Thermal deformation behavior and microstructure evolution of Mo–14Re alloys prepared by powder metallurgy
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摘要:
通过Gleeble
1500 热模拟试验机对粉末冶金法制备的Mo–14Re合金进行了恒应变速率压缩实验，分析了变形温度（1100 ～1400 ℃）和应变速率（0.100～0.001 s−1）对流变应力及组织演变的影响，并采用双曲正弦型Arrhenius模型建立了Mo–14Re合金的本构方程。结果表明：随着变形温度升高或者应变速率降低，粉末冶金Mo–14Re合金在热变形过程的流变应力也随之减小，真应力–真应变曲线表现出明显的加工硬化和动态软化现象。动态软化行为主要归结于粉末冶金Mo–14Re合金热压缩变形处于低应变速率（0.010 s−1和0.001 s−1）或较高变形温度（＞1200 ℃）时发生的动态再结晶，形核方式为晶界凸出形核，随着应变速率的降低或温度的升高，再结晶程度不断增加，晶粒不断长大，当温度为1400 ℃，应变速率为0.001 s−1时，完全再结晶完成。Abstract:The constant strain rate compression experiment of powder metallurgy Mo–14Re alloys was carried out by Gleeble
1500 thermal simulation tester. The effects of deformation temperature (1100 ~1400 ℃) and strain rate (0.100~0.001 s−1) on the flow stress and microstructure evolution were analyzed. The constitutive equation of Mo–14Re alloys was established by hyperbolic sinusoidal Arrhenius model. The results show that, the flow stress of powder metallurgy Mo–14Re alloys decreases with the increase of deformation temperature or the decrease of strain rate during the thermal deformation, and the true stress-true strain curve shows the obvious work hardening and dynamic softening phenomenon. The dynamic softening behavior is mainly attributed to the dynamic recrystallization of Mo–14Re alloys at low strain rate (0.010 s−1 and 0.001 s−1) or high deformation temperature (>1200 ℃) during the thermal compression. The nucleation mode is grain boundary protruding nucleation. With the decrease of strain rate or the increase of temperature, the degree of recrystallization continues to increase, the grains continue to grow, and the Mo–14Re alloys are completely recrystallized at1400 ℃ with the strain rate of 0.001 s−1.-
Keywords:
- Mo–14Re alloys /
- thermal deformation /
- constitutive equation /
- microstructure
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图 1 经混合后的钼铼合金粉显微形貌（a），锻造后Mo–14Re合金的轴向显微组织（b），热压缩后试样俯视图（c）和热压缩后试样正视图（d）
Figure 1. Microstructure of the mixed Mo–14Re alloy powders (a), the axial microstructure of the forged Mo–14Re alloys (b), the top view of the hot compression samples (c), and the front view of the hot compression samples (d)
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图 2 Mo–14Re合金在不同应变速率条件下的真应力–真应变曲线及抗压强度：（a）0.100 s−1；（b）0.010 s−1；（c）0.001 s−1；（d）抗压强度
Figure 2. Stress-strain curves and compressive strength of the Mo–14Re alloys at the different true strains: (a) 0.100 s−1; (b) 0.010 s−1; (c) 0.001 s−1; (d) compressive strength
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图 3 Mo–14Re合金热变形的应变速率–流变应力关系曲线：（a）ln
$ \dot \varepsilon $ –σ；（b）ln$ \dot \varepsilon $ –lnσFigure 3. Relationship between the strain rate and steady-state stress during the thermal deformation of Mo–14Re alloys: (a) ln
$ \dot \varepsilon $ –σ; (b) ln$ \dot \varepsilon $ –lnσ![]()
图 4 Mo–14Re合金热变形的流变应力–应变速率与温度–流变应力关系曲线：（a）ln
$ \dot \varepsilon $ −ln[sinh(ασ)]；（b）ln[sinh(ασ)]−1000 /TFigure 4. Flow stress-strain rate and temperature-flow stress of the Mo–14Re alloys during the thermal deformation: (a) ln
$ \dot \varepsilon $ −ln[sinh(ασ)]; (b) ln[sinh(ασ)]−1000 /T![]()
图 5 Mo–14Re合金热变形的lnZ−ln[sinh(ασ)]曲线
Figure 5. lnZ−ln[sinh(ασ)] curve of the thermal deformation for the Mo–14Re alloys
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图 6 粉末冶金Mo−14Re合金实验峰值应力与Arrhenius模型本构方程预测应力
Figure 6. Experimental peak stress and stress prediction by constitutive equation of Arrhenius model for the powder metallurgy Mo−14Re alloys
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