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Vandermeer, R.A.; Jensen, D. Juul

doi:10.1023/a:1008668604733

Cited by 61 publications

(41 citation statements)

References 7 publications

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“…But, V V , isn't enough for define nucleation mode. In this way, for studies of recrystallization, was developed microstructural path (MP) by Gokhale and DeHoff 16 , connect area per unit of volume, S V , with V V and after extended by Vandermeer and coauthors [17][18][19][20] . MP which may be written as…”

Section: Introductionmentioning

confidence: 99%

Sigma Phase in Superduplex Stainless Steel: Formation, Kinetics and Microstructural Path

et al. 2017

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The superduplex stainless steels (SDSS) are widely used in chemical, oil and gas industries, to pipelines and storage material facilities. In welding process or working in temperature elevated, secondary phases may appear in the form of precipitates, as the sigma phase (σ) which is an intermetallic compound. This compound is harmful to the properties of steel, deteriorating its mechanical properties, such as decreasing corrosion resistance and toughness. In this paper it is analyzed the formation, kinetics and microstructural evolution of sigma phase in SDSS UNS S32750 after isothermal aging at 700ºC, 750ºC and 800ºC. In this work sigma phase kinetics is studied by JMAK theory and by two microstructural path descriptors, S V , interfacial area per unit of volume between sigma phase and austenite, and <λ>, mean chord length of sigma, both in function of the V V , volumetric fraction of sigma, known in the literature as microstructural partial path (MP). The MP formulation is common in recrystallization studies, but so far has not been used in the sigma phase precipitation studies, being applied here for the first time. The results indicated that the sigma phase nucleates by site saturation with anisotropic linear impingement. This means that sigma phase nucleates on edges.

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Section: Introductionmentioning

confidence: 99%

Sigma Phase in Superduplex Stainless Steel: Formation, Kinetics and Microstructural Path

et al. 2017

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“…Only a combination of pre-existing nuclei and a decreasing growth rate at constant temperature leads to such low values of n. Indeed, decreasing growth rates have been observed experimentally. [15][16][17] At late stages of recrystallization, the recrystallization rate drops, causing the slope in the double-logarithmic plot to decrease. This behavior cannot be explained by a growth rate that is continuously decreasing exponentially with time, [3] since this would lower the slope in doublelogarithmic plots for the entire recrystallization, and not only for late stages.…”

Section: A Kineticsmentioning

confidence: 99%

The Kinetics of and the Microstructure Induced by the Recrystallization of Copper

Jägle

Mittemeijer

2011

Metall Mater Trans A

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The kinetics of the recrystallization of pure copper was investigated by differential scanning calorimetry (DSC). The associated microstructural change was characterized by electron backscatter diffraction imaging (EBSD), by analyzing deformed specimens before recrystallization and specimens after partial recrystallization and after completed recrystallization. The experimental results acquired by the two methods were compared with each other and discussed in the context of the available body of literature results. The observed kinetics deviate from Johnson-Mehl-Avrami-Kolmogorov (JMAK)-like behavior. The observed grain-area distribution is unusually broad and skewed toward large grains. Comparison with mesoscopic, geometric simulations showed that previously proposed (simple) models fail to correctly describe the microstructure resulting from recrystallization, although they can successfully model the recrystallization kinetics. It was concluded that the experimental results on both the kinetics and the microstructure can be reconciled employing a recrystallization model incorporating ongoing (i.e., beyond time t = 0) nucleation and accounting for the inhomogeneous nature of the deformed material.

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“…5), this value is surprisingly close to literature values of 172-217 kJ/mol. 18,19) As the deformed matrix is fairly homogeneous neither large changes in misorientation between the growing grain and the matrix or big changes in driving force can be the reason for the observed stop-go type boundary migration. This result is substantiated by very recent EBSP observations of deformed Ni.…”

Section: Growth Of Grains During Recrystallizationmentioning

confidence: 99%

Time Evolution in 3D Metal Microstructures — Recrystallization

Jensen

Schmidt

2009

Mater. Trans.

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The three dimensional x-ray diffraction (3DXRD) concept is shortly described and new experimental updates are highlighted. The potentials and limitation of the 3DXRD method are compared to those of other 3D methods. 3DXRD has been used for in-situ studies of recrystallization and new migration rate results are presented. Migration mechanism for boundary segments surrounding a recrystallizing grain are described and discussed.

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Untitled

Cited by 61 publications

References 7 publications

Sigma Phase in Superduplex Stainless Steel: Formation, Kinetics and Microstructural Path

Sigma Phase in Superduplex Stainless Steel: Formation, Kinetics and Microstructural Path

The Kinetics of and the Microstructure Induced by the Recrystallization of Copper

Time Evolution in 3D Metal Microstructures — Recrystallization

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Untitled

Cited by 61 publications

References 7 publications

Sigma Phase in Superduplex Stainless Steel: Formation, Kinetics and Microstructural Path

Sigma Phase in Superduplex Stainless Steel: Formation, Kinetics and Microstructural Path

The Kinetics of and the Microstructure Induced by the Recrystallization of Copper

Time Evolution in 3D Metal Microstructures &mdash; Recrystallization

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Product

Resources

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Time Evolution in 3D Metal Microstructures — Recrystallization