Effect of microstructure evolution on tensile properties of novel nickel-based powder metallurgy superalloys during long-term aging
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摘要: 研究了新型镍基粉末高温合金在800 ℃时效100～5000 h后显微组织对拉伸性能的影响。结果表明：随着时效时间的增加，合金的晶粒尺寸未发生明显变化，晶界粗化并呈现为不连续“锯齿状”；二次γ′相发生合并粗化，粗化符合LSW理论；TCP相的析出量随时效时间的增加而增大，1000 h后在晶界处呈现细小白条状析出，2000 h后在晶内呈现大量长条形针状析出，5000 h时TCP相含量达到最大；受二次γ′相粗化的影响，合金的700 ℃拉伸强度和塑性随时效时间的增加而逐渐降低；拉伸断口具有颈缩和韧窝特征，断裂均为韧窝断裂。Abstract: The influence of microstructure evolution on the tensile properties of the novel nickel-based powder metallurgy superalloys after long-term aging at 800 ℃ for 100~5000 h was studied. The results show that the grain size of the alloys does not change significantly with the increase of aging time, and the grain boundaries are coarsened and appear the discontinuous “sawtooth”. Secondary γ′ phase particles obviously coarsen which conforms to the LSW theory. The content of TCP phases precipitated increases with the increase of aging time. After aging for 1000 h, the intermittent long white precipitates are observed at the grain boundary. After aging for 2000 h, a large number of elongate needle-like precipitates appear in the grain. The content of TCP phases reaches the maximum after aging for 5000 h. Due to the coarsening of the secondary γ′ phase, the tensile strength and plasticity of the alloys at 700 ℃ gradually decrease with increasing the aging time. The tensile fracture has the characteristics of necking and dimple, and the fracture shows the dimple fracture.
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图 1 标准热处理后合金显微组织：（a）、（b）金相显微镜；（c）、（d）扫描电镜
Figure 1. Microstructure of the alloys after the standard heat treatment: (a), (b) OM; (c), (d) SEM
图 2 800 ℃长期时效合金晶粒显微组织：（a）100 h；（b）500 h；（c）1000 h；（d）2000 h；（e）、（f）5000 h
Figure 2. Grain structure of the alloys aged at 800 ℃ for different times: (a) 100 h; (b) 500 h; (c) 1000 h; (d) 2000 h; (e), (f) 5000 h
图 3 800 ℃长期时效合金γ′相显微形貌：（a）100 h；（b）500 h；（c）1000 h；（d）2000 h；（e）5000 h
Figure 3. SEM images of the γ′ phases aged at 800 ℃ for different times: (a) 100 h; (b) 500 h; (c) 1000 h; (d) 2000 h; (e) 5000 h
图 4 800 ℃长期时效合金的二次γ′相平均半径与失效时间关系曲线
Figure 4. Relationship between the secondary γ′ phase size of the alloys and aging time at 800 ℃
图 5 800 ℃长期时效合金TCP相形貌：（a）100 h；（b）500 h；（c）1000 h；（d）2000 h；（e）5000 h
Figure 5. BSE images of the TCP phases aged at 800 ℃ for different times: (a) 100 h; (b) 500 h; (c) 1000 h; (d) 2000 h; (e) 5000 h
图 6 800 ℃长期时效合金拉伸性能
Figure 6. Tensile properties of the alloys aged at 800 ℃ for different times
图 7 800 ℃长期时效合金拉伸断口整体形貌：（a）100 h；（b）500 h；（c）1000 h；（d）2000 h；（e）5000 h
Figure 7. Tensile fractures SEM images of the alloys aged at 800 ℃ for different times: (a) 100 h; (b) 500 h; (c) 1000 h; (d) 2000 h; (e) 5000 h
图 8 800 ℃长期时效5000 h下合金拉伸断口形貌：（a）断口局部；（b）裂纹萌生；（c）裂纹扩展；（d）裂纹断裂
Figure 8. Tensile fractures SEM images of the alloys aged at 800 ℃ for 5000 h: (a) local morphology of tensile fracture; (b) crack initiation region; (c) crack propagation region; (d) rapidly fracture region
表 1 镍基粉末高温合金化学成分（质量分数）
Table 1. Chemical composition of the nickel-based powder metallurgy superalloys
% Cr Co Mo Ta W Al Nb Ti C B Zr Ni 11.0～13.0 19.0～22.0 3.5～6.0 2.4～4.0 2.1～2.5 3.0～5.0 0.5～1.0 3.0～4.5 0.05 0.03 0.05 余量 
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表 2 800 ℃长期时效合金晶粒尺寸
Table 2. Grain size of the alloys aged at 800 ℃ for different times
时效时间 / h 晶粒尺寸 / μm 标准差 100 13.80 6.78 500 14.48 6.27 1000 14.97 8.34 2000 12.97 6.46 5000 14.78 7.22
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表 3 800 ℃长期时效合金二次γ′相平均尺寸
Table 3. Size of the secondary γ′ phases aged at 800 ℃ for different times
时效时间 / h 二次γ′相平均尺寸（半径） / nm 100 71.4 500 71.4 1000 85.6 2000 110.0 5000 132.3
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表 4 800 ℃长期时效合金TCP相含量
Table 4. Content of the TCP phases aged at 800 ℃ for different times
时效时间 / h TCP相面积分数 / % 100 — 500 — 1000 0.392 2000 2.430 5000 2.667
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