Effect of Milling Time on the Microstructure and Tensile Properties of Ultrafine Grained Ni-SiC Composites at Room Temperature

doi:10.1016/j.jmst.2014.12.009

Abstract

Abstract: Bulk metallic nickel-silicon carbide nano-particle (Ni-SiC_NP) composites, with milling time ranged from 8 to 48 h, were prepared in a planetary ball mill and sintered using a spark plasma sintering (SPS) furnace. The microstructure of the Ni-SiC_NP composites was characterized by transmission electron microscopy (TEM) and their mechanical properties were investigated by tensile measurements. The TEM results showed well-dispersed SiC_NP particles, either within the matrix, between twins or along grain boundaries (GB), as well as the presence of stacking faults and twin structures, characteristics of materials with low stacking fault energy. Dislocation lines were also observed to interact with the SiC_NP which were plastically nondeformable. A synergistic relationship existed between Hall-Petch strengthening and dispersion strengthening mechanisms, which was shown to greatly influence the mechanical properties of the Ni-SiC_NP composites. Both the maximum yield and tensile strengths were found in the Ni-SiC_NP composite with a milling time of 48 h, whereas the increased rate of strengths drastically decreased in material milled above 8 h due to the significant SiC_NP agglomeration. The ball milling process resulted in the formation of nano-scale, ultra-fine grained (UFG) Ni-SiC_NP composites when the milling time was extended for longer periods, greatly strengthening these materials. The sharp decrease in elongation percentages, however, should be comprehensively considered before irreversible inelastic deformation.

Key words: Ni-SiCNP composite, Mechanical alloying, Spark plasma sintering, Transmission electron microscopy, Tensile test, Ultra-fine grained (UFG)

Hefei Huang, Chao Yang, Massey de los Reyes, Yongfeng Zhou, Long Yan, Xingtai Zhou. Effect of Milling Time on the Microstructure and Tensile Properties of Ultrafine Grained Ni-SiC Composites at Room Temperature[J]. J. Mater. Sci. Technol., 2015, 31(9): 923-929.

Figures/Tables 10

(a) SEM micrograph of pure nickel, (b) TEM image of SiCNP powder.

Dimension of the dogbone-style tensile specimens.

Bright-field TEM images of unreinforced pure nickel (a) and Ni-SiCNP composites with a milling time of 8 h (b), 24 h (c), 36 h (d) and 48 h (e). High number densities of dispersed SiCNP (marked with red arrows) are visible in the Ni-SiCNP composites.

EBSD images of unreinforced pure nickel (a) and Ni-SiCNP composites with a milling time of 8 h (b), 24 h (c), 36 h (d) and 48 h (e).

Grain size distribution (a) and average grain diameter (b) of Ni-SiC composites with the extension of milling time from 8 h to 48 h.

Bright-field TEM images of the Ni-SiCNP composites with a milling time of 24 h (a) and (b) SAED pattern along a [110] zone axis taken from the twin boundary (circled in (a)).

Bright-field TEM images showing the distribution of SiCNP in matrix, twin boundary sites and on GB. The interaction of dislocation lines with SiCNP in the Ni-SiCNP composites (24 h) was also observed.

Variation in yield strength (a) and tensile strength (b) of both the unreinforced pure nickel and the Ni-SiCNP composites milled at different time. The uncertainties are given by the standard deviation (2σ

Variation in elongation percentages of unreinforced pure nickel and Ni-SiCNP composites milled at different time. The uncertainties are given by the standard deviation (2σ

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