EP0260465B1 - Oxide dispersion-strengthened nickel-base superalloy with improved corrosion resistance - Google Patents
Oxide dispersion-strengthened nickel-base superalloy with improved corrosion resistance Download PDFInfo
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- EP0260465B1 EP0260465B1 EP87112012A EP87112012A EP0260465B1 EP 0260465 B1 EP0260465 B1 EP 0260465B1 EP 87112012 A EP87112012 A EP 87112012A EP 87112012 A EP87112012 A EP 87112012A EP 0260465 B1 EP0260465 B1 EP 0260465B1
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- oxide dispersion
- corrosion resistance
- improved corrosion
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- 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 at high temperatures, are used thermally and mechanically under high stress during construction of 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 with regard to high-temperature strength, long-term stability and resistance to oxidation and corrosion in an aggressive atmosphere.
- Ni rest (See HF Merrick, LR Curwick and YG Kim, Nasa Report CR-135150, Contract NAS-3-19694, 1977, Cleveland, Ohio, USA and RC Benn, LR Curwick and GAJ hack, Powder Met. 1981, No. 4 , p. 191-195).
- This alloy which has increased Cr and Al contents compared to MA 6000, has improved corrosion resistance, but tends to become unstable due to the formation of brittle phases in certain temperature ranges, which deteriorate the mechanical properties.
- the invention has for its object an oxide dispersion hardened superalloy based on nickel Specify which, while maintaining the highest possible heat resistance, in particular creep limit, while avoiding the formation of brittle phases, has an increased resistance to sulfidation.
- the alloy should be stable over the long term and should not change even over a long period of operation.
- a melt of the above composition was prepared, but without the addition of Y2O3 and converted into a powder by gas atomization using argon under high pressure.
- the powder was comparatively coarse. Particles with a diameter of over 300 ⁇ m were retained using a sieve. The fractions below were used again.
- the alloy powder was mixed with fine Y2O3 powder with a maximum particle diameter of 1 ⁇ m and a maximum crystallite diameter of 100 nm. Then the powder mixture was mechanically alloyed in the attritor for 36 hours under an argon atmosphere.
- the Attritor 5-1 from Netzsch, Federal Republic of Germany had a volume of 3 liters and a filling of 12 kg steel balls. The capacity for the powder was 1 kg.
- the mechanical properties were examined. In particular, the creep rupture strength (creep limit) for a period of 5. 104 h measured at different temperatures. The values were: Temperature (° C) Creep rupture strength (MPa) 800 215 900 158 1000 138
- the resistance to oxidation and corrosion was better than that of the known alloy with the trade name MA 6000.
- Samples with a smooth surface were subjected to a temperature cycle in air and the specific weight change per unit area was determined after 1000 cycles.
- One cycle lasted approximately one hour: the test specimen was heated to a temperature of 1000 ° C. and left at this temperature for 1 hour. Then, it was cooled and reheated at a rate of 500 ° C / min, and so on.
- the change in weight is a measure of the resistance to oxidation.
- the change in weight was + 0.5 mg / cm2 surface
- the creep rupture strength measured on samples for a period of 5.104 h as a function of temperature was: Temperature (° C) Creep rupture strength (MPa) 800 221 900 165 1000 140
- the resistance to oxidation was determined by weight change as defined in Example I and was + 0.5 mg / cm2 surface.
- the creep rupture strength measured on samples for a period of 5 ⁇ 104 h as a function of temperature was: Temperature (° C) Creep rupture strength (MPa) 800 205 900 145 1000 115
- the resistance to oxidation was determined by weight change as defined in Example I and was + 0.4 mg / cm2 surface.
- the invention is not restricted to the exemplary embodiments.
- the hafnium improves cross-strength in particular.
