Modeling constitutive relationship of Ti17 titanium alloy with lamellar starting microstructure

Ma, Xiong; Zeng, Weidong; Sun, Yu; Wang, Kaixuan; Lai, Yunjin; Zhou, Yigang

doi:10.1016/j.msea.2012.01.027

Cited by 56 publications

(12 citation statements)

References 31 publications

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“…Similar conclusions have been drawn by Ma et al [20]. The strain localization process driving to the formation of shear bands has been investigated by Huang et al [21].…”

supporting

confidence: 83%

Impact of the initial microstructure and the loading conditions on the deformation behavior of the Ti17 titanium alloy

et al. 2019

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In this work, the impact of the microstructure and the loading conditions on the mechanical behavior of a brich Ti17 titanium alloy is investigated. For this purpose, two different initial microstructures are considered : (i) a two-phase lamellar a ? b microstructure and (ii) a single-phase equiaxed b-treated microstructure. First, compression tests are performed at different strain rates (from 10 À1 to 10 s-1) and different temperatures (from 25 to 900 C) for both microstructures. Then, optical microscopy, scanning electron microscopy, EBSD and X-ray diffraction analyses of deformed specimens are carried out. Whatever the loading conditions are, the flow stress of the as-received a ? b Ti17 is higher than that of the b-treated Ti17. Also, because of a higher strain-rate sensitivity, the b-treated Ti17 is less prone to shear banding. At low temperatures (i.e., T 450 C), the deformation behavior of both the as-received a ? b and the b-treated Ti17 is controlled by strain hardening. For the b-treated Ti17 alloy, martensitic transformation is systematically detected in this temperature range. The softening behavior of the as-received a ? b Ti17 observed at high temperatures is due to the joint effect of dynamic recrystallization, dynamic transformation , adiabatic heating and morphological texture evolution. For the b-treated Ti17 alloy, when the temperature exceeds 700 C, stressstrain curves display a yield drop phenomenon, which is explained by dynamic recrystallization.

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“…Similar conclusions have been drawn by Ma et al [20]. The strain localization process driving to the formation of shear bands has been investigated by Huang et al [21].…”

supporting

confidence: 83%

Impact of the initial microstructure and the loading conditions on the deformation behavior of the Ti17 titanium alloy

et al. 2019

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“…Furthermore, the higher discontinuous yielding degree at a higher strain rate can be related to the more rapid dislocation generation at the grain boundary. Lai et al [12] observed the dislocations piling up at the β boundary and then entering into the adjacent the β grain in Ti-17, which supports the second pattern to cause discontinuous yielding.…”

Section: Introductionmentioning

confidence: 79%

Relationship between Flow Behavior and Microstructure Evolution during Isothermal Compression of near β Titanium Alloy Ti-55531 with Acicular Starting Microstructure

Zhang

et al. 2018

Metals

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Near β titanium alloy Ti-55531 with an acicular starting microstructure was isothermally compressed at 750-825 • C and 10 −3 −1 s −1 . The microstructure evolution and its influence on the flow behavior of yielding and softening were investigated. Discontinuous or continuous yielding depends on the hindrance to the dislocation motion coming from the β grain boundary or α phase. At higher temperatures, the hindrance mainly comes from the β grain boundary. Its discontinuous action, including the piling-up and subsequent loosening of dislocations at the β grain boundary, leads to discontinuous yielding. At lower temperatures, the continuous hindrance to the dislocation motion, which is exerted by the β grain boundary and acicular α, causes continuous yielding. Sequentially, the substructures in acicular α are evolved from high-density dislocations or local shear bands, which depend on the orientation relationship between β and α. Then, the β matrix edges into the acicular α along substructure boundaries. The higher strain rate decreases the deformation time to carry out the fragmentation of acicular α, while the higher temperature decreases the dislocation density due to the recovery of β, which does not benefit the substructure formation and subsequent fragmentation of acicular α. Therefore, the retardation of acicular fragmentation and the as-resulted decreased flow softening rate are observed.

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“…The flow plastic instability maps proposed by the Prasad criteria demonstrated analogous zones to the flow instability maps of the Murty criterion. Zeng et al (Xiong et al, 2012b) investigated the hot deformation behavior and the hot processing map of Ti-22Al-25Nb alloys based on the Murty criterion. In this work, the flow instability map was established by the procedure described by the Prasad criteria.…”

Section: Processing Mapmentioning

confidence: 99%

Characterization of Ti-25.5Al-13.5Nb-2.8Mo-1.8Fe Alloy Hot Deformation Behavior Through Processing Map

Cheng

Zhang

et al. 2020

Front. Mater.

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The isothermal compression tests of Ti-25. 5Al-13.5Nb-2.8Mo-1.8Fe (at.%) alloys were executed under a deformation temperature range of 950-1,100 • C with a strain rate range of 0.001-1 s −1 for a total height reduction of 0.5. The isothermal compression deformation behavior was investigated based on flow stress curves and dynamic model analysis. The processing map of the Ti-25.5Al-13.5Nb-2.8Mo-1.8Fe alloy was obtained for the optimum hot process parameters. The calculated value of Q (activation energy) was 634.5 kJ/mol. The constitutive model of the alloy was constructed. Based on DMM and the Prasad flow instability criteria, the hot processing map was established with a strain of 0.7. The deformation mechanisms were interpreted by microstructural observation within both stability and instability zones. A processing map showed a stable region under a deformation temperature range of 950-1,100 • C with a strain rate range of 0.001-1 s −1 . One certain maximum power dissipation efficiency value was ∼43% and occurred at 950 • C/0.001 s −1 . Another peak power dissipation efficiency value was about 58% at 1,050 • C/0.001 s −1 . Both areas were the optimum processing regions. Furthermore, while the strain rate value exceeded 1 s −1 , the alloy sustained a deformation instability phenomenon, such as a shearing band or flow localization.

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Modeling constitutive relationship of Ti17 titanium alloy with lamellar starting microstructure

Cited by 56 publications

References 31 publications

Impact of the initial microstructure and the loading conditions on the deformation behavior of the Ti17 titanium alloy

Impact of the initial microstructure and the loading conditions on the deformation behavior of the Ti17 titanium alloy

Relationship between Flow Behavior and Microstructure Evolution during Isothermal Compression of near β Titanium Alloy Ti-55531 with Acicular Starting Microstructure

Characterization of Ti-25.5Al-13.5Nb-2.8Mo-1.8Fe Alloy Hot Deformation Behavior Through Processing Map

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