Cross slip in phases having the $ L1_{2} $ structure
Abstract Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress...
Ausführliche Beschreibung
Gespeichert in:
| Autor*in: |
Thornton, P. H. [verfasserIn] |
|---|
| Format: |
E-Artikel |
|---|---|
| Sprache: |
Englisch |
| Erschienen: |
1972 |
|---|
| Schlagwörter: |
|---|
| Anmerkung: |
© The Metallurgical of Society of AIME 1972 |
|---|
| Übergeordnetes Werk: |
Enthalten in: Metallurgical and materials transactions - New York, NY : Springer Sciences & Business Media, 1975, 3(1972), 1 vom: 01. Jan., Seite 291-300 |
|---|---|
| Übergeordnetes Werk: |
volume:3 ; year:1972 ; number:1 ; day:01 ; month:01 ; pages:291-300 |
| Links: |
|---|
| DOI / URN: |
10.1007/BF02680608 |
|---|
| Katalog-ID: |
SPR021437785 |
|---|
| LEADER | 01000caa a22002652 4500 | ||
|---|---|---|---|
| 001 | SPR021437785 | ||
| 003 | DE-627 | ||
| 005 | 20230519174447.0 | ||
| 007 | cr uuu---uuuuu | ||
| 008 | 201006s1972 xx |||||o 00| ||eng c | ||
| 024 | 7 | |a 10.1007/BF02680608 |2 doi | |
| 035 | |a (DE-627)SPR021437785 | ||
| 035 | |a (SPR)BF02680608-e | ||
| 040 | |a DE-627 |b ger |c DE-627 |e rakwb | ||
| 041 | |a eng | ||
| 100 | 1 | |a Thornton, P. H. |e verfasserin |4 aut | |
| 245 | 1 | 0 | |a Cross slip in phases having the $ L1_{2} $ structure |
| 264 | 1 | |c 1972 | |
| 336 | |a Text |b txt |2 rdacontent | ||
| 337 | |a Computermedien |b c |2 rdamedia | ||
| 338 | |a Online-Ressource |b cr |2 rdacarrier | ||
| 500 | |a © The Metallurgical of Society of AIME 1972 | ||
| 520 | |a Abstract Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed. | ||
| 650 | 4 | |a Flow Stress |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a Slip System |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a Resolve Shear Stress |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a Secondary Slip |7 (dpeaa)DE-He213 | |
| 650 | 4 | |a Primary Slip System |7 (dpeaa)DE-He213 | |
| 773 | 0 | 8 | |i Enthalten in |t Metallurgical and materials transactions |d New York, NY : Springer Sciences & Business Media, 1975 |g 3(1972), 1 vom: 01. Jan., Seite 291-300 |w (DE-627)325572062 |w (DE-600)2037524-4 |x 1543-1916 |7 nnns |
| 773 | 1 | 8 | |g volume:3 |g year:1972 |g number:1 |g day:01 |g month:01 |g pages:291-300 |
| 856 | 4 | 0 | |u https://dx.doi.org/10.1007/BF02680608 |z lizenzpflichtig |3 Volltext |
| 912 | |a GBV_USEFLAG_A | ||
| 912 | |a SYSFLAG_A | ||
| 912 | |a GBV_SPRINGER | ||
| 912 | |a SSG-OLC-PHA | ||
| 912 | |a GBV_ILN_120 | ||
| 912 | |a GBV_ILN_121 | ||
| 912 | |a GBV_ILN_150 | ||
| 951 | |a AR | ||
| 952 | |d 3 |j 1972 |e 1 |b 01 |c 01 |h 291-300 | ||
| author_variant |
p h t ph pht |
|---|---|
| matchkey_str |
article:15431916:1972----::rssiipaehvnte |
| hierarchy_sort_str |
1972 |
| publishDate |
1972 |
| allfields |
10.1007/BF02680608 doi (DE-627)SPR021437785 (SPR)BF02680608-e DE-627 ger DE-627 rakwb eng Thornton, P. H. verfasserin aut Cross slip in phases having the $ L1_{2} $ structure 1972 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Metallurgical of Society of AIME 1972 Abstract Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed. Flow Stress (dpeaa)DE-He213 Slip System (dpeaa)DE-He213 Resolve Shear Stress (dpeaa)DE-He213 Secondary Slip (dpeaa)DE-He213 Primary Slip System (dpeaa)DE-He213 Enthalten in Metallurgical and materials transactions New York, NY : Springer Sciences & Business Media, 1975 3(1972), 1 vom: 01. Jan., Seite 291-300 (DE-627)325572062 (DE-600)2037524-4 1543-1916 nnns volume:3 year:1972 number:1 day:01 month:01 pages:291-300 https://dx.doi.org/10.1007/BF02680608 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 AR 3 1972 1 01 01 291-300 |
| spelling |
10.1007/BF02680608 doi (DE-627)SPR021437785 (SPR)BF02680608-e DE-627 ger DE-627 rakwb eng Thornton, P. H. verfasserin aut Cross slip in phases having the $ L1_{2} $ structure 1972 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Metallurgical of Society of AIME 1972 Abstract Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed. Flow Stress (dpeaa)DE-He213 Slip System (dpeaa)DE-He213 Resolve Shear Stress (dpeaa)DE-He213 Secondary Slip (dpeaa)DE-He213 Primary Slip System (dpeaa)DE-He213 Enthalten in Metallurgical and materials transactions New York, NY : Springer Sciences & Business Media, 1975 3(1972), 1 vom: 01. Jan., Seite 291-300 (DE-627)325572062 (DE-600)2037524-4 1543-1916 nnns volume:3 year:1972 number:1 day:01 month:01 pages:291-300 https://dx.doi.org/10.1007/BF02680608 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 AR 3 1972 1 01 01 291-300 |