- Cobalt increases strength and improves workability
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- Mechanical Engineering (AREA)
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Description
Oxyddispersionsgehärtete Superlegierungen auf der Basis von Nickel, welche dank ihrer hervorragenden mechanischen Eigenschaften bei hohen Temperaturen beim Bau thermisch und mechanisch hochbeanspruchtër thermischer Maschinen Verwendung finden. Bevorzugte Verwendung als Schaufelwerkstoffe für Gasturbinen.Oxide dispersion-hardened superalloys based on nickel, which, thanks to their excellent mechanical properties at high temperatures, are used thermally and mechanically under high stress during construction of thermal machines. Preferred use as blade materials for gas turbines.
Die Erfindung bezieht sich auf die Weiterentwicklung von oxyddispersionsgehärteten Nickelbasis-Superlegierungen mit insgesamt optimalen Eigenschaften bezüglich Hochtemperaturfestigkeit, Langzeitstabilität und Widerstand gegen Oxydation und Korrosion in agressiver Atmosphäre.The invention relates to the further development of oxide dispersion-hardened nickel-based superalloys with overall optimal properties with regard to high-temperature strength, long-term stability and resistance to oxidation and corrosion in an aggressive atmosphere.
Insbesondere betrifft sie eine oxyddispersionsgehärtete Superlegierung mit verbesserter Korrosionsbeständigkeit auf der Basis von Nickel.In particular, it relates to an oxide dispersion hardened superalloy with improved corrosion resistance based on nickel.
Zum Stand der Technik wird folgende Literatur zitiert:
- G.H. Gessinger, Powder Metallurgy of Superalloys, Butterworths, London, 1984
- R.F. Singer and E. Arzt, To be published in: Conf. Proc. "High Temperature Materials for Gas Turbines", Liège, Belgium, Oktober 1986
- J.S. Benjamin, Metall. Trans., 1970, 1, 2943 - 2951.
- GH Gessinger, Powder Metallurgy of Superalloys, Butterworths, London, 1984
- RF Singer and E. Arzt, To be published in: Conf. Proc. "High Temperature Materials for Gas Turbines", Liège, Belgium, October 1986
- JS Benjamin, metal. Trans., 1970, 1, 2943-2951.
Im Verlauf der vergangenen Jahre ist eine neue Klasse von hochwarmfesten Superlegierungen, insbesondere für Bauteile thermischer Maschinen (Gasturbinenschaufeln) entwickelt worden. Es handelt sich um Nickelbasislegierungen, welche fein verteilte Dispersoide in Form von Oxyden enthalten. Meistens handelt es sich bei letzteren um Y₂0₃-Partikel. Eine der bekanntesten derartigen oxyddispersionsgehärteten Legierungen ist die von INCO unter dem Handelsnamen MA 6000 erhältliche Nickelbasislegierung folgender Zusammensetzung:
Cr = 15,0 Gew.-%
Al = 4,5 Gew.-%
Ti = 2,5 Gew.-%
Mo = 2,0 Gew.-%
N = 4,0 Gew.-%
Ta = 2,0 Gew.-%
Zr = 0,15 Gew.-%
B = 0,01 Gew.-%
C = 0,05 Gew.-%
Y₂O₃ = 1,1 Gew.-%
Ni = Rest
(Vergl. H.F. Merrick, L.R. Curwick and Y.G. Kim, Nasa Report CR-135150, Contract NAS-3-19694, 1977, Cleveland, Ohio, USA und R.C. Benn, L.R. Curwick and G.A.J. Hack, Powder Met. 1981, No. 4, p. 191-195).Over the past few years, a new class of high-temperature super alloys has 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 Y₂0₃ particles. One of the best known oxide dispersion hardened alloys of this type is the nickel-base alloy of the following composition, available from INCO under the trade name MA 6000:
Cr = 15.0% by weight
Al = 4.5% by weight
Ti = 2.5% by weight
Mo = 2.0% by weight
N = 4.0% by weight
Ta = 2.0% by weight
Zr = 0.15% by weight
B = 0.01% by weight
C = 0.05% by weight
Y₂O₃ = 1.1% by weight
Ni = rest
(See HF Merrick, LR Curwick and YG Kim, Nasa Report CR-135150, Contract NAS-3-19694, 1977, Cleveland, Ohio, USA and RC Benn, LR Curwick and GAJ Hack, Powder Met. 1981, No. 4 , p. 191-195).
