Structural Changes of High-Temperature Nickel Alloy Containing Rhenium and Lanthanum on Heat Treatment; Steel in Translation; Vol. 48, iss. 4
| Parent link: | Steel in Translation Vol. 48, iss. 4.— 2018.— [P. 214-218] |
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| Korporativní autor: | |
| Další autoři: | , , , , |
| Shrnutí: | Title screen The properties of high-temperature nickel alloys for manufacturing depend on the thermal stability of the structure, the particle size, the shape, the quantity of strengthening γ' phase, and the strength of the γ solid solution. Such alloys are strengthened by the addition of rhenium and lanthanum. In the present work, the structure and phase composition of high-temperature nickel alloy with added rhenium (0.4 at %) and lanthanum (0.006 at %) are qualitatively and quantitatively investigated. The methods employed are transmission diffraction electron microscopy and scanning electron microscopy. The alloy structure is considered in three states: after directed crystallization (the initial state, sample 1); after directed crystallization, annealing at 1150°C for 1 h, and annealing at 1100°C for 480 h (sample 2); and after directed crystallization, annealing at 1150°C for 1 h, and annealing at 1100°C for 1430 h (sample 3). Primary and secondary phases are observed in the superalloy. The primary phases are Y' and Y. They form the structure of the alloy and are present in the form of Y' quasi-cuboids separated by Y layers. The secondary phases due to the presence of rhenium and lanthanum are [beta] NiAl, AlRe, NiAl2Re, [sigma], x, and Ni3La2. The secondary phases seriously disrupt the structure of the Y+Н' quasi-cuboids. The rhenium and lanthanum do not uniformly fill the whole alloy volume, but only appear in local sections. Therefore, in all three states of the alloy, only some volume of Y+Y' quasicuboids is disrupted. Analysis of the secondary phases' morphology shows that the σ particles are thin needles, whereas the Ni3La2 particles have internal structure with characteristic contrast and are relatively thick. Interestingly, the [sigma] phase and Ni3La2 are deposited at the same locations. The introduction of rhenium and lanthanum changes the phase composition of the alloy, suppressing the formation of Y phase. The particles of secondary phase are localized in individual sections of the alloy with specific periodicity. The secondary phases are refractory: the melting point is about 1600°C for [beta] phase, 2600°C for [sigma] phase; and 2800° for x phase. Thanks to the formation of refractory secondary phases and their periodic distribution in the structure, the strength of the superalloy with added rhenium and lanthanum is increased. Режим доступа: по договору с организацией-держателем ресурса |
| Jazyk: | angličtina |
| Vydáno: |
2018
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| Témata: | |
| On-line přístup: | https://doi.org/10.3103/S0967091218040095 |
| Médium: | Elektronický zdroj Kapitola |
| KOHA link: | https://koha.lib.tpu.ru/cgi-bin/koha/opac-detail.pl?biblionumber=663973 |
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| 200 | 1 | |a Structural Changes of High-Temperature Nickel Alloy Containing Rhenium and Lanthanum on Heat Treatment |f E. L. Nikonenko, N. A. Popova, N. R. Sizonenko [et al.] | |
| 203 | |a Text |c electronic | ||
| 300 | |a Title screen | ||
| 320 | |a [References: p. 218 (20 tit.)] | ||
| 330 | |a The properties of high-temperature nickel alloys for manufacturing depend on the thermal stability of the structure, the particle size, the shape, the quantity of strengthening γ' phase, and the strength of the γ solid solution. Such alloys are strengthened by the addition of rhenium and lanthanum. In the present work, the structure and phase composition of high-temperature nickel alloy with added rhenium (0.4 at %) and lanthanum (0.006 at %) are qualitatively and quantitatively investigated. The methods employed are transmission diffraction electron microscopy and scanning electron microscopy. The alloy structure is considered in three states: after directed crystallization (the initial state, sample 1); after directed crystallization, annealing at 1150°C for 1 h, and annealing at 1100°C for 480 h (sample 2); and after directed crystallization, annealing at 1150°C for 1 h, and annealing at 1100°C for 1430 h (sample 3). Primary and secondary phases are observed in the superalloy. The primary phases are Y' and Y. They form the structure of the alloy and are present in the form of Y' quasi-cuboids separated by Y layers. | ||
| 330 | |a The secondary phases due to the presence of rhenium and lanthanum are [beta] NiAl, AlRe, NiAl2Re, [sigma], x, and Ni3La2. The secondary phases seriously disrupt the structure of the Y+Н' quasi-cuboids. The rhenium and lanthanum do not uniformly fill the whole alloy volume, but only appear in local sections. Therefore, in all three states of the alloy, only some volume of Y+Y' quasicuboids is disrupted. Analysis of the secondary phases' morphology shows that the σ particles are thin needles, whereas the Ni3La2 particles have internal structure with characteristic contrast and are relatively thick. Interestingly, the [sigma] phase and Ni3La2 are deposited at the same locations. The introduction of rhenium and lanthanum changes the phase composition of the alloy, suppressing the formation of Y phase. The particles of secondary phase are localized in individual sections of the alloy with specific periodicity. The secondary phases are refractory: the melting point is about 1600°C for [beta] phase, 2600°C for [sigma] phase; and 2800° for x phase. Thanks to the formation of refractory secondary phases and their periodic distribution in the structure, the strength of the superalloy with added rhenium and lanthanum is increased. | ||
| 333 | |a Режим доступа: по договору с организацией-держателем ресурса | ||
| 461 | |t Steel in Translation | ||
| 463 | |t Vol. 48, iss. 4 |v [P. 214-218] |d 2018 | ||
| 610 | 1 | |a электронный ресурс | |
| 610 | 1 | |a труды учёных ТПУ | |
| 610 | 1 | |a high-temperature nickel alloy | |
| 610 | 1 | |a strengthening | |
| 610 | 1 | |a rhenium | |
| 610 | 1 | |a lanthanum | |
| 610 | 1 | |a secondary phases | |
| 610 | 1 | |a superalloy | |
| 610 | 1 | |a morphology | |
| 610 | 1 | |a annealing | |
| 610 | 1 | |a никелевые сплавы | |
| 610 | 1 | |a жаропрочные сплавы | |
| 610 | 1 | |a упрочнение | |
| 610 | 1 | |a рений | |
| 610 | 1 | |a лантан | |
| 610 | 1 | |a суперсплавы | |
| 610 | 1 | |a морфология | |
| 610 | 1 | |a отжиг | |
| 701 | 1 | |a Nikonenko |b E. L. |c physicist |c Associate Professor of Tomsk Polytechnic University, candidate of physical and mathematical sciences |f 1962- |g Elena Leonidovna |3 (RuTPU)RU\TPU\pers\35823 |9 18968 | |
| 701 | 1 | |a Popova |b N. A. |g Nataljya Anatoljevna | |
| 701 | 1 | |a Sizonenko |b N. R. |g Nina Robertovna | |
| 701 | 1 | |a Dement |b T. V. |g Taras Valerjevich | |
| 701 | 1 | |a Koneva |b N. A. |g Nina Aleksandrovna | |
| 712 | 0 | 2 | |a Национальный исследовательский Томский политехнический университет |b Школа базовой инженерной подготовки |b Отделение русского языка |3 (RuTPU)RU\TPU\col\23517 |
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| 856 | 4 | |u https://doi.org/10.3103/S0967091218040095 | |
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