| allfields_unstemmed |
10.1007/BF02680608 doi (DE-627)SPR021437785 (SPR)BF02680608-e DE-627 ger DE-627 rakwb eng Thornton, P. H. verfasserin aut Cross slip in phases having the $ L1_{2} $ structure 1972 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Metallurgical of Society of AIME 1972 Abstract Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed. Flow Stress (dpeaa)DE-He213 Slip System (dpeaa)DE-He213 Resolve Shear Stress (dpeaa)DE-He213 Secondary Slip (dpeaa)DE-He213 Primary Slip System (dpeaa)DE-He213 Enthalten in Metallurgical and materials transactions New York, NY : Springer Sciences & Business Media, 1975 3(1972), 1 vom: 01. Jan., Seite 291-300 (DE-627)325572062 (DE-600)2037524-4 1543-1916 nnns volume:3 year:1972 number:1 day:01 month:01 pages:291-300 https://dx.doi.org/10.1007/BF02680608 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 AR 3 1972 1 01 01 291-300 |
| allfieldsGer |
10.1007/BF02680608 doi (DE-627)SPR021437785 (SPR)BF02680608-e DE-627 ger DE-627 rakwb eng Thornton, P. H. verfasserin aut Cross slip in phases having the $ L1_{2} $ structure 1972 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Metallurgical of Society of AIME 1972 Abstract Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed. Flow Stress (dpeaa)DE-He213 Slip System (dpeaa)DE-He213 Resolve Shear Stress (dpeaa)DE-He213 Secondary Slip (dpeaa)DE-He213 Primary Slip System (dpeaa)DE-He213 Enthalten in Metallurgical and materials transactions New York, NY : Springer Sciences & Business Media, 1975 3(1972), 1 vom: 01. Jan., Seite 291-300 (DE-627)325572062 (DE-600)2037524-4 1543-1916 nnns volume:3 year:1972 number:1 day:01 month:01 pages:291-300 https://dx.doi.org/10.1007/BF02680608 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 AR 3 1972 1 01 01 291-300 |
| allfieldsSound |
10.1007/BF02680608 doi (DE-627)SPR021437785 (SPR)BF02680608-e DE-627 ger DE-627 rakwb eng Thornton, P. H. verfasserin aut Cross slip in phases having the $ L1_{2} $ structure 1972 Text txt rdacontent Computermedien c rdamedia Online-Ressource cr rdacarrier © The Metallurgical of Society of AIME 1972 Abstract Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed. Flow Stress (dpeaa)DE-He213 Slip System (dpeaa)DE-He213 Resolve Shear Stress (dpeaa)DE-He213 Secondary Slip (dpeaa)DE-He213 Primary Slip System (dpeaa)DE-He213 Enthalten in Metallurgical and materials transactions New York, NY : Springer Sciences & Business Media, 1975 3(1972), 1 vom: 01. Jan., Seite 291-300 (DE-627)325572062 (DE-600)2037524-4 1543-1916 nnns volume:3 year:1972 number:1 day:01 month:01 pages:291-300 https://dx.doi.org/10.1007/BF02680608 lizenzpflichtig Volltext GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 AR 3 1972 1 01 01 291-300 |
| language |
English |
| source |
Enthalten in Metallurgical and materials transactions 3(1972), 1 vom: 01. Jan., Seite 291-300 volume:3 year:1972 number:1 day:01 month:01 pages:291-300 |
| sourceStr |
Enthalten in Metallurgical and materials transactions 3(1972), 1 vom: 01. Jan., Seite 291-300 volume:3 year:1972 number:1 day:01 month:01 pages:291-300 |
| format_phy_str_mv |
Article |
| institution |
findex.gbv.de |
| topic_facet |
Flow Stress Slip System Resolve Shear Stress Secondary Slip Primary Slip System |
| isfreeaccess_bool |
false |
| container_title |
Metallurgical and materials transactions |
| authorswithroles_txt_mv |
Thornton, P. H. @@aut@@ |
| publishDateDaySort_date |
1972-01-01T00:00:00Z |
| hierarchy_top_id |
325572062 |
| id |
SPR021437785 |
| language_de |
englisch |
| fullrecord |