Obwohl diese Legierung bei hohen Temperaturen vorzügliche mechanische Eigenschaften hat, genügt sie im Hinblick auf Oxydations- und Sulfidationsbeständigkeit in zahlreichen Verwendungsfällen den Anforderungen des Betriebes nicht.Although this alloy has excellent mechanical properties at high temperatures, it does not meet the requirements of the company in numerous applications with regard to resistance to oxidation and sulfidation.
Um die Antikorrosionseigenschaften zu verbessern, hat INCO eine neue Legierung entwickelt. Sie hat folgende Zusammensetzung:
Cr = 20,0 Gew.-%
Al = 6,0 Gew.-%
Mo = 2,0 Gew.-%
W = 3,5 Gew.-%
Zr = 0,19 Gew.-%
B = 0,01 Gew.-%
C = 0,05 Gew.-%
Y₂O₃ = 1,1 Gew.-%
Ni = RestINCO has developed a new alloy to improve the anti-corrosion properties. It has the following composition:
Cr = 20.0% by weight
Al = 6.0% by weight
Mo = 2.0% by weight
W = 3.5% by weight
Zr = 0.19% by weight
B = 0.01% by weight
C = 0.05% by weight
Y₂O₃ = 1.1% by weight
Ni = rest
Diese, gegenüber MA 6000 erhöhte Cr- und Al-Gehalte aufweisende Legierung hat zwar verbesserte Korrosionsbeständigkeit, neigt aber durch Bildung spröder Phasen in bestimmten Temperaturbereichen zu Instabilitäten, welche die mechanischen Eigenschaften verschlechtern.This alloy, which has increased Cr and Al contents compared to MA 6000, has improved corrosion resistance, but tends to become unstable due to the formation of brittle phases in certain temperature ranges, which deteriorate the mechanical properties.
Der Erfindung liegt die Aufgabe zugrunde, eine oxyddispersionsgehärtete Superlegierung auf der Basis von Nickel anzugeben, die bei Wahrung höchstmöglicher Warmfestigkeit, insbesondere Kriechgrenze, unter Vermeidung der Bildung von spröden Phasen eine erhöhte Beständigkeit gegen Sulfidation aufweist. Die Legierung soll langzeitstabil sein und sich auch im Verlaufe längerer Betriebsdauer nicht verändern.The invention has for its object an oxide dispersion hardened superalloy based on nickel Specify which, while maintaining the highest possible heat resistance, in particular creep limit, while avoiding the formation of brittle phases, has an increased resistance to sulfidation. The alloy should be stable over the long term and should not change even over a long period of operation.
Diese Aufgabe wird durch die in den Ansprüchen gekennzeichnete Erfindung gelöst.This object is achieved by the invention characterized in the claims.
Die Erfindung wird anhand der nachfolgenden Ausführungsbeispiele erläutert.The invention is explained using the following exemplary embodiments.
