Damage Evolution and Fracture Behavior of Three-directional Orthogonal Fiber Reinforced Aluminum Matrix Composites under Longitudinal Tensile Loading

doi:10.11901/1005.3093.2020.448

Chinese Journal of Materials Research

2022, Vol. 36

Issue (7): 500-510 DOI: 10.11901/1005.3093.2020.448

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Damage Evolution and Fracture Behavior of Three-directional Orthogonal Fiber Reinforced Aluminum Matrix Composites under Longitudinal Tensile Loading

LIU Fenghua¹, ZHAO Wenhao¹, CAI Changchun¹, WANG Zhenjun¹(

), SHEN Gaofeng¹, ZHANG Yingfeng¹^,², XU Zhifeng¹, YU Huan¹

^1.School of Aeronautical Manufacturing Engineering, Nanchang Hangkong University, Nanchang 330063, China
^2.School of Mechanical Engineering, Northwestern Polytechnical University, Xi'an 710072, China

Cite this article:

LIU Fenghua, ZHAO Wenhao, CAI Changchun, WANG Zhenjun, SHEN Gaofeng, ZHANG Yingfeng, XU Zhifeng, YU Huan. Damage Evolution and Fracture Behavior of Three-directional Orthogonal Fiber Reinforced Aluminum Matrix Composites under Longitudinal Tensile Loading. Chinese Journal of Materials Research, 2022, 36(7): 500-510.

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Abstract

A novel 3D orthogonal weaving carbon fibre reinforced Al-matrix composite was prepared by vacuum-pressure infiltration method. A finite element based micromechanical model by considering the interfacial action was developed according to the characteristics of cross-section morphology and weaving structure of yarns in the composite, and then the progressive damage and fracture behavior of the composites subjected to longitudinal tensile loading were assessed via experiment and numerical simulation. The results shown that the acquired tensile modulus, ultimate strength and fracture strain is 120.7 GPa, 771.75 MPa and 0.83%, respectively. The computationally predicted stress-strain curve agrees well with the experimental ones, and the calculation error of the above properties is -3.21%, 1.75% and -9.63%, respectively. At the initial tensile stage local interface failure was observed between the matrix alloy and Z directional yarns. With the increase of tensile strain, the matrix damage zone in the interspace of yarns accumulate gradually and lead to the transverse cracking of Z directional yarns and weft yarns successively. At the final tensile stage, the warp yarns and matrix alloy failed concurrently, and hence the composite lost its bearing capacity. Warp yarns fracture and transverse cracking of weft and Z directional yarns were observed on the tensile fracture morphology. The axial fracture of warp yarns, which play predominant role in load bearing, is flat and with limited fiber pull-out morphology. As a result, the composites exhibit quasi-brittle fracture behavior during the longitudinal tensile process.

Key words: composite mechanical property micromechanics progressive damage

Received: 25 October 2020

ZTFLH:

TB331

Fund: National Natural Science Foundation of China(52162018);National Natural Science Foundation of China(51765045);Aeronautical Science Foundation of China(2019ZF056013);Jiangxi Provincial Natural Science Foundation(20202ACBL204010);National Defense Basic Research Program(JCKY2018401C004)

About author: WANG Zhenjun, Tel: 18970951974, E-mail: wangzhj@nchu.edu.cn

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	Fenghua LIU
	Wenhao ZHAO
	Changchun CAI
	Zhenjun WANG
	Gaofeng SHEN
	Yingfeng ZHANG
	Zhifeng XU
	Huan YU

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https://www.cjmr.org/EN/10.11901/1005.3093.2020.448 OR https://www.cjmr.org/EN/Y2022/V36/I7/500

Table 1 performance parameters of graphite fiber M40J

Table 2 Chemical composition of the aluminum alloy ZL301 (mass fraction, %)

Table 3 Architecture parameters of the 3D orthogonal woven fabric

Fig.1 3D orthogonal woven fabric and 3DOW-CF/Al composites (a) fabric appearance, (b) fabric architecture, (c) 3DOW-CF/Al composite

Fig.2 Schematic diagram of the vacuum-assisted pressure infiltration apparatus

Fig.3 Tensile specimen of the 3DOW-CF/Al composites (a) specimen size (mm), (b) specimen appearance

Fig.4 Architecture and cross-section of yarns in the 3DOW-CF/Al composites (a) warp yarn direction, (b) weft yarn direction, (c) Z yarn direction, (d) microstructure of yarns

Fig.5 Mesoscale structure model of the 3DOW-CF/Al composites

Fig.6 Mesoscale structure unit cell model of the 3DOW-CF/Al composites (a) with matrix alloy, (b) without matrix alloy

Fig.7 Schematic of the improved PBCs

/MPa

E m

ν m

$σ y m$

/MPa

$E H m$

/MPa

$σ u m$

/MPa

$ε 0 p l$

$ε f p l$

81700

0.33

79.0

24900

130.0

0.16

0.80

Table 4 Elastic and plastic properties of the matrix alloy

$E 11 f$ /GPa	$E 22 f$ /GPa	$υ 12 f$	$υ 23 f$	$G 12 f$ /GPa	$G 23 f$ /GPa	$X t f$ /MPa	$X c f$ /MPa
377	19	0.26	0.3	8.9	7.3	1760	900

Table 5 Elastic constants and strength parameters of the fiber

$E 11$ /MPa	$E 22$ /MPa	$G 12$ /MPa	$G 23$ /MPa	$ν 12$	$ν 23$
285460	21840	10120	8380	0.28	0.59
$X t$ /MPa	$X c$ /MPa	$Y t$ /MPa	$Y c$ /MPa	$S 12$ /MPa	$S 23$ /MPa
1240	750	34	112	100	16

Table 6 Elastic constants and strength parameters of the yarn

$t n 0$ /MPa	$t s 0$ /MPa	$t t 0$ /MPa	$Δ ¯ 0$ /10^-6m	$Δ ¯ f$ /10^-6m
16.0	9.5	9.5	0.08	0.72

Table 7 Interfacial property parameters used in the micro-scale and mesoscale model

Fig.8 Traction-separation displacement rule of cohesion model

Fig.9 Experimental and predicted tensile stress-strain curves of the 3DOW-CF/Al composites under warp directional tension

Table 8 Experimental and computational results of the mechanical properties of 3DOW-CF/Al composites

Fig.10 Damage progression and failure process of the 3DOW-CF/Al composites: (a) local interface failure, (b) initial matrix damage, (c) local failure of Z yarns, (d) failure of weft and Z yarns, (e) initial failure of warp yarns, (f) local failure of matrix, (g) fracture status of yarns

Fig.11 Fracture morphology of the 3DAW-CF/Al composites at warp directional tension condition (a) fracture morphology of the yarns, (b) fracture morphology inside the warp yarn

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