非晶合金失效行为与准则

doi:10.1007/s10409-022-09022-j

Failure behavior and criteria of metallic glasses

doi: 10.1007/s10409-022-09022-j

Chen Yan^{1,, 2},
Dai Lanhong^{1,, 2,*
,}

1.
State Key Laboratory of Nonlinear Mechanics, Institute of Mechanics, Chinese Academy of Sciences, Beijing 100190, China;
2.
School of Engineering Science, University of Chinese Academy of Sciences, Beijing 101408, China

Funds:

the National Natural Science Foundation of China Grant

the National Key Research and Development Program of China Grant

the Strategic Priority Research Program Grant

the Key Research Program of Frontier Sciences Grant

and the Science Challenge Project Grant

More Information

Corresponding author: Corresponding author. E-mail address: lhdai@lnm.imech.ac.cn (Lanhong Dai)

摘要

摘要: 非晶合金具有优异的力学性能, 是一类新兴的先进结构材料. 然而, 该材料常温下表现的脆性断裂与复杂断裂行为极大地限制了其工程应用. 在过去的几十年, 国内外学者针对非晶合金的延性或脆性变形与断裂, 其中涉及材料成分、加载条件、样品尺寸等, 开展了广泛研究, 并在非晶合金失效行为认识上取得了重要进展. 剪切带、孔洞化和裂纹尖端场本质等微观断裂机制被一一揭示. 延脆转变行为与其内在的控制参数被发现. 为了有效描述和预测非晶合金的失效行为, 研究者们分别基于经验或从原子间相互作用出发, 建立了延性和脆性非晶合金的失效准则. 在本文中, 我们对以上进展进行了回顾和评述, 并提出了非晶合金失效有待进一步研究和厘清的重要问题.
Abstract: Metallic glasses (MGs) constitute an emerging class of advanced structural materials due to their excellent mechanical properties. However, brittle failure at room temperature and the resultant complicated fracture behavior greatly limit their wide engineering applications. Over the past decades, the deformation and fracture in ductile or brittle mode referring to material compositions, load conditions, sample size, etc., have been widely studied, and significant progress has been made in understanding the failure behavior of MGs. Micromechanisms of fracture have been revealed involving shear banding, cavitation and the nature of the crack tip field. The ductile-to-brittle transition and inherent governing parameters have been found. To well describe and predict the failure behavior of MGs, failure criteria for ductile and brittle MGs have been established empirically or based on atomic interactions. In this paper, we provide a detailed review of the above advances and identify outstanding issues in the failure of MGs that need to be further clarified.
- Metallic glasses /
- Failure behavior /
- Shear band /
- Cavitation /
- Failure criteria

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1. Illustration of the two-unit mechanism for STZ percolation: a at small loads, the STZ near the notch experiences a small distortion, which has a negligible effect on the neighboring matrix, b the STZ is activated at a higher load, and collective vortex-like motion is caused, and c the following STZ is activated once the stress exceeds the threshold value [127].

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2. Evolution of local von Mises strain and L5FS with macroscopic shear strain. Deformation patterns at a γ = 0.05 (before yielding) and at b γ = 0.15 (right before the emergence of the shear band), respectively. Strain gradient fields in the z direction immediately c before and d after shear band formation, respectively [128].

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3. Plastic strain to fracture varies with sample thickness for ∆u = 10 μm (red solid line) and ∆u = 50 μm (blue solid line). The analytical prediction is consistent with experimental data [146] for Vit-1 and other similar compositions [29].

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4. Energy dissipation map for shear band nucleation and growth as a function of sample thickness [29].

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5. MGs experience necking behavior during the in situ TEM tensile tests. Necking starts early from the “notches” on the surfaces in the virgin sample (indicated by the white arrow in a) and then b-d develops gradually to e final failure [27].

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6. Schematic of two fundamental atomic motions in MGs: a a classical STZ and b an envisioned TTZ [15].

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7. Numerical results of crack propagation at various applied strains in a-c Fep glass and d-f CuZr glass. The color indicates the local von Mises strain [33].

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8. Experimental observation of the cavitation-dominated fracture process in the Fe-based MG. The experimental setup of inclined indentation is illustrated in a. b, c Scanning electron microscope images, atomic force microscope topographic image of the zoom-in straight crack (left) and height profiles of the top 10 cavities (right) after inclined indentation, respectively. d Zoomed-in topographic images of the pink (left) and blue (right) rectangular zones in c. e, f Topographic images of the crack tip and the cavity ahead of the crack tip, respectively. Inset: height profile of the cavity. g, h Three-dimensional close-up topographies of another crack tip. i Crack propagation [177].

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9. Cavitation pressure decreases with increasing pressure sensitivity coefficient [179].

