Influence of microstructure and loading conditions on the dynamic tensile property of Ni-based single crystal superalloys
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摘要: 为促进装备热端部件在动态载荷下服役性能的评估和预测，针对不同微结构特征的镍基单晶高温合金开展了一系列分离式霍普金森拉杆（split Hopkinson tensile bar，SHTB）试验和扫描电镜表征，系统研究了沉淀相体积分数、相粗化程度、应变率和加载角度等因素对合金动态拉伸性能的影响。结果表明：微结构和应变率对镍基单晶高温合金动态拉伸性能具有显著影响，且相粗化后合金动态拉伸性能呈现出复杂的各向异性特征。总体而言，合金屈服强度和抗拉强度呈正相关关系，随着沉淀颗粒体积分数或应变率的增大，试件逐渐表现出脆性断裂特征，且其屈服强度和抗拉强度逐渐增大，而极限伸长率则逐渐减小；其次，时效处理所导致的颗粒相粗化对合金强度有着明显的弱化作用，而对极限伸长率起到强化效果，即相粗化后合金试样表现出混合断裂特征，随着相粗化程度增加，其屈服强度和抗拉强度逐渐降低，而极限伸长率逐渐增大。此外，在55°加载角度时，合金强度和极限伸长率均低于0°加载角度下的情况；然而，在应变率较高时，对于体积分数和相粗化程度均较大的合金，其极限伸长率在55°加载角度时取得最大值。相关变化同断口纤维区面积和解理面特征密切相关，材料微结构和加载条件的改变将影响材料内部微裂纹形核和运动特性，进而影响合金变形特征和动态拉伸性能。研究结果可为提高镍基单晶高温合金性能和优化热端部件结构设计提供理论支持和数据支撑。Abstract: To enhance the evaluation and prediction for service performance of hot-end components in equipment under the dynamic loads, a comprehensive study was conducted on Ni-based single crystal superalloys with diverse microstructures. This study involved a series of split Hopkinson tensile bar (SHTB) tests and related scanning electron microscopy (SEM) characterization. The influences of various factors, including the volume fraction of precipitation particles, phase coarsening, loading angle and strain rate, etc., on the dynamic tensile properties of superalloys were systematically investigated. Moreover, the relationships between these factors and the fracture morphology of alloys were thoroughly discussed. The results indicated that the microstructural features and strain rate have significant effect on the dynamic tensile properties of alloys, leading to a complex anisotropic characteristic occur in their dynamic tensile behaviors after phase coarsening. In general, the yielding strength displays a positive relationship with the tensile strength. As the volume fraction of precipitation particles or the strain rate increases, the alloy specimen gradually exhibits brittle fracture characteristics, with an increase in strength and a decrease in elongation. Besides, phase coarsening derived from the aging treatment significantly weakens the strength of alloys while enhancing their elongation, i.e., the specimens progressively show mixed fracture characteristics after phase coarsening, and both yielding strength and tensile ultimate strength gradually decrease while the elongation increases with the degree of phase coarsening. Furthermore, the strength and elongation of alloys at the loading angle of 55° are lower than those at the loading angle of 0°. Comparatively, for alloys with high volume fraction of precipitation particles and high degree of phase coarsening, the elongation achieves the maximum value at the loading angle of 55°. The corresponding variation characteristics are closely related to the fibrous zone and the cleavage plane on the fracture surface. Meanwhile, the variations in microstructure of materials and loading conditions affect the microcrack nucleation and fracture mode within the specimen, leading to various dynamic tensile properties in Ni-based single crystal superalloys. The present research and related results provide theoretical guidance and experimental data support for improving the mechanical performance of Ni-based single crystal superalloys and optimizing the design of hot-end components.
