Composition and solidification microstructure selection in the interdendritic matrix between primary Al3Fe dendrites in hypereutectic AlFe alloys

Dong, Liang; Korgul, P.; Jones, H.

doi:10.1016/1359-6454(95)00381-9

Cited by 32 publications

(13 citation statements)

References 17 publications

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“…Construction design details of this unit are given elsewhere. [37,38] The drive mechanism of the furnace operating chamber was started after the temperature had stabilized at 1723 K for Fe-C, 1143 K for Al-Si, and 1243 K for Al-Fe alloys. The temperature gradient values in the liquid metal just preceding the solid-liquid interface are given in Table III.…”

Section: Test Results and Their Analysismentioning

confidence: 99%

Modeling structure parameters of irregular eutectic growth: Modification of Magnin-Kurz theory

Guzik

Kopyciński

2006

Metall Mater Trans A

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A new approach to irregular eutectic growth (faceted/nonfaceted crystallization) in Fe-C and Al-Si alloys has been presented in this article. The results of unidirectional crystallization of the irregular eutectic in the Fe-C, Al-Si, and Al-Fe systems were used for the experimental verification of the resulting model. For the oriented graphite, a(Al)-Si and a(Al)-Al 3 Fe eutectics, a decrease of the interlamellar spacing l and in protrusion d b of the nonfaceted phase (austenite, a(Al)) by the leading faceted phase (graphite, silicon, and Al 3 Fe), the increase of growth rate v was observed. The MagninKurz theory of irregular eutectic growth has been modified in order to better understand the physical mechanisms driving the crystallization process. A comparison of the measured and calculated average l values has revealed good agreement for the (g)Fe-graphite, a(Al)-Si, and a(Al)-Al 3 Fe eutectics. The developed model also considered the influence of the material constants of the examined alloys on the interlamellar spacing and protrusion of the leading phase-graphite, silicon, and Al 3 Fe. It has been found that material constants such as the wetting angle, diffusion coefficient, and GibbsThomson coefficient are of great importance in this eutectic growth.

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Section: Test Results and Their Analysismentioning

confidence: 99%

Modeling structure parameters of irregular eutectic growth: Modification of Magnin-Kurz theory

Guzik

Kopyciński

2006

Metall Mater Trans A

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“…[1] The effect of some ternary additions on the formation of Al-Al 3 Fe, Al-Al 6 Fe, Al-Al x Fe, and Al-␣AlFeSi eutectics in Bridgman grown Al-3 wt pct Fe based alloy was reported previously, together with associated growth morphologies and the eutectic spacing vs growth velocity relationship for the Al-Al x Fe eutectic in Al-2.85 wt pct Fe-0.12 wt pct V. [2,3,4] The present contribution reports corresponding measurements of growth temperature T G vs growth velocity V for the same alloy for the velocity range 0.1 to 0.71 mm/s over which Al-Al x Fe eutectic was the sole product of solidification. [14] from the transition velocity to displace Al-Al 3 Fe by Al-Al x Fe eutectic, and B EU is similar in magnitude to val- Table II from thermal analysis or from phase diagram assessments. [5,6] The results shown in Table I and plotted as T G vs V 1/2 in Figure 1 confirm the expected relationship: [7] T EU Ϫ T G ϭ B EU V 1/2 [1] (temperature T G2 in Table I the experimental data.…”

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confidence: 75%

“…Each value tabulated is the mean of three separate measurements, and the standard deviation of these measurements is indicated. Table II compares these values with available published data [8][9][10][11][12][13][14][15][16][17][18] for the competing eutectics and some related Al-based eutectics. [1] The effect of some ternary additions on the formation of Al-Al 3 Fe, Al-Al 6 Fe, Al-Al x Fe, and Al-␣AlFeSi eutectics in Bridgman grown Al-3 wt pct Fe based alloy was reported previously, together with associated growth morphologies and the eutectic spacing vs growth velocity relationship for the Al-Al x Fe eutectic in Al-2.85 wt pct Fe-0.12 wt pct V. [2,3,4] The present contribution reports corresponding measurements of growth temperature T G vs growth velocity V for the same alloy for the velocity range 0.1 to 0.71 mm/s over which Al-Al x Fe eutectic was the sole product of solidification.…”

mentioning

confidence: 99%

“…The experimental method involved quenching the Bridgman sample shortly after the growth front had passed a pair of calibrated embedded thermocouples, some 3 mm apart, allowing T G to be determined from the relative separations of the thermocouple beads and the growth front on a longitudinal section made subsequently. [12][13][14][15][16][17] A particular encouraging feature is that the val-ues [6,[8][9][10][11] for the other Al-based eutectics listed in Table II. Table II compares these values with available published data [8][9][10][11][12][13][14][15][16][17][18] for the competing eutectics and some related Al-based eutectics.…”

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confidence: 99%

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Effect of growth velocity on the growth temperature of the Al-AlxFe eutectic in Al-2.85Fe-0.12V alloy

Wang

Jones

2001

Metall Mater Trans A

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is small and the concentration of dissolved nitrogen exceeds the solubility limit in the melt containing the given content of Ti. The second possibility is rejection of the solutes, Ti and N, into the liquid region at the solidifying interface, their accumulation in the intercellular region, and precipitation of TiN on the cell boundaries during and after resolidification. Since the physical processes in LSM are highly complicated [8] and relevant thermodynamic data at high temperatures were not found in the literature, it is presently uncertain which mechanism of TiN formation in the Ni-base alloy 600 would be applicable under the present experimental conditions. The solid solubilities of Mg and S in Ni are known to be negligible. [9] Therefore, the two elements preferentially segregated on the cell boundaries during solidification are expected to precipitate as MgS with a low freeenergy formation, [10] even though the original contents of Mg and S are low, i.e., only 80 and 20 ppm in the 600H specimen, respectively. Fig. 5-Bright-field image of TiN and MgS, showing a parallel Moire pattern due to ⌬g ϭ 200 TiN Ϫ 200 MgS .

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“…The morphology of the primary phase of Al 13 Fe 4 is plate-like, needle-like, or star-shaped under the conventional melting and casting of the hypereutectic composition of the alloys [10]. The morphology of star-shaped Al 13 Fe 4 could be modified to rectangular or hexagonal morphology by a small addition of Mg [11].…”

Section: Selection Of Matrix Alloymentioning

confidence: 99%

Combination of reinforcing powders and matrix alloys for fabrication of aluminum matrix composites by plasma synthesis method

et al. 2003

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Several kinds of powders and aluminum alloys are adopted to study the feasibility of the fabrication of aluminum matrix composites through plasma synthesis. Some powders do not incorporate into the molten aluminum due to reflection on the melt surface and dissolution in the plasma arc. On the contrary, iron powders are well incorporated into the molten aluminum. The iron powders incorporated into the molten aluminum make angular Al 13 Fe 4 intermetallic compounds in the matrix. In addition, some portion of iron powders dissolve into the matrix and change the microstructures of the matrix alloys. The effects of dissolved Fe on the microstructures and mechanical properties of the composites are examined.

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Composition and solidification microstructure selection in the interdendritic matrix between primary Al3Fe dendrites in hypereutectic AlFe alloys

Cited by 32 publications

References 17 publications

Modeling structure parameters of irregular eutectic growth: Modification of Magnin-Kurz theory

Modeling structure parameters of irregular eutectic growth: Modification of Magnin-Kurz theory

Effect of growth velocity on the growth temperature of the Al-AlxFe eutectic in Al-2.85Fe-0.12V alloy

Combination of reinforcing powders and matrix alloys for fabrication of aluminum matrix composites by plasma synthesis method

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