The deformation mechanisms of superplasticity
Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point...
Ausführliche Beschreibung
Gespeichert in:
| Autor*in: |
Hayden, H. W. [verfasserIn] |
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| Format: |
E-Artikel |
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| Sprache: |
Englisch |
| Erschienen: |
1972 |
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| Schlagwörter: |
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| Anmerkung: |
© The Metallurgical of Society of AIME 1972 |
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| Übergeordnetes Werk: |
Enthalten in: Metallurgical and materials transactions - New York, NY : Springer Sciences & Business Media, 1975, 3(1972), 4 vom: 01. Apr., Seite 833-842 |
|---|---|
| Übergeordnetes Werk: |
volume:3 ; year:1972 ; number:4 ; day:01 ; month:04 ; pages:833-842 |
| Links: |
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| DOI / URN: |
10.1007/BF02647657 |
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| 520 | |a Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point grain boundary diffusion should be the dominant diffusion path while at higher temperatures volume diffusion should dominate. At intermediate stresses, grain boundary sliding should be the major deformation mode, but the sliding rate should be governed by the lesser rate of dislocation creep within the grains. At temperatures between 40 and 65 pct of the melting point, the rate of dislocation creep should be controlled by dislocation pipe diffusion, while at higher temperatures volume diffusion should be ratecontrolling. At high stresses the superplastic effect of unusually large tensile extensibility should diminish due to the greater possibility of work-hardening processes such as dislocation cell, tangle, and pile-up formation. | ||
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10.1007/BF02647657 doi (DE-627)SPR021439419 (SPR)BF02647657-e DE-627 ger DE-627 rakwb eng Hayden, H. W. verfasserin aut The deformation mechanisms of superplasticity 1972 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Metallurgical of Society of AIME 1972 Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point grain boundary diffusion should be the dominant diffusion path while at higher temperatures volume diffusion should dominate. At intermediate stresses, grain boundary sliding should be the major deformation mode, but the sliding rate should be governed by the lesser rate of dislocation creep within the grains. At temperatures between 40 and 65 pct of the melting point, the rate of dislocation creep should be controlled by dislocation pipe diffusion, while at higher temperatures volume diffusion should be ratecontrolling. At high stresses the superplastic effect of unusually large tensile extensibility should diminish due to the greater possibility of work-hardening processes such as dislocation cell, tangle, and pile-up formation. Metallurgical Transaction (dpeaa)DE-He213 Creep Rate (dpeaa)DE-He213 Volume Diffusion (dpeaa)DE-He213 Dislocation Creep (dpeaa)DE-He213 Pipe Diffusion (dpeaa)DE-He213 Floreen, S. aut Goodell, P. D. aut Enthalten in Metallurgical and materials transactions New York, NY : Springer Sciences & Business Media, 1975 3(1972), 4 vom: 01. Apr., Seite 833-842 (DE-627)325572062 (DE-600)2037524-4 1543-1916 nnns volume:3 year:1972 number:4 day:01 month:04 pages:833-842 https://dx.doi.org/10.1007/BF02647657 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 AR 3 1972 4 01 04 833-842 |
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10.1007/BF02647657 doi (DE-627)SPR021439419 (SPR)BF02647657-e DE-627 ger DE-627 rakwb eng Hayden, H. W. verfasserin aut The deformation mechanisms of superplasticity 1972 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Metallurgical of Society of AIME 1972 Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point grain boundary diffusion should be the dominant diffusion path while at higher temperatures volume diffusion should dominate. At intermediate stresses, grain boundary sliding should be the major deformation mode, but the sliding rate should be governed by the lesser rate of dislocation creep within the grains. At temperatures between 40 and 65 pct of the melting point, the rate of dislocation creep should be controlled by dislocation pipe diffusion, while at higher temperatures volume diffusion should be ratecontrolling. At high stresses the superplastic effect of unusually large tensile extensibility should diminish due to the greater possibility of work-hardening processes such as dislocation cell, tangle, and pile-up formation. Metallurgical Transaction (dpeaa)DE-He213 Creep Rate (dpeaa)DE-He213 Volume Diffusion (dpeaa)DE-He213 Dislocation Creep (dpeaa)DE-He213 Pipe Diffusion (dpeaa)DE-He213 Floreen, S. aut Goodell, P. D. aut Enthalten in Metallurgical and materials transactions New York, NY : Springer Sciences & Business Media, 1975 3(1972), 4 vom: 01. Apr., Seite 833-842 (DE-627)325572062 (DE-600)2037524-4 1543-1916 nnns volume:3 year:1972 number:4 day:01 month:04 pages:833-842 https://dx.doi.org/10.1007/BF02647657 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 AR 3 1972 4 01 04 833-842 |
