Discontinuous mode of dissolution of a β phase precipitate into α Cu-Cd solid solutions

Sulonen, M.S.

doi:10.1016/0001-6160(60)90197-8

Cited by 71 publications

(15 citation statements)

References 3 publications

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“…In such a way, time for the go distance should be ca. τ go = 4-6 s. The same analysis made for the Cu-Cd [4]) provided the average distance between two successive "ghost lines" ca. 1.0 and 1.25 µm, respectively.…”

Section: Discussionmentioning

confidence: 94%

“…Besides the "ghost lines," the "ghost traces" at the places where the β phase lamellae had previously existed were also revealed after DD process by means of optical microscopy [4,5], scanning [6,7] and transmission electron microscopy [8,9]. They show strong enhancement of solute concentration as confirmed by an energy-dispersive X-ray microanalysis [9,10].…”

Section: Introductionmentioning

confidence: 82%

“…1.0 and 1.25 µm, respectively. This can only be compared with the average velocities 88 and 417 nm/s determined by measurements receding distances of the RF versus time of dissolution [4]. The resulting time is between 11 and 3 s. Obviously, for all the above-discussed cases the real go time should be much shorter as the average DD velocity takes into account both go-and-stop periods.…”

Section: Discussionmentioning

confidence: 99%

“…In the case of diffusion-induced grain boundary migration (DIGM) [3] or discontinuous dissolution (DD) [4][5][6][7][8][9][10], the go-and-stop movement is frequently manifested by the presence of so-called "ghost images" (Fig. 1) existing in the regions swept by the migrating RF after etching with concentration-sensitive etchant.…”

Section: Introductionmentioning

confidence: 99%

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On the go-and-stop motion of the discontinuous precipitation front

Chronowski

Zięba

2020

Archiv.Civ.Mech.Eng

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The growth of lamellar structure during discontinuous precipitation occurs frequently by so-called go-and-stop fashion. The results of simulation combined with the changes of Cahn's parameter C revealed two types of such motion. The process takes place in the successive stages which can be distinguished judging from the value of C parameter. For lower values of linear growth rate (v = 10÷20 nm/s) and smaller α lamella thickness (100÷200 nm), the full cycle with relaxation takes 4-6 s. The faster movement of the reaction front (v = 30 nm/s) resulted in dramatic decrease of the full cycle to τ total = 0.8 s. The same behavior is observed if the α lamella thickness increases beyond 200 nm at constant v equal to 10 nm/s. Both predicted types of go-and-stop motion can experimentally be observed during growth or dissolution of discontinuous precipitates. What is the reason that particular type prevails is unknown, and this is invitation for further studies especially using high-resolution transmission electron microscope operating in in situ mode.

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Section: Discussionmentioning

confidence: 94%

Section: Introductionmentioning

confidence: 82%

Section: Discussionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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On the go-and-stop motion of the discontinuous precipitation front

Chronowski

Zięba

2020

Archiv.Civ.Mech.Eng

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“…The elastic mechanism appears to have been first proposed in about 1960 by Sulonen [8] who says [9], "A zone, impoverished or enriched in solute ... is formed ahead of the .. interface as a result of rapid grain boundary diffusion ... . This zone ... is subjected to ... lattice misfit stresses...…”

Section: Introductionmentioning

confidence: 99%

On the elastic driving force in diffusion-induced grain boundary motion

Penrose

2004

Acta Materialia

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In 1983 Hillert obtained the formula Y η 2 (c + −c − ) 2 for the driving force per unit area of grain boundary arising from elastic misfit in an isotropic alloy, where the mole fractions c + and c − on the two sides of the grain boundary are small, η is a measure of the elastic misfit and Y = E/(1 − ν) where E is Young's modulus and ν is Poisson's ratio. It is shown here that the formula is still valid (with suitably defined Y, η) when c + , c − are not small. The formula for Y in a general anisotropic solid is given. The physical origin of the elastic force on the grain boundary is considered, with help from the 'energy-momentum tensor' devised by Eshelby to quantify the forces on other crystal imperfections such as dislocations. The theory also makes a prediction about the direction of motion of an initially stationary grain boundary.

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