间隙C掺杂CoCrNi基中熵合金的应变率效应和温度效应

王强; 王建军; 赵聃; 王志华

doi:10.11883/bzycj-2025-0087

间隙C掺杂CoCrNi基中熵合金的应变率效应和温度效应

doi: 10.11883/bzycj-2025-0087

王强^1,,
王建军^{2, 3},
赵聃^{2, 3},
王志华^{2, 3}

1.
山西省检验检测中心（山西省标准计量技术研究院）计量科学研究所，山西太原 030000
2.
太原理工大学航空航天学院，山西太原 030024
3.
太原理工大学材料强度与结构冲击山西省重点实验室，山西太原 030024

基金项目: 中国检验检测学会2025年科研项目（KY202502）

详细信息

作者简介:
王　强（1995－　），男，博士，工程师，wqiang2013@163.com

中图分类号: O347
计量
- 文章访问数: 208
- HTML全文浏览量: 38
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- 被引次数: 0
出版历程
- 收稿日期: 2025-03-19
- 修回日期: 2025-08-18
- 网络出版日期: 2025-08-19

Strain rate effect and temperature effect of CoCrNi-based medium entropy alloy with interstitial C doping

WANG Qiang^1
,,
WANG Jianjun^{2, 3},
ZHAO Dan^{2, 3},
WANG Zhihua^{2, 3}

1.
Shanxi Institute of Metrology, Shanxi Inspection and Testing Center, Taiyuan 030000, Shanxi, China
2.
College of Aeronautics and Astronautics, Taiyuan University of Technology, Taiyuan 030024, Shanxi, China
3.
Shanxi Key Laboratory of Material Strength and Structural Impact, Taiyuan University of Technology, Taiyuan 030024, Shanxi, China

摘要

摘要: 为了进一步探索间隙C原子对CoCrNi基中熵合金的应变率效应和温度效应的影响，系统地研究了由面心立方（face-centered cubic，FCC）基体和三级层级沉淀微观结构组成的CoCrNiSi_0.3C_0.048中熵合金在宽温域、宽应变率范围内的压缩力学行为、微结构演化过程以及变形机理。结果表明，该合金在400 ℃下变形时，其真应力-真应变曲线呈现出明显的“锯齿流变”现象，而且随着应变的增大，锯齿的振幅逐渐减小，直至消失。此外，其准静态下流动应力随温度的变化曲线上出现了反常应力峰（第三型应变时效现象），在高应变率下，第三型应变时效引起的反常应力峰消失。通过微观结构的表征分析，推测其准静态下出现第三型应变时效现象主要是由于间隙C原子的存在，在塑性变形的不断进行和发展过程中，产生了一系列由致密位错胞、微带、层错、位错簇和变形孪晶等组成的类似于非均质结构的混合结构。这些混合结构加剧了间隙原子与移动位错之间的相互作用，进而钉扎位错，出现动态应变时效现象。在动态情况下并未出现第三型应变时效的原因可能是溶质原子的运动相较于位错的运动速度较慢，无法及时钉扎位错。另外，大量的纳米级SiC沉淀的析出弱化了动态加载下间隙原子的“钉扎”作用。
- 应变率效应 /
- 温度效应 /
- 应变时效现象 /
- 中熵合金 /
- 间隙C掺杂
Abstract: To further explore the influence of interstitial C atom on the strain rate effect and temperature effect of CoCrNi-based medium-entropy alloy, the compression mechanical behavior, microstructure evolution and deformation mechanism of CoCrNiSi_0.3C_0.048 medium-entropy alloy were systematically studied at a wide temperature and strain rate range. The investigated alloy is composed of face-centered cubic (FCC) matrix and three-level precipitate microstructure, i.e. the primary Cr₂₃C₆ carbides (2−10 μm), the secondary SiC precipitates (200−500 nm), and the tertiary SiC precipitates (～50 nm). The results show that the serrated flow phenomenon is observed on the true stress-strain curve of the alloy at 400 ℃, and the amplitude of the serrations decreases gradually with the increase of strain and ultimately vanishes. In addition, the abnormal stress peak (the 3rd-type strain aging phenomenon) appears on the curve of the quasi-static flow stress with temperature, but at high strain rate, the abnormal stress peak disappears. Through the analysis of the characterization of the deformed microstructure, it is speculated that the main reason for the phenomenon of 3rd-type strain aging under quasi-static conditions may be the existence of interstitial C atoms. During the process of continuous plastic deformation and development, a series of mixed structures similar to heterogeneous structures are generated, which are composed of dense dislocation cells, micro bands, stack faults, dislocation clusters and deformation twins. These mixed structures intensify the interaction between interstitial atoms and moving dislocation, and then pin the dislocation, which results in dynamic strain aging phenomenon occurs. The reason why the 3rd-type strain aging does not appear under dynamic conditions may be that the solute atoms move slower than the dislocation. The dislocation cannot be pinned in time. In addition, the precipitation of a large number of nanoscale SiC precipitates weakens the "pinning" effect of interstitial atoms under dynamic loading.
- strain rate effect /
- temperature effect /
- dynamic strain aging /
- medium-entropy alloy /
- interstitial element C doping

HTML全文

图 1 压缩试样几何尺寸、加载变形过程及变形后试样的微观观测区域示意图

Figure 1. Schematic diagram of the geometric dimensions of the specimens, the loading deformation process, and the microscopic observation area of the deformed specimen.

下载: 全尺寸图片幻灯片

图 2 准静态0.001 s⁻¹应变率下C48-800-1h MEA的真应力-真应变曲线随温度的变化

Figure 2. The true stress - strain curves of C48-800-1h MEA under different temperatures at a quasi-static strain rate of 0.001 s⁻¹

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图 3 不同动态应变率下C48-800-1h MEA的真应力-真应变曲线随温度的变化

Figure 3. True stress - strain curves of C48-800-1h MEA under different temperatures at different dynamical strain rates

下载: 全尺寸图片幻灯片

图 4 C48-800-1h合金在不同应变率下的流动应力随温度的变化

Figure 4. Flow stress variation of C48-800-1h MEA at different strain rates with temperature

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图 5 DH36钢在$ \varepsilon $=0.10时真应力随温度变化曲线上出现的反常应力峰^[31]

Figure 5. Anomalous stress peaks in the true stress- temperature curve of DH36 steel at $ \varepsilon $=0.10^[31]

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图 6 $ \varepsilon $=0.10下，应变率对C48-800-1h MEA的流变应力-温度曲线的影响

Figure 6. Strain rate effect on flow stress-temperature curves of C48-800-1h MEA at $ \varepsilon $=0.10

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图 7 金属材料在热变形过程典型的应力-应变曲线^[45]

Figure 7. Typical stress-strain curves of metal materials during thermal deformation^[45]

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图 8 不同应变率下，随着温度的升高，C48-800-1h MEA的微观结构演化

Figure 8. Microstructure evolution of C48-800-1h MEA with increasing temperature at strain rates of 0.001, 1000 and 4000 s⁻¹

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图 9 扩散的溶质原子对运动位错的钉扎引起第三型应变时效的示意图^[36]

Figure 9. Schematic diagram of the third-type strain aging induced by the pining effect of moving dislocation by diffused solute atoms^[36]

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图 10 C48-800-1h合金准静态（0.001 s⁻¹）和动态（4000 s⁻¹）下，400 ℃变形后的微观结构

Figure 10. Microstructures of the deformed C48-800-1h alloy at 400 ℃ under quasi-static (0.001s⁻¹) and dynamic (4000 s⁻¹) conditions

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