A thermodynamic description of the Al–Fe–Si system over the whole composition and temperature ranges via a hybrid approach of CALPHAD and key experiments

Du, Yong; Schuster, Julius C.; Liu, Zhe; Hu, Renjie; Nash, Philip; Sun, Weihua; Zhang, Weiwei; Wang, Jiong; Zhang, Lijun; Tang, Chengying; Zhu, Zhijun; Liu, Shuhong; Ouyang, Yifang; Zhang, Wenqing; Krendelsberger, Nataliya

doi:10.1016/j.intermet.2008.01.003

Cited by 188 publications

(102 citation statements)

References 30 publications

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“…This is also true for the ascast alloys Fe-74.5Al and Fe-74.9Al (see also Table 4). Table 3 Invariant reaction temperatures in the Al-rich part of the Fe-Al system as obtained from thermodynamic modelling based on the CALPHAD approach [30][31][32][33] Invariant reaction Reaction temperature from CALPHAD modelling,°C Seierstein [30] Du et al [31] Sundman et al [32] Jacobs and Schmid-Fetzer [33] L + FeAl M Fe 5 After heat treatment, in all cases precipitates of Fe 2 Al 5 were found (Fig. 5b) in accordance with the phase diagram.…”

Section: Liquidus and Invariantmentioning

confidence: 99%

“…For comparison, also calculated data from thermodynamic modelling applying the CALPHAD approach are given (Table 3). [30][31][32][33] Xiaolin Li and Frank Stein, Max Planck-Institut für Eisenforschung GmbH, Düsseldorf, Germany; Anke Scherf and Martin Heilmaier, Institute for Applied Materials (IAM-WK), Karlsruhe Institute of Technology (KIT), Karlsruhe, Germany. Contact e-mail: x.li@mpie.de.…”

Section: Introduction and Literature Reviewmentioning

confidence: 99%

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The Al-Rich Part of the Fe-Al Phase Diagram

Scherf

Heilmaier

et al. 2016

J. Phase Equilib. Diffus.

213

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The Al-rich part of the Fe-Al phase diagram between 50 and 80 at.% Al including the complex intermetallic phases Fe 5 Al 8 (e), FeAl 2 , Fe 2 Al 5 , and Fe 4 Al 13 was re-investigated in detail. A series of 19 alloys was produced and heat-treated at temperatures in the range from 600 to 1100°C for up to 5000 h. The obtained data were further complemented by results from a number of diffusion couples, which helped to determine the homogeneity ranges of the phases FeAl 2 , Fe 2 Al 5 , and Fe 4 Al 13 . All microstructures were inspected by scanning electron microscopy (SEM), and chemical compositions of the equilibrium phases as well as of the alloys were obtained by electron probe microanalysis (EPMA). Crystal structures and the variation of the lattice parameters were studied by x-ray diffraction (XRD) and differential thermal analysis (DTA) was applied to measure all types of transition temperatures. From these results, a revised version of the Al-rich part of the phase diagram was constructed.

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Section: Liquidus and Invariantmentioning

confidence: 99%

Section: Introduction and Literature Reviewmentioning

confidence: 99%

The Al-Rich Part of the Fe-Al Phase Diagram

Scherf

Heilmaier

et al. 2016

J. Phase Equilib. Diffus.

213

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“…Based on literature data [25][26][27] and experimental results, [28,29] the compound compositions and phase equilibria reported in this section were also used for the latest updates and assessments of the Al-Fe-Si system. [30][31][32][33] …”

Section: Introductionmentioning

confidence: 99%

Chemical Changes at the Interface Between Low Carbon Steel and an Al-Si Alloy During Solution Heat Treatment

Zhe

Dezellus

Gardiola

et al. 2011

J. Phase Equilib. Diffus.

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The aim of this work was to characterize the chemical changes during solid state solution heat treatment of a metallurgically bonded steel/Al-Si interface. For this purpose, low carbon steel plates covered with the A-S7G03 aluminium alloy (7 wt.% Si, 0.3 wt.% Mg analogous to A356) were prepared by dip coating, water-quenching to room temperature and reheating in the solid state at 480-560°C for 3-160 h. Upon reheating at 535°C, a reaction layer was observed to grow at the interface between steel and the iron-saturated Al-Si alloy. As long as an intimate contact could be maintained, the total thickness, x, of the reaction layer increased with time, t, according to a nearly parabolic growth law x 2 = KAEt 2 b. At 535°C, the value of the growth constant was K = 4.045310 214 m 2 s 21 . This constant was found to be thermally activated [K = K 0 exp(2Q/ RT)] with K 0 = 4.37310 24 m 2 s 21 and Q = 153 kJ mol 21 . The whole chemical interaction process was controlled by solid state volume diffusion and the reaction layer sequence corresponded to a diffusion path in the Al-Fe-Si phase diagram. A striking feature of the reaction process is the unbalanced diffusion of aluminium atoms through the reaction zone which rapidly results in the formation of Kirkendall voids. As these voids coalesce, solid state diffusion becomes more and more difficult and the steel/alloy bond gets weakened. Oxidation appears to be an aggravating factor, where applicable.

