WO2010082632A1 - Ni基単結晶超合金 - Google Patents
Ni基単結晶超合金 Download PDFInfo
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- WO2010082632A1 WO2010082632A1 PCT/JP2010/050428 JP2010050428W WO2010082632A1 WO 2010082632 A1 WO2010082632 A1 WO 2010082632A1 JP 2010050428 W JP2010050428 W JP 2010050428W WO 2010082632 A1 WO2010082632 A1 WO 2010082632A1
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- Prior art keywords
- mass
- single crystal
- strength
- creep
- tmf
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Classifications
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- 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
-
- 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
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B11/00—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/10—Inorganic compounds or compositions
- C30B29/52—Alloys
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
- F01D5/00—Blades; Blade-carrying members; Heating, heat-insulating, cooling or antivibration means on the blades or the members
- F01D5/12—Blades
- F01D5/28—Selecting particular materials; Particular measures relating thereto; Measures against erosion or corrosion
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
- F05D2300/00—Materials; Properties thereof
- F05D2300/60—Properties or characteristics given to material by treatment or manufacturing
- F05D2300/607—Monocrystallinity
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02T—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO TRANSPORTATION
- Y02T50/00—Aeronautics or air transport
- Y02T50/60—Efficient propulsion technologies, e.g. for aircraft
Definitions
- the present invention relates to a Ni-based single crystal superalloy.
- the turbine blade rotates at a high speed at the same time as being exposed to high-temperature combustion gas, so it must withstand high stress due to centrifugal force.
- the creep characteristics at high temperature are also TMF. Equally important.
- Patent Documents 1 and 2 Ni-base superalloys aimed at heat fatigue resistance are known (Patent Documents 1 and 2).
- Patent Document 3 the Ni-base superalloy having excellent creep characteristics (Patent Document 3) is used in many high-temperature devices.
- Ni-based superalloys with superior thermal fatigue characteristics, creep characteristics, and resistance to sulfidation corrosion is desired.
- the creep characteristics at 900 ° C./392 MPa are 600 hours or more
- the creep characteristics at 1000 ° C./245 MPa are 160 hours or more
- the TMF characteristics are a temperature range: 400 to 900 ° C.
- frequency 66 min / cycle waveform: triangular wave + trapezoidal wave
- phase 200 times or more under anti-phase conditions
- sulfidation corrosion resistance is 75% Na 2 SO 4 + 25% NaCl component salt heated to 900 ° C.
- a specific target is that the weight loss of corrosion when immersed for a period of time is 0.001 mm or less.
- the present invention is a Ni-based single crystal excellent in TMF characteristics, creep characteristics and sulfidation corrosion resistance, which is suitable as a high temperature member used under high temperature and high stress such as a turbine blade or turbine vane of a gas turbine for large power generation.
- the challenge is to provide a superalloy.
- the present invention has the following features.
- 1st invention is the mass%, Co: 8-12%, Cr: 5 to 7.5% Mo: 0.2-1.2%, W: 5-7% Al: 5 to 6.5%, Ta: 8-12%, Hf: 0.01 to 0.2%, Re: 2-4%, Si: 0.005 to 0.1% And the balance is a single crystal having a chemical composition composed of Ni and inevitable impurities.
- % By mass Co 8-11% Cr: 5-7%, Mo: 0.2-1%, W: 5.5-7% Al: 5-6%, Ta: 9-12%, Hf: 0.05 to 0.2%, Re: 2.5-4%, Si: 0.005 to 0.08% And the balance is a single crystal having a chemical composition composed of Ni and inevitable impurities.
- % By mass Co 8-10% Cr: 6-7%, Mo: 0.5 to 1%, W: 5.5-6.5% Al: 5-6%, Ta: 9-11%, Hf: 0.05 to 0.15%, Re: 2.5-3.5% Si: 0.005 to 0.08% And the balance is a single crystal having a chemical composition composed of Ni and inevitable impurities.
- Ni-based single crystal superalloy excellent in TMF characteristics, creep characteristics, and sulfidation corrosion resistance is provided, and this Ni-based single crystal alloy is used for high temperature such as turbine blades and turbine vanes of large-scale power generation gas turbines. -Suitable as a high temperature member used under high stress.
- the reason for limiting the chemical composition in the Ni-based single crystal superalloy of the present invention is as follows.
- Co is an element that replaces gamma-phase Ni and strengthens the matrix by solid solution.
