Torsion/Simple Shear of Single Crystal Copper

We analyze simple shear and torsion of single crystal copper by employing experiments, molecular dynamics simulations, and finite element simulations in order to focus on the kinematic responses and the apparent yield strengths at different length scales of the specimens. In order to compare torsion with simple shear, the specimens were designed to be of similar size. To accomplish this, the ratio of the cylinder circumference to the axial gage length in torsion equaled the ratio of the length to height of the simple shear specimens (0.43). With the [110] crystallographic direction parallel to the rotational axis of the specimen, we observed a deformation wave of material that oscillated around the specimen in torsion and through the length of the specimen in simple shear. In torsion, the ratio of the wave amplitude divided by cylinder circumference ranged from 0.02 ‐0.07 for the three different methods of analysis: experiments, molecular dynamics simulations, and finite element simulations. In simple shear, the ratio of the deformation wave amplitude divided by the specimen length and the corresponding values predicted by the molecular dynamics and finite element simulations (simple shear experiments were not performed) ranged from 0.23‐0.26. Although each different analysis method gave similar results for each type boundary condition, the simple shear case gave approximately five times more amplitude than torsion. We attributed this observation to the plastic spin behaving differently as the simple shear case constrained the dislocation activity to planar double slip, but the torsion specimen experienced quadruple slip. The finite element simulations showed a clear relation with the plastic spin and the oscillation of the material wave. As for the yield stress in simple shear, a size scale dependence was found regarding two different size atomistic simulations for copper (332 atoms and 23628 atoms). We extrapolated the atomistic yield stresses to the order of a centimeter, and these comparisons were close to experimental data in the literature and the present study. @DOI: 10.1115/1.1480407#

[1]  U. F. Kocks,et al.  Theory of torsion texture development , 1984 .

[2]  J. Jonas,et al.  Axial stresses and texture development during the torsion testing of Al, Cu and α-Fe , 1984 .

[3]  M. Stoneham,et al.  The Shell Model and Interatomic Potentials for Ceramics , 1996 .

[4]  David L. McDowell,et al.  Modeling temperature and strain rate history effects in OFHC Cu , 1998 .

[5]  Lawrence E Murr,et al.  Metallurgical Applications of Shock-Wave and High-Strain-Rate Phenomena, with K. P. Staudhammer and M. A. Meyers , Marcel Dekker, Inc., New York, , 1986 .

[6]  D. Brenner Chemical Dynamics and Bond-Order Potentials , 1996 .

[7]  M. Ashby,et al.  Strain gradient plasticity: Theory and experiment , 1994 .

[8]  Foiles,et al.  Calculation of the surface segregation of Ni-Cu alloys with the use of the embedded-atom method. , 1985, Physical review. B, Condensed matter.

[9]  F. Zwicky,et al.  On the Plasticity of Crystals , 1933 .

[10]  G. R. Johnson,et al.  Response of Various Metals to Large Torsional Strains Over a Large Range of Strain Rates—Part 1: Ductile Metals , 1983 .

[11]  Mark F. Horstemeyer,et al.  Atomistic Finite Deformation Simulations: A Discussion on Length Scale Effects in Relation to Mechanical Stresses , 1999 .

[12]  J. Jonas,et al.  Equivalent strain in large deformation torsion testing : Theoretical and practical considerations , 1982 .

[13]  Lajos Kator,et al.  Plastic Deformation of Metals , 1953, Nature.

[14]  S. Karashima,et al.  Stagnation of Strain Hardening During Reversed Straining of Prestrained Aluminium, Copper and Iron , 1985 .

[15]  Michael Ortiz,et al.  Computational modelling of single crystals , 1993 .

[16]  Neville Reid Moody,et al.  COMMENT: Trapping of hydrogen to lattice defects in nickel , 1995 .

[17]  Application of the Taylor polycrystal plasticity model to complex deformation experiments , 1998 .

[18]  Steven J. Plimpton,et al.  LENGTH SCALE AND TIME SCALE EFFECTS ON THE PLASTIC FLOW OF FCC METALS , 2001 .

[19]  R. Honeycombe,et al.  Plastic Deformation of Metals , 1932, Nature.

[20]  B. Adams,et al.  Unrecoverable Strain Hardening in Torsionally Strained OFHC Copper , 1990 .

[21]  David L. McDowell,et al.  Modeling effects of dislocation substructure in polycrystal elastoviscoplasticity , 1998 .

[22]  U. F. Kocks,et al.  Channel die tests on Al and Cu polycrystals: Study of the prestrain history effects on further large strain texture , 1987 .

[23]  Murray S. Daw,et al.  The embedded-atom method: a review of theory and applications , 1993 .

[24]  Akhtar S. Khan,et al.  An experimental study on subsequent yield surface after finite shear prestraining , 1993 .

[25]  S. Quilici,et al.  On sire effects in torsion of multi- and polycrystalline specimens , 1998 .

[26]  P. Jackson,et al.  Latent Hardening and the Flow Stress in Copper Single Crystals , 1967 .

[27]  M. Baskes,et al.  Embedded-atom method: Derivation and application to impurities, surfaces, and other defects in metals , 1984 .

[28]  David L. McDowell,et al.  Design of experiments for constitutive model selection: application to polycrystal elastoviscoplasticity , 1999 .

[29]  Foiles,et al.  Application of the embedded-atom method to liquid transition metals. , 1985, Physical review. B, Condensed matter.

[30]  Sia Nemat-Nasser,et al.  Heterogeneous deformations in copper single crystals at high and low strain rates , 1992 .

[31]  D. McDowell,et al.  Deformation, temperature and strain rate sequence experiments on OFHC Cu , 1999 .

[32]  A. Khan,et al.  Large deformation in polycrystalline copper under combined tension-torsion, loading, unloading and reloading or reverse loading: A study of two incremental theories of plasticity , 1986 .