Recrystallization During Thermo-Mechanical Fatigue of Two High-Generation Ni-Based Single Crystal Superalloys
ZHAO Peng1,2, XIE Guang3, DUAN Huichao1, ZHANG Jian3, DU Kui1()
1Shenyang National Laboratory for Materials Science, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China 2School of Materials Science and Engineering, University of Science and Technology of China, Shenyang 110016, China 3Shi -changxu Innovation Center for Advanced Materials, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
Cite this article:
ZHAO Peng, XIE Guang, DUAN Huichao, ZHANG Jian, DU Kui. Recrystallization During Thermo-Mechanical Fatigue of Two High-Generation Ni-Based Single Crystal Superalloys. Acta Metall Sin, 2023, 59(9): 1221-1229.
Ni-based single crystal superalloys are widely used for turbine engine blades because of their excellent high-temperature mechanical properties. Thermo-mechanical fatigue (TMF) is a complex deformation process that combines strain and temperature effects. This process is also considered as a deformation method related to the working conditions of aviation turbine blades. Therefore, understanding the deformation mechanism of materials undergoing TMF is important for extending the service life of aviation turbine blades. Here, third-generation and fourth-generation single crystal superalloys that experienced TMF deformation are investigated by SEM and TEM, including aberration-corrected STEM. The results show the formation of deformation twins on different {111} planes of the single crystal superalloys. In addition, a large number of recrystallized grains are found in parallel twin lamellae or around the intersection of twin lamellae. The grain boundary of recrystallized grains is primarily composed of twin boundaries, low-angle grain boundaries, and large-angle grain boundaries generated by twin intersections. Furthermore, the twinning boundaries after deformation are analyzed using aberration-corrected TEM. Consequently, the process of twinning-induced dynamic recrystallization is comprehensively understood, which improved the TMF fracture mechanism of single crystal high-temperature alloys. These results improve the understanding of the deformation mechanism of single crystal superalloys under service conditions.
Fund: National Natural Science Foundation of China(91960202);National Natural Science Foundation of China(52171020);National Natural Science Foundation of China(51901229);National Natural Science Foundation of China(51911530154);National Natural Science Foundation of China(91860201);National Natural Science Foundation of China(52271042);National Science and Technology Major Project(P2022-C-IV-001-001)
Table 1 Chemical compositions of the studied Ni-based single crystal superalloys
Fig.1 Fractography and deformation bands of sample (The third-generation single crystal superalloy) (a) fracture surface morphology and deformation bands with one type of {111} active plane (The dotted area indicates the sample of SEM and TEM location) (b) back scattered electron (BSE) image of the deformed samples showing twin lamellae (Two different twin planes are shown by twin plane A and twin plane B) (c, d) secondary electron (SE) images showing the microstructure of fracture sample
Fig.2 EBSD analyses of the area including the paralleled twin lamellae (The third-generation single crystal superalloy) (a) Kikuchi contrast map (b) Euler angle map (c) grain boundary map (d) misorientation profile transverse to bands of localized deformation correspond to directions denoted by yellow and black arrows in Fig.2b (e) misorientation angle distribution in the paralleled twin lamellae area
Fig.3 Microstructures of twin lamellae on twin plane A and twin plane B in deformed samples viewed along [10] zone axis (The third-generation single crystal superalloy) (a) bright-field (BF) TEM image and selected area electron diffraction (SAED) pattern (inset) of twin A (b) BF TEM image and SAED pattern (inset) of twin B (c) HAADF-STEM image of twin lamellae (d) aberration-corrected HAADF-STEM image of dislocations at the twin lamellae
Fig.4 Microstructures of ‘subgrain-lite’ and recrystallization grains, and orientation map of ‘subgrain-lite’ (a) BF-STEM image of ‘subgrain-lite’ from the [10] zone axis of paralleled twin lamellae (The third-generation single crystal superalloy) (b, c) BF-TEM images of ‘subgrain-lite’ from the [10] zone axis of twin intersection in different locations (The fourth-generation single crystal superalloy) (d) orientation map of the area in Fig.4c obtained by procession electron diffraction (PED) (e, f) BF-STEM images of recrystallization (RX) grains from the [10] zone axis of paralleled twin lamellae in different locations (The third-generation single crystal superalloy)
Fig.5 BF-STEM image of paralleled twin lamellae for the third-generation single crystal superalloy (a) and HAADF-STEM image of paralleled twin lamellae and schematic illustration (inset) for the fourth-generation single crystal superalloy (b) from the [10] zone axis (TB—twin boundary, LAGB—low angle grain boundary)
Fig.6 SEM image (a) and high magnification SEM-BSE image (b) of fracture surface of the third-generation single crystal alloy (TCP—topologically close-packed)
Fig.7 Diagrams of thermo-mechanical fatigue fracture mechanism (The third & fourth-generation single crystal superalloy) (a) Ni-based superalloy microstructure before deformation (b) after plastic deformation, twins are formed and intersected with each other (c) recrystallization occurs in the twin lamellae, TCP phases are formed at the intersection of twins, and cracks initiate
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