Improving mechanical properties of heterogeneous Mg-Gd alloy laminate via accumulated extrusion bonding

Liu, Shuaishuai; Zhang, Junlei; Chen, Xiang; Huang, Guangsheng; Xia, Dabiao; Tang, Aitao; Zhu, Yuntian; Jiang, Bin; Pan, Fusheng

doi:10.1016/j.msea.2020.139324

Cited by 35 publications

(5 citation statements)

References 64 publications

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“…It indicates that the additional strengthening effect increases first and then decreases with the increase of the layer thickness, with the maximum level for a layer thickness of about 66 μm, which may be beneficial to obtain an optimized IAZ. Previous studies [ 5,40 ] reported that the width of the IAZ remains independent of the layer thickness for layered materials with a certain material system. It was also reported that when the layer thickness approaches two times the width of the IAZ, the layer structure would cause the strongest additional strengthening effect.…”

Section: Discussionmentioning

confidence: 99%

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Study on Microstructures and Mechanical Properties of Layered and Layered‐Gradient Zr/Ti Materials

Zhou

et al. 2021

Adv Eng Mater

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To achieve good combination of strength and ductility, more and more attention is paid to heterostructured (HS) materials in the material community. [1,2] The microstructures of HS materials generally comprise multiple domains with remarkably different mechanical properties. The interdomain transition may be sharp or in the form of a gradient. [3][4][5] Many HS materials show better combination of strength and ductility than their homogeneous counterparts. [6][7][8][9][10] The superior properties are generally attributed to the heterozone interaction. During the loading of an HS material, the asynchronous deformation of the hard and soft domains generally causes a strong strain gradient near the interface, where geometrically necessary dislocations are accumulated to induce heterodeformationinduced (HDI) strengthening and hardening, thus contributing to achieve better strength and ductility. [11][12][13][14] Gradient materials are typical HS materials, which are characterized by a spatial gradient in the microstructure and/or composition along a certain direction. [15] In the past decades, many methods were proposed to fabricate gradient materials. Surface mechanical treatments, including surface mechanical attrition treatment (SMAT), [16] surface mechanical grinding treatment (SMGT), [17,18] and surface mechanical rolling treatment (SMRT), [19] were developed to fabricate gradient metals or alloys, with a fine grain/twin near the surface and a coarser size grain/twin in the core region. Torsion, with larger strain at the surface and smaller strain in the core of a rod, was also used to produce gradient microstructures. [20] Except for mechanical treatments, physical and chemical deposition techniques, such as electrodeposition, magnetron sputtering, and 3D printing, were developed to fabricate gradient materials. [21][22][23] By controlling the deposition kinetic and other processing parameters, such as current density, temperature, and additive content, various gradient microstructures can be tailored. In addition, laser shock peening, which applies a highenergy and ultrashort-duration laser pulse to produce a compressive shock wave and heavy plastic deformation on the surface of treated materials, was also used to prepare gradient materials. [24] Despite the aforementioned methods, it is still a challenge to fabricate bulk gradient materials with a controlled microstructure. So far, most researches have focused on materials with a gradient microstructure. A single layer of gradient microstructure was generally produced from the surface to the core region in most of the studied gradient materials. The depth or range of the gradient microstructure was limited. Few studies focus on composition-gradient materials. In natural materials, many gradient structures arose from a graded chemical composition. [25]

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Section: Discussionmentioning

confidence: 99%

“…The interdomain transition may be sharp or in the form of a gradient. [3][4][5] Many HS materials show better combination of strength and ductility than their homogeneous counterparts. [6][7][8][9][10] The superior properties are generally attributed to the heterozone interaction.…”

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confidence: 99%

Study on Microstructures and Mechanical Properties of Layered and Layered‐Gradient Zr/Ti Materials

Zhou

et al. 2021

Adv Eng Mater

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“…Additionally, no material specimen or die preheat is used as indicated in the research performed in [49]. Most unique, no research has reported using AEB to manufacture multilayered bimetals in the form of tube as current research utilizes plate or sheet as done in [48][49][50][51]. For this reason, as part of the AEB process used for this research, expansion is necessary to facilitate restacking.…”

