WO1995032314A1 - Intermetallische nickel-aluminium-basislegierung - Google Patents
Intermetallische nickel-aluminium-basislegierung Download PDFInfo
- Publication number
- WO1995032314A1 WO1995032314A1 PCT/EP1995/001921 EP9501921W WO9532314A1 WO 1995032314 A1 WO1995032314 A1 WO 1995032314A1 EP 9501921 W EP9501921 W EP 9501921W WO 9532314 A1 WO9532314 A1 WO 9532314A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- chromium
- tantalum
- nial
- alloy
- alloy according
- Prior art date
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
Definitions
- the invention relates to an intermetallic nickel aluminum base alloy which has the binary phase NiAl.
- the invention further relates to the use of the intermetallic nickel-aluminum base alloy.
- DE-AS 18 12 144 describes a process for producing a high-strength nickel-aluminum material with good resistance to oxidation.
- nickel powder is mixed with aluminum powder and then pressed and cold-formed, so that a self-supporting and coherent shaped body with a fibrous or lamenarene
- connection NissAl is also created. This solid solution as well as the compound Ni3Al could be verified with X-ray analysis. The extent to which other connections between nickel and aluminum can be achieved with the method cannot be found in the design specification.
- the object of the invention is to improve the thermo-mechanical properties of a nickel-aluminum alloy. These include in particular the heat resistance, the oxidation resistance and the thermal shock resistance. Another object of the invention is to provide a use of such an improved nickel-aluminum alloy.
- the object directed to a nickel-aluminum alloy is achieved by an intermetallic nickel-aluminum base alloy which predominantly has the binary phase NiAl and additionally chromium and tantalum, wherein the total proportion of chromium and tantalum is a maximum of 12 at.%.
- the proportion of the binary phase NiAl is preferably between 70 to 95 at .-%, in particular between 85 and 90 at * t .-%.
- the preferred content ranges for tantalum and chromium are 0.3 to 3.8 at .-% and 1.0 to 9.0 at .-%. Within these ranges, 0.3 to 0.9 at.% Tantalum and 1.0 to 3 at.% Chromium or 1.7 to 3.0 at.% Tan tal and 6.0 to 9 are preferred .0 at .-% chromium used.
- the ratio of tantalum to chromium is preferably 1: 3 or less. With such a ratio, the concentration of substitution elements in the NiAl reaches a maximum.
- the ratio of tantalum and chromium precipitations occur in the coarse, mul- tular Laves phase in the non-metallic nickel-aluminum base alloy on the grain boundaries of the binary phase NiAl, on which the elements Ni, Al, Cr and Ta can be involved.
- there are excretions of finely divided Laves phase and ⁇ -chromium within the NiAl grains It is preferred that the structure of 5 to 11% by volume Laves phase, 3 to 10% by volume precipitates in NiAl and one
- a structure has proven to be particularly advantageous which comprises approximately 11 vol.% Laves phase on the grain boundaries and approximately 10 vol.% Precipitates in the NiAl and NiAl as the remainder.
- a further improvement in certain properties results if at least one element from the group iron, molybdenum, tungsten and hafnium is present in the alloy in an amount of up to 1 at.%, But not more than 3 at are included.
- the alloy can also contain trace elements such as oxygen, nitrogen and sulfur, as well as production-related impurities.
- the coarse or fine-particle multinary Laves phases and ⁇ -chromium are formed. These excretions are usually based on gussets points of different NiAl grains. Higher than the specified amounts of alloying elements tantalum or chromium can lead to an undesirable increase in the amount of precipitates. If the volume fractions of Laves phase increases too much, a cellular structure arises in which the Laves phase takes over the function of the matrix. Too large a proportion of Laves phase in the structure makes the intermetallic alloy brittle and difficult to process.
- the object aimed at using the alloy is achieved according to the invention in that components of a gas turbine, in particular components exposed to high temperatures, such as gas turbine blades, are produced with the NiAl base alloy.
- a component of a gas turbine, in particular a turbine blade, made from the base alloy is particularly suitable due to the high oxidation resistance for continuous use at high temperatures, for example above 1100 ° C., in particular at 1350 ° C.
- an additional coating with protective layers can be dispensed with in such a component, depending on the requirements.
- the intermetallic nickel-aluminum base alloy is generally also suitable as a material for the production of objects which must have high strength, high heat resistance, good toughness, good oxidation resistance and good thermal shock resistance.
- the strength lies here with a 0.2% proof stress at room temperature of over 600 MPa.
- the heat resistance lies at the 0.2% proof stress at over 200 MPa at 800 ° C and at over 90 MPa at 1000 ° C.
- the toughness is at least 7 MPa / m and the oxidation resistance is of the order of magnitude
- composition (in at.%) Of alloys sought is given in Table 1 below.