- it is an element that has the effect of expanding the solution temperature range by lowering the gamma prime solvus temperature and improving the heat treatment characteristics.
- the content is 8 to 12% by mass. When it is less than 8% by mass, the solution temperature range is small, and when it is more than 12% by mass, the gamma prime amount is decreased, and the strength is lowered.
- the Co content is preferably 8 to 11%, more preferably 8 to 10%.
- the Cr is an element that improves high temperature corrosion resistance.
- the content is 5 to 7.5% by mass. If it is less than 5% by mass, the corrosion resistance is lowered, and if it exceeds 7.5% by mass, a harmful phase is formed and the high temperature strength is lowered.
- the Cr content is preferably 5 to 7%, more preferably 6 to 7%.
- Mo is an element that promotes the raft effect, which is one of the strengthening mechanisms at high temperatures, with negative gamma / gamma prime misfit.
- the content is 0.2 to 1.2% by mass.
- Mo is dissolved in the substrate to increase the high temperature strength, and contributes to the high temperature strength by precipitation hardening. When the amount is less than 0.2% by mass, the high temperature strength is lowered. When the amount exceeds 4% by mass, a harmful phase is generated and the high temperature strength is lowered.
- the Mo content is preferably 0.2 to 1%, and more preferably 0.5 to 1%.
- W like Mo
- the content is 5 to 7% by mass. In order to obtain the required creep strength and TMF strength, at least 5% by mass is required, and addition exceeding 7% by mass generates a harmful phase and the strength is lowered.
- the W content is preferably 5.5 to 7%, more preferably 5.5 to 6.5%.
- Al combines with Ni to form an intermetallic compound represented by Ni3Al that constitutes the gamma prime phase that precipitates in the gamma matrix at a volume fraction of 50 to 70%, and has TMF strength and creep strength. To improve.
- the content is 5 to 6.5% by mass. If the Al content is less than 5% by mass, the required TMF strength and creep strength cannot be obtained because the amount of gamma prime phase is small, and if the Al content exceeds 6.5% by mass, the required TMF strength and creep strength cannot be obtained.
- the Al content is preferably 5 to 6%.
- Ta is an effective element that strengthens the gamma prime phase and improves the creep strength.
- the content is 8 to 12% by mass. If Ta is less than 8% by mass, the required TMF strength and creep strength cannot be obtained, and if it exceeds 12% by mass, the formation of a eutectic gamma prime phase is promoted and solution heat treatment becomes difficult.
- the content of Ta is preferably 9 to 12%, more preferably 9 to 11%.
- Hf Since Hf has the effect of improving the oxidation resistance, it is effective to add it as a chemical composition component.
- the addition amount is 0.01 to 0.2% by mass. If Hf is less than 0.01% by mass, the effect of oxidation resistance cannot be obtained, and if it exceeds 0.2% by mass, the formation of a harmful phase is promoted, so the TMF strength and creep strength are lowered.
- the amount of Hf added is preferably 0.05 to 0.2%, more preferably 0.05 to 0.15%.
- Re Re dissolves in the gamma phase and improves high temperature strength by solid solution strengthening. Re also has the effect of improving corrosion resistance.
- the addition amount is 2 to 4% by mass. If it is less than 2% by mass, the strength is lowered, and if it exceeds 4% by mass, the creep strength due to precipitation of the TCP phase is lowered.
- the amount of Re added is preferably 2.5 to 4%, and more preferably 2.5 to 3.5%.
- Si is an element effective for improving oxidation resistance.
- the content is 0.005 to 0.1% by mass. If it is less than 0.005% by mass, the effect of oxidation resistance cannot be obtained. If it exceeds 0.1% by mass, the required creep strength cannot be obtained.
- the Si content is preferably 0.005 to 0.08%.
- Ni-based single crystal alloy of the present invention having the chemical composition as described above can be manufactured by the following process, for example.
- the raw material having the above chemical composition is melted and cast to obtain a single crystal casting, and then the solution treatment, the primary aging treatment, and the secondary aging treatment are performed on the single crystal casting.
- This Ni-based single crystal alloy is manufactured.
- the solution treatment conditions include holding in a temperature range of 1250 to 1350 ° C. in a vacuum for 1 to 20 hours and then air cooling.
- the conditions for the primary aging treatment include holding in a temperature range of 1000 to 1200 ° C. in a vacuum for 1 to 10 hours and then air cooling.