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10. Void growth for different rise times with an initial void radius of 1 μm under the same loading amplitude of 2 GPa [179].

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11. Optical micrographs of the shear bands ahead of a the notch tip in the mode I case before crack initiation and b the crack trajectory along the curved shear band ABC [20].

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12. The variation of plane-strain fracture toughness a with the ratio G/K and b with notch-root radius [196].

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13. a Radial, b tangential, and c shear stress distributions in the plastic zone. d The angular distributions of stress components for different values of μ and β [46].

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14. a Effective and b mean stress distributions in the plastic zone. The angular distributions of c the effective stress and d the mean stress for different values of μ and β [46].

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15. a Radial, b tangential, and c shear strain distributions in the plastic zone [46].

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16. Isolines of mode I a fracture toughness, b R_maxc, and c R_xc as a function of shear dilatancy β (μ = β) and Poisson’s ratio v [46].

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17. Isolines of shape factor Λ_c as a function of shear dilatancy β (μ = β) and Poisson’s ratio v [46].

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18. The correlation of fracture energy G_f with elastic modulus ratio for the as-cast MGs [50].

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19. Schematic illustration of shear failure along the easiest shear direction and local quasi-cleavage fracture along the normal direction at the atomic scale [14].

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20. Tensile fracture strength σ_T and tensile shear fracture angle θ_T vary with the ratio $\overset{⌢}{α}$ [52].

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21. Eccentric ellipse-like failure envelope in the τ-σ stress space: a shear failure with 45° < θ^T < 90° and 0° < θ^C < 45° and b normal tensile fracture with θ^T = 90° [14].

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22. Tensile and compressive failure angles varying with the factors α and β_SD [14].

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Table 1. Failure strengths and angles of MGs in tension and compression [14]

Composites	Failure strengths		Failure angles		Ref.
Composites	σ^T (GPa)	σ^C (GPa)	θ^T (°)	θ^C (°)	Ref.
Pd_77.5Cu₆Si_16.5	1.44	1.51	50	45	[71]
Pd₇₈Cu₆Si₁₆	1.45	1.54	55	45	[72]
Pd₄₀Ni₄₀P₂₀	1.46	1.78	50	41.9	[73]
	1.6	1.74	56	42	[74,75]
Zr_40.1Ti₁₂Ni_9.3Cu_12.2Be_26.4	1.98	2.0	51.6	40.8	[76]
Zr_41.2Ti_13.8Ni₁₀Cu_12.5Be_22.5	1.8	2.0	55	44	[15]
	1.8	1.95	56	42	[77]
	1.89	1.9	–	–	[78]
Zr_52.5Ni_14.6Al₁₀Cu_17.9Ti₅	1.65	1.88	54	44	[79]
	1.66	1.82	60	42.5	[80]
	1.66	1.76	56	42	[81]
Zr₅₅Al₁₀Cu₃₀Ni₅	1.53	1.77	53	41	[82]
	1.6	1.8	–	–	[83]
	1.51	1.82	–	–	[84]
Zr_56.2Ti_13.8Nb_5.0Ni_5.6Cu_6.9Be_12.5	1.487	1.669	59	45	[85]
Zr₅₇Cu_15.4Ni_12.6Al₁₀Nb₅	1.2	1.8	–	–	[86]
Zr₅₉Cu₂₀Al₁₀Ni₈Ti₃	1.58	1.69	54	43	[87]
Zr₆₀Al₁₀Cu₂₀Pd₁₀	1.68	1.88	55	45	[88]
Zr₆₀Al₁₀Cu₂₅Ni₅	1.63	1.76	–	–	[82]
Co₈₀Nb₁₄B₆	2.88	3.47	–	–	[73]
Cu₆₀Zr₃₀Ti₁₀	2.0	2.15	–	–	[89]
Cu₆₀Hf₂₅Ti₁₅	2.13	2.16	–	–	[89]
Pd₈₀Si₂₀	1.33	–	90	–	[90]
(Al₈₄Y₉Ni₅Co₂)_0.95Sn₅	–	–	90		[91]
La₆₂Al₁₄(Cu,Ni)₂₄	0.55	0.56	90	40-45	[92]
Zr_52.5Ni_14.6Al₁₀Cu_17.9Ti₅	–	–	90		[93]
Zr₅₉Cu₂₀Al₁₀Ni₈Ti₃	–	–	90		[93]
Zr₈₀Pd₂₀	–	–	90		[94]
Zr₅₅Al₁₀Ni₅Cu₃₀			Break or split		[93]
Ti₅₀Cu₂₀Ni₂₃Sn₇			Break or split		[93]
Fe_65.5Cr₄Mo₄Ga₄P₁₂C₅B_5.5			Break		[95]

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