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Chinese Journal of Materials Research  2023, Vol. 37 Issue (10): 721-730    DOI: 10.11901/1005.3093.2022.524
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Microstructural Stability and Stress Rupture Property of a 6Re/3Ru Containing Nickel-based Single Crystal Superalloy
CHEN Ruizhi1, LIU Lirong1(), GUO Shengdong1, ZHANG Mai2, LU Guangxian2, LI Yuan2, ZHAO Yunsong2, ZHANG Jian2
1.School of Material Science and Engineering, Shenyang University of Technology, Shenyang 110870, China
2.Science and Technology on Advanced High Temperature Structural Material Laboratory, AECC Beijing Institute of Aeronautical Materials, Beijing 100095, China
Cite this article: 

CHEN Ruizhi, LIU Lirong, GUO Shengdong, ZHANG Mai, LU Guangxian, LI Yuan, ZHAO Yunsong, ZHANG Jian. Microstructural Stability and Stress Rupture Property of a 6Re/3Ru Containing Nickel-based Single Crystal Superalloy. Chinese Journal of Materials Research, 2023, 37(10): 721-730.

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Abstract  

The microstructural evolution during long-term aging at 1000℃ and 1130℃ and the stress rupture property at 1100℃/140 MPa of a fourth-generation nickel-based single crystal superalloy with 6Re/3Ru were investigated. The microstructure and dislocation configuration of the alloy were observed by field emission scanning electron microscopy (FE-SEM) and transmission electron microscopy (TEM) in terms of its microstructural stability and stress rupture property. The results showed that the alloy displayed excellent microstructural stability. During long-term aging at 1000℃, γ′ phase grew up gradually, but γ′ phase still remained high cubic degree, however, the TCP phases did not precipitate after aging for 1000 h. After aging at 1130℃ for 500 h, the γ′ phase connected each other and became rafting ed. The TCP phase started to precipitate after long-term aging at 1130℃ for 200 h, however, the content of TCP phase was only 0.04% after aging for 1000 h in the alloy. After aging at 1130℃ for 500 h, dislocation networks formed at γ/γ′ interfaces which became more regular and denser with the increase of aging time. The stress rupture life of the alloy at 1100℃/140 MPa was 676.5 h, which reached the level of the fourth-generation nickel-based single crystal superalloy. The γ′ phase underwent N-type rafting, the needle-like TCP phase (μ phase) precipitated, and dislocation pile-up was found near TCP phase after fracture. During stress rupture test, the formation of γ/γ′ interfacial dislocation networks and a<010> super-dislocations in the alloy was beneficial to the stress rupture property.

Key words:  metallic materials      4th generation nickel-based single crystal superalloy      long-term aging      stress rupture property      interfacial dislocation networks      TCP phase     
Received:  29 September 2022     
ZTFLH:  TG132.3  
Fund: National Natural Science Foundation of China(52001297);Natural Science Foundation of Liaoning Province(2020-MS-212)
Corresponding Authors:  LIU Lirong, Tel: 18642002619, E-mail: lrliu@sut.edu.cn

URL: 

https://www.cjmr.org/EN/10.11901/1005.3093.2022.524     OR     https://www.cjmr.org/EN/Y2023/V37/I10/721

Fig. 1  Schematic diagram of stress rupture specimen (a) and observed regions of fractured specimens (b)
Fig.2  SEM morphology (a), TEM morphology and selectron diffraction (b) of the alloy after fully heat treatment
Fig.3  Microstructure of γ′ phase after long-term aging at 1000℃ (a~e) and 1130℃ (f~j) for different time
Fig.4  Average size (a)、volume fraction (b) and coarsening rate(c) of γ' phase after long-term aging at 1000℃ and 1130℃ for different time
Fig.5  Precipitation of TCP phase after long-term aging at 1000℃ and 1130℃ for different times (a) 1000℃/1000 h; (b) 1130℃/200 h; (c) 1130℃/500 h; (d) 1130℃/1000 h
Time / hReWCoTaHfCrMoRuNi
20037.5917.8911.679.123.592.680.980.64Bal.
50037.8718.1611.719.043.682.631.080.76Bal.
100039.2519.6611.758.334.632.620.670.13Bal.
Table 1  Compositions of TCP phase after long-term aging at 1130℃ for different time by SEM-EDS (mass fraction,%)
Fig.6  Dislocation networks at γ/γ′ interface (a)~(c) and statistics of dislocation spacing (d)~(f) after long-term aging at 1130℃ for different times (a) 200 h; (b) 500 h; (c) 1000 h
Fig.7  γ/γ′ morphology (a~c) and TCP phase (d~f) of different regions in fractured specimens (a) (d) region A; (b) (e) region B; (c) (f) region C
Fig.8  Morphology of TCP phase in fractured specimens (a) and selected area electron diffraction pattern (b)
ReWNiCoTaHfCrMoRu
38.8519.2613.5311.288.864.512.710.680.32
Table 2  Composition of μ phase in fractured specimen measured by SEM-EDS (mass fraction,%)
Fig.9  Dislocation configuration of the alloy after fracture at 1100℃/140 MPa
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