E. J. Savino

Simple Flexible Boundary Conditions for the Atomistic Simulation of Dislocation Core Structure and Motion

Flexible boundary codes for the atomistic simulation of dislocations and other defects have been developed in the past mainly by Sinclair [1], Gehlen et al.[2], and Sinclair et al.[3]. These codes permitted the use of smaller atomic arrays than rigid boundary codes, gave descriptions of core non-linear effects and allowed fair assessments of the Peierls stress for dislocation motion. Green functions (continuum or discrete) or surface traction forces were used to relax the boundary atoms. A much simpler approach is followed here. Core and mobility effects at the boundary are accounted for by a dipole tensor centered at the dislocation line, whose components constitute six more parameters of the minimization process. Results are presented for [100] dislocations in NiAl. It is shown that, within the limitations of the technique, reliable values of the Peierls stress are obtained.

Computer Simulation of Point Defects in Hexagonal Close Packed Metals

Pair interaction potentials have been developed by spline fitting cubic functions to reproduce perfect lattice properties. The lattice symmetry is taken as hcp with the rigid sphere c/a ratio and a cut-off distance between second and third neighbor is assumed. The lattice parameter, elastic constants and vacancy formation energy of Mg, Ti and Zr are consistently fitted by the potentials. We have calculated the lattice relaxation predicted by these potentials for the vacancy, and self interstitial in an otherwise perfect hcp lattice. The stability and dynamics of those defects are studied within the quasi-harmonic approximation. The interstitial site occupancy in hcp lattice and the vacancy and interstitial diffusion are discussed.

Characterization and Statistical Distribution of Grain Boundaries in Ni 3 Al

Grain Boundaries in two specimens of Ni 4 Al of different compositions and mechanical behavior were studied by electron microscopy. SEM was used to determine the distribution of Σ values in both samples. TEM results were combined with CSL theory to completely characterize the nature of the boundaries, including Σ values and the grain boundary plane orientation. The boundaries most commonly observed in the experiments were also studied using a computer simulation technique and the results correlated with the experimental observations.

Beyond the Embedded Atom Interatomic Potential

We briefly discuss some of the advantages and limitations of using embedded atom interatomic potentials for simulating the static configuration and dynamics of lattice defects. In metals, the embedded atom potentials provide a physically more realistic approximation than simple pair interaction potentials without a significant increase in computer time needed for defect simulation studies. However, in some cases, n-body shear forces, i.e bond angle interatomic forces may be needed for fitting experimental results related to defect configuration. One such example is the elastic neutron scattering data from N interstitials in Nb [1]. Also, such bond angle forces must be included in a realistic model of atomic interactions in metals, expecially in highly anisotropic bee transition metals. Extending the concept of the embedded atom method, we propose a new form for the interatomic potential in metals which includes bond angle forces. General expressions for the elastic constants in bee and fee structures are deduced.