Etude de la Diffusion des Radioindicateurs à l'etat solide par la méthode de Gruzin

Seibel, G.

doi:10.1016/0020-708x(64)90034-1

Cited by 25 publications

(5 citation statements)

References 3 publications

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“…This means that the high density of dislocations does not affect the lattice diffusion behavior. The solution of Fick's law for the case of a thin layer source condition was used to determine the lattice diffusion coefficients (D l ) [4],…”

Section: Resultsmentioning

confidence: 99%

Direct Measurement of Titanium Pipe Diffusion Coefficients in Sapphire

Nakagawa¹,

Sakaguchi

Shibata

et al. 2007

MSF

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The diffusion behavior of Ti3+ along basal dislocations in sapphire has been investigated by SIMS technique. High-density unidirectional dislocations were introduced by the high-temperature mechanical deformation, and Ti3+ ions were subsequently diffused along the dislocations. The SIMS diffusion profiles clearly showed diffusion tail due to the short circuit diffusion along the dislocations called pipe diffusion. Lattice diffusion coefficient and pipe diffusion coefficient of Ti3+ at 1300°C were measured to be 1.0±0.2×10-19 [m2/sec] and 2.0±0.6× 10-13 [m2/sec], respectively.

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Section: Resultsmentioning

confidence: 99%

Direct Measurement of Titanium Pipe Diffusion Coefficients in Sapphire

Nakagawa¹,

Sakaguchi

Shibata

et al. 2007

MSF

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“…The tracer content of each layer was determined from the activity of each solution measured with a scintillation counter. This approach allows a determination of the diffusion parameters without recourse to Gruzin's general method (Seibel 1964). The penetration curves for the 59Fe and 113Sn are similar in general shape and are shown in figures 2-4.…”

Section: (C) Radiotracer Measurements Of Diffusionmentioning

confidence: 97%

The role of solute segregation in grain boundary diffusion

Bernardini

Gas

Hondros

et al. 1982

Proc. R. Soc. Lond. A

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In measurements of grain boundary transport it is the product of the grain boundary enrichment ratio and the grain boundary diffusivity that is usually obtained. This work presents the first study in which these two terms are separated and in which the role of the grain boundary composition in grain boundary diffusion is analysed in detail. This leads to the general prediction that the grain boundary diffusion of solute and solvent will be reduced by strongly segregating solutes if they do not simultaneously enhance the bulk diffusivities. The converse occurs if the solute weakly segregates but strongly enhances the bulk diffusivities. The diffusion measurements are made in iron–tin alloys in the temperature range 563–750 °C by using radiotracers, and the segregation measurements, similarly, by Auger electron spectroscopy. The measured bulk diffusivities are similar to those found previously. The grain boundary diffusivities, determined via Suzuoka’s (1964) analysis, for iron and tin in pure iron have pre-exponential coefficients of 225 x 10 -4 and 9.2 x 10 -4 m 2 s -1 and activation energies of 165770 and 166600 J mol -1 respectively. Contrary to the increase in the bulk diffusivity produced by the ‘fast’ diffuser, tin, both grain boundary diffusivities are sharply reduced as the tin content rises. These and earlier results are interpreted through the effect of tin segregation on the grain boundary energy described by the theory of Borisov et al . (1964).

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“…After cach sectioning we counted the residual activity of the sample. The relation between activity and concentration [5] is expressed by the equation…”

Section: Penetration Plotsmentioning

confidence: 99%