Competitive effect of stacking fault energy and short-range clustering on the plastic deformation behavior of Cu-Ni alloys

• Published in: Materials science & engineering. A, Structural materials : properties, microstructure and processing Vol. 679; pp. 484 - 492
• Main Authors: Wang, Z.Y., Han, D., Li, X.W.
• Format: Journal Article
• Language: English
• Published: Lausanne Elsevier B.V 02-01-2017; Elsevier BV
• Subjects: Alloys; Clustering; COPPER ALLOYS (40 TO 99.3 CU); Copper base alloys; Cu-Ni alloy; DEFORMATION; Deformation effects; Dislocation structure; Dislocations; Ductility; Edge dislocations; GRAIN SIZE AND SHAPE; Hardening rate; Mechanical tests; Microstructure; MICROSTRUCTURES; Nickel base alloys; Planes; Plastic deformation; PLASTIC STRAIN; Promotion; Short-range cluster; Slip; Slip deformation mode; Slip planes; Stacking fault energy; STACKING FAULTS; Strain; Strain concentration; Strain hardening; STRAIN HARDENING MECHANISMS; Tensile plastic deformation; TENSILE STRENGTH; Tensile tests; Ultimate tensile strength; Cu-Ni alloy; Stacking fault energy; Dislocation structure; Tensile plastic deformation; Short-range cluster; Slip deformation mode
• ISSN: 0921-5093; 1873-4936
• DOI: 10.1016/j.msea.2016.10.064

Uniaxial tensile tests were conducted to investigate the plastic deformation behavior and deformation microstructures of coarse-grained Cu-Ni alloys containing a wide range of Ni contents (5–20at%), which possess higher stacking fault energies (SFE) than pure Cu. The mechanical testing results show that, with increasing Ni content, i.e., jointly increasing SFE and degree of short range clustering (SRC), the ultimate tensile strength increases, but the ductility keeps almost unchanged; meanwhile, there exists an obvious increasing stage (or “bump”) in the strain-hardening rate curves at around 3% engineering strain. Microstructural examinations demonstrate that dislocations are apt to slip on primary slip planes at the initial stage of deformation (e.g., 3% engineering strain) to form planar slip bands, indicating that the existence of SRCs in Cu-Ni alloys is beneficial to the promotion of planar slip, leading to the occurrence of a “bump” phenomenon in the strain-hardening rate curves. With increasing deformation amount to a certain degree, wavy slip becomes the major deformation mode under the joint influence of high SFE and diminution of SRCs, and the final deformation microstructures transform from dislocation cells and cell blocks into extended dislocation walls with increasing Ni content. Both the cell block structures and extended dislocation walls subdivide the coarse grains uniformly to disperse local strain concentration, thus enabling the Cu-Ni alloys to maintain a high ductility with an increased tensile strength with increasing Ni content. In a word, the plastic deformation behavior of Cu-Ni alloys is actually governed by the competitive influence of SRC and SFE.