Es wurde eine Legierung der nachfolgenden Zusammensetzung hergestellt:
Cr = 17,0 Gew.-%
Al = 6,0 Gew.-%
Mo = 2,0 Gew.-%
W = 3,5 Gew.-%
Ta = 2,0 Gew.-%
Zr = 0,15 Gew.-%
B = 0,01 Gew.-%
C = 0,05 Gew.-%
Y₂O₃ = 1,1 Gew.-%
Ni = Rest
An alloy of the following composition was produced:
Cr = 17.0% by weight
Al = 6.0% by weight
Mo = 2.0% by weight
W = 3.5% by weight
Ta = 2.0% by weight
Zr = 0.15% by weight
B = 0.01% by weight
C = 0.05% by weight
Y₂O₃ = 1.1% by weight
Ni = rest
Zunächst wurde eine Schmelze obiger Zusammensetzung, jedoch ohne Y₂O₃-Zusatz hergestellt und durch Gaszerstäubung mittels Argon unter hohem Druck in ein Pulver übergeführt. Das Pulver war vergleichsweise grobkörnig. Partikel von über 300 µm Durchmesser wurden mittels Sieb zurückgehalten. Die darunter liegenden Fraktionen wurden weiter verwendet. Das Legierungspulver wurde mit feinem Y₂O₃-Pulver mit maximalem Partikeldurchmesser von 1 µm bei maximalem Kristallitdurchmesser von 100 nm gemischt. Dann wurde die Pulvermischung während 36 h unter Argonatmosphäre im Attritor mechanisch legiert. Der Attritor 5-1, Fa. Netzsch, Bundesrepublik Deutschland hatte 3 Liter Inhalt und eine Füllung von 12 kg Stahlkugeln. Die Kapazität für das Pulver betrug 1 kg.First, a melt of the above composition was prepared, but without the addition of Y₂O₃ and converted into a powder by gas atomization using argon under high pressure. The powder was comparatively coarse. Particles with a diameter of over 300 µm were retained using a sieve. The fractions below were used again. The alloy powder was mixed with fine Y₂O₃ powder with a maximum particle diameter of 1 µm and a maximum crystallite diameter of 100 nm. Then the powder mixture was mechanically alloyed in the attritor for 36 hours under an argon atmosphere. The Attritor 5-1, from Netzsch, Federal Republic of Germany had a volume of 3 liters and a filling of 12 kg steel balls. The capacity for the powder was 1 kg.
Das mechanisch legierte Pulver wurde nun in eine Dose aus weichem Stahl von 73 mm Aussendurchmesser und 75 mm Höhe abgefüllt. Das Ganze wurde unter Vakuum auf 300°C erhitzt und die Dose luftdicht verschweisst. Nun wurde das eingekapselte Pulver in einer Strangpresse bei einer Temperatur von 975°C zu einer Stange verpresst. Diese hatte einen Durchmesser von ca. 19,5 mm (Reduktionsverhältnis der Strangpresse = 14:1). Die Stahloberflächenschicht wurde durch Abdrehen entfernt, so dass die Stange schliesslich einen Durchmesser von 18 mm aufwies. Die Stange wurde nun einem Zonenglühprozess unterworfen.The mechanically alloyed powder was then filled into a can made of soft steel with an outside diameter of 73 mm and a height of 75 mm. The whole was heated to 300 ° C under vacuum and the can sealed airtight. The encapsulated powder was then pressed into a rod in an extruder at a temperature of 975 ° C. This had a diameter of approx. 19.5 mm (reduction ratio of the extrusion press = 14: 1). The steel surface layer was removed by twisting, so that the rod finally had a diameter of 18 mm. The rod has now been subjected to a zone annealing process.
Mit einem Temperaturgradienten, welcher den Wert von 8°C/mm überstieg, wurden längsgerichtete Körner mit einem Längen- zu Breitenverhältnis von mehr als 10 erreicht.With a temperature gradient that exceeded 8 ° C / mm, longitudinal grains with a length to width ratio of more than 10 were achieved.
Die mechanischen Eigenschaften wurden untersucht. Insbesondere wurde die Zeitstandfestigkeit (Kriechgrenze) für eine Zeitdauer von 5 . 10⁴ h bei verschiedenen Temperaturen gemessen. Die Werte betrugen:
Der Oxydations- und Korrosionswiderstand war besser als derjenige der bekannten Legierung mit dem Handelsnamen MA 6000.The resistance to oxidation and corrosion was better than that of the known alloy with the trade name MA 6000.
Es wurden Proben mit glatter Oberfläche einem Temperaturzyklus in Luft unterworfen und die spezifische Gewichtsveränderung per Flächeneinheit nach 1000 Zyklen bestimmt. Ein Zyklus dauerte ungefähr eine Stunde: Der Probekörper wurde auf eine Temperatur von 1000 °C aufgeheizt und während 1h bei dieser Temperatur belassen. Dann wurde er mit einer Geschwindigkeit von 500 °C/min abgekühlt und wieder erhitzt, und so fort. Die Gewichtsveränderung ist ein Mass für die Oxydationsbeständigkeit.Samples with a smooth surface were subjected to a temperature cycle in air and the specific weight change per unit area was determined after 1000 cycles. One cycle lasted approximately one hour: the test specimen was heated to a temperature of 1000 ° C. and left at this temperature for 1 hour. Then, it was cooled and reheated at a rate of 500 ° C / min, and so on. The change in weight is a measure of the resistance to oxidation.