- the structure of the structure ie the grain size, the distribution of precipitates and the size of the precipitate, varies greatly with the manufacturing process.
- the distribution of the Laves phase particles is homogenized by thermodynamic treatments, extrusion (SP) or by using the powder metallurgical production route (PM).
- SP thermodynamic treatments
- PM powder metallurgical production route
- the mechanical properties of the alloys are also heavily dependent on the selected manufacturing process. The following production routes for these alloys were followed:
- Powder metallurgy by inert gas atomization and subsequent hot isostatic pressing at 1250 ° C.
- the creep resistance (in MPa) of the alloys tested in the compression test (secondary stationary creep resistance than Funk ⁇ tion of the strain rate [1 / s] at 1000 ° C and 1100 ° C *) is shown in Table 3 below.
- the creep strengths of this alloy are higher than the creep strengths of comparable intermetallic phases, for example higher than the creep strength of binary NiAl or NiAlCr alloys.
- Table 4a gives a comparison of the 0.2% proof stress (in MPa) in the compression test of a conventional superalloy, a binary NiAl alloy and a NiAl-Ta-Cr alloy.
- the superiority of the alloy according to the invention proves at temperatures above 1000 ° C.
- the NiAl-Ta-Cr alloy Compared to conventional superalloys, the NiAl-Ta-Cr alloy has the advantage that it also has sufficient strength above 1050 ° C to 1150 ° C. There is no sudden drop in strength in this alloy due to the dissolution of the solidified phase.
- Table 5 shows a comparison of the values of K ⁇ values of various ceramics known from industry data and of the powder-metallurgical processed NiAl-Ta-Cr alloy produced.
- the alloy has a good oxidation resistance of the order of magnitude 5 * 10- ⁇ g 2 c " ⁇ s, which is therefore equal to or better than the oxidation resistance of binary NiAl.
- no protective layers for example, are formed at high temperatures ceramic material, this eliminates the problem of the connection between ceramic and metallic components.
- Adequate thermal shock resistance is given. At 1350 ° C, 500 temperature cycles of the alloy are achieved without damaging the material.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
Abstract
Description
Claims
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP7530056A JPH10500453A (ja) | 1994-05-21 | 1995-05-19 | 金属間ニッケル−アルミニウム−ベース合金 |
EP95920844A EP0760869B1 (de) | 1994-05-21 | 1995-05-19 | Intermetallische nickel-aluminium-basislegierung |
RU96124081A RU2148671C1 (ru) | 1994-05-21 | 1995-05-19 | Интерметаллический сплав на основе никель-алюминия |
DE59509221T DE59509221D1 (de) | 1994-05-21 | 1995-05-19 | Intermetallische nickel-aluminium-basislegierung |
CZ963426A CZ342696A3 (en) | 1994-05-21 | 1995-05-19 | Intermetallic base alloy of nickel and aluminium |
US08/757,554 US5935349A (en) | 1994-05-21 | 1996-11-21 | Intermetallic nickel-aluminum base alloy and material formed of the alloy |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE4417936A DE4417936C1 (de) | 1994-05-21 | 1994-05-21 | Nickel-Aluminium-Legierung |
DEP4417936.7 | 1994-05-21 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US08/757,554 Continuation US5935349A (en) | 1994-05-21 | 1996-11-21 | Intermetallic nickel-aluminum base alloy and material formed of the alloy |
Publications (1)
Publication Number | Publication Date |
---|---|
WO1995032314A1 true WO1995032314A1 (de) | 1995-11-30 |
Family
ID=6518734
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/EP1995/001921 WO1995032314A1 (de) | 1994-05-21 | 1995-05-19 | Intermetallische nickel-aluminium-basislegierung |
Country Status (8)
Country | Link |
---|---|
EP (1) | EP0760869B1 (de) |
JP (1) | JPH10500453A (de) |
KR (1) | KR100359187B1 (de) |
CN (1) | CN1044493C (de) |
CZ (1) | CZ342696A3 (de) |
DE (2) | DE4417936C1 (de) |
RU (1) | RU2148671C1 (de) |
