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摘要:
钼铼合金属于高熔点、低膨胀系数的固溶强化合金，添加稀土氧化物能够细化钼铼合金晶粒，起到弥散强化的作用。采用粉末冶金技术和交叉轧制法制备钼铼（Mo–Re）合金和钼铼镧（Mo–Re–La2O3）合金板材，并对两种合金板材进行不同温度的退火热处理。通过金相显微镜和电子扫描显微镜观察了钼铼合金板材和钼铼镧合金板材在不同退火温度下合金显微组织和室温拉伸断口形貌，比较了两种合金板材的维氏硬度和室温拉伸性能。结果表明，钼铼合金的再结晶温度为
1200 ℃左右，而钼铼镧合金的再结晶温度为1400 ℃，La2O3的加入使再结晶温度提升200 ℃左右；随着退火温度提高，钼铼合金和钼铼镧合金的硬度和抗拉强度显著降低，而钼铼镧合金的延伸率得以升高，最高可达27.5%。Abstract:Molybdenum rhenium alloys are the solid solution strengthening alloys with high melting point and low expansion coefficient, and the addition of rare earth oxides can refine the grains and play a role in dispersion strengthening. Molybdenum−rhenium (Mo–Re) and molybdenum−rhenium−lanthanum (Mo–Re–La2O3) alloy plates were prepared by powder metallurgy and cross rolling method in this paper, and were annealed at different temperatures. The microstructure and room temperature tensile fracture morphology of the Mo–Re alloys and Mo–Re–La2O3 alloys annealed at different temperatures were observed by metallographic microscope and scanning electron microscope. The Vickers hardness and room temperature tensile properties of the two alloy plates were compared. The results show that the recrystallization temperature of Mo–Re alloys is about
1200 ℃, while that of the Mo–Re–La2O3 alloys is1400 ℃. The addition of La2O3 increases the recrystallization temperature by about 200 ℃. With the increase of annealing temperature, the hardness and tensile strength of the Mo–Re alloys and Mo–Re–La2O3 alloys decrease significantly, while the elongation of Mo–Re–La2O3 alloys increases, up to 27.5%. -
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图 2 烧结态钼合金的金相组织：（a）Mo–Re；（b）Mo–Re–La2O3
Figure 2. Metallographic structure of the sintered molybdenum alloys: (a) Mo–Re; (b) Mo–Re–La2O3
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图 3 轧制态及不同温度退火后Mo–Re合金金相组织：（a）轧制态；（b）
1100 ℃退火；（c）1200 ℃退火；（d）1300 ℃退火Figure 3. Microstructure of the Mo–Re alloys in rolled state and after annealing at different temperatures: (a) rolled state; (b) annealing at
1100 ℃; (c) annealing at1200 ℃; (d) annealing at1300 ℃![]()
图 4 轧制态及不同温度退火后Mo–Re–La2O3合金金相组织：（a）轧制态；（b）
1300 ℃退火；（c）1400 ℃退火；（d）1500 ℃退火Figure 4. Microstructure of the Mo–Re–La2O3 alloys in rolled state and after annealing at different temperatures: (a) rolled state; (b) annealing at
1300 ℃; (c) annealing at1400 ℃; (d) annealing at1500 ℃![]()
图 5 轧制态及不同温度退火后Mo–Re合金的电子背散射衍射反极图：（a）轧制态；（b）
1100 ℃退火；（c）1200 ℃退火；（d）1300 ℃退火Figure 5. IPF color maps of the Mo–Re alloys in rolled state and after annealing at different temperatures: (a) rolled state; (b) annealing at
1100 ℃; (c) annealing at1200 ℃; (d) annealing at1300 ℃![]()
图 6 轧制态及不同温度退火后Mo–Re–La2O3合金的电子背散射衍射反极图：（a）轧制态；（b）
1300 ℃退火；（c）1400 ℃退火；（d）1500 ℃退火Figure 6. IPF color maps of the Mo–Re–La2O3 alloys in rolled state and after annealing at different temperatures: (a) rolled state; (b) annealing at
1300 ℃; (c) annealing at1400 ℃; (d) annealing at1500 ℃![]()
图 7 轧制态及不同温度退火后钼合金的维氏硬度：（a）Mo–Re合金；（b）Mo–Re–La2O3合金
Figure 7. Vickers hardness of the molybdenum alloys in rolled state and after annealing at different temperatures: (a) Mo–Re alloys; (b) Mo–Re–La2O3 alloys
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图 8 轧制态及不同温度退火后Mo–Re合金的抗拉强度与延伸率
Figure 8. Tensile strength and elongation of the Mo–Re alloys in rolled state and after annealing at different temperatures
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图 9 轧制态及不同温度退火后Mo–Re–La2O3合金的抗拉强度与延伸率
Figure 9. Tensile strength and elongation of the Mo–Re–La2O3 alloys in rolled state and after annealing at different temperatures
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图 10 轧制态及不同温度退火后Mo–Re合金断口形貌：（a）轧制态；（b）
1100 ℃退火；（c）1200 ℃退火；（d）1300 ℃退火Figure 10. Fracture morphology of the Mo–Re alloys in rolled state and after annealing at different temperatures: (a) rolled state; (b) annealing at
1100 ℃; (c) annealing at1200 ℃; (d) annealing at1300 ℃![]()
图 11 轧制态及不同温度退火后Mo–Re–La2O3合金的断口形貌：（a）轧制态；（b）
1300 ℃退火；（c）1400 ℃退火；（d）1500 ℃退火Figure 11. Fracture morphology of the Mo–Re–La2O3 alloys in rolled state and after annealing at different temperatures: (a) rolled state; (b) annealing at
1300 ℃; (c) annealing at1400 ℃; (d) annealing at1500 ℃表 1 热处理前钼合金的性能
Table 1 Physical properties of the molybdenum alloys before heat treatment
试样 La2O3质量分数 / % 晶粒尺寸 / μm 密度 / (g·cm−3) 维氏硬度，HV 轧制变形量 / % Mo–Re 0 78.8 10.85 163.02 82 Mo–Re–La2O3 0.78 25.2 10.89 191.14 82 
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