Im vorliegenden Fall betrug die Gewichtsveränderung
+ 0,5 mg/cm² Oberfläche
Im Vergleich die Legierung MA 6000
- 10,5 mg/cm²In the present case, the change in weight was
+ 0.5 mg / cm² surface
In comparison the alloy MA 6000
- 10.5 mg / cm²
Es wurde eine Legierung der nachfolgenden Zusammensetzung hergestellt.
Cr = 17,0 Gew.-%
Al = 6,0 Gew.-%
Mo = 2,0 Gew.-%
W = 3,5 Gew.-%
Ta = 2,0 Gew.-%
Hf = 1,0 Gew.-%
Zr = 0,15 Gew.-%
B = 0,01 Gew.-%
C = 0,05 Gew.-%
Y₂O₃ = 1,1 Gew.-%
Ni = RestAn alloy of the following composition was produced.
Cr = 17.0% by weight
Al = 6.0% by weight
Mo = 2.0% by weight
W = 3.5% by weight
Ta = 2.0% by weight
Hf = 1.0% by weight
Zr = 0.15% by weight
B = 0.01% by weight
C = 0.05% by weight
Y₂O₃ = 1.1% by weight
Ni = rest
Die Pulverherstellung und die Weiterverarbeitung erfolgte nach den unter Beispiel I angegebenen Verfahrensschritten.The powder production and further processing was carried out according to the process steps given in Example I.
Die an Proben gemessene Zeitstandfestigkeit (Kriechgrenze) für eine Zeitdauer von 5.10⁴ h betrug in Funktion der Temperatur:
Die Oxydationsbeständigkeit wurde durch Gewichtsveränderung gemäss Definition in Beispiel I bestimmt und betrug
+ 0,5 mg/cm² Oberfläche.The resistance to oxidation was determined by weight change as defined in Example I and was
+ 0.5 mg / cm² surface.
Es wurde eine Legierung der nachfolgenden Zusammensetzung hergestellt:
Cr = 17,0 Gew.-%
Al = 6,0 Gew.-%
Co = 10,0 Gew.-%
Ta = 5,0 Gew.-%
Zr = 0,15 Gew.-%
B = 0,01 Gew.-%
C = 0,05 Gew.-%
Y₂O₃ = 1,1 Gew.-%
Ni = RestAn alloy of the following composition was produced:
Cr = 17.0% by weight
Al = 6.0% by weight
Co = 10.0% by weight
Ta = 5.0% by weight
Zr = 0.15% by weight
B = 0.01% by weight
C = 0.05% by weight
Y₂O₃ = 1.1% by weight
Ni = rest
Die Pulverherstellung und die Weiterverarbeitung erfolgte nach den unter Beispiel I angegebenen Verfahrensschritten.The powder production and further processing was carried out according to the process steps given in Example I.
Die an Proben gemessene Zeitstandfestigkeit (Kriechgrenze) für eine Zeitdauer von 5`10⁴ h betrug in Funktion der Temperatur:
Die Oxydationsbeständigkeit wurde durch Gewichtsveränderung gemäss Definition in Beispiel I bestimmt und betrug
+ 0,4 mg/cm² Oberfläche.The resistance to oxidation was determined by weight change as defined in Example I and was
+ 0.4 mg / cm² surface.
