Effect of heat treatment temperature on microstructure and mechanical properties of Mo–14Re alloy tubes
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摘要: 研究了真空退火状态下不同热处理温度对Mo–14Re合金管材显微组织和室温力学性能的影响。结果表明：经轧制加工后的Mo–14Re合金管材晶粒组织沿轧制方向被拉长，呈明显的纤维组织，1100 ℃热处理后晶粒组织局部有宽化现象；随着热处理温度升高，1300 ℃热处理合金管材晶粒组织完成再结晶。热处理条件为1100 ℃、1 h的Mo–14Re合金管材表现出优异的强度与塑性组合，抗拉强度为710 MPa，延伸率为36.5%。断口分析发现，当退火温度在1100 ℃以下，Mo–14Re合金管材出现木纹状撕裂型断裂，表现出明显的塑性变形特征；当热处理温度提高到1300 ℃时，由于发生了再结晶，断口呈准解理断裂，塑性明显下降，变形主要以晶界滑移为主。综合分析表明，Mo–14Re合金轧制管材最佳热处理温度应该控制在1100～1300 ℃之间。
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关键词:
- Mo–14Re合金管 /
- 微观组织 /
- 真空退火 /
- 力学性能 /
- 断口形貌
Abstract: The effects of heat treatment temperatures on the microstructure and mechanical properties of Mo–14Re alloy tubes after the vacuum annealing were studied in this paper. The results show that, the grains of Mo–14Re alloy tubes after rolling are elongated along the rolling direction, showing the obvious fiber structure, and the grains are locally widened after the heat treatment at 1100 ℃. With the increase of heat treatment temperature, the grains of Mo–14Re alloy tubes are completely recrystallized at 1300 ℃. The Mo–14Re alloy tubes show the excellent combination of strength and plasticity at 1100 ℃ for 1 h, the tensile strength is 710 MPa, and the elongation is 36.5%. In the fracture analysis, it is found that the Mo–14Re alloy tubes have the wood grain tearing fracture at the annealing temperature below 1100 ℃, showing the obvious plastic deformation characteristics. However, when the heat treatment temperature is increased to 1300 ℃, the fracture is quasi-cleavage due to the recrystallization, and the plastic deformation is mainly caused by grain boundary slip. Comprehensive analysis shows that the optimal heat treatment temperature of Mo–14Re alloy rolling tubes should be controlled between 1100 ℃ and 1300 ℃.-
Key words:
- Mo–14Re alloy tubes /
- microstructure /
- vacuum annealing /
- mechanical properties /
- fracture morphology
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图 1 实验原料粉末：（a）高纯钼粉；（b）高纯铼粉；（c）混合钼铼粉
Figure 1. Experimental raw powders: (a) high purity molybdenum powders; (b) high purity rhenium powders; (c) mixed molybdenum-rhenium powders
图 2 烧结Mo–14Re坯锭显微组织（a）和轧制Mo–14Re管材（b）
Figure 2. Microstructure of Mo–14Re billets after sintering (a) and the Mo–14Re pipes after rolling (b)
图 3 经过不同温度热处理的Mo–14Re管材微观组织：（a）轧制态；（b）900 ℃，1 h；（c）1100 ℃，1 h；（d）1300 ℃，1 h
Figure 3. Microstructure of the Mo–14Re tubes after heat treatment at the different temperatures: (a) rolling state; (b) 900 ℃, 1 h; (c) 1100 ℃, 1 h; (d) 1300 ℃, 1 h
图 4 不同退火温度下Mo–14Re管材强度和延伸率
Figure 4. Tensile strength and elongation of the Mo–14Re tubes at the different annealing temperatures
图 5 不同温度热处理的Mo–14Re管材室温拉伸宏观和断口形貌：（a）轧制态；（b）900 ℃，1 h；（c）1100 ℃，1 h；（d）1300 ℃，1 h
Figure 5. Tensile macromorphology and fracture morphology of the Mo–14Re tubes at room temperature under the different heat treatments: (a) rolling state; (b) 900 ℃, 1 h; (c) 1100 ℃, 1 h; (d) 1300 ℃, 1 h
表 1 Mo–14Re管材轧制前后密度
Table 1. Density of the Mo–14Re pipes before and after rolling
材料状态 实测密度 / (g·cm−3) 相对密度 / % 烧结坯料 10.13 92.1 轧制管材 10.98 99.7 
下载: 导出CSV
表 2 Murakamig腐蚀剂成分
Table 2. Component of Murakamig etchant
K3Fe(CN)6 KOH（或者NaOH） H2O 10 g 10 g 100 mL
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