WO (1) | WO1995032314A1 (de) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2002088407A1 (en) * | 2001-03-27 | 2002-11-07 | Koncentra Verkstads Ab | Nickel-aluminide based wear resistant material for piston rings |
US9995393B2 (en) | 2013-08-01 | 2018-06-12 | Mahle Metal Leve S/A | Piston ring and method for manufacturing same |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN100422369C (zh) * | 2006-12-13 | 2008-10-01 | 北京航空航天大学 | Ti改性NiAl-Cr(Mo)多相共晶结构金属间化合物 |
CN104073688B (zh) * | 2014-06-19 | 2016-08-17 | 湖南科技大学 | 一种NiAl-2.5Ta-7.5Cr合金作为碱腐蚀工况下自润滑耐磨材料的应用 |
CN104294328B (zh) * | 2014-10-23 | 2017-02-01 | 上海应用技术学院 | 一种镍钼铝稀土镀层及其制备方法 |
DE102017109156A1 (de) | 2016-04-28 | 2017-11-02 | Hochschule Flensburg | Hochwarmfester Werkstoff und dessen Herstellung |
CN115595486B (zh) * | 2022-10-14 | 2024-03-22 | 中国科学院金属研究所 | 一种高温涡轮叶片叶尖耐磨切削涂层及其制备方法和应用 |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE1812144A1 (de) * | 1967-12-06 | 1969-08-14 | Union Carbide Corp | Metallurgischer Werkstoff und Verfahren zu seiner Herstellung |
EP0502654A1 (de) * | 1991-03-04 | 1992-09-09 | General Electric Company | Mikrolegierte Nial-intermetallische Verbindungen mit verbesserter Duktilität |
-
1994
- 1994-05-21 DE DE4417936A patent/DE4417936C1/de not_active Expired - Fee Related
-
1995
- 1995-05-19 RU RU96124081A patent/RU2148671C1/ru active
- 1995-05-19 CN CN95193622A patent/CN1044493C/zh not_active Expired - Fee Related
- 1995-05-19 EP EP95920844A patent/EP0760869B1/de not_active Expired - Lifetime
- 1995-05-19 JP JP7530056A patent/JPH10500453A/ja not_active Ceased
- 1995-05-19 DE DE59509221T patent/DE59509221D1/de not_active Expired - Fee Related
- 1995-05-19 CZ CZ963426A patent/CZ342696A3/cs unknown
- 1995-05-19 WO PCT/EP1995/001921 patent/WO1995032314A1/de not_active Application Discontinuation
- 1995-05-19 KR KR1019960706538A patent/KR100359187B1/ko not_active IP Right Cessation
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE1812144A1 (de) * | 1967-12-06 | 1969-08-14 | Union Carbide Corp | Metallurgischer Werkstoff und Verfahren zu seiner Herstellung |
EP0502654A1 (de) * | 1991-03-04 | 1992-09-09 | General Electric Company | Mikrolegierte Nial-intermetallische Verbindungen mit verbesserter Duktilität |
Non-Patent Citations (3)
Title |
---|
CHEMICAL ABSTRACTS, vol. 113, no. 26, 24 December 1990, Columbus, Ohio, US; abstract no. 235621 * |
DAROLIA R.: "NiAl Alloys for High-Temperature Structural Applications", JOURNAL OF METALS, no. 3, pages 44 - 49 * |
KUPCHENKO ET AL.: "Life and fracture of directionally solidified eutectic composite materials", FIZ. MET. METALLOVVED., no. 8, MINSK, pages 204 - 206 * |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2002088407A1 (en) * | 2001-03-27 | 2002-11-07 | Koncentra Verkstads Ab | Nickel-aluminide based wear resistant material for piston rings |
WO2002088406A1 (en) * | 2001-03-27 | 2002-11-07 | Koncentra Verkstads Ab | Intermetallic wear-resistant material for piston rings |
US6838196B2 (en) | 2001-03-27 | 2005-01-04 | Koncentra Holding Ab | Nickel-aluminide based wear resistant material for piston rings |
US7052018B2 (en) | 2001-03-27 | 2006-05-30 | Koncentra Marine & Power Ab | Piston ring having wear resistant composition |
US7144017B2 (en) | 2001-03-27 | 2006-12-05 | Koncentra Marine & Power Ab | Piston ring having wear resistant composition |
KR100854666B1 (ko) * | 2001-03-27 | 2008-08-27 | 콘센트라 마린 앤드 파워 아베 | 피스톤 링용의 내마모성 니켈-알루미나이드계 재료 |
KR100854667B1 (ko) * | 2001-03-27 | 2008-08-27 | 콘센트라 마린 앤드 파워 아베 | 피스톤 링용의 내마모성 금속간 화합물 재료 |
US9995393B2 (en) | 2013-08-01 | 2018-06-12 | Mahle Metal Leve S/A | Piston ring and method for manufacturing same |
Also Published As
Publication number | Publication date |
---|---|
CN1044493C (zh) | 1999-08-04 |
KR100359187B1 (ko) | 2003-01-24 |
KR970703438A (ko) | 1997-07-03 |
EP0760869B1 (de) | 2001-04-25 |
DE59509221D1 (de) | 2001-05-31 |
CN1150826A (zh) | 1997-05-28 |
JPH10500453A (ja) | 1998-01-13 |
DE4417936C1 (de) | 1995-12-07 |
EP0760869A1 (de) | 1997-03-12 |
RU2148671C1 (ru) | 2000-05-10 |
CZ342696A3 (en) | 1997-08-13 |
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