Die Erfindung ist nicht auf die Ausführungsbeispiele beschränkt. Vorzugsweise können die Legierungen im Rahmen der nachfolgenden Zusammensetzungsgrenzen liegen:
Cr = 17 - 18 Gew.-%
Al = 6 - 7 Gew.-%
Mo = 2 - 2,5 Gew.-%
W = 3 - 3,5 Gew.-%
Ta = 2 - 2,5 Gew.-%
Zr < 0,2 Gew.-%
B < 0,02 Gew.-%
C < 0,1 Gew.-%
Y₂O₃ = 1 - 1,5 Gew.-%
Ni = RestThe invention is not restricted to the exemplary embodiments. The alloys can preferably be within the following composition limits:
Cr = 17-18% by weight
Al = 6-7% by weight
Mo = 2-2.5% by weight
W = 3 - 3.5% by weight
Ta = 2-2.5% by weight
Zr <0.2% by weight
B <0.02% by weight
C <0.1% by weight
Y₂O₃ = 1 - 1.5% by weight
Ni = rest
Eine weitere vorteilhafte Gruppe mit Hafniumzusatz hat die nachfolgende Zusammensetzung:
Cr = 17 - 18 Gew.-%
Al = 6 - 7 Gew.-%
Mo = 2 - 2,5 Gew.-%
W = 3 - 3,5 Gew.-%
Ta = 2 - 2,5 Gew.-%
Hf = 0,5 - 1,5 Gew.-%
Zr < 0,2 Gew.-%
B < 0,02 Gew.-%
C < 0,1 Gew.-%
Y₂O₃ = 1 - 1,5 Gew.-%
Ni = RestAnother advantageous group with hafnium addition has the following composition:
Cr = 17-18% by weight
Al = 6-7% by weight
Mo = 2-2.5% by weight
W = 3 - 3.5% by weight
Ta = 2-2.5% by weight
Hf = 0.5-1.5% by weight
Zr <0.2% by weight
B <0.02% by weight
C <0.1% by weight
Y₂O₃ = 1 - 1.5% by weight
Ni = rest
Das Hafnium verbessert insbesondere die Querfestigkeit.The hafnium improves cross-strength in particular.
Die Legierungen können gemäss nachfolgender Darstellung auch Kobalt als Legierungselement enthalten:
Cr = 16 - 18 Gew.-%
Al = 6 - 7 Gew.-%
Co = 8 - 10 Gew.-%
Ta = 5 - 7 Gew.-%
Zr < 0,2 Gew.-%
B < 0,02 Gew.-%
C < 0,1 Gew.-%
Y₂O₃ = 1 - 1,5 Gew.-%
Ni = RestAs shown below, the alloys can also contain cobalt as an alloying element:
Cr = 16-18% by weight
Al = 6-7% by weight
Co = 8-10% by weight
Ta = 5-7% by weight
Zr <0.2% by weight
B <0.02% by weight
C <0.1% by weight
Y₂O₃ = 1 - 1.5% by weight
Ni = rest
Kobalt steigert die Festigkeit und verbessert die Verarbeitbarkeit`Cobalt increases strength and improves workability
Insbesondere erweist sich auch die nachfolgende Zusammensetzung als vorteilhaft:
Cr = 17,0 Gew`-%
Al = 6,0 Gew.-%
Co = 8,0 Gew`-%
Ta = 6,5 Gew.-%
Zr = 0,15 Gew.-%
B = 0,01 Gew.-%
C = 0,05 Gew.-%
Y₂O₃ = 1,1 Gew.-%
Ni = RestIn particular, the following composition also proves to be advantageous:
Cr = 17.0% by weight
Al = 6.0% by weight
Co = 8.0% by weight
Ta = 6.5% by weight
Zr = 0.15% by weight
B = 0.01% by weight
C = 0.05% by weight
Y₂O₃ = 1.1% by weight
Ni = rest
Claims (7)
- Superalloy with oxide dispersion hardening having improved corrosion resistance and based on nickel, characterised in that it has the following composition:
Cr = 17 - 18% by weight,
Al = 6 - 7% by weight,
Mo = 2 - 2.5% by weight,
W = 3 - 3.5% by weight,
Ta = 2 - 2.5% by weight,
Zr < 0.2 % by weight,
B < 0.02 % by weight,
C < 0.1 % by weight,
Y₂O₃ = 1 - 1.5% by weight,
Ni = Remainder. - Superalloy with oxide dispersion hardening according to Claim 1, characterised by the following composition:
Cr = 17.0% by weight,
Al = 6.0% by weight,
Mo = 2.0% by weight,
W = 3.5% by weight,
Ta = 2.0% by weight,
Zr = 0.15% by weight,
B = 0.01% by weight,
