EP0325760A1 - Werkstück aus einer oxyddispersionsgehärteten Superlegierung auf der Basis von Nickel - Google Patents
Werkstück aus einer oxyddispersionsgehärteten Superlegierung auf der Basis von Nickel Download PDFInfo
- Publication number
- EP0325760A1 EP0325760A1 EP88121056A EP88121056A EP0325760A1 EP 0325760 A1 EP0325760 A1 EP 0325760A1 EP 88121056 A EP88121056 A EP 88121056A EP 88121056 A EP88121056 A EP 88121056A EP 0325760 A1 EP0325760 A1 EP 0325760A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- weight
- boron
- hardened
- oxide dispersion
- nickel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Ceased
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Classifications
-
- 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
- C22C32/001—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 with only oxides
- C22C32/0015—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 with only oxides with only single oxides as main non-metallic constituents
- C22C32/0026—Matrix based on Ni, Co, Cr or alloys thereof
Definitions
- Oxide dispersion-hardened superalloys based on nickel which thanks to their excellent mechanical properties are used at high temperatures in the construction of thermally and mechanically highly stressed thermal machines. Preferred use as blade materials for gas turbines.
- the invention relates to the further development of oxide-dispersion-hardened nickel-based superalloys with overall optimal properties, in particular with regard to behavior during secondary recrystallization, in order to achieve coarse-grained structure and for the production of single crystals of large dimensions.
- It also relates to a method for expanding the temperature range of the secondary recrystallization of an oxide-dispersion-hardened nickel-based superalloy during the coarse grain annealing of a workpiece and during annealing to produce a single crystal of large dimensions with a cross section of at least 5 cm 2.
- high-temperature super alloys have been developed, particularly for components of thermal machines (gas turbine blades). These are nickel-based alloys that contain finely divided dispersoids in the form of oxides. Most often, the latter are Y2O3 particles.
- the alloys are used in the state of coarse-grained stem crystals aligned in the longitudinal axis of the component. The coarser the crystals, the better the mechanical high-temperature properties (resistance to creep and fatigue strength with a comparatively low number of load cycles, etc.).
- the desired structural state is attempted by means of an annealing process of the forged, hot-pressed or mostly extruded, fine-grained semi-finished product, with "zone annealing" playing a dominant role.
- the workpiece is briefly heated in zones above the recrystallization temperature, the highest possible temperature / displacement gradient having to be achieved during the heating. This applies to the entire workpiece cross section. In the case of large cross sections, this requirement encounters difficulties because of the transverse heat flow required for this. Only the temperature range between recrystallization and solidus temperature (occurrence of the first liquid phase) is available as a "window" for carrying out the annealing process. This area is relatively narrow in the case of the conventional, commercially available oxide-dispersion-hardened nickel-based superalloys and is not sufficient to successfully convert large-diameter workpieces into coarse grains and, ideally, into a single crystal.
- the alloy with the trade name MA6000 from INCO is cited as prior art and an example of a known conventional precipitation-hardenable, oxide-dispersion-strengthened nickel-base superalloy (cf. DE-A-23 53 971).
- Corresponding alloys with a comparatively low chromium content are also known (see K.Mino and K.Asakawa, "An oxide dispersion strengthened nickel-base superalloy with excellent high temperature strength", Transactions of the Iron and Steel Institute of Japan, Vol. 27 , p. 823-829, Tokyo 1987).
- the invention is based on the object of specifying oxide-dispersion-hardened nickel-based superalloys which have a wider range of temperature limits than known alloys for carrying out the annealing required for producing coarse grains (secondary recrystallization).
- the task consists in particular in specifying a method for expanding the temperature range of the secondary recrystallization, which allows suitable methods Annealing processes (eg "zone annealing") to produce even single crystals of large dimensions (cross section at least 5 cm2).
- oxide-dispersion-hardened nickel-base superalloy is doped with a boron content of more than 0.011% by weight in the process mentioned at the outset.
- 1 shows a diagram of the course of the recrystallization temperature and the solidus temperature as a function of the boron content of an oxide-dispersion-hardened nickel-base superalloy with 15% by weight of chromium.
- 1 is the curve for the course of the recrystallization temperature
- 2 the curve for the course of the solidus temperature.
- ⁇ T is the maximum temperature range available for secondary recrystallization. No recrystallization takes place below curve 1 and annealing with the aim of growing coarse grain or even a single crystal is pointless. Liquid phases appear above curve 2 and the crystal structure is destroyed. The dispersoids agglomerate and become ineffective as a hardening factor.
- curve 2 the solidus temperature decreases slightly with increasing boron content, but the recrystallization temperature according to curve 1 increases significantly, which increases ⁇ T.
- 3 relates to a diagram of the course of the recrystallization temperature and the solidus temperature as a function of the boron content of an oxide-dispersion-hardened nickel-base superalloy with 17% by weight of chromium.
- 5 is the curve for the course of the recrystallization temperature, 6 that for the course of the solidus temperature.