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10.1007/BF02647657 doi (DE-627)SPR021439419 (SPR)BF02647657-e DE-627 ger DE-627 rakwb eng Hayden, H. W. verfasserin aut The deformation mechanisms of superplasticity 1972 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Metallurgical of Society of AIME 1972 Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point grain boundary diffusion should be the dominant diffusion path while at higher temperatures volume diffusion should dominate. At intermediate stresses, grain boundary sliding should be the major deformation mode, but the sliding rate should be governed by the lesser rate of dislocation creep within the grains. At temperatures between 40 and 65 pct of the melting point, the rate of dislocation creep should be controlled by dislocation pipe diffusion, while at higher temperatures volume diffusion should be ratecontrolling. At high stresses the superplastic effect of unusually large tensile extensibility should diminish due to the greater possibility of work-hardening processes such as dislocation cell, tangle, and pile-up formation. Metallurgical Transaction (dpeaa)DE-He213 Creep Rate (dpeaa)DE-He213 Volume Diffusion (dpeaa)DE-He213 Dislocation Creep (dpeaa)DE-He213 Pipe Diffusion (dpeaa)DE-He213 Floreen, S. aut Goodell, P. D. aut Enthalten in Metallurgical and materials transactions New York, NY : Springer Sciences & Business Media, 1975 3(1972), 4 vom: 01. Apr., Seite 833-842 (DE-627)325572062 (DE-600)2037524-4 1543-1916 nnns volume:3 year:1972 number:4 day:01 month:04 pages:833-842 https://dx.doi.org/10.1007/BF02647657 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 AR 3 1972 4 01 04 833-842 |
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10.1007/BF02647657 doi (DE-627)SPR021439419 (SPR)BF02647657-e DE-627 ger DE-627 rakwb eng Hayden, H. W. verfasserin aut The deformation mechanisms of superplasticity 1972 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Metallurgical of Society of AIME 1972 Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point grain boundary diffusion should be the dominant diffusion path while at higher temperatures volume diffusion should dominate. At intermediate stresses, grain boundary sliding should be the major deformation mode, but the sliding rate should be governed by the lesser rate of dislocation creep within the grains. At temperatures between 40 and 65 pct of the melting point, the rate of dislocation creep should be controlled by dislocation pipe diffusion, while at higher temperatures volume diffusion should be ratecontrolling. At high stresses the superplastic effect of unusually large tensile extensibility should diminish due to the greater possibility of work-hardening processes such as dislocation cell, tangle, and pile-up formation. Metallurgical Transaction (dpeaa)DE-He213 Creep Rate (dpeaa)DE-He213 Volume Diffusion (dpeaa)DE-He213 Dislocation Creep (dpeaa)DE-He213 Pipe Diffusion (dpeaa)DE-He213 Floreen, S. aut Goodell, P. D. aut Enthalten in Metallurgical and materials transactions New York, NY : Springer Sciences & Business Media, 1975 3(1972), 4 vom: 01. Apr., Seite 833-842 (DE-627)325572062 (DE-600)2037524-4 1543-1916 nnns volume:3 year:1972 number:4 day:01 month:04 pages:833-842 https://dx.doi.org/10.1007/BF02647657 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 AR 3 1972 4 01 04 833-842 |
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10.1007/BF02647657 doi (DE-627)SPR021439419 (SPR)BF02647657-e DE-627 ger DE-627 rakwb eng Hayden, H. W. verfasserin aut The deformation mechanisms of superplasticity 1972 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Metallurgical of Society of AIME 1972 Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point grain boundary diffusion should be the dominant diffusion path while at higher temperatures volume diffusion should dominate. At intermediate stresses, grain boundary sliding should be the major deformation mode, but the sliding rate should be governed by the lesser rate of dislocation creep within the grains. At temperatures between 40 and 65 pct of the melting point, the rate of dislocation creep should be