Low-Temperature Elastic Moduli of Aluminum

Kamm, G. N.; Alers, G. A.

doi:10.1063/1.1713309

Cited by 317 publications

(104 citation statements)

References 12 publications

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“…% Ga is also plotted. The Poisson's ratios of aluminum 91,92 , austenitic steel 93 , α-Fe 94 and diamond 95,96 are plotted for comparison. 97 α-Pu, β-Pu and γ-Pu (and δ-Pu 2.36 at.…”

Section: Datamentioning

confidence: 99%

Temperature dependence of elastic moduli of polycrystalline β plutonium

et al. 2011

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The elastic moduli of pure polycrystalline beta plutonium were measured over its full range of existence (417 K to 491 K) using resonant ultrasound spectroscopy. The Debye temperature (138 K), Poisson's ratio (0.28), Grüneisen parameter (2.3), and the zerotemperature atomic volume (21.2 Å 3 ) were computed from the measurements. Both bulk and shear moduli decrease smoothly on warming with expected discontinuities at the phase boundaries. The shear modulus is surprisingly nearly the same for beta and gamma Pu. The temperature dependence of bulk moduli for beta Pu is, like gamma Pu, unusually small. Poisson's ratio shows very strong differences among alpha, beta, and gamma Pu indicating they are entirely different metals. The zero-temperature elastic moduli were computed for the three phases as well as for gallium-stabilized delta Pu (also measured by us) and compared to calculations.PACS numbers: 62.20. de, 63.70.+h, 65.40.G-, 62.20.dj

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“…% Ga is also plotted. The Poisson's ratios of aluminum 91,92 , austenitic steel 93 , α-Fe 94 and diamond 95,96 are plotted for comparison. 97 α-Pu, β-Pu and γ-Pu (and δ-Pu 2.36 at.…”

Section: Datamentioning

confidence: 99%

Temperature dependence of elastic moduli of polycrystalline β plutonium

et al. 2011

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“…As an example, we summarize in Figure 1 published experimental data on the adiabatic C 12 elastic constant of fcc aluminum as a function of temperature from four different studies [2][3][4][5] . In these studies, the elastic constants were determined by identifying the resonant frequencies of single crystalline specimens within the kHz-to-MHz range.…”

Section: Introductionmentioning

confidence: 99%

“…Based on the published experimental results [2][3][4][5] alone, it is impossible to determine a priori which of the published data most accurately represents the actual thermo-elastic behavior of fcc aluminum. Moreover, the puzzling hardening of C 12 reported by Tallon 5 , if true, may indicate unexpected significant anharmonic phenomena in a metal that is normally considered to be slightly anharmonic at most.…”

Section: Introductionmentioning

confidence: 99%

Finite-temperature elasticity of fcc Al: Atomistic simulations and ultrasonic measurements

et al. 2011

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Though not very often, in literature there are cases where discrepancies exist in temperature dependence of elastic constants of materials. A particular example of this case is the behavior of C 12 coefficient of a simple metal, aluminum. Here, we attempt to provide insight into various contributions to temperature-dependence in elastic properties by investigating the thermo-elastic properties of fcc aluminum as a function of temperature through the use of two computational techniques and experiments. First, ab initio calculations based on density functional theory (DFT) are used in combination with quasi-harmonic theory to calculate the elastic constants at finite temperatures through a strain-free energy approach. Molecular dynamics (MD) calculations using tight-binding potentials are then used to extract the elastic constants through a fluctuation-based formalism. Through this dynamic approach, the different contributions (Born, kinetic and stress fluctuations) to the elastic constants are isolated and the underlying physical basis for the observed thermally-induced softening is elucidated. The two approaches are then used to shed light on the relatively large discrepancies in the reported temperature dependence of the elastic constants of fcc aluminum. Finally, the polycrystalline elastic constants (and their temperature dependence) of fcc aluminum are determined using Resonant Ultrasound Spectroscopy (RUS) and compared to previously published data as well as the atomistic calculations performed in this work.

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“…The variations in elastic constants of a single crystalline aluminum with temperature have been determined experimentally [16][17][18][19] and computationally [20]. The isotropic elastic moduli for a polycrystalline aggregate can be estimated using the Voigt or Reuss models.…”

mentioning

confidence: 99%

“…The isotropic elastic moduli for a polycrystalline aggregate can be estimated using the Voigt or Reuss models. The shear modulus µ and Poisson's ratio ν of polycrystalline aluminum are calculated using the experimental data given by Kamm and Alers [17] and Gerlich and Fisher [18] (Fig. 1).…”

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confidence: 99%

Temperature dependence of the yield strength of aluminum thin films: Multiscale modeling approach

Davoudi

2017

Scripta Materialia

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Modeling deformation at elevated temperatures using discrete dislocation dynamics (DDD) is a recent area of high interest. However, the literature dedicated to this subject fails to address the variations of DDD parameters with temperature. This study aims to investigate the effect of temperature on the yield strength of aluminum thin films in two-dimensional DDD simulations. To this end, the temperature dependence of DDD parameters has been studied using molecular dynamics, three-dimensional DDD simulations, and the existing experimental results. Based on these calculations, we observed 18% decrease in the yield strength when temperature was increased from 100 K to 600 K. Discrete dislocation dynamics (DDD) is a powerful tool that has been successfully applied to simulate plastic deformation in crystalline materials specially at the micron and submicron scales in various modeling problems. In this method, the material is modeled as a continuous medium containing dislocations as the main plastic carriers, where evolution of dislocations is tracked. In the formulation of the DDD approach, it is assumed that the motion of a dislocation of unit length is governed by:where v is the dislocation velocity, m * is the effective mass, B is the drag coefficient, and F(t) is the driving force arising from externally applied stresses, image stresses, self-stress, interactions with other defects, and the lattice friction (Peierls stress). In this method, long range interactions between dislocations are calculated through theory of elasticity; short range interactions are determined based on local rules.DDD is implemented either in two-or three-dimensional frameworks. Three-dimensional DDD (3d DDD) includes dislocations in realistic geometries and many dislocation phenomena such as junction formation and cross-slip. 2d simulations include only infinitely long edge dislocations.In 2d approach, Frank-Read (FR) sources are represented by points; when the resolved shear stress exceeds a prescribed nucleation stress during a period of time, called nucleation time, the *

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Low-Temperature Elastic Moduli of Aluminum

Cited by 317 publications

References 12 publications

Temperature dependence of elastic moduli of polycrystalline β plutonium

Temperature dependence of elastic moduli of polycrystalline β plutonium

Finite-temperature elasticity of fcc Al: Atomistic simulations and ultrasonic measurements

Temperature dependence of the yield strength of aluminum thin films: Multiscale modeling approach

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