Texture formation during equal channel angular extrusion of fcc and bcc materials: comparison with simple shear

Li, Saiyi; Beyerlein, Irene J.; Bourke, M.A.M.

doi:10.1016/j.msea.2004.11.032

Cited by 283 publications

(116 citation statements)

References 24 publications

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“…As elongations >400 % were observed in this condition [71], the randomness of the texture and the high misorientations between neighbouring grains suggests that the ECAP-processed alloy deforms by grain boundary In Fig. 8(a) there is a typical ECAP shear texture [74][75][76][77] after ECAP and annealing.…”

Section: Grain Structure and Texture Of The Ufg Al-mg-sc Alloymentioning

confidence: 90%

Influence of grain size on the flow properties of an Al-Mg-Sc alloy over seven orders of magnitude of strain rate

Pereira

Wang

Huang

et al. 2017

Materials Science and Engineering: A

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This is a PDF file of an unedited manuscript that has been accepted for publication. As a service to our customers we are providing this early version of the manuscript. The manuscript will undergo copyediting, typesetting, and review of the resulting galley proof before it is published in its final citable form. Please note that during the production process errors may be discovered which could affect the content, and all legal disclaimers that apply to the journal pertain. AbstractExperiments were conducted to evaluate the flow properties of an Al-3Mg-0.2Sc alloy both without and with processing using equal-channel angular pressing (ECAP). The initial grain size was ~300 m and this was reduced to ~250 nm by ECAP and then increased to ~600 nm by annealing at 673 K for 10 min. Tests were conducted to determine the mechanical properties over seven orders of magnitude of strain rate from ~10 -4 to ~10 3 s -1 .The results confirm the validity of the Hall-Petch relationship in the material processed by ECAP. Shear banding occurred in the coarse-grained material during dynamic testing but in the ECAP-processed alloy there was only minor grain coarsening. There was evidence for dynamic strain ageing in both the coarse and the ultrafine-grained (UFG) alloy with a transition in flow mechanism at high temperatures from dislocation climb in the coarsegrained material to superplasticity in the UFG alloy.

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Section: Grain Structure and Texture Of The Ufg Al-mg-sc Alloymentioning

confidence: 90%

Influence of grain size on the flow properties of an Al-Mg-Sc alloy over seven orders of magnitude of strain rate

Pereira

Wang

Huang

et al. 2017

Materials Science and Engineering: A

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“…From the PFs in Figures 8(f) or 10(c), the (110) poles pass through the endpoint of the TD axis; thus, the SD aligns with the h110i direction. This most likely suggests B= B or C (the notation is adopted from [23] and used below), or both components. If this is the case, the SDs of all the regions surrounding the weld center has the same rotation relation as the PFs about the ND.…”

Section: Development Of the Microstructure In The Horizontal Crossmentioning

confidence: 99%

Texture Development and Material Flow Behavior During Refill Friction Stir Spot Welding of AlMgSc

Shen¹,

Lage

Suhuddin³

et al. 2017

Metall Mater Trans A

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The microstructural evolution during refill friction stir spot welding of an AlMgSc alloy was studied. The primary texture that developed in all regions, with the exception of the weld center, was determined to be h110i fibers and interpreted as a simple shear texture with the h110i direction aligned with the shear direction. The material flow is mainly driven by two components: the simple shear acting on the horizontal plane causing an inward-directed spiral flow and the extrusion acting on the vertical plane causing an upward-directed or downward-directed flow. Under such a complex material flow, the weld center, which is subjected to minimal local strain, is the least recrystallized. In addition to the geometric effects of strain and grain subdivision, thermally activated high-angle grain boundary migration, particularly continuous dynamic recrystallization, drives the formation of refined grains in the stirred zone.

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“…The symmetry, number of peaks, and uniformity of their intensity reveal that this texture corresponds to slight variations about a single specific crystal orientation with 101 at the center and 111 towards the right. Comparing this orientation to ideal shear textures of bcc alloys [26,33] (see Figure 5(c)) reveals this to correspond to the bcc D 1 ideal shear texture. (Recall that, for this particular viewing orientation and location in the weld, the shear direction is towards the right and the shear plane normal is upwards, in agreement with the orientation of the calculated shear textures.)…”

Section: Resultsmentioning

confidence: 76%

Thermal Stir Welds in Titanium

Fonda

Knipling

Pilchak

2015

Metall Mater Trans A

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Although conventional friction stir welding (FSW) has proven unsuccessful in joining thick sections of alpha and near-alpha titanium alloys, thermal stir welding, a variant of the FSW process in which an external heat source is used to preheat the workpiece, is demonstrated to be able to reliably join 12.3-mm-thick plates of CP titanium. This paper describes the microstructures and textures that develop in these thermal stir welds. The observed microstructure was used to reconstruct the high-temperature microstructure and texture present during the welding process and therefore reveal the genesis of the welding structures.

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Texture formation during equal channel angular extrusion of fcc and bcc materials: comparison with simple shear

Cited by 283 publications

References 24 publications

Influence of grain size on the flow properties of an Al-Mg-Sc alloy over seven orders of magnitude of strain rate

Influence of grain size on the flow properties of an Al-Mg-Sc alloy over seven orders of magnitude of strain rate

Texture Development and Material Flow Behavior During Refill Friction Stir Spot Welding of AlMgSc

Thermal Stir Welds in Titanium

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