controlled by dislocation pipe diffusion, while at higher temperatures volume diffusion should be ratecontrolling. At high stresses the superplastic effect of unusually large tensile extensibility should diminish due to the greater possibility of work-hardening processes such as dislocation cell, tangle, and pile-up formation. Metallurgical Transaction (dpeaa)DE-He213 Creep Rate (dpeaa)DE-He213 Volume Diffusion (dpeaa)DE-He213 Dislocation Creep (dpeaa)DE-He213 Pipe Diffusion (dpeaa)DE-He213 Floreen, S. aut Goodell, P. D. aut Enthalten in Metallurgical and materials transactions New York, NY : Springer Sciences & Business Media, 1975 3(1972), 4 vom: 01. Apr., Seite 833-842 (DE-627)325572062 (DE-600)2037524-4 1543-1916 nnns volume:3 year:1972 number:4 day:01 month:04 pages:833-842 https://dx.doi.org/10.1007/BF02647657 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 AR 3 1972 4 01 04 833-842 |
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Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point grain boundary diffusion should be the dominant diffusion path while at higher temperatures volume diffusion should dominate. At intermediate stresses, grain boundary sliding should be the major deformation mode, but the sliding rate should be governed by the lesser rate of dislocation creep within the grains. At temperatures between 40 and 65 pct of the melting point, the rate of dislocation creep should be controlled by dislocation pipe diffusion, while at higher temperatures volume diffusion should be ratecontrolling. At high stresses the superplastic effect of unusually large tensile extensibility should diminish due to the greater possibility of work-hardening processes such as dislocation cell, tangle, and pile-up formation. © The Metallurgical of Society of AIME 1972 |
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Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point grain boundary diffusion should be the dominant diffusion path while at higher temperatures volume diffusion should dominate. At intermediate stresses, grain boundary sliding should be the major deformation mode, but the sliding rate should be governed by the lesser rate of dislocation creep within the grains. At temperatures between 40 and 65 pct of the melting point, the rate of dislocation creep should be controlled by dislocation pipe diffusion, while at higher temperatures volume diffusion should be ratecontrolling. At high stresses the superplastic effect of unusually large tensile extensibility should diminish due to the greater possibility of work-hardening processes such as dislocation cell, tangle, and pile-up formation. © The Metallurgical of Society of AIME 1972 |
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Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point grain boundary diffusion should be the dominant diffusion path while at higher temperatures volume diffusion should dominate. At intermediate stresses, grain boundary sliding should be the major deformation mode, but the sliding rate should be governed by the lesser rate of dislocation creep within the grains. At temperatures between 40 and 65 pct of the melting point, the rate of dislocation creep should be controlled by dislocation pipe diffusion, while at higher temperatures volume diffusion should be ratecontrolling. At high stresses the superplastic effect of unusually large tensile extensibility should diminish due to the greater possibility of work-hardening processes such as dislocation cell, tangle, and pile-up formation. © The Metallurgical of Society of AIME 1972 |
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<?xml version="1.0" encoding="UTF-8"?><collection xmlns="http://www.loc.gov/MARC21/slim"><record><leader>01000caa a22002652 4500</leader><controlfield tag="001">SPR021439419</controlfield><controlfield tag="003">DE-627</controlfield><controlfield tag="005">20230519174450.0</controlfield><controlfield tag="007">cr uuu---uuuuu</controlfield><controlfield tag="008">201006s1972 xx |||||o 00| ||eng c</controlfield><datafield tag="024" ind1="7" ind2=" "><subfield code="a">10.1007/BF02647657</subfield><subfield code="2">doi</subfield></datafield><datafield tag="035" ind1=" " ind2=" "><subfield code="a">(DE-627)SPR021439419</subfield></datafield><datafield tag="035" ind1=" " ind2=" "><subfield code="a">(SPR)BF02647657-e</subfield></datafield><datafield tag="040" ind1=" " ind2=" "><subfield code="a">DE-627</subfield><subfield code="b">ger</subfield><subfield code="c">DE-627</subfield><subfield code="e">rakwb</subfield></datafield><datafield tag="041" ind1=" " ind2=" "><subfield code="a">eng</subfield></datafield><datafield tag="100" ind1="1" ind2=" "><subfield code="a">Hayden, H. W.