Nickel aluminide: Difference between revisions
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== Ni<sub>3</sub>Al == |
== Ni<sub>3</sub>Al == |
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An important disadvantage of polycrystalline Ni<sub>3</sub>Al-based alloys are their room-temperature and high-temperature brittleness, which interferes with potential structural applications. This brittleness is generally attributed to the inability of dislocations to move in the highly ordered lattices.<ref>{{Cite journal|last1=Wu|first1=Yu-ting|last2=Li|first2=Chong|last3=Li|first3=Ye-fan|last4=Wu|first4=Jing|last5=Xia|first5=Xing-chuan|last6=Liu|first6=Yong-chang|date=2020|title=Effects of heat treatment on the microstructure and mechanical properties of Ni3Al-based superalloys: A review|journal=International Journal of Minerals, Metallurgy and Materials|volume=28|issue=4|pages=553–566|doi=10.1007/s12613-020-2177-y|issn=1674-4799|doi-access=free}}</ref> The introduction of small amount of boron can drastically increase the ductility by suppressing intergranular fracture.<ref>{{Cite journal|last=K|first=Aoki|date=1990|title=Ductilization of L12 Intermetallic Compound Ni3Al by Microalloying with Boron|url=https://www.jstage.jst.go.jp/article/matertrans1989/31/6/31_6_443/_article|journal=Materials Transactions, JIM|volume=31|issue=6|pages=443–448|doi=10.2320/matertrans1989.31.443|via=J-STAGE|doi-access=free}}</ref> |
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Ni-based [[superalloy]]s derive their strength from the formation of γ' precipitates (Ni<sub>3</sub>Al) in the γ phase (Ni) which strengthen the alloys through [[precipitation hardening]]. In these alloys the volume fraction of the γ' precipitates is as high as 80%.<ref name=":2">{{Cite journal|last1=Wu|first1=Yuting|last2=Liu|first2=Yongchang|last3=Li|first3=Chong|last4=Xia|first4=Xingchuan|last5=Wu|first5=Jing|last6=Li|first6=Huijun|date=2019-01-15|title=Coarsening behavior of γ′ precipitates in the γ'+γ area of a Ni3Al-based alloy|url=https://www.sciencedirect.com/science/article/pii/S0925838818331542|journal=Journal of Alloys and Compounds|language=en|volume=771|pages=526–533|doi=10.1016/j.jallcom.2018.08.265|s2cid=139682282|issn=0925-8388}}</ref> Because of this high volume fraction, the evolution of these γ' precipitates during the alloys' life cycles is important: a major concern is the coarsening of these γ' precipitates at high temperature (800 to 1000 °C), which greatly reduces the alloys' strength.<ref name=":2" /> This coarsening is due to the balance between interfacial and elastic energy in the γ + γ' phase and is generally inevitable over long durations of time.<ref name=":2" /> This coarsening problem is addressed by introducing other elements such as Fe, Cr and Mo, which generate multiphase configurations that can significantly increase the creep resistance.<ref name=":3">{{Cite journal|last1=Wu|first1=Jing|last2=Li|first2=Chong|last3=Wu|first3=Yuting|last4=Huang|first4=Yuan|last5=Xia|first5=Xingchuan|last6=Liu|first6=Yongchang|date=2020-07-14|title=Creep behaviors of multiphase Ni3Al-based intermetallic alloy after 1000°C-1000h long-term aging at intermediate temperatures|url=https://www.sciencedirect.com/science/article/pii/S0921509320307796|journal=Materials Science and Engineering: A|language=en|volume=790|pages=139701|doi=10.1016/j.msea.2020.139701|s2cid=225742080|issn=0921-5093}}</ref> This creep resistance is attributed to the formation of inhomogeneous precipitate Cr<sub>4.6</sub>MoNi<sub>2.1</sub>, which pins dislocations and prevents further coarsening of the γ' phase.<ref name=":3" /> The addition of Fe and Cr also drastically increases the weldability of the alloy.<ref name=":3" /> |
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== NiAl == |
== NiAl == |
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Revision as of 07:53, 2 January 2024
Nickel aluminide refers to either of two widely used intermetallic compounds, Ni3Al or NiAl, but the term is sometimes used to refer to any nickel–aluminium alloy. These alloys are widely used because of their high strength even at high temperature, low density, corrosion resistance, and ease of production.[1] Ni3Al is of specific interest as a precipitate in nickel-based superalloys, where it is called the γ' (gamma prime) phase. It gives these alloys high strength and creep resistance up to 0.7–0.8 of its melting temperature.[1][2] Meanwhile, NiAl displays excellent properties such as lower density and higher melting temperature than those of Ni3Al, and good thermal conductivity and oxidation resistance.[2] These properties make it attractive for special high-temperature applications like coatings on blades in gas turbines and jet engines. However, both these alloys have the disadvantage of being quite brittle at room temperature, with Ni3Al remaining brittle at high temperatures as well.[1] To address this problem, has been shown that Ni3Al can be made ductile when manufactured in single-crystal form rather than in polycrystalline form.[3]
Properties
- Ni3Al has a cubic crystalline structure of the L12 type, with lattice parameter a = 355.9 pm.