- Examples of the conditions for the secondary aging treatment include holding in a temperature range of 850 to 900 ° C. in a vacuum for 15 to 30 hours and then air cooling.
- the conditions adopted for each treatment are set to an appropriate one according to the chemical composition of the Ni-based single crystal superalloy.
- a Ni-based superalloy having the chemical composition shown in Table 1 was melted and cast in a vacuum at a solidification rate of 200 mm / h to obtain a single crystal casting.
- the obtained single crystal casting is preheated in vacuum at 1300 ° C. (10 ° C. unit; the same shall apply hereinafter) for 1 hour, then held at 1330 ° C. for 10 hours and then air-cooled, followed by solution treatment.
- a primary aging treatment was performed in which air was cooled at 1100 ° C. for 4 hours in vacuum, and a secondary aging treatment in which air cooling was performed at 870 ° C. for 20 hours in vacuum.
- the single crystal alloy casting was processed into a creep test piece having a parallel part diameter of 4 mm and a parallel part length of 20 mm, and a creep test was performed under the conditions of 900 ° C., 392 MPa, 1000 ° C., and 245 MPa.
- the TMF test was performed by heating the test piece at a high frequency.
- the temperature was varied from the lower limit of 400 ° C. to the upper limit of 900 ° C.
- strain was added at ⁇ 0.64%, and the temperature variation and strain were linked.
- the frequency was 66 min in one cycle
- the waveform was a triangular wave, and was held for 60 minutes during compression.
- These test conditions simulate the operating conditions of the gas turbine, and the turbine blade surface temperature was assumed to be 900 ° C. during steady state and 400 ° C. during stoppage. Further, the temperature raising / lowering speed is 166.7 ° C./min.
- FIG. 3 a 75% Na 2 SO 4 + 25% NaCl component salt was heated and melted at 900 ° C., and the sample was immersed in the molten salt for 20 hours to conduct a sulfide corrosion test.
- the vertical axis in FIG. 3 shows the sulfide corrosion weight loss in terms of length.
- the alloy of the present invention has a creep property at 900 ° C./392 MPa of 600 hours or more, a creep property at 1000 ° C./245 MPa of 160 hours or more, a TMF property of 200 times or more under the above conditions, and a corrosion weight loss of 0 0.001 mm or less. It is confirmed that a Ni-based single crystal superalloy excellent in TMF characteristics, creep characteristics and sulfidation corrosion resistance is obtained.
- Ni-based single crystal superalloy of the present invention is excellent in TMF characteristics, creep characteristics and sulfidation corrosion resistance, and is suitable as a high temperature member used under high temperature and high stress.
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Abstract
Description
Co:8~12%、
Cr:5~7.5%、
Mo:0.2~1.2%、
W:5~7%、
Al:5~6.5%、
Ta:8~12%、
Hf:0.01~0.2%、
Re:2~4%、
Si:0.005~0.1%
を含有し、残部がNiおよび不可避的不純物からなる化学組成を有し、単結晶であることを特徴としている。
質量%で、
Co:8~11%、
Cr:5~7%、
Mo:0.2~1%、
W:5.5~7%、
Al:5~6%、
Ta:9~12%、
Hf:0.05~0.2%、
Re:2.5~4%、
Si:0.005~0.08%
を含有し、残部がNiおよび不可避的不純物からなる化学組成を有し、単結晶であることを特徴としている。
質量%で、
Co:8~10%、
Cr:6~7%、
Mo:0.5~1%、
W:5.5~6.5%、
Al:5~6%、
Ta:9~11%、
Hf:0.05~0.15%、
Re:2.5~3.5%、
Si:0.005~0.08%
を含有し、残部がNiおよび不可避的不純物からなる化学組成を有し、単結晶であることを特徴としている。
[実施例]
Claims (3)
- 質量%で、
Co:8~12%、
Cr:5~7.5%、
