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Sujata, M; Bhargava, S.; Sangal, S.

doi:10.1023/a:1018509026596

Cited by 34 publications

(24 citation statements)

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“…Therefore, the formation of products in the reaction between TiAl and Al is Fig. 1 Micrograph of cross-section of the c-TiAl after hot-dip aluminizing not thermodynamically controlled even though the free energy of formation of TiAl 3 is higher than that of TiAl 2 [25]. It was suggested that the mechanism for the absence of phases other than TiAl 3 is caused by growth selection, which results from different diffusion fluxes in the competing phases [30].…”

Section: Resultsmentioning

confidence: 99%

“…Besides the above processes for developing TiAl 3 -rich coatings, hot-dip aluminizing should be a reliable commercial method for protection of c-TiAl based alloys against high temperature oxidation, considering that the methods for fabricating TiAl 3 based compounds by reaction synthesis from solid Ti and liquid Al have been reported in the literature [24][25][26]. Especially, the thick Al-rich barrier coatings from hot-dip aluminizing enable the c-TiAl based alloys to work for long-term at high temperatures without suffering the depletion of Al in the surface coatings.…”

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confidence: 99%

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Improvement of Oxidation Resistance of γ-TiAl at 900 and 1000 °C Through Hot-dip Aluminizing

et al. 2009

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Hot-dip aluminizing method and subsequent interdiffusion treatment were used to develop a TiAl 3 coating on Ti-45Al-2Cr-2Nb-0.15B (at.%) alloy. A two-phase coating consisting of an outer pure Al layer and an inner TiAl 3 layer formed on the alloy after the hot-dip and then a single phase TiAl 3 coating was obtained by using interdiffusion treatment. Oxidation of the TiAl 3 coating was conducted at 900 and 1000°C. Both the interrupt oxidation and the isothermal oxidation tests indicated that the coating provided high protectiveness for the alloy. The coating was stable for at least 300 h during the interrupt oxidation at 900 and 1000°C, and it was stable for at least 500 h at 1000°C and 1000 h at 900°C during the isothermal oxidation. The oxidation behavior of the coating was discussed in detail.

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Section: Resultsmentioning

confidence: 99%

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confidence: 99%

Improvement of Oxidation Resistance of γ-TiAl at 900 and 1000 °C Through Hot-dip Aluminizing

et al. 2009

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“…[31,32] The formation of Al 3 Ti was primarily expected during the reaction sintering. This compound together with Al 2 Ti and Al 2 Ti 5 has the lowest free energy of formation.…”

Section: A Structural Investigations Of Mil Compositesmentioning

confidence: 99%

“…This compound together with Al 2 Ti and Al 2 Ti 5 has the lowest free energy of formation. [31] However, it was reported that Al 2 Ti 5 and Al 2 Ti can be formed only through the solid state or solid-liquid reaction involving the AlTi compound. [31] Thus, it can be concluded that Al 3 Ti was the first phase, which formed during the reaction between liquid Al and solid Ti.…”

Section: A Structural Investigations Of Mil Compositesmentioning

confidence: 99%

Metal-Intermetallic Laminate Ti-Al3Ti Composites Produced by Spark Plasma Sintering of Titanium and Aluminum Foils Enclosed in Titanium Shells

Lazurenko

Mali

Батаев

et al. 2015

Metall Mater Trans A

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Metal-intermetallic laminate composites are considered as promising materials for application in the aerospace industry. In this study, Ti-Al 3 Ti composites enclosed in titanium cases were produced by reactive spark plasma sintering. Sintering was carried out at 1103 K and 1323 K (830°C and 1050°C) for 10 minutes. In both cases, high-quality Ti-Al 3 Ti composites containing thin transition layers at the interfaces were obtained. Al 2 Ti, AlTi, and AlTi 3 intermetallic phases and a solid solution of aluminum in titanium were observed in the transition layers by scanning and transmission electron microscopy. The material sintered at 1323 K (1050°C) had higher strength in comparison with the composite obtained at 1103 K (830°C). However, the hardness of the intermetallic component in the sample sintered at higher temperature decreased due to the grain growth. The impact toughness values of both materials were approximately identical.

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“…[1] is smaller than that of Ti 3 Al or TiAl 2 , indicating that TiAl grows more slowly than Ti 3 Al or TiAl 2 . The reasons for this slower growth rate of TiAl in comparison with the other two phases are because (1) the formation energy of TiAl is thermodynamically higher than those of other intermetallic phases at 800 ЊC to 1000 ЊC, [31,32] and (2) the forma- phases. This is also consistent with the diffusion-test results of van Loo and Rieck, [33] who reported that the k value of TiAl grown between Ti and TiAl 2 layers was smaller than Thus, the actual composition of Al in the total Ti/Al that grown between Ti 3 Al and TiAl 2 layers.…”

Section: Growth Behavior Of Interfacial Ti Aluminidesmentioning

confidence: 99%

Microstructural analysis of multilayered titanium aluminide sheets fabricated by hot rolling and heat treatment

Lee²,

Pyo³

et al. 2002

Metall Mater Trans A

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This study is concerned with the microstructural analysis of multilayered or bulk Ti aluminide sheets fabricated by the self-propagating high-temperature synthesis (SHS) reaction using hot rolling and heat treatment. Multilayered Ti/Al sheets were prepared by stacking thin Ti and Al sheets alternately, and a good Ti/Al interfacial bonding was achieved after rolling at 500 ЊC. When these sheets were held at 1000 ЊC, spheroidal TiAl 3 phases were formed by the SHS reaction at Ti/Al interfaces and inside Al layers. Microstructural analysis on the hot-rolled, multilayered Ti/TiAl 3 sheets revealed that intermetallic phases such as TiAl 2 , TiAl, and Ti 3 Al were formed at Ti/TiAl 3 interfaces due to interaction between Ti and TiAl 3 and that pores formed in the TiAl 3 layer were significantly reduced during hot rolling. When multilayered Ti/Ti aluminide sheets were heat treated at 1000 ЊC, Ti 3 Al, TiAl, and TiAl 2 were grown as Ti and TiAl 3 were consumed. As the heat treatment proceeded, TiAl grew further, eventually leading to the fabrication of multilayered sheets composed of Ti 3 Al and TiAl. Bulk Ti aluminide sheets, having a lamellar structure of Ti 3 Al and TiAl, instead of multilayered sheets, were also fabricated successfully by heat treatment at 1400 ЊC. This fabrication method of the bulk sheets had several advantages over the method by hot forging or rolling of conventional cast Ti aluminides. From these findings, an idea to fabricate multilayered or bulk Ti aluminide sheets by hot rolling and heat treatment is suggested as an economical and continuous fabrication method, and the formation and growth mechanisms of interfacial phases are elucidated in this study.

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Cited by 34 publications

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Improvement of Oxidation Resistance of γ-TiAl at 900 and 1000 °C Through Hot-dip Aluminizing

Improvement of Oxidation Resistance of γ-TiAl at 900 and 1000 °C Through Hot-dip Aluminizing

Metal-Intermetallic Laminate Ti-Al3Ti Composites Produced by Spark Plasma Sintering of Titanium and Aluminum Foils Enclosed in Titanium Shells

Microstructural analysis of multilayered titanium aluminide sheets fabricated by hot rolling and heat treatment

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