- Density = 7.16 g/cm3
- Yield Strength = 855 MPa
- Hardness = HRC 12
- Thermal Conductivity Ni3Al = 28.85 (W/m.K)[4]
- Thermal Conductivity NiAl = 76 (W/m.K) [4]
- Melting Point Ni3Al = 1,668 K (1,395 °C; 2,543 °F)
- Melting Point NiAl = 1,955 K (1,682 °C; 3,059 °F)
- Thermal expansion coefficient = 12.5 (10−6/K)
- Bonding = covalent/metallic
- Electrical resistivity = 32.59 (10−8Ωm)
Ni3Al
An important disadvantage of polycrystalline Ni3Al-based alloys are their room-temperature and high-temperature brittleness, which interferes with potential structural applications. This brittleness is generally attributed to the inability of dislocations to move in the highly ordered lattices.[5] The introduction of small amount of boron can drastically increase the ductility by suppressing intergranular fracture.[6]
Ni-based superalloys derive their strength from the formation of γ' precipitates (Ni3Al) in the γ phase (Ni) which strengthen the alloys through precipitation hardening. In these alloys the volume fraction of the γ' precipitates is as high as 80%.[7] Because of this high volume fraction, the evolution of these γ' precipitates during the alloys' life cycles is important: a major concern is the coarsening of these γ' precipitates at high temperature (800 to 1000 °C), which greatly reduces the alloys' strength.[7] This coarsening is due to the balance between interfacial and elastic energy in the γ + γ' phase and is generally inevitable over long durations of time.[7] This coarsening problem is addressed by introducing other elements such as Fe, Cr and Mo, which generate multiphase configurations that can significantly increase the creep resistance.[8] This creep resistance is attributed to the formation of inhomogeneous precipitate Cr4.6MoNi2.1, which pins dislocations and prevents further coarsening of the γ' phase.[8] The addition of Fe and Cr also drastically increases the weldability of the alloy.[8]
NiAl
Despite its beneficial properties, NiAl generally suffers from two factors: very high brittleness at low temperatures (<330 °C (626 °F)) and rapid loss of strength for temperatures higher than 550 °C (1,022 °F).[9] The brittleness is attributed to both the high energy of anti-phase boundaries as well as high atomic order along grain boundaries.[9] Similar to that of Ni3Al-based alloys these issues are generally addressed via the integration of other elements. Attempted elements can be broken into three groups depending on their influence of microstructure:
- Elements that form ternary intermetallic phases such as Ti and Hf[9]
- Pseudobinary eutectic forming elements such as Cr[9]
- Elements with high solubility in NiAl such as Fe, Co and Cu[9]
Some of the more successful elements have been shown to be Fe, Co and Cr which drastically increase room temperature ductility as well as hot workability.[10] This increase is due to the formation of γ phase which modifies the β phase grains.[10] Alloying with Fe, Ga and Mo has also been shown to drastically improve room temperature ductility as well.[11] Most recently, refracturing metals such as Cr, W and Mo have been added and resulted in not only increases in room temperature ductility but also increases in strength and fracture toughness at high temperatures.[12] This is due to the formation of unique microstructures such as the eutectic alloy Ni45.5Al9Mo and α-Cr inclusions that contribute to solid solution hardening.[12] It is even being shown that these complex alloys (Ni42Al51Cr3Mo4) have the potential to be fabricated via additive manufacturing processes such as selective laser manufacturing, vastly increasing the potential applications for these alloys.[12]
Nickel-based superalloys
In nickel-based superalloys, regions of Ni3Al (called γ' phase) precipitate out of the nickel-rich matrix (called γ phase) to give high strength and creep resistance. Many alloy formulations are available and they usually include other elements, such as chromium, molybdenum, and iron, in order to improve various properties.
Examples
IC-221M
An alloy of Ni3Al, known as IC-221M, is made up of nickel aluminide combined with several other metals including chromium, molybdenum, zirconium and boron. Adding boron increases the ductility of the alloy by positively altering the grain boundary chemistry and promoting grain refinement. The Hall-Petch parameters for this material were σo = 163 MPa and ky = 8.2 MPaˑcm1/2.[13] Boron increases the hardness of bulk Ni3Al by a similar mechanism.
This alloy is extremely strong for its weight, five times stronger than common SAE 304 stainless steel. Unlike most alloys, IC-221M increases in strength from room temperature up to 800 °C (1,470 °F).