Mo:0.2~1.2%、
W:5~7%、
Al:5~6.5%、
Ta:8~12%、
Hf:0.01~0.2%、
Re:2~4%、
Si:0.005~0.1%
を含有し、残部がNiおよび不可避的不純物からなる化学組成を有し、単結晶であることを特徴とするNi基単結晶超合金。 - 質量%で、
Co:8~11%、
Cr:5~7%、
Mo:0.2~1%、
W:5.5~7%、
Al:5~6%、
Ta:9~12%、
Hf:0.05~0.2%、
Re:2.5~4%、
Si:0.005~0.08%
を含有し、残部がNiおよび不可避的不純物からなる化学組成を有し、単結晶であることを特徴とする請求項1に記載のNi基単結晶合金。 - 質量%で、
Co:8~10%、
Cr:6~7%、
Mo:0.5~1%、
W:5.5~6.5%、
Al:5~6%、
Ta:9~11%、
Hf:0.05~0.15%、
Re:2.5~3.5%、
Si:0.005~0.08%
を含有し、残部がNiおよび不可避的不純物からなる化学組成を有し、単結晶であることを特徴とする請求項2に記載のNi基単結晶合金。
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CA2749755A CA2749755C (en) | 2009-01-15 | 2010-01-15 | Ni-based single crystal superalloy |
EP10731301.7A EP2381000B1 (en) | 2009-01-15 | 2010-01-15 | Ni-based single crystal superalloy |
US13/144,748 US8900512B2 (en) | 2009-01-15 | 2010-01-15 | Ni-based single crystal superalloy |
CN2010800045549A CN102282276B (zh) | 2009-01-15 | 2010-01-15 | Ni基单晶超合金 |
Applications Claiming Priority (2)
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JP2009006746A JP5439822B2 (ja) | 2009-01-15 | 2009-01-15 | Ni基単結晶超合金 |
JP2009-006746 | 2009-01-15 |
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WO2010082632A1 true WO2010082632A1 (ja) | 2010-07-22 |
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PCT/JP2010/050428 WO2010082632A1 (ja) | 2009-01-15 | 2010-01-15 | Ni基単結晶超合金 |
Country Status (7)
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US (1) | US8900512B2 (ja) |
EP (1) | EP2381000B1 (ja) |
JP (1) | JP5439822B2 (ja) |
KR (1) | KR101618649B1 (ja) |
CN (1) | CN102282276B (ja) |
CA (1) | CA2749755C (ja) |
WO (1) | WO2010082632A1 (ja) |
Cited By (1)
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JP2010163659A (ja) * | 2009-01-15 | 2010-07-29 | National Institute For Materials Science | Ni基単結晶超合金 |
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JP2012027113A (ja) | 2010-07-21 | 2012-02-09 | Ricoh Co Ltd | 投射光学系及び画像投射装置 |
CA2867489A1 (en) | 2012-03-30 | 2013-10-03 | Pacific Biosciences Of California, Inc. | Methods and composition for sequencing modified nucleic acids |
JP6016016B2 (ja) * | 2012-08-09 | 2016-10-26 | 国立研究開発法人物質・材料研究機構 | Ni基単結晶超合金 |
JP6730936B2 (ja) | 2014-05-27 | 2020-08-05 | クエステック イノベーションズ リミテッド ライアビリティ カンパニー | 高度に加工性の単結晶性ニッケル合金 |
CN111235433B (zh) * | 2020-01-16 | 2021-10-08 | 成都航宇超合金技术有限公司 | 用于制备镍基单晶叶片的籽晶合金 |
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- 2009-01-15 JP JP2009006746A patent/JP5439822B2/ja active Active
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2010
- 2010-01-15 WO PCT/JP2010/050428 patent/WO2010082632A1/ja active Application Filing
- 2010-01-15 CA CA2749755A patent/CA2749755C/en active Active
- 2010-01-15 EP EP10731301.7A patent/EP2381000B1/en active Active
- 2010-01-15 CN CN2010800045549A patent/CN102282276B/zh active Active
- 2010-01-15 US US13/144,748 patent/US8900512B2/en active Active
- 2010-01-15 KR KR1020117015971A patent/KR101618649B1/ko active Search and Examination
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EP2381000B1 (en) | 2016-06-01 |
JP2010163659A (ja) | 2010-07-29 |
KR101618649B1 (ko) | 2016-05-09 |
CA2749755C (en) | 2016-10-11 |
CA2749755A1 (en) | 2010-07-22 |
JP5439822B2 (ja) | 2014-03-12 |
CN102282276B (zh) | 2013-09-25 |
EP2381000A4 (en) | 2015-02-25 |
KR20110106352A (ko) | 2011-09-28 |
EP2381000A1 (en) | 2011-10-26 |
US20120014832A1 (en) | 2012-01-19 |
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