Yield Evolution Behavior Characterization and Crystal Plasticity Simulation for 5182-O Aluminum Alloy

doi:10.11900/0412.1961.2024.00421

Acta Metall Sin

2025, Vol. 61

Issue (8): 1276-1292 DOI: 10.11900/0412.1961.2024.00421

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Yield Evolution Behavior Characterization and Crystal Plasticity Simulation for 5182-O Aluminum Alloy

SHANG Hongchun¹, TIAN Zhongwang¹^,²(

), NIU Lanjie¹, FAN Chenyang¹, ZHANG Zhewei³, LOU Yanshan⁴(

)

^1.Science and Technology on Electromechanical Dynamic Control Laboratory, Xi'an Institute of Electromechanical Information Technology, Xi'an 710065, China
^2.School of Mechatronical Engineering, Beijing Institute of Technology, Beijing 100081, China
^3.Military Representative Bureau of the Army Equipment Department in Xi'an, Xi'an 710065, China
^4.School of Mechanical Engineering, Xi'an Jiaotong University, Xi'an 710065, China

Cite this article:

SHANG Hongchun, TIAN Zhongwang, NIU Lanjie, FAN Chenyang, ZHANG Zhewei, LOU Yanshan. Yield Evolution Behavior Characterization and Crystal Plasticity Simulation for 5182-O Aluminum Alloy. Acta Metall Sin, 2025, 61(8): 1276-1292.

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Abstract

The development of lightweight materials presents challenges to constitutive modeling and numerical analysis of lightweight components. The hardening of lightweight materials varies more under different stress states than with inherent anisotropy. Although anisotropy is an intrinsic property of rolled sheets, accurate numerical analysis of lightweight components necessitates precise modeling of complex hardening under different loading conditions and anisotropy. This study characterizes the yield evolution of 5182-O aluminum alloy and employs crystal plasticity simulations to understand its plastic deformation characteristics. The mechanical properties of the 5182-O aluminum alloy were examined under different complex stress states through uniaxial tensile, plane-strain tensile, and shear experiments. Initially, the hardening behavior was accurately calibrated using inverse engineering, and plastic deformation characteristics were described analytically using the pDrucker yield equation. The pDrucker yield function was then extended to an analytical anisotropic form using an improved linear transformation tensor. The parameters of the yield function can be analyzed to model differential hardening across various stress states and anisotropic hardening along different loading directions. In addition, the evolution of voids under different stress states and grain orientations was analyzed using crystal plasticity finite element simulations combined with representative volume element (RVE) modeling. Void growth in polycrystalline materials strongly depends on the surrounding microstructure, such as grain morphology and crystallographic orientation. The RVE of single and polycrystalline aggregates containing voids was constructed using a three-dimensional Voronoi mosaic. Crystal plasticity finite element simulations were conducted to perform several simulation experiments with different combinations of grain morphology and crystallographic orientation. Results demonstrated that the anisotropic strength difference of the 5182-O aluminum alloy was < 1%, whereas the maximum strength difference between different stress states was approximately 8%, highlighting the importance of accurately modeling hardening differences due to anisotropy and stress state. The comparison of the calibrated pDrucker yield function with the experimental values under the uncorrelated flow criterion demonstrated relatively high prediction accuracy for different loading directions. The proposed yield function accurately characterized the differential and anisotropic hardening of the 5182-O aluminum alloy under various stress states. Crystal plasticity simulations revealed a strong correlation between stress triaxiality and grain orientation with evolution based on cumulative plastic slip and normalized void volume fraction.

Key words: yield evolution stress state anisotropy crystal plasticity representative volume element

Received: 10 December 2024

ZTFLH:

TG113.25

Fund: National Natural Science Foundation of China(52075423);National Natural Science Foundation of China(U2141214);Independent Research Project of the Key Laboratory of National Defense Science and Technology

Corresponding Authors: TIAN Zhongwang, professor, Tel: 18049027662, E-mail: tianzw129@163.com;

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	SHANG Hongchun
	TIAN Zhongwang
	NIU Lanjie
	FAN Chenyang
	ZHANG Zhewei
	LOU Yanshan

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https://www.ams.org.cn/EN/10.11900/0412.1961.2024.00421 OR https://www.ams.org.cn/EN/Y2025/V61/I8/1276

Fig.1 Schematics of shape and size of the specimens for mechanical tests (unit: mm)
(a) uniaxial tension (UT) specimen
(b) plane strain tension (PST) specimen
(c) shear (SS) specimen

Fig.2 Photo of three-dimensional full-field strain measurement and analysis system based on digital image correlation (DIC) (Insets are contour diagram of strain and equipment photo for taking pictures)