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图 1 不同镍基单晶高温合金的棒材形貌及SEM图像
Figure 1. Macroscopic shape and SEM image of various Ni-based single crystal superalloys
图 2 SHTB试验试件形貌及尺寸(单位：mm)
Figure 2. Specimen structures and the corresponding size for SHTB test (unit: mm)
图 4
$ \theta $ =0°时SHTB试验中不同相粗化程度合金对应的应力-应变曲线Figure 4. Stress-strain curves corresponding to different degrees of phase coarsening in alloys in the SHTB tests at
$ \theta $ =0°
图 5
$ \theta $ =0°时不同相粗化程度对应合金拉伸力学性能变化特征Figure 5. Dynamic tensile properties corresponding to alloys with different degrees of phase coarsening in the condition of
$ \theta $ =0°
图 6
$ \theta $ =0°时SHTB试验在$ \dot{\varepsilon } $ =1500 s−1时不同沉淀颗粒体积分数对应的应力-应变曲线和动态拉伸力学性能变化特征Figure 6. Stress-strain curves and dynamic tensile properties corresponding to different volume fractions of precipitation particles in the SHTB tests with
$ \dot{\varepsilon } $ =1500 s−1 and$ \theta $ =0°
图 7 SHTB试验中不同加载方向对应的应力-应变曲线
Figure 7. Stress-strain curves corresponding to different loading angles in the SHTB tests
图 8 不同材料和不同加载方向对应的拉伸力学性能变化特征
Figure 8. Dynamic tensile properties corresponding to different alloys and loading angles
图 9
$ \theta $ =0°时$ \varphi $ =60%合金试件在$ \dot{\varepsilon } $ =900 s−1应变率下拉伸变形形貌Figure 9. Tensile deformation morphologies of
$ \varphi $ =60% alloy specimen under strain rate of$ \dot{\varepsilon } $ =900 s−1 at$ \theta $ =0°
图 10
$ \theta $ =0°时$ \varphi $ =60%合金试件在$ \dot{\varepsilon } $ =1500 s−1应变率下拉伸断口形貌Figure 10. Tensile fracture morphologies of
$ \varphi $ =60% alloy specimen under strain rate of$ \dot{\varepsilon } $ =1500 s−1 at$ \theta $ =0°
图 11
$ \theta $ =55°时$ \varphi $ =60%合金试件拉伸断口形貌Figure 11. Tensile fracture morphologies of
$ \varphi $ =60% alloy specimen under different strain rates at$ \theta $ =55°
图 12
$ \theta $ =0°时$ \varphi $ =30% &$ t $ =100 h合金试件在$ \dot{\varepsilon } $ =1500 s−1应变率下拉伸断口形貌Figure 12. Tensile fracture morphologies of
$ \varphi $ =30% &$ t $ =100 h alloy specimen under strain rate of$ \dot{\varepsilon } $ =1500 s−1$ \mathrm{a}\mathrm{t} $ $ \theta $ =0°
图 13
$ \theta $ =0°时$ \varphi $ =60% &$ t $ =100 h合金试件在$ \dot{\varepsilon } $ =1500 s−1应变率下的断口形貌Figure 13. SEM fractographies of fracture surface of
$ \varphi $ =60% &$ t $ =100 h alloy specimen under strain rate of$ \dot{\varepsilon } $ =1500 s−1 at$ \theta $ =0°
图 14
$ \theta $ =0°时$ \varphi $ =60% &$ t $ =500 h合金试件在$ \dot{\varepsilon } $ =1500 s−1应变率下的断口形貌Figure 14. SEM fractographies of fracture surface of
$ \varphi $ =60% &$ t $ =500 h alloy specimen under strain rate of$ \dot{\varepsilon } $ =1500 s−1 at$ \theta $ =0°
图 15
$ \theta $ =0°时$ \varphi $ =60% &$ t $ =1000 h合金试件在$ \dot{\varepsilon } $ =1500 s−1应变率下的断口形貌Figure 15. SEM fractographies of fracture surface of
$ \varphi $ =60% &$ t $ =1000 h alloy specimen under strain rate of$ \dot{\varepsilon } $ =1500 s−1 at$ \theta $ =0°
图 16
$ \theta $ =0°时$ \varphi $ =30% &$ t $ =100 h合金试件在$ \dot{\varepsilon } $ =1500 s−1应变率下的断口形貌Figure 16. SEM fractographies of fracture surface of
$ \varphi $ =30% &$ t $ =100 h alloy specimen under strain rate of$ \dot{\varepsilon } $ =1500 s−1 at$ \theta $ =0°
图 18
$ \theta $ =55°时$ \varphi $ =60% &$ t $ =500 h合金试件在$ \dot{\varepsilon } $ =1500 s−1应变率下的断口形貌Figure 18. SEM fractographies of fracture surface of
$ \varphi $ =60% &$ t $ =500 h alloy specimen under strain rate of$ \dot{\varepsilon } $ =1500 s−1 at$ \theta $ =55°
图 19
$ \theta $ =55°时$ \varphi $ =60% &$ t $ =1000 h合金试件在$ \dot{\varepsilon } $ =1500 s−1应变率下的断口形貌Figure 19. SEM fractographies of fracture surface of
$ \varphi $ =60% &$ t $ =1000 h alloy specimen under strain rate of$ \dot{\varepsilon } $ =1500 s−1 at$ \theta $ =55°
图 20
$ \theta $ =55°时$ \varphi $ =60% &$ t $ =1000 h合金试件在$ \dot{\varepsilon } $ =900 s−1应变率下的断口形貌Figure 20. SEM fractographies of fracture surface of
$ \varphi $ =60% &$ t $ =1000 h alloy specimen under strain rate of$ \dot{\varepsilon } $ =900 s−1 at$ \theta $ =55°表 1 镍基单晶高温合金的化学成分
Table 1. Chemical composition of Ni-based single crystal superalloys
φ=30% φ=60% w(C) /% w(Al)/% w(Cr)/% w(Co)/% w(Ta)/% w(W)/% w(C)/% w(Al)/% w(Cr)/% w(Co)/% w(Ta)/% w(W)/% 0.021 4.00 18.63 13.91 3.51 4.04 0.014 6.16 18.58 9.49 5.17 4.00 
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