Effect of aging treatment on the behavior of room temperature tensile of P/M superalloys used for inertia friction welding joints
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摘要: 对惯性摩擦焊扩散连接的FGH96合金试样经时效处理前后的室温拉伸行为进行了研究，并对其失效机制进行了评估。结果表明，对于焊接态（原状态）FGH96合金试样，由于焊缝区和热影响区的γ′相综合强化效果弱，晶界平直化，导致焊缝区和热影响区的强度低于基体，在室温拉伸过程中塑性应变量大；由于热影响区的晶粒尺寸大，晶界强化效果弱，且位错强化效果低于焊缝区，使热影响区成为整个试样强度的最薄弱区域，裂纹从该处萌生，断口表现出一定的塑性特征。对于时效处理后的FGH96合金试样，由于γ′相的粗化，强化相体积分数的提高，及γ′/γ之间错配度的增加，提高了γ′相的综合强化效果，使焊缝区和热影响区的强度较焊接态试样显著提高，并高于基体，在室温拉伸过程中基体的塑性应变量相对较大。连续或半连续析出的M23C6型碳化物弱化了焊缝区晶界的结合强度，导致试样从该处断裂，并出现了脆性断裂的特征。显微硬度的测试结果较好验证了焊接态和时效态试样强度的分布情况。Abstract: The behavior of the room temperature tensile of the FGH96 P/M superalloys connected by the inertia friction welding before and after the aging treatment was investigated, and the failure mechanism of the FGH96 P/M superalloys was evaluated. The results show that, for the FGH96 P/M superalloy samples in the as-welded (original) state, the strength of the superalloy samples in the welding line zone (WLZ) and the heat affected zone (HAZ) is lower than that of the parent alloys, and the plastic strain is the largest during the room temperature tensile process, due to the weak comprehensive strengthening effect of γ′ phase and the straight grain boundaries in WLZ and HAZ. Because of the large grain size in HAZ, the weak strengthening effect of grain boundaries, and the lower dislocation density than that of WLZ, the strength of the superalloy samples in HAZ becomes the weakest, where the cracks originate and show a certain plastic characteristic of the fracture. For the FGH96 P/M superalloy samples after the aging treatment, the comprehensive strengthening effect of γ′ phase is improved, due to the coarsening of γ′ phase, the increase of the strengthened phase volume fraction, and the mismatch increase between γ and γ′, compared with the superalloy samples in the as-welded state, the strength of the superalloy samples after the aging treatment in WLZ and HAZ is higher than that of the parent alloys, and the plastic strain of the parent alloys is larger during the room temperature tensile process. The M23C6 carbide precipitated continuously or semi-continuously weakens the bonding strength of grain boundary in the as-welded state, leading to the sample fracture and showing the characteristic of brittle fracture. The results of microhardness test verify the strength distribution of the FGH96 P/M superalloy samples in the as-welded state and after the aging treatment.
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图 1 惯性摩擦焊接前后构件：（a）焊接前；（b）焊接后
Figure 1. Components for theinertia friction weld: (a) before welding; (b) after welding
图 3 FGH96粉末高温合金惯性摩擦焊试样室温拉伸应力–应变曲线
Figure 3. Stress−straincurve of the FGH96 P/M superalloy samplesconnected by the inertia friction welding for the room temperature tensile tests
图 4 FGH96粉末高温合金惯性摩擦焊试样断裂位置及断口形貌：（a）焊接态；（b）时效态
Figure 4. Fracture location and morphology of the FGH96 P/M superalloy samples connected by the inertia friction welding: (a) as-welded state; (b) PWHT
图 5 室温拉伸过程中两组试样工作段的应变分布情况：（a）焊接态试样S1-Y1；（b）时效态试样S2-Y2
Figure 5. Strain distribution of the tested samples for the room temperature tensile: (a) S1-Y1 in as-welded state; (b) S2-Y2 by PWHT
图 6 FGH96粉末高温合金惯性摩擦焊试样不同区域晶粒尺寸：（a）焊接态；（b）时效态
Figure 6. Grain size in different zones of the FGH96 P/M superalloy samples connected by the inertia friction welding: (a) as-welded state; (b) PWHT
图 7 FGH96粉末高温合金焊接态试样不同部位晶界形貌：（a）焊缝区；（b）基体区
Figure 7. Grain boundary images of the FGH96 P/M superalloy samples in as-welded state: (a) WLZ; (b) PAZ
图 8 时效处理后焊缝处析出的碳化物相
Figure 8. Carbide phase images precipitated in WLZ after the aging treatment
图 9 试样部位及时效处理对晶体取向差的影响：（a）焊接态焊缝区；（b）焊接态热影响区；（c）焊接态基体区；（d）时效态焊缝区；（e）时效态热影响区；（f）时效态基体区
Figure 9. Influence of the sample zones and ageing treatment on the grain misorientation: (a) WLZ in as-welded state; (b) HAZ in as-welded state; (c) PAZ in as-welded state; (d) WLZ by PWHT; (e) HAZ by PWHT; (f) PAZ by PWHT
图 10 试样部位及时效处理对三次γ′相尺寸的影响：（a）焊接态焊缝区；（b）焊接态热影响区；（c）焊接态基体区；（d）时效态焊缝区；（e）时效态热影响区；（f）时效态基体区
Figure 10. Influence of the sample zones and ageing treatment on the grain size of tertiary γ′: (a) WLZ in as-welded state; (b) HAZ in as-welded state; (c) PAZ in as-welded state; (d) WLZ by PWHT; (e) HAZ by PWHT; (f) PAZ by PWHT
图 12 焊接态和时效态试样显微硬度沿轴向的分布
Figure 12. Micro-hardness in the axial distribution of the FGH96 P/M superalloy samples in as-welded state or by PWHT
表 1 FGH96合金化学成分（质量分数）
Table 1. Chemical composition of the FGH96 alloys
% Co Cr Mo W Al Ti Nb C B Zr Ni 12.960 16.170 4.040 4.010 2.200 3.780 0.690 0.050 0.016 0.042 余量 
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