Table 1 Parameters of the DIC analysis system

Fig.3 Strain contours of the specimens under strains of 0.02 (a1-c1), 0.04 (a2-c2), and 0.08 (a3-c3) from DIC testing for UT₀ specimen (a1-a3), SS₀ specimen (b1-b3), and PST₀ specimen (c1-c3)

Fig.4 von Mises equivalent stress-equivalent plastic strain curves under different stress states (0, 45, and 90 represent 0°, 45°, and 90° directions relative to the rolling direction, respectively)

Table 2 Calibration parameters for different hardening behaviors

Fig.5 SEM images showing fracture morphologies of UT₀ (a), PST₀ (b), and SS₀ (c) specimens

Fig.6 Evolutions of pDrucker function parameters of 5182-O aluminum alloys under three stress states
(a) anisotropic hardening parameters (

c 1'

c 2'

, and

c 3'

)
(b) hardening difference parameters (a, b, and c)

Fig.7 Comparisons of 3D yield surfaces and experimental results of 5182-O aluminum alloys under different $λ ¯$ ( $λ ¯$ —equivalent plastic strain calculated by plastic potential, UC—uniaxial compression; EBC—equibiaxial compres-sion, EBT—equibiaxial tension, θ—loading angle)
(a)

λ ¯

= 0.002 (b)

λ ¯

= 0.04

Fig.8 Comparisons of isotropic and anisotropic yield surface evolutions (Blue, red, and black lines and open symbols represent calculated and experimental yield surfaces under 0.02, 0.04, and 0.08 strains, respectively)

Fig.9 Evolutions of anisotropic yield strengths of 5182-O aluminum alloys under uniaxial tension
(a)

λ ¯

= 0.08 (b)

λ ¯

= 0.04 (b)

λ ¯

= 0.002

Fig.10 Evolutions of 3D yield surfaces under three $λ ¯$

Parameter	Unit	Value
C₁₁	MPa	91040
C₁₂	MPa	51084
C₄₄	MPa	25900
h₀	MPa	80.6659
τ_s	MPa	46.3126
τ₀	MPa	33.6519
q		1
$γ ˙ α 0$	s^-1	0.001

Table 3 Material parameters of the plastic constitutive model of the crystal

Fig.11 Inverse pole figure (a) and volume fraction distributions (b) of initial orientation texture for 5182-O aluminum alloy

Fig.12 Finite element mesh model of 1/8 representative volume element (RVE)

Fig.13 Pole figures of textures for 5182-O aluminum alloys
(a) initial orientation (b) 400 grain orientation (c) 500 grain orientation

Fig.14 Cross-section models of the microstructure
(a) single crystals with holes (b) polycrystals with holes

Fig.15 Macroscopic stress states of RVE model ( $B 1 -$ , $B 1 +$ , $B 2 +$ , $B 3 +$ —periodic boundary conditions; Σ₁₁, Σ₂₂, Σ₃₃—diagonal components of the macroscopic Cauchy stress tensors)

Fig.16 Contour maps of cumulative plastic slips of 5182-O aluminum alloy at 0.2 strain under uniaxial tension (a-e) and cross-sectional profile at strains of 0.0-0.2 (f)
(a) Cube texture (b) Goss texture (c) Brass texture (d) Copper texture (e) S texture

Fig.17 Contour maps of cumulative plastic slips of 5182-O aluminum alloy at 0.2 strain under uniaxial compression (a-e) and cross-sectinal profile at strains of 0.0-0.2 (f)
(a) Cube texture (b) Goss texture (c) Brass texture (d) Copper texture (e) S texture

Fig.18 Evolutions of normalized volume fractions (a, b) and principal strains (c, d) with $λ ¯$ for 5182-O aluminum alloys (η—stress triaxiality)
(a, c) uniaxial tensile stress state (η = 1/3) (b, d) uniaxial compressive stress state (η = -1/3)

Fig.19 Contour maps of cumulative plastic slips for 5182-O aluminum alloys with 0.2 strain under different stress states (a-d) and cross-sectional profiles (e-h)
(a, e) plane strain tension (b, f) plane strain compression (c, g) equiaxed double tension (d, h) equiaxed double compression

Fig.20 Evolutions of normalized volume fractions (a) and principal strains (b) with $λ ¯$ for 5182-O aluminum alloys under different stress states (PSC—plane strain compression)

Fig.21 Contour maps of cumulative plastic slips (a, b) and evolutions of normalized volume fractions (c) and principal strains (d) with $λ ¯$ for polycrystal 5182-O aluminum alloys under different strains
(a)

λ ¯

= 0.2 (b)

λ ¯

= 0.4

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