C = 0.05% by weight,
Y₂O₃ = 1.1% by weight,
Ni = Remainder. - Superalloy with oxide dispersion hardening having improved corrosion resistance and based on nickel, characterised in that it has the following composition:
Cr = 17 - 18% by weight,
Al = 6 - 7% by weight,
Mo = 2 - 2.5% by weight,
W = 3 - 3.5% by weight,
Ta = 2 - 2.5% by weight,
Hf = 0.5 - 1.5% by weight,
Zr < 0.2 % by weight,
B < 0.02 % by weight,
C < 0.1 % by weight,
Y₂O₃ = 1 - 1.5% by weight,
Ni = Remainder. - Superalloy with oxide dispersion hardening according to Claim 3, characterised by the following composition:
Cr = 17.0% by weight,
Al = 6.0% by weight,
Mo = 2.0% by weight,
W = 3.5% by weight,
Ta = 2.0% by weight,
Hf = 1.0% by weight,
Zr = 0.15% by weight,
B = 0.01% by weight,
C = 0.05% by weight,
Y₂O₃ = 1.1% by weight,
Ni = Remainder. - Superalloy with oxide dispersion hardening having improved corrosion resistance and based on nickel, characterised in that it has the following composition:
Cr = 16 - 18% by weight,
Al = 6 - 7% by weight,
Co = 8 - 10% by weight,
Ta = 5 - 7% by weight,
Zr < 0.2 % by weight,
B < 0.02 % by weight,
C < 0.1 % by weight,
Y₂O₃ = 1 - 1.5% by weight,
Ni = Remainder. - Superalloy with oxide dispersion hardening according to Claim 5, characterised by the following composition:
Cr = 17.0% by weight,
Al = 6.0% by weight,
Co = 10.0% by weight,
Ta = 5.0% by weight,
Zr = 0.15% by weight,
B = 0.01% by weight,
C = 0.05% by weight,
Y₂O₃ = 1.1% by weight,
Ni = Remainder. - Superalloy with oxide dispersion hardening according to Claim 5, characterised by the following compositions:
Cr = 17.0% by weight,
Al = 6.0% by weight,
Co = 8.0% by weight,
Ta = 6.5% by weight,
Zr = 0.15% by weight,
B = 0.01% by weight,
C = 0.05% by weight,
Y₂O₃ = 1.1% by weight,
Ni = Remainder.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CH359386 | 1986-09-08 | ||
| CH3593/86 | 1986-09-08 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| EP0260465A1 EP0260465A1 (en) | 1988-03-23 |
| EP0260465B1 true EP0260465B1 (en) | 1992-01-02 |
Family
ID=4259333
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP87112012A Expired - Lifetime EP0260465B1 (en) | 1986-09-08 | 1987-08-19 | Oxide dispersion-strengthened nickel-base superalloy with improved corrosion resistance |
Country Status (5)
| Country | Link |
|---|---|
| US (1) | US4798625A (en) |
| EP (1) | EP0260465B1 (en) |
| JP (1) | JP2630323B2 (en) |
| DE (1) | DE3775671D1 (en) |
| NO (1) | NO873738L (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0398121B1 (en) * | 1989-05-16 | 1994-11-23 | Asea Brown Boveri Ag | Process for producing coarse columnar grains directionally oriented along their length in an oxide dispersion hardened nickel base superalloy |
| US5427601A (en) * | 1990-11-29 | 1995-06-27 | Ngk Insulators, Ltd. | Sintered metal bodies and manufacturing method therefor |
| DE4110543A1 (en) * | 1991-03-30 | 1992-10-01 | Pm Hochtemperatur Metall Gmbh | OXIDE DISPERSION HARDENED ELIGIBLE CHROME CHROME ALLOY |
| CZ290109B6 (en) * | 1991-08-02 | 2002-06-12 | Isover Saint-Gobain | Process for producing mineral wool from melted mineral material and apparatus for making the same |
