPrymak, David,$eauthor. =245 10$aA High-Pressure Shear Testing Approach to Measure Flow Stresses Near a Friction Stir Welding Tool /$cDavid Prymak, Michael Miles, Tracy Nelson, Fredrick Michael. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA new approach for measuring flow stresses near a spinning friction stir welding (FSW) tool is evaluated on AA 6061-T6 plate. The test consists of plunging a cylindrical tool with a flat face into the plate at different rotational speeds, using a variety of constant vertical loads. A viscosity-based model of the shear layer created under the tool is employed to estimate local flow stresses. The flow stresses measured by this approach exhibited an inverse relationship with temperature and a positive dependence on the pressure imposed by the spinning flat-faced tool. Compared to hot compression and hot torsion results, estimated flow stress levels in high-pressure shear were lower by 20–68 %, for similar temperatures and strain rates, owing to grain refinement induced by continuous dynamic recrystallization. This high-pressure shear approach could be used to characterize material behavior near a rapidly spinning FSW tool, leading to improved process model predictions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aHigh pressure measurements. =650 \0$aFriction stir welding. =650 \0$aDissimilar welding. =700 1\$aMiles, Michael,$eauthor. =700 1\$aNelson, Tracy,$eauthor. =700 1\$aMichael, Fredrick,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210049.html =LDR 03762nab 2200553 i 4500 =001 MPC20210043 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210043$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210043$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS207.3.C65 =082 04$a671.3$223 =100 1\$aRajesh Kannan, A.,$eauthor. =245 10$aMicrostructure and Mechanical Properties of Dissimilar Aluminum Alloys AA5052-H32 and AA2219-T31 Welded Using Cold Metal Transfer Process /$cA. Rajesh Kannan, S. Mohan Kumar, R. Pramod, N. Siva Shanmugam, Yasam Palguna, M. Vishnukumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aLightweight structures fabricated from dissimilar aluminum alloys in aerospace and marine industries involve a lot of welding. Aluminum alloys AA5052-H32 and AA2219-T31 were successfully welded with the low heat input welding technology, the cold metal transfer (CMT) process. Microstructures indicated the existence of finer equiaxed dendrites and strengthening precipitates in the weld metal (WM). The microliquefaction cracks were discontinuous and propagated along the grain boundaries and with the grains of α-Al matrix in the WM. The tensile properties of the dissimilar welded joint attained a joint efficiency of 70.1 % and fracture ended in ductile nature with dimples and microvoids. The heat affected zone was narrow and noticed a drop in the hardness at both the interfaces caused by a softening phenomenon, ending up with coarse precipitates having lower hardness. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMetals$xCold working. =650 \0$aCold roll forming. =650 \0$aMetals$xExtrusion. =700 1\$aMohan Kumar, S.,$eauthor. =700 1\$aPramod, R.,$eauthor. =700 1\$aSiva Shanmugam, N.,$eauthor. =700 1\$aPalguna, Yasam,$eauthor. =700 1\$aVishnukumar, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210043.html =LDR 03762nab 2200553 i 4500 =001 MPC20200091 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200091$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200091$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.7 =082 04$a621.3$223 =100 1\$aTung, Simon C.,$eauthor. =245 10$aSurface Engineering Development Trends and Impact of Surface Coatings and Textures on Automotive Powertrain Friction and Wear Control /$cSimon C. Tung, Victor Wong. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (31 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe global automotive industry is facing higher energy costs, more legislative pressure, and an ever-increasing environmental awareness to achieve fuel efficiency and environmental sustainability. In recent years the automotive industry has undergone a revolution in hardware and materials. Among these approaches, engine friction reduction and wear control by surface engineering are the most effective approaches. In this paper, surface engineering and its impact of surface coatings and texture technologies on powertrain components will be reviewed. Recently the lightweight nonferrous alloy and nanocomposites are being incorporated into the emerging powertrain technologies—including a wide range of surface coating materials such as thermal sprayed aluminum liners, diamond-like carbon-coated valve train components, and hard nitride piston rings or composite coatings toward energy-efficient and wear-resistant systems. The major section of this paper will discuss the future development trends of engine friction reduction and wear control by surface modification such as friction-reducing and wear-resistant coatings or surface textures in powertrain components. The impact of surface coatings or surface textures on tribological characteristics will be reviewed. Specifically, this review paper will address the impact of these emerging technologies on engine material requirements. The connection between surface engineering and the emerging powertrain technologies will be described. In summary, this paper will review the impact of emerging surface engineering technologies on tribological performance and future trends for advanced powertrain components. In addition, the bench and engine wear and scuffing assessments will be reviewed in terms of wear and scuffing resistance for a variety of surface coatings or textures applied to engine components. This paper also addresses the interactions between powertrain components and surface coatings or textures and their effects on friction, wear, and engine durability. The increasing importance of surface coatings and textures in engine component design and tribological performance will be fully illustrated. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aSurfaces (Technology) ; Coatings. =650 \0$aSurfaces (Physics)$xMathematical models. =650 \0$aSurfaces (Physics) =700 1\$aWong, Victor,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200091.html =LDR 03762nab 2200553 i 4500 =001 MPC20200035 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200035$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200035$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.186$223 =100 1\$aKrishnanunni, S.,$eauthor. =245 10$aInfluence of Retrogression and Reaging Treatment on Intergranular Corrosion Resistance and Exfoliation Corrosion Resistance in AA7010 Aluminum Alloy /$cS. Krishnanunni, R. Ranganatha, V. Anil Kumar, R. K. Gupta, G. Ajithkumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe aluminum alloys with zinc as the primary alloying element (AA7XXX series) exhibit high strength and are widely used as aircraft structural materials. These categories of aluminum alloys in their peak aging condition (T6) are known to be highly susceptible to general as well as stress corrosion cracking (SCC). Retrogression and reaging (RRA) treatment of this category of alloys leads to improvement in the corrosion resistance without significant compromise in strength. SCC was found to be improving in general in these alloys, but the intergranular corrosion (IGC) and exfoliation corrosion (EXCO) need to be evaluated. The effect of RRA heat treatment on the IGC and exfoliation of AA7010 aluminum alloy has been investigated and compared with T6 and T73 temper conditions of the alloy. The results indicate that the corrosion susceptibility of AA7010 aluminum alloy decreased by subjecting the alloy to multistage (RRA) heat treatment. It is attributed to the grain boundary precipitate coarsening and is also the major factor responsible for reducing the susceptibility to IGC and EXCO. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCorrosion and anti-corrosives. =650 \0$aAluminum$xCorrosion. =650 \0$aAluminum alloys$xCorrosion. =700 1\$aRanganatha, R.,$eauthor. =700 1\$aAnil Kumar, V.,$eauthor. =700 1\$aGupta, R. K.,$eauthor. =700 1\$aAjithkumar, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200035.html =LDR 03762nab 2200553 i 4500 =001 MPC20200082 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200082$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200082$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.1723$223 =100 1\$aRenner, Peter,$eauthor. =245 10$aCorrosive Behavior of 3D–Printed 316L Stainless Steel /$cPeter Renner, Yan Chen, Ming Li, Chao Ma, Dilworth Parkinson, Hong Liang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAdditively manufactured metals such as stainless steels have promising futures because of their adaptive and one-step fabrication. However, an understanding of their properties and behavior in corrosive environments has not yet been achieved. This is due to a lack of methodology used to study the morphology of interior surfaces in porous materials. Thus, this research investigates the corrosion characteristics of three-dimensional–printed stainless steels made with five volume printing powers. Accelerated corrosion experiments were conducted at 35°C–40°C under atmospheric pressure in salt fog under predesigned durations. Electrochemical study was carried out with a potentiostat. Tomographic studies were conducted using a scanning electron microscope and micro X-ray computed tomography technology to analyze the effects of corrosion. Results revealed three findings. First, corrosion took place internally for all additively manufactured stainless steel samples regardless of printing parameters. Second, localized corrosion between printed layers was most pronounced. Third, elongated and oriented internal pits formed during corrosion and were associated with a dendrite-like structure, which is different from the conventional understanding of subsurface pitting directed by gravity. This research not only generates new knowledge on additively manufactured stainless steels but also opens new revenues for future investigation on the design and additive manufacturing of metals and alloys. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aStainless steel$xCorrosion. =650 \0$aCorrosion and anti-corrosives. =650 \0$aStainless steel. =700 1\$aChen, Yan,$eauthor. =700 1\$aLi, Ming,$eauthor. =700 1\$aMa, Chao,$eauthor. =700 1\$aParkinson, Dilworth,$eauthor. =700 1\$aLiang, Hong,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200082.html =LDR 03762nab 2200553 i 4500 =001 MPC20200025 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200025$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200025$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS1735 =082 04$a677.13$223 =100 1\$aMaruthi Prashantha, B. H.,$eauthor. =245 10$aImproved Mechanical Properties of Jute-Banana Fiber Phenol Formaldehyde Composites through Low-Cost Portable Hot Pressing Machine /$cB. H. Maruthi Prashantha, T. S. Manjunatha, P. S. Shiva Kumar Gouda, Abhilash Edacherian. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aEco-friendliness and biodegradability are the primary requirements of many of the composite products used in view of the growing concern to save our earth. There is a need to explore the means and protocols for developing eco-friendly and biodegradable products with quality parameters to perform for the specified end use. Products for Auto-Tech and Aero-Tech need to be designed based on the characteristic properties of the specific plant fibers. The optimum quantity and type of fiber play a crucial role in assessment of the mechanical and viscoelastic properties of the composites. In this work, an attempt has been made to design and develop a low-cost portable hot pressing machine for manufacturing polymer composites to improve the mechanical properties. Jute and banana fiber hybrid composites were produced with varying weight percentages of phenol formaldehyde (PF) in the range of 40–70 wt.%. The tensile, flexural, impact, hardness, and water absorption tests were carried out on jute-banana fiber hybrid PF composite. The study shows that hybrid composites with 50 % fibers by weight yield a significant increase in tensile and flexural strength with respect to other weight percentages of fibers, but the impact strength was lower in the case of 50 % fibers by weight. The microphotographs from a scanning electron microscope revealed a reasonably good fracture failure mechanisms, indicating enhanced mechanical properties. Further, to know the viscoelastic properties, a dynamic mechanical analysis was carried out to assess the properties of temperature dependency such as storage modulus, loss modulus, and damping factor. The results indicate that the composite with 50 wt.% fiber content has great storage modulus values and reduced damping behavior. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aJute spinning. =650 \0$aJute fiber$xPrices. =650 \0$aJute fiber. =700 1\$aManjunatha, T. S.,$eauthor. =700 1\$aShiva Kumar Gouda, P. S.,$eauthor. =700 1\$aEdacherian, Abhilash,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200025.html =LDR 03762nab 2200553 i 4500 =001 MPC20200106 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200106$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200106$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA409 =082 04$a620.126$223 =100 1\$aDing, Mingchao,$eauthor. =245 10$aOn the Use of the a /$cMingchao Ding, Yuanliang Zhang, Huitian Lu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn our previous work, a parameter areaΔ was proposed to describe fatigue damage caused by micro scratch, whose validity was verified by fracture mechanics. In this article, we summarize an attempt to check the applicability of the areaΔ in the field of the classic S-N curve method. For the sake of objective verification, the experiment data used in this article are from our published work. A high cycle fatigue life model of TC17 based on micro scratches is established with the synthesis of the three-parameter model and Murakami equation modified by areaΔ. Prediction results gave accuracy to mainly fall into the scatter band of factor 2. It can be suggested that areaΔ is suitable for being used in both fracture mechanics and classic S-N curve method. Furthermore, the validity of areaΔ in fatigue behavior analysis combined with current fatigue theories and materials is summarized. The measurement method of scratch depth and width suitable for areaΔ is also introduced. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMaterials.; Materials science. =650 \0$aTest of English as a Foreign Language. =650 \0$aEnglish language. =700 1\$aZhang, Yuanliang,$eauthor. =700 1\$aLu, Huitian,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200106.html =LDR 03762nab 2200553 i 4500 =001 MPC20200022 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200022$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200022$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.B55 =082 04$a620.192323$223 =100 1\$aMwema, F. M.,$eauthor. =245 10$aEffect of Heat Treatment on the Structure and Morphology of Silver-Coated Three-Dimensional Printed Flexible Polylactic Acid Thin Plates /$cF. M. Mwema, D. Sobola, A. D. Baruwa, E. T. Akinlabi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe micromorphology of three-dimensional (3D) printed silver/polylactic acid (PLA) exposed to heat treatment is reported. The PLA samples were printed through fused deposition modeling and then coated using a conductive silver paint. They were then heat treated in an electric furnace at 5, 10, and 20 min at 100°C. The samples were then characterized using X-ray diffraction, X-ray photoelectron spectroscopy, low-resolution and high-resolution scanning electron microscopy, atomic force microscopy, and roughness analyses. The results revealed that there is transformation of the structure and morphology of the silver/PLA samples on exposure to heat treatment at different times. On heat treatment, the PLA structure transforms from unstable δ state to thermally stable state (α). A slight shift of the 2θ for each peak was observed at heat treatment. There are shifts up to 0.7 eV on the binding energy of the Ag3d as shown by the X-ray photoelectron spectroscopy analysis, indicating an enhancement of bonding of silver onto the PLA structure on thermal treatment. The surface appearance was described by root mean square roughness, mean roughness, skew, kurtosis, and fractal dimension. The inner structure of the samples is shown by scanning electron microscopy at cross sections. The morphology and topography on the surface of the silver/PLA samples indicate a considerable structure growth and adhesion between the silver and PLA. These results illustrate that in situ deposition of silver paint onto PLA substrate, and subsequent heat treatment can be explored as a viable process for enhancing metallization of 3D printed polymer parts for various applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aPolylactic acid. =650 \0$aThermodynamics. =650 \0$aChemistry. =700 1\$aSobola, D.,$eauthor. =700 1\$aBaruwa, A. D.,$eauthor. =700 1\$aAkinlabi, E. T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200022.html =LDR 03762nab 2200553 i 4500 =001 MPC20200153 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200153$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200153$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC271 =082 04$a536.5028$223 =100 1\$aMorchhale, Ayush,$eauthor. =245 10$aPrediction of Flow Stress and Forming Limits for IN625 at Elevated Temperature Using the Theoretical and Neural Network Approach /$cAyush Morchhale, Nitin Kotkunde, Swadesh Kumar Singh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present work, the prediction of flow stress for IN625 has been done using two of the latest constitutive models, namely, modified Arrhenius (m-A) and combined Johnson-Cook and Zerilli-Armstrong (JC-ZA), and also by an artificial neural network (ANN) at 300, 473, 673, 873, and 973 K. On comparing the predictive efficiency of flow stress using constitutive models, the m-A model displayed better statistical parameters. It includes the effect of activation energy, temperature, and strain rate while predicting the flow stress, which are the most critical parameters while working at elevated temperature. The ANN approach helped predict the best flow stress results with the least average absolute error (AAE) of 0.93 % and the highest correlation coefficient (R) of 0.992. Further, the Barlat 1989 yielding function best predicted the yield loci among the Hill 1948 and Barlat 1989 criteria. The experimental stretch forming test has been conducted, and the forming limits improved by approximately 30.25 % as the temperature increased from 300 to 973 K. Additionally, the theoretical model, namely, Marciniak–Kuczyński (MK) model, has been used by inducing the combined effect of the constitutive model and yielding function for predicting the forming limits. The m-A constitutive model, in combination with Barlat 1989 yielding function, best predicted the forming limit curve. The ANN method has also been used after rigorously training the neural network, and it displayed the least AAE while predicting the forming limits. Thus, the neural network technique can be used as a modern tool to predict results involving extreme virtual experimental conditions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aTemperature measurements. =650 \0$aFluid dynamics. =650 \0$aTemperature measuring instruments. =700 1\$aKotkunde, Nitin,$eauthor. =700 1\$aSingh, Swadesh Kumar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200153.html =LDR 03762nab 2200553 i 4500 =001 MPC20200099 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200099$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200099$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.6 =082 04$a620.1/1228$223 =100 1\$aVarela, L. B.,$eauthor. =245 10$aCorrosion Resistance of Low-Temperature and Conventional Plasma-Nitrided 410S Ferritic-Martensitic Stainless Steels /$cL. B. Varela, M. T. Umemura, J. W. Calderón-Hernández, C. E. Pinedo, F. O. Kolawole, A. P. Tschiptschin. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aLow-temperature plasma nitriding (LTPN) of 410S ferritic-martensitic stainless steel was carried out in a 75 % N2 – 25 % H2 gas mixture, at 400°C, for 20 h. Conventional plasma nitriding (CPN) was also carried out in the same atmosphere but at 530°C. The corrosion resistance was assessed by potentiodynamic polarization (PP) testing in 3.5-wt. % NaCl. Measuring of the mass loss was carried out after immersion of the specimens in a 3 % FeCl3 solution during 88 h. To define the sensitivity to intergranular corrosion, the degree of sensitization (DOS) was measured using the double-loop electrochemical PP technique (DL-EPR). DL-EPR results indicated that the potentiodynamic-polarization measurements showed that pitting corrosion resistance of the nitrided samples was enhanced, whereas the weight loss experiments showed that LTPN samples presented a corrosion resistance equal to the untreated samples. The DOS results displayed that the untreated samples were less resistant to intergranular corrosion correlated with the LTPN specimens. On the contrary, the CPN specimens exhibited typical behavior of general corrosion. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aFerritic steels. =650 \0$aMaterials$xEffect of radiation on$vCongresses. =650 \0$aStainless steel$xCorrosion. =700 1\$aUmemura, M. T.,$eauthor. =700 1\$aCalderón-Hernández, J. W.,$eauthor. =700 1\$aPinedo, C. E.,$eauthor. =700 1\$aKolawole, F. O.,$eauthor. =700 1\$aTschiptschin, A. P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200099.html =LDR 03762nab 2200553 i 4500 =001 MPC20200031 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200031$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200031$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418 =082 04$a620.11296$223 =100 1\$aAgarwala, Swati,$eauthor. =245 10$aA Quantitative Approach for Thermal Characterization of Phase Change Materials /$cSwati Agarwala, K. Narayan Prabhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA quantitative method for the calculation of phase change parameters of salt-based phase change materials (PCMs) has been proposed. This technique involves the estimation of mold-salt interfacial heat flux by solving Fourier’s law of heat conduction within the salt and using it for the calculation of phase change enthalpy of salt PCMs. Radial heat transfer was ensured by keeping the length to diameter (L/D) ratio of the mold equal to 5. The proposed method eliminates any drawbacks involved with sample size, reference material, the baseline fitting calculations, and the errors introduced due to the selection of solidification points. Pure salt PCMs such as potassium nitrate (KNO3), sodium nitrate (NaNO3), and solar salt mixture (60 wt. % NaNO3 + 40 wt. % KNO3) were used for validation of this technique. The thermal behaviors of the salt and the mold during solidification of the salt sample were analyzed, and solidification characteristics such as cooling rate, solidification time, and phase change enthalpy of PCMs were determined. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMaterials$xThermal properties. =650 \0$aEnvironmental engineering. =650 \0$aComposite materials. =700 1\$aNarayan Prabhu, K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200031.html =LDR 03762nab 2200553 i 4500 =001 MPC20200068 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200068$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200068$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA684 =082 04$a660$223 =100 1\$aYang, Mei,$eauthor. =245 10$aBainite Percentage Determination and Effect of Bainite Percentage on Mechanical Properties in Austempered AISI 5160 Steel /$cMei Yang, Bryer Sousa, Richard Smith, Hooman Sabarou, Danielle Cote, Yu Zhong, Richard D. Sisson. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aX-ray diffraction (XRD) analysis with Rietveld refinement was used to determine the percentage of each microstructural constituent in AISI 5160 steel parts, which were austempered at 315°C for 1 minute, 2 min, 5 min, 30 min, and 90 min, separately. Nanoindentation was also conducted to quantify the concentration of bainite to compare with the XRD results. Thus, the bainitic transformation kinetics for AISI 5160 was determined for the selected austempering temperature. The mechanical properties of these parts were also tested to investigate their correlation to the bainite percentage. The results show that the tensile properties, including the yield strength, ultimate tensile strength, and elongation, increase with the austempering holding time at the selected austempering temperature, which corresponds to the bainite percentage increase. And in the same vein, hardness (both macro- and micro-hardness) decreases with austempering holding time, which corresponds to the martensite percentage decrease. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aSteel, Structural$xFatigue. =650 \0$aSteel, Structural$xTesting. =650 \0$aStructural design$xStandards. =700 1\$aSousa, Bryer,$eauthor. =700 1\$aSmith, Richard,$eauthor. =700 1\$aSabarou, Hooman,$eauthor. =700 1\$aCote, Danielle,$eauthor. =700 1\$aZhong, Yu,$eauthor. =700 1\$aSisson, Richard D.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200068.html =LDR 03762nab 2200553 i 4500 =001 MPC20200121 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200121$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200121$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS320 =082 04$a669.142$223 =100 1\$aWang, Yuankang,$eauthor. =245 10$aA Comparison Study of the Austenite Grain Growth and Its Transformation Behavior during Uniform Continuous Cooling of a Wrought and Selective Laser Melting 4340 Steels /$cYuankang Wang, Pedro de Souza Ciacco, Raymundo Ordonez, C. Isaac Garcia. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis study compares austenite grain growth and its continuous cooling transformation (CCT) behavior between selective laser melting (SLM) 4340 and conventional wrought 4340 steels. Standard dilatometry tests were used to determine the austenite decomposition behavior at different cooling rates. The analysis of the data from the controlled cooling paths was used to generate CCT diagrams for the two steels investigated in this study. Advanced microstructural characterization techniques, Scanning Electron Microscopy and Orientation Imaging Microscopy, were employed to support the CCT diagrams. Electron Backscatter Diffraction (EBSD) and a special EBSD-Image Quality characterization technique were used to assess the percentage of the microstructural components observed. Three important observations were made: (1) the hardenability of the wrought 4340 steel was higher than the SLM 4340 steel; (2) the presence of granular bainite was observed after slow cooling conditions in both steels; (3) the SLM steel exhibited finer austenite grain size distribution than the wrought steel in the temperature range studied. MTEX, a MatLab program, was used to reconstruct the prior austenite grains. The SLM steel exhibited finer austenite grain size distribution than the wrought steel in the temperature range studied. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aPlates, Iron and steel$xCooling. =650 \0$aSteel$xCooling. =650 \0$aSteel. =700 1\$ade Souza Ciacco, Pedro,$eauthor. =700 1\$aOrdonez, Raymundo,$eauthor. =700 1\$aIsaac Garcia, C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200121.html =LDR 03762nab 2200553 i 4500 =001 MPC20200036 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200036$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200036$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS1548.7.P58 =082 04$a677.4743$223 =100 1\$aBharath, K. N.,$eauthor. =245 10$aMechanical and Chemical Properties Evaluation of Sheep Wool Fiber–Reinforced Vinylester and Polyester Composites /$cK. N. Bharath, P. Madhu, T. G. Yashas Gowda, Akarsh Verma, M. R. Sanjay, Suchart Siengchin. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe present research study focuses on some mechanical and chemical characterizations of sheep wool fabric–reinforced thermosetting polymeric matrix composites. Mechanical tests, such as tensile and bending tests, along with chemical tests, such as water absorption test, swelling test, and chemical absorption test of sheep wool fabric reinforced with 50% vinylester and 50% polyester composites, were deliberated under different operating conditions. The results affirm that the tensile and bending strength of sheep wool fiber laminate of vinylester composition have high strength compared to that of polyester-composed laminates. The moisture absorption as well as the chemical absorption properties are found to be greater in the case of vinylester-based laminates, indicating the better mechanical interlocking behavior between sheep wool fabric and vinylester matrix. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aPolyester fibers$xTesting. =650 \0$aSynthetic fabrics$xTesting. =650 \0$aPolyester fibers. =700 1\$aMadhu, P.,$eauthor. =700 1\$aYashas Gowda, T. G.,$eauthor. =700 1\$aVerma, Akarsh,$eauthor. =700 1\$aSanjay, M. R.,$eauthor. =700 1\$aSiengchin, Suchart,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200036.html =LDR 03762nab 2200553 i 4500 =001 MPC20200086 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200086$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200086$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.B55 =082 04$a620.192323$223 =100 1\$aRane, Ajay Vasudeo,$eauthor. =245 10$aDensity and Its Role in Predicting Interphase Characteristics and Dispersion in Poly(Lactic Acid) – Particulate Fillers Composites /$cAjay Vasudeo Rane, Krishnan Kanny, Mohan Turup Pandurangan, Sabu Thomas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDensity measurements (i.e., physical magnitude) are quick, efficient, and crucial in determining the structure and quality of solid materials. For polymer composites, properties tend to increase, decrease, or both with density. In this work, poly(lactic acid) composites (PLAC) filled with carbon black (CB), multiwalled carbon nanotubes (MWCNTs), and cellulose nanofibers (CNFs) were prepared using the dissolution–dispersion method (DD) and oligomeric–dispersion method (OD). To study the hybrid effect, PLAC with 2.5 weight percent (wt%) CB + MWCNTs (0.2, 0.4, 0.6, 0.8, 1.0, 1.5 and 2.0wt%) and 2.5wt% CB + CNFs (0.2, 0.4, 0.6, 0.8, 1.0, 1.5 and 2.0wt%) were prepared using DD and OD. Density measurements were performed on PLAC to determine the extent of dispersion and interphase characteristics. PLAC prepared by OD showed an increase in density values in comparison to DD, irrespective of the filler. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aPolymers. =650 \0$aPolylactic acid. =650 \0$aLactic acid. =700 1\$aKanny, Krishnan,$eauthor. =700 1\$aPandurangan, Mohan Turup,$eauthor. =700 1\$aThomas, Sabu,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200086.html =LDR 03762nab 2200553 i 4500 =001 MPC20200076 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200076$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200076$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a620.1$223 =100 1\$aHassanifard, S.,$eauthor. =245 10$aMonotonic and Fatigue Response of Heat-Treated Friction Stir Welded Al 6061-T6 Joints :$bTesting and Characterization /$cS. Hassanifard, A. Nabavi-Kivi, A. Ghiasvand, A. Varvani-Farahani. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe present study evaluates the influence of post-weld heat treatment on the fatigue strength of friction stir welded aluminum 6061-T6 joints. The solution-treatment artificial aging (STA) was applied to the friction stir welding samples prior to cyclic tests. Hardness distributions along the centerline of the welded specimens as well as the tensile properties and microstructural features were initially examined. The stress-controlled cyclic tests were then conducted at constant amplitude loading with the load ratio of R = 0.1. Experimental results revealed that tensile strength of STA heat-treated samples increased 73 % as compared to the as-welded (AW) joints. Furthermore, the STA heat-treated specimens experienced 28 % higher elongation than those of AW samples. A 3D finite element analysis was developed to (i) simulate residual stress distribution of the welded joints after heat treatment processing and (ii) analyze stress/strain components at weld toe induced as a result of applied loading cycles. The heat-affected zone with critical local stress/strain values was found to be the most vulnerable zone for cracking. Predicted fatigue lives by means of the Smith, Watson, and Topper model were found in close agreement with those experimentally obtained values. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aFriction stir welding. =650 \0$aFriction welding. =650 \0$aDissimilar welding. =700 1\$aNabavi-Kivi, A.,$eauthor. =700 1\$aGhiasvand, A.,$eauthor. =700 1\$aVarvani-Farahani, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200076.html =LDR 03762nab 2200553 i 4500 =001 MPC20200144 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200144$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200144$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL521.3 =082 04$a634.9618$223 =100 1\$aSanchez-Sarmiento, Fernando B.,$eauthor. =245 10$aNumerical Calculation of the Heat Transfer Coefficients in Multi-Thermocouple Probes by the Reconstruction Temperature Method /$cFernando B. Sanchez-Sarmiento, Miguel A. Cavaliere. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe numerical simulation of the heat transfer problem of the quenching process requires an accurate characterization of the heat transfer coefficient dependence on surface temperature, which is usually determined by measuring the cooling curve and applying an inverse method. In most cases, the thermocouple is located at the center of the probe (ISO 9950, Industrial Quenching Oils — Determination of Cooling Characteristics — Nickel-Alloy Probe Test Method), but, in recent years, probes with several thermocouples have been developed (e.g., Tensi test) and the process to estimate the coefficients turned out to be more complex. The proposed methodology has considered the numerical reconstruction of the temperature field of the probe using multi-thermocouple measurements, actual material properties, and heat transfer equations. The heat transfer coefficients are directly obtained from the numerically reconstructed thermal field based on the fact that its gradient at the boundaries is proportional to the heat flux transferred. It is important to remark that neither parameter optimization nor curve fitting is needed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aTemperature measuring instruments. =650 \0$aThermocouples. =650 \0$aSoil temperature. =700 1\$aCavaliere, Miguel A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200144.html =LDR 03762nab 2200553 i 4500 =001 MPC20200210 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200210$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200210$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQL801 =082 04$a591$223 =100 1\$aWang, Lili,$eauthor. =245 10$aStudy on the Effect of Laser Processing Parameters on Microtexture Morphology /$cLili Wang, Min Wang, Wei Zhang, Xingtang Zhao, Xue Ge. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe microtexture with different morphological characteristics is obtained by changing the processing parameters of laser marking machine. The microtexture morphology characteristics are observed, and the width and depth of microtexture is measured. At the same time, the theoretical model of laser processing is established to solve the change rule of the processing morphology. The average friction coefficient variation of specimens obtained by different processing parameters is tested by universal friction and wear tester. The results show that the width of microtexture increases with the increase of laser processing power and decreases with the increase of laser scanning frequency, which is consistent with the theoretical results of laser processing. The depth of microtexture increases with the increase of laser processing power and scanning frequency. When the scanning times are 3, the width and depth of microtexture reach the maximum. With the decrease of scanning speed, the width and depth of microtexture increase gradually. Friction experiments show that when the processing power is 60–70 %, the lubrication can achieve the optimal value. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMorphology. =650 \0$aPhysiology. =650 \0$aLasers. =700 1\$aWang, Min,$eauthor. =700 1\$aZhang, Wei,$eauthor. =700 1\$aZhao, Xingtang,$eauthor. =700 1\$aGe, Xue,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200210.html =LDR 03762nab 2200553 i 4500 =001 MPC20200027 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200027$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200027$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS280 =082 04$a671.84$223 =100 1\$aMofid, Mohammad Ammar,$eauthor. =245 10$aEffect of Interlayer Composition on Microstructure and Properties of Titanium/Aluminum TLP Bond /$cMohammad Ammar Mofid, Mahmoud Farshbaf, Hamid Naeimian. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe transient liquid phase bonding of titanium and aluminum alloys was investigated, in which the interlayer was a 30-µm-thick brass foil and pure silver foil. The optimized variables used in this work are bonding temperature and time of 600°C and 30 min, respectively. The bonding temperature of 600°C (higher than both Al–Ag and Al–Cu eutectic temperatures) was selected to ensure melting. In both cases, an interesting intergranular eutectic-like phase was observed along the Al2024 grain boundaries. The evaluation of the interfaces of joints via optical microscopy, scanning electron microscopy, line scan, and X-ray diffraction demonstrated that a high temperature in the transient liquid phase process leads to the diffusion of alloying elements to form the molten eutectic. By holding the joint at the bonding temperature, the diffusion of alloying elements resumes, and the liquid interlayer solidifies isothermally because of the changes in the composition of the melted interlayer. The formation of Al2Cu, MgZn2, and TiMg3Zn15 phases was confirmed in the specimen made with brass foil as the interlayer. The interface width is decreased significantly from 8 µm to 2 µm by using silver foil instead of Cu–Zn foil as the interlayer. It is suggested that applying silver interlayer was successful in controlling the diffusion between two base metals and resulted in the formation of Ag2Al and AgMg phases on the fracture surface. This joint gave a higher shear strength of 154.7 MPa. The significant reduction in the strength of the bond due to using Cu–Zn foil as an interlayer (70.2 MPa) can be attributed to aggregation and growth of the brittle intermetallic compounds (IMCs) in the vicinity of the joint interface. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aTitanium-aluminum-vanadium alloys. =650 \0$aMetal-work. =650 \0$aTitanium alloys$xIndustrial applications. =700 1\$aFarshbaf, Mahmoud,$eauthor. =700 1\$aNaeimian, Hamid,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200027.html =LDR 03762nab 2200553 i 4500 =001 MPC20190240 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190240$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190240$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQE389.5 =082 04$a552.5$223 =100 1\$aKuntikana, Ganaraj,$eauthor. =245 10$aAmelioration of Bauxite Residues by Sequential Slurry Carbonation /$cGanaraj Kuntikana, Sayeeda Syed, Devendra Narain Singh, Sagar S. Pandit, Nageswar Kapuri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe safe handling, storage, disposal, and use of the bauxite residues (BRs) has become a bug bear to alumina refineries not only because of the enormous quantity that gets generated but also because of its characteristics, namely, extremely high alkalinity and sodicity. One of the ways to negotiate with this situation would be to “neutralize the BRs,” a hypothesis that would transform them into a nonhazardous (chemically less or partially inert) material that could be used as a man-made resource for its bulk utilization in various infrastructure development and agronomical projects. In order to demonstrate the feasibility of this hypothesis, BRs from an alumina refinery of India were collected in their slurry form and neutralized by resorting to sequential slurry carbonation (SSC) technique. The SSC was achieved by employing (1) gaseous phase carbon dioxide, CO2, and (2) synthetic flue gas, which has a composition like that of stack gases produced from the industries. The study observed a sharp decline in pH of the BRs slurry in the initial phase of treatment, which lasted for 120 min, and the formation of neutralized BRs, designated as NBRs. The exposure, when continued beyond 120 min to 1,440 min, yielded NBRs that exhibit almost constant pH. The exposure of NBRs to the atmosphere resulted in a pH rebound with time. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aNuclear Facilities. =650 \0$aCalcium Compounds. =650 \0$aBauxite. =700 1\$aSyed, Sayeeda,$eauthor. =700 1\$aSingh, Devendra Narain,$eauthor. =700 1\$aPandit, Sagar S.,$eauthor. =700 1\$aKapuri, Nageswar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20190240.html =LDR 03762nab 2200553 i 4500 =001 MPC20200047 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200047$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200047$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.S7 =082 04$a668.4233$223 =100 1\$aIghalo, Joshua O.,$eauthor. =245 10$aThermal, Functional Group and Microstructural Analysis of Fibrillated Composites Developed from Polystyrene and Plantain Stalk Wastes /$cJoshua O. Ighalo, Adewale George Adeniyi, Sulyman A. Abdulkareem. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis study aims to examine the thermal, functional group and microstructural properties developed from polystyrene (as a matrix) and plantain stalk waste (as reinforcing material). The composite was developed by manual-mixing and hand-layup and cured at 25°C±2°C for 7 days. The composites were analyzed by Fourier transform infrared (FTIR) spectroscopy, differential scanning calorimetry (DSC), and scanning electron microscope with energy-dispersive spectroscopy. The maximum amount of heat flow for plainly cured polystyrene resin was 3.25 mW, and the maximum for the composites was 7.9 mW at 30 % plantain filler. Optimum specific heat capacity of the composite was achieved at 40 % filler loading. The peak specific capacity at 2, 4, 6, 8, and 10 min at optimum filler loading (40 %) were 154, 308, 462, 616, and 770 J/Kg°C, respectively. FTIR analysis revealed that chemical interaction between the polymer resin and the biomass filler was confirmed. The microstructural analysis confirmed the poor interfacial bonding between the filler and resin. The composite shows good potential for use in mild to moderate temperature applications (25°C–125°C). Besides the advantage of materials development, this study has also been able to proffer a solution in biomass valorization and solid waste management. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aPolystyrene. =650 \0$aMicrocrystalline polymers. =650 \0$aThermoplastics. =700 1\$aAdeniyi, Adewale George,$eauthor. =700 1\$aAbdulkareem, Sulyman A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200047.html =LDR 03762nab 2200553 i 4500 =001 MPC20200053 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200053$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200053$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA481 =082 04$a620.16$223 =100 1\$aBachchhav, B. D.,$eauthor. =245 10$aDrilling of High Volume Fraction Al 2 O 3 Metal Matrix Composites /$cB. D. Bachchhav, Sachin Salunkhe, Vishal Naranje. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aComposites of high volume fraction are suitable in many applications because of their high strength-to-weight ratio, high hardness, and wear resistance. In this study, the influence of drilling parameters and volume fraction of aluminum oxide (Al2O3) on the material removal rate (MRR), surface finish, and overcut was investigated. Al-Al2O3 metal matrix composites were stirred cast with 10 %, 20 %, and 30 % of Al2O3 concentration and subsequently machined using computer numerical controlled drilling. Experiments based on Taguchi’s methodology were carried out with L9 orthogonal array. Analysis of variance and signal-to-noise ratio analysis revealed the ranking of the most influencing process parameters. High volume fraction reinforcement of Al2O3 shows an adverse effect on MRR, surface roughness, and overcut. The drilling of high volume fraction ceramic-reinforced composite shows a brittle fracture of hard particles leading to the generation of overcut on the top surface. An empirical relationship between the process parameters under consideration and response variables were established by using regression analysis. The mathematical equations obtained through this work can be extended to find out the optimum volume fraction of Al2O3 to have better MRR and accuracies. This work will be useful to the metalworking industry towards the development of products having excellent tribo-mechanical properties. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMetallic composites. =650 \0$aThermodynamics. =650 \0$aChemical kinetics. =700 1\$aSalunkhe, Sachin,$eauthor. =700 1\$aNaranje, Vishal,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200053.html =LDR 03762nab 2200553 i 4500 =001 MPC20200057 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200057$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200057$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.16 =082 04$a620.112$223 =100 1\$aManda, Sanjay,$eauthor. =245 10$aEffect of Cyclic Prestrain on Tensile Behavior of Commercially Pure Copper /$cSanjay Manda, Sumeet Mishra, N. P. Gurao. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe effect of prestrain induced by load and displacement control low cycle fatigue (LCF) on subsequent tensile behavior of commercially pure copper was investigated. Mechanical properties obtained after post-fatigue tension (half-life fatigue followed by tension) were superior compared to quasistatic tension. There was significant improvement in strength with little change in ductility for the displacement control LCF prestrained sample after tensile test. However, there was appreciable simultaneous increment in both strength and ductility for load control half-life fatigue followed by tension sample compared to quasistatic tension. A thorough microstructural investigation reveals the presence of persistent slip bands (PSBs) in displacement control LCF sample, whereas the load control LCF sample shows a composite microstructure comprising cells and PSBs. This composite microstructure provides higher strength and ductility. The introduction of cyclic prestrain to a material will improve its monotonic properties, which is attributed to the cyclic prestrain-induced dislocation substructure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCopper industry and trade. =650 \0$aCopper industry and trade$xFinance. =700 1\$aMishra, Sumeet,$eauthor. =700 1\$aGurao, N. P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200057.html =LDR 03762nab 2200553 i 4500 =001 MPC20200163 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200163$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200163$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP690 =082 04$a665.53$223 =100 1\$aKandavel, T. K.,$eauthor. =245 10$aCorrosion Behavior of P/M Plain Carbon Steel under the Influence of Various Heat Treatment Processes /$cT. K. Kandavel, T. Panneerselvam, P. Karthikeyan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe present research work focuses on the effects of heat treatment on corrosion behavior of sintered plain carbon steel (Fe-0.5%C). Investigation on corrosion mechanism has been carried out on three different heat-treated (annealing, normalizing, and hardening) powder metallurgy plain carbon steel specimens. Aqueous immersion and electrochemical pickling corrosion tests were conducted on the heat-treated specimens. It has been found that the heat treatments have enhanced the percentage of theoretical density as well as the hardness of the specimen compared with the as-sintered specimen. The corrosion resistance of the oil-quenched specimen was found to be higher than that of the other heat-treated specimens. Larger grains are observed in the case of as-sintered and annealed specimens, and more iron carbides are observed in the normalized and oil-quenched specimens. Intergranular and pitting types of corrosion have been observed in the scanning electron microscopy images of corroded specimens. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCarbon steel$xCorrosion. =650 \0$aSaline water conversion$xFlash distillation process. =650 \0$aCorrosion and anti-corrosives. =700 1\$aPanneerselvam, T.,$eauthor. =700 1\$aKarthikeyan, P.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200163.html =LDR 03762nab 2200553 i 4500 =001 MPC20200049 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200049$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200049$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.1723$223 =100 1\$aWolf, Witor,$eauthor. =245 10$aEffect of Aging Temperature and Time on Secondary Phase Precipitation and Texture in an Ultrafine Grained 2205 Duplex Stainless Steel after Cold Rolling /$cWitor Wolf, Lóren Kelly de Paula Inácio, Dagoberto Brandão Santos. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe present work evaluates the precipitation of secondary phases in a cold-rolled ultrafine-grained 2205 duplex stainless steel after aging at temperatures ranging from 600°C to 950°C for different annealing times (300–86,400 s). X-ray diffraction, scanning electron microscopy coupled with electron backscattered diffraction, and transmission electron microscopy were used for microstructural characterization. Mechanical properties were evaluated using tensile and Vickers microhardness tests. σ- (sigma), χ- (chi), and chromium carbide (M23C6) phases were identified. σ- and austenite phase volume fractions increased with aging time, whereas χ-phase and carbides remained nearly constant, and the ferritic volume fraction decreased. Inverse pole figures of σ-phase, for a specimen aged at 850°C for 24 h, showed a localized distribution of orientations, normal to the rolling direction, being centered around the [001], whereas for the other annealing conditions, a concentration between the orientations [001] and [110] was observed. Although mechanical strength was increased, the ductility was reduced as the secondary phase precipitation proceeded. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aStainless steel$xCorrosion. =650 \0$aStainless steel. =650 \0$aSteel, Heat resistant. =700 1\$aInácio, Lóren Kelly de Paula,$eauthor. =700 1\$aBrandão Santos, Dagoberto,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200049.html =LDR 03762nab 2200553 i 4500 =001 MPC20200117 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200117$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200117$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7871.75 =082 04$a621.381/334$223 =100 1\$aChauhan, Kamlesh V.,$eauthor. =245 10$aExperimental Investigation of Molybdenum Oxide Coatings Prepared by RF Magnetron Sputtering /$cKamlesh V. Chauhan, Akshay L. Sonera. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMolybdenum oxide films were deposited by radio frequency (RF) reactive magnetron sputtering. The study of surface structure and wettability with variations in deposition power and deposition time was carried out. The RF power was varied in the range of 125 W to 200 W, which led to evolution of (540), (001), (015), and (100) textures of molybdenum oxide. The X-ray diffractometer results show an increment of preferred orientation along the (001) plane for deposited molybdenum oxide films. The average crystallite size is within the range 17–18 nm with an increase of RF power from 125 W to 200 W and 19–31 nm with an increment in deposition time from 15 to 60 minutes. The outcome demonstrated that RF power and the time of deposition are the capacities that influence the static and dynamic contact angle framed by water and formamide. The surface roughness or unpleasantness increases in increments from 9.12 to 27.77 nm with an expansion in RF power from 125 W to 200 W and from 39.56 to 238.77 nm with increases in time of deposition from 15 min to an hour. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMagnetron sputtering. =650 \0$aMolybdenum oxides. =650 \0$aChemical vapor deposition. =700 1\$aSonera, Akshay L.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200117.html =LDR 03762nab 2200553 i 4500 =001 MPC20200150 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200150$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200150$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK4660 =082 04$a671.5212$223 =100 1\$aSubramani, Naveen Kumar,$eauthor. =245 10$aInfluence of Welding Consumables on Ballistic Performance of Gas Metal Arc Welded Ultra-high Hard Armor Steel Joints /$cNaveen Kumar Subramani, Balasubramanian Visvalingam, Malarvizhi Sudersanan, Hafeezur Rahman Abdur, Balaguru Vadivel. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSteels with high strength and high hardness are considered to be the essential criteria for weight reduction in armored fighting vehicles (AFVs). Ultrahigh hard armor (UHA) steels are higher hardness (>500 HV) and higher strength (>1,500 MPa) than the currently used rolled homogenous armor (RHA) steels. The occurrence of both a tempered region in the grain-refined heat-affected zone (HAZ) and hydrogen-induced cracking (HIC) has become the limiting factor in the life extension of weld in high-strength and high-hardness armor grade steels. Hence, an attempt was made to weld UHA steel by gas metal arc welding (GMAW) process using different three filler metals (1) austenitic stainless steel (ASS), (2) duplex stainless steel (DSS), and (3) low-hydrogen ferritic. The ballistic performance of the joints was evaluated based on the area density and depth of penetration. The mechanical properties (transverse tensile, hardness, and impact toughness) and microstructural features of welded joints are correlated with the ballistic performance. All the joints stopped the 7.62 × 51 ball projectile at the weld metal region. However, through-hole (perforation) was observed when tested against the 7.62 × 54 armor piercing projectile. The joints fabricated using ASS filler wire showed superior ballistic resistance, a lesser degree of HAZ softening, and better impact toughness properties due to the higher energy absorption capability of the austenitic phase. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aGas metal arc welding. =650 \0$aWelding. =650 \0$aElectric welding. =700 1\$aVisvalingam, Balasubramanian,$eauthor. =700 1\$aSudersanan, Malarvizhi,$eauthor. =700 1\$aAbdur, Hafeezur Rahman,$eauthor. =700 1\$aVadivel, Balaguru,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200150.html =LDR 03762nab 2200553 i 4500 =001 MPC20210028 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210028$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210028$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN775 =082 04$a669.722$223 =100 1\$aDakhel, A. A.,$eauthor. =245 10$aHydrogenation and Dopant Concentration-Dependent Structural, Optical, and Magnetic Properties of Synthesized Manganese/Aluminum–Codoped Anatase Nanoparticles /$cA. A. Dakhel. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present work, titanium oxide (TiO2) codoped with 2 at % and 5 at % manganese/aluminum nanoparticle samples were synthesized by a coprecipitation method. The effects of manganese/aluminum dopant concentrations and hydrogenation temperatures on the structural, optical, and magnetic properties of the synthesized nanoparticles were studied. The investigation was aimed at considering manganese dopant ions as the foundation of stable magnetic properties and using Al3+ ions to supply itinerant electrons to study and synthesize a dilute magnetic semiconductor based on TiO2. The synthesized doped nanopowders were studied by several methods: X-ray diffraction, optical absorption spectroscopy, and magnetic measurements. It was established that the Anatase structure was the main structure of the synthesized codoped powders. The dopant and the hydrogenation did not introduce qualitative change in the phase structure of the powder. It was found that the hydrogenation increased the crystallite size, and the high-temperature hydrogenation (500°C) deteriorated the crystalline structures. The optical study was aimed at investigating the formation of F+-centers. The shift in the optical absorption edge was explained in terms of the Urbach and Moss-Burstein effects. The magnetic energy parameter was calculated to compare the strength of the resulting room-temperature ferromagnetic ordering in the samples. The greatest saturation magnetization parameter was 0.005 μB/manganese for the sample with the lower studied doping level (2 %) and hydrogenated (H) at low temperature (400°C); TiO2: 2 % manganese: aluminum–H (hydrogenated). The magnetic saturation magnetization was lowered for a higher doping level and higher hydrogenation temperature (500°C). =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aAluminum-manganese alloys. =650 \0$aAluminum. =650 \0$aAluminum alloys. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210028.html =LDR 03762nab 2200553 i 4500 =001 MPC20200051 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200051$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200051$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP594 =082 04$a662.669$223 =100 1\$aXia, Zhenguo,$eauthor. =245 10$aDensity Functional Study of Methanol Synthesis from CO Hydrogenation on Cu-Based Catalysts /$cZhenguo Xia, Xiaochen Duan, Yan Yao, Geng Chen, Yingying Zhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe reaction mechanism of carbon monoxide (CO) hydrogenation to methanol has been carried out theoretically in this paper. The atomic configuration was analyzed by an unlimited B3LYP calculation method in density functional theory. The reaction model for CO hydrogenation to methanol was established by using Gaussian 09. The adsorption sites, bond angles, bond lengths, reaction intermediates, transition-state structures, adsorption energy, reaction-energy barriers, and reaction heat of CO hydrogenation to methanol with different amounts of copper-based catalysts were calculated. The calculations provided the elementary reaction of methanol in the synthesis, and the reaction potential-energy diagram for methanol synthesis was plotted. The optimum reaction path for CO hydrogenation to methanol was as follows: CO→HCO*→H2CO*→H3CO*→CH3OH. The rate-limiting step was the hydrogenation of the methoxy (H3CO) species with an activation barrier of 1.28 eV. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMethanol. =650 \0$aThermochemistry. =650 \0$aHydrogenation. =700 1\$aDuan, Xiaochen,$eauthor. =700 1\$aYao, Yan,$eauthor. =700 1\$aChen, Geng,$eauthor. =700 1\$aZhu, Yingying,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200051.html =LDR 03762nab 2200553 i 4500 =001 MPC20200092 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200092$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200092$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA417.6 =082 04$a620.1/123$223 =100 1\$aHu, Zhiqiang,$eauthor. =245 10$aA High-Throughput Forging Technique and Its Application in the Optimization of the Deformation Conditions /$cZhiqiang Hu, Kaikun Wang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe high-throughput (HT) forging technique is introduced for speeding up the research on the forming property of materials. The core concept of the HT forging technology is to assign two influencing factors to multiple samples simultaneously. By se4tting gradients with different factors in the vertical direction and the horizontal direction, all the samples will be forged at different deformations and HT experimentation will be achieved. HT forging equipment was designed and developed to accomplish the 5 by 6 HT experimentation by establishing a temperature gradient in the vertical direction and a strain or a strain rate gradient in the horizontal direction. A simplified experiment with 5CrNiMoV steel to verify the reliability and efficiency was carried out. Combined with the analysis of microstructure, the relatively excellent deformation condition for the steel was the temperature of 1,000°C and strain rate of 1s−1. For obtaining the optimum deformation condition, more specimens should be forged in the HT equipment. It evidenced that the HT forging technique and the HT equipment would be favorable for analyzing the property and optimize the forming process rapidly. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aDeformations (Mechanics) =650 \0$aMaterials$xAnalysis$xData processing. =650 \0$aMultivariate analysis. =700 1\$aWang, Kaikun,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200092.html =LDR 03762nab 2200553 i 4500 =001 MPC20200070 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200070$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200070$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.A5 =082 04$a669.722$223 =100 1\$aMenapace, C.,$eauthor. =245 10$aHot Deformation Behavior of Al-20Si-5Fe-2Ni Alloy Obtained by Spray Forming /$cC. Menapace, L. Menapace, G. Perricone. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe hot deformation behavior of an aluminum alloy containing 20 % silicon, 5 % iron, and 2 % nickel produced by spray forming has been investigated through hot compression tests. Tests were carried out at 400°C, 450°C, and 500°C and 2 strain rates (0.25 and 1 s−1). It was found that, under the deformation conditions applied, stress–strain curves were characterized by a distinct stress peak or a multipeaks trend indicating the occurrence of dynamic recrystallization (DRX). Microstructural observations, together with X-ray diffraction (XRD) analysis, also indicated a change in the type of intermetallics during hot deformation, with a reduction of δ-Al4FeSi2 and a corresponding increase of the stable β-Al5FeSi phase. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aAluminum alloys$xFracture. =650 \0$aAluminum alloys$xMetallography. =650 \0$aAluminum alloys. =700 1\$aMenapace, L.,$eauthor. =700 1\$aPerricone, G.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200070.html =LDR 03762nab 2200553 i 4500 =001 MPC20200127 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200127$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200127$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.B55 =082 04$a620.192323$223 =100 1\$aRane, Ajay Vasudeo,$eauthor. =245 10$aUnderstanding Zones of Molecular Dimension in Poly (Lactic Acid) Composites through Attenuated Total Reflectance Fourier Transform Infrared Spectroscopy :$bCorrelation with Tensile Yield Test Measurements /$cAjay Vasudeo Rane, Deepti Yadav, Krishnan Kanny, Neerish Revaprasadu, Sabu Thomas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMultiwalled carbon nanotubes (MWCNTs) filled poly (lactic acid) composites (MWCNTs PLAC) and hybrid poly (lactic acid) composites (HPLAC) filled with hybrid fillers, i.e., combining variable weight percentage of MWCNTs (0.2, 0.4, 0.6, 0.8, and 1.0 wt. %) and fixed weight percentage of carbon black (CB) (2.5 wt. %) were prepared using oligomeric dispersion. This article focuses on the use of attenuated total reflectance Fourier transform infrared (ATR-FTIR) spectroscopy to analyze the intermolecular interactions and zones of molecular dimension within polymer composite materials. For the first time percent transmittance (%T) and transmittance area (A) of peaks from ATR-FTIR spectra were corroborated with the zones of molecular dimension within MWCNTs PLAC and HPLAC. Tensile measurements were performed on test specimens of MWCNTs PLAC and HPLAC, and the numerical values of tensile yield strength were determined. The numerical values of tensile yield test measurements of MWCNTs PLAC and HPLAC were then compared with the %T and A of MWCNTs PLAC and HPLAC ATR-FTIR spectra, which presented a new way to qualitatively analyze the zones of molecular dimension and their role toward the change in the tensile yield strength of the MWCNTs PLAC and HPLAC. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aLactic acid. =650 \0$aPolylactic acid. =650 \0$aPolymers$xBiodegradation. =700 1\$aYadav, Deepti,$eauthor. =700 1\$aKanny, Krishnan,$eauthor. =700 1\$aRevaprasadu, Neerish,$eauthor. =700 1\$aThomas, Sabu,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200127.html =LDR 03762nab 2200553 i 4500 =001 MPC20200158 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200158$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200158$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP1180.B55 =082 04$a620.192323$223 =100 1\$aTrivedi, Kunal,$eauthor. =245 10$aDeposition of TiN and TiAlN Thin Films on Stainless Steel Tubes by a Cylindrical Magnetron Sputtering Method /$cKunal Trivedi, Ramkrishna Rane, Alphonsa Joseph, Shashi Bhushan Arya. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTitanium nitride (TiN) and titanium aluminum nitride (TiAlN) coatings are very hard materials that are mostly coated on cutting tools to increase the tool life. These coatings have also been successfully applied as a coating material for biomedical applications mainly due to their tribological properties, biocompatibility, and affordable price. In an attempt to develop transition metal nitride coatings on specimens of cylindrical geometry, TiN and TiAlN thin films were deposited successfully on stainless steel tubes using a direct-current cylindrical magnetron cosputtering method. Both types of coatings were uniform in nature and had good adherence to the substrate. TiN and TiAlN thin films were characterized systematically to determine their structure, surface morphology, chemical states, chemical structure, and electrochemical behavior using X-ray diffraction (XRD), scanning electron microscopy (SEM), X-ray photoelectron spectroscopy (XPS), Raman spectroscopy, and potentiodynamic methods, respectively. The XRD patterns of the TiN and TiAlN coatings indicated (111) preferential orientation. Cross-sectional SEM images revealed a columnar growth of the coatings with an arrow-headed geometry. XPS characterization showed the presence of TiN, Titanium dioxide, titanium oxynitride, aluminum oxide, and aluminum nitride phases. Potentiodynamic polarization tests in 3.5 % sodium chloride solution revealed that the TiAlN coating exhibited superior corrosion resistance compared with the TiN coating. Furthermore, TiAlN coating showed 94 % of average absorption in ultraviolet-visible region using photospectrometry. The cylindrical magnetron sputter deposition technique enables development of uniform protective coatings on tubular geometries, which are frequently employed in solar thermal and nuclear applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMagnetron sputtering. =650 \0$aCoatings. =650 \0$aStainless steel$xCorrosion. =700 1\$aRane, Ramkrishna,$eauthor. =700 1\$aJoseph, Alphonsa,$eauthor. =700 1\$aArya, Shashi Bhushan,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200158.html =LDR 03762nab 2200553 i 4500 =001 MPC20200191 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200191$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200191$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS360 =082 04$a672.81$223 =100 1\$aBaldin, Vitor,$eauthor. =245 10$aCharacterization and Performance of TiAlN and TiN Coatings on Plasma-Nitrided AISI 4140 Steel /$cVitor Baldin, Leonardo Rosa Ribeiro da Silva, Claudia Regina Bernardi Baldin, César Augusto Neitzke, Ricardo Diego Torres, Alisson Rocha Machado. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSteels can go through a duplex treatment process, consisting of depositing a physical vapor deposition (PVD) coating on plasma-nitrided substrates. The coating layer varies from 1.5 to 5 µm, depending on the application needs. The work's objective is to analyze the performance and evaluate the mechanical characteristics of titanium nitride (TiN) and titanium aluminum nitride (TiAlN) coatings deposited in AISI 4140 with quenched/tempered or plasma-nitrided treatment. Scanning electron microscopy/energy dispersive spectroscopy and X-ray diffraction performed the microstructural and chemical characterization of the duplex-treated samples. The mechanical properties were measured by performing nanohardness tests, allowing the extraction of hardness and elastic modulus out of the load/unload behavior of the samples, and the scratch test according to ASTM C1624-05 (2010), Standard Test Method for Adhesion Strength and Mechanical Failure Modes of Ceramic Coatings by Quantitative Singles Point Scratch Testing (Superseded), coupled with acoustic emission analysis, probed adhesion of the TiN and TiAlN coating on the steel substrates. Also, pin-on-disk tribological tests probed the wear resistance of the duplex-treated samples. It was found that the nitriding process increases the surface hardness and elastic modulus. The TiAlN coating has the highest load capacity with the least amount of wear. The adhesion of the TiAlN coatings is worse than TiN. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aProtective coatings. =650 \0$aSheet-steel. =650 \0$aTin. =700 1\$ada Silva, Leonardo Rosa Ribeiro,$eauthor. =700 1\$aBaldin, Claudia Regina Bernardi,$eauthor. =700 1\$aAugusto Neitzke, César,$eauthor. =700 1\$aDiego Torres, Ricardo,$eauthor. =700 1\$aRocha Machado, Alisson,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200191.html =LDR 03762nab 2200553 i 4500 =001 MPC20200176 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200176$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200176$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN710 =082 04$a672.09714451$223 =100 1\$aAzouani, O.,$eauthor. =245 10$aKinetic Analysis of Pack-Borided Gray Cast Iron /$cO. Azouani, M. Keddam, O. Allaoui, A. Sehisseh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this work, a gray cast iron containing copper of grade EN-GJL-250 was pack-borided within the temperature range of 800°C–1,000°C with treatment times of 2–6 h. According to the X-ray diffraction analysis, the Fe2B phase has been identified over the surface of this material and the boride layer has an average thickness between 20.8 ± 2.9 and 149.1 ± 10.2 µm. The morphological aspect of the Fe2B layer was investigated with a scanning electron microscope. The regression model based on the ANOVA analysis has been established to investigate the growth kinetics of boride layers on EN-GJL-250 gray cast iron. The boron activation energies in the EN-GJL-250 cast iron were estimated as 148.03 and 147.96 kJ mol−1 by the parabolic growth law and the mean diffusion coefficient method, respectively. Furthermore, the experimental Fe2B layers’ thicknesses were in accord with the predicted values given by the regression model and the MDC method. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCast-iron$xAnalysis. =650 \0$aIron-works. =650 \0$aSteel. =700 1\$aKeddam, M.,$eauthor. =700 1\$aAllaoui, O.,$eauthor. =700 1\$aSehisseh, A.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200176.html =LDR 03762nab 2200553 i 4500 =001 MPC20200149 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200149$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200149$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS227 =082 04$a671.52$223 =100 1\$aDharmik, Bhushan Y.,$eauthor. =245 10$aInvestigations on Magnetic and Corrosive Characteristics of Thin Cold-Rolled Nonoriented Electrical Steel Sheets Post Gas Tungsten Arc and Laser Welding /$cBhushan Y. Dharmik, Nitin Kumar Lautre. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThin sheets (0.5 × 10−3 m) of cold-rolled nonoriented (CRNO) electrical steel are widely used for rotating electrical machines. Gas tungsten arc (GTA) and, recently, laser welding are used for welding M-43 grade CRNO steel. The performance of CRNO is thus explored because of changes in low-carbon, high-silicon content and thin insulation coatings post welding. The welding current for GTA varied from 30 to 110 A, whereas a laser of 800 W was used to estimate the heat affected zone (HAZ), fusion zone (FZ), and weld characteristic ratio. Ferritic phases with polygonal grain size, percent silicon content, magnetic losses, and welded corrosive samples corrosion rate (in mils penetration per year) are compared with the base material (average grain size 55 ± 12 μm). Five different corrodent (NaCl, NaOH, HCl, H2O, H2CO3) environments were created for 2,000 h as per ASTM B895-16(2020)e1, Standard Test Methods for Evaluating the Corrosion Resistance of Stainless Steel Powder Metallurgy (PM) Parts/Specimens by Immersion in a Sodium Chloride Solution, and ASTM G31-72(1999), Standard Practice for Laboratory Immersion Corrosion Testing of Metals standards. The GTA weld samples revealed much-increased weld geometry with welding current, and a significant increase in grain sizes up to 189.2 ± 4 μm for GTA and 187 ± 3 μm for the laser sample near the weld zone is observed. Microhardness variation is found to be in the range of 55 HV for GTA and 51 HV for laser samples in the FZ region with reference to the base metal hardness of 227 HV. In addition, the increase in core loss of 58.72 % for GTA and 39.82 % for laser samples with reference to nonwelded samples is observed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aWelding. =650 \0$aGas tungsten arc welding. =650 \0$aGas metal arc welding. =700 1\$aLautre, Nitin Kumar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200149.html =LDR 03762nab 2200553 i 4500 =001 MPC20200135 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200135$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200135$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP245.T85 =082 04$a661/.0512$223 =100 1\$aRajagopalan, Sudheer,$eauthor. =245 10$aEffect of Carbon Black and Titanium Dioxide Dispersants on Solidification of Multiwall Carbon Nanotube–Added Salt-Based Phase Change Material /$cSudheer Rajagopalan, K. N. Prabhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe effect of carbon black and titanium dioxide (TiO2) dispersants on solidification of potassium nitrate phase change material (PCM) with multiwall carbon nanotube (MWCNT) addition was investigated using the Fourier method of thermal analysis. On addition of 0.1 % of MWCNT, the solidification time of PCM decreased by 26 %, enhancing the heat release rates. A decrease in thermal diffusivity of the PCM was observed on addition of MWCNT particles. These benefits were observed to diminish over successive thermal cycles because of the agglomeration of MWCNT particles. To prevent the agglomeration of additives, dispersants such as carbon black and TiO2 were used. In the presence of carbon black, the nanosalt PCM retained all the cooling curve parameters over 10 thermal cycles, preventing the agglomeration of nanoadditives. On the other hand, the dispersant TiO2 significantly enhanced the thermal diffusivity property of PCM by virtue of its superior thermal conductivity. These are critical outcomes in development of nanosalt PCMs for thermal energy storage applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aTitanium dioxide$xDefects. =650 \0$aTitanium dioxide$xIndustrial applications. =650 \0$aTitanium dioxide$xEnvironmental aspects. =700 1\$aPrabhu, K. N.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200135.html =LDR 03762nab 2200553 i 4500 =001 MPC20200151 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200151$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200151$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.C5 =082 04$a620.17170287$223 =100 1\$aTassi, Fernanda,$eauthor. =245 10$aDuplex Treatments of Chromizing and Nitriding :$bInfluence of the Steel Composition and Treatment Sequence on the Surface Properties/Performance /$cFernanda Tassi, Rodrigo Perito Cardoso, Ana Sofia C. M. d’Oliveira. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSurface engineering is unavoidable for most high-performance components manufacturing. Frequently when very specific properties are required duplex treatments are necessary. In the case of diffusion-based treatments, like nitriding and chromizing, the substrate composition plays an important role in the obtained results. Consequently, for duplex treatments, the second treatment will be influenced by the first one. Putting these aspects in evidence, Deutsches Institut für Normung (DIN) CK15, DIN C45Pb, and DIN X40CrMoV5-1 steels were exposed to pack chromizing followed by plasma nitriding and plasma nitriding followed by pack chromizing. Results showed that the treated surface features are very sensitive to the steel composition and treatment sequence. In nitrided and chromized surfaces, the iron nitrides formed during the first treatment are dissolved and replaced by chromium nitrides (CrxNy) during chromizing. The inverse sequence resulted in surfaces containing chromium carbide (Cr7C3) formed during chromizing with CrxNy and iron nitrides formed during nitriding. The higher measured hardness (1,499 Vickers hardness [HV]) was obtained for the chromized and nitride DIN X40CrMoV5-1 steel. Salt spray tests showed that treatments ending by chromizing are the most promising for enhancing the surface corrosion resistance, except for the low carbon steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMetals$xEffect of high temperatures on. =650 \0$aSteel$xCreep. =650 \0$aChrome steel$xTesting. =700 1\$aCardoso, Rodrigo Perito,$eauthor. =700 1\$ad’Oliveira, Ana Sofia C. M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200151.html =LDR 03762nab 2200553 i 4500 =001 MPC20200104 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200104$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200104$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN751 =082 04$a672.36$223 =100 1\$aHassan, Azzam D.,$eauthor. =245 10$aNew Prediction Model of Tempered Martensite Hardnesses for Quenched and Tempered Low-Alloy Steel /$cAzzam D. Hassan, Murtadha Abbas Jabbar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSeveral experimental formulas have been proposed by many researchers to estimate the tempered martensite hardness of high-strength low-alloy (HSLA) steel under different tempering conditions. The objective of the present study was to develop a new mathematical model to estimate the tempered martensite hardness and the tensile strength for low-alloy steels under different tempering conditions with enhanced accuracy. The experimental results of previous research were relied on to develop the new mathematical models. A best fit for the tempered martensite hardness model has been developed by adding a factor of correlation obtained from the difference (error) between the hardness values measured by literature and the calculated hardness values from the tempered martensite hardness model. Moreover, the best equation that feature the value of this difference was presented as a function of the tempering temperature. The new model considered the combined parameters, which are tempering conditions (temperature and time) and the parameters of alloy elements. The proposed model has been examined and compared with the experimental results of a previous research and was shown to provide a good reasonable approximation with mean percentage error between the measured and calculated of hardness values was 0.89% and 0.79% for holding time of 2 and 48 h, respectively. Furthermore, it was concluded that the hardness feature is affected significantly by tempering parameters and the parameters of alloy elements. The hardness showed also decreasing in values with increasing the tempering temperature and holding. Also, the proposed equation for the tensile strength and area reduction have been written as a function of the tempering temperature. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aSteel alloys$xHeat treatment. =650 \0$aCast-iron$xHeat treatment. =650 \0$aPhysical metallurgy. =700 1\$aJabbar, Murtadha Abbas,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200104.html =LDR 03762nab 2200553 i 4500 =001 MPC20190247 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20190247$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20190247$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a624.183$223 =100 1\$aYadav, Rajat,$eauthor. =245 10$aSynthesis and Mechanical Behavior of Ball-Milled Agro-Waste RHA and Eggshell Reinforced Composite Material /$cRajat Yadav, Shashi Prakash Dwivedi, V. K. Dwivedi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aNowadays, there are various industrial wastes from industries that produce lots of environmental pollution. Rice husk ash (RHA) is agricultural waste and eggshell waste is industrial waste. These wastes also produce lots of soil pollution. However, by utilizing these wastes, some environmental problems can be reduced. In the present investigation, an attempt was made to utilize RHA and eggshells as reinforcement material in the development of aluminum-based composite material. Carbonized eggshell ash (CESA) particles and RHA were ball-milled for 75 hours to obtain a single entity. The mixture of CESA and RHA particles has been varied from 2.5 % to 12.5 % in the development of the composite. Ball-milled reinforcement particles in the single entity showed uniform distribution in the aluminum-based matrix material. Results showed that after the heat treatment process, the tensile strength and hardness of the aluminum/5 % CESA/5 % RHA composite was found to be 189.95 MPa and 56 brinell hardness number (kgf/mm2) respectively. The tensile strength and hardness of the composite after heat treatment were enhanced by 31 % and 60 %, respectively. However, the toughness and ductility were reduced after adding the mixture of carbonized eggshell particles and alumina in the aluminum alloy. Corrosion loss and thermal expansion behavior were also observed to identify the carbonized eggshell and RHA addition in the aluminum alloy. Corrosion loss and thermal expansion of the AA3105/5 % eggshell powder/5 % RHA composite after heat treatment were found to be 0.011 gm and 4.35 mm3, respectively. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aComposite materials. =650 \0$aCement composites. =650 \0$aComposite-reinforced concrete. =700 1\$aDwivedi, Shashi Prakash,$eauthor. =700 1\$aDwivedi, V. K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20190247.html =LDR 03762nab 2200553 i 4500 =001 MPC20200075 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200075$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200075$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.T54 =082 04$a669.7322$223 =100 1\$aMalkiya Rasalin Prince, R.,$eauthor. =245 10$aZrC-Impregnated Titanium-Based Coating as an Effective Lubricating Barrier for Artificial Hip Prosthesis /$cR. Malkiya Rasalin Prince, N. Selvakumar, D. Arulkirubakaran, S. Christopher Ezhil Singh, M. Chrispin Das, Praveen Kumar Bannaravuri, R. Mercy Russelin Prabha, J. Aldrin Raj, R. B. Jeen Robert. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe important properties of implant materials are extended component life, wear resistance, and biocompatibility. The wear characteristics depend, for implant materials, on the nature of the implant, movement of joints, and usage of the part. Hard ceramic Ti-6Al-4V-2ZrC (Titanium (Ti), Aluminium (Al), Vanadium (V), Zirconium Carbide (ZrC)) was coated over stainless steel (SS) 316L for analyzing the wear and mechanical properties against E-52100 steel balls sliding for artificial hip joints. The coating crystallography was examined by X-ray diffraction analysis and the topography was inspected by an Atomic Force Microscope (AFM). The coating thickness has been measured as 5–6 µm using a scanning electron microscope (SEM), and the smooth surface roughness of 0.03 µm was measured using AFM. The Ti-6Al-4V-2ZrC coated surface nanohardness has been enhanced three times higher than uncoated. The ball-on-disk wear was investigated with a load of 2–3 N, sliding distance 110 m, and sliding velocity 0.25–0.95 m/s. The investigated wear rates are mostly higher than 10−5 mm3/Nm, and the frictional coefficient reduces from 0.8 to 0.35. The morphology of worn surfaces was analyzed using SEM. Based on the improvement in nanohardness, it is concluded that the Ti-6Al-4V-2ZrC coated SS 316L is a good replacement for an artificial hip joint because of its better wear resistance and coefficient of friction. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aTitanium alloys. =650 \0$aTitanium. =650 \0$aTitanium alloys$xIndustrial applications. =700 1\$aSelvakumar, N.,$eauthor. =700 1\$aArulkirubakaran, D.,$eauthor. =700 1\$aChristopher Ezhil Singh, S.,$eauthor. =700 1\$aChrispin Das, M.,$eauthor. =700 1\$aBannaravuri, Praveen Kumar,$eauthor. =700 1\$aMercy Russelin Prabha, R.,$eauthor. =700 1\$aAldrin Raj, J.,$eauthor. =700 1\$aJeen Robert, R. B.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200075.html =LDR 03762nab 2200553 i 4500 =001 MPC20200206 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200206$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200206$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS156 =082 04$a658.562015195$223 =100 1\$aChavhan, Ganesh R.,$eauthor. =245 10$aMultiresponse Optimization of Wear Parameters of Steel-Embedded Glass-Epoxy Hybrid Composites Using Taguchi-Grey Method Optimization /$cGanesh R. Chavhan, Lalit N. Wankhade. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this work, Taguchi-grey relational analysis (GRA) has been used to optimize the process parameters during the tribological performance of steel-embedded glass-epoxy hybrid composites. The specific wear rate (SWR) and the average coefficient of friction (CoF) were investigated. The tribological test was planned by using Taguchi L27 orthogonal array. The tests were carried using different factors like steel volume % (0–10 %), applied load (80–100 N), and sliding distance (1,000–2,000 m) for a constant time (20 min). The optimal process parameters were obtained with Taguchi-GRA, and the influencing factor was determined with the help of analysis of variance. The results show that the most influencing factor is steel volume %, followed by applied load and sliding distance. The dry sliding wear performance was optimized to achieving minimal SWR and average CoF. Steel volume 10 %, sliding distance 1,000 m, and applied load 80 N were observed as optimum parameters to achieving minimal SWR and average CoF. A confirmation test was carried out to verify the tests. The results show that the multiresponses such as SWR and average CoF were significantly enhanced through GRA. Finally, the worn surfaces of the hybrid composites were studied through scanning electron microscope (SEM). The SEM shows that the pits on the surface of the image were covered with voids and other defects. The SEM also shows that the specimen’s porosity decreases with the increasing fractional volume of steel in the composite. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aQuality control$xStatistical methods. =650 \0$aEngineering design$xStatistical methods. =650 \0$aTaguchi methods (Quality control) =700 1\$aWankhade, Lalit N.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200206.html =LDR 03762nab 2200553 i 4500 =001 MPC20200199 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200199$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200199$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9 =082 04$a667.9$223 =100 1\$aReddy, Sadhgun,$eauthor. =245 10$aThe Effect of Nanocoatings on Critical Heat Flux (CHF) under Pool Boiling Conditions /$cSadhgun Reddy, K. Narayan Prabhu, U. Vignesh Nayak. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (6 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe effect of nanomaterial coating on heat transfer characteristics of a copper substrate during pool boiling with distilled water (>99.9 %) was studied. The peak on the pool boiling curve between nucleate and transition boiling is termed the critical heat flux. Multi-walled carbon nanotubes and graphene were used to obtain coatings on the copper substrate. Experiments were carried out at atmospheric pressure. The results showed enhanced critical heat flux for the coated substrates. Graphene-coated copper showed the highest critical heat transfer characteristics compared with that on bare and multi-walled carbon nanotube-coated substrates. The study has significant implications for the enhancement of heat transfer during quench heat treatment. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aNanostructured materials. =650 \0$aNanoparticles. =650 \0$aCoatings. =700 1\$aNarayan Prabhu, K.,$eauthor. =700 1\$aVignesh Nayak, U.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200199.html =LDR 03762nab 2200553 i 4500 =001 MPC20200132 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200132$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200132$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA459-492 =082 04$a670$223 =100 1\$aKhan Rana, Ahmad Raza,$eauthor. =245 10$aEffect of Graphene Enrichment on Solid Particle Erosion Performance of Electroless Ni-P Composite Coatings /$cAhmad Raza Khan Rana, Zhi Li, Jamal Umer, Zoheir Farhat. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSolid particle erosion (SPE) and dents (from contact loads) are among numerous surface degradations in the hydrocarbon industry that can in turn compromise the longevity of protective coatings. Both these degradation mechanisms can induce cracks that allow the corrosive solutions to seep through those cracks and corrode the underlying metal, thereby defeating the purpose of surface protection. Nickel-phosphorus (Ni-P) coatings have been known for decades for their corrosion resistance, but their applications in hydrocarbon industries are impeded by their tribological limitations, namely low wear resistance. In the current research work, graphene nanoplatelets were introduced to an Ni-P electroless plating bath in various concentrations (30 mg/L, 60 mg/L, and 100 mg/L) to achieve three different compositions of ternary Ni-P–graphene coatings, namely Ni-P-30 mg G, Ni-P-60 mg G, and Ni-P-100 mg G, respectively. Surface roughness was characterized via topography employing a laser confocal microscope. Coating hardness was characterized using Vickers hardness and the composition analyses were carried out via energy dispersive spectroscopy. SPE was conducted via Tungsten carbide (WC) erodent ball at three different impact angles and two different particle velocities. Finally, Hertzian indentation was performed under two different loads to characterize the denting behavior of coatings. Eroded and dented coatings were further visualized via an optical microscope. The highest concentration of graphene (by 18 vol.%) in Ni-P-30 mg G coating improved the hardness, leading to the smallest size of indents during both SPE and Hertzian indentation. Also, Ni-P-30 mg G exhibited no evidence of cracking under normal impact angle and particle velocities of 35 ms−1 and 52 ms−1. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aGraphene. =650 \0$aNanostructured materials. =650 \0$aElectronic structure. =700 1\$aLi, Zhi,$eauthor. =700 1\$aUmer, Jamal,$eauthor. =700 1\$aFarhat, Zoheir,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200132.html =LDR 03762nab 2200553 i 4500 =001 MPC20200064 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200064$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200064$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD251.3 =082 04$a547$223 =100 1\$aLiu, Yuwei,$eauthor. =245 10$aThe Structure and Properties of Bilayer Carbon Films with Various Layer Thickness /$cYuwei Liu, A. V. Rogachev, Xiaohong Jiang, Bing Zhou, E. A. Kulesh, D. G. Piliptsou, A. S. Rudenkov. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article studies the microstructure and mechanical properties of diamond-like carbon films (α-C), depending on their architecture. The bilayer (titanium/a-C) and (titanium nitride [TiN]/a-C) films were deposited from the flows of the metal plasma, formed through sputtering a titanium cathode by a direct current arc, and the carbon plasma, formed as a result of pulsed arc sputtering of a graphite cathode. The effect of titanium and TiN sublayers on the structure and mechanical properties of carbon films has been shown. It has been found that the catalytic effect of the sublayer is most pronounced when the carbon layer thickness is less than 90 nm; when the carbon layer thickness is less than 30 nm, the size of Csp2 clusters decreases, and the fraction of atoms with Csp3 bonds increases. The annealing of the films does not significantly affect the behavior of the phase composition and the structure of the films with an increase in the carbon layer thickness. It has been demonstrated that the size dependences of the optical properties, which are manifested in a transparency increase and a change in the band gap when increasing the carbon layer thickness, are associated with the occurrence of mutual diffusion processes in the interfacial zone. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aChemistry, Organic. =650 \0$aChemistry. =650 \0$aCarbon. =700 1\$aRogachev, A. V.,$eauthor. =700 1\$aJiang, Xiaohong,$eauthor. =700 1\$aZhou, Bing,$eauthor. =700 1\$aKulesh, E. A.,$eauthor. =700 1\$aPiliptsou, D. G.,$eauthor. =700 1\$aRudenkov, A. S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200064.html =LDR 03762nab 2200553 i 4500 =001 MPC20200159 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200159$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200159$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.P58 =082 04$a620.1/92$223 =100 1\$aBedi, Deepa,$eauthor. =245 10$aEffect of Coating of Carbon Nanotubes on Mechanical Properties of Polymer Composites :$bA Review /$cDeepa Bedi, Sumit Sharma, Saurabh Kango, Nitin Sharma, Pramod Rakt Patel. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (26 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCarbon nanotubes (CNTs) possess superior mechanical properties in addition to other functional features. The last decade has seen rapid growth in the usage of CNTs in polymer matrix composites. This has led to the development of novel dispersion and functionalization techniques. Though the CNTs exhibit excellent properties, their use in commercial applications has been restricted by the problem of dispersion in polymers. Perfect bonding of CNTs and polymer interphase with uniform distribution of CNTs are required for fully utilizing the reinforcement effect of the CNTs. In this review, the techniques and principles of CNT dispersion and functionalization/coating have been discussed in depth. The readers will be able to further their understanding of the field of CNT-reinforced polymer composites. Functionalization of CNTs and their dispersion effects are highlighted for polymer-based composites to observe the changes that occur in their mechanical behavior. The issues that require further work include the need to develop the tools and techniques to analyze the extent of dispersion or cluster of CNTs in a matrix of polymer, the need to optimize the process variables, and the need to resolve the inconsistency among the studies involving functionalization of CNTs. Comprehensive studies are needed to determine the association between different variables, such as surface treatment, degree of functionality, conditions of processing, and thermal, mechanical, optical, and electrical properties. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aPolymers. =650 \0$aPolymers$xMechanical properties. =650 \0$aPolymeric composites. =700 1\$aSharma, Sumit,$eauthor. =700 1\$aKango, Saurabh,$eauthor. =700 1\$aSharma, Nitin,$eauthor. =700 1\$aRakt Patel, Pramod,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200159.html =LDR 03762nab 2200553 i 4500 =001 MPC20210003 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210003$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210003$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.1/4$223 =100 1\$aEzeh, Emmanuel C.,$eauthor. =245 10$aNovel Immobilized Ligand on Polymer Matrix as Adsorbent for Water Purification /$cEmmanuel C. Ezeh, Pius O. Ukoha, Habila Bulus, John C. Attah. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA novel polymer material that is capable of adsorption of Pb2+ and Cu2+ in aqueous solutions has been synthesized. 3-Aminopropyltriethoxysilane was reacted with tetraethylethoxysilane in methanol and aqueous solution of HCl to yield 3-aminopropypolysiloxane (APP). Reacting the APP with ethylchloroacetate in triethylamine yielded a functionalized 3-aminopropypolysiloxane (FAPP). The FAPP was reacted with urea to yield urea immobilized polysiloxane. FTIR spectra of the APP showed major absorption bands (cm−1) at: 1032.5-1042.7 (Si-O-Si), while the Urea-immobilized polysiloxanes (APPU) showed major absorption bands (cm−1) at: 3200 − 3400 υ(NH), 2929 − 2957 υ(C-H), 1505-1643 (C=O, C=C, C=N), and 1032.5-1042.7 (Si-O-Si). SEM-EDX analysis of APP and APPU showed mean pore volumes (nm3) of 113.49 ± 7.91 and 44.89 ± 7.44 respectively, and elemental composition (%) as follows: APP, O (36.68), Si (39.91); FAPP, O (29.43), Si (41.64), Cl (9.06); APPU, O (32.15), Si (28.42), N (25.42). APP maximum percentage adsorption of Pb2+ and Cu2+ in simulated water were 79.44 and 74.81 respectively, while APPU maximum percentage adsorption of Pb2+ and Cu2+ were in the range of 78.36 − 85.44 and 79.63 − 82.87 respectively. The maximum percentage adsorption of Pb2+ and Cu2+ which indicate the sorption capacities of the adsorbents occurred within the pH range of 8-10, contact time between 70-90 min, metal ion concentration of 20-25 ppm, dosage of adsorbent of 0.01 − 0.03 g for Pb2+ adsorption, and 0.04 − 0.05 g for Cu(II), and at a temperature of 90°C. The statistical analyses showed significant difference in the means of the effects of pH, time and concentration as F > Fcrit, except in the case of contact time for Cu2+. Temkin isotherm gave values of R2 in the range of 0.9210 − 0.9735 and best fitted the adsorption process. The urea immobilized polysiloxane (APPU) exhibited very high potential for adsorption of Pb2+ and Cu2+ in industrial effluent up to 100 %. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCeramic-matrix composites. =650 \0$aPolymeric composites. =650 \0$aPolymers. =700 1\$aUkoha, Pius O.,$eauthor. =700 1\$aBulus, Habila,$eauthor. =700 1\$aAttah, John C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210003.html =LDR 03762nab 2200553 i 4500 =001 MPC20210020 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210020$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210020$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA1 =082 04$a622$223 =100 1\$aMirzahosseini, Mohammadreza,$eauthor. =245 10$aAnalysis of the Effects of Voids in Mineral Aggregate on Pavement Fatigue Performance Using AASHTOWare Pavement ME Design and FlexPAVE /$cMohammadreza Mirzahosseini, Jusang Lee, Jan Olek, Jongmyung Jeon, Tommy E. Nantung. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDeviation of volumetric properties of asphalt mixtures, such as voids in mineral aggregates (VMA), from the agency–specified thresholds can cause minor to significant changes in pavement performance. This paper presents the results of the study on the effects of the deficiency of VMA parameters (ΔVMADesign) on the fatigue performance of asphalt pavements. Dynamic modulus and fatigue tests were performed on two types of mixtures (one with 9.5-mm nominal maximum aggregate size (NMAS) and the second one with 19-mm NMAS) at three levels of ΔVMADesign. The results were analyzed using two simulation models (i.e., FlexPAVE 1.1Alpha and AASHTOWare Pavement ME Design version 2.3.0 (Pavement ME)). The results showed that fatigue service life reduction was linearly correlated to an increase in ΔVMADesign and could reach almost 50 % for a pavement with ΔVMADesign of 3 %. Additionally, while both Pavement ME and FlexPAVE showed comparable results in terms of top-down cracking/damage predictions, the results of the analysis performed by FlexPAVE in terms of bottom-up damage prediction were more consistent with respect to the expected behavior of pavement structure in terms of damage. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aPavements, Asphalt concrete$xTesting. =650 \0$aRoads$xDesign and construction. =650 \0$aMineral industries. =700 1\$aLee, Jusang,$eauthor. =700 1\$aOlek, Jan,$eauthor. =700 1\$aJeon, Jongmyung,$eauthor. =700 1\$aNantung, Tommy E.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210020.html =LDR 03762nab 2200553 i 4500 =001 MPC20200141 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200141$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200141$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA462 =082 04$a620.11223$223 =100 1\$aHuang, I.-Wen,$eauthor. =245 10$aUnderstanding the Impact of Polishing and Environmental Factors on Corrosion Potential—An Optimization by Robust Design /$cI.-Wen Huang, Ashley Weitzel, Fred Goodwin, Kuo-Hsiang Chang, Lisa Reagan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aASTM G180-13, Standard Test Method for Corrosion Inhibiting Admixtures for Steel in Concrete by Polarization Resistance in Cementitious Slurries (Superseded), testing was used to determine the effectiveness of corrosion inhibiting admixtures. However, inconsistent results have been reported due to the polishing process. Although not standardized, polished metal specimens have been used to remove contaminants or native oxides prior to electrochemical measurements to acquire stabilized electrochemical measurements. Furthermore, the open circuit potential (OCP) delay before electrochemical testing was found to be critical to the consistency of the subsequent experiment. The goal of this study was to investigate the influence of polishing and environmental factors on the OCP value and its variation. The OCP of carbon steel in high pH simulated pore solutions was measured as functions of polishing, time, chloride content, and nitrite concentration. By using a full-factorial experimental design and regression analysis, the effects of the factors were studied on both the mean value and on the standard deviation of corrosion potential. The standard deviation of repeated tests was quantified and ranked to provide guidance on specimen preparation. The regression result showed that polishing does not influence the mean value of the OCP but that the OCP standard deviation heavily depends on the polishing consistency. Based on the experimental data and analysis, a suggestion was provided for specimen preparation to address the observed inconsistency in specimen preparation for ASTM G180-13 testing. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCorrosion and anti-corrosives. =650 \0$aSteel$xCorrosion. =650 \0$aMetals$xDefects. =700 1\$aWeitzel, Ashley,$eauthor. =700 1\$aGoodwin, Fred,$eauthor. =700 1\$aChang, Kuo-Hsiang,$eauthor. =700 1\$aReagan, Lisa,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200141.html =LDR 03762nab 2200553 i 4500 =001 MPC20200213 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200213$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200213$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7871.75 =082 04$a621.381334$223 =100 1\$aLathia, Rutvik,$eauthor. =245 10$aInvestigation of Post Annealed Titanium Nitride Thin Films Deposited with Magneto-Sputtering /$cRutvik Lathia, Kamlesh V. Chauhan, Kevin Dobariya, Ankit Patel, Vishal Parmar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aStructural and wettability properties of titanium nitride (TiN) thin films for different annealing temperatures have been characterized, and critical parameters have been identified. TiN thin films were deposited onto the silicon substrates by using the magneto-sputtering technique for two different powers, 150 W and 350 W. Subsequently, the films were annealed in the air at 573–973 K for the duration of 1 h. The X-ray diffraction spectra showed the appearance of titanium dioxide (TiO2) above 773 K temperature (termed as transformation temperature). The relative intensity of the TiO2 peaks rapidly increase with the temperature. The thin and dense oxide overlayer appeared at 773 K, and the thicker oxide layer was observed at 973 K. Surface roughness is observed to increase with the increase in annealing temperature but with the limiting value at 773 K; after that, the roughness decreases because of the stable formation of TiO2. Similarly, with an increase in temperature, the hydrophobic nature of thin films becomes more significant; however at 973 K, the formation of TiO2 declines the hydrophobic nature, and thus the surface energy increases. Transformation temperature is also found to be responsible for the reduction in grain size and compressive strain of the thin film. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMagnetron sputtering. =650 \0$aThin films. =650 \0$aMaterials science. =700 1\$aChauhan, Kamlesh V.,$eauthor. =700 1\$aDobariya, Kevin,$eauthor. =700 1\$aPatel, Ankit,$eauthor. =700 1\$aParmar, Vishal,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200213.html =LDR 03762nab 2200553 i 4500 =001 MPC20210044 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210044$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210044$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA404.6 =082 04$a620$223 =100 1\$aOkano, Shigetaka,$eauthor. =245 10$aDiagnosis of Mechanical Properties with Instrumented Indentation Technique Using Multiple Pyramid Indenters /$cShigetaka Okano, Masahito Mochizuki. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis paper presents a semi-nondestructive method for diagnosing mechanical properties through an instrumented indentation technique using multiple pyramid indenters with different dihedral angles. In the developed method, an approximated true stress–true strain curve can be obtained from the plots of the representative stress–representative strain relation estimated for each of the four different pyramid indenters. A functional relation between the representative stress and the indentation load–depth curve was derived from dimension analysis using the π theorem. Then, specific values of constants in the functional equation were determined for each of the pyramid indenters using experimentally validated finite element analysis of the instrumented indentation test. Meanwhile, the representative strain levels were quantified according to the dihedral angle of the pyramid indenters. The developed method was applied to estimate the true stress–true strain curve of non- and prestrained steels. As a result, a small difference could be seen only in non-strained steel with Lüders strain, but the estimated results are nearly in agreement with those obtained by tensile tests. The approximated curves were also used to estimate yield stress and prestrain. The results showed that estimation accuracy of yield stress was better than that based on an empirical correlation with Vickers hardness, and the estimated values of prestrain were in good agreement with those actually introduced by tensile tests. It is expected that the developed multi-indenter method will become useful for semi-nondestructively diagnosing mechanical properties for steel. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aChemical engineering. =650 \0$aCharacterization and Evaluation of Materials. =650 \0$aIndustrial Chemistry/Chemical Engineering. =700 1\$aMochizuki, Masahito,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210044.html =LDR 03762nab 2200553 i 4500 =001 MPC20210059 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210059$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210059$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.N5 =082 04$a669.7332$223 =100 1\$aDalpasquale, Alana S.,$eauthor. =245 10$aAl-Cr Diffusion Coatings Processed on a Cast and a Heat-Treated Ni-Base Alloy /$cAlana S. Dalpasquale, Ana Sofia C. M. D’Oliveira. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDiffusion coatings are used to protect components against oxidation and corrosion in high-temperature applications. The processing route and parameters determine the coating characteristics for each substrate. When more than one element is deposited, the number of processing variables increases, as single-step or two-step deposition can be used. With a two-step procedure, the element deposited first affects subsequent diffusion. Under these conditions, a better understanding of the phenomena involved is required, as the substrate plays an important role. To this end, a systematic assessment of chromium and aluminum diffusion coatings processed by out-of-pack cementation on a nickel alloy was carried out. The precipitation-hardened alloy was supplied as-cast and in a heat-treated condition. Three processing routes were used: a single-step procedure and two two-step procedures (AC, aluminizing+chromizing, and CA, chromizing+aluminizing). Characterization of the as-processed coatings showed that the nonuniform structure of the as-cast nickel alloy allowed preferential diffusion paths to form, reducing coating thickness and minimizing differences caused by the processing route. Synthesis of nickel aluminide (NiAl) occurs on coatings processed with the CA route, as aluminum diffuses in a nickel matrix that is richer in chromium, favoring the synthesis of the aluminide. Regardless of the processing route used, exposure to 1,100°C results in parabolic growth of the coating. At 1,100°C, partitioning of aluminum occurs between the upper surface of the coating and the nickel alloy, forming a diffusion barrier. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aNickel-aluminum alloys. =650 \0$aNickel alloys. =650 \0$aMaterials. =700 1\$aD’Oliveira, Ana Sofia C. M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210059.html =LDR 03762nab 2200553 i 4500 =001 MPC20200177 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200177$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200177$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.C9 =082 04$a669.963$223 =100 1\$aBachchhav, B. D.,$eauthor. =245 10$aTribological Performance of Copper-Titanium Alloy under Dry Sliding Contact /$cB. D. Bachchhav, H. Bagchi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aFrictional heating leads to sparking and excessive wear of components in engineering applications. Until now, copper-beryllium alloys have been used extensively in frictional contacts where nonsparking ability is desired. However, copper-beryllium creates an inhalation hazard when there is exposure to the dust or fumes from beryllium metal, metal oxides. Besides nonsparking ability, an environmentally friendly alternate material having equally good electrical and tribo-mechanical properties needs to be developed. In achieving the objective of this article, tribological properties of copper titanium alloy as an alternative under dry sliding contact were investigated and compared. Experiments were conducted on copper-titanium alloy having 2 % and 4.2 % titanium sliding against an EN-31 disk using a pin-on-disk apparatus. Taguchi-based design of experiments was used to find out significance of parameters and their effect on friction coefficient and wear rate. The microstructure was studied for distribution of titanium powder in alloy and its effect on grain distribution vis-à-vis tribo-properties using scanning electron microscopy analysis. It was found that the coefficient of friction decreases as titanium concentration and velocity increase. Titanium concentration has a significant effect on reducing wear. Results are indicative for potential use of copper-titanium alloy instead of copper-beryllium alloy. Because copper-titanium is a more recent material, its tribological properties are yet to be researched. Apparently, hardly any literature is available exclusively in this type of application. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aPrecipitation hardening. =650 \0$aCopper-titanium alloys. =650 \0$aAluminum-copper alloys. =700 1\$aBagchi, H.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200177.html =LDR 03762nab 2200553 i 4500 =001 MPC20210062 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210062$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210062$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.S62 =082 04$a620.1/12$223 =100 1\$aManikandan, S. G. K.,$eauthor. =245 10$aReview on Self-Healing Thermal Barrier Coatings for Space Applications /$cS. G. K. Manikandan, M. Kamaraj, C. Jebasihamony. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (29 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe demand for reusable space transportation systems is increasing, which leads to the need for higher-performance, reliable rocket engines at the lowest possible cost. The steep thermal gradient in the combustion chamber of rocket engines is catered by certain cooling mechanisms. In the case of reusable rocket engines, a progressive deformation and thinning of the cooling passage wall during engine operation is encountered because of the plastic ratcheting after numerous thermal cycles. This phenomenon may lead to the catastrophic failure of the engine when in operation and it also limits the number of operation cycles, adding cost. Thermal barrier coating (TBC) was successfully employed initially, and the functionally graded coatings were subsequently employed. However, the spallation of TBCs exists upon repeated thermal cycles. It is felt as necessary to induct the self-healing concept in such applications to enhance the number of thermal cycles. Various researchers have investigated crack-healing behavior of ceramic materials in recent years. This article provides a comprehensive analysis on the findings in the self-healing TBC and discusses future perspectives in this research area. This article mainly focusses on self-healing systems based on molybdenum disilicide (MoSi2)/MoSi2(B) with yttria partially stabilized zirconia and MCrAlY. In addition, the isothermal kinetics of MoSi2/MoSi2B and the formation of zircon are also discussed. The methodology of encapsulating the self-healing particles in order to avoid premature oxidation of MoSi2 self-healing particles is also discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aSelf-healing materials. =650 \0$aSpace sciences. =650 \0$aArtificial satellites in remote sensing. =700 1\$aKamaraj, M.,$eauthor. =700 1\$aJebasihamony, C.