Deformation banding and recrystallization of α fibre components in heavily rolled IF steel

Quadir, Zakaria; Duggan, B.J.

doi:10.1016/j.actamat.2004.05.017

Cited by 108 publications

(71 citation statements)

References 19 publications

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“…This has been demonstrated by Barnett and Jonas, [13] who rolled IF steel in the ferrite phase field up to 700°C and found an increasing spreading along the {100}//RP fiber from its common point with the a fiber, {100}<011>, toward {100}<001> as rolling temperature increased from 70°C to 700°C. Quadir and Duggan [14] repeated this work and found similar results. When ferritic stainless steel (Fe-16.5 pct Cr) was rolled at a temperature that ensured that the material remained in the bcc phase field, it also showed the {100}//RP, although Raabe [15] did not comment on this aspect of his results.…”

Section: A Initial and Rolling Texturessupporting

confidence: 83%

Texture Development in a Cold-Rolled and Annealed Body-Centered-Cubic Mg-Li Alloy

Shen

Duggan

2007

Metall Mater Trans A

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The rolling and annealing textures formed in bcc Mg 14 wt pct Li have been investigated and compared with interstitial-free (IF) and more heavily alloyed ferritic steel rolled at the same temperature. The a fiber texture component (<110>//rolling direction) is very strong after 90 pct rolling at room temperature; however, there is evidence that the c fiber ({111}//rolling plane) weakens with increasing rolling strain to give a peaklike texture centered on {111}<110>. A rarely found cold rolling fiber texture has been identified, which has {100}// rolling plane and peaks at {100}<014>. Annealing at 200°C very rapidly produces {554}<225>, which gives way to components near {111}<123> on grain growth. The a fiber is destroyed by recrystallization; however, the {100}//rolling plane fiber shifts intensity from the as-rolled orientation {100}<014> to {100}<012>. Since texture largely determines drawability, the best that can be achieved in terms of press performance of this alloy is most likely a Lankford parameter of unity.

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Section: A Initial and Rolling Texturessupporting

confidence: 83%

Texture Development in a Cold-Rolled and Annealed Body-Centered-Cubic Mg-Li Alloy

Shen

Duggan

2007

Metall Mater Trans A

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“…These results suggest that recrystallized grains would be able to nucleate from the α-fiber region in the 99.8% coldrolled sample. Quadir et al reported that the recrystallization from {100} < 011 > was possible by cold rolling with high reduction, 9) because the misorientation in {100} < 011 > grains increased due to the high cold rolling reduction.…”

Section: Discussionmentioning

confidence: 99%

Development of Recrystallization Texture in Severely Cold-rolled Pure Iron

et al. 2016

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The mechanism of recrystallization texture development is changed by the chemical composition of materials, cold-rolling reduction, and annealing conditions. This study discusses the development of recrystallization texture for severely cold-rolled pure iron. In cold-rolled iron with 99.8% reduction, the deformation texture was a strong α-fiber (RD// < 011 > ) with high strain. During annealing in a temperature range from 20°C to 800°C, in this highly strained α-fiber, the microstructure started to recover from a low temperature. Thereafter, recrystallized grains began to appear at 350°C, and many recrystallized grains were generated at random locations. Their textural components were {100}, {211}, {111}, and {411}, which were already included in the α-fiber. At 550°C, recrystallization was completed, and the resulting recrystallization texture was similar to the original cold-rolling texture. This texture was developed by unique microstructural changes, which could be classified as continuous recrystallization. During grain growth stage, the recrystallization texture changed into the {100} < 012 > component presumably by the selective growth of recrystallized grains governed by the size effect.

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“…It is generally reported that deformation bands break up large initial grains into segments, each of which later adopt a unique deformation mode and, hence, develop microstructures as independent grains. 15,16) In regions A and B of Fig. 4 is generally found to be present with fairly strong intensities (i.e.…”

Section: Resultsmentioning

confidence: 99%

“…It is inspiring to find that the common <110> pole falls on this trace at a distance of 14° from the RD-ND axis (which is the trace of the TD). This indicates that if the microband boundary trace has ~14° inclinations with the TD in the TD-ND cross section (an angle which is within the range of commonly reported inclinations [7][8][9][14][15][16] ), then the interface normal coincides with the common <110> pole. Similarly, the common <110> poles observed in Fig.…”

Section: Discussionmentioning

confidence: 99%

“…3 and 4 is important to study for representing another classical scenario of microband structures containing S-and micro-shear banding. [12][13][14][15][16][17][18] Earlier, Chen et al 9) argued that the microband structure is a precursor for S-and micro-shear band formation in the γ-oriented grains of the rolling microstructures of micro-alloyed and ultra-low carbon steels. Figure 5(a) is a high resolution TD IPF map of the rectangular area shown in Fig.…”

Section: Resultsmentioning

confidence: 99%

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Unusual Crystallographic Aspects of Microband Boundaries within {111}^|^lt;110^|^gt; Oriented Grains in a Cold Rolled Interstitial Free Steel

et al. 2014

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Microbands are well-known deformation features that generate in the rolling microstructures of many metals and alloys. The boundaries across two neighbouring microbands are comprised of dense dislocation walls and they accommodate a small average crystallographic rotation in the range of 1-4°. In this study, a combination of high resolution electron backscattered diffraction (EBSD) and transmission electron microscopy (TEM) was used to observe orientation differences of up to 20° across microband boundaries in the rolling substructures of {111}<110> oriented grains in steel. Despite their high angle nature, the microband interfaces maintain their well-known crystallographic characteristics, by being closely aligned with highly stressed slip planes. Rigid body rotations are argued to take place around the interface normal between adjacent microband lattices. This results in an unusual microstructure whereby alternating microband boundaries, oriented in equal and opposite relative angles, produce an array of orientation pairs in their spatial distributions.

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Deformation banding and recrystallization of α fibre components in heavily rolled IF steel

Cited by 108 publications

References 19 publications

Texture Development in a Cold-Rolled and Annealed Body-Centered-Cubic Mg-Li Alloy

Texture Development in a Cold-Rolled and Annealed Body-Centered-Cubic Mg-Li Alloy

Development of Recrystallization Texture in Severely Cold-rolled Pure Iron

Unusual Crystallographic Aspects of Microband Boundaries within {111}^|^lt;110^|^gt; Oriented Grains in a Cold Rolled Interstitial Free Steel

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