Strain hardening of titanium: role of deformation twinning

Salem, Ayman A.; Kalidindi, Surya R.; Doherty, R.D.

doi:10.1016/s1359-6454(03)00239-8

Cited by 414 publications

(182 citation statements)

References 17 publications

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“…[46,47] For any slip system, possible streak directions at peak (hkl) due to edge GNDs on that slip system can be calculated using Eq. [5] and compared with the experimentally collected diffraction patterns. This method has been successfully used to identify the GND content in a few materials.…”

Section: A Sample and Deformationmentioning

confidence: 99%

“…[1,2] On the other hand, dislocation-twin interaction can make a significant contribution to the work hardening of the material. [3][4][5][6] The latent hardening model has typically been used to describe dislocation-twin interaction in crystal plasticity frameworks that generally give good prediction of the measured stress-strain curves. [7,8] However, the latent hardening model may be too simplified to incorporate detailed accommodation mechanisms around twins that were experimentally observed, which include (1) glide dislocations' dissociation at the twin boundary (TB), [4,9,10] (2) transmutation of existing matrix dislocations into the twin lattice, [11][12][13][14][15] (3) formation of kink bands or secondary twins at the twin-twin intersection, [4,10,16,17] etc.…”

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confidence: 99%

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Study of $$ \{ 11\bar{2} 1\} $$ Twinning in α-Ti by EBSD and Laue Microdiffraction

Wang

Barabash

Bieler

et al. 2013

Metall Mater Trans A

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Activity of the f11 " 21gh " 1 " 126i extension twinning (T2) mode was analyzed in a commercial purity Ti sample after 2 pct tensile strain imposed by four-point bending. The sample had a moderate c-axis fiber texture parallel to the tensile axis. Compared with the many f10 " 12gh " 1011i extension (T1) twins that formed in 6 pct of the grains, T2 twins were identified in 0.25 pct of the grains by scanning electron microscopy (SEM) and electron backscattered diffraction (EBSD) maps. Most of the T2 twins exhibited irregular twin boundaries (TBs) on one side of the twin. Highresolution EBSD revealed both intermediate orientations at some matrix/twin interfaces and substantial lattice rotation within some T2 twins. Interactions between matrix hc + ai dislocations 1 3 h1 " 213i and a f11 " 21g T2 twin were investigated by combining SEM/EBSD slip trace characterization and Laue microdiffraction peak streak analysis. hc + ai dislocations that originally glided on a pyramidal plane in the matrix were found on other planes in both the matrix and the twin, which was attributed to extensive cross-slip of the screw component, whose Burgers vector was parallel to the twinning plane. On the other hand, thickening of the twin could engulf some pile-up edge components in front of the TB. During this process, these hc + ai dislocations transmuted from a pyramidal plane ð0 " 111Þ in the matrix to a prismatic plane ð " 1010Þ T in the twin lattice. Finally, possible mechanisms for the nucleation and growth of T2 twins will be discussed.

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Section: A Sample and Deformationmentioning

confidence: 99%

mentioning

confidence: 99%

Study of $$ \{ 11\bar{2} 1\} $$ Twinning in α-Ti by EBSD and Laue Microdiffraction

Wang

Barabash

Bieler

et al. 2013

Metall Mater Trans A

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“…1b). This effect may be related to the suppression of twinning at large strains [13] as well as with texture changes, discussed below. Furthermore, the strain hardening rate approached almost zero at the maximum level of deformation (Fig.…”

Section: Microhardnessmentioning

confidence: 98%

“…4a and b). This effect was presumably associated with relatively easy slip within twinned regions [13,17,18]. The LABs were usually short, curved, and irregular in appearance.…”

Section: Low Strainsmentioning

confidence: 99%

Grain-structure development in heavily cold-rolled alpha-titanium

D’yakonov

Mironov

Zherebtsov

et al. 2014

Materials Science and Engineering: A

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a b s t r a c tHigh-resolution electron back-scatter diffraction (EBSD) analysis was employed to establish mircostructure evolution in heavily cold-rolled alpha-titanium. After thickness reductions of 75% to 96%, significant microstructure and texture changes were documented. The surface area of high-angle grain boundaries was almost tripled, thus giving rise to an ultra-fine microstructure with a mean grain size of 0.6 μm. Moreover, orientation spread around typical 'split-basal' rolling texture substantially increased.These effects were suggested to be related to the enhancement of pyramidal 〈c þa〉 slip.

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“…Moreover, the microstructures, including the crystal orientations, grain size, and grain boundaries, also play vital roles in determining the mechanical behavior [13]. Many studies have been conducted to determine the mechanical responses of CP-Ti under various loading conditions from both micro-and macroscopic viewpoints [14][15][16][17][18][19]. A literature survey on the previous studies is presented in our past paper [9].…”

Section: Introductionmentioning

confidence: 99%

Anisotropic deformation behavior under various strain paths in commercially pure titanium Grade 1 and Grade 2 sheets

Hama

Kobuki

et al. 2016

Materials Science and Engineering: A

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In this study, the anisotropic deformation behavior in commercially pure titanium Grade 1 and Grade 2 sheets under various strain paths was examined. A small but sharp stress peak arose during tension following compression in the Grade 1 sheet when loaded in the rolling direction, and the occurrence of a stress peak was retarded when the sheet was subjected to cyclic loading; however, such behavior did not occur in the Grade 2 sheet. Similarly, the work-hardening rate was different between the initial and latter stages of compression following tension. These behaviors did not arise when the sheets were loaded in other directions. The type of active twin mode was different depending on the loading path. When loaded in the rolling direction in both Grade 1 and Grade 2 sheets, <101 � 2> twinning and detwinning were active, respectively, during compression and tension following compression, whereas <112 � 2> twinning and detwinning were active during tension and compression following tension. The twinning activity was much more pronounced in the Grade 1 sheet than in the Grade 2 sheet. The abovementioned stress-strain responses were presumed to result from twinning and detwinning activities as for magnesium alloy sheets.However, we concluded that the effect of twinning activity on the stress-strain curves was much smaller in the titanium sheet than in magnesium alloy sheets.

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Strain hardening of titanium: role of deformation twinning

Cited by 414 publications

References 17 publications

Study of $$ \{ 11\bar{2} 1\} $$ Twinning in α-Ti by EBSD and Laue Microdiffraction

Study of $$ \{ 11\bar{2} 1\} $$ Twinning in α-Ti by EBSD and Laue Microdiffraction

Grain-structure development in heavily cold-rolled alpha-titanium

Anisotropic deformation behavior under various strain paths in commercially pure titanium Grade 1 and Grade 2 sheets

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