Effect of Tension-Torsion Coupled Loading on the Mechanical Properties and Deformation Mechanism of GH4169 Superalloys

doi:10.11900/0412.1961.2022.00142

Acta Metall Sin

2024, Vol. 60

Issue (1): 30-42 DOI: 10.11900/0412.1961.2022.00142

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Effect of Tension-Torsion Coupled Loading on the Mechanical Properties and Deformation Mechanism of GH4169 Superalloys

YANG Junjie, ZHANG Changsheng(

), LI Hongjia, XIE Lei, WANG Hong, SUN Guang'ai

Key Laboratory for Neutron Physics, Institute of Nuclear Physics and Chemistry, Chinese Academy of Engineering Physics, Mianyang 621999, China

Cite this article:

YANG Junjie, ZHANG Changsheng, LI Hongjia, XIE Lei, WANG Hong, SUN Guang'ai. Effect of Tension-Torsion Coupled Loading on the Mechanical Properties and Deformation Mechanism of GH4169 Superalloys. Acta Metall Sin, 2024, 60(1): 30-42.

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Abstract

GH4169 superalloys are used in gas turbine engines and power plants owing to their excellent mechanical properties and corrosion resistance at temperatures exceeding 600^oC. Because of their service condition, involving high temperature and complex stress, much attention has been attracted to the effect of temperature and loading mode on the mechanical properties and deformation mechanism. The effect of the loading mode, especially the multiaxial or coupled loading, on the mechanism of plastic deformation is still an outstanding open question despite numerous investigations on the effect of temperature on mechanical properties. In this study, the effect of tension-torsion coupled loading on deformation behavior was investigated, where the microstructures and underlying mechanism were revealed using SEM, TEM, EBSD, and neutron diffraction. It is found that the mechanical properties are dependent on the tension-torsion loading. For the tension specimens, the yield and ultimate strengths increase with the pretorsion angle; for instance, at the pretorsion angle of 720°, the increase rate is approximately 150% and 13%, respectively. At the pretension strain of 20%, the yield strength and elongation increase by approximately 31% and 16%, respectively. The density of dislocations increases in those samples after tensile and torsional deformations compared to the undeformed samples. Moreover, the density of dislocations for specimens deformed under the coupled loading is lower than those deformed under axial loading, indicating the dislocation annihilation effect. The yield strength is enhanced due to the strengthening effect of the initial dislocations produced during the preloading. The ultimate strength for the torsional specimens after pretension decreases because of the dislocation annihilation effect during the subsequent coupled loading. However, for the tensile specimens after pretorsion, such dislocation annihilation effect can be counteracted to some extent by the strengthening effect of the formed gradient structure by pretorsion on mechanical strength. These findings provide some insight into the regulation of the microdeformation mechanism process of materials through designing the coupled or multiaxial loading modes and the coordinated improvement of strength and toughness based on the achievement of gradient or hierarchical microstructure.

Key words: polycrystalline nickel-based superalloy coupled loading mechanical property deformation mechanism neutron diffraction

Received: 27 March 2022

ZTFLH:

TG132.32

Fund: National Science and Technology Major Project(2019-VII-0019-0161);National Natural Science Foundation of China(U1930121)

Corresponding Authors: ZHANG Changsheng, associate professor, Tel: (0816)2495141, E-mail: johmzhangc@caep.cn

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	YANG Junjie
	ZHANG Changsheng
	LI Hongjia
	XIE Lei
	WANG Hong
	SUN Guang'ai

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https://www.ams.org.cn/EN/10.11900/0412.1961.2022.00142 OR https://www.ams.org.cn/EN/Y2024/V60/I1/30

Fig.1 Schematic of the samples for mechanical property measurements (unit: mm)

Fig.2 Equivalent stress-strain curves (a, c) and mechanical properties (b, d) for PRTOR (a, b) and PRTEN (c, d) specimens (PRTOR and PRTEN are the shortened name for pre-torsion and pre-tension, respectively)

Fig.3 Strain hardening rate curves of PRTOR (a) and PRTEN (b) specimens (Insets show the corres-ponding enlargement for the range of relatively low strains as marked by the squares)

Fig.4 Photographs of PRTOR (a) and PRTEN (b) specimens after fracture (Insets show the measured angle ψ between the fracture plane and transverse cross section)

Fig.5 Low magnification SEM images (a, d, g, j) for specimens after fracture, and the corresponding high magnification images for the center (b, e, h, k) and edge (c, f, i, l) areas that are marked by open squares in low magnification images for PRTOR-0 (a-c), PRTOR-360 (d-f), PRTEN-0 (g-i), and PRTEN-20 (j-l) specimens

Fig.6 Schematic of the fracture of specimens under tension-torsion loading (a) and the force analysis at one point in the lateral surface (σ and τ represent the tensile and shear stresses on the fracture plane, respectively; σ_y and σ_z denote the normal stresses perpendicular to XZ and XY planes, respectively; τ_zy and τ_yz represent the shear stresses within XY and XZ planes, respectively) (b)

Fig.7 Neutron diffraction patterns (a) as well as the partial enlargement of square area in Fig.7a (b) for the undeformed specimen and those deformed PRTOR and PRTEN specimens under different loading modes

Table 1 Lattice parameters and dislocation densities for the undeformed specimen and those deformed PRTOR and PRTEN specimens under different loading modes

Fig.8 Linear fitting curves of (ΔK)² and K²C for undeformed (a), PRTOR-0 (b), PRTOR-360 (c), PRTEN-0 (d), and PRTEN-20 (e) specimens (K, ΔK, and C denote the length of reciprocal lattice vector, peak broadening, and average contrast factor, respectively)

Fig.9 Development of the reflection (200) during torsion process at the pre-tension loading

Fig.10 TEM images for PRTOR-0 (a) and PRTOR-360 (b) specimens

Fig.11 Grain boundary maps (a, b) and misorientation distribution profiles (c, d) of center (a, c) and edge (b, d) areas for PRTOR-360 specimens (Insets in Figs.11a and b show schematically the positions of sampling point or testing area. The red and black lines represent the low angle (< 15°) grain boundaries (LAGBs) and high angle (> 15°) grain boundaries (HAGBs), respectively)

Fig.12 Schmid factor maps of center (a) and edge (b) areas for PRTOR-360 specimen

Fig.13 Schematics of microscopic deformation mecha-nism under pre-torsion (φ—torsion angle) (a) and pre-tension (ε—strain) (b) modes

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