The Al-Zr (aluminum-zirconium) system

Murray, J. L.; Peruzzi, Andrea; Abriata, J. P.

doi:10.1007/bf02667556

Cited by 224 publications

(86 citation statements)

References 34 publications

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“…These measurements were performed using a SIGMATEST 2.069 (Foerster Instruments, Pittsburgh, PA) eddy current apparatus at room temperature. Five measurements were recorded, each corresponding to a different frequency (60,120,240,480, and 960 kHz), on each specimen. For consistency, a single specimen of each alloy (aged for various times) was used for conductivity measurements.…”

Section: B Aging Treatments and Analytical Techniquesmentioning

confidence: 99%

“…[60] The solubility limits of Ti and Zr in a-Al, in equilibrium with their respective metastable L1 2 structure Al 3 M trialuminides, have been evaluated employing ab initio calculations by Liu et al, [61,62] who show that the ratio of the solid solubilities of the stable and metastable phases may be written as…”

Section: B Classical Nucleation Theorymentioning

confidence: 99%

“…Fig. 7-Equilibrium Al-rich Al-Zr binary phase diagram (adapted from Murray [60] ) with metastable Al 3 Zr (L1 2 ) solvus calculated by Liu et al [61,62] Fig. 6-Equilibrium Al-rich Al-Ti binary phase diagram (adapted from Murray [59] ) with metastable Al 3 Ti (L1 2 ) solvus calculated by Liu et al [61,62] According to classical nucleation theory, [63][64][65][66][67] the steady-state nucleation current (nucleation rate per unit volume) is given by…”

Section: ½2mentioning

confidence: 99%

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Nucleation and Precipitation Strengthening in Dilute Al-Ti and Al-Zr Alloys

Knipling

Dunand

Seidman

2007

Metall Mater Trans A

175

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Two conventionally solidified Al-0.2Ti alloys (with 0.18 and 0.22 at. pct Ti) exhibit no hardening after aging up to 3200 hours at 375°C or 425°C. This is due to the absence of Al 3 Ti precipitation, as confirmed by electron microscopy and electrical conductivity measurements. By contrast, an Al-0.2Zr alloy (with 0.19 at. pct Zr) displays strong age hardening at both temperatures due to precipitation of Al 3 Zr (L1 2 ) within Zr-enriched dendritic regions. This discrepancy between the two alloys is explained within the context of the equilibrium phase diagrams: (1) the disparity in solid and liquid solubilities of Ti in a-Al is much greater than that of Zr in a-Al; and (2) the relatively small liquid solubility of Ti in a-Al limits the amount of solute retained in solid solution during solidification, while the comparatively high solid solubility reduces the supersaturation effecting precipitation during post-solidification aging. The lattice parameter mismatch of Al 3 Ti (L1 2 ) with a-Al is also larger than that of Al 3 Zr (L1 2 ), further hindering nucleation of Al 3 Ti. Classical nucleation theory indicates that the minimum solute supersaturation required to overcome the elastic strain energy of Al 3 Ti nuclei cannot be obtained during conventional solidification of Al-Ti alloys (unlike for Al-Zr alloys), thus explaining the absence of Al 3 Ti precipitation and the presence of Al 3 Zr precipitation.

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Section: B Aging Treatments and Analytical Techniquesmentioning

confidence: 99%

Section: B Classical Nucleation Theorymentioning

confidence: 99%

Section: ½2mentioning

confidence: 99%

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Nucleation and Precipitation Strengthening in Dilute Al-Ti and Al-Zr Alloys

Knipling

Dunand

Seidman

2007

Metall Mater Trans A

175

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“…We compare in table X the value of Ω obtained from our calculations to the ones obtained by a fit of the phase diagram through a Calphad approach 51,52 . …”

Section: Disordered Phasementioning

confidence: 99%

First-principles study of the solubility of Zr in Al

Clouet¹,

Sanchez²,

Sigli³

2002

Phys. Rev. B

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The experimental solubility limit of Zr in Al is well-known. Al3Zr has a stable structure DO23 and a metastable one L12. Consequently there is a metastable solubility limit for which only few experimental data are available. The purpose of this study is to obtain by ab-initio calculations the solubility limit of Zr in Al for the stable as well as the metastable phase diagrams. The formation energies of several ordered compounds AlxZr (1−x) , all based on an fcc underlying lattice, were calculated using the FP-LMTO (Full Potential Linear Muffin Tin Orbital) method. Taking into account all the relaxations allowed by the symmetry, we found the DO23 structure to be the stable one for Al3Zr. This set of results was then used with the cluster expansion in order to fit a generalized Ising model through the inverse method of Connolly-Williams. Different ways to consider volume relaxations were examined. This allowed us to calculate in the Bragg-Williams approximation the configurational free energy at finite temperature. According to the previous FP-LMTO calculations the free energy due to electronic excitations can be neglected. For the vibrational free energy of ordered structures we compared results obtained from a calculation of the elastic constants used with the Debye model and results obtained from a calculation of the phonon spectrum. All these different steps lead to a calculation of the solubility limit of Zr in Al which is found to be lower than the experimental one. The solubility limit in the metastable phase diagram is calculated in the same way and can thus be compared to the stable one.

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“…1 is one of the most complicated of all the transition metal aluminide binary phase diagrams [11]. According to the evaluation of Murray et 3 ; all of which experimentally are found to have extremely narrow concentration ranges [12]. Two of them Al 4 Zr 5 and Al 3 Zr 5 are high-temperature phases.…”

Section: Introductionmentioning

confidence: 99%

Enthalpy of formation of intermetallic phases from Al–Zr system determined by calorimetric solution method

Maciąg

2017

J Therm Anal Calorim

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Intermetallic phases represent a group of materials of unique properties. Many of those materials have found practical application, whereas others are still intensively examined. There are ten stable intermetallic phases in Al-Zr system, among which few are prospective materials to work at elevated temperature, nuclear reactors, etc. On top of that, researches are focused on obtaining amorphous phases, nanoparticles and zirconium-based pressure pipes covered with aluminum. As a result, better understanding of thermal effects accompanying those compounds formation becomes crucial. In this paper, solution calorimetry method was used for determination of formation enthalpy D f H of intermetallic phases from Al-Zr system at room temperature (298 K). Experiments were conducted using test station built by author. Material used as bath was aluminum. Additionally, alloys preparation methodology was described and presented. Calorimetric measurements were taken on phases: Al 3 Zr, Al 2 Zr, Al 3 Zr 2 , AlZr, Al 2 Zr 3 , AlZr 2 and AlZr 3 . Heat of dissolution of zirconium in aluminum bath at temperature 1073 K was determined experimentally and was equal to -244.5 ± 5.4 kJ mol -1 . Obtained results of enthalpy of formation were summarized and compared with the literature data.

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The Al-Zr (aluminum-zirconium) system

Cited by 224 publications

References 34 publications

Nucleation and Precipitation Strengthening in Dilute Al-Ti and Al-Zr Alloys

Nucleation and Precipitation Strengthening in Dilute Al-Ti and Al-Zr Alloys

First-principles study of the solubility of Zr in Al

Enthalpy of formation of intermetallic phases from Al–Zr system determined by calorimetric solution method

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