<?xml version="1.0" encoding="UTF-8"?><collection xmlns="http://www.loc.gov/MARC21/slim"><record><leader>01000caa a22002652 4500</leader><controlfield tag="001">SPR021437785</controlfield><controlfield tag="003">DE-627</controlfield><controlfield tag="005">20230519174447.0</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/BF02680608</subfield><subfield code="2">doi</subfield></datafield><datafield tag="035" ind1=" " ind2=" "><subfield code="a">(DE-627)SPR021437785</subfield></datafield><datafield tag="035" ind1=" " ind2=" "><subfield code="a">(SPR)BF02680608-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">Thornton, P. H.</subfield><subfield code="e">verfasserin</subfield><subfield code="4">aut</subfield></datafield><datafield tag="245" ind1="1" ind2="0"><subfield code="a">Cross slip in phases having the $ L1_{2} $ structure</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 Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed.</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Flow Stress</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Slip System</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Resolve Shear Stress</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Secondary Slip</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Primary Slip System</subfield><subfield code="7">(dpeaa)DE-He213</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), 1 vom: 01. Jan., Seite 291-300</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:1</subfield><subfield code="g">day:01</subfield><subfield code="g">month:01</subfield><subfield code="g">pages:291-300</subfield></datafield><datafield tag="856" ind1="4" ind2="0"><subfield code="u">https://dx.doi.org/10.1007/BF02680608</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">1</subfield><subfield code="b">01</subfield><subfield code="c">01</subfield><subfield code="h">291-300</subfield></datafield></record></collection>
|
| author |
Thornton, P. H. |
| spellingShingle |
Thornton, P. H. misc Flow Stress misc Slip System misc Resolve Shear Stress misc Secondary Slip misc Primary Slip System Cross slip in phases having the $ L1_{2} $ structure |
| authorStr |
Thornton, P. H. |
| ppnlink_with_tag_str_mv |
@@773@@(DE-627)325572062 |
| format |
electronic Article |
| delete_txt_mv |
keep |
| author_role |
aut |
| collection |
springer |
| remote_str |
true |
| illustrated |
Not Illustrated |
| issn |
1543-1916 |
| topic_title |
Cross slip in phases having the $ L1_{2} $ structure Flow Stress (dpeaa)DE-He213 Slip System (dpeaa)DE-He213 Resolve Shear Stress (dpeaa)DE-He213 Secondary Slip (dpeaa)DE-He213 Primary Slip System (dpeaa)DE-He213 |
| topic |
misc Flow Stress misc Slip System misc Resolve Shear Stress misc Secondary Slip misc Primary Slip System |
| topic_unstemmed |
misc Flow Stress misc Slip System misc Resolve Shear Stress misc Secondary Slip misc Primary Slip System |
| topic_browse |
misc Flow Stress misc Slip System misc Resolve Shear Stress misc Secondary Slip misc Primary Slip System |
| format_facet |
Elektronische Aufsätze Aufsätze Elektronische Ressource |
| format_main_str_mv |
Text Zeitschrift/Artikel |
| carriertype_str_mv |
cr |
| hierarchy_parent_title |
Metallurgical and materials transactions |
| hierarchy_parent_id |
325572062 |
| hierarchy_top_title |
Metallurgical and materials transactions |
| isfreeaccess_txt |
false |
| familylinks_str_mv |
(DE-627)325572062 (DE-600)2037524-4 |
| title |
Cross slip in phases having the $ L1_{2} $ structure |
| ctrlnum |
(DE-627)SPR021437785 (SPR)BF02680608-e |
| title_full |
Cross slip in phases having the $ L1_{2} $ structure |
| author_sort |
Thornton, P. H. |
| journal |
Metallurgical and materials transactions |
| journalStr |
Metallurgical and materials transactions |
| lang_code |
eng |
| isOA_bool |
false |
| recordtype |
marc |
| publishDateSort |
1972 |
| contenttype_str_mv |
txt |
| container_start_page |
291 |
| author_browse |
Thornton, P. H. |
| container_volume |
3 |
| format_se |
Elektronische Aufsätze |
| author-letter |
Thornton, P. H. |
| doi_str_mv |
10.1007/BF02680608 |
| title_sort |
cross slip in phases having the $ l1_{2} $ structure |
| title_auth |
Cross slip in phases having the $ L1_{2} $ structure |
| abstract |
