Molecular Dynamics Modeling and Studying of Micro-Deformation Behavior in Metal Roll-Bonding Process

doi:10.11900/0412.1961.2018.00524

Acta Metall Sin

2019, Vol. 55

Issue (7): 919-927 DOI: 10.11900/0412.1961.2018.00524

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Molecular Dynamics Modeling and Studying of Micro-Deformation Behavior in Metal Roll-Bonding Process

Qingdong ZHANG,Shuo LI,Boyang ZHANG(

),Lu XIE,Rui LI

School of Mechanical Engineering, University of Science and Technology Beijing, Beijing 100083, China

Cite this article:

Qingdong ZHANG,Shuo LI,Boyang ZHANG,Lu XIE,Rui LI. Molecular Dynamics Modeling and Studying of Micro-Deformation Behavior in Metal Roll-Bonding Process. Acta Metall Sin, 2019, 55(7): 919-927.

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Abstract

Stainless steel/carbon steel bimetallic products, which have the characteristic corrosion resistance of stainless steel as well as the characteristics of high strength and low cost of carbon steel, have been widely used in petrochemical, aviation, shipping and other industries. Roll-bonding is an efficient solid-phase joining method for industrial production of bimetallic products. Different from diffusion bonding and friction welding process, the atoms bond and diffuse at interface while the base metal undergoes severe plastic deformation in the process of roll-bonding. In present work, the micro-deformation behavior in the interfacial area of stainless steel/carbon steel during roll-bonding process is studied based on the molecular dynamics method. Firstly, the applicability of the potential function for the bimetallic composite models with different lattice structures was discussed. Then bimetallic model of FeCrNi/Fe and single metal model of FeCrNi, Fe were established. The effect of non-coherent interface on the deformation behavior was revealed by comparing the deformation process of three models. The results show that the mechanical properties and deformation processes of bimetal and single metal are different in the process of deformation bonding. Due to the existence of non-coherent interface, the dislocation in pure Fe matrix is accumulated at the interface during deformation. The local shear effect of interface atoms makes the dislocation formation in FeCrNi matrix easier, thus reducing the yield strength of FeCrNi matrix. The effect of interface on dislocation propagation during alternation makes the dislocation density change alternately in the two matrixes, which improves the ability of material to resist plastic deformation. In addition, the alternately change of the dislocation density within the two matrixes during the deformation process leads to the special phenomenon that the deformation of the two matrixes is alternately changed.

Key words: molecular dynamics 304 stainless steel/Q235 carbon steel FeCrNi/Fe roll-bonding

Received: 20 November 2018

ZTFLH:

TG331

Fund: National Natural Science Foundation of China(No.51575040)

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	Qingdong ZHANG
	Shuo LI
	Boyang ZHANG
	Lu XIE
	Rui LI

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https://www.ams.org.cn/EN/10.11900/0412.1961.2018.00524 OR https://www.ams.org.cn/EN/Y2019/V55/I7/919

Fig.1 Contents of various lattice structures of FeCrNi/Fe in the relaxation process with potential function 1 (a) and potential function 2 (b) (The green, red and blue colors represent the fcc, hcp and bcc atoms, respectively)

Fig.2 Potential energies of FeCrNi (a) and Fe (b) under different lattice constants with potential function 1

Fig.3 Initial configurations of FeCrNi/Fe (a), FeCrNi (b) and Fe (c)

Fig.4 Stress-strain curves for FeCrNi/Fe、FeCrNi and Fe under z-direction compression

Fig.5 Stress-strain curve and the sequence of snapshots capturing the atomic deformation process for FeCrNi/Fe under z-direction uniaxial compression at 600 K (The red, blue and yellow colors represent the Fe, Cr and Ni atoms, respectively, in FeCrNi matrix. The white color represents the Fe atoms in Fe matrix)

Fig.6 Atomic configurations (a1, b1, a2, b2) and dislocation distributions (c1, c2) at point A (a1~c1) and point B (a2~c2) in Fig.5 showing the process of dislocation at the interface emitted to the FeCrNi matrix (Red color represents the hcp atoms and two adjacent hcp atoms mean an intrinsic stacking fault)

Fig.7 Atomic configurations at point A (a), point B (b) and point C (c) in Fig.5 showing the process of atoms rearrangement of Fe matrix

Fig.8 Dislocation distributions of FeCrNi/Fe at points A~F in Fig.5, respectively, during deformation (a1~f1) and dislocation distributions of FeCrNi when the strain is 0.078, 0.1, 0.2 and 0.3, respectively (a2~d2)

Fig.9 Thicknesses (a) and lengths of the total dislocation line (b) of two matrices of FeCrNi/Fe under different strains

Fig.10 Thickness variations of two base metals during deformation bonding process

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