- the temperature range ⁇ T is approx. 145 ° C.
- FIG. 4 is a diagram of the course of the recrystallization temperature and the solidus temperature as a function of the boron Ge of an oxide dispersion hardened nickel-base superalloy with a low chromium content. In the present case, the latter was approximately 6% by weight. 7 is the curve for the course of the recrystallization temperature, 8 is the curve for the course of the solidus temperature. With a boron content of 0.04% by weight, the temperature range ⁇ T is approx. 140 ° C.
- a prismatic body 20 mm thick, 50 mm wide and 180 mm long was subjected to a zone annealing process from the above material with 0.04% by weight boron. Longitudinal stem crystals with an average of 25 mm wide, 8 mm thick and 60 mm long could be obtained.
- the investigation referred to a fine-grained oxide dispersion hardened nickel-base superalloy as delivered.
- a fine-grained oxide dispersion-hardened nickel-base superalloy extruded in the delivered condition was subjected to the test.
- a cylindrical body 40 mm in diameter and 200 mm in length was worked out from the above material with 0.035% by weight of boron and subjected to a zone annealing process.
- the recrystallized structure consisted of longitudinal stem crystals with an average thickness of 10 mm on all sides and 130 mm in length.
- a fine-grained oxide dispersion-hardened nickel-base superalloy with a row structure that was hot-kneaded as delivered was examined.
- a semi-cylindrical body 55 mm in diameter and 220 mm in length was made from the above material with 0.045% by weight of boron worked out.
- the workpiece was subjected to a zone annealing process to produce a single crystal.
- the invention is not restricted to the exemplary embodiments.
- the new method relates to the expansion of the temperature range of the secondary recrystallization of an oxide-dispersion-hardened nickel-based superalloy during the coarse-grain annealing of a workpiece and during annealing to produce a single crystal of large dimensions with a cross section of at least 10 cm2, the oxide-dispersion-hardened nickel-based superalloy with a boron content of more is doped as 0.011% by weight.
- the doping is preferably 0.026 to 0.3% by weight of boron or 0.026 to 0.1% by weight of boron.
- the advantages of the claimed alloys and the new process lie in that created by expanding the temperature range of the secondary recrystallization greater freedom of the annealing process, especially the zone annealing process. This enables the complete, flawless recrystallization to coarse, longitudinally oriented stem crystals in the case of large workpiece cross sections to be treated. This applies even more to the annealing of a workpiece for the production of a single crystal of large dimensions.
- the new process made it possible to manufacture single-section turbine blades with a large cross-section, as required for modern high-performance industrial gas turbines.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
- Powder Metallurgy (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CH159/88A CH674019A5 (ja) | 1988-01-18 | 1988-01-18 | |
CH159/88 | 1988-01-18 |
Publications (1)
Publication Number | Publication Date |
---|---|
EP0325760A1 true EP0325760A1 (de) | 1989-08-02 |
Family
ID=4180599
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP88121056A Ceased EP0325760A1 (de) | 1988-01-18 | 1988-12-16 | Werkstück aus einer oxyddispersionsgehärteten Superlegierung auf der Basis von Nickel |
Country Status (3)
Country | Link |
---|---|
US (1) | US4995922A (ja) |
EP (1) | EP0325760A1 (ja) |
CH (1) | CH674019A5 (ja) |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0447858A1 (de) * | 1990-03-20 | 1991-09-25 | Asea Brown Boveri Ag | Verfahren zur Erzeugung von längsgerichteten grobkörnigen Stengelkristallen in einem aus einer oxyddispersionsgehärteten Nickelbasis-Superlegierung bestehenden Werkstück |
WO1992013179A1 (en) * | 1991-01-23 | 1992-08-06 | Man B&W Diesel A/S | Valve with hard-facing |
EP0525816A1 (en) * | 1991-08-02 | 1993-02-03 | Isover Saint-Gobain | Method and apparatus for manufacturing mineral wool, and mineral wool produced thereby |
EP0583791A1 (en) * | 1992-08-20 | 1994-02-23 | Isover Saint-Gobain | Method for producing mineral wool, and mineral wool produced thereby |
EP1903121A1 (en) * | 2006-09-21 | 2008-03-26 | Honeywell International, Inc. | Nickel-based alloys and articles made therefrom |
EP2431489A1 (en) * | 2010-09-20 | 2012-03-21 | Siemens Aktiengesellschaft | Nickel-base superalloy |
CN111379028A (zh) * | 2020-04-08 | 2020-07-07 | 中国科学院金属研究所 | 一种Ni-Al二元单晶合金、Ni-Al二元模型单晶合金及其制备方法 |
Families Citing this family (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5427601A (en) * | 1990-11-29 | 1995-06-27 | Ngk Insulators, Ltd. | Sintered metal bodies and manufacturing method therefor |