Abstract Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed. © The Metallurgical of Society of AIME 1972 |
| abstractGer |
Abstract Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed. © The Metallurgical of Society of AIME 1972 |
| abstract_unstemmed |
Abstract Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed. © The Metallurgical of Society of AIME 1972 |
| collection_details |
GBV_USEFLAG_A SYSFLAG_A GBV_SPRINGER SSG-OLC-PHA GBV_ILN_120 GBV_ILN_121 GBV_ILN_150 |
| container_issue |
1 |
| title_short |
Cross slip in phases having the $ L1_{2} $ structure |
| url |
https://dx.doi.org/10.1007/BF02680608 |
| remote_bool |
true |
| ppnlink |
325572062 |
| mediatype_str_mv |
c |
| isOA_txt |
false |
| hochschulschrift_bool |
false |
| doi_str |
10.1007/BF02680608 |
| up_date |
2024-07-03T22:34:06.238Z |
| _version_ |
1803599002982154240 |
| fullrecord_marcxml |
<?xml version="1.0" encoding="UTF-8"?><collection xmlns="http://www.loc.gov/MARC21/slim"><record><leader>01000caa a22002652 4500</leader><controlfield tag="001">SPR021437785</controlfield><controlfield tag="003">DE-627</controlfield><controlfield tag="005">20230519174447.0</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/BF02680608</subfield><subfield code="2">doi</subfield></datafield><datafield tag="035" ind1=" " ind2=" "><subfield code="a">(DE-627)SPR021437785</subfield></datafield><datafield tag="035" ind1=" " ind2=" "><subfield code="a">(SPR)BF02680608-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">Thornton, P. H.</subfield><subfield code="e">verfasserin</subfield><subfield code="4">aut</subfield></datafield><datafield tag="245" ind1="1" ind2="0"><subfield code="a">Cross slip in phases having the $ L1_{2} $ structure</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 Plastic deformation in phases having the $ Ll_{2} $ structure can occur on the {001} (110) system (cube slip) as well as on the {1ll} (101) system (octahedral slip). Primary and secondary slip may therefore occur with various combinations of the cube and octahedral slip systems. The stress fields around dislocation pile-ups on the primary slip system are calculated for these various combinations of slip system and it is shown that secondary slip can occur on the cube slip system over distances which are an appreciable fraction of the pile-up length, even when the Schmid factor for cube slip is zero, such as for (001) oriented crystals. Thus the change in the mechanism of work-hardening which was previously $ proposed^{5} $ to account for the anomalous temperature dependence of the flow stress of the γ’ phase based upon M3AI and which has the $ Ll_{2} $ structure, can also be applied to (001) oriented crystals of γ’, which also show the anomalous flow stress temperature dependence.3 The hypothesis predicts that the mobile dislocation behavior should be modified with change in temperature. Etch pit results are presented to show that freshly nucleated dislocation sources do respond differently under the same stress at 25° and at 400°. The observed behavior is consistent with the work-hardening model previously proposed.</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Flow Stress</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Slip System</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Resolve Shear Stress</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Secondary Slip</subfield><subfield code="7">(dpeaa)DE-He213</subfield></datafield><datafield tag="650" ind1=" " ind2="4"><subfield code="a">Primary Slip System</subfield><subfield code="7">(dpeaa)DE-He213</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), 1 vom: 01. Jan., Seite 291-300</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:1</subfield><subfield code="g">day:01</subfield><subfield code="g">month:01</subfield><subfield code="g">pages:291-300</subfield></datafield><datafield tag="856" ind1="4" ind2="0"><subfield code="u">https://dx.doi.org/10.1007/BF02680608</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">1</subfield><subfield code="b">01</subfield><subfield code="c">01</subfield><subfield code="h">291-300</subfield></datafield></record></collection>
|
| score |
7.3975716 |