Influence of Stresses on Precipitation

Sauthoff, Gerhard

doi:10.1051/jp4:1996109

Cited by 13 publications

(22 citation statements)

References 11 publications

(18 reference statements)

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“…[12] Unfortuit with Eq. [5]. nately, this value is not known explicitly when ␤ is a soluSimilar to the molar Gibbs energy diagrams used by tion phase.…”

Section: Ma Qianmentioning

confidence: 94%

“…In this article, using a constructed molar Gibbs energy diagram, a general description of the Gibbs-Thomson effect [5] in a dilute binary system is introduced for the case when both x ␣ B and x ␤ B can freely change with the size of ␤. As will Equation [5] is an exact Gibbs-Thomson expression valid be shown, this description is the same form as Eq.…”

Section: Ma Qianmentioning

confidence: 99%

“…When ␤ is not pure B, e.g., sions have been proposed or employed. These include [3][4][5][6][7][8][9][10][11] x ␣ B (r) ϭ x ␣…”

Section: Ma Qianmentioning

confidence: 99%

“…Equations [4] and [5], including their variations, have probably reflected all of the representative expressions must still equilibrate both activities, i.e., use a common tangent. [12] A generalized Gibbs-Thomson equation has reported to date for the Gibbs-Thomson effect in a dilute binary system.…”

Section: Ma Qianmentioning

confidence: 99%

“…However, Eq. [5] is restricted to a constant been given by Hillert [9] for this case based on a molar Gibbs energy diagram, i.e., Eq.…”

Section: Ma Qianmentioning

confidence: 99%

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The gibbs-thomson effect in dilute binary systems

Qian

2002

Metall Mater Trans A

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The solubility of a precipitate, which is commonly referred to as the composition of the matrix in equilibrium with the precipitate in the presence of a curved interface, has been well documented. For a pure precipitate ␤, which consists of component B, in an ␣ matrix that is a dilute solution of B in A, the Gibbs-Thomson effect is well known as [1,2] xwhere x ␣ B (r) and x ␣ B (ϱ) are the equilibrium atomic fractions of B in ␣ at a curved interface of a spherical precipitate (␤ ) of radius r and a planar interface, respectively. The term ␣␤ is the specific interfacial free energy, which is assumed to be isotropic and independent of precipitate size (r), and V ␤ m is the molar volume of ␤. When ␤ is not pure B, e.g., Fig. 3-The temperature dependence of the specific strength for the its composition is given by x ␤ B , a number of different exprestested alloyssions have been proposed or employed. These include [3][4][5][6][7][8][9][10][11] x

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“…[12] Unfortuit with Eq. [5]. nately, this value is not known explicitly when ␤ is a soluSimilar to the molar Gibbs energy diagrams used by tion phase.…”

Section: Ma Qianmentioning

confidence: 94%

Section: Ma Qianmentioning

confidence: 99%

“…When ␤ is not pure B, e.g., sions have been proposed or employed. These include [3][4][5][6][7][8][9][10][11] x ␣ B (r) ϭ x ␣…”

Section: Ma Qianmentioning

confidence: 99%

Section: Ma Qianmentioning

confidence: 99%

“…However, Eq. [5] is restricted to a constant been given by Hillert [9] for this case based on a molar Gibbs energy diagram, i.e., Eq.…”

Section: Ma Qianmentioning

confidence: 99%

See 3 more Smart Citations

The gibbs-thomson effect in dilute binary systems

Qian

2002

Metall Mater Trans A

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Analysis of the Combined Strengthening Effect of Solute Atoms and Precipitates on Creep of Aluminum Alloys

et al. 2020

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The creep strengthening mechanisms in (age-hardenable) aluminum alloys are analyzed on the basis of a new microstructural study of powder samples, an analysis of a comprehensive revision of creep data from the literature, and a new modeling approach. A strategy based on the strength difference (SD) method to separate the contributions of solid solution atoms and precipitates to creep strengthening is proposed. The new methodology considers the combination of the two contributions avoiding the need of a threshold stress term in the creep equation. The contribution of both precipitates and solid solution is taken into account by means of the analysis of the lattice parameter variation with aging time. For this study, powders of two commercial AA2xxx alloys have been analyzed using diffraction methods. The experimental results are modeled using Lubarda's approach combined with the SD method.

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Supersolvus Recrystallization and Grain Growth Kinetics for the Fine Tuning of Grain Size in VDM Alloy 780 Forgings

Haghighat¹,

Sharma

Gehrmann³

et al. 2023

Metall Mater Trans A

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VDM Alloy 780 is a new polycrystalline nickel-based superalloy developed for aeronautical applications. In most of the targeted applications, grain size after forging must be precisely controlled to meet the targeted mechanical properties and in-service life requirements. Grain size in forgings is the direct consequence of the recrystallization and grain growth kinetics which are addressed in this paper at high temperatures, above the solvus temperature of γ′ and η/δ phases. The dynamic and post-dynamic recrystallization kinetics as well as the grain growth kinetics of VDM Alloy 780 are detailed over a range of thermomechanical conditions. Dynamic recrystallization appears to be limited, with only 30 pct recrystallized at quite high strain of 1.7 applied at 1050 °C and 0.01 s−1 for instance, but this is compensated by fast post-dynamic evolution. Within the investigated thermomechanical range, recrystallization is completed with 5 minutes of post-deformation hold in VDM Alloy 780 independent of the prior strain, strain rate and dynamic recrystallization fraction. For a strain as low as 0.08, an isothermal annealing of 30 minutes at 1050 °C generates a homogenous and fully recrystallized microstructure. Capillarity driven grain growth following recrystallization is also relatively slow, for instance an exposure at 1050 °C (50 °C above the solvus temperature) for 2 hours results in an increase in average grain size from 20 to 70 μm. This opens the possibility to fine tune the grain sizes by subsequent heat treatments within a time scale that is compatible with industrial conditions. The high cobalt content (25 pct) is suspected to play a role in the control of microstructure evolution kinetics. It is noteworthy that VDM Alloy 780 is shown here to not undergo the heterogeneous grain growth phenomenon reported in low strain regions for other nickel-based superalloys, which is also an asset for applications requiring strict control of grain sizes and grain size distributions.

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Influence of Stresses on Precipitation

Cited by 13 publications

References 11 publications

The gibbs-thomson effect in dilute binary systems

The gibbs-thomson effect in dilute binary systems

Analysis of the Combined Strengthening Effect of Solute Atoms and Precipitates on Creep of Aluminum Alloys

Supersolvus Recrystallization and Grain Growth Kinetics for the Fine Tuning of Grain Size in VDM Alloy 780 Forgings

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