Dynamic deformation behavior and constitutive model of multi-component alloys at high temperature
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摘要: 为加速多主元合金在航空工业领域的应用，将航空发动机经常面临的高温高应变率耦合环境作为实验条件，在5种温度下开展了CoCrFeNiMn多主元合金的动态压缩实验和变形后试样的塑性变形机理微观表征。结果表明：在1273 K的高温环境中，多主元合金的动态屈服强度可达200 MPa，表现出较好的耐高温性能；随着动态塑性应变的增加，材料内部出现了晶粒粗化的现象，并且在晶界处具有更高的亚结构孕育能力。此外，量化了不同环境温度下动态塑性变形过程中绝热温升的变化规律，指出了现有动态本构关系对CoCrFeNiMn多主元合金在宽温度域内动态应力-应变关系预测能力的不足。最后，通过解耦分析初始屈服与塑性流动阶段的温度效应，建立了一个指数形式的唯象动态本构方程。该本构方程可用于预测冲击载荷作用下宽温度域内多主元合金的屈服强度和塑性流动规律。Abstract: Compared to traditional alloys, the new multi-component alloy exhibits an excellent "cocktail effect". This effect allows for the collaborative control of structure and performance, making it highly suitable for application in the demanding service environment of the aviation industry. To expedite the adoption of multi-principal component alloys in the aviation industry, experimental conditions simulating high temperature and high strain rate coupling environments encountered by aero engines are employed. Using the CoCrFeNiMn multi-principal element alloy as the research object, dynamic impact tests were conducted at different temperatures (298, 673, 873, 1073, 1273 K) by using a split Hopkinson pressure bar with an impact velocity of 20 m/s. Dynamic stress-strain curves at five temperatures were obtained, and the results indicate that the stress-strain curve at 1273 K has higher strain hardening ability compared to 873 K and 1073 K. When the temperature increases to 1273 K, the material's yield strength can still reach 200 MPa, demonstrating good high-temperature performance. The grain size, dislocation density, and microstructure types of the samples before and after deformation were discussed by electron backscatter diffraction tests. The experiment result reveals that an increase in dynamic plastic strain at 1273 K leads to grain coarsening phenomenon, with higher substructure breeding ability observed at the grain boundary. In addition, the change in adiabatic temperature rise and ambient temperature during dynamic plastic deformation is quantified. It is also highlighted that the current dynamic constitutive relationship is inadequate in predicting the dynamic stress-strain relationship of the CoCrFeNiMn multi-principal component alloy across a wide temperature range. Finally, an exponentially phenomenological dynamic constitutive equation is established by decoupling the temperature effect between the initial yield and the plastic flow stage. This constitutive equation allows for the accurate prediction of the yield strength and plastic flow behavior of multi-component alloys under impact loads across a wide temperature range.
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图 1 CoCrFeNiMn多主元合金的XRD谱
Figure 1. XRD pattern of the CoCrFeNiMn multi-principal component alloy
图 2 CoCrFeNiMn多主元合金的EBSD测量结果
Figure 2. EBSD measurement results of CoCrFeNiMn multicomponent alloy
图 3 高温动态实验加载装置与试样形貌
Figure 3. High temperature dynamic experimental loading device and morphologies of samples
图 4 不同温度下CoCrFeNiMn多主元合金的动态应力-应变曲线
Figure 4. Dynamic stress-strain curves of CoCrFeNiMn multi-principal component alloys at different temperatures
图 5 不同温度下CoCrFeNiMn多主元合金的微观结构演变
Figure 5. Microstructure evolution of CoCrFeNiMn multi-component alloys at different temperatures
图 6 不同温度下CoCrFeNiMn多主元合金变形后的局部平均取向差和晶界角
Figure 6. The KAM and grain boundary misorientation of CoCrFeNiMn multi-component alloys after deformation at different temperatures
图 7 不同温度下塑性应变与绝热温升之间的关系
Figure 7. Relationship between plastic strain and adiabatic temperature rise at different temperatures
图 8 不同温度下塑性应变与温度敏感指数之间的关系
Figure 8. Relationship between plastic strain and temperature sensitivity index at different temperatures
图 9 动态加载下初始屈服应力与变形温度的关系
Figure 9. Relationship between initial yield stress and deformation temperature under dynamic loading
图 10 材料参数A与变形温度的关系
Figure 10. Relationship between material parameter A and deformation temperature
图 11 不同温度下动态应力-应变曲线实验结果与理论结果的对比
Figure 11. Comparison between predicted and experimental dynamic stress-strain curves at different temperatures
表 1 模型参数
Table 1. Parameters of proposed model
$ {\sigma _{\text{t}}} $/MPa $ \beta $/K−1 a/MPa $ {\beta _{\text{1}}} $/K−1 b/MPa n $ {\sigma _{{\text{at}}}} $/MPa 733.16 1.23×10−3 226.01 1.36×10−3 204.90 0.69 115.42 
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