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Dislocations in Deformed Beryllium

  • V. V. Damiano
  • M. Herman

Abstract

High-purity beryllium single crystals were deformed in tension for basal and for prism slip. Some of the work-hardening mechanisms operating at various stages were deduced from observations of dislocations in foils cut from the bulk crystals and from slip lines observed on the surface. Observation of long-edge pairs and edge dipoles in foils cut from crystals deformed in stage I for basal slip suggests that screws have high mobility on the basal plane in stage I and that the crystals exhibit very little hardening. In stage II the presence of numerous edge boundaries was associated with the onset of a rapid rate of work hardening just prior to failure. Three stages of hardening were observed for crystals deformed for prism slip. In stage I the observation of a predominance of screw dislocations suggested that screw dislocation intersections with the grown-in networks had to occur, producing jogs in the screws which acted to impede the motion of the screw dislocations. In stage II complex interactions produced complicated tangled masses of dislocations. In stage III the onset of duplex slip produces stable low-angle boundaries as a result of dislocation interactions along intersections of glide planes.

Keywords

Basal Plane Burger Vector Stack Fault Energy Screw Dislocation Edge Dislocation 
These keywords were added by machine and not by the authors. This process is experimental and the keywords may be updated as the learning algorithm improves.

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References

  1. 1.
    J. J. Gilman, Trans. AIME 221: 456 (1961).Google Scholar
  2. 2.
    P. Ward Flynn, J. Mote, and J. E. Dorn, Trans. AIME 221: No. 6, 1148 (1961).Google Scholar
  3. 3.
    A. T. Churchman, Proc. Roy. Soc. A226: 216 (1954).Google Scholar
  4. 4.
    N. Thompson, Proc. Phys. Soc. 66: 481 (1953).CrossRefGoogle Scholar
  5. 5.
    V. V. Damiano, Trans. AIME 222: 788 (1963).Google Scholar
  6. 6.
    G. E. Spangler, M. Herman, and E. J. Arndt, Franklin Institute, Final Report F-A2476, Department of the Navy, Bureau of Naval Weapons, Contract No. NoW 61–0221-d.Google Scholar
  7. 7.
    W. L. Grube and S. R. Rouze, Proc. ASTM 52: 573 (1952).Google Scholar
  8. 8.
    F. Wilhelm and H. G. F. Wilsdorf, Franklin Institute Report on Air Force Contract No. AF 33(616)7065 (1961).Google Scholar
  9. 9.
    G. V. T. Ranzetta and V. D. Scott, J. Nucl. Mater. 10: 113 (1963).CrossRefGoogle Scholar
  10. 10.
    W. G. Johnston and J. J. Gilman, J. Appl. Phys. 31: 632 (1960).CrossRefGoogle Scholar
  11. 11.
    A.S. Tetelman, Acta Met. 10, 813 (1962).CrossRefGoogle Scholar
  12. 12.
    P. B. Price, Phil. Mag. 5, 873 (1960).CrossRefGoogle Scholar
  13. 13.
    L. Segall, Electron Microscopy and Strength of Crystals ( Interscience, New York, 1963 ), p. 515.Google Scholar
  14. 14.
    P. B. Hirsch, Symposium on Internal Stress and Fatigue in Metals, General Moton Laboratories (1958).Google Scholar

Copyright information

© Plenum Press 1965

Authors and Affiliations

  • V. V. Damiano
    • 1
  • M. Herman
    • 1
  1. 1.The Franklin Institute Research LaboratoriesPhiladelphiaUSA

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