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Acta Metall Sin  2016, Vol. 52 Issue (8): 905-915    DOI: 10.11900/0412.1961.2016.00053
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INFLUENCES OF DISLOCATIONS ON NUCLEATION AND MICRO-TEXTURE FORMATION OFα PHASE IN Ti-6Al-4V ALLOY
Jinhu ZHANG1,Dongsheng XU1(),Yunzhi WANG2,Rui YANG1
1 Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
2 The Ohio State University, Columbus, OH 43210, USA
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Abstract  

Titanium alloys are widely applied in aerospace, chemical and other related industries. The α+β alloys may obtain various microstructures and mechanical properties simply by varying their thermomechanical processing. Ti-6Al-4V alloy is the most common α+β titanium alloy. Its strength, ductility, fracture toughness and fatigue properties depend strongly on the microstructure especially texture. The understanding of the formation mechanisms of α micro-texture during processing is necessary for the optimization of the mechanical properties. In this work, the nucleation of α precipitates and micro-texture formation process under the influence of dislocations during the βα transformation in Ti-6Al-4V alloy was simulated by phase field method. The stress field of an infinite straight dislocation was calculated by Willis-Steeds-Lothe method and used as input of the phase field model. It was shown that the normal stress component S33 plays a dominant role in α variants nucleation in the presence of edge dislocation, while the shear stress component S23 is the most important one for screw dislocation. The effect of edge dislocation on α variant selection is generally stronger than that of screw. V1 and V7 are the main variants selected by the edge dislocation while V7, V10 and V12 dominate around the screw dislocation, with V1/V7, V1/V4/V6 being the main variant cluster types around the edge dislocation, and V7/V10/V12 being the primary one for the screw dislocation. In a system with the presence of dislocations in the parent phase, the precipitate microstructure is determined by the combined effect of elastic interactions between the dislocation and different variants of a low symmetry precipitate phase, and elastic interactions among different variants. Variants with interfaces of relatively high energy may appear because of variants selection by dislocations.

Key words:  Ti-6Al-4V alloy      dislocation      phase field simulation      variant selection      micro-texture     
Received:  02 February 2016     
Fund: Supported by National Basic Research Program of China (Nos.2006CB605104 and 2011CB606404) and National Natural Science Foundation of China (Nos.51101158 and 51171195)

Cite this article: 

Jinhu ZHANG,Dongsheng XU,Yunzhi WANG,Rui YANG. INFLUENCES OF DISLOCATIONS ON NUCLEATION AND MICRO-TEXTURE FORMATION OFα PHASE IN Ti-6Al-4V ALLOY. Acta Metall Sin, 2016, 52(8): 905-915.

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https://www.ams.org.cn/EN/10.11900/0412.1961.2016.00053     OR     https://www.ams.org.cn/EN/Y2016/V52/I8/905

Fig.1  Schematics of simulation boxes containing an infinite straight edge (a) or screw (b) dislocation (b—Burgers vector)
Fig.2  Stress field around an infinite straight edge dislocation (S11, S22 and S33 are normal stress components; S23 is shear stress component) (a) S11 (b) S22 (c) S33 (d) S23
Fig.3  Morphology (a) and enlarged image (b) of α variants along edge dislocation line at τ=104 (τ is reduced time), and {0001} (c) and {1120} (d) pole figures of α micro-texture
Fig.4  Stress field around an infinite straight screw dislocation (S12 and S13 are shear stress components) (a) S11 (b) S22 (c) S33 (d) S12 (e) S13 (f) S23
Fig.5  Morphology (a) and enlarged image (b) of α variants along screw dislocation line at τ=104, and {0001} (c) and {1120} (d) pole figures of α micro-texture
Fig.6  Minimum of interaction energy between different α variants and an infinite straight edge (a) or screw (b) dislocation
Fig.7  Average values of elastic interaction energies ? (a) and Bˉ1p (b) ( p=1, Bˉ7p, 12) between V1, V7 and other variants, respectively
Fig.8  Contributions of the major stress components to the minimum of interaction energy between edge dislocation and V1 (a) or V7 (b) in Fig.6a, and between screw dislocation and V7 (c) or V10 (d) in Fig.6b
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