Effect of Deformation Rate on the Elastic-Plastic Deformation Behavior of GH3625 Alloy

doi:10.11900/0412.1961.2020.00508

Acta Metall Sin

2022, Vol. 58

Issue (5): 695-708 DOI: 10.11900/0412.1961.2020.00508

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Effect of Deformation Rate on the Elastic-Plastic Deformation Behavior of GH3625 Alloy

GAO Yubi¹^,²^,³, DING Yutian¹^,²(

), LI Haifeng⁴, DONG Hongbiao⁵(

), ZHANG Ruiyao⁶, LI Jun⁵, LUO Quanshun³

^1.State Key Laboratory of Advanced Processing and Recycling of Non-Ferrous Metals, Lanzhou University of Technology, Lanzhou 730050, China
^2.School of Materials Science and Engineering, Lanzhou University of Technology, Lanzhou 730050, China
^3.Materials and Engineering Research Institute, Sheffield Hallam University, Sheffield S1 1WB, UK
^4.State Key Laboratory of Nonferrous Metals and Processes, General Research Institute for Nonferrous Metals, Beijing 100088, China
^5.Department of Engineering, University of Leicester, Leicester LE1 7RH, UK
^6.Engineering & Innovation, Open University, Milton Keynes MK7 6AA, UK

Cite this article:

GAO Yubi, DING Yutian, LI Haifeng, DONG Hongbiao, ZHANG Ruiyao, LI Jun, LUO Quanshun. Effect of Deformation Rate on the Elastic-Plastic Deformation Behavior of GH3625 Alloy. Acta Metall Sin, 2022, 58(5): 695-708.

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Abstract

GH3625 alloy is a typical polycrystalline material. The mechanical properties of a crystal within the alloy depend on the single crystal properties, lattice orientation, and orientations of neighboring crystals. However, accurate determination of single crystal properties is critical in developing a quantitative understanding of the micromechanical behavior of GH3625. In this study, the effect of deformation rate on the elastoplastic deformation behavior of GH3625 was investigated using in situ neutron diffraction room-temperature compression experiments, EBSD, and TEM. The results showed that the microscopic stress-strain curve included elastic deformation (applied stress σ ≤ 300 MPa), elastoplastic transition (300 MPa < σ ≤ 350 MPa), and plastic deformation (σ > 350 MPa) stages, which agreed with the mesoscopic lattice strain behavior. Meanwhile, the deformation rate was closely related to the crystal elastic and plastic anisotropy. The results of the lattice strain, peak width, and peak intensity reflected by the specific hkl showed that the deformation rate had little effect on the elastic anisotropy of the crystal, but had a significant effect on the plastic anisotropy of the crystal. With the increase in the deformation rate, the high angle grain boundaries gradually changed to the low angle grain boundaries, and the proportion of twin boundaries gradually reduced. Also, the grains transformed from uniform deformation to nonuniform deformation. Moreover, with the increase in deformation rate, the total dislocation density (ρ) of the alloy first decreased and then increased, whereas the geometrically necessary dislocation density (ρ^GND) monotonically increased, and the statistically stored dislocation (SSD) density (ρ^SSD) monotonically decreased. Meanwhile, the abnormal work hardening behavior of the sample at a deformation rate of 0.2 mm/min was mainly related to the SSD generated by uniform deformation. Additionally, the contribution of dislocation strengthening and TEM observation confirmed that the dominant deformation of GH3625 was dislocation slip, and its work hardening mechanism was dislocation strengthening.

Key words: GH3625 alloy deformation rate in situ neutron diffraction lattice strain elastic and plastic anisotropy

Received: 18 December 2020

ZTFLH:

TG146.15

Fund: National Key Research and Development Program of China(2017YFA0700703);National Natural Science Foundation of China(51661019);Program for Major Projects of Science and Technology in Gansu Province(145RTSA004);Hongliu First-Class Discipline Construction Plan of Lanzhou University of Technology, Incubation Program of Excellent Doctoral Dissertation-Lanzhou University of Technology, and Lanzhou University of Technology Excellent Students Studying Abroad Learning Exchange Fund and State Key Laboratory of Cooperation and Exchange Fund

About author: DONG Hongbiao,DONG Hongbiao, professor, Tel: 00441162522528, E-mail: h.dong@le.ac.uk
DING Yutian, professor, Tel: (0931)2976688, E-mail: dingyt@lut.edu.cn