US5316866A (en) * | 1991-09-09 | 1994-05-31 | General Electric Company | Strengthened protective coatings for superalloys |
US5712050A (en) * | 1991-09-09 | 1998-01-27 | General Electric Company | Superalloy component with dispersion-containing protective coating |
US5455119A (en) * | 1993-11-08 | 1995-10-03 | Praxair S.T. Technology, Inc. | Coating composition having good corrosion and oxidation resistance |
US20070144622A1 (en) * | 2002-11-04 | 2007-06-28 | Flahaut Dominique M L | High temperature resistant alloys |
GB2394959A (en) * | 2002-11-04 | 2004-05-12 | Doncasters Ltd | Hafnium particle dispersion hardened nickel-chromium-iron alloys |
IT1394975B1 (it) * | 2009-07-29 | 2012-08-07 | Nuovo Pignone Spa | Superlega a base di nichel, componente meccanico realizzato con detta superlega, turbomacchina comprendente tale componente e metodi relativi |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2204700A1 (ja) * | 1972-10-30 | 1974-05-24 | Int Nickel Ltd | |
US4386976A (en) * | 1980-06-26 | 1983-06-07 | Inco Research & Development Center, Inc. | Dispersion-strengthened nickel-base alloy |
Family Cites Families (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4668312A (en) * | 1985-03-13 | 1987-05-26 | Inco Alloys International, Inc. | Turbine blade superalloy I |
-
1988
- 1988-01-18 CH CH159/88A patent/CH674019A5/de not_active IP Right Cessation
- 1988-12-16 EP EP88121056A patent/EP0325760A1/de not_active Ceased
-
1989
- 1989-01-11 US US07/295,559 patent/US4995922A/en not_active Expired - Fee Related
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2204700A1 (ja) * | 1972-10-30 | 1974-05-24 | Int Nickel Ltd | |
US4386976A (en) * | 1980-06-26 | 1983-06-07 | Inco Research & Development Center, Inc. | Dispersion-strengthened nickel-base alloy |
Cited By (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0447858A1 (de) * | 1990-03-20 | 1991-09-25 | Asea Brown Boveri Ag | Verfahren zur Erzeugung von längsgerichteten grobkörnigen Stengelkristallen in einem aus einer oxyddispersionsgehärteten Nickelbasis-Superlegierung bestehenden Werkstück |
US5180451A (en) * | 1990-03-20 | 1993-01-19 | Asea Brown Boveri Ltd. | Process for the production of longitudinally-directed coarse-grained columnar crystals in a workpiece consisting of an oxide-dispersion-hardened nickel-based superalloy |
WO1992013179A1 (en) * | 1991-01-23 | 1992-08-06 | Man B&W Diesel A/S | Valve with hard-facing |
EP0525816A1 (en) * | 1991-08-02 | 1993-02-03 | Isover Saint-Gobain | Method and apparatus for manufacturing mineral wool, and mineral wool produced thereby |
WO1993002977A1 (en) * | 1991-08-02 | 1993-02-18 | Isover Saint-Gobain | Method and apparatus for manufacturing mineral wood, and mineral wool produced thereby |
US6158249A (en) * | 1991-08-02 | 2000-12-12 | Isover Saint-Gobain | Apparatus for manufacturing mineral wool |
WO1994004468A1 (en) * | 1992-08-20 | 1994-03-03 | Isover Saint-Gobain | Method for producing mineral wool, and mineral wool produced thereby |
EP0583791A1 (en) * | 1992-08-20 | 1994-02-23 | Isover Saint-Gobain | Method for producing mineral wool, and mineral wool produced thereby |
EP1903121A1 (en) * | 2006-09-21 | 2008-03-26 | Honeywell International, Inc. | Nickel-based alloys and articles made therefrom |
US7824606B2 (en) | 2006-09-21 | 2010-11-02 | Honeywell International Inc. | Nickel-based alloys and articles made therefrom |
EP2431489A1 (en) * | 2010-09-20 | 2012-03-21 | Siemens Aktiengesellschaft | Nickel-base superalloy |
WO2012038166A2 (en) | 2010-09-20 | 2012-03-29 | Siemens Aktiengesellschaft | Nickel-base superalloy |
WO2012038166A3 (en) * | 2010-09-20 | 2012-09-07 | Siemens Aktiengesellschaft | Nickel-base superalloy |
US9593583B2 (en) | 2010-09-20 | 2017-03-14 | Siemens Aktiengesellschaft | Nickel-base superalloy |
CN111379028A (zh) * | 2020-04-08 | 2020-07-07 | 中国科学院金属研究所 | 一种Ni-Al二元单晶合金、Ni-Al二元模型单晶合金及其制备方法 |
Also Published As
Publication number | Publication date |
---|---|
CH674019A5 (ja) | 1990-04-30 |
US4995922A (en) | 1991-02-26 |
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Legal Events
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PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
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AK | Designated contracting states |
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17P | Request for examination filed |
Effective date: 19900118 |
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17Q | First examination report despatched |
Effective date: 19910916 |
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STAA | Information on the status of an ep patent application or granted ep patent |
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Effective date: 19940409 |