Explore a magnified edge-dislocation cross-section. Resolved shear moves the defect across the slip plane; atoms behind it shift by a Burgers vector and leave a permanent surface step.
• 3D scene parts: upper atomic rows; lower atomic rows; edge-dislocation core / extra half-plane; slip plane and Burgers vector; applied and resolved loading. • Controls: applied tensile stress (0–200 MPa), slip orientation θ (0–90 °), critical resolved shear stress (10–80 MPa), illustrative glide mobility (0.02–0.12 nm/(MPa·s)), burgers-vector magnitude (0.2–0.35 nm). • Live readouts: resolved shear stress; schmid factor; glide distance; glide velocity; completed Burgers-vector steps; plastic shear estimate b×steps/h. • Guided experiments: Unfavorable orientation; Maximum Schmid factor; Raise resistance. • Four tabs (visual laboratory, curves and measurements, experiments, learn and assess), a model-verification run, a timestamped event log and a trial report.
τ=σ cosφ cosλ=σ sinθ cosθ v=M max(0,τ−τ_c) Glide distance=min(8b,v t) A completed traversal produces slip b; γ_p=b/h with h=8b.
A single ideal edge-dislocation traverse across an eight-spacing crystal strip. Motion is mobility-limited with a sharp teaching threshold. The half-plane/core and atom trajectories are schematic; this is not atomistic elasticity, a Peierls potential, dislocation multiplication or a hardening law. One animation second is one chosen model second. Try the preset experiments, then compare the live readouts with the equations.
No, a localized defect can propagate. Dislocation glide moves the local rearrangement across the plane.
Yes. Orientation controls the Schmid factor.
A single ideal edge-dislocation traverse across an eight-spacing crystal strip. Motion is mobility-limited with a sharp teaching threshold. The half-plane/core and atom trajectories are schematic; this is not atomistic elasticity, a Peierls potential, dislocation multiplication or a hardening law. One animation second is one chosen model second.