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	Yubi GAO
	Yutian DING
	Haifeng LI
	Hongbiao DONG
	Ruiyao ZHANG
	Jun LI
	Quanshun LUO

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https://www.ams.org.cn/EN/10.11900/0412.1961.2020.00508 OR https://www.ams.org.cn/EN/Y2022/V58/I5/695

Fig.1 Compression stress-strain curves (a, b) and work hardening rate curves (c, d) of GH3625 alloy at different deformation rates (r) (Inset in Fig.1c show the locally enlarged work hardening rate curve of alloy elastic deformation stage at different deformation rates; A, B, and C represent the widths of the alloy elasto-plastic transition stage at different deformation rates in Figs.1b and d, while a, b, and c are the elasto-plastic transition points at different deformation rates; The sawtooth on the curve in Fig.1a represents the stress relaxation phenomenon under displacement-control mode (holding strain))

Fig.2 Evolutions of neutron diffraction patterns of GH3625 alloy during compression deformation at r = 0.2 mm/min (a), r = 0.5 mm/min (b), and r = 1.0 mm/min (c) (d—interplanar spacing)

Table 1 d, diffraction peak intensity (I), and full width at half maximum (FWHM) of GH3625 alloy at different stresses/strains and different (hkl) crystal planes under r = 0.2 mm/min

Table 2 d, I, and FWHM of GH3625 alloy at different stresses/strains and different (hkl) crystal planes under r = 0.5 mm/min

Table 3 d, I, and FWHM of GH3625 alloy at different stresses/strains and different (hkl) crystal planes under r = 1.0 mm/min

Fig.3 Lattice strain as a function of applied stress for GH3625 alloy at different deformation rates and different (hkl) crystal planes
(a) (111) crystal plane (b) (200) crystal plane
(c) (220) crystal plane (d) (311) crystal plane

Table 4 Elastic moduli (E_hkl ) and Young's Modulus anisotropies (r_E ) of GH3625 alloy under different deformation rates

Fig.4 Evolutions of diffraction peak intensity of GH3625 alloy during compression deformation at different deformation rates and different (hkl) crystal planes
(a) (111) crystal plane (b) (200) crystal plane (c) (220) crystal plane (d) (311) crystal plane

Fig.5 Evolutions of diffraction peak width of GH3625 alloy during compression deformation at different deformation rates and different (hkl) crystal planes
(a) (111) crystal plane (b) (200) crystal plane (c) (220) crystal plane (d) (311) crystal plane

Fig.6 Evolutions of microstructure and strain distribution characteristics in GH3625 alloy under different states (TD—transverse direction, LD—longitudinal direction, TBs—twin boundaries; gray lines show the low angle grain boundaries (LAGBs), black lines show the high angle grain boundaries (HAGBs); Insets show the kernel average misorientation (KAM) images of rectangle regions)
(a) solution state (b) r = 0.2 mm/min (c) r = 0.5 mm/min (d) r = 1.0 mm/min

Fig.7 Evolutions of misorientation angle distribution of GH3625 alloy under different states (f_LAGB—fraction of LAGB, f_HAGB—fraction of HAGB, f_TB—fraction of TB)
(a) solution state (b) r = 0.2 mm/min (c) r = 0.5 mm/min (d) r = 1.0 mm/min

Fig.8 TEM images showing the microstructures of GH3625 alloy after compression deformation at r = 0.5 mm/min
(a) dislocation network(b) dislocation tangle(c) grain (Inset in Fig.8c shows the SAED pattern of deformation band )

Fig.9 Geometrically necessary dislocation density (ρ^GND) distribution (a) and average ρ^GND (b) of GH3625 alloy under different states

Fig.10 Variations of total dislocation density (ρ)with strain for GH3625 alloy at different defor-mation rates (a) and contribution of dislocation strengthening (b)

Table 5 ρ, ρ^GND, and statistically stored dislocation density (ρ^SSD) of GH3625 alloy after compression deformation under different rates

Fig.11 Orientation distribution function (ODF) sections of GH3625 alloy under different states (Φ, φ₁, and φ₂—Euler angles)
(a) solution state (b) r = 0.2 mm/min (c) r = 0.5 mm/min (d) r = 1.0 mm/min

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