Influence of strong static magnetic field on intermediate phase growth in Mg–Al diffusion couple

Li, Z.F.; Dong, Jie; Zeng, Xiaoqin; Lu, Cen; Ding, Wenjiang; Ren, Zhongming

doi:10.1016/j.jallcom.2006.09.032

Cited by 76 publications

(62 citation statements)

References 14 publications

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“…This must be accounted for to accurately determine the contribution made by grain boundary diffusion. Grain growth kinetics generally follows the typical grain growth equation [20] :…”

Section: Grain Growthmentioning

confidence: 99%

“…[20] This classic grain growth model is valid for equiaxed grains. For columnar grains, which are often observed in the IMC layer formed in a diffusion couple, if only the widening of grains is considered, then Eq.…”

Section: Grain Growthmentioning

confidence: 99%

“…[9] can also be applied, but the grain size L should be the average width of the columnar grains measured from 2-D section. [20] It is difficult to determine the appropriate values for k and n a priori, and so in the present work, these are derived by fitting to experimental measurements of the IMC grain size made at different times. A further complication arises because the grain size is often not uniform through the IMC layer.…”

Section: Grain Growthmentioning

confidence: 99%

“…The basic approach is from Kajihara's model [1,2] extended to include multiple phases. A classical grain growth model [20] is applied to predict IMC grain size. The model is demonstrated by application to the case of Al-Mg alloy couples produced by ultrasonic welding and diffusion annealing.…”

Section: Introductionmentioning

confidence: 99%

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Modeling of Intermetallic Compounds Growth Between Dissimilar Metals

Wang

Prangnell

et al. 2015

Metall Mater Trans A

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A model has been developed to predict growth kinetics of the intermetallic phases (IMCs) formed in a reactive diffusion couple between two metals for the case where multiple IMC phases are observed. The model explicitly accounts for the effect of grain boundary diffusion through the IMC layer, and can thus be used to explore the effect of IMC grain size on the thickening of the reaction layer. The model has been applied to the industrially important case of aluminum to magnesium alloy diffusion couples in which several different IMC phases are possible. It is demonstrated that there is a transition from grain boundary-dominated diffusion to lattice-dominated diffusion at a critical grain size, which is different for each IMC phase. The varying contribution of grain boundary diffusion to the overall thickening kinetics with changing grain size helps explain the large scatter in thickening kinetics reported for diffusion couples produced under different conditions.

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“…This must be accounted for to accurately determine the contribution made by grain boundary diffusion. Grain growth kinetics generally follows the typical grain growth equation [20] :…”

Section: Grain Growthmentioning

confidence: 99%

Section: Grain Growthmentioning

confidence: 99%

Section: Grain Growthmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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Modeling of Intermetallic Compounds Growth Between Dissimilar Metals

Wang

Prangnell

et al. 2015

Metall Mater Trans A

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“…It can be seen, in both cases, an obvious linear relationship is found between the thicknesses of the intermediate phase layers and the square root of annealing time. The relation could be represented by the parabolic rate law [8] : layers is controlled by the volume diffusion mechanism [9] . This observation is in partial agreement with the reported results on the Ni-Al diffusion couple [3] .…”

Section: Growth Kineticsmentioning

confidence: 99%

Formation and growth kinetics of intermediate phases in Ni-Al diffusion couples

Ren

Zhou

et al. 2009

J. Wuhan Univ. Technol.-Mat. Sci. Edit.

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Formation and growth of the intermediate phases in the Ni-Al diffusion couples prepared by pouring technique were investigated. Electron probe microanalysis, scanning electron microscopy and X-ray diffraction were used to characterize the product phases in the joints. The results show that two intermediate phases form in the sequence of NiAl 3 and Ni 2 Al 3 during solidification. After annealed, Ni 2 Al 3 and NiAl 3 still exist in the joints of the couples. The reasons for the formation of Ni 2 Al 3 and NiAl 3 , as well as the absence of NiAl, Ni 5 Al 3 and Ni 3 Al were discussed, respectively. The growth kinetics of both product phase layers indicates that their growth obeys the parabolic rate law. The activation energies and frequency factors for NiAl 3 and Ni 2 Al 3 phases were also calculated according to the Arrhenius equation.

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