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Transmission Electron Microscopy Study of Strain-Induced Low- and High-Angle Boundary Development in Equal-Channel Angular-Pressed Commercially Pure Aluminum

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Abstract

The evolution of the microstructure in a commercially pure aluminum during equal channel angular pressing (ECAP) using route BC was investigated by transmission electron microscopy. Subgrains, or cells, form, which have both high (ϕ > 15 deg) and low (ϕ < 15 deg) misorientation. Misorientations and spacings of cell boundaries were determined from about 250 boundaries per pass of ECAP cell boundaries on the basis of Kikuchi patterns and Moiré fringes. The average cell size and misorientation saturate within the first two passes. Misorientations and spacings of high-angle boundaries decrease with the number of passes. After eight passes, the cell size is ≈1.3 μm and the fraction of high-angle boundaries is ≈0.7. The marked differences in the rate of grain structure evolution per pass are linked to differences in the ability of dislocations introduced in new passes to recombine with the existing ones. With increasing ECAP strain, the distribution of misorientations develops strong deviations from the MacKenzie distribution for statistical grain orientation. This is interpreted as a result of the tendency to form equiaxed grains in a textured grain structure.

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Notes

  1. PHILIPS is a trademark of Philips Electronic Instruments Corp., Mahwah, NJ.

  2. The sign of the Burgers vector changes with the sign of the dislocation line direction. As opposite sides of a dislocation loop have opposite line directions, the Burgers vectors are opposite on opposite sides of the loop if the line directions are chosen to be the same. This means that Burgers vectors of opposite sign are generated at equal amounts. In 50 pct of the encounters of dislocations with the favored Burgers vector of passes 1 and 2, an energetically favorable recombination to a dislocation with Burgers vector of type \( {\left\langle {110} \right\rangle } \) is possible.

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Acknowledgments

The support from NSF European Collaborative Grant No. DMR-041222 and INFM PAIS-UFIGRAL 6001 is gratefully acknowledged.

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Authors and Affiliations

  1. Department of Mechanics, Marche Polytechnic University, Via Brecce Bianche, 60131, Ancona, Italy

    M. Cabibbo (Associate Professor) & E. Evangelista (Full Professor)

  2. Institute for Werkstoffwissenschaften LS 1, University of Erlangen–Nürnberg, 91058, Erlangen, Germany

    W. Blum (Emeritus Full Professor)

  3. Department of Aerospace and Mechanical Engineering, University of Southern California, Los Angeles, CA, 90089-1453, USA

    M.E. Kassner (Full Professor)

  4. Mechanical and Aerospace Engineering Department, University of California, San Diego, La Jolla, CA, 92093-0411, USA

    M.A. Meyers (Full Professor)

Authors
  1. M. Cabibbo
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  2. W. Blum
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  3. E. Evangelista
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  4. M.E. Kassner
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  5. M.A. Meyers
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Correspondence to M. Cabibbo.

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Appendix

Appendix

The area per volume of (low-angle and high-angle) cell boundaries is k λ /λ. Analogously, the area per volume of high-angle boundaries is k d /d. The numerical factors k λ and k d depend on (sub-) grain shape. For instance, they equal 2 for equiaxed grains and 1 for parallel, plane boundaries and the test line perpendicular to the boundaries. The area fraction of high-angle boundaries results in f HAB = (k d /d)/(k λ /λ). Assuming that the deviations from equiaxiality are the same for cells and grains and that the cell intercepts are approximately perpendicular to the direction of grain elongation, k λ  = k d holds. Then, f HAB = λ/d is the fraction of high-angle boundaries.

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Cabibbo, M., Blum, W., Evangelista, E. et al. Transmission Electron Microscopy Study of Strain-Induced Low- and High-Angle Boundary Development in Equal-Channel Angular-Pressed Commercially Pure Aluminum. Metall Mater Trans A 39, 181–189 (2008). https://doi.org/10.1007/s11661-007-9350-z

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