| US6412465B1 (en) | 2000-07-27 | 2002-07-02 | Federal-Mogul World Wide, Inc. | Ignition device having a firing tip formed from a yttrium-stabilized platinum-tungsten alloy |
| JP2013181213A (en) * | 2012-03-01 | 2013-09-12 | Hokkaido Univ | Oxide dispersion strengthened nickel-base superalloy |
Family Cites Families (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3738817A (en) * | 1968-03-01 | 1973-06-12 | Int Nickel Co | Wrought dispersion strengthened metals by powder metallurgy |
| US3728088A (en) * | 1968-03-01 | 1973-04-17 | Int Nickel Co | Superalloys by powder metallurgy |
| US3776704A (en) * | 1968-03-01 | 1973-12-04 | Int Nickel Co | Dispersion-strengthened superalloys |
| US3754902A (en) * | 1968-06-05 | 1973-08-28 | United Aircraft Corp | Nickel base superalloy resistant to oxidation erosion |
| US3809545A (en) * | 1969-08-25 | 1974-05-07 | Int Nickel Co | Superalloys by powder metallurgy |
| US3660049A (en) * | 1969-08-27 | 1972-05-02 | Int Nickel Co | Dispersion strengthened electrical heating alloys by powder metallurgy |
| NL171309C (en) * | 1970-03-02 | 1983-03-01 | Hitachi Ltd | METHOD FOR THE MANUFACTURE OF A SEMICONDUCTOR BODY FORMING A SILICONE DIOXIDE LAYER ON A SURFACE OF A SILICONE MONOCRYSTALLINE BODY |
| US3749612A (en) * | 1971-04-06 | 1973-07-31 | Int Nickel Co | Hot working of dispersion-strengthened heat resistant alloys and the product thereof |
| US3743548A (en) * | 1971-05-06 | 1973-07-03 | Cabot Corp | Dispersion hardened metals having improved oxidation characteristics at elevated temperature |
| US3926568A (en) * | 1972-10-30 | 1975-12-16 | Int Nickel Co | High strength corrosion resistant nickel-base alloy |
| US4080204A (en) * | 1976-03-29 | 1978-03-21 | Brunswick Corporation | Fenicraly alloy and abradable seals made therefrom |
| US4386976A (en) * | 1980-06-26 | 1983-06-07 | Inco Research & Development Center, Inc. | Dispersion-strengthened nickel-base alloy |
| JPS58193335A (en) * | 1982-05-06 | 1983-11-11 | Sumitomo Electric Ind Ltd | Dispersion-strengthened nickel-based heat-resistant sintered alloy and its manufacturing method |
| US4599214A (en) * | 1983-08-17 | 1986-07-08 | Exxon Research And Engineering Co. | Dispersion strengthened extruded metal products substantially free of texture |
| US4631082A (en) * | 1985-02-20 | 1986-12-23 | Pfizer Hospital Products Group Inc. | Cobalt-chromium superalloy |
-
1987
- 1987-08-19 EP EP87112012A patent/EP0260465B1/en not_active Expired - Lifetime
- 1987-08-19 DE DE8787112012T patent/DE3775671D1/en not_active Expired - Lifetime
- 1987-08-28 US US07/090,346 patent/US4798625A/en not_active Expired - Fee Related
- 1987-09-07 NO NO873738A patent/NO873738L/en unknown
- 1987-09-08 JP JP62225133A patent/JP2630323B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6369936A (en) | 1988-03-30 |
| DE3775671D1 (en) | 1992-02-13 |
| NO873738D0 (en) | 1987-09-07 |
| JP2630323B2 (en) | 1997-07-16 |
| NO873738L (en) | 1988-03-09 |
| EP0260465A1 (en) | 1988-03-23 |
| US4798625A (en) | 1989-01-17 |
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