The alloy is very resistant to heat and corrosion, and finds use in heat-treating furnaces and other applications where its longer lifespan and reduced corrosion give it an advantage over stainless steel.[14] It has been found that the microstructure of this alloy includes Ni5Zr eutectic phase and therefore solution treatment is effective for hot working without cracking.[15]
References
- ^ a b c Kurbatkina, Victoria V. (2017-01-01), "Nickel Aluminides", in Borovinskaya, Inna P.; Gromov, Alexander A.; Levashov, Evgeny A.; Maksimov, Yuri M. (eds.), Concise Encyclopedia of Self-Propagating High-Temperature Synthesis, Amsterdam: Elsevier, pp. 212–213, ISBN 978-0-12-804173-4, retrieved 2021-03-07
- ^ a b Dey, G. K. (2003-02-01). "Physical metallurgy of nickel aluminides". Sādhanā. 28 (1): 247–262. doi:10.1007/BF02717135. ISSN 0973-7677. S2CID 122260602.
- ^ Pope, D. P.; Ezz, S. S. (1984-01-01). "Mechanical properties of Ni3AI and nickel-base alloys with high volume fraction of γ'". International Metals Reviews. 29 (1): 136–167. doi:10.1179/imtr.1984.29.1.136. ISSN 0308-4590.
- ^ a b Dey, G. K. (2003). "Physical Metallurgy of Nickel Aluminides" (PDF). Sādhanā. 28 (Parts 1 & 2): 247–262. doi:10.1007/bf02717135. S2CID 122260602. Retrieved 2014-03-05.
- ^ Wu, Yu-ting; Li, Chong; Li, Ye-fan; Wu, Jing; Xia, Xing-chuan; Liu, Yong-chang (2020). "Effects of heat treatment on the microstructure and mechanical properties of Ni3Al-based superalloys: A review". International Journal of Minerals, Metallurgy and Materials. 28 (4): 553–566. doi:10.1007/s12613-020-2177-y. ISSN 1674-4799.
- ^ K, Aoki (1990). "Ductilization of L12 Intermetallic Compound Ni3Al by Microalloying with Boron". Materials Transactions, JIM. 31 (6): 443–448. doi:10.2320/matertrans1989.31.443 – via J-STAGE.
- ^ a b c Wu, Yuting; Liu, Yongchang; Li, Chong; Xia, Xingchuan; Wu, Jing; Li, Huijun (2019-01-15). "Coarsening behavior of γ′ precipitates in the γ'+γ area of a Ni3Al-based alloy". Journal of Alloys and Compounds. 771: 526–533. doi:10.1016/j.jallcom.2018.08.265. ISSN 0925-8388. S2CID 139682282.
- ^ a b c Wu, Jing; Li, Chong; Wu, Yuting; Huang, Yuan; Xia, Xingchuan; Liu, Yongchang (2020-07-14). "Creep behaviors of multiphase Ni3Al-based intermetallic alloy after 1000°C-1000h long-term aging at intermediate temperatures". Materials Science and Engineering: A. 790: 139701. doi:10.1016/j.msea.2020.139701. ISSN 0921-5093. S2CID 225742080.
- ^ a b c d e Czeppe, Tomasz; Wierzbinski, Stanislaw (2000-08-01). "Structure and mechanical properties of NiAl and Ni3Al-based alloys". International Journal of Mechanical Sciences. 42 (8): 1499–1518. doi:10.1016/S0020-7403(99)00087-9. ISSN 0020-7403.
- ^ a b Ishida, K.; Kainuma, R.; Ueno, N.; Nishizawa, T. (1991-02-01). "Ductility enhancement in NiAl (B2)-base alloys by microstructural control". Metallurgical Transactions A. 22 (2): 441–446. Bibcode:1991MTA....22..441I. doi:10.1007/BF02656811. ISSN 1543-1940. S2CID 135574438.
- ^ Darolia, Ram (1991-03-01). "NiAl alloys for high-temperature structural applications". JOM. 43 (3): 44–49. Bibcode:1991JOM....43c..44D. doi:10.1007/BF03220163. ISSN 1543-1851. S2CID 137019796.
- ^ a b c Khomutov, M.; Potapkin, P.; Cheverikin, V.; Petrovskiy, P.; Travyanov, A.; Logachev, I.; Sova, A.; Smurov, I. (2020-05-01). "Effect of hot isostatic pressing on structure and properties of intermetallic NiAl–Cr–Mo alloy produced by selective laser melting". Intermetallics. 120: 106766. doi:10.1016/j.intermet.2020.106766. ISSN 0966-9795. S2CID 216231029.
- ^ Liu, C. T.; White, C. L.; Horton, J. A. (1985). "Effect of boron on grain-boundaries in Ni3Al". Acta Metall. 33 (2): 213–229. doi:10.1016/0001-6160(85)90139-7.
- ^ Crawford, Gerald (April 2003). "Exotic Alloy Finds Niche". Nickel magazine. Retrieved 2006-12-19.
- ^ Hadi, Morteza; Kamali, Ali Reza (2009-10-19). "Investigation on hot workability and mechanical properties of modified IC-221M alloy". Journal of Alloys and Compounds. 485 (1): 204–208. doi:10.1016/j.jallcom.2009.06.010. ISSN 0925-8388.