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Article: Microstructure evolution in an interstitial-free steel during cold rolling at low strain levels

TitleMicrostructure evolution in an interstitial-free steel during cold rolling at low strain levels
Authors
KeywordsCold rolling
Dislocation
Interstitial-free steel
Microband
Microstructure
Issue Date2003
PublisherThe Royal Society. The Journal's web site is located at http://www.pubs.royalsoc.ac.uk/index.cfm?page=1086
Citation
Proceedings Of The Royal Society A: Mathematical, Physical And Engineering Sciences, 2003, v. 459 n. 2035, p. 1661-1685 How to Cite?
AbstractMicrostructure development in an interstitial-free steel during cold rolling at low strain levels (ε ≤ 9.8%) has been investigated by using transmission electron microscopy. At a strain of 2.2%, {112} slip systems operate in addition to {110} slip planes. Dislocation reactions occur at this stage to produce immobile 100 segments in the scissors configuration and these segments are also found at higher strain in the dislocation walls of microbands. The formation of microbands starts at small reductions (ε ∼ 6.7%), and microbands are of lenticular shapes and have habit planes running approximately parallel to {110} planes. Two sets of dislocations comprise the microband walls; one is predominant and has its Burgers vector lying on the microband's habit plane. The secondary set is much less dense, and its slip plane is not coplanar with the microband habit plane. A considerable misorientation exists between the inner region of a microband and either of its two neighbouring matrices, rather than between the two matrices, which is consistent with Jackson's double cross-slip model. However, the growing end of a microband indicates the splitting of a dense dislocation sheet. In the specimen that was rolled to ε = 9.8%, some grains contain one or two sets of microbands, while some are microband-free. The crystallographic measurement and deformation geometry calculation reveal that the habit plane of an observed microband has the largest Schmid factor; and when one (111) slip direction is intensively activated in this plane, one set of microbands is formed on this plane. Two sets of microbands form if two (111) slip directions have high and nearly equal shear stresses. In the case of microband-free crystals, up to seven slip systems have similar Schmid factors and thus are activated concurrently. This leads to homogeneous deformation and as a result, no microbands form. Based on these results, a new mechanism is proposed for microband formation involving double cross-slip, dislocation wall splitting and dislocation exchange between the walls.
Persistent Identifierhttp://hdl.handle.net/10722/76098
ISSN
2015 Impact Factor: 1.935
2015 SCImago Journal Rankings: 0.894
ISI Accession Number ID
References

 

DC FieldValueLanguage
dc.contributor.authorChen, QZen_HK
dc.contributor.authorNgan, AHWen_HK
dc.contributor.authorDuggan, BJen_HK
dc.date.accessioned2010-09-06T07:17:37Z-
dc.date.available2010-09-06T07:17:37Z-
dc.date.issued2003en_HK
dc.identifier.citationProceedings Of The Royal Society A: Mathematical, Physical And Engineering Sciences, 2003, v. 459 n. 2035, p. 1661-1685en_HK
dc.identifier.issn1364-5021en_HK
dc.identifier.urihttp://hdl.handle.net/10722/76098-
dc.description.abstractMicrostructure development in an interstitial-free steel during cold rolling at low strain levels (ε ≤ 9.8%) has been investigated by using transmission electron microscopy. At a strain of 2.2%, {112} slip systems operate in addition to {110} slip planes. Dislocation reactions occur at this stage to produce immobile 100 segments in the scissors configuration and these segments are also found at higher strain in the dislocation walls of microbands. The formation of microbands starts at small reductions (ε ∼ 6.7%), and microbands are of lenticular shapes and have habit planes running approximately parallel to {110} planes. Two sets of dislocations comprise the microband walls; one is predominant and has its Burgers vector lying on the microband's habit plane. The secondary set is much less dense, and its slip plane is not coplanar with the microband habit plane. A considerable misorientation exists between the inner region of a microband and either of its two neighbouring matrices, rather than between the two matrices, which is consistent with Jackson's double cross-slip model. However, the growing end of a microband indicates the splitting of a dense dislocation sheet. In the specimen that was rolled to ε = 9.8%, some grains contain one or two sets of microbands, while some are microband-free. The crystallographic measurement and deformation geometry calculation reveal that the habit plane of an observed microband has the largest Schmid factor; and when one (111) slip direction is intensively activated in this plane, one set of microbands is formed on this plane. Two sets of microbands form if two (111) slip directions have high and nearly equal shear stresses. In the case of microband-free crystals, up to seven slip systems have similar Schmid factors and thus are activated concurrently. This leads to homogeneous deformation and as a result, no microbands form. Based on these results, a new mechanism is proposed for microband formation involving double cross-slip, dislocation wall splitting and dislocation exchange between the walls.en_HK
dc.languageengen_HK
dc.publisherThe Royal Society. The Journal's web site is located at http://www.pubs.royalsoc.ac.uk/index.cfm?page=1086en_HK
dc.relation.ispartofProceedings of the Royal Society A: Mathematical, Physical and Engineering Sciencesen_HK
dc.subjectCold rollingen_HK
dc.subjectDislocationen_HK
dc.subjectInterstitial-free steelen_HK
dc.subjectMicrobanden_HK
dc.subjectMicrostructureen_HK
dc.titleMicrostructure evolution in an interstitial-free steel during cold rolling at low strain levelsen_HK
dc.typeArticleen_HK
dc.identifier.emailNgan, AHW: hwngan@hkucc.hku.hken_HK
dc.identifier.emailDuggan, BJ: bjduggan@hkucc.hku.hken_HK
dc.identifier.authorityNgan, AHW=rp00225en_HK
dc.identifier.authorityDuggan, BJ=rp01686en_HK
dc.description.naturelink_to_subscribed_fulltext-
dc.identifier.doi10.1098/rspa.2002.1051en_HK
dc.identifier.scopuseid_2-s2.0-1542722146en_HK
dc.identifier.hkuros79090en_HK
dc.relation.referenceshttp://www.scopus.com/mlt/select.url?eid=2-s2.0-1542722146&selection=ref&src=s&origin=recordpageen_HK
dc.identifier.volume459en_HK
dc.identifier.issue2035en_HK
dc.identifier.spage1661en_HK
dc.identifier.epage1685en_HK
dc.identifier.isiWOS:000184160000004-
dc.publisher.placeUnited Kingdomen_HK
dc.identifier.scopusauthoridChen, QZ=8353179600en_HK
dc.identifier.scopusauthoridNgan, AHW=7006827202en_HK
dc.identifier.scopusauthoridDuggan, BJ=7005772998en_HK

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