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210062.html =LDR 03762nab 2200553 i 4500 =001 MPC20210060 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210060$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210060$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTD491 =082 04$a628.1/44$223 =100 1\$aMopoung, Kunpot,$eauthor. =245 10$aRaman Spectroscopy Investigation of a Manganese Oxide Layer Caused by Water Corrosion on an IrMn Thin Film /$cKunpot Mopoung, Pattana Suwanyangyaun, Kanogkwan Sawaengsai, Laddawan Supadee, Noppadon Nuntawong, Sukkaneste Tungasmita, Sakuntam Sanorpim. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aRaman spectroscopy was used to identify a manganese oxide layer established on iridium manganese (IrMn) thin films. A thin manganese oxide layer on the IrMn surface was created by dropping deionized (DI) water for 30 min. Field emission scanning electron microscope and Raman spectroscopy with a 532-nm laser wavelength were used to investigate the DI-water–exposed IrMn surface. The intensity of the Raman laser beam, varied from 0.05 to 50 mW, was carefully optimized to avoid laser-induced heat effects on the manganese oxide layer and IrMn thin film. The results showed that the laser-induced heat produced an α-Mn3O4 phase on the IrMn surface and a manganese oxide layer at 25 mW. Raman optimization was used to investigate the DI-water corrosion and manganese oxide structures on different areas of the IrMn surface. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aRaman spectroscopy$xTechnique. =650 \0$aWater$xDistribution. =650 \0$aCorrosion and anti-corrosives$xTesting. =700 1\$aSuwanyangyaun, Pattana,$eauthor. =700 1\$aSawaengsai, Kanogkwan,$eauthor. =700 1\$aSupadee, Laddawan,$eauthor. =700 1\$aNuntawong, Noppadon,$eauthor. =700 1\$aTungasmita, Sukkaneste,$eauthor. =700 1\$aSanorpim, Sakuntam,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210060.html =LDR 03762nab 2200553 i 4500 =001 MPC20200050 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200050$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200050$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aR857.T55 =082 04$a610.28$223 =100 1\$aBanitaba, Seyedeh Nooshin,$eauthor. =245 10$aFabrication and Characterization of the Electrospun Polyvinyl Alcohol Nanofibers Incorporated with the Extracted Fruit Peel Pectin and Zinc Oxide Nanoparticles /$cSeyedeh Nooshin Banitaba, Arezou Khoshnama, Nazanin Poursharifi, Mina Nasari, Dariush Semnani, Maryam Jafari. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHerein, pomegranate, orange, and cantaloupe peel pectins were extracted. Then, nanofibrous membranes of polyvinyl alcohol (PVA)/pectin with various ratios (70:30, 80:20, and 90:10) were fabricated by using a standard electrospinning procedure. In the next step, various concentrations of zinc oxide (ZnO) nanofiller were introduced into the PVA/pectin electrospun fibers. Finally, the effects of pectin and ZnO ratios on morphology and mechanical characteristics of the electrospun fibers were evaluated. Based on the scanning electron microscopy images, thinner fibers were formed by an increase of the pectin and ZnO proportions in the electrospun fibers. According to the obtained Fourier-transform infrared spectroscopy (FTIR), all extracted pectins were high methoxy. In addition, complexation between the PVA polymer chains, extracted pectins, and ZnO particles was confirmed by FTIR spectra. Moreover, increase of the pectin and ZnO ratios led to fabrication of fibers with superior mechanical strength and lower strain. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aNanofibers. =650 \0$aElectrospinning. =650 \0$aTissue engineering. =700 1\$aKhoshnama, Arezou,$eauthor. =700 1\$aPoursharifi, Nazanin,$eauthor. =700 1\$aNasari, Mina,$eauthor. =700 1\$aSemnani, Dariush,$eauthor. =700 1\$aJafari, Maryam,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200050.html =LDR 03762nab 2200553 i 4500 =001 MPC20200183 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200183$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200183$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7871.15.S54 =082 04$a621.38152$223 =100 1\$aPerepezko, J. H.,$eauthor. =245 10$aMo-Silicide Alloys for High-Temperature Structural Applications /$cJ. H. Perepezko, M. Krüger, M. Heilmaier. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (24 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe challenges of a high-temperature environment (T > 1,400°C) impose severe material performance constraints in terms of melting point, oxidation resistance, and structural functionality. A number of ceramic materials, intermetallic compounds, and refractory metals with high melting temperatures are available as material choices. However, in a single-component single-phase form, these materials do not satisfy all the aforementioned requirements. One clear message from the evolutionary development of high-temperature alloys is the importance of developing multicomponent alloys with multiphase microstructures and the capability to control phase fractions and morphologies to satisfy a number of mechanical property requirements. Besides the essential structural requirements, elevated temperatures often also involve aggressive environments that require a material to display an inherent oxidation protection that can be further enhanced by coating. Among the leading candidates to advance beyond the capability of the current nickel (Ni)-base superalloys, the multiphase microstructures that can be developed in the molybdenum-silicon-boron (Mo-Si-B) system involving a high melting temperature (>2,100°C) ternary-based intermetallic Mo5SiB2 (T2) offer an attractive performance. Most of the attention has been on three-phase alloys comprised of Mo(ss), T2, and Mo3Si that offer high-temperature stability and robust microstructures, but new alloy designs are in development. In this review the recent advances in the development of Mo-silicide alloys are discussed in terms of alloy design, microstructure control, structural performance, environmental resistance, and component analysis. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aSilicides. =650 \0$aIntegrated circuits$xMaterials. =650 \0$aSilicon alloys. =700 1\$aKrüger, M.,$eauthor. =700 1\$aHeilmaier, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200183.html =LDR 03762nab 2200553 i 4500 =001 MPC20200166 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200166$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200166$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN780 =082 04$a669.3$223 =100 1\$aRajendran, Anbukkarasi,$eauthor. =245 10$aEffect of Axial Load-Dependent Deformation Rate on the Grain Size Distribution and Mechanical Properties of Friction Stir Processed Copper /$cAnbukkarasi Rajendran, Naresh Nadammal, Kuldeep Singh, Satish V. Kailas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDuring friction stir processing (FSP), the combination of rotation and movement of the tool leads to frictional heat generation and plastic deformation at the tool-material contact surface, leading to a microstructurally refined formation region. The deformation rate in the material can be altered by varying the axial load by increasing or decreasing the tool’s plunging depth. In the present study, FSP was carried out on a pure copper plate of 3-mm thickness by varying the plunge depth from 2.3 to 2.6 mm for a tool pin length of 2.4 mm. The microstructure of the processed samples was studied by optical microscopy, and the grain size was measured by the linear intercept method. Tensile testing was carried out perpendicular to the processing direction. The grain size distribution was narrower at low axial loads and wider at the higher axial loads, measured between 1 and 120 µm. At higher axial loads, microstructure consisted of bands indicative of the heterogeneity in the deformation. The formation of bands at higher axial loads leads to improved mechanical properties. The ductility of the processed materials at higher axial loads was 16%, which was four times the increase observed at lower axial loads (4%). The formation of a bi-modal microstructure (alternating layers of fine and coarse grains) at high axial load enhanced the processed materials’ strength and ductility. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCopper$xMetallurgy. =650 \0$aCopper$xMagnetic properties. =650 \0$aCopper$xThermal properties. =700 1\$aNadammal, Naresh,$eauthor. =700 1\$aSingh, Kuldeep,$eauthor. =700 1\$aKailas, Satish V.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200166.html =LDR 03762nab 2200553 i 4500 =001 MPC20200172 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200172$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200172$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA483 =082 04$a620.16$223 =100 1\$aEdachery, Vimal,$eauthor. =245 10$aEnhancing Tribological Properties of Inconel X-750 Superalloy through Surface Topography Modification by Shot Blasting /$cVimal Edachery, Aashish John, Anbukkarasi Rajendran, Vivek Srinivasappa, Sribalaji Mathiyalagan, Santosh Kumar, Satish Vasu Kailas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe profound usage of Inconel X-750 in structural and high-pressure conditions mandates improved tribological properties. One of the methods to achieve this is through surface topography modifications. In this work, the viability of the shot blasting technique is explored to enhance the wear resistance of Inconel X-750. For this purpose, aluminum oxide particles with 80 mesh size were shot blasted on the superalloy surface at a constant pressure of 0.6 MPa. The 3D surface topography of Inconel X-750 alloy confirms substantial surface deformation and increased surface roughness after shot blasting. Furthermore, the surface characteristics of shot-blasted superalloy were meticulously examined using a string of techniques: optical profilometer, scanning electron microscope, and electron probe microanalysis. The tribological properties of Inconel X-750 before and after shot blasting were examined using a reciprocating tribometer with a ball-on-flat configuration. Results showed that shot blasting the superalloy has tremendously enhanced the wear resistance by ∼78%, which could be attributed to the reduced sliding contact area, enhanced surface hardness, and the hindrance in the transition of wear mechanism from abrasion tribo-oxidation to adhesion. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aAlloys. =650 \0$aMetals. =650 \0$aMechanical alloying. =700 1\$aJohn, Aashish,$eauthor. =700 1\$aRajendran, Anbukkarasi,$eauthor. =700 1\$aSrinivasappa, Vivek,$eauthor. =700 1\$aMathiyalagan, Sribalaji,$eauthor. =700 1\$aKumar, Santosh,$eauthor. =700 1\$aKailas, Satish Vasu,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200172.html =LDR 03762nab 2200553 i 4500 =001 MPC20200138 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200138$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200138$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN698 =082 04$a671.37$223 =100 1\$aUmezawa, Osamu,$eauthor. =245 10$aReview of the Mechanical Properties of High-Strength Alloys at Cryogenic Temperatures /$cOsamu Umezawa. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTo advance the understanding of metallic materials for structural components at cryogenic temperatures, a review of previous studies on the mechanical properties of austenitic stainless steels, titanium alloys, aluminum alloys, and copper alloys is presented herein. In particular, the evaluation of strength and toughness balance intends to clarify key differences between these alloys to facilitate better alloy design and potentially bolster further alloy development. Several key points on cryogenic mechanical tests are also introduced. Temperature control, testing tools, and test conditions should be properly calibrated to avoid experimental errors. Furthermore, substantial progress for subsurface crack initiation in high-cycle fatigue at cryogenic temperatures is presented, in which the mechanism of subsurface crack generation is highlighted as a key design consideration in microstructure of high-strength alloys. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aStrength of materials. =650 \0$aMetals. =650 \0$aAlloys. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200138.html =LDR 03762nab 2200553 i 4500 =001 MPC20200167 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200167$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200167$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aLD4330 =082 04$a620$223 =100 1\$aMukherjee, Shreya,$eauthor. =245 10$aCreep-Fatigue Behavior of a Newly Developed Ultra-Supercritical Steam Turbine Grade Nickel-Based Superalloy, HAYNES 282 /$cShreya Mukherjee, Kaustav Barat, Soumitra Tarafder, S. Sivaprasad, Sujoy Kumar Kar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMost engineering components used in gas/steam turbines are exposed to a range of complex loading conditions resulting from startup and shutdown procedures. These loading conditions involve superimposition of time-dependent creep on cyclic fatigue and can be simulated by properly designed high-temperature creep-fatigue tests. Creep-fatigue interaction is a function of duration and position of dwell in the loading waveform, and the material microstructure. The objective of this work is to investigate the creep-fatigue interaction response of a newly developed γ′-strengthened wrought nickel-based superalloy (HAYNES 282), which has a potential application in advanced ultra-supercritical steam turbines. Creep-fatigue tests are conducted at 760°C with strain dwell either at tensile peak or compressive peak or at both tensile and compressive peak positions for different dwell times of 100 and 1,000 s. The test results are analyzed with respect to evolutions of peak stress, stress amplitude, stress relaxation, hysteresis loop, inelastic strain energy density, and degree of softening. Degree of softening is found to increase with dwell position at tensile, compressive, and both peaks in that order. Tests with dwell at both tensile and compressive peak positions are found to be the most damaging, showing the least life. Between tensile dwell and compressive dwell tests, interestingly, those with compressive dwell show a significantly reduced life. Increasing dwell time aggravates the damaging effect manifold. The mechanism of fracture at the end of life is illustrated with fractographic characterization. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aNickel alloys$xCracking. =650 \0$aNickel alloys$xFatigue. =650 \0$aSteam-turbines$xMaterials$xFatigue. =700 1\$aBarat, Kaustav,$eauthor. =700 1\$aTarafder, Soumitra,$eauthor. =700 1\$aSivaprasad, S.,$eauthor. =700 1\$aKar, Sujoy Kumar,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200167.html =LDR 03762nab 2200553 i 4500 =001 MPC20200178 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200178$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200178$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ778 =082 04$a621.43/3$223 =100 1\$aKulkarni, Anand,$eauthor. =245 10$aAdvanced Materials and Manufacturing Technology Developments for Extreme Environment Gas Turbine Applications /$cAnand Kulkarni, Allister James, Ahmed Kamel. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aElectrical power generation is becoming increasingly reliant on gas turbines with multiple fuel capability, with research advances focusing on increased efficiency/power output and reduced emissions. Increasing gas turbine efficiency primarily requires higher operating temperatures and reduced coolant flow in the turbine flow path, which makes it challenging to increase component performance, as these will encounter high stresses and large temperature gradients. Current nickel-based alloys, which operate at operate at extreme environments, are exposed to stress caused by temperature or static/dynamic loading like creep and fatigue, oxidation and corrosion, wear, and damage due to vibrations. Higher turbine inlet temperatures are currently managed with internal/film cooling and thermal/environmental barrier coatings for hot section parts. Comprehensive solutions are needed to translate to achieve ultrahigh efficiencies, lower parts cost, reduced scrape rate, and life cycle savings. The paper discusses material developments coupled with innovative manufacturing approaches to be married with advanced design strategies to realize the needed improvements for hot gas path components. The case studies for combustion and turbine components will be presented to demonstrate the structure property relationships and improved component performance at lower cost. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aGas-turbines$vHandbooks, manuals, etc. =650 \0$aGas-turbines$xAerodynamics. =650 \0$aGas-turbines. =700 1\$aJames, Allister,$eauthor. =700 1\$aKamel, Ahmed,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200178.html =LDR 03762nab 2200553 i 4500 =001 MPC20200161 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200161$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200161$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL521 =082 04$a621.38152$223 =100 1\$aKumar, Shobhit,$eauthor. =245 10$aDevelopment of C/SiC Fasteners for High-Temperature Applications /$cShobhit Kumar, Anil Painuly, Anurag Kamal, Sajimon Kuttappan, Ravi Ranjan Kumar, Shyin Palani Prabhakaran, Renjith Devasia. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aContinuous carbon fiber reinforced silicon carbide (C/SiC) ceramic matrix composites are the candidate materials for high-temperature structural applications owing to their high specific strength, low coefficient of thermal expansion, and moderate thermal conductivity. C/SiC based fasteners provide reliability with oxidation resistance up to 1,650°C for joining such C/SiC structural components used in reusable launch vehicles for space applications. The present study describes the methodology to realize C/SiC based M8 fasteners by isothermal-isobaric chemical vapor infiltration process using 2D-stitched carbon fabric preforms. The realized fasteners exhibited a density of 2.10 g/cm3, a tensile strength of 191 ± 3 MPa, a shear strength of 230 ± 69 MPa in non-threaded and 150 ± 86 MPa in threaded regions of shank at room temperature, a high-temperature tensile strength of 170 ± 12 MPa, and a tensile modulus of 70 ± 8 GPa at 1,100°C in the atmospheric conditions. The tensile failure of the C/SiC bolts was observed to depend upon the relative dimensions of fillet radius and thread root radius, wherein a small fillet radius was observed to be detrimental, as it resulted in failure at the head-shank interface of the bolts. The scanning electron microscope images of tensile tested C/SiC bolts indicate extensive fiber pullout, characteristic of quasi-ductile failure of bolts. It is clearly evident from the studies that the C/SiC fasteners are a promising alternative over the currently used molybdenum alloy fasteners. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aChemical engineering$vCongresses. =650 \0$aChemical engineering. =650 \0$aSilicon solar cells$xPerformance. =700 1\$aPainuly, Anil,$eauthor. =700 1\$aKamal, Anurag,$eauthor. =700 1\$aKuttappan, Sajimon,$eauthor. =700 1\$aKumar, Ravi Ranjan,$eauthor. =700 1\$aPrabhakaran, Shyin Palani,$eauthor. =700 1\$aDevasia, Renjith,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200161.html =LDR 03762nab 2200553 i 4500 =001 MPC20200145 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200145$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200145$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS653 =082 04$a667.9$223 =100 1\$aVetrivendan, E.,$eauthor. =245 10$aDevelopment of Silicon Carbide Interlayers for Plasma Spray Yttria Topcoat on Graphite for High-Temperature Applications /$cE. Vetrivendan, B. Madhura, Ch. Jagadeeswara Rao, S. Ningshen, U. Kamachi Mudali. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPlasma-sprayed yttria (Y2O3) coatings on commercial high-density graphite (HDG) as a chemical barrier coating are presently being explored for uranium-zirconium alloy melting crucibles in pyrochemical reprocessing of spent metallic fuel of future fast breeder reactors. The performance and durability of Y2O3 coatings for high-temperature exposure up to 1,823 K for multiple batch operations are critical to reducing solid active waste generation. However, plasma-sprayed Y2O3 coatings on HDG experience large thermal mismatch stresses due to the difference in the coefficient of thermal expansion (CTE) value of ∼8 × 10−6 K−1 for Y2O3 and ∼4 × 10−6 K−1 for HDG, combined with partial active oxidation of HDG interface leading to premature cracking and spallation of the coating. Silicon carbide (SiC) coating with intermediate CTE (∼6 × 10−6 K−1) offers superior oxidation protection for HDG, which can suitably be used as an interlayer to improve the durability of Y2O3 coatings. In the present work, SiC interlayer coating is developed on HDG substrates using conventional coating techniques such as pack cementation and chemical vapor deposition techniques for subsequent deposition of Y2O3 topcoat by plasma spraying. The thermal fatigue studies simulating uranium melting condition by isothermal hold at 1,723, 1,773, and 1,823 K for 1 h showed twofold improvements in the life of Y2O3 coatings with SiC interlayer. The evolution of thermal cycling damage and failure mechanisms are discussed. The role of interfacial microstructure, the stability of phases, and the underlying mechanisms for life enhancement in the presence of SiC interlayer for plasma-sprayed Y2O3 coating for high-temperature applications are highlighted. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aPlasma spraying. =650 \0$aMetal spraying. =650 \0$aChemical engineering. =700 1\$aMadhura, B.,$eauthor. =700 1\$aJagadeeswara Rao, Ch.,$eauthor. =700 1\$aNingshen, S.,$eauthor. =700 1\$aKamachi Mudali, U.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200145.html =LDR 03762nab 2200553 i 4500 =001 MPC20200171 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200171$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200171$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN697.T5 =082 04$a669.7$223 =100 1\$aSreejith, K. J.,$eauthor. =245 10$aPreparation of Titanium-Aluminum-Carbon MAX Phase via a Simple Precursor Route for High-Temperature Coating Applications /$cK. J. Sreejith, Vipin Vijay, T. Jayalatha. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMAX phase materials are gaining increased research interest because of the unique combination of metallic and ceramic properties. For high-temperature applications, titanium-aluminum-carbon (MAX) phases are extensively investigated. In order to utilize these MAX phase materials as coatings for high-temperature space applications, a pressureless preparation route employing a polymer-based precursor would be advantageous. A cost-effective, pressureless synthetic route using a carbonaceous polymer-based slurry was explored to obtain titanium-alumnium-carbon MAX phase. In continuation of our earlier report on the preliminary investigations on a precursor system, in the present study, an investigation on the effect of (i) heat treatment duration and (ii) nucleating filler on the formation of titanium-aluminum-carbon MAX phase from the precursor was carried out. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aTitanium alloys$xTesting. =650 \0$aTitanium-aluminum-vanadium alloys$xTesting. =650 \0$aTitanium alloys. =700 1\$aVijay, Vipin,$eauthor. =700 1\$aJayalatha, T.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200171.html =LDR 03762nab 2200553 i 4500 =001 MPC20200193 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200193$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200193$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS227.6 =082 04$a624.1821$223 =100 1\$aAnoop, C. R.,$eauthor. =245 10$aA Review on Steels for Cryogenic Applications /$cC. R. Anoop, R. K. Singh, Ravi Ranjan Kumar, M. Jayalakshmi, T. Antony Prabhu, K. Thomas Tharian, S. V. S. Narayana Murty. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (73 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCryogenic systems have played a crucial role in almost all of the finest technological achievements of mankind. Cryogenic applications demand materials with a unique combination of properties, which drastically limits the choice of materials. In most other engineering applications, because of wide tailorability of their properties and excellent combination of strength and toughness, coupled with lower cost compared with nonferrous materials, steels have become the preferred/dominant structural material for cryogenic applications. The contradictory requirement of higher strength without compromising toughness at cryogenic temperatures posed considerable challenges and led to the development of large array of steels tailored for specific applications. This review is an attempt to survey the metallurgical aspects, material selection, mechanical property evaluation, and application of various standard and nonstandard steels for cryogenic applications. This review covers the influence of low temperatures on material properties, simulative mechanical tests for property evaluation, metallurgy of steels, and application examples surveying the published literature to date. The review also analyzes the origins of low-temperature toughness, various application requirements, and the work carried out at authors’ laboratories. The issues pertaining to mechanical tests at low temperatures and status of data generation in international scenario have been critically analyzed. Physical metallurgy aspects have been highlighted in the review, and microstructure-property-processing correlations for various steels have also been covered. One of the recent advances in steels for cryogenic applications, high-entropy alloys, which are proposed as alternatives for the conventional steels, have been reviewed, and mechanical property data have been critically analyzed. The potential of additive manufactured steels for low-temperature applications has been reviewed. Finally, this review article discusses challenges in processing–mechanical properties correlation for various grades of steels for cryogenic applications. It also provides useful information for researchers working on steels for cryogenic applications with a glimpse of recent advances made in this area. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aWelding$xResearch. =650 \0$aSteel, Structural. =650 \0$aSteel. =700 1\$aSingh, R. K.,$eauthor. =700 1\$aKumar, Ravi Ranjan,$eauthor. =700 1\$aJayalakshmi, M.,$eauthor. =700 1\$aAntony Prabhu, T.,$eauthor. =700 1\$aThomas Tharian, K.,$eauthor. =700 1\$aNarayana Murty, S. V. S.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200193.html =LDR 03762nab 2200553 i 4500 =001 MPC20200083 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200083$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200083$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA483 =082 04$a620.16$223 =100 1\$aSonar, Tushar,$eauthor. =245 10$aInfluence of InterPulsed TIG Welding Parameters on the Evolution of Microstructure and Tensile Properties of Su-718 Alloy Sheets /$cTushar Sonar, Visvalingam Balasubramanian, Sudersanan Malarvizhi, Thiruvenkatam Venkateswaran, Dhenuvakonda Sivakumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (31 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSuperalloy 718 (Su-718) is a high-performance nickel-based alloy typically employed in high-temperature applications of aero-engine components. It is mostly joined by the Tungsten Inert Gas (TIG) welding process for clean and precise joints. However, the joints are more prone to premature failure owing to the metallurgical problems during solidification, such as constitutional segregation in the fusion zone (FZ) and microfissuring in the heat affected zone (HAZ). To overcome these problems, in this investigation, a recently emerged InterPulsed TIG (IP-TIG) welding process was utilized for joining Su-718 alloy. It is the advanced variant of the TIG welding process principally differentiated by electromagnetic condensation of the arc and high-frequency pulsation up to 20 kHz. The primary objective of this study is to make the potential use of electromagnetic condensation of the arc and pulsation for minimizing the Laves phase growth in FZ and enhancing the tensile strength of joints. To achieve this, the effect of IP-TIG welding parameters on evolution of the microstructure and tensile properties of Su-718 alloy joints is investigated and the results are analyzed in detail in this paper. The analysis of microstructural features was done using optical microscopy, scanning electron microscopy, and Energy Dispersive X-ray Spectroscopy techniques. The influence of Laves phase morphology on the strength and elongation of joints is revealed and correlated to the fracture surface. The principal mechanism responsible for changes in microstructural features and consequential influence on tensile behavior of joints is explained briefly and correlated to the cooling rate and heat input conditions during welding. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aAlloys. =650 \0$aMetals. =650 \0$aMechanical alloying. =700 1\$aBalasubramanian, Visvalingam,$eauthor. =700 1\$aMalarvizhi, Sudersanan,$eauthor. =700 1\$aVenkateswaran, Thiruvenkatam,$eauthor. =700 1\$aSivakumar, Dhenuvakonda,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200083.html =LDR 03762nab 2200553 i 4500 =001 MPC20200146 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200146$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200146$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN799.Z5 =082 04$a620$223 =100 1\$aPatel, Vivek,$eauthor. =245 10$aPrediction of Long-Term Creep Properties of Zirconium-2.5 % Niobium Alloy Using Wilshire Method /$cVivek Patel, R. N. Singh, Madangopal Krishnan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aZirconium-2.5 % niobium alloy, used as a pressure tube material in pressurized heavy water reactors, have to experience extreme stress, temperature, and radioactive conditions to serve within the designed dimensional tolerance limit. Prolonged duration under high stress and high temperature causes the creep deformation, ultimately leading to deformation beyond the permitted limit or interference with other components, or both. Hence, a priori using particular material for a specific application, mechanical testing has to be done to investigate its deformation behavior. However, creep tests of material can last from a few hours to several months or even years. The cost of testing the material can eventually impact the cost of the component. Instead of carrying out long-term creep tests, an extrapolation technique named the Wilshire method is applied to predict the creep behavior of the material under any given test conditions. This method is also capable of reconstructing the complete creep curve using the data from accelerated creep tests. Such an approach can drastically scale down the cost and time required for the long-term creep tests. In the present study, zirconium 2.5 % niobium alloy, which is used as pressure tube material in pressurized heavy water reactors, is employed as a test material for the analysis using the Wilshire method. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aZirconium$xMetallurgy. =650 \0$aMetals$xHeat treatment. =650 \0$aMetals$xMechanical properties.Niobium alloys. =700 1\$aSingh, R. N.,$eauthor. =700 1\$aKrishnan, Madangopal,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200146.html =LDR 03762nab 2200553 i 4500 =001 MPC20200133 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200133$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200133$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.118$223 =100 1\$aSonber, J. K.,$eauthor. =245 10$aProcessing of ZrB 2 - and HfB 2 -Based Ultra-High Temperature Ceramic Materials :$bA Review /$cJ. K. Sonber, T. S. R. Ch. Murthy, Sanjib Majumdar, Vivekanand Kain. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (33 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aZrB2 and HfB2 are leading materials in the category of ultra-high temperature ceramics (UHTCs). UHTCs are a group of ceramic materials that can withstand ultra-high temperature (>2,000°C) in oxidizing conditions. Such a high temperature will be encountered by future hypersonic reentry vehicles. Future reentry vehicles will have sharp edges to improve aerodynamic performance. The sharp leading edges will cause higher surface temperature than that of the actual blunt-edged vehicles. The sharp edges have less surface area to dissipate heat and thus the temperature gets increased. To withstand the intense heat generated when these vehicles reenter the earth’s upper atmosphere, UHTC materials are needed. UHTC materials are composed of borides of early transition metals. From the larger list of borides, ZrB2 and HfB2 have received the most attention as potential candidates for leading edge materials because their oxidation resistance is superior to that of other borides because of the stability of the ZrO2 and HfO2 scales that form on these materials at elevated temperatures in oxidizing environments. Processing of these materials is very difficult because these materials are very refractory in nature. Powder synthesis usually involves high-temperature solid state reactions. Dense bodies are generally produced by hot pressing and spark plasma sintering. For coating preparation, plasma spray, chemical vapor deposition, and physical vapor deposition is used. All these processing methods for ZrB2 and HfB2 are difficult because of the involvement of very high temperatures. In this review, the present state of the knowledge on processes employed for powder synthesis, fabrication of dense bodies, and coating processes is discussed. The advantages, limitations, and challenges in the different processing methods are addressed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCeramic-matrix composites$vCongresses. =650 \0$aHeat resistant materials$vCongresses. =650 \0$aFiber-reinforced ceramics$vCongresses. =700 1\$aMurthy, T. S. R. Ch.,$eauthor. =700 1\$aMajumdar, Sanjib,$eauthor. =700 1\$aKain, Vivekanand,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200133.html =LDR 03762nab 2200553 i 4500 =001 MPC20200131 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200131$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200131$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK7871.15.S56 =082 04$a621.38152$223 =100 1\$aHarrison, Shay,$eauthor. =245 10$aHigh-Temperature Performance of Next-Generation Silicon Carbide Fibers for CMCs /$cShay Harrison, John Schneiter, Joseph Pegna, Erik Vaaler, Ramkiran Goduguchinta, Kirk Williams. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSingle-fiber (monofilament, not twisted tow) high-temperature creep performance of refractory ceramic compositions is a fundamental material property that must be examined and understood for the successful deployment of ceramic matrix composite material systems in demanding applications. A novel creep testing approach was devised utilizing an innovative approach to fiber sample attachment and used to evaluate the creep behavior of Free Form Fibers’ LP-30SC and Nippon Carbon-based Hi-Nicalon Type S (HNS) silicon carbide fiber products. The testing apparatus, analytical basis for the creep calculations, including the sample gage length, and collected data are presented. Test conditions include a range of peak hold temperatures, from 1,300°C to 1,500°C, gas environments, and hold time patterns at the peak temperature. Clear differences in resistance to creep degradation were evident between the LP-30SC and HNS fibers, as the LP-30SC demonstrated strong resiliency to high temperature exposure while the HNS showed performance degradation consistent with oxidation attack. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aSilicon carbide. =650 \0$aSemiconductors. =650 \0$aMicroelectromechanical systems. =700 1\$aSchneiter, John,$eauthor. =700 1\$aPegna, Joseph,$eauthor. =700 1\$aVaaler, Erik,$eauthor. =700 1\$aGoduguchinta, Ramkiran,$eauthor. =700 1\$aWilliams, Kirk,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200131.html =LDR 03762nab 2200553 i 4500 =001 MPC20200157 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200157$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200157$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN693.T5 =082 04$a620.189322$223 =100 1\$aThammaiah, B. R.,$eauthor. =245 10$aHigh Strain Rate Behavior of GTM-900 Titanium Alloy /$cB. R. Thammaiah, Chandru D. Fernando, Anuradha Nayak Majila, A. R. Anilchandra, M. S. Nandana, Udaya K. Bhat, C. M. Manjunatha. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aGTM-900 is an α + β alloy of titanium used in low-pressure (LP) compressor blades of gas turbine (GT) engines. The maximum allowable operating temperature of this alloy is 500°C. Silicon is added to enhance the creep resistance at elevated temperatures. The aim of this work is to establish the microstructural stability of this alloy and determine the high strain rate Johnson-Cook (J-C) material parameters such as A, B, and n. The material parameters are subsequently used by designers to simulate the “blade-off” and “casing containment” capability of the LP compressor blade. Split Hopkinson tensile bar was used to conduct high strain rate tests at about 2,000 s−1, and at three different temperatures, viz., 25°C, 300°C, and 500°C, to simulate critical conditions. Data obtained from these testing were used to construct a J-C model. Flow stress increased with an increase in strain rate and decreased with an increase in temperature because of thermal softening. Characterization, using optical and electron microscopes, indicated that the microstructure was stable even after the deformation at 500°C. The presence of needle-like silicide phase was observed under transmission electron microscopy and the composition was verified with X-ray diffraction results. A high strain hardening rate was observed even at elevated temperatures in this alloy (n ≈ 0.54 at 2,000 s−1 and 500°C) compared to Ti-6Al-4V titanium alloy (n ≈ 0.28). Considering good strength and microstructural stability up to 500°C, the present material offers to be an attractive alternate to other contemporary titanium alloys currently used in GT engine applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aTitanium alloys. =650 \0$aAlloys. =650 \0$aMaterials. =700 1\$aFernando, Chandru D.,$eauthor. =700 1\$aMajila, Anuradha Nayak,$eauthor. =700 1\$aAnilchandra, A. R.,$eauthor. =700 1\$aNandana, M. S.,$eauthor. =700 1\$aBhat, Udaya K.,$eauthor. =700 1\$aManjunatha, C. M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200157.html =LDR 03762nab 2200553 i 4500 =001 MPC20200125 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200125$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200125$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.C37 =082 04$a672.52$223 =100 1\$aNagai, Kotobu,$eauthor. =245 10$aEvaluation of Fire Resistance for a Recycled 0.15 mass% Carbon Steel /$cKotobu Nagai, Satoru Terayama. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA recycled steel with 0.2 % offset stress higher than 295 MPa was verified as a candidate for fire-resistant use, based on an academic standard in Japan. The chemical compositions were 0.15 mass% carbon-0.02 mass% silicon-0.5% mass% manganese and unavoidable alloy elements. The amount of elements inevitably contained in recycling was kept within the regulation, and then the dispersion of tensile properties among hot coils was controlled to be sufficiently small. The recycled steel satisfied the requirements by the academic standard in terms of tensile properties at elevated temperatures. No significant evolution was observed in the ferrite-based microstructure within the temperature and time range tested. The plastic deformation is apparently a strain-controlled one up to 400°C and a strain rate-controlled one at 600°C and 700°C. At 500°C, it is in the middle of the two. In the adopted test method, a constant strain rate was realized over the entire strain range except for the beginning stage of deformation. A peak strain rate occurs at about 0.2 % strain, which brings about the uncertainty in determination of 0.2 % offset stress at elevated temperatures. However, the constant strain rate requirement is satisfied in the determination of 1 % offset stress that the academic standard specifies. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCarbon steel. =650 \0$aCarbon steel$xMetallurgy. =650 \0$aSteel. =700 1\$aTerayama, Satoru,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 10, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200125.html =LDR 03762nab 2200553 i 4500 =001 MPC20200152 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200152$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200152$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.A88 =082 04$a620.1723$223 =100 1\$aDas, Annesha,$eauthor. =245 10$aStress Corrosion Cracking in Austenitic Stainless Steels in Reactor Primary Water–High Purity Oxidizing and in Supercritical Conditions /$cAnnesha Das, Supratik Roychowdhury, Vivekanand Kain. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAustenitic stainless steels (SS) commonly used in the primary circuit of light water reactors (LWRs) have excellent corrosion resistance in demineralized (DM) water at high temperature (290°C–330°C) and pressure (7.4 MPa for boiling water reactor [BWR], 16 MPa for pressurized water reactor [PWR]). Radiolysis of primary DM water in BWR forms 200–300 ppb of oxidizing species (normal water chemistry [NWC]), which elevates the electrochemical potential of the SS from −300 to −600 mVSHE (mV with standard hydrogen electrode) when dissolved oxygen is 10–20 ppb to +100 to +200 mVSHE. Neutron irradiation of SS further induces metallurgical and microstructural changes, which compromises corrosion resistance. Thus, radiation makes BWR (NWC) environment hostile, causing extensive irradiation-assisted stress corrosion cracking (same as intergranular stress corrosion cracking [IGSCC]) in austenitic SS. IGSCC occurs in both sensitized (grain boundary chromium depletion) and nonsensitized conditions (strain-hardened region in base metal immediately adjacent to the weld fusion zone) and is a generic problem. IGSCC in BWR can be mitigated by hydrogen addition in water (hydrogen water chemistry [HWC]). BWR-HWC has limitations and is ineffective where boiling occurs. IGSCC of SS in PWR is limited because hydrogen addition in primary water suppresses radiolysis though the formation of aggressive environment in low-flow occluded regions can cause IGSCC in SS. Increasing demand for economic power has led to the primary environment in nuclear reactors to become hostile. Conceptual supercritical water reactor (SCWR) will use DM water at 500°C–600°C and 25 MPa, which is extreme for conventional LWR materials. IGSCC in austenitic SS and nickel-based alloys occurs in both oxidizing and reducing SCWR conditions, which can be further exacerbated by radiation. This article reviews how benign primary DM water becomes hostile in LWRs and extreme in SCWR conditions, causing SCC to be a generic problem in austenitic alloys. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCorrosion and anti-corrosives. =650 \0$aSteel$xCorrosion. =650 \0$aAustenitic stainless steel$xCorrosion. =700 1\$aRoychowdhury, Supratik,$eauthor. =700 1\$aKain, Vivekanand,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200152.html =LDR 03762nab 2200553 i 4500 =001 MPC20200148 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200148$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200148$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.M3 =082 04$a620.18623$223 =100 1\$aKumar, K. Pradeep Prem,$eauthor. =245 10$aImproving the Corrosion Resistance of Magnesium Alloy AZ31 by a Duplex Anodized and Sol-Gel Coating /$cK. Pradeep Prem Kumar, R. Subasri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMagnesium and its alloys have found application in several areas viz., aerospace, electronics industry, and automobile, owing to their specific strength-to-weight ratio, thermal conductivity, electromagnetic shielding, etc. However, poor corrosion resistance limits their applicability for widespread use. Anodization and micro arc oxidation (MAO) are commonly used to enhance the corrosion protection of magnesium alloys. The anodized or MAO layers are porous, and hence, organic sealants are conventionally used for sealing the pores. There are not many reports on the use of organic-inorganic hybrid coatings as sealants on anodized layers of magnesium alloys. In this study, the hybrid sol-gel silica-based coatings were investigated as sealants on anodized magnesium alloy AZ31 substrates. A thick (∼20 µm) and porous oxide layer was deposited by anodization using sodium silicate as electrolyte. Ambient curable hybrid silica coatings with and without corrosion inhibitors like cerium oxide and 8-hydroxyquinoline were deposited by dip coating method. The anodized layer and the duplex coating were analyzed using X-ray diffraction and field emission scanning electron microscopy with energy-dispersive X-ray analysis (EDAX) attachment. Electrochemical impedance spectroscopy and potentiodynamic polarization studies were used to assess the corrosion protection performance of these coatings in 0.61M NaCl solution. The porous anodized magnesium oxide layer improved the binding strength of the adjacent sol-gel layer; the sol-gel layer physically sealed the porous anodized coating and offered higher corrosion protection. The duplex coating prevented the diffusion of aggressive ions onto the magnesium alloy AZ31 and enhanced the corrosion resistance significantly. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aCorrosion and anti-corrosives. =650 \0$aMagnesium alloys$xCorrosion. =650 \0$aMagnesium alloys. =700 1\$aSubasri, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200148.html =LDR 03762nab 2200553 i 4500 =001 MPC20200174 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200174$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200174$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA485 =082 04$a620.16$223 =100 1\$aStewart, Calvin M.,$eauthor. =245 10$aAccelerated Creep Testing of Inconel 718 Using the Stepped Isostress Method (SSM) /$cCalvin M. Stewart, Md Abir Hossain, Jacob Pellicotte, Robert Mach, David Alexander, Sanna F. Siddiqui. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis paper demonstrates the stepped isostress method (SSM), an accelerated creep test (ACT) for the rapid assessment of metallic materials. The SSM test is based on the time-temperature-stress superposition principle in which temperature, stress, or both, are step increased to accelerate the time to rupture. The SSM test has proven successful for the ACT of polymers and polymeric composites but has yet to be proven for metallic materials. In this study, new test matrix design rules for the SSM of metals are established based on deformation mechanism, time-temperature transformation, and time-temperature precipitation maps. A test matrix of SSM and conventional creep tests (CCTs) are executed for alloy Inconel 718 at 750°C (1,382°F) with stress levels ranging from 100 to 350 MPa. Validation CCT data are gathered from the Japan National Institute of Material Science. Material constants for the Sine-hyperbolic (Sinh) constitutive model are calibrated using the SSM data and employed to predict the conventional creep response. When blindly compared with the CCT data, the SSM-calibrated Sinh model can accurately predict the conventional creep response across logarithmic decades and, thus, accelerate the capture of conventional creep data. Fractography indicates ductile fracture by transgranular microvoid coalescence with the same fracture mode observed in both SSM and CCT specimens. Creep cavitation is indicated by the population, smoothness, and size of microvoids. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aInconel. =650 \0$aHeat resistant alloys. =700 1\$aHossain, Md Abir,$eauthor. =700 1\$aPellicotte, Jacob,$eauthor. =700 1\$aMach, Robert,$eauthor. =700 1\$aAlexander, David,$eauthor. =700 1\$aSiddiqui, Sanna F.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200174.html =LDR 03762nab 2200553 i 4500 =001 MPC20200168 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200168$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200168$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN757.A6 =082 04$a672$223 =100 1\$aZala, Arunsinh B.,$eauthor. =245 10$aStudy of Weldability for Aluminide Coated Steels through A-TIG Welding Process /$cArunsinh B. Zala, N. I. Jamnapara, Vishvesh J. Badheka, C. S. Sasmal, Shiju Sam, Mukesh Ranjan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTo achieve higher efficiency in high-temperature environments, 9Cr-1Mo steels (also known as P91 steels) are promising candidates in power plants, petrochemical industries, heat exchangers, and nuclear applications. To enhance the performance against harsh environments, such as high-temperature oxidation and corrosion during operations, adding aluminum oxide (Al2O3)/iron aluminide (FeAl) coating through the aluminizing process has been found promising. Such coatings have been considered reliable for resistance to liquid-metal corrosion against flowing lead-lithium liquid breeders and against tritium permeation in blanket modules of fusion reactors. However, the welding process for aluminized coated steels is a challenge and is scarcely reported. The aluminum-rich coating at the top may alter the metallurgy of weld metal and subsequently the mechanical properties after welding. To investigate the same, preliminary bead-on-plate trials with a novel activated-tungsten inert gas welding process has been attempted for the first time. Bead-on-plate welding samples were prepared (with the same welding parameters) with five different fluxes, such as iron (III) oxide (Fe2O3), nickel (II) oxide (NiO), copper (II) oxide (CuO), cobalt tetroxide (Co3O4), and Al2O3, for aluminized coated 9Cr-1Mo steel. The resultant weld metal microstructure was evaluated using optical and electron microscopy, elemental analysis using energy-dispersive X-ray spectroscopy, phase analysis using X-ray diffraction, and Vickers hardness testing. It was observed that the presence of oxide-type fluxes results in arc constriction, which thereby affects the depth of penetration. The weld metal prepared with Fe2O3 flux demonstrates a superior depth-to-width ratio compared to other fluxes. An analysis for delta ferrite was also carried out and was observed to be present in Fe2O3 flux welds only. A detailed analysis of the weld metal under different activated fluxes is presented in the paper. The outcome of this work presents the feasibility of the welds of aluminized 9Cr steels as relevant for fusion reactor applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aSteel-aluminum alloys. =650 \0$aIron-aluminum alloys. =650 \0$aAluminum coating. =700 1\$aJamnapara, N. I.,$eauthor. =700 1\$aBadheka, Vishvesh J.,$eauthor. =700 1\$aSasmal, C. S.,$eauthor. =700 1\$aSam, Shiju,$eauthor. =700 1\$aRanjan, Mukesh,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200168.html =LDR 03762nab 2200553 i 4500 =001 MPC20200156 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200156$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200156$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.9.C6 =082 04$a620.11$223 =100 1\$aKumar, Sanjeev,$eauthor. =245 10$aCorrosion Behavior of Surface Nanostructured IN718 Superalloy at 650°C /$cSanjeev Kumar, K. Chattopadhyay, Z. Alam, Vakil Singh, D. V. V. Satyanarayana, Vikas Kumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present study, the process of ultrasonic shot peening (USP) was adopted for developing nanostructures with a grain size of 62 ± 10 nm on the surface of the alloy IN718. The effect of nanostructures was investigated on high-temperature corrosion behavior under cyclic exposure at 650°C for 100 h in different salty environments (weight percent): 100NaCl (T1), 75Na2SO4 + 25NaCl (T2), and 90Na2SO4 + 5NaCl + 5V2O5 (T3). A near parabolic rate law was observed in both non-treated and treated conditions; however, the parabolic rate constant (kp) was reduced for the USP-treated specimens coated with Salt T1 and Salt Mixtures T2 and T3 by nearly 41 %, 52 %, and 50 %, respectively, with respect to the non-treated specimens. Several oxides and spinels such as TiO2, Fe2O3, Fe3O4, Cr2O3, FeVO4, NbO2, NiFe2O4, NiCr2O4, NiVO3, FeNbO4, FeCr2O4, Na2Cr2O7, and Cr2(MoO4)3 and sulfides NiS and FeS and chlorides CrCl3 and NiCl2 were observed in both treated as well as non-treated samples. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aManufacturing processes. =650 \0$aMaterials. =700 1\$aChattopadhyay, K.,$eauthor. =700 1\$aAlam, Z.,$eauthor. =700 1\$aSingh, Vakil,$eauthor. =700 1\$aSatyanarayana, D. V. V.,$eauthor. =700 1\$aKumar, Vikas,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200156.html =LDR 03762nab 2200553 i 4500 =001 MPC20200189 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200189$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200189$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK1193.U5 =082 04$a621.31210973$223 =100 1\$aBhaduri, A. K.,$eauthor. =245 10$aDevelopment and Qualification of Materials for Indian Advanced Ultra-Supercritical Coal-Fired Power Plant /$cA. K. Bhaduri, Shaju K. Albert, A. Nagesha, A. Moitra, Utpal Borah, G. V. Prasad Reddy, K. Laha, Kulvir Singh, A. K. Das. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIndia has embarked on an ambitious program of setting up efficient advanced ultra-supercritical (AUSC) technology with steam temperature and pressure of 993 K and 31 MPa, respectively. This article deals with the testing and qualification of indigenously produced materials for the Indian AUSC mission project, the research and development phase of which is currently in the advanced stage of completion. As part of this, exhaustive database pertaining to various mechanical properties including creep, low cycle fatigue (LCF), creep-fatigue interaction (CFI), high cycle fatigue (HCF), fracture toughness, and crack growth has been generated covering important candidate materials such as alloy 617M tubes and forgings, 304HCu stainless steel tubes, and alloy 625 castings. Tubes of both alloy 617M and 304HCu stainless steels are to be used in the boilers, whereas alloy 617M forgings would be used as turbine rotor and alloy 625 castings as turbine casings. The data have been subsequently used to establish design curves identifying safe regimes of operation with respect to creep, LCF, HCF, CFI, and fatigue and creep crack growths. The properties were seen to be comparable with those derived from internationally developed equivalent grades. The bimetallic weld joints between alloy 617M and 10Cr steels were also evaluated to derive the appropriate strength reduction factors under creep and cyclic loadings. Additionally, the influence of thermal aging at service temperature on the microstructural evolution and mechanical properties was investigated based on tensile and fracture properties to account for the service exposure induced degradation and associated embrittlement. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aElectric power-plants. =650 \0$aElectric power-plants$xDesign and construction. =700 1\$aAlbert, Shaju K.,$eauthor. =700 1\$aNagesha, A.,$eauthor. =700 1\$aMoitra, A.,$eauthor. =700 1\$aBorah, Utpal,$eauthor. =700 1\$aPrasad Reddy, G. V.,$eauthor. =700 1\$aLaha, K.,$eauthor. =700 1\$aSingh, Kulvir,$eauthor. =700 1\$aDas, A. K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200189.html =LDR 03762nab 2200553 i 4500 =001 MPC20200147 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200147$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200147$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.M3 =082 04$a669.723$223 =100 1\$aAdsul, Swapnil H.,$eauthor. =245 10$aActive Protection of Magnesium Alloy AZ91D Using Corrosion Inhibitor Encapsulated Halloysite Nanoclay-Based Smart Sol-Gel Coatings /$cSwapnil H. Adsul, Shirish H. Sonawane, R. Subasri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMagnesium alloys are preferred extensively in automobile and aerospace industries, because of their very low density and high-specific strength. However, magnesium alloys are unstable in highly corrosive environments because of their extremely low standard electrode potential (−2.37 V). One of the most promising approaches to overcome this limitation is the use of eco-friendly and versatile sol-gel coatings. In the present work, corrosion-inhibition ability of various corrosion inhibitors, such as Ce3+-Zr4+, 8-hydroxyquinoline and 2-mercaptobenzothaizole, was evaluated on magnesium alloy AZ91D. For this purpose, inhibitors were loaded in as-received halloysite nanotubes (HNTs), which were then end-stoppered using polymeric microcapsules and dispersed in a hybrid silane matrix. The surface morphology of raw and inhibitor-loaded HNTs was examined with transmission electron microscopy analysis, whereas Brunauer-Emmett-Teller and scanning electron microscopy/energy-dispersive X-ray spectroscopy analyses were carried out to verify the encapsulation of inhibitors. The coatings were developed on coupons of AZ91D by the dip-coating technique, which were then thermally cured for 1 h at 130°C. The anticorrosion ability of inhibitor-encapsulated, HNT-based sol-gel coatings on AZ91D was evaluated using electrochemical impedance spectroscopy and potentiodynamic polarization for different durations of exposure to sodium chloride solution of 0.6 M concentration. Salt spray analysis was also carried out according to ASTM B117, Standard Practice for Operating Salt Spray (Fog) Apparatus, to examine the anticorrosion ability of coatings for a prolonged duration of exposure, 168 h. Electrochemical measurements and salt spray analyses have revealed that Ce3+-Zr4+-loaded HNT-based coatings were found to give better anticorrosion properties during prolonged durations of exposure to extremely corrosive environments, such as a 0.6 M sodium chloride solution. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMagnesium alloys. =650 \0$aMagnesium. =700 1\$aSonawane, Shirish H.,$eauthor. =700 1\$aSubasri, R.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200147.html =LDR 03762nab 2200553 i 4500 =001 MPC20200118 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200118$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200118$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.17$223 =100 1\$aManikandan, S. G. K.,$eauthor. =245 10$aDissimilar Welding of Cast Alloy 706 with Different Prior Heat Treatment Conditions and Austenitic Stainless Steel 321 /$cS. G. K. Manikandan, Tejas Baliram Patil, M. Kamaraj. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe welding of dissimilar joints is most common in the aerospace applications, especially, cast nickel-based superalloys are welded with austenitic stainless steel for high-temperature service conditions. It is well known that heat-affected zone (HAZ) cracking is a common phenomenon while welding age-hardened alloy 706. In this study, an alloy equivalent to cast alloy 706 subjected to three different heat treatment cycles and was welded with annealed austenitic stainless steel 321. The HAZ on the alloy 706 was investigated, and it was found that the HAZ of alloy 706 that underwent stabilization heat treatment was free from microfissures. The fusion zone microstructures were also investigated. The mechanical properties were evaluated, and it was found that the alloy 706 welded in stabilized and age-hardened condition furnished better mechanical properties than in both room temperature and elevated temperature. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aStainless steel industry. =650 \0$aStainless steel. =700 1\$aBaliram Patil, Tejas,$eauthor. =700 1\$aKamaraj, M.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200118.html =LDR 03762nab 2200553 i 4500 =001 MPC20200208 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200208$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200208$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK9203.L5 =082 04$a621.4834$223 =100 1\$aPrasad Reddy, G. V.,$eauthor. =245 10$aCore Materials for Sodium-Cooled Fast Reactors :$bPast to Present and Future Prospects /$cG. V. Prasad Reddy, V. Karthik, S. Latha, C. N. Venkiteswaran, Divakar Ramachandran, Shaju K. Albert. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (51 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe Sodium-Cooled Fast Reactor (SFR) is the most promising and technologically evolved among the six nuclear reactor concepts selected by the Generation IV International Forum. Although it is compatible with a closed fuel cycle for sustainable energy production, its competitiveness depends on being able to achieve high fuel burn-up up to 200 GWd/t. This would enable efficient fuel utilization to minimize fuel cycle costs. Hence, development of optimized core materials, especially for fuel cladding tubes that are subjected to extreme conditions of intense fast-spectrum neutron irradiation, high temperatures, and mechanical and chemical fuel–cladding interactions, continues to be a priority worldwide. Resistance to void swelling, irradiation creep, and embrittlement are required to be enhanced to minimize dimensional changes and loss of ductility in core components, which limit achievable burn-up. Current SFR core materials comprise austenitic stainless steels (SS) and ferritic-martensitic (FM) steels. Cold-worked austenitic SS grades 304, 316, 316Ti, niobium-stabilized grades FV548, EI-847, EP-172, and Ti-modified 15Cr-15Ni SS, such as D9, 1.4970, 15/15Ti SS, and ChS-68, have been used for fuel cladding and ducts in SFRs built to date, and they withstand neutron irradiation damage up to 80–100 dpa. Subsequent improvements have been made by optimizing minor elements (titanium, silicon, and phosphorous) and multi-stabilization to develop advanced grades such as Si-modified 15-15Ti, Indian Fast Reactor Advanced Clad (IFAC-1), PNC-316, EK-164, and HT-UPS, which could support burn-up of 150 GWd/t. In the case of FM steels, several commercial grades are found suitable in view of their inherent void swelling resistance to 200 dpa, and are being developed for improved creep strength by oxide dispersion strengthening to realize burn-up of 200–250 GWd/t. This article presents the development of structural materials for SFR fuel pin cladding and ducts and associated enhancement of permissible fuel burn-up. Indian and international experience resulting from extensive in-pile and out-of-pile mechanical testing and fuel–cladding interactions has been covered. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aSodium cooled reactors. =650 \0$aBreeder reactors. =700 1\$aKarthik, V.,$eauthor. =700 1\$aLatha, S.,$eauthor. =700 1\$aVenkiteswaran, C. N.,$eauthor. =700 1\$aRamachandran, Divakar,$eauthor. =700 1\$aAlbert, Shaju K.,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200208.html =LDR 03762nab 2200553 i 4500 =001 MPC20200170 =003 IN-ChSCO =005 20220119061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220419s2021\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200170$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20200170$bASTM International =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.17$223 =100 1\$aRajendran, Anbukkarasi,$eauthor. =245 10$aInfluence of Complete Tool-Offset Position on Intrinsic Microstructure and Its Effect on Fatigue Life of AA2024 Alloy-Copper Joint Made by Friction Stir Welding /$cAnbukkarasi Rajendran, Rajneesh Hariharan, Satish Vasu Kailas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2021. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTool offset position is the key parameter to consider during the welding of dissimilar metals by friction stir welding technique. It helps to control the formation of brittle intermetallics and volume defects. Even tool offset position can leave defects at the interface when it exceeds a certain limits, and it has been reported as two-thirds of the bottom radius of the tool. In this work, the effect of the maximum tool deviation (complete offset) on intrinsic microstructure and fatigue life of AA 2024-copper weld was studied. For this, an experiment was carried out with complete tool offset position. The results highlighted that the stir zone was formed mainly by aluminum and the total volume of copper transferred into the stir zone was measured as 5.6 % of the total volume of the stir zone. This kind of structure gives excellent fatigue life to the weld compared to the regular microstructure formed during friction stir welding. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 19, 2022. =650 \0$aMaterials. =650 \0$aStainless steel. =700 1\$aHariharan, Rajneesh,$eauthor. =700 1\$aKailas, Satish Vasu,$eauthor. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2.$dWest Conshohocken, Pa. :$bASTM International, 2021$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200170.html =LDR 03617nab a2200445 i 4500 =001 MPC20210121 =003 IN-ChSCO =005 20220430061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220430s2022\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210121$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210121$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =100 1\$aChai, Maozhou,$eauthor. =245 12$aA Graphene Oxide–Based Hydrogel with Excellent Adhesive, Tough, and Antibacterial Properties /$cMaozhou Chai, Meiwen An, Xiangyu Zhang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2022. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHydrogels have attracted extensive attention in the field of wound dressing because of the high water content and a structural similarity to human soft tissue. However, the hydrogels are usually vulnerable and easy to be destroyed during movement. Moreover, the hydrogels without antibacterial function cannot prevent bacterial infection during chronic wound healing. In this work, graphene oxide (GO) containing polyacrylamide hydrogel with both adhesiveness and superior mechanical properties was prepared. Since GO possesses good photothermal conversion capability and photodynamic property, the hybrid hydrogel exhibits excellent antibacterial property under the irradiation of near-infrared light. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed April 30, 2022. =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals =700 1\$aAn, Meiwen,$eauthor. =700 1\$aZhang, Xiangyu,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210121.html =LDR 03617nab a2200445 i 4500 =001 MPC20210086 =003 IN-ChSCO =005 20220430061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220430s2022\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210086$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210086$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =100 1\$aBhyravajoshulu, Shashank Dutt,$eauthor. =245 12$aA Study on the Effect of Test Temperatures on Tensile and Fracture Behavior of SS 316LN /$cShashank Dutt Bhyravajoshulu, Nani Babu Matcha, Shanthi Ganesan, Ganesan Vidyanathan, Aniruddha Moitra. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2022. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present study, the influence of test temperatures in the range of 25°C–550°C on the deformation and fracture behavior of SS 316LN has been investigated. The tensile properties and fracture toughness (J1c) of SS 316LN have been evaluated in this temperature range. From tensile properties, strain energy density was estimated as a function of plastic strain and strain-hardening parameters. The fracture tests (J-R curves) are conducted in this temperature range to determine fracture toughness and tearing resistance. From the fracture tested specimens, fractographic studies were carried out to further understand crack initiation mechanisms. From the results of fracture toughness in the temperature range of 350°C–450°C, an attempt to understand the deformation mechanism was made based on an empirical equation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed April 30, 2022. =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals =700 1\$aMatcha, Nani Babu,$eauthor. =700 1\$aGanesan, Shanthi,$eauthor. =700 1\$aVidyanathan, Ganesan,$eauthor. =700 1\$aMoitra, Aniruddha,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210086.html =LDR 03617nab a2200445 i 4500 =001 MPC20210142 =003 IN-ChSCO =005 20220430061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220430s2022\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210142$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210142$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =100 1\$aAbdelgawad, Khaled,$eauthor. =245 10$aAnalytical and Numerical Study of the Ring Expansion Testing Technique /$cKhaled Abdelgawad, Ahmed Nassef, Mohamed T. Eraky. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2022. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article presents a design development for the ring expansion test as an alternative technique of burst test to determine the mechanical properties of circular homogeneous thin-walled tubes in the hoop direction where it is supposed to fail. This is done by replacing the internal fluid pressure in burst test by a solid mandrel partitioned into an equal number of pieces. The numerical analyses were carried out using the commercial finite element method (FEM) package ABAQUS/CAE. The testing system consists of a multispecies mandrel assembled with two identical cones from top and bottom, and the ring specimen circumscribes the mandrel, which expands radially as a result of the cone’s axial displacement. The FEM was used to optimize the proposed design in terms of the minimum number of pieces in use. In addition, the effects of friction between the cones/the mandrel and between the ring/the mandrel are investigated. The FEM revealed that eight mandrel pieces or more are needed to preserve a uniform hoop stress throughout the ring circumference. Moreover, the FEM results in conjunction with theoretical formulas revealed that eight mandrel pieces at a minimum are required to minimize the power dissipated because of friction to a nuance value of 2 %. It is concluded that the higher the number of pieces used, the more uniform the hoop stress generated in the ring specimen. Moreover, it can effectively decrease friction effect at the ring/mandrel interface. The FEM also makes a great contribution in estimating the friction coefficients as it is restricted to be evaluated experimentally. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed April 30, 2022. =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals =700 1\$aNassef, Ahmed,$eauthor. =700 1\$aEraky, Mohamed T.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210142.html =LDR 03617nab a2200445 i 4500 =001 MPC20210080 =003 IN-ChSCO =005 20220430061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220430s2022\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210080$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210080$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.38 =082 04$a620.1$223 =100 1\$aKumar, Rajinder,$eauthor. =245 10$aEffect of Yttria-Stabilized Zirconia (Y2O3/ZrO2) Nanoparticles Reinforced Cr3C2-25NiCr Coatings on the Microstructural and Mechanical Properties of Turbine Steel /$cRajinder Kumar, Deepak Bhandari, Khushdeep Goyal. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2022. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe present work is mainly focused on the investigation of Cr3C2-25NiCr coatings reinforced with 5 % and 10 % of yttria-stabilized zirconia (YSZ) nanoparticles deposited on the CA6NM turbine steel by using the high-velocity oxy-fuel technique. The coatings were analyzed by scanning electron microscope (SEM)/energy-dispersive X-ray spectroscopy (EDS). The phase identification of a crystalline material was done with the X-ray diffraction (XRD) technique. The SEM/EDS analysis showed that dense and homogeneous coatings were developed by the reinforcement of YSZ nanoparticles. The peaks of XRD graphs of Cr3C2-25NiCr coating reinforced with 5 % and 10 % of YSZ nanoparticles revealed that the chromium and carbon were present as a major phase, and the presence of nickel, yttrium, and zirconium was observed as a minor phase. The porosity level decreased up to 32 % and 45 % by the addition 5 % and 10 % of YSZ nanoparticles as compared with conventional Cr3C2-25NiCr coating. The surface roughness values for coated samples were found to be 5.03, 4.89, and 4.28. The nanocomposite coatings reinforced with 10 % YSZ nanoparticles exhibited the highest microhardness value (1,251 HV). The Cr3C2-25NiCr coatings reinforced with 10 % of YSZ nanoparticles resulted in low porosity, low surface roughness, and high microhardness. During the coating process, the nanoparticles of YSZ flow into the pores and gaps that exist in the coatings and provide a better shield to the substrate material. The Cr3C2-25NiCr with 10 % of YSZ nanoparticles showed better results in terms of mechanical and microstructural properties during the investigation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed April 30, 2022. =650 \0$aShot peening. =650 \0$aFatigue testing machines$xStandards. =700 1\$aBhandari, Deepak,$eauthor. =700 1\$aGoyal, Khushdeep,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210080.html =LDR 03617nab a2200445 i 4500 =001 MPC20210132 =003 IN-ChSCO =005 20220430061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220430s2022\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210132$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210132$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =100 1\$aPrasanna Nagasai, Bellamkonda,$eauthor. =245 10$aMechanical Properties and Microstructural Characteristics of AA5356 Aluminum Alloy Cylindrical Components Made by Wire Arc Additive Manufacturing Process /$cBellamkonda Prasanna Nagasai, S. Malarvizhi, V. Balasubramanian. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2022. =300 \\$a1 online resource (26 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aWire arc additive manufacturing (WAAM) is a high-quality technology for producing large and complicated geometries in close proximity to net shape with low-cost production resources, including welding machines and filler wires. It offers the cost-effective fabrication of large-scale metal parts with high deposition. AA5356 aluminum–magnesium (Al-Mg) alloys can reach medium strength without a solid solution and quenching treatment, thereby avoiding product distortion caused by quenching, which has attracted the attention of WAAM researchers. However, challenges during the additive manufacturing of aluminum alloys, such as porosity or poor mechanical properties, can be overcome by using arc technologies with low heat input. This paper presents metallurgical characteristics and mechanical properties of WAAM AA5356 alloy cylindrical components fabricated by gas metal arc welding (GMAW) and cold metal transferred (CMT) arc welding processes. Herein, a comparison between the welding processes and the resulting heat input shows the effect on the resulting microstructure and the mechanical properties of additively manufactured AA5356 parts. Firstly, the influence of heat input on the porosity and microstructural characteristics were analyzed. Subsequently, the effect of heat input on the mechanical properties of the cylindrical components was studied. The cylindrical component produced by CMT process exhibits fewer and smaller pores with finer grains and reduced segregation of β-(Al3Mg2) phases than the GMAW process. The component fabricated by CMT process showed isotropic superior mechanical properties (tensile properties, hardness, and impact toughness) than the component made by GMAW process. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed April 30, 2022. =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals =700 1\$aMalarvizhi, S.,$eauthor. =700 1\$aBalasubramanian, V.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210132.html =LDR 03617nab a2200445 i 4500 =001 MPC20210055 =003 IN-ChSCO =005 20220430061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220430s2022\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210055$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210055$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =100 1\$aKheradmandan, Hasan,$eauthor. =245 10$aModeling and Optimizing the Penetration in the Submerged Arc Welding Process in the Presence of ZrO 2 Nanoparticles /$cHasan Kheradmandan, Masood Aghakhani, Tahereh Kheradmandan, Sepideh Kheradmandan, Maziar Mahdipour Jalilian, A. Ghiasvand, Seyed Abbas Hosseini. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2022. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPenetration is one of the most vital parameters because of its influences on weld strength and weld quality. Choosing the input parameters in submerged arc welding (SAW) has significant effects on input heat into the weld pool, which affects the quality of weldment. The amazing advancement of nanotechnology in various industrial areas persuaded researchers to use nanoparticles in new research. Zirconium dioxide (ZrO2) nanoparticles were selected in order to identify their effects in the weld pool in combination with other welding input parameters. The five-level, five-parameter central composite rotatable design, response surface methodology, the slime mold algorithm, and Harris hawks optimization were utilized to design and develop the research and finally to predict and optimize the weld penetration affected by the arc voltage, welding current, nozzle-to-plate distance, welding speed, and the thickness of ZrO2 nanoparticles coated on ST-37 steel. The main and interaction effects of input parameters on weld penetration were drawn. The results demonstrated that weld penetration decreased initially by increasing the thickness of ZrO2 nanoparticles up to 0.25 mm, which was due to reversing Marangoni convection mode. Furthermore, weld penetration increased with increase in ZrO2 nanoparticles above thicknesses of 0.75 mm. The reason for increase in weld penetration was because of the fact the ZrO2 nanoparticles have low thermal conductivity, which leads to less heat transfer. The results confirmed that the accuracy of model obtained by slime mold algorithm was 5.2 % more than response surface methodology. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed April 30, 2022. =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals =700 1\$aAghakhani, Masood,$eauthor. =700 1\$aKheradmandan, Tahereh,$eauthor. =700 1\$aKheradmandan, Sepideh,$eauthor. =700 1\$aMahdipour Jalilian, Maziar,$eauthor. =700 1\$aGhiasvand, A.,$eauthor. =700 1\$aAbbas Hosseini, Seyed,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210055.html =LDR 03617nab a2200445 i 4500 =001 MPC20210127 =003 IN-ChSCO =005 20220430061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220430s2022\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210127$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210127$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =100 1\$aLu, Yu,$eauthor. =245 10$aPhotocatalytic Degradation of Printing and Dyeing Wastewater by F-N/TiO 2 /AC and F-N/TiO 2 /MAC Composite Photocatalysts /$cYu Lu, Zhen Chen, Yingying Zhu, Zhenguo Xia, Geng Chen. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2022. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA fluorine/nitrogen-co-doped titania/activated carbon (F-N/TiO2/AC) composite has been prepared through an immersion–hydrothermal method. Magnetic activated carbon (MAC) has been prepared through a chemical coprecipitation method and used to assemble the analogous composite F-N/TiO2/MAC. The characterization results show that F-N/TiO2/MAC contains a certain amount of magnetic ferrous oxide material, and the presence of magnetic ferrous oxide material will not affect the crystalline shape of TiO2. F-N/TiO2/MAC is a weak magnetic material, and it could be conveniently recycled by applying a strong magnetic field. Methyl orange solution has been used as a target to assess the photocatalytic degradation and recycling performances of the composites. Results show that the adsorption of methyl orange on the photocatalysts follows a pseudo second-order kinetic model, and the adsorption rate of F-N/TiO2/AC is higher. In the photocatalytic degradation of methyl orange pseudo first-order reaction kinetics study, the k value of F-N/TiO2/MAC was 0.00497 min−1, which was higher than that of F-N/TiO2/AC. Even though the adsorption performance of F-N/TiO2/MAC is not as good as that of F-N/TiO2/AC, its photocatalytic degradation performance is superior. Overall, the two composite materials show roughly the same removal efficiencies for methyl orange, reaching 100 % for F-N/TiO2/AC and 98.9 % for F-N/TiO2/MAC. In terms of recycling performance, the magnetic property of F-N/TiO2/MAC makes it easier to recover from mixed solutions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed April 30, 2022. =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals =700 1\$aChen, Zhen,$eauthor. =700 1\$aZhu, Yingying,$eauthor. =700 1\$aXia, Zhenguo,$eauthor. =700 1\$aChen, Geng,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210127.html =LDR 03617nab a2200445 i 4500 =001 MPC20210100 =003 IN-ChSCO =005 20220430061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220430s2022\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210100$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210100$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =100 1\$aPonam,$eauthor. =245 10$aPorous Coordination Polymers as Active Fillers for Solid Polymer Electrolytes of Lithium-Ion Batteries /$cPonam, Parshuram Singh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2022. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe role of renewable energy is crucial for energy sustainability and depends upon the energy storage devices and their technical progress. The batteries prove themselves as reliable, efficient, and environmentally friendly energy storage devices. However, limitations such as safety issues, low energy density, leakage, etc. In view of that, solid-state electrolytes are the most promising alternative to liquid electrolytes because of their higher safety factor and potential for enough energy density. In contrast, these solid electrolytes also have limitations of low ionic conductivity and a higher interfacial resistance compared to conventional electrolytes. To overcome the mentioned limitations, the doping of filler materials in the electrolyte during synthesis is proven as one of the favorable techniques. The filler materials not just improve the ionic conductivity of the electrolyte but also enhance the thermal and mechanical stability. Furthermore, to decrease the interfacial resistance, the electrolyte should have good mechanical strength and a higher surface area. In this context, the use of microporous coordination polymers is proven to be the most practical and effective approach. The main aim of this work is to highlight the recent advancement in the applicability of porous polymers for solid-state electrolytes and to also provide the major benefits and limitations of porous material-based solid electrolytes. Along with this, a brief description of ultramodern porous coordination polymers is also included in this article. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed April 30, 2022. =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals =700 1\$aSingh, Parshuram,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210100.html =LDR 03617nab a2200445 i 4500 =001 MPC20210091 =003 IN-ChSCO =005 20220430061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220430s2022\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210091$2doi =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =037 \\$aMPC20210091$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =100 1\$aGibson, Cody,$eauthor. =245 10$aResults of a Pilot Study in Support of a Round-Robin on Creep-Fatigue Crack Growth Testing of a Creep-Brittle Material for ASTM E2760 /$cCody Gibson, Robert Stephens, Santosh B. Narasimhachary, David E. Mills, Andrew Rosenberger. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2022. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis paper describes pilot test results from a round-robin conducted in support of the standard ASTM E2760, Standard Test Method for Creep-Fatigue Crack Growth Testing, on creep-fatigue crack growth testing. Results from the pilot study are recommended to participants to develop their individual experimental testing. This round-robin is an international effort with 10 participants from five countries from Asia, North America, and Europe. All participants are testing compact type (C(T)) specimens according to the procedure described in the standard. A few participants are evaluating the Kb-bar (surface crack) specimen configuration. The test material is Inconel-718 (IN718) nickel-based alloy, which is a creep-brittle alloy. Pilot creep-fatigue crack growth tests were conducted at 600°C using C(T) specimens under constant load amplitude conditions. The tests were conducted at hold times of 0, 60, and 600 s. Creep-fatigue crack growth rates were analyzed using the methods proposed and included in the test standard. It was found that the procedures followed throughout the pilot test program were sufficient in generating the desired outcomes. As a result, it is proposed that the various participants follow the procedures and test matrix as close as possible and document any deviations. This will allow data from the various participants to be assessed and determine the levels of precision and bias in creep-fatigue crack growth data obtained using the ASTM standard. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed April 30, 2022. =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals =700 1\$aStephens, Robert,$eauthor. =700 1\$aNarasimhachary, Santosh B.,$eauthor. =700 1\$aMills, David E.,$eauthor. =700 1\$aRosenberger, Andrew,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210091.html =LDR 03286nas a2200733 i 4500 =001 MPC111 =003 IN-ChSCO =005 20220430061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 220430c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =082 04$a620.11$223 =245 00$aMaterials performance and characterization. =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed Sep. 20, 2012). =588 \\$aLatest issue consulted: Volume 11, Issue 1 (viewed Apr. 30, 2022). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/journals/volume/listing/coden/MPCACD/issue/1/volume/11/online-issue-date/2022-04-28+00%3A00%3A00 =LDR 03617nab a2200445 i 4500 =001 MPC20200118 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200118$2doi =037 \\$aMPC20200118$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS236 =082 04$a671.2$223 =100 1\$aManikandan, S. G. K.,$eauthor. =245 10$aDissimilar Welding of Cast Alloy 706 with Different Prior Heat Treatment Conditions and Austenitic Stainless Steel 321 /$cS. G. K. Manikandan, Tejas Baliram Patil, M. Kamaraj. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe welding of dissimilar joints is most common in the aerospace applications, especially, cast nickel-based superalloys are welded with austenitic stainless steel for high-temperature service conditions. It is well known that heat-affected zone (HAZ) cracking is a common phenomenon while welding age-hardened alloy 706. In this study, an alloy equivalent to cast alloy 706 subjected to three different heat treatment cycles and was welded with annealed austenitic stainless steel 321. The HAZ on the alloy 706 was investigated, and it was found that the HAZ of alloy 706 that underwent stabilization heat treatment was free from microfissures. The fusion zone microstructures were also investigated. The mechanical properties were evaluated, and it was found that the alloy 706 welded in stabilized and age-hardened condition furnished better mechanical properties than in both room temperature and elevated temperature. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetal castings. =650 \0$aHeat resistant alloys. =650 \0$aMetals. =700 1\$aBaliram Patil, Tejas,$eauthor. =700 1\$aKamaraj, M.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200118.html =LDR 03617nab a2200445 i 4500 =001 MPC20200139 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200139$2doi =037 \\$aMPC20200139$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.38 =082 04$a620.1126$223 =100 1\$aSunil, Saurav,$eauthor. =245 10$aEffect of Specimen Thickness on Threshold Stress Intensity Factor ( ) Associated with DHC in Zr-2.5 Nb Alloy Pressure Tube Material /$cSaurav Sunil, A. K. Bind, T. N. Murty, R. N. Singh, G. Avinash, I. V. Singh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDelayed hydride cracking (DHC) behavior for zirconium alloys is characterized in terms of DHC velocity, VDHC, and Threshold Stress Intensity factor, KIH. The effect of specimen thickness on KIH associated with DHC of unirradiated Zr-2.5 Nb pressure tube material was investigated. For this purpose, KI at crack arrest for 1 mm–, 2 mm–, and 4.5 mm–thick specimens was determined using the load drop technique. Significant tunneling of the crack was observed for 1 mm– and 2 mm–thick specimens in the load drop test at 250°C. The KI at crack arrest was found to be increasing with the decrease in specimen thickness. However, extended finite element model (FEM) simulation revealed that KI at crack arrest in the center of the 1-mm specimen and 2-mm specimen is comparable to the values 9.2 ± 0.5 MPa.m1/2obtained for the 4.5 mm–thick specimen. Hence, if tunneling is not present in the specimen, the KIH was found to be independent of specimen thickness. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aFracture mechanics. =650 \0$aMaterials$xFatigue. =650 \0$aMetals$xFracture. =700 1\$aBind, A. K.,$eauthor. =700 1\$aMurty, T. N.,$eauthor. =700 1\$aSingh, R. N.,$eauthor. =700 1\$aAvinash, G.,$eauthor. =700 1\$aSingh, I. V.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200139.html =LDR 03617nab a2200445 i 4500 =001 MPC20200140 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200140$2doi =037 \\$aMPC20200140$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.A6 =082 04$a620.186$223 =100 1\$aSadasivam, Prakash,$eauthor. =245 10$aComparative Studies on Normal and Pulsed Cold Metal Transfer Welding of Aerospace Grade Aluminum Alloy 2024 /$cPrakash Sadasivam, S. Jerome, M. Sathishkumar, M. Manikandan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAluminum alloy 2024 (AA2024) sheets are mostly used in the fuselage and wings of the aircraft and structural applications; it is because of better fatigue resistance and high strength. The joining of AA2024 through gas metal arc welding (high heat input) is complicated because of hot cracking (solidification cracking), softening of the heat-affected zone (HAZ), and formation of porosity. However, these problems could be minimized by employing cold metal transfer (CMT) (low heat input) welding. The ultimate aim of the present research is to compare the metallurgical integrity and mechanical properties of the butt-welded AA2024 through normal CMT (N-CMT) and pulsed mode CMT (P-CMT) methods. The fine-grain structure observed in the P-CMT contributed better mechanical properties compared to N-CMT. The segregations of magnesium, silicon, and copper have revealed the intermetallic compounds such as aluminum-copper (2:1), Al2CuMg, magnesium silicide, and tetracopper silicide. This results in an intergranular fracture of both N-CMT and P-CMT joints. Besides, P-CMT exhibited a higher ultimate tensile strength and % elongation than the N-CMT. Also, the joint efficiencies of N-CMT and P-CMT were 64 % and 68 %, respectively. Furthermore, the hardness value in HAZ of N-CMT (93 HV) was inferior to P-CMT (126 HV). Hence, P-CMT is recommended for joining AA2024 compared to N-CMT. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aAluminum alloys$xMechanical properties. =650 \0$aAluminum castings. =700 1\$aJerome, S.,$eauthor. =700 1\$aSathishkumar, M.,$eauthor. =700 1\$aManikandan, M.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200140.html =LDR 03617nab a2200445 i 4500 =001 MPC20200147 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200147$2doi =037 \\$aMPC20200147$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.M3 =082 04$a669.723$223 =100 1\$aAdsul, Swapnil H.,$eauthor. =245 10$aActive Protection of Magnesium Alloy AZ91D Using Corrosion Inhibitor Encapsulated Halloysite Nanoclay-Based Smart Sol-Gel Coatings /$cSwapnil H. Adsul, Shirish H. Sonawane, R. Subasri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMagnesium alloys are preferred extensively in automobile and aerospace industries, because of their very low density and high-specific strength. However, magnesium alloys are unstable in highly corrosive environments because of their extremely low standard electrode potential (−2.37 V). One of the most promising approaches to overcome this limitation is the use of eco-friendly and versatile sol-gel coatings. In the present work, corrosion-inhibition ability of various corrosion inhibitors, such as Ce3+-Zr4+, 8-hydroxyquinoline and 2-mercaptobenzothaizole, was evaluated on magnesium alloy AZ91D. For this purpose, inhibitors were loaded in as-received halloysite nanotubes (HNTs), which were then end-stoppered using polymeric microcapsules and dispersed in a hybrid silane matrix. The surface morphology of raw and inhibitor-loaded HNTs was examined with transmission electron microscopy analysis, whereas Brunauer-Emmett-Teller and scanning electron microscopy/energy-dispersive X-ray spectroscopy analyses were carried out to verify the encapsulation of inhibitors. The coatings were developed on coupons of AZ91D by the dip-coating technique, which were then thermally cured for 1 h at 130°C. The anticorrosion ability of inhibitor-encapsulated, HNT-based sol-gel coatings on AZ91D was evaluated using electrochemical impedance spectroscopy and potentiodynamic polarization for different durations of exposure to sodium chloride solution of 0.6 M concentration. Salt spray analysis was also carried out according to ASTM B117, Standard Practice for Operating Salt Spray (Fog) Apparatus, to examine the anticorrosion ability of coatings for a prolonged duration of exposure, 168 h. Electrochemical measurements and salt spray analyses have revealed that Ce3+-Zr4+-loaded HNT-based coatings were found to give better anticorrosion properties during prolonged durations of exposure to extremely corrosive environments, such as a 0.6 M sodium chloride solution. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMagnesium$xMetallurgy. =650 \0$aMaterials science. =650 \0$aMagnesium alloys. =700 1\$aSonawane, Shirish H.,$eauthor. =700 1\$aSubasri, R.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200147.html =LDR 03617nab a2200445 i 4500 =001 MPC20200148 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200148$2doi =037 \\$aMPC20200148$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC374 =082 04$a620.112$223 =100 1\$aKumar, K. Pradeep Prem,$eauthor. =245 10$aImproving the Corrosion Resistance of Magnesium Alloy AZ31 by a Duplex Anodized and Sol-Gel Coating /$cK. Pradeep Prem Kumar, R. Subasri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMagnesium and its alloys have found application in several areas viz., aerospace, electronics industry, and automobile, owing to their specific strength-to-weight ratio, thermal conductivity, electromagnetic shielding, etc. However, poor corrosion resistance limits their applicability for widespread use. Anodization and micro arc oxidation (MAO) are commonly used to enhance the corrosion protection of magnesium alloys. The anodized or MAO layers are porous, and hence, organic sealants are conventionally used for sealing the pores. There are not many reports on the use of organic-inorganic hybrid coatings as sealants on anodized layers of magnesium alloys. In this study, the hybrid sol-gel silica-based coatings were investigated as sealants on anodized magnesium alloy AZ31 substrates. A thick (∼20 µm) and porous oxide layer was deposited by anodization using sodium silicate as electrolyte. Ambient curable hybrid silica coatings with and without corrosion inhibitors like cerium oxide and 8-hydroxyquinoline were deposited by dip coating method. The anodized layer and the duplex coating were analyzed using X-ray diffraction and field emission scanning electron microscopy with energy-dispersive X-ray analysis (EDAX) attachment. Electrochemical impedance spectroscopy and potentiodynamic polarization studies were used to assess the corrosion protection performance of these coatings in 0.61M NaCl solution. The porous anodized magnesium oxide layer improved the binding strength of the adjacent sol-gel layer; the sol-gel layer physically sealed the porous anodized coating and offered higher corrosion protection. The duplex coating prevented the diffusion of aggressive ions onto the magnesium alloy AZ31 and enhanced the corrosion resistance significantly. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aOptical materials. =650 \0$aSurfaces (Physics) =650 \0$aThin films. =700 1\$aSubasri, R.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200148.html =LDR 03617nab a2200445 i 4500 =001 MPC20200152 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200152$2doi =037 \\$aMPC20200152$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a624.1821$223 =100 1\$aDas, Annesha,$eauthor. =245 10$aStress Corrosion Cracking in Austenitic Stainless Steels in Reactor Primary Water–High Purity Oxidizing and in Supercritical Conditions /$cAnnesha Das, Supratik Roychowdhury, Vivekanand Kain. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aAustenitic stainless steels (SS) commonly used in the primary circuit of light water reactors (LWRs) have excellent corrosion resistance in demineralized (DM) water at high temperature (290°C–330°C) and pressure (7.4 MPa for boiling water reactor [BWR], 16 MPa for pressurized water reactor [PWR]). Radiolysis of primary DM water in BWR forms 200–300 ppb of oxidizing species (normal water chemistry [NWC]), which elevates the electrochemical potential of the SS from −300 to −600 mVSHE (mV with standard hydrogen electrode) when dissolved oxygen is 10–20 ppb to +100 to +200 mVSHE. Neutron irradiation of SS further induces metallurgical and microstructural changes, which compromises corrosion resistance. Thus, radiation makes BWR (NWC) environment hostile, causing extensive irradiation-assisted stress corrosion cracking (same as intergranular stress corrosion cracking [IGSCC]) in austenitic SS. IGSCC occurs in both sensitized (grain boundary chromium depletion) and nonsensitized conditions (strain-hardened region in base metal immediately adjacent to the weld fusion zone) and is a generic problem. IGSCC in BWR can be mitigated by hydrogen addition in water (hydrogen water chemistry [HWC]). BWR-HWC has limitations and is ineffective where boiling occurs. IGSCC of SS in PWR is limited because hydrogen addition in primary water suppresses radiolysis though the formation of aggressive environment in low-flow occluded regions can cause IGSCC in SS. Increasing demand for economic power has led to the primary environment in nuclear reactors to become hostile. Conceptual supercritical water reactor (SCWR) will use DM water at 500°C–600°C and 25 MPa, which is extreme for conventional LWR materials. IGSCC in austenitic SS and nickel-based alloys occurs in both oxidizing and reducing SCWR conditions, which can be further exacerbated by radiation. This article reviews how benign primary DM water becomes hostile in LWRs and extreme in SCWR conditions, causing SCC to be a generic problem in austenitic alloys. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aAustenitic stainless steel. =650 \0$aStainless steel$xWelding. =650 \0$aStress corrosion. =700 1\$aRoychowdhury, Supratik,$eauthor. =700 1\$aKain, Vivekanand,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200152.html =LDR 03617nab a2200445 i 4500 =001 MPC20200155 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200155$2doi =037 \\$aMPC20200155$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA404.8 =082 04$a620.11292$223 =100 1\$aGupta, R. K.,$eauthor. =245 10$aMicrostructural and Mechanical Characterization of 1.6-mm-Thick Nimonic-75 Superalloy Welds /$cR. K. Gupta, V. Anil Kumar, Ravi Ranjan Kumar, R. Vivek, P. V. Venkitakrishnan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aGas tungsten arc welding (GTAW) and electron beam welding (EBW) studies on thin Nimonic-75 sheets of 1.6-mm thickness have been carried out using butt-weld configuration. Manual GTAW was done using Inconel-718 filler wire with a two-pass welding and EBW was done by autogenous welding. The strength of both the weldments at ambient temperature is found to be marginally (~4%) higher than the base metal. Marginally higher strength in the case of GTAW joints was observed at ambient temperature and is attributed to the use of Inconel-718 filler wire, where the additional alloying elements (niobium, aluminum, molybdenum) and their contents in the weldment contribute to increase in strength. The microstructure of the fusion zone in EBW reveals a needle-shaped/acicular structure with fine dendrites, whereas the dendrites are coarser in the case of GTAW welds. At elevated temperatures (600°C–700°C), the strength of GTAW is similar to the base metal. However, EBW coupon exhibited higher strength (~20–45%) than GTAW coupon, indicating the beneficial role of faster heating/cooling in EBW leading to acicular microstructure. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aEngineering instruments. =650 \0$aMaterials$xDynamic testing. =650 \0$aDispersion$xMathematical models. =700 1\$aAnil Kumar, V.,$eauthor. =700 1\$aKumar, Ravi Ranjan,$eauthor. =700 1\$aVivek, R.,$eauthor. =700 1\$aVenkitakrishnan, P. V.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200155.html =LDR 03617nab a2200445 i 4500 =001 MPC20200156 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200156$2doi =037 \\$aMPC20200156$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS236 =082 04$a671.2$223 =100 1\$aKumar, Sanjeev,$eauthor. =245 10$aCorrosion Behavior of Surface Nanostructured IN718 Superalloy at 650°C /$cSanjeev Kumar, K. Chattopadhyay, Z. Alam, Vakil Singh, D. V. V. Satyanarayana, Vikas Kumar. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present study, the process of ultrasonic shot peening (USP) was adopted for developing nanostructures with a grain size of 62 ± 10 nm on the surface of the alloy IN718. The effect of nanostructures was investigated on high-temperature corrosion behavior under cyclic exposure at 650°C for 100 h in different salty environments (weight percent): 100NaCl (T1), 75Na2SO4 + 25NaCl (T2), and 90Na2SO4 + 5NaCl + 5V2O5 (T3). A near parabolic rate law was observed in both non-treated and treated conditions; however, the parabolic rate constant (kp) was reduced for the USP-treated specimens coated with Salt T1 and Salt Mixtures T2 and T3 by nearly 41 %, 52 %, and 50 %, respectively, with respect to the non-treated specimens. Several oxides and spinels such as TiO2, Fe2O3, Fe3O4, Cr2O3, FeVO4, NbO2, NiFe2O4, NiCr2O4, NiVO3, FeNbO4, FeCr2O4, Na2Cr2O7, and Cr2(MoO4)3 and sulfides NiS and FeS and chlorides CrCl3 and NiCl2 were observed in both treated as well as non-treated samples. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetal castings. =650 \0$aHeat resistant alloys. =650 \0$aMetals. =700 1\$aChattopadhyay, K.,$eauthor. =700 1\$aAlam, Z.,$eauthor. =700 1\$aSingh, Vakil,$eauthor. =700 1\$aSatyanarayana, D. V. V.,$eauthor. =700 1\$aKumar, Vikas,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200156.html =LDR 03617nab a2200445 i 4500 =001 MPC20200160 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200160$2doi =037 \\$aMPC20200160$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK9204 =082 04$a538.6$223 =100 1\$aBowen, Michael S.,$eauthor. =245 10$aHigh Temperature Corrosion Stability of Ceramic Materials for Magnetohydrodynamic Generators /$cMichael S. Bowen, Kyei-Sing Kwong, Peter Hsieh, David P. Cann, C. Rigel Woodside. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCorrosion by alkali metals and their compounds poses a significant challenge to the long-term material stability and service life for both metal alloys and ceramics at high operating temperatures. Chemical reactivity between alkali metals and materials underlie numerous industry challenges ranging from fireside corrosion in biomass-fired boilers to reaction with silica-based refractory ceramics in glass furnaces. The problem is particularly significant in magnetohydrodynamic (MHD) generators, where potassium or cesium compounds are introduced to improve the electrical conductivity of the working fluid. Thus, resistance to attack by alkali metal vapor is an important consideration in the selection and fabrication of ceramic electrodes and insulators for MHD generators. We evaluated several refractory ceramics to assess phase stability and known reactions with potassium and its compounds at high temperatures (T > 1,200 °C). Refractory ceramics were tested for potassium vapor corrosion using a modified ASTM standard test method with in situ monitoring of gas composition. Unlike other materials, the magnesia (MgO) and ceria (CeO2) samples did not exhibit corrosion, and no phase or mass changes were observed. This indicates that CeO2 and MgO could exhibit long lifetimes as plasma facing components in MHD generators. Ultimately, this development provides valuable data in evaluating critical materials performance issues that can attest to the viability of high temperature direct fired MHD generator applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMagnetohydrodynamic generators. =650 \0$aMagnetohydrodynamics. =650 \0$aPlasma instabilities. =700 1\$aKwong, Kyei-Sing,$eauthor. =700 1\$aHsieh, Peter,$eauthor. =700 1\$aCann, David P.,$eauthor. =700 1\$aWoodside, C. Rigel,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200160.html =LDR 03617nab a2200445 i 4500 =001 MPC20200168 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200168$2doi =037 \\$aMPC20200168$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK4660 =082 04$a671.5212$223 =100 1\$aZala, Arunsinh B.,$eauthor. =245 10$aStudy of Weldability for Aluminide Coated Steels through A-TIG Welding Process /$cArunsinh B. Zala, N. I. Jamnapara, Vishvesh J. Badheka, C. S. Sasmal, Shiju Sam, Mukesh Ranjan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTo achieve higher efficiency in high-temperature environments, 9Cr-1Mo steels (also known as P91 steels) are promising candidates in power plants, petrochemical industries, heat exchangers, and nuclear applications. To enhance the performance against harsh environments, such as high-temperature oxidation and corrosion during operations, adding aluminum oxide (Al2O3)/iron aluminide (FeAl) coating through the aluminizing process has been found promising. Such coatings have been considered reliable for resistance to liquid-metal corrosion against flowing lead-lithium liquid breeders and against tritium permeation in blanket modules of fusion reactors. However, the welding process for aluminized coated steels is a challenge and is scarcely reported. The aluminum-rich coating at the top may alter the metallurgy of weld metal and subsequently the mechanical properties after welding. To investigate the same, preliminary bead-on-plate trials with a novel activated-tungsten inert gas welding process has been attempted for the first time. Bead-on-plate welding samples were prepared (with the same welding parameters) with five different fluxes, such as iron (III) oxide (Fe2O3), nickel (II) oxide (NiO), copper (II) oxide (CuO), cobalt tetroxide (Co3O4), and Al2O3, for aluminized coated 9Cr-1Mo steel. The resultant weld metal microstructure was evaluated using optical and electron microscopy, elemental analysis using energy-dispersive X-ray spectroscopy, phase analysis using X-ray diffraction, and Vickers hardness testing. It was observed that the presence of oxide-type fluxes results in arc constriction, which thereby affects the depth of penetration. The weld metal prepared with Fe2O3 flux demonstrates a superior depth-to-width ratio compared to other fluxes. An analysis for delta ferrite was also carried out and was observed to be present in Fe2O3 flux welds only. A detailed analysis of the weld metal under different activated fluxes is presented in the paper. The outcome of this work presents the feasibility of the welds of aluminized 9Cr steels as relevant for fusion reactor applications. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aPlasma arc welding. =650 \0$aElectric welding. =650 \0$aGas tungsten arc welding. =700 1\$aJamnapara, N. I.,$eauthor. =700 1\$aBadheka, Vishvesh J.,$eauthor. =700 1\$aSasmal, C. S.,$eauthor. =700 1\$aSam, Shiju,$eauthor. =700 1\$aRanjan, Mukesh,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200168.html =LDR 03617nab a2200445 i 4500 =001 MPC20200170 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200170$2doi =037 \\$aMPC20200170$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTS228.9 =082 04$a671.52$223 =100 1\$aRajendran, Anbukkarasi,$eauthor. =245 10$aInfluence of Complete Tool-Offset Position on Intrinsic Microstructure and Its Effect on Fatigue Life of AA2024 Alloy-Copper Joint Made by Friction Stir Welding /$cAnbukkarasi Rajendran, Rajneesh Hariharan, Satish Vasu Kailas. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTool offset position is the key parameter to consider during the welding of dissimilar metals by friction stir welding technique. It helps to control the formation of brittle intermetallics and volume defects. Even tool offset position can leave defects at the interface when it exceeds a certain limits, and it has been reported as two-thirds of the bottom radius of the tool. In this work, the effect of the maximum tool deviation (complete offset) on intrinsic microstructure and fatigue life of AA 2024-copper weld was studied. For this, an experiment was carried out with complete tool offset position. The results highlighted that the stir zone was formed mainly by aluminum and the total volume of copper transferred into the stir zone was measured as 5.6 % of the total volume of the stir zone. This kind of structure gives excellent fatigue life to the weld compared to the regular microstructure formed during friction stir welding. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aFriction welding. =700 1\$aHariharan, Rajneesh,$eauthor. =700 1\$aKailas, Satish Vasu,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200170.html =LDR 03617nab a2200445 i 4500 =001 MPC20200173 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200173$2doi =037 \\$aMPC20200173$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTJ164 =082 04$a621.3121$223 =100 1\$aPatil, Jeet P.,$eauthor. =245 12$aA Review on the Material Development and Corresponding Properties for Power Plant Applications /$cJeet P. Patil, Manas Paliwal, Sushil K. Mishra. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (35 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aOver the past decade, increased demand for energy generation at affordable rates and in a clean state has been the driving force for material development for energy generation. In developing countries, coal-fired thermal power plants are the major source of electricity generation. However, coal-fired plants induce a higher carbon footprint and contribute to greenhouse gas emissions. Hence, several strategies have been formulated to mitigate environmental pollution while maintaining high energy output. This review comprehensively presents the historical material development process that led to an increase in the efficiency of a coal-fired power plant. Candidate material identification and application, essential alloying elements, and their impact on service life are comprehensively reviewed. Adapting the ultra-supercritical (USC) and advanced ultra-supercritical (A-USC) power generation technology requires the development of new alloys that can withstand harsh operating conditions (700–725°C and 25–35 MPa), which demands the replacement of conventional materials (ferritic/austenitic steel) with better ones. The candidate alloys should be evaluated across several key issues such as high-temperature material response to loading, creep strength, high-temperature oxidation, and component fabricability. The evaluation of creep strength data suggests that nickel-based alloys like Inconel alloy 282 are preferred because of the high stability of the γ′ phase. Moreover, at higher temperatures, nickel-based alloys are preferred over ferritic/austenitic steel alloys because of their superior corrosion resistance. The fireside corrosion and high-temperature oxidation resistance are governed by the formation of different oxide layers depending on the temperature, pressure, and alloy content. Furthermore, the weldability of different candidate alloys is discussed in detail, along with the microstructural evolution in the heat-affected zone. This review also focuses on the cost of constructing a greenfield USC/A-USC power plant. Lastly, a perspective on new alloy development for A-USC/USC application is presented, and the microstructure and property relationships of these alloys are discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aPower (Mechanics) =650 \0$aPower resources. =650 \0$aPower-plants. =700 1\$aPaliwal, Manas,$eauthor. =700 1\$aMishra, Sushil K.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200173.html =LDR 03617nab a2200445 i 4500 =001 MPC20200174 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200174$2doi =037 \\$aMPC20200174$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA460 =082 04$a620.1633$223 =100 1\$aStewart, Calvin M.,$eauthor. =245 10$aAccelerated Creep Testing of Inconel 718 Using the Stepped Isostress Method (SSM) /$cCalvin M. Stewart, Md Abir Hossain, Jacob Pellicotte, Robert Mach, David Alexander, Sanna F. Siddiqui. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (20 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis paper demonstrates the stepped isostress method (SSM), an accelerated creep test (ACT) for the rapid assessment of metallic materials. The SSM test is based on the time-temperature-stress superposition principle in which temperature, stress, or both, are step increased to accelerate the time to rupture. The SSM test has proven successful for the ACT of polymers and polymeric composites but has yet to be proven for metallic materials. In this study, new test matrix design rules for the SSM of metals are established based on deformation mechanism, time-temperature transformation, and time-temperature precipitation maps. A test matrix of SSM and conventional creep tests (CCTs) are executed for alloy Inconel 718 at 750°C (1,382°F) with stress levels ranging from 100 to 350 MPa. Validation CCT data are gathered from the Japan National Institute of Material Science. Material constants for the Sine-hyperbolic (Sinh) constitutive model are calibrated using the SSM data and employed to predict the conventional creep response. When blindly compared with the CCT data, the SSM-calibrated Sinh model can accurately predict the conventional creep response across logarithmic decades and, thus, accelerate the capture of conventional creep data. Fractography indicates ductile fracture by transgranular microvoid coalescence with the same fracture mode observed in both SSM and CCT specimens. Creep cavitation is indicated by the population, smoothness, and size of microvoids. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetals$xCreep. =650 \0$aMetals$xTesting. =650 \0$aMaterials$xCreep. =700 1\$aHossain, Md Abir,$eauthor. =700 1\$aPellicotte, Jacob,$eauthor. =700 1\$aMach, Robert,$eauthor. =700 1\$aAlexander, David,$eauthor. =700 1\$aSiddiqui, Sanna F.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200174.html =LDR 03617nab a2200445 i 4500 =001 MPC20200181 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200181$2doi =037 \\$aMPC20200181$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA480.T54 =082 04$a621.825$223 =100 1\$aRaj, Manil,$eauthor. =245 10$aEffect of Bonding Temperature and Interlayer(s) on Microstructure Evolution, Hardness, and Shear Properties of Diffusion Bonded Ti-6Al-4V Alloys /$cManil Raj, M. J. N. V. Prasad, K. Narasimhan. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe workhorse Ti-6Al-4V alloy has numerous applications under extreme conditions, and there is a necessity to produce metallic joints with the alloy for fabrication of some industrial components. In the present study, the solid-state diffusion bonding (DB) process was used to produce similar metal joints between Ti-6Al-4V alloy sheets with and without copper and nickel interlayers. The effect of the bonding temperature as well as the influence of interlayers on the joint interface microstructure and, subsequently, on the mechanical performance of the bonded joints were investigated. The DB was performed at three different bonding temperatures of 1,023, 1,123, and 1,223 K under high-vacuum conditions using a thermomechanical deformation simulator. The microstructure across interface of the joint was examined using optical and scanning electron microscopes. The joint strength was evaluated using both the nanoindentation technique and the shear test. The findings show the formation of intermetallic phases between titanium and interlayer(s) elements across the interface up to the bonding temperature of 1,123 K. Further increase in the bonding temperature led to a complete diffusion of the interlayers into the base metals, thereby forming the Widmanstätten microstructure across the interface. In the case of direct DB, there was a gradual closure of voids along with a homogenized joint interface with an increase in the bonding temperature. The variation of hardness across the bonding interface and the shear properties were found to be consistent with the resultant microstructural features evolved with the bonding temperature and type of interlayer(s). =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetallurgy. =650 \0$aMaterials$xBiodegradation. =650 \0$aTitanium$xTesting. =700 1\$aN. V. Prasad, M. J.,$eauthor. =700 1\$aNarasimhan, K.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200181.html =LDR 03617nab a2200445 i 4500 =001 MPC20200187 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200187$2doi =037 \\$aMPC20200187$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA460 =082 04$a620.16$223 =100 1\$aTorizuka, Shiro,$eauthor. =245 10$aFormation of Ultrafine Single-Variant Martensite from Prior Ferrite + Cementite Microstructure and Its Mechanical Properties /$cShiro Torizuka, Ryusuke Oya, Kartik Prasad, Atsushi Ito. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present investigation, changes in the single-variant martensite structure of 0.1%C-2%Si-5%Mn steel with a decrease in the prior austenite grain size have been investigated. While prior austenite grain size in the range of 150 to 24 µm led to the formation of martensite with a multi-packet and multi-block structure, a single packet and multi-block martensite structure formed from the prior austenite grain size of about 7 µm. Furthermore, the prior austenite grain size of about 2 µm led to the formation of a single-variant (single-block) martensite structure. This microstructural analysis indicates that the critical prior austenite grain size to form martensite with a single-variant structure is about 2 µm. The tensile strength (TS, 1,490 MPa), uniform elongation (UEL, 7.1 %), and total elongation (TEL, 14.2 %) of the single-variant martensite was found to be higher than that of the multi-packet multi-block martensite (TS = 1,270 MPa, UEL = 6.2 %, and TEL = 13.6 %). The improvement in the mechanical properties of the single-variant martensite was attributed to enhancement in its strain-hardening rate as a result of change in the structure from the multivariant to the single variant. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetals$xMechanical properties. =650 \0$aComposite materials. =650 \0$aMechanical properties. =700 1\$aOya, Ryusuke,$eauthor. =700 1\$aPrasad, Kartik,$eauthor. =700 1\$aIto, Atsushi,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200187.html =LDR 03617nab a2200445 i 4500 =001 MPC20200189 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200189$2doi =037 \\$aMPC20200189$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTD195.E4 =082 04$a629.25$223 =100 1\$aBhaduri, A. K.,$eauthor. =245 10$aDevelopment and Qualification of Materials for Indian Advanced Ultra-Supercritical Coal-Fired Power Plant /$cA. K. Bhaduri, Shaju K. Albert, A. Nagesha, A. Moitra, Utpal Borah, G. V. Prasad Reddy, K. Laha, Kulvir Singh, A. K. Das. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIndia has embarked on an ambitious program of setting up efficient advanced ultra-supercritical (AUSC) technology with steam temperature and pressure of 993 K and 31 MPa, respectively. This article deals with the testing and qualification of indigenously produced materials for the Indian AUSC mission project, the research and development phase of which is currently in the advanced stage of completion. As part of this, exhaustive database pertaining to various mechanical properties including creep, low cycle fatigue (LCF), creep-fatigue interaction (CFI), high cycle fatigue (HCF), fracture toughness, and crack growth has been generated covering important candidate materials such as alloy 617M tubes and forgings, 304HCu stainless steel tubes, and alloy 625 castings. Tubes of both alloy 617M and 304HCu stainless steels are to be used in the boilers, whereas alloy 617M forgings would be used as turbine rotor and alloy 625 castings as turbine casings. The data have been subsequently used to establish design curves identifying safe regimes of operation with respect to creep, LCF, HCF, CFI, and fatigue and creep crack growths. The properties were seen to be comparable with those derived from internationally developed equivalent grades. The bimetallic weld joints between alloy 617M and 10Cr steels were also evaluated to derive the appropriate strength reduction factors under creep and cyclic loadings. Additionally, the influence of thermal aging at service temperature on the microstructural evolution and mechanical properties was investigated based on tensile and fracture properties to account for the service exposure induced degradation and associated embrittlement. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aCoal-fired power plants. =650 \0$aEnvironmental aspects. =650 \0$aPower-plants. =700 1\$aAlbert, Shaju K.,$eauthor. =700 1\$aNagesha, A.,$eauthor. =700 1\$aMoitra, A.,$eauthor. =700 1\$aBorah, Utpal,$eauthor. =700 1\$aPrasad Reddy, G. V.,$eauthor. =700 1\$aLaha, K.,$eauthor. =700 1\$aSingh, Kulvir,$eauthor. =700 1\$aDas, A. K.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200189.html =LDR 03617nab a2200445 i 4500 =001 MPC20200203 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200203$2doi =037 \\$aMPC20200203$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.P58 =082 04$a547.7046$223 =100 1\$aPaul, Jhon,$eauthor. =245 10$aThermo-Oxidative Behavior of Four-Directional Carbon-Carbon Composites as Throat Inserts for Solid Propulsion Systems /$cJhon Paul, B. Santhosh, E. N. Ananthapadmanabhan, P. K. Das. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (18 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aCarbon-carbon (C-C) composites are considered as one of the ideal materials of construction for high-temperature applications in rockets and dimensionally stable structures for satellites. Thermo-oxidative behavior of four-directional (4D) C-C composites makes it a candidate material for throat inserts of nozzles in solid propulsion systems. For the realization of throat inserts, although 4D C-C composites can be manufactured by different process methodologies, its selection is crucial, as the methodology dictates the material behavior to meet the functional requirements. In this study, high-density 4D C-C composites are manufactured through a unique combination of processes, which can meet the functional requirements. Thermostructural behavior of 4D C-C composites in an oxidative environment is studied, and critical insights on the performance of the material are established. The material behavior of 4D C-C composites is examined with respect to the operating environment. The phenomenon of ablation for 4D C-C composites is investigated through plasma arc jet testing. The ablation mechanism of the material and its constitutive behavior is proposed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aPolymers$xAnalysis. =650 \0$aPolymers$xDeterioration. =650 \0$aMaterials at high temperatures. =700 1\$aSanthosh, B.,$eauthor. =700 1\$aAnanthapadmanabhan, E. N.,$eauthor. =700 1\$aDas, P. K.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200203.html =LDR 03617nab a2200445 i 4500 =001 MPC20200208 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20200208$2doi =037 \\$aMPC20200208$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK9203.L5 =082 04$a621.4834$223 =100 1\$aPrasad Reddy, G. V.,$eauthor. =245 10$aCore Materials for Sodium-Cooled Fast Reactors: Past to Present and Future Prospects /$cG. V. Prasad Reddy, V. Karthik, S. Latha, C. N. Venkiteswaran, Divakar Ramachandran, Shaju K. Albert. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (51 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe Sodium-Cooled Fast Reactor (SFR) is the most promising and technologically evolved among the six nuclear reactor concepts selected by the Generation IV International Forum. Although it is compatible with a closed fuel cycle for sustainable energy production, its competitiveness depends on being able to achieve high fuel burn-up up to 200 GWd/t. This would enable efficient fuel utilization to minimize fuel cycle costs. Hence, development of optimized core materials, especially for fuel cladding tubes that are subjected to extreme conditions of intense fast-spectrum neutron irradiation, high temperatures, and mechanical and chemical fuel–cladding interactions, continues to be a priority worldwide. Resistance to void swelling, irradiation creep, and embrittlement are required to be enhanced to minimize dimensional changes and loss of ductility in core components, which limit achievable burn-up. Current SFR core materials comprise austenitic stainless steels (SS) and ferritic-martensitic (FM) steels. Cold-worked austenitic SS grades 304, 316, 316Ti, niobium-stabilized grades FV548, EI-847, EP-172, and Ti-modified 15Cr-15Ni SS, such as D9, 1.4970, 15/15Ti SS, and ChS-68, have been used for fuel cladding and ducts in SFRs built to date, and they withstand neutron irradiation damage up to 80–100 dpa. Subsequent improvements have been made by optimizing minor elements (titanium, silicon, and phosphorous) and multi-stabilization to develop advanced grades such as Si-modified 15-15Ti, Indian Fast Reactor Advanced Clad (IFAC-1), PNC-316, EK-164, and HT-UPS, which could support burn-up of 150 GWd/t. In the case of FM steels, several commercial grades are found suitable in view of their inherent void swelling resistance to 200 dpa, and are being developed for improved creep strength by oxide dispersion strengthening to realize burn-up of 200–250 GWd/t. This article presents the development of structural materials for SFR fuel pin cladding and ducts and associated enhancement of permissible fuel burn-up. Indian and international experience resulting from extensive in-pile and out-of-pile mechanical testing and fuel–cladding interactions has been covered. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aSodium cooled reactors. =650 \0$aBreeder reactors. =650 \0$aLiquid metal cooled reactors. =700 1\$aKarthik, V.,$eauthor. =700 1\$aLatha, S.,$eauthor. =700 1\$aVenkiteswaran, C. N.,$eauthor. =700 1\$aRamachandran, Divakar,$eauthor. =700 1\$aAlbert, Shaju K.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 2 (January 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20200208.html =LDR 03617nab a2200445 i 4500 =001 MPC20210055 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210055$2doi =037 \\$aMPC20210055$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK4660 =082 04$a671.5212$223 =100 1\$aKheradmandan, Hasan,$eauthor. =245 10$aModeling and Optimizing the Penetration in the Submerged Arc Welding Process in the Presence of ZrO Nanoparticles /$cHasan Kheradmandan, Masood Aghakhani, Tahereh Kheradmandan, Sepideh Kheradmandan, Maziar Mahdipour Jalilian, A. Ghiasvand, Seyed Abbas Hosseini. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (21 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPenetration is one of the most vital parameters because of its influences on weld strength and weld quality. Choosing the input parameters in submerged arc welding (SAW) has significant effects on input heat into the weld pool, which affects the quality of weldment. The amazing advancement of nanotechnology in various industrial areas persuaded researchers to use nanoparticles in new research. Zirconium dioxide (ZrO2) nanoparticles were selected in order to identify their effects in the weld pool in combination with other welding input parameters. The five-level, five-parameter central composite rotatable design, response surface methodology, the slime mold algorithm, and Harris hawks optimization were utilized to design and develop the research and finally to predict and optimize the weld penetration affected by the arc voltage, welding current, nozzle-to-plate distance, welding speed, and the thickness of ZrO2 nanoparticles coated on ST-37 steel. The main and interaction effects of input parameters on weld penetration were drawn. The results demonstrated that weld penetration decreased initially by increasing the thickness of ZrO2 nanoparticles up to 0.25 mm, which was due to reversing Marangoni convection mode. Furthermore, weld penetration increased with increase in ZrO2 nanoparticles above thicknesses of 0.75 mm. The reason for increase in weld penetration was because of the fact the ZrO2 nanoparticles have low thermal conductivity, which leads to less heat transfer. The results confirmed that the accuracy of model obtained by slime mold algorithm was 5.2 % more than response surface methodology. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aElectric welding. =650 \0$aWelding. =650 \0$aAluminum alloys$xWelding. =700 1\$aAghakhani, Masood,$eauthor. =700 1\$aKheradmandan, Tahereh,$eauthor. =700 1\$aKheradmandan, Sepideh,$eauthor. =700 1\$aMahdipour Jalilian, Maziar,$eauthor. =700 1\$aGhiasvand, A.,$eauthor. =700 1\$aAbbas Hosseini, Seyed,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210055.html =LDR 03617nab a2200445 i 4500 =001 MPC20210057 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210057$2doi =037 \\$aMPC20210057$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD461 =082 04$a546.3$223 =100 1\$aMangal, Pradyumna,$eauthor. =245 10$aMechanical Recycling of Metal-Bonded Multilayered Flexible Packaging /$cPradyumna Mangal, Navami Mohan, P. C. Vishakh Raja, Thamizh R. Selvan, Shantanu Bhowmik. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSince the introduction of multilayered flexible plastics (MLFP) in the global market, their consumption has been on a rise. Because of the use of different plastics and metals with varying properties, recycling this form of packaging is a tedious task and a huge challenge for humanity. In this work, an attempt is made to recycle this waste using the methods in mechanical recycling to make useful commodities. After the making these commodities, their mechanical properties, such as tensile and compression strength, are tested, and the results are discussed. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aChemical bonds. =650 \0$aMetals. =650 \0$aMetal bonding. =700 1\$aMohan, Navami,$eauthor. =700 1\$aVishakh Raja, P. C.,$eauthor. =700 1\$aSelvan, Thamizh R.,$eauthor. =700 1\$aBhowmik, Shantanu,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210057.html =LDR 03617nab a2200445 i 4500 =001 MPC20210080 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210080$2doi =037 \\$aMPC20210080$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA460 =082 04$a620.16$223 =100 1\$aKumar, Rajinder,$eauthor. =245 10$aEffect of Yttria-Stabilized Zirconia (Y2O3/ZrO2) Nanoparticles Reinforced Cr3C2-25NiCr Coatings on the Microstructural and Mechanical Properties of Turbine Steel /$cRajinder Kumar, Deepak Bhandari, Khushdeep Goyal. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe present work is mainly focused on the investigation of Cr3C2-25NiCr coatings reinforced with 5 % and 10 % of yttria-stabilized zirconia (YSZ) nanoparticles deposited on the CA6NM turbine steel by using the high-velocity oxy-fuel technique. The coatings were analyzed by scanning electron microscope (SEM)/energy-dispersive X-ray spectroscopy (EDS). The phase identification of a crystalline material was done with the X-ray diffraction (XRD) technique. The SEM/EDS analysis showed that dense and homogeneous coatings were developed by the reinforcement of YSZ nanoparticles. The peaks of XRD graphs of Cr3C2-25NiCr coating reinforced with 5 % and 10 % of YSZ nanoparticles revealed that the chromium and carbon were present as a major phase, and the presence of nickel, yttrium, and zirconium was observed as a minor phase. The porosity level decreased up to 32 % and 45 % by the addition 5 % and 10 % of YSZ nanoparticles as compared with conventional Cr3C2-25NiCr coating. The surface roughness values for coated samples were found to be 5.03, 4.89, and 4.28. The nanocomposite coatings reinforced with 10 % YSZ nanoparticles exhibited the highest microhardness value (1,251 HV). The Cr3C2-25NiCr coatings reinforced with 10 % of YSZ nanoparticles resulted in low porosity, low surface roughness, and high microhardness. During the coating process, the nanoparticles of YSZ flow into the pores and gaps that exist in the coatings and provide a better shield to the substrate material. The Cr3C2-25NiCr with 10 % of YSZ nanoparticles showed better results in terms of mechanical and microstructural properties during the investigation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetals$xMechanical properties. =650 \0$aIntermetallic compounds$xMechanical properties. =650 \0$aMechanical properties. =700 1\$aBhandari, Deepak,$eauthor. =700 1\$aGoyal, Khushdeep,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210080.html =LDR 03617nab a2200445 i 4500 =001 MPC20210086 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210086$2doi =037 \\$aMPC20210086$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA403 =082 04$a621.4833$223 =100 1\$aBhyravajoshulu, Shashank Dutt,$eauthor. =245 12$aA Study on the Effect of Test Temperatures on Tensile and Fracture Behavior of SS 316LN /$cShashank Dutt Bhyravajoshulu, Nani Babu Matcha, Shanthi Ganesan, Ganesan Vidyanathan, Aniruddha Moitra. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn the present study, the influence of test temperatures in the range of 25°C–550°C on the deformation and fracture behavior of SS 316LN has been investigated. The tensile properties and fracture toughness (J1c) of SS 316LN have been evaluated in this temperature range. From tensile properties, strain energy density was estimated as a function of plastic strain and strain-hardening parameters. The fracture tests (J-R curves) are conducted in this temperature range to determine fracture toughness and tearing resistance. From the fracture tested specimens, fractographic studies were carried out to further understand crack initiation mechanisms. From the results of fracture toughness in the temperature range of 350°C–450°C, an attempt to understand the deformation mechanism was made based on an empirical equation. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMartensitic transformations. =650 \0$aFracture mechanics. =650 \0$aNotched bar testing. =700 1\$aMatcha, Nani Babu,$eauthor. =700 1\$aGanesan, Shanthi,$eauthor. =700 1\$aVidyanathan, Ganesan,$eauthor. =700 1\$aMoitra, Aniruddha,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210086.html =LDR 03617nab a2200445 i 4500 =001 MPC20210089 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210089$2doi =037 \\$aMPC20210089$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTN799.M2 =082 04$a669.7$223 =100 1\$aMuraliraja, R.,$eauthor. =245 10$aThe Effects of Electroless Ni-P Coated SiC on the Properties of Magnesium Composite /$cR. Muraliraja, K. Pradeepkumar, P. Mohanraj, T. Vinod Kumar, C. Dhanasekaran, M. Chandrasekaran, S. Ragavanantham, V. S. Shaisundaram. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aReuse of magnesium alloy is an essential approach to protecting the natural resources, and it eliminates the waste products dumped in landfills, water, and air. Therefore, the first time the scrap magnesium alloy materials are collected and fabricated, the newly formulated magnesium composites use different techniques, such as vacuum, squeeze, and stir casting. AZ91 alloy from the automobile scrap is used as matrix material, and silicon carbide (SiC) is used as reinforcement. Electroless nickel-phosphorous coating is applied to the ceramic particles to avoid unwanted chemical reactions during the casting process. The adhesion between the matrix and reinforcement is improved by masking the surface of the nonmetallic SiC particles. Magnesium composite is most commonly used in automotive and aerospace applications to reduce weight and improve the strength of the component. The magnesium composite is fabricated through four different methods, and the substrates are tested and analyzed for better results. The sample results taken from the composites are compared to the magnesium alloy obtained from the scrap stock. Comparatively, the substrate produced using squeeze casting shows a lower porosity level of 5.5 %, and it is clearly shown in optical images. Significant improvements in the mechanical properties, such as hardness and compression strength, are obtained, and the wear rate in the prepared composites is reduced to 28 % for the sample produced using squeeze casting instead of the vacuum and stir casting processes. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMagnesium alloys. =650 \0$aMagnesium Composite. =650 \0$aElectrolyte solutions. =700 1\$aPradeepkumar, K.,$eauthor. =700 1\$aMohanraj, P.,$eauthor. =700 1\$aVinod Kumar, T.,$eauthor. =700 1\$aDhanasekaran, C.,$eauthor. =700 1\$aChandrasekaran, M.,$eauthor. =700 1\$aRagavanantham, S.,$eauthor. =700 1\$aShaisundaram, V. S.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210089.html =LDR 03617nab a2200445 i 4500 =001 MPC20210091 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210091$2doi =037 \\$aMPC20210091$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL500 =082 04$a629.472$223 =100 1\$aGibson, Cody,$eauthor. =245 10$aResults of a Pilot Study in Support of a Round-Robin on Creep-Fatigue Crack Growth Testing of a Creep-Brittle Material for ASTM E2760 /$cCody Gibson, Robert Stephens, Santosh B. Narasimhachary, David E. Mills, Andrew Rosenberger. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (14 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis paper describes pilot test results from a round-robin conducted in support of the standard ASTM E2760, Standard Test Method for Creep-Fatigue Crack Growth Testing, on creep-fatigue crack growth testing. Results from the pilot study are recommended to participants to develop their individual experimental testing. This round-robin is an international effort with 10 participants from five countries from Asia, North America, and Europe. All participants are testing compact type (C(T)) specimens according to the procedure described in the standard. A few participants are evaluating the Kb-bar (surface crack) specimen configuration. The test material is Inconel-718 (IN718) nickel-based alloy, which is a creep-brittle alloy. Pilot creep-fatigue crack growth tests were conducted at 600°C using C(T) specimens under constant load amplitude conditions. The tests were conducted at hold times of 0, 60, and 600 s. Creep-fatigue crack growth rates were analyzed using the methods proposed and included in the test standard. It was found that the procedures followed throughout the pilot test program were sufficient in generating the desired outcomes. As a result, it is proposed that the various participants follow the procedures and test matrix as close as possible and document any deviations. This will allow data from the various participants to be assessed and determine the levels of precision and bias in creep-fatigue crack growth data obtained using the ASTM standard. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aBrittleness. =650 \0$aCeramic materials. =650 \0$aMetals$xBrittleness. =700 1\$aStephens, Robert,$eauthor. =700 1\$aNarasimhachary, Santosh B.,$eauthor. =700 1\$aMills, David E.,$eauthor. =700 1\$aRosenberger, Andrew,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210091.html =LDR 03617nab a2200445 i 4500 =001 MPC20210095 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210095$2doi =037 \\$aMPC20210095$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA404.6 =082 04$a666.04$223 =100 1\$aKamal, Anurag,$eauthor. =245 12$aA Comparative Study on the Oxidative Stability of Polycarbosilane-Based C /C–SiC and C /SiC Composites /$cAnurag Kamal, Anil Painuly, Shyin Palani Prabhakaran, S. Packirisamy. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA carbon/carbon–silicon carbide (C/C–SiC) composite was prepared by first fabricating a C/C preform using carbon fiber and phenolic resin and subsequently densifying with a polymer precursor of SiC, viz., polycarbosilane (PCS). The C/SiC composite was realized by using PCS. These composites were machined and were subjected to oxidation resistance tests at 1,000°C and 1,500°C under a constant flow of air (6 slpm (standard litre per minute)) for a total duration of 60 min. The oxidation study was extended to the porous C/C preform and a commercially available dense C/C composite. The plot of mass loss versus time for all four types of composites indicates early saturation of mass loss for C/SiC, delayed saturation for C/C–SiC, whereas there was no saturation for C/C composites. The reasons for this behavior are analyzed using a scanning electron microscope equipped with an electron dispersive spectrometer, which reveal that the higher SiC content in C/SiC composite is responsible for self-sealing of the pores even at 1,500°C, whereas the lesser SiC content in C/C–SiC composite and C/C composites is unable to deliver the same results for the chosen set of experiments. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$apolycarbosilane. =650 \0$aMaterials. =650 \0$aComposite materials. =700 1\$aPainuly, Anil,$eauthor. =700 1\$aPrabhakaran, Shyin Palani,$eauthor. =700 1\$aPackirisamy, S.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210095.html =LDR 03617nab a2200445 i 4500 =001 MPC20210096 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210096$2doi =037 \\$aMPC20210096$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTL242 =082 04$a629.231$223 =100 1\$aBrett, S. J.,$eauthor. =245 10$aImpression Creep Workshop Agreement Activity /$cS. J. Brett, W. Sun, J. H. Rantala, D. Purdy, A. Bridges, J. Eaton-Mckay, C. Austin, J. Holden, A. Clark, B. Kuhn, D. Omacht. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aImpression creep testing is now an established, small-scale testing technique in which the indentation rate of a rectangular indenter can be converted into an equivalent uniaxial creep strain rate. Its increasing use and practical application to power plants has led to a need for standardization. This paper reports on activity by six laboratories currently using the technique to produce a CEN Workshop Agreement covering this testing methodology. Consensus is being sought on the details of the test itself, both in the form of the original single step test and in the form of the more complex stepped stress test, which can provide data at multiple test conditions in the same specimen. Associated matters being addressed include the standardization of specimen and indenter sizes; a standard methodology for measuring the indentation rate and the creep strain rate, with an appropriate validity check; and an agreement on a pretest rig hysteresis check. A further activity will define a maximum indentation depth, supported by finite element analysis. The agreed impression creep test procedure will be used in an interlaboratory “Round Robin” exercise on selected materials. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetals$xTesting. =650 \0$aMetals$xStress corrosion$xTesting. =650 \0$aAlloys$xFatigue$xTesting. =700 1\$aSun, W.,$eauthor. =700 1\$aRantala, J. H.,$eauthor. =700 1\$aPurdy, D.,$eauthor. =700 1\$aBridges, A.,$eauthor. =700 1\$aEaton-Mckay, J.,$eauthor. =700 1\$aAustin, C.,$eauthor. =700 1\$aHolden, J.,$eauthor. =700 1\$aClark, A.,$eauthor. =700 1\$aKuhn, B.,$eauthor. =700 1\$aOmacht, D.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 3 (October 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210096.html =LDR 03617nab a2200445 i 4500 =001 MPC20210099 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210099$2doi =037 \\$aMPC20210099$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK148 =082 04$a621.3$223 =100 1\$aHiyoshi, Noritake,$eauthor. =245 10$aChallenge of Establishing Materials Testing Standards with Miniature Specimen for Solders /$cNoritake Hiyoshi, Takamoto Itoh, Takaei Yamamoto, Hideyuki Kanayama. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aSolder is an essential material for connecting parts inside electrical devices. Although there is an international standard for the chemical composition of solder, there is no testing standard for evaluating the mechanical properties and characteristics of solder as a structural material. The Committee on High Temperature Strength of Materials, the Society of Materials Science, Japan, proposed some testing standards for solders in the early 2000s based on the results from research activities of the Solder Strength Evaluation Method Working Group. The primary objective of the standardization at that time was to acquire stable testing data and to eliminate institutional differences. The recommended specimen diameter is 10 mm. To verify the size difference between the 10-mm-diameter specimen and an actual solder joint inside an electrical device, the working group has been investigating materials testing techniques using a specimen with a reduced diameter of 3 mm. The research results were published in 2020 as Standard for Miniature Testing of Solders. We have also conducted a series of systematic experiments based on the testing standards for Sn-3.0Ag-0.5Cu. The results obtained so far are as follows: In the tensile tests, the tensile strength of the 10-mm- and 3-mm-diameter specimens are almost identical, independent of the specimen size, although the casting method and heat treatment conditions are different. The effect of specimen size on the creep rupture life is insignificant. In the low-cycle fatigue tests, stable fatigue data can be obtained even at high temperatures using the 3-mm-diameter specimen. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aElectric apparatus and appliances. =650 \0$aElectricity$xExperiments. =700 1\$aItoh, Takamoto,$eauthor. =700 1\$aYamamoto, Takaei,$eauthor. =700 1\$aKanayama, Hideyuki,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 3 (October 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210099.html =LDR 03617nab a2200445 i 4500 =001 MPC20210100 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210100$2doi =037 \\$aMPC20210100$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD565 =082 04$a541.372$223 =100 1\$aPonam,,$eauthor. =245 10$aPorous Coordination Polymers as Active Fillers for Solid Polymer Electrolytes of Lithium-Ion Batteries /$cPonam, Parshuram Singh. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe role of renewable energy is crucial for energy sustainability and depends upon the energy storage devices and their technical progress. The batteries prove themselves as reliable, efficient, and environmentally friendly energy storage devices. However, limitations such as safety issues, low energy density, leakage, etc. In view of that, solid-state electrolytes are the most promising alternative to liquid electrolytes because of their higher safety factor and potential for enough energy density. In contrast, these solid electrolytes also have limitations of low ionic conductivity and a higher interfacial resistance compared to conventional electrolytes. To overcome the mentioned limitations, the doping of filler materials in the electrolyte during synthesis is proven as one of the favorable techniques. The filler materials not just improve the ionic conductivity of the electrolyte but also enhance the thermal and mechanical stability. Furthermore, to decrease the interfacial resistance, the electrolyte should have good mechanical strength and a higher surface area. In this context, the use of microporous coordination polymers is proven to be the most practical and effective approach. The main aim of this work is to highlight the recent advancement in the applicability of porous polymers for solid-state electrolytes and to also provide the major benefits and limitations of porous material-based solid electrolytes. Along with this, a brief description of ultramodern porous coordination polymers is also included in this article. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aPolyelectrolytes. =650 \0$aLithium cells. =650 \0$aElectrolytes$xConductivity. =700 1\$aSingh, Parshuram,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210100.html =LDR 03617nab a2200445 i 4500 =001 MPC20210103 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210103$2doi =037 \\$aMPC20210103$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA409 =082 04$a620.1126$223 =100 1\$aHuang, Suxia,$eauthor. =245 10$aStudy on the Fracture Mechanisms of a Grade 91 Steel at 600°C via Interrupted Miniature Tensile Testing /$cSuxia Huang, Wei Sun, Hezong Li, Wei Sun. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe study of the deformation and fracture mechanisms of power plant materials at elevated service temperature is of utmost importance in structural integrity assessment. In this work, interrupted miniature uniaxial tensile tests (MUTT) have been conducted to investigate the fracture evolution mechanisms for a Grade 91 steel at 600°C. The engineering stress–strain curves of the MUTT can be divided into six different stages, including the elastic stage, strain hardening stage, homogeneous plastic deformation stage, necking across the transverse and thickness direction stage, and finally, the fracture propagation stage. In addition to full history tests, MUTT were interrupted in each of the different stages to study the entire failure process evolution from the uniform deformation, necking to specimen separation, using optical microscopy and Scanning Electron Microscope (SEM). It has been shown that the necking of the interrupted testing specimens appears at Stage IV across the width direction prior to the thickness direction at Stage V. The thickness direction necking would lead to fracture rapidly. The void coalescence directly caused by damage has been observed in Stage VI. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetals$xFracture. =650 \0$aWelded joints$xCracking. =650 \0$aFracture mechanics. =700 1\$aSun, Wei,$eauthor. =700 1\$aLi, Hezong,$eauthor. =700 1\$aSun, Wei,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 3 (October 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210103.html =LDR 03617nab a2200445 i 4500 =001 MPC20210104 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210104$2doi =037 \\$aMPC20210104$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA473 =082 04$a620.1724$223 =100 1\$aYaguchi, Masatsugu,$eauthor. =245 10$aRemaining Creep Life Prediction Method for In-Service Boiler Pipe Weldment Using Small Scale Specimen /$cMasatsugu Yaguchi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (22 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThe author proposes a remaining creep life prediction method for weldment of Grade 91 steel using a small specimen taken not from the weldment but from the base metal. Analysis of creep data obtained from long-term used steels indicates that the shape of the master rupture curve given by the Larson-Miller parameter remains almost the same regardless of the heat-to-heat variation of the creep life of the steels, and the life of each steel can be expressed by the parallel displacement of the master rupture curves along the abscissa direction. Therefore, we can estimate the life of used steels with only one datum even if it is obtained with a short-time creep test. This approach of extrapolation is effective for the proposed method because the number of test specimens taken from the pipe is at most two or three in power plants in Japan. The results of investigation of the relationships among creep strength, deformation, and ductility suggest that the creep deformation property primarily determines the creep life of the materials used in this study. Finally, the proposed method is applied to the in-service boiler pipe weldment of Grade 91 steel, and its features are described in comparison with the conventional life assessment method. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMaterials$xTesting$xStandards. =650 \0$aAlloys$xAnalysis. =650 \0$aAlloys$xThermomechanical properties. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 3 (October 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210104.html =LDR 03617nab a2200445 i 4500 =001 MPC20210106 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210106$2doi =037 \\$aMPC20210106$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA410 =082 04$a620.1126$223 =100 1\$aTsurui, M.,$eauthor. =245 10$aOptimization and Verification of Ultra-Miniature Specimen for Evaluating Creep Property of In-Service Component Material under Uniaxial Loading /$cM. Tsurui, C. Hisaka, K. Takahashi, A. Nitta, M. Yaguchi. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA practical procedure of creep life prediction has already been applied to an in-service boiler steam pipe in Japan. The procedure is based on a few creep tests by a small punch creep (SPC) specimen machined from a thin coupon sample, which is successfully taken from the outer surface of the pipe by an electric discharge sampling equipment. However, a coefficient converting the applied load into stress is required in the application of the SPC test data to the life prediction. Thus, in this study, as an alternative specimen with a dimension equivalent to a SPC disc specimen (8 mm in diameter and 0.5 mm in thickness), a thin plate specimen referred to as the ultra-miniature creep (UMC) specimen (2 mm in width, 10 mm in length, and 0.5 mm in thickness) was devised for a uniaxial tension creep test. Compared to the creep and creep-rupture properties obtained by a standard round bar (φ6 mm) specimen machined from a replaced steam pipe material (ASME Grade 91 steel), the stress-rupture relationship of the UMC specimen was found to coincide with that of the standard one. However, the creep strain and creep rate of the UMC specimen measured by a pull-rod displacement were larger than those of the standard one. From an elastic-creep analysis by a finite element method, this was attributed to superimposition of creep deformation in a grip portion clamping the UMC specimen on the creep strain in the parallel portion of the specimen. So, from the analytical results, an adjustment factor was derived to modify the creep property of the UMC specimen. As a result, application of this factor was found to lead to coincidence of the creep property between UMC and standard specimens. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetals$xCreep. =650 \0$aWire$xTesting. =700 1\$aHisaka, C.,$eauthor. =700 1\$aTakahashi, K.,$eauthor. =700 1\$aNitta, A.,$eauthor. =700 1\$aYaguchi, M.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 3 (October 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210106.html =LDR 03617nab a2200445 i 4500 =001 MPC20210107 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210107$2doi =037 \\$aMPC20210107$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.17 =082 04$a620.11292$223 =100 1\$aNakatsuka, H.,$eauthor. =245 10$aEvaluation of Internal Pressure Creep Rupture Life of Boiler Tube Using Miniature Tensile Creep Test /$cH. Nakatsuka, K. Katoh, T. Naitoh, M. Tomobe, A. Nitta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (17 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aMany studies have been made for evaluating the creep rupture life of a boiler tube. The working stress of a tube under internal pressure is calculated mostly by the mean-diameter formula adopted in design for pressurized components. However, this stress is not always representative of a complex stress state under internal pressure. So, focusing on the representative stress, internal pressure and uniaxial creep tests were conducted using unused and 90,000-h used boiler tubes of Type 321 stainless steel in this study. A miniature specimen (1.5 mm in width, 1.5 mm in thickness, and 25 mm in length) for the uniaxial test was taken from the middle of the tube wall in the direction of the maximum principal stress. As a result, the mean-diameter formula did not present good agreement between internal pressure and uniaxial creep rupture lives. Hence, as an alternative stress, von Mises equivalent stress, which presents good correlation between uniaxial and multiaxial creep rupture properties, was chosen. The equivalent stress, σ*, at the middle of a tube wall was calculated using Rimrott’s solution to internal pressure creep of thick-walled tubes considering large deformation. Because σ* increases with creep strain under internal pressure, σ* at εθo = εθof / 2 (where, εθo and εθ0f are tangential and tangential rupture strains on the outer diameter, respectively) was employed as the representative stress. Consequently, this stress resulted in good agreement between both creep rupture lives for the unused tube. However, the internal pressure creep rupture life of the used tube was inconsistent with the uniaxial life, which was attributed to the existence of an outside layer due to exposure to combustion gas. Using a reduction rate of the rupture ductility of the layer, the internal pressure creep rupture life of the used tube was evaluated well with the unused tube. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetals$xFracture. =650 \0$aNotched bar testing. =700 1\$aKatoh, K.,$eauthor. =700 1\$aNaitoh, T.,$eauthor. =700 1\$aTomobe, M.,$eauthor. =700 1\$aNitta, A.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 3 (October 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210107.html =LDR 03617nab a2200445 i 4500 =001 MPC20210113 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210113$2doi =037 \\$aMPC20210113$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.6 =082 04$a620.11228$223 =100 1\$aWelschen, Romy,$eauthor. =245 10$aSmall Punch Test Setup for In-Cell Testing of Irradiated Materials /$cRomy Welschen, Frideriki Naziris, Peter ten Pierick, Murthy Kolluri. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (9 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA number of surveillance programs for pressurized water reactor (PWR)-type reactors do not contain enough surveillance samples for their long-term operation (LTO) beyond the original design life of 40 years. The use of testing methods based on small/sub-sized specimen is considered a promising approach to overcome this limitation. In addition, small specimen testing will lead to a reduction in the costs of testing radioactive materials, particularly when it comes to the radiation protection measures and radioactive waste management. One miniature testing method that has been recently standardized is the small punch test (SPT) technique, which can be used for estimating mechanical properties such as yield strength (σYS) and tensile strength of structural components. In literature, various validation studies can be found on the estimation of mechanical properties using SPT on nonirradiated materials. However, SPT data regarding (highly) irradiated materials are scarce. Material characterization in hot cells introduces several challenges, such as remote handling of instrumentation and samples, manipulator sensitivity, and limited accessibility of the setup. Within the framework of the STRUctural MATerials research for safe Long Term Operation of LWR NPPs (STRUMAT) project, the Nuclear Research and Consulting Group has developed tools and in-cell methods for producing and testing irradiated SPT disks. This paper presents a newly developed SPT fabrication and test setup that works under hot-cell conditions. Preliminary test results for estimation of tensile properties of 15Kh2NMFA reference material under hot-cell machining and testing condition are presented in this paper. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMaterials$xEffect of radiation on. =650 \0$aMicrostructure. =700 1\$aNaziris, Frideriki,$eauthor. =700 1\$aten Pierick, Peter,$eauthor. =700 1\$aKolluri, Murthy,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 3 (October 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210113.html =LDR 03617nab a2200445 i 4500 =001 MPC20210118 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210118$2doi =037 \\$aMPC20210118$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP894.5 =082 04$a667.140272$223 =100 1\$aAridi, Aida Safina,$eauthor. =245 10$aIsolation of Cellulose from Mature Pods and How Different Bleaching Agents Affect Its Characterization /$cAida Safina Aridi, Yus Aniza Yusof, Chin Nyuk Ling, Nur Akmal Ishak, Nor Nadiah Mohammad Yusof. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (8 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA Fourier-transform infrared spectrometer was used to investigate the effect of using different bleaching agents during the bleaching process on the functional group of cellulose obtained from Leucaena leucocephala pods. The spectra showed that fiber treated with 5 % sodium hypochlorite (NaCIO) showed a similar functional group with the commercial cellulose. Moreover, the chemical composition analysis and whiteness index showed that fiber treated with NaCIO produced 89.37 % cellulose. The whiteness index was 78.5 %, which was the highest. Therefore, these results are expected to provide insight into the potential of utilizing L. leucocephala pods as the alternative raw material for the isolation of cellulose, as the pods of these plants are underutilized. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aBleaching. =650 \0$aBleaching materials. =650 \0$aBleaching industry. =700 1\$aYusof, Yus Aniza,$eauthor. =700 1\$aNyuk Ling, Chin,$eauthor. =700 1\$aIshak, Nur Akmal,$eauthor. =700 1\$aMohammad Yusof, Nor Nadiah,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210118.html =LDR 03617nab a2200445 i 4500 =001 MPC20210121 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210121$2doi =037 \\$aMPC20210121$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP247.5 =082 04$a541.345$223 =100 1\$aChai, Maozhou,$eauthor. =245 12$aA Graphene Oxide–Based Hydrogel with Excellent Adhesive, Tough, and Antibacterial Properties /$cMaozhou Chai, Meiwen An, Xiangyu Zhang. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (7 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aHydrogels have attracted extensive attention in the field of wound dressing because of the high water content and a structural similarity to human soft tissue. However, the hydrogels are usually vulnerable and easy to be destroyed during movement. Moreover, the hydrogels without antibacterial function cannot prevent bacterial infection during chronic wound healing. In this work, graphene oxide (GO) containing polyacrylamide hydrogel with both adhesiveness and superior mechanical properties was prepared. Since GO possesses good photothermal conversion capability and photodynamic property, the hybrid hydrogel exhibits excellent antibacterial property under the irradiation of near-infrared light. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aPharmaceutical biotechnology. =650 \0$aColloids. =650 \0$aDiabetes$xTreatment. =700 1\$aAn, Meiwen,$eauthor. =700 1\$aZhang, Xiangyu,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210121.html =LDR 03617nab a2200445 i 4500 =001 MPC20210122 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210122$2doi =037 \\$aMPC20210122$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA404.6 =082 04$a620.18$223 =100 1\$aAbendroth, Martin,$eauthor. =245 10$aCharacterization of Iron-Based Shape Memory Alloys Using the Small Punch Test /$cMartin Abendroth, Anna Hasche, Tarak Ben Zineb, Bjöern Kiefer. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIron-based shape memory alloys (Fe-SMAs) are currently of high interest for potential smart material applications in civil engineering construction but also other fields that do not require biocompatibility but demand low cost of the SMA. The envisioned civil engineering application examples, for some of which prototypes have already been realized, include connectors in concrete, metal, and timber structures, concrete reinforcement, and isolators/dampers for earthquake-resistant technologies. In this contribution, we first present results regarding the experimental characterization of Fe-SMAs using a versatile miniaturized testing method, specifically the small punch test (SPT). Its main advantages are that it is relatively simple, requires only small amounts of material, and allows testing under well-defined biaxial stress states (triaxiality of approximately 0.6). The difficulty of identifying material parameters with this test and its variants is that it always requires the numerical solution of an inverse problem because the experiment records a structural response rather than a pure constitutive response. To address this, an in-house parameter identification tool has been developed, which combines finite element analysis, user-defined material models, and nonlinear optimization algorithms. Building on this expertise, our current contribution investigates the employment of the SPT as an efficient methodology to characterize Fe-SMAs under biaxial loading. Such data is of great interest to constitutive model developers for both calibration and validation purposes. Generally, sufficiently rich experimental data on SMA behavior that goes beyond results obtained in one-dimensional tests (e.g., tension-compression-torsion or planar-biaxial loading) is scarce in the literature. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMaterials science. =650 \0$aCharacterization and Evaluation of Materials. =700 1\$aHasche, Anna,$eauthor. =700 1\$aBen Zineb, Tarak,$eauthor. =700 1\$aKiefer, Bjöern,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 3 (October 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210122.html =LDR 03617nab a2200445 i 4500 =001 MPC20210125 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210125$2doi =037 \\$aMPC20210125$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA418.32 =082 04$a620.1126$223 =100 1\$aKomazaki, Shin-ichi,$eauthor. =245 10$aApplication of SBF Test to Fatigue Damage Assessment of Type 316 Steel /$cShin-ichi Komazaki, Kosuke Egami, Masayuki Kamaya, Chiaki Hisaka, Akito Nitta. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA new fatigue testing technique, the small bulge fatigue (SBF) test, was recently developed by some of the present authors. In this technique, a cyclic oil pressure is alternatively applied to both surfaces of a small disk-type specimen (8 mm in diameter) with flat and concave surfaces. This SBF test is a kind of biaxial fatigue test as well as the disk bending fatigue (DBF) test. In this study, damaged specimens were subjected to the SBF test to examine the adaptability of this test to the fatigue damage assessment of actual components. To prepare these damaged specimens, Type 316 austenitic stainless steel was subjected to the DBF test using large disk specimens (87 mm in diameter) by considering that most of components were generally operating under multiaxial loading condition. The test was stopped at several stages of the fatigue life. Then, the SBF test specimens were taken from the surfaces of the interrupted DBF test specimens. It was expected that fatigue life of the SBF tests corresponded to the degrees of fatigue damage induced by the DBF test. The SBF test results showed that the fatigue life of the damaged SBF specimen, which contained microcracks formed by the DBF test, was only one tenth as long as that of the undamaged specimen. It was noteworthy that some microcracks introduced by the DBF test were opened and became clearly visible after the SBF test, although they were closed and not visible just after the DBF tests. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMaterials$xFatigue. =650 \0$aThin-walled structures. =650 \0$aHeat resistant alloys. =700 1\$aEgami, Kosuke,$eauthor. =700 1\$aKamaya, Masayuki,$eauthor. =700 1\$aHisaka, Chiaki,$eauthor. =700 1\$aNitta, Akito,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 3 (October 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210125.html =LDR 03617nab a2200445 i 4500 =001 MPC20210127 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210127$2doi =037 \\$aMPC20210127$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTP247.5 =082 04$a540$223 =100 1\$aLu, Yu,$eauthor. =245 10$aPhotocatalytic Degradation of Printing and Dyeing Wastewater by F-N/TiO /AC and F-N/TiO /MAC Composite Photocatalysts /$cYu Lu, Zhen Chen, Yingying Zhu, Zhenguo Xia, Geng Chen. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (12 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA fluorine/nitrogen-co-doped titania/activated carbon (F-N/TiO2/AC) composite has been prepared through an immersion–hydrothermal method. Magnetic activated carbon (MAC) has been prepared through a chemical coprecipitation method and used to assemble the analogous composite F-N/TiO2/MAC. The characterization results show that F-N/TiO2/MAC contains a certain amount of magnetic ferrous oxide material, and the presence of magnetic ferrous oxide material will not affect the crystalline shape of TiO2. F-N/TiO2/MAC is a weak magnetic material, and it could be conveniently recycled by applying a strong magnetic field. Methyl orange solution has been used as a target to assess the photocatalytic degradation and recycling performances of the composites. Results show that the adsorption of methyl orange on the photocatalysts follows a pseudo second-order kinetic model, and the adsorption rate of F-N/TiO2/AC is higher. In the photocatalytic degradation of methyl orange pseudo first-order reaction kinetics study, the k value of F-N/TiO2/MAC was 0.00497 min−1, which was higher than that of F-N/TiO2/AC. Even though the adsorption performance of F-N/TiO2/MAC is not as good as that of F-N/TiO2/AC, its photocatalytic degradation performance is superior. Overall, the two composite materials show roughly the same removal efficiencies for methyl orange, reaching 100 % for F-N/TiO2/AC and 98.9 % for F-N/TiO2/MAC. In terms of recycling performance, the magnetic property of F-N/TiO2/MAC makes it easier to recover from mixed solutions. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aPhotochemistry. =650 \0$aTetrachloroethylene. =650 \0$aHazardous wastes$xPurification. =700 1\$aChen, Zhen,$eauthor. =700 1\$aZhu, Yingying,$eauthor. =700 1\$aXia, Zhenguo,$eauthor. =700 1\$aChen, Geng,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210127.html =LDR 03617nab a2200445 i 4500 =001 MPC20210131 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210131$2doi =037 \\$aMPC20210131$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTK4660 =082 04$a721.044742$223 =100 1\$aSankar, N.,$eauthor. =245 10$aPerformance and Characteristics of Stationary Arc and Rotating Arc-Gas Metal Arc Welded DMR 249 Naval Grade Steel Joints /$cN. Sankar, S. Malarvizhi, V. Balasubramanian. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (23 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this investigation, 12-mm thickness naval grade high-strength low-alloy steel plates were welded by rotating arc-gas metal arc welding (RA-GMAW) and stationary arc-gas metal arc welding (SA-GMAW) processes. The main objective of this work was to carry out the comparative analysis of mechanical properties and microstructural characteristics of the joints fabricated by the outlined welding processes. From this experimental work, it is found that the ultimate tensile strength, yield strength, and impact toughness of the RA-GMAW joint are 15 % higher than those of the SA-GMAW joint. This is because of the formation of a higher volume percentage of acicular ferrite microstructure and island martensite/austenite constituent in the weld metal region of the RA-GMAW joint. Moreover, from the productivity point of view, the number of passes in the RA-GMAW process was minimized to three (from six passes), and the width of the heat-affected zone was also reduced by 45 % to SA-GMAW processes. Overall, the RA-GMAW joints are found to have superior mechanical properties and microstructural characteristics compared to SA-GMAW joints. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aSteel, Structural. =650 \0$aElectric welding. =650 \0$aGirders$xWelding. =700 1\$aMalarvizhi, S.,$eauthor. =700 1\$aBalasubramanian, V.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210131.html =LDR 03617nab a2200445 i 4500 =001 MPC20210132 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210132$2doi =037 \\$aMPC20210132$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA460 =082 04$a620.16$223 =100 1\$aPrasanna Nagasai, Bellamkonda,$eauthor. =245 10$aMechanical Properties and Microstructural Characteristics of AA5356 Aluminum Alloy Cylindrical Components Made by Wire Arc Additive Manufacturing Process /$cBellamkonda Prasanna Nagasai, S. Malarvizhi, V. Balasubramanian. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (26 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aWire arc additive manufacturing (WAAM) is a high-quality technology for producing large and complicated geometries in close proximity to net shape with low-cost production resources, including welding machines and filler wires. It offers the cost-effective fabrication of large-scale metal parts with high deposition. AA5356 aluminum–magnesium (Al-Mg) alloys can reach medium strength without a solid solution and quenching treatment, thereby avoiding product distortion caused by quenching, which has attracted the attention of WAAM researchers. However, challenges during the additive manufacturing of aluminum alloys, such as porosity or poor mechanical properties, can be overcome by using arc technologies with low heat input. This paper presents metallurgical characteristics and mechanical properties of WAAM AA5356 alloy cylindrical components fabricated by gas metal arc welding (GMAW) and cold metal transferred (CMT) arc welding processes. Herein, a comparison between the welding processes and the resulting heat input shows the effect on the resulting microstructure and the mechanical properties of additively manufactured AA5356 parts. Firstly, the influence of heat input on the porosity and microstructural characteristics were analyzed. Subsequently, the effect of heat input on the mechanical properties of the cylindrical components was studied. The cylindrical component produced by CMT process exhibits fewer and smaller pores with finer grains and reduced segregation of β-(Al3Mg2) phases than the GMAW process. The component fabricated by CMT process showed isotropic superior mechanical properties (tensile properties, hardness, and impact toughness) than the component made by GMAW process. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMetals$xMechanical properties. =650 \0$aIntermetallic compounds$xMechanical properties. =650 \0$aMechanical properties. =700 1\$aMalarvizhi, S.,$eauthor. =700 1\$aBalasubramanian, V.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210132.html =LDR 03617nab a2200445 i 4500 =001 MPC20210135 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210135$2doi =037 \\$aMPC20210135$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA455.P58 =082 04$a620.19204297$223 =100 1\$aKrawczyk, Sara,$eauthor. =245 10$aSynthesis and Characterization of Electroactive PEDOT Platform with -Octylphenotiazine Derivative /$cSara Krawczyk, Sylwia Golba, Justyna Jurek-Suliga. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (13 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aPoly(3,4-ethylenedioxythiophene) (PEDOT) was synthesized in the presence of a phenothiazine derivative (PTZN_C8). The aim of the research was to use phenothiazine (PTZ) as a doping ion, investigate the possibility of synthesis, and determine the influence of PTZN_C8 on the state of order of forming PEDOT chains. The synthesis of PEDOT in the presence of a PTZN_C8 by cyclic voltammetry allowed characterizing the polymer films by determining the accumulated charge capacity. Different synthetic protocols were used to obtain layers of PEDOT as a matrix and PTZ derivative as a substance that changed the structure of a material. Layers were investigated by Fourier Transform Infrared Spectroscopy (FTIR) to identify the presence of compounds incorporated during synthesis as well as to estimate the degree of polymerization calculated to characterize the length of chains. Ultraviolet-visible spectrophotometry (UV-Vis) spectra allowed drawing releasing curves of PTZN_C8 from the PEDOT matrix. Results showed that it is possible to synthesize PEDOT with PTZN_C8, but deposited PEDOT was modified in terms of the length of the chains—as the content of the PTZN_C8 was higher, the chains were shorter. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aElectrochromic devices. =650 \0$aOptical materials. =650 \0$aSurfaces (Physics) =700 1\$aGolba, Sylwia,$eauthor. =700 1\$aJurek-Suliga, Justyna,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210135.html =LDR 03617nab a2200445 i 4500 =001 MPC20210136 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210136$2doi =037 \\$aMPC20210136$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA479.S7 =082 04$a620.17$223 =100 1\$aKarnati, Sreekar,$eauthor. =245 12$aA Comparative Study on Representativeness and Stochastic Efficacy of Miniature Tensile Specimen Testing /$cSreekar Karnati, Sriram Praneeth Isanaka, Yunlu Zhang, Frank F. Liou, Jason L. Schulthess. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (16 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aIn this article, a miniature dog bone tensile coupon design was tested against the existing ASTM standard specimen design. Specimens were prepared from commercially sourced austenitic stainless steel 304 alloy, and a defect-ridden additively manufactured 304L alloy was studied. By utilizing a tensile specimen design that is 1/230th volume of the smallest ASTM E8-04(2016), Standard Test Methods for Tension Testing of Metallic Materials, dog bone specimen, coupled to a digital image correlation (DIC) setup, case studies were performed to compare tensile property measurements and strain field evolution. Whereas yield strength measurements were observed to be similar, post-yield, the ultimate strength measurements and ductility measurements from the miniature specimens were observed to be higher than the ASTM specimen design. Although the strength measurements were comparable, the strain evolution was found to differ in the miniature specimens. Studies to assess effects of varying thickness and defect population were also pursued on the miniature tensile specimen. From the DIC strain field estimations, the peak local strain values at ultimate tensile strength were observed to be increasing with reducing specimen thickness. Testing of defect ridden stainless steel revealed the sensitivity to failure through strain localization and the influence of defect size was captured in the strength measurements. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aStainless steel industry. =650 \0$aStainless steel. =700 1\$aIsanaka, Sriram Praneeth,$eauthor. =700 1\$aZhang, Yunlu,$eauthor. =700 1\$aLiou, Frank F.,$eauthor. =700 1\$aSchulthess, Jason L.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 3 (October 2022).$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210136.html =LDR 03617nab a2200445 i 4500 =001 MPC20210142 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20210142$2doi =037 \\$aMPC20210142$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD400.5.S95 =082 04$a547.59$223 =100 1\$aAbdelgawad, Khaled,$eauthor. =245 10$aAnalytical and Numerical Study of the Ring Expansion Testing Technique /$cKhaled Abdelgawad, Ahmed Nassef, Mohamed T. Eraky. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (15 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aThis article presents a design development for the ring expansion test as an alternative technique of burst test to determine the mechanical properties of circular homogeneous thin-walled tubes in the hoop direction where it is supposed to fail. This is done by replacing the internal fluid pressure in burst test by a solid mandrel partitioned into an equal number of pieces. The numerical analyses were carried out using the commercial finite element method (FEM) package ABAQUS/CAE. The testing system consists of a multispecies mandrel assembled with two identical cones from top and bottom, and the ring specimen circumscribes the mandrel, which expands radially as a result of the cone’s axial displacement. The FEM was used to optimize the proposed design in terms of the minimum number of pieces in use. In addition, the effects of friction between the cones/the mandrel and between the ring/the mandrel are investigated. The FEM revealed that eight mandrel pieces or more are needed to preserve a uniform hoop stress throughout the ring circumference. Moreover, the FEM results in conjunction with theoretical formulas revealed that eight mandrel pieces at a minimum are required to minimize the power dissipated because of friction to a nuance value of 2 %. It is concluded that the higher the number of pieces used, the more uniform the hoop stress generated in the ring specimen. Moreover, it can effectively decrease friction effect at the ring/mandrel interface. The FEM also makes a great contribution in estimating the friction coefficients as it is restricted to be evaluated experimentally. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aBiochemical engineering. =650 \0$aChemistry. =650 \0$aBiochemistry. =700 1\$aNassef, Ahmed,$eauthor. =700 1\$aEraky, Mohamed T.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20210142.html =LDR 03617nab a2200445 i 4500 =001 MPC20220003 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20220003$2doi =037 \\$aMPC20220003$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQC176.8.E35 =082 04$a620.11297$223 =100 1\$aDakhel, A. A.,$eauthor. =245 10$aLa/V Codoping Induced Modification in the Structural, Optical, and Electrical Properties of TCO TiO Nanoparticles /$cA. A. Dakhel. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (10 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aTitanium dioxide (TiO2) anatase (A) nanoparticles co-doped with La/V ions were synthesized by a precipitation technique. The samples were structurally characterized by the X-ray diffraction and optically by the absorption spectroscopy methods. It was concluded under certain preparation conditions in the formation of substitutional solid solutions of type core/shell structure. Therefore, dielectric investigations were performed and established the creation of weak colossal permittivity (CP) with prepared La/V-codoped TiO2 (A). The results were explained in the framework of the core/shell model and doping mechanisms. The calcination of the samples at 1,000°C transformed the [A] structure to rutile [R] and removed the CP. Moreover, it was established that the preparation of the ceramic by a solid-state reaction processing technique of fine powders of mixed oxides (TiO2, La2O3, and V2O5) cannot create CP. Therefore, the preparation procedure is a critical condition to obtain CP. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMaterials$xElectric properties. =650 \0$aSolids$xElectric properties. =650 \0$aFree electron theory of metals. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20220003.html =LDR 03617nab a2200445 i 4500 =001 MPC20220007 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20220007$2doi =037 \\$aMPC20220007$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aTA404.6 =082 04$a669.9$223 =100 1\$aPranesh Rao, K. M.,$eauthor. =245 12$aA Novel LiNO -Based Eutectic Salt Mixture for Industrial Heat Treatment /$cK. M. Pranesh Rao, K. Narayan Prabhu. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aA potassium nitrate–lithium nitrate–sodium nitrate (KNO3-LiNO3-NaNO3) eutectic mixture having a low melting point has been proposed as an alternative high-temperature quench medium. Inconel and steel probes were used to compare the quench performance of a conventional sodium nitrite (NaNO2) eutectic mixture and the proposed alternative medium at different bath temperatures. For the Inconel probe, the heat extraction rate was higher in the eutectic LiNO3 mixture maintained at 150°C. At elevated bath temperatures of 200°C, 250°C, and 300°C, the heat extraction rate was higher in the eutectic NaNO2 mixture. AISI 52100 steel probes quenched in eutectic LiNO3 quench medium at 150°C and 200°C showed higher hardness. At bath temperatures of 250°C and 300°C, the hardness of AISI 4140 steel probes quenched in both media was comparable. Wettability studies on Inconel and steel surfaces revealed the occurrence of nonuniform dilation of a LiNO3 eutectic mixture droplet. On the steel surface, the phenomenon occurred at lower temperatures, which resulted in an extended boiling stage and increased hardness. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aMechanical engineering. =650 \0$aMetals$xHeat treatment. =650 \0$aTempering. =700 1\$aPrabhu, K. Narayan,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20220007.html =LDR 03617nab a2200445 i 4500 =001 MPC20220016 =003 IN-ChSCO =005 20230127161000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127s2023\\\\pau|||||o|||||||||||eng|| =024 7\$a10.1520/MPC20220016$2doi =037 \\$aMPC20220016$bASTM =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQR100.8.B55 =082 04$a579.17$223 =100 1\$aFrancetic, M.,$eauthor. =245 10$aCorrosion Protection of Phosphate Conversion Coatings to Carbon Steel in the Presence of Bacterial Biofilms /$cM. Francetic, S. Madrid, M. Viera. =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2023. =300 \\$a1 online resource (11 pages) :$billustrations, figures, tables =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =504 \\$aIncludes bibliographical references. =520 3\$aDespite its relatively limited corrosion resistance, carbon steel is one of the most widely used engineering materials. An effective technique to improve its corrosion resistance, particularly during transport and storage, is phosphating. On the other hand, it is well known that different environmental bacteria can grow and develop on metal surfaces, forming biofilms. Some of those bacteria are capable of solubilizing phosphate. The objective of this work was to evaluate the stability of iron and manganese phosphate conversion coatings applied on SAE 1010 carbon steel in the presence of biofilms for two environmental bacterial strains: Pseudomonas aeruginosa and Paenebacillus sp. Both strains are biofilm-forming and phosphate solubilizing bacteria. Electrochemical techniques complemented with surface observation by scanning electron microscopy were applied. The electrochemical results showed that, although the presence of a bacterial biofilm in most cases produced a decrease in the corrosion rate, they provoked a shift of the pitting potential to more active values. This shift led to narrower passive zones, compromising the protection provided by the phosphate conversion coating to the 1010 SAE carbon steel by facilitating the onset of localized corrosion. The degree of the compromise of passivity was dependent on the coating and the bacterial strain. P. aeruginosa biofilms were more detrimental for both coatings than the Paenabacillus sp. biofilms. Thus, it is important to point out that to maintain the corrosion protection imparted by phosphate conversion coating to carbon steel, it is necessary to avoid the development of biofilms on the coated surface. =541 \\$aASTM International$3PDF$cPurchase price$hUSD25.00. =588 \\$aDescription based on publisher's website, viewed January 25, 2023. =650 \0$aBacteria. =650 \0$aBiofilms. =650 \0$aBacterial diversity. =700 1\$aMadrid, S.,$eauthor. =700 1\$aViera, M.,$eauthor. =710 2\$aAmerican Society for Testing and Materials. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =773 0\$tMaterials Performance and Characterization.$gVolume 11, Issue 1.$dWest Conshohocken, Pa. :$bASTM International, 2022$x2165-3992$yMPCACD =856 40$uhttps://www.astm.org/mpc20220016.html =LDR 01580nas a2200421 i 4500 =001 MPC20230101 =003 IN-ChSCO =005 20230127061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =245 00$aMaterials performance and characterization. =082 04$a620.11$223 =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed October 13, 2020). =588 \\$aLatest issue consulted: 2022 Volume 11, Issue 1 (viewed January 27, 2023). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/journals/volume/listing/coden/MPCACD/issue/1/volume/11/online-issue-date/2022-08-22+00%3A00%3A00/ =LDR 01580nas a2200421 i 4500 =001 MPC20230102 =003 IN-ChSCO =005 20230127061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =245 00$aMaterials performance and characterization. =082 04$a620.11$223 =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed October 13, 2020). =588 \\$aLatest issue consulted: 2022 Volume 11, Issue 2 (January 2022) (viewed January 27, 2023). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/journals/volume/listing/coden/MPCACD/issue/2/volume/11/online-issue-date/2022-01-27+00%3A00%3A00/ =LDR 01580nas a2200421 i 4500 =001 MPC20230103 =003 IN-ChSCO =005 20230127061000.0 =006 m|||||o||||||||||| =007 cr\|n||||||||n =008 230127c20129999pau|||||o|||||||||||eng|| =022 \\$a2165-3992 =022 \\$z2379-1365 =030 \\$aMPCACD =037 \\$bASTM International, 100 Barr Harbor Dr., West Conshohocken, PA 19428 =040 \\$aASTM$cSCOPE$beng$erda =041 \\$aeng =050 \4$aQD130 =245 00$aMaterials performance and characterization. =082 04$a620.11$223 =246 3\$aASTM International materials performance and characterization =246 3\$aMPC =264 \1$aWest Conshohocken, Pa. :$bASTM International,$c2012- =310 \\$aAnnual =336 \\$atext$2rdacontent =337 \\$acomputer$2rdamedia =338 \\$aonline resource$2rdacarrier =347 \\$atext file$bPDF$2rda =362 0\$aVolume 1, Issue 1 (2012)- =588 \\$aDescription based on: Volume 1, Issue 1; title from table of contents page (publisher's website, viewed October 13, 2020). =588 \\$aLatest issue consulted: 2022 Volume 11, Issue 3 (October 2022) (viewed January 27, 2023). =650 \0$aComposite materials$vPeriodicals. =650 \0$aMaterials$xAnalysis$vPeriodicals. =650 \0$aPolymers$vPeriodicals. =710 2\$aASTM International. =710 2\$aAmerican Society for Testing and Materials.$tMaterials Performance and Characterization. =710 2\$aAmerican Society for Testing and Materials. =856 40$uhttps://www.astm.org/journals/volume/listing/coden/MPCACD/issue/3/volume/11/online-issue-date/2022-10-11+00%3A00%3A00/