Crystal plasticity finite element study of tensile behavior of two-phase titanium alloy Ti-6Al-4V
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摘要: 通过晶体塑性有限元方法探究了α/β相含量和晶粒尺寸对Ti-6Al-4V双相钛合金拉伸力学性能的影响，通过滑移相对分数定量化评估不同滑移系对塑性变形的贡献。结果表明：Ti-6Al-4V钛合金拉伸变形过程中应力应变分布不均匀，应力集中在β相变体晶粒及晶界处，应变集中在α相晶粒附近。随β相含量升高，应力集中区域更多，三叉晶界处越易产生应变集中，β相$ \left\{110\right\} $滑移系对塑性变形的贡献大幅提高。随着α相、β相或两相晶粒尺寸同时扩大，塑性段应力应变曲线下降，且初始变形都主要由柱面滑移系主导，锥面$ \left\langle\mathrm{c}+\mathrm{a}\right\rangle $滑移系贡献次之。增大α相晶粒尺寸，锥面$ \left\langle\mathrm{c}+\mathrm{a}\right\rangle $滑移系活性下降，导致塑性阶段应力值降低。增大β相晶粒尺寸，塑性阶段应力的降低与β相中$ \left\{110\right\} $滑移系活性下降有关。同时增大α及β相晶粒尺寸时，会同时影响柱面滑移系和$ \left\{110\right\} $滑移系的相对分数，应力值的下降与界面数量的显著下降有关。Abstract: The influence of α/β volume fraction and grain size on the tensile mechanical properties of Ti-6Al-4V dual-phase titanium alloy was investigated in this study using the crystal plasticity finite element method. The contribution of different slip systems to plastic deformation was evaluated quantitatively by slip relative fraction. The results demonstrate that the stress-strain distribution during the tensile deformation of Ti-6Al-4V titanium alloy is non-uniform. The stress is primarily concentrated on the β phase grain and grain boundary, while the strain is concentrated on the α phase grain. Increasing the volume fraction of β phase leads to a larger stress concentration area, easier generation of strain concentration at the triple-junction of grain boundaries, and a significant increase in contribution from the β phase{110} slip system to the plasticity deformation. Increasing α, β or two-phase grain size results in decreased stress-strain curve in the plastic region, where initial deformation is predominantly governed by prismatic slip system while pyramidal <c+a> slip system contribute slightly less. An increase in α-phase grain size leads to a decrease in the activity of pyramidal <c+a> slip system, resulting in reduced stress values in the plastic region. Increasing the β-phase grain size results in a reduction of stress during the plastic stage, which is attributed to the decreased activity of {110} slip system within the β-phase. Simultaneously increasing the grain size of both the α and β phases will affect the activation fraction of prismatic and {110} slip systems. The reduction in stress is associated with the significant decrease in the number of interfaces.
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Key words:
- Ti-6Al-4V /
- tensile behaviors /
- crystal plasticity /
- stress-strain /
- slip system /
- finite element method
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图 1 (a)Dream3D微观结构中相、晶粒、欧拉角、晶界分布；(b)单轴拉伸模拟与试验应力应变对比
Figure 1. (a) Phase, grain, Euler Angle and grain boundary distribution in Dream3D microstructure, (b) stress-strain comparison between uniaxial tensile simulation and experiment
图 2 不同β相体积分数下拉伸模拟结果
（a）应力分布；（b）应变分布；（c） β相分布
Figure 2. Tensile simulation results with different β-phase volume fractions
图 3 25% β相含量下拉伸15%应变后变形情况
Figure 3. Deformation of 15% strain at 25% β-phase volume fraction
图 4 不同β相体积分数下应力应变曲线
Figure 4. Stress-strain curves with different β-phase volume fractions
图 5 不同β相体积分数下滑移活性分析
（a）基面滑移；（b）柱面滑移；（c）锥面$ \left\langle\mathrm{c}+\mathrm{a}\right\rangle $滑移；（d）$ \left\{110\right\} $滑移
Figure 5. Slip activity analysis under different β-phase volume fractions
图 7 不同α相晶粒尺寸下滑移活性分析
（a）基面滑移；（b）柱面滑移；（c）锥面$ \left\langle{{\mathrm{c}}+{\mathrm{a}}}\right\rangle $滑移；（d）$ \left\{110\right\} $滑移
Figure 7. Slip activity analysis under different α-phase grain sizes
图 9 不同β相晶粒尺寸下滑移活性分析
（a）基面滑移；（b）柱面滑移；（c）锥面$ \left\langle{{\mathrm{c}}+{\mathrm{a}}}\right\rangle $滑移；（d）$ \left\{110\right\} $滑移
Figure 9. Slip activity analysis under different β-phase grain sizes
图 10 不同α及β相晶粒尺寸下应力应变曲线
Figure 10. Stress-strain curves for different grain sizes of α and β phases
图 11 不同α和β尺寸下滑移活性分析
（a）基面滑移；（b）柱面滑移；（c）锥面$ \left\langle{{\mathrm{c}}+{\mathrm{a}}}\right\rangle $滑移；（d）$ \left\{110\right\} $滑移
Figure 11. Slip activity analysis under different grain sizes of α and β phases
图 12 不同α及β相晶粒尺寸下拉伸模拟结果
（a）应力分布；（b）应变分布；（c）晶粒分布
Figure 12. Distributions of stress and strain under different grain sizes of α and β phase
滑移系 $ {\tau }_{0}/\mathrm{M}\mathrm{P}\mathrm{a} $ m $ {\dot{\gamma }}_{0}/{\mathrm{s}}^{-1} $ $ {h}_{0}/\mathrm{M}\mathrm{P}\mathrm{a} $ $ a $ 基面$ \left\langle\mathrm{a}\right\rangle $ 390 0.01 1.0 190 50 柱面$ \left\langle\mathrm{a}\right\rangle $ 390 0.01 1.0 190 50 锥面$ \left\langle\mathrm{c}+\mathrm{a}\right\rangle $ 663 0.01 1.0 190 50 β$ \left\{110\right\}\left\langle{111}\right\rangle $ 390 0.01 1.0 190 50 
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