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TSUKUDA, Makoto; Harada, Masayuki; Suzuki, Toshio; Koike, Susumu

doi:10.2464/jilm.28.109

Cited by 24 publications

(5 citation statements)

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“…Also, the time to peak hardness gets shorter at all aging temperatures, and the hardness of Al-10%Si-0.8%Mg alloy casting is larger than that of Al-10%Si-0.5%Mg alloy casting in all aging temperatures. M. Tsukuda 7) et al reported that the strengthening of Al-7 mass%Si alloy under T6 treatment occurred with the Mg addition up to 0.7 mass%. It is thought that the reason for difference of age hardening behavior in 0.5 mass%Mg and 0.8 mass%Mg containing alloys, the age precipitation hardening is promoted with the increasing of Mg content.…”

Section: Age Hardeningmentioning

confidence: 99%

Evaluation of Age Hardening Behavior Using Composite Rule and Microstructure Observation in Al-Si-Mg Alloy Castings

et al. 2011

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Al-Si hypoeutectic alloys have excellent castability and sufficient strength in combination with other alloying elements. Especially, Al-Si alloy containing Mg used for high-quality die-casting is well-known as a high strength alloy brought by the appropriate heat treatment and consequential precipitation hardening of Mg 2 Si intermediate phase. T6-heat treatment must be applied for maximum strength, but solution at high temperature and quenching treatment often conduct the product deformation and extra cost for fabrication. Therefore only artificial aging (T5-heat treatment) at comparatively lower temperature is mainly applied to industrial die-casting products. However, there are few studies on age hardening characteristics supplied by T5-heat treatment to Al-Si hypoeutectic alloys. To understand the age hardening behavior of Al-10 mass%Si-0.5 mass%Mg and Al-10 mass%Si-0.8 mass%Mg alloys in detail, microstructure observation and hardness measurement were performed. These alloys quenched in iced water, naturally aged at room temperature and artificially aged at 423-523 K, showed conspicuously age hardening behavior. Age hardening of Al-Si-Mg alloy generally considered to be the main cause of the precipitation-based hardening in phase, nevertheless it was seen that precipitation occurred in -Al+Si eutectic phase. Consequently, from the microstructure observation using SEM, it's thought that the age hardening of these alloys was mainly composed of the hardness change in -Al+Si eutectic phase.

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Section: Age Hardeningmentioning

confidence: 99%

Evaluation of Age Hardening Behavior Using Composite Rule and Microstructure Observation in Al-Si-Mg Alloy Castings

et al. 2011

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“…For example, the study of Haque et al [15] showed that maximum strength properties were obtained at~0.4 pct Mg for both sand and permanent mold castings. Tsukuda et al [16] showed that, in permanent molds, the ultimate tensile strength (UTS) and the yield strength (YS) of Na-modified alloys containing 0.2 pct and 0.006 pct Fe exponentially increased with Mg content up to 0.4 pct. In the same study, it also was reported that solution treatment and aging temperatures had a greater impact on the mechanical properties than Mg content.…”

Section: Introductionmentioning

confidence: 98%

“…However, using the information in the literature, a trend and estimations can be given for this relation. The studies discussed [15,16] showed that the maximum UTS and YS are obtained at 0.4 pct Mg, which corresponds to the maximum of 0.63 pct Mg 2 Si, assuming a sufficient amount of Si is present and that all supersaturated Mg is used. This implies that UTS and YS increase with the increase of Mg up to 0.4 pct or with the increase of amount of Mg 2 Si precipitates to approximately 0.63 pct.…”

Section: Introductionmentioning

confidence: 99%

Aging Effects on Heat Treatment Response and Mechanical Properties of Al-(1 to 13 pct)Si-Mg Cast Alloys

Apelian

Wang

2010

Metall Mater Trans B

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The effects of artificial aging time on the mechanical properties of Al-Si-Mg cast alloys were investigated as a function of Si content and morphology. Five alloys with Si ranging from 1 to 13 pct, unmodified and Sr-modified, were tested systematically in as-cast, T4, and T61 conditions with different aging times. The results indicated that the ultimate tensile strength (UTS) and the yield strength (YS) increased with increasing aging time, and that the YS increased more than the UTS. The increase was low during the first 2 hours, significantly increased after 2 hours, and slowed down at~10 hours; after 10 hours of aging, both UTS and YS remained nearly constant. The elongation decreased with increasing aging time. The decrease was observed from~2 hours to~14 hours, and no significant change was observed after~14 hours. In T61 conditions with different aging times, UTS increased up to 24 pct, whereas YS increased up to 88 pct. The Si level had significant effects on UTS, YS, and elongation. For all aging conditions, alloys with a higher Si level had higher UTS and YS. Si content increased alloys' response to aging. Si modification also increased YS. The changes in mechanical properties were correlated to the fundamentals of the formation and evolution of Mg 2 Si phase from forming clusters of Si atoms, GP zones, rod-like b¢ precipitates, and equilibrium Mg 2 Si platelets.

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“…[1] This element is known for contaminating Al-Si casting alloys and for being most deleterious with respect to the strength and toughness of the alloy, because it forms the needlelike b-Al 5 FeSi intermetallic phase during solidification. [2][3][4][5][6] Dissolution is the only practical method for reducing the presence of iron in aluminum. The solubility of iron in molten aluminum is high, leading to the eventual dissolution of ferrous material once it comes into contact with molten aluminum.…”

Section: Introductionmentioning

confidence: 99%

Precipitation of β-Al5FeSi Phase Platelets in Al-Si Based Casting Alloys

Liu

Mohamed

Samuel

et al. 2009

Metall Mater Trans A

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The aim of the present work has been to investigate the factors affecting the precipitation of the b-Al 5 FeSi iron intermetallic phase of directionally solidified A356-and 319-type alloys as a function of the iron content, a Sr addition of~250 ppm, and superheating or cooling rates. The iron levels selected varied from 0.12 to 0.8 wt pct and cover the range of Fe levels in commercial casting alloys. The use of an end-chill mold provided different cooling rates along the height of the same casting, with dendritic arm spacing values that varied from~15 to 85 lm, corresponding to levels of 5, 10, 30, 50, and 100 mm above the chill end. The microstructure and phase identification were monitored using optical microscopy, scanning electron microscopy (SEM), thermal analysis, and electron probe microanalysis (EPMA) techniques. An image analyzer was used in conjunction with the optical microscope for quantification purposes. The results showed that, for the range of cooling rates covered in the present study, the highest cooling rate (at a 5-mm distance from the chill) is the more significant parameter in controlling the size and distribution of theb-Al 2 FeSi intermetallic phase in the nonmodified 319 and 356 alloys. The addition of strontium leads to fragmentation of coeutectic or posteutectic b platelets. This effect diminishes with an increase in the iron concentration, and further strontium addition leads to the precipitation of Al 2 Si 2 Sr phase particles, instead.

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Cited by 24 publications

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Evaluation of Age Hardening Behavior Using Composite Rule and Microstructure Observation in Al-Si-Mg Alloy Castings

Evaluation of Age Hardening Behavior Using Composite Rule and Microstructure Observation in Al-Si-Mg Alloy Castings

Aging Effects on Heat Treatment Response and Mechanical Properties of Al-(1 to 13 pct)Si-Mg Cast Alloys

Precipitation of β-Al5FeSi Phase Platelets in Al-Si Based Casting Alloys

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