Section: Introductionmentioning

confidence: 99%

Towards Manufacturing of Ultrafine-Laminated Structures in Metallic Tubes by Accumulative Extrusion Bonding

Standley

Knežević

2021

Metals

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A severe plastic deformation process, termed accumulative extrusion bonding (AEB), is conceived to steady-state bond metals in the form of multilayered tubes. It is shown that AEB can facilitate bonding of metals in their solid-state, like the process of accumulative roll bonding (ARB). The AEB steps involve iterative extrusion, cutting, expanding, restacking, and annealing. As the process is iterated, the laminated structure layer thicknesses decrease within the tube wall, while the tube wall thickness and outer diameter remain constant. Multilayered bimetallic tubes with approximately 2 mm wall thickness and 25.25 mm outer diameter of copper-aluminum are produced at 52% radial strain per extrusion pass to contain eight layers. Furthermore, tubes of copper-copper are produced at 52% and 68% strain to contain two layers. The amount of bonding at the metal-to-metal interfaces and grain structure are measured using optical microscopy. After detailed examination, only the copper-copper bimetal deformed to 68% strain is found bonded. The yield strength of the copper-copper tube extruded at 68% improves from 83 MPa to 481 MPa; a 480% increase. Surface preparation, as described by the thin film theory, and the amount of deformation imposed per extrusion pass are identified and discussed as key contributors to enact successful metal-to-metal bonding at the interface. Unlike in ARB, bonding in AEB does not occur at ~50% strain revealing the significant role of more complex geometry of tubes relative to sheets in solid-state bonding.

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“…The forged alloy exhibited an excellent ultimate tensile strength (UTS) and ductility of 581 MPa and 15.9%, respectively. Jiang et al [27] processed a heterogeneous Mg-1Gd/Mg-13Gd alloy laminate via accumulative extrusion bonding (AEB), whose strength and ductility were much superior to that of the individual component material. Wu et al [28] demonstrated that the bimodal structure brought into high strength in the Mg-15Gd-1Zn-0.4Zr (wt.…”

Section: Introductionmentioning

confidence: 99%

Wear Behavior of the Multiheterostructured AZ91 Mg Alloy Prepared by ECAP and Aging

Sun

Yang

et al. 2020

Scanning

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The microstructure design based on the development of heterostructure provides a new way for high strength and ductility Mg alloys. However, the wear property, as an important service performance, of Mg alloys with heterostructure is scarcely investigated. In this work, a high strength and ductility AZ91 Mg alloy with multiheterostructure was prepared via a processing route combined industrial-scale equal channel angular pressing (ECAP) and aging. The multiheterostructure consists of the heterogeneous grain structure and heterogeneous precipitates. The dry sliding wear behavior of this multiheterostructured (MH) alloy is investigated compared to the as-cast alloy. The impacts of the applied load and duration time on the wear volume and coefficient of friction (COF) are analyzed, and the wear mechanism is further discussed. The result indicates that although the MH alloy exhibits high-desirable strength-ductility synergy, it shows a poorer wear resistance but a relatively lower COF compared to the as-cast alloy at the present condition. The wear mechanism of both alloys mainly involves abrasive wear, as well as mild adhesion, delamination, and oxidation. In comparison, the MH alloy shows relatively severe adhesion, delamination, and oxidation. The poor wear resistance of the MH alloy at the present dry sliding wear condition is linked to the abundant grain boundaries and fine precipitates. Therefore, one should reasonably use the MH Mg alloy considering the service conditions to seek advantages and avoid disadvantages.

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Improving mechanical properties of heterogeneous Mg-Gd alloy laminate via accumulated extrusion bonding

Cited by 35 publications

References 64 publications

Study on Microstructures and Mechanical Properties of Layered and Layered‐Gradient Zr/Ti Materials

Study on Microstructures and Mechanical Properties of Layered and Layered‐Gradient Zr/Ti Materials

Towards Manufacturing of Ultrafine-Laminated Structures in Metallic Tubes by Accumulative Extrusion Bonding

Wear Behavior of the Multiheterostructured AZ91 Mg Alloy Prepared by ECAP and Aging

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