</subfield><subfield code="e">verfasserin</subfield><subfield code="4">aut</subfield></datafield><datafield tag="245" ind1="1" ind2="4"><subfield code="a">The deformation mechanisms of superplasticity</subfield></datafield><datafield tag="264" ind1=" " ind2="1"><subfield code="c">1972</subfield></datafield><datafield tag="336" ind1=" " ind2=" "><subfield code="a">Text</subfield><subfield code="b">txt</subfield><subfield code="2">rdacontent</subfield></datafield><datafield tag="337" ind1=" " ind2=" "><subfield code="a">Computermedien</subfield><subfield code="b">c</subfield><subfield code="2">rdamedia</subfield></datafield><datafield tag="338" ind1=" " ind2=" "><subfield code="a">Online-Ressource</subfield><subfield code="b">cr</subfield><subfield code="2">rdacarrier</subfield></datafield><datafield tag="500" ind1=" " ind2=" "><subfield code="a">© The Metallurgical of Society of AIME 1972</subfield></datafield><datafield tag="520" ind1=" " ind2=" "><subfield code="a">Abstract Under various conditions of stress and temperature various deformation mechanisms could be rate-controlling for superplastic deformation. In general at low stresses diffusion creep should be rate-controlling. At temperatures between approximately 40 and 65 pct of the absolute melting point grain boundary diffusion should be the dominant diffusion path while at higher temperatures volume diffusion should dominate. At intermediate stresses, grain boundary sliding should be the major deformation mode, but the sliding rate should be governed by the lesser rate of dislocation creep within the grains. At temperatures between 40 and 65 pct of the melting point, the rate of dislocation creep should be controlled by dislocation pipe diffusion, while at higher temperatures volume diffusion should be ratecontrolling. At high stresses the superplastic effect of unusually large tensile extensibility should diminish due to the greater possibility of work-hardening processes such as dislocation cell, tangle, and pile-up formation.</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Metallurgical Transaction</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Creep Rate</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Volume Diffusion</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Dislocation Creep</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Pipe Diffusion</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="700" ind1="1" ind2=" "><subfield code="a">Floreen, S.</subfield><subfield code="4">aut</subfield></datafield><datafield tag="700" ind1="1" ind2=" "><subfield code="a">Goodell, P. D.</subfield><subfield code="4">aut</subfield></datafield><datafield tag="773" ind1="0" ind2="8"><subfield code="i">Enthalten in</subfield><subfield code="t">Metallurgical and materials transactions</subfield><subfield code="d">New York, NY : Springer Sciences & Business Media, 1975</subfield><subfield code="g">3(1972), 4 vom: 01. Apr., Seite 833-842</subfield><subfield code="w">(DE-627)325572062</subfield><subfield code="w">(DE-600)2037524-4</subfield><subfield code="x">1543-1916</subfield><subfield code="7">nnns</subfield></datafield><datafield tag="773" ind1="1" ind2="8"><subfield code="g">volume:3</subfield><subfield code="g">year:1972</subfield><subfield code="g">number:4</subfield><subfield code="g">day:01</subfield><subfield code="g">month:04</subfield><subfield code="g">pages:833-842</subfield></datafield><datafield tag="856" ind1="4" ind2="0"><subfield code="u">https://dx.doi.org/10.1007/BF02647657</subfield><subfield code="z">lizenzpflichtig</subfield><subfield code="3">Volltext</subfield></datafield><datafield tag="912" ind1=" " ind2=" "><subfield code="a">GBV_USEFLAG_A</subfield></datafield><datafield tag="912" ind1=" " ind2=" "><subfield code="a">SYSFLAG_A</subfield></datafield><datafield tag="912" ind1=" " ind2=" "><subfield code="a">GBV_SPRINGER</subfield></datafield><datafield tag="912" ind1=" " ind2=" "><subfield code="a">SSG-OLC-PHA</subfield></datafield><datafield tag="912" ind1=" " ind2=" "><subfield code="a">GBV_ILN_120</subfield></datafield><datafield tag="912" ind1=" " ind2=" "><subfield code="a">GBV_ILN_121</subfield></datafield><datafield tag="912" ind1=" " ind2=" "><subfield code="a">GBV_ILN_150</subfield></datafield><datafield tag="951" ind1=" " ind2=" "><subfield code="a">AR</subfield></datafield><datafield tag="952" ind1=" " ind2=" "><subfield code="d">3</subfield><subfield code="j">1972</subfield><subfield code="e">4</subfield><subfield code="b">01</subfield><subfield code="c">04</subfield><subfield code="h">833-842</subfield></datafield></record></collection>
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