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“…Figure 2(a) shows the liquidus projection calculated by the unmodified default database of Thermo-Calc. Comparing this liquidus projection to that obtained from collected up-to-date references [26][27][28] to check the validity of the Thermo-Calc result, there was a considerable disagreement between the calculated and the collected results, especially in the region of high Fe alloys. In order to construct a thermodynamic database for precise calculated results, thermodynamic models (e.g., Gibbs free energy model and formula) and parameters (e.g., Gibbs free energy for pure standard state ( G) and interaction parameter (L)) were collected from the up-to-date references, [27][28][29][30][31] and proper thermodynamic data sets were carefully determined by evaluating the quality of the experimental and calculated thermodynamic results.…”

Section: Theoretical Predictionmentioning

confidence: 74%

“…20,21) More recently, experimental data for establishing the accurate phase equilibria of the ternary system were presented by Bosselet and Pontevichi [22][23][24][25] and Krendelsberger et al 26) Precise thermodynamic datasets of the ternary system were reasonably assessed by Liu and Du. 27,28) According to Du et al,28) the Al-Si-Fe ternary system is an extremely complex one with twenty seven ternary invariant reactions involving eleven stable ternary intermetallic compounds and a number of binary phases. Although many studies have continued to be performed, it is still tremendously difficult to predict the solidification path of high Fe-containing Al-Si alloys because of metastability, incomplete reactions, and solid-state reactions that are not well understood.…”

Section: Introductionmentioning

confidence: 99%

Prediction of Solidification Paths in Al-Si-Fe Ternary System and Experimental Verification: Part I. Fe-Containing Hypoeutectic Al-Si Alloys

2011

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The effects of Fe content and cooling rate on the solidification path and formation behavior of the Al 5 FeSi () phase in Fe-containing hypoeutectic Al-Si alloys were studied based on thermodynamic analysis and pertinent experiments. The thermodynamic calculations were performed using the Thermo-Calc program. For analyses in the high alloy region of the Al-Si-Fe ternary system, a thermodynamic database for Thermo-Calc was correctly updated and revised by the collected up-to-date references. For thermodynamics-based predictions of the solidification path in Fe-containing hypoeutectic Al-Si alloys, liquidus projection (including various invariant, monovariant, and bivariant reactions and isotherms) and equilibrium phase fraction were calculated as functions of composition and temperature in the Al-Si-Fe ternary system. The calculated results were compared to experimental results using various casting runs. In order to analyze the solidification path as a function of Fe content, two representative hypoeutectic Al-Si alloys with different Fe levels were designed. To better understand the influence of cooling rate on the formation behavior of the phase, the two alloys were solidified under slowly-and rapidly-cooled conditions, respectively. The cooling curves of the solidified alloys were recorded by thermal analysis and various important solidification events were detected using the first derivative of the cooling curves. Microstructures of the casting samples were studied by combined analyses of optical microscopy (OM) and scanning electron microscopy (SEM). For the slowly-cooled condition with the high Fe level, the primary phase enveloping the Al 8 Fe 2 Si () phase was mainly formed by the quasi-peritectic reaction of L + ! (Al) + (612 C). For the rapidly-cooled condition with the high Fe level, the primary phase with morphology of a curved needle was mainly formed by the reaction of L ! (Al) + (579612 C).

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A thermodynamic description of the Al–Fe–Si system over the whole composition and temperature ranges via a hybrid approach of CALPHAD and key experiments

Cited by 188 publications

References 30 publications

The Al-Rich Part of the Fe-Al Phase Diagram

The Al-Rich Part of the Fe-Al Phase Diagram

Chemical Changes at the Interface Between Low Carbon Steel and an Al-Si Alloy During Solution Heat Treatment

Prediction of Solidification Paths in Al-Si-Fe Ternary System and Experimental Verification: Part I. Fe-Containing Hypoeutectic Al-Si Alloys

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