EP0639654B1 - Fe-Ni-Cr-Basis-Superlegierung, Motorenventil und kettengewirkter Netzwerkträgerkörper für einen Abgaskatalysator - Google Patents

Fe-Ni-Cr-Basis-Superlegierung, Motorenventil und kettengewirkter Netzwerkträgerkörper für einen Abgaskatalysator Download PDF

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EP0639654B1
EP0639654B1 EP94112923A EP94112923A EP0639654B1 EP 0639654 B1 EP0639654 B1 EP 0639654B1 EP 94112923 A EP94112923 A EP 94112923A EP 94112923 A EP94112923 A EP 94112923A EP 0639654 B1 EP0639654 B1 EP 0639654B1
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base superalloy
superalloy according
weight
temperature
alloy
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EP0639654A2 (de
EP0639654A3 (de
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Koji Sato
Takehiro Ohno
Katsuaki Sato
Tsutomu Saka
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Honda Motor Co Ltd
Proterial Ltd
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Honda Motor Co Ltd
Hitachi Metals Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent

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  • the present invention relates to an inexpensive Fe-Ni-Cr-base superalloy which is excellent in high-temperature strength, and an engine valve for a motor vehicle and a knitted mesh supporter for an exhaust gas catalyzer for a motor vehicle which are made of the alloy.
  • JIS SUH35 Fe-8.5Mn-21Cr-4Ni-0.5C-0.4N
  • JIS NCF751 Ni-15.5Cr-1Nb-2.3Ti-1.2Al-7Fe
  • JIS NCF751 which contains about 70 % Ni
  • JIS NCF751 is by far more expensive than JIS SUH35. Therefore, there have been developed alloys which contain less valuable alloying elements than JIS NCF751 and which have high-temperature strength and stability of alloy structure after long-time heating which are as close to those of JIS NCF751 as possible.
  • JP-B2-1-12827 JP-A-62-214149, JP-A-58-189359, JP-A-63-213631, JP-A-61-238942, JP-B2-62-50542, JP-B2-4-11613, JP-A-60-211028, JP-A- 56 020 148, US-A- 4 172 742 and so on.
  • lead-free gasoline As gasoline fuel for engines of motor vehicles, lead-free gasoline has recently been employed for answering the demand of treatment of exhaust gas, and engines for which lead-free gasoline is exclusively used have been mainly produced.
  • engine parts which are used at a particularly high temperature such as engine valves and knitted mesh supporters for exhaust gas catalyzers for a motor vehicle
  • use of lead-free gasoline leads to an improvement of wear environment. If the same level of oxidation resistance property as JIS NCF751 is provided, no consideration must be given to the wear resistance property with respect to lead oxide, which has conventionally been a problem to be considered.
  • the alloys proposed in JP-A-63-213631, JP-B2-4-11613 and JP-A-60-211028 can provide high-temperature strength and long-time stability of alloy structure which are close to those of JIS NCF751.
  • the Ni content exceeds 50 %, reduction of resources and costs is not sufficiently accomplished as compared with JIS NCF751.
  • the alloys proposed in JP-B2-1-12827, JP-A-62-214149 and JP-A-58-189359 have excellent oxidation resistance and wear resistance properties because Cr content is high.
  • An objective of the present invention resides in providing a resource-saving Fe-Ni-Cr-base superalloy which is excellent in high-temperature strength and normal-temperature ductility after long-time heating, which could not be accomplished by the above-described conventional alloys, and which has a sufficient oxidation resistance property, and further to provide an engine valve and a knitted mesh supporter for an exhaust gas catalyzer which are made of this alloy.
  • samples were manufactured by heating at 800°C for 400 hours, and their tensile strength at 800°C and rotary bending fatigue strength were measured, to thereby measure high-temperature strength of the alloy after long-time heating. Meanwhile, normal-temperature (20°C) U-notch Charpy impact tests of the samples were performed, and toughness of the material was evaluated from the impact values. In respect of the acid resistance property, weight changes after heating at 850°C for 400 hours were measured.
  • alloys having these compositions exhibit U-notch Charpy impact values after heating at 800°C for 400 hours not less than 0.5 MJ/m 2 . Further, they exhibit a rupture strength in 800°C-294 MPa rotary bending fatigue tests after heating at 800°C for 400 hours of not less than 0.5x10 6 times. Moreover, engine valves for motor vehicles and knitted mesh supporters for exhaust gas catalyzers for motor vehicles which are made of the above-described Fe-Ni-Cr-base superalloys have excellent properties which have not been observed in the conventional alloys.
  • Fig. 1 is a diagram in which the relationship between Al+Ti+Zr+Hf+V+Nb+Ta and Al/(Al+Ti+Zr+Hf+V+Nb+Ta) of invention alloys, comparative alloys and conventional alloys are plotted.
  • a small amount of carbon must be added because carbon combines with Ti and Nb and forms carbides, thereby preventing coarsening of crystal grains and improving the creep rupture ductility.
  • excessive addition over 0.15 % causes a large amount of decomposition reactions from MC carbides into M 23 C 6 carbides during long-time heating, and deteriorates the ductility on crystal grain boundaries at a normal temperature. Therefore, up to 0.15 % C is added. Preferably, up to 0.08 % C is added.
  • the Si and Mn are added to the invention alloy as deoxidizing elements. However, excessive addition of either of them results in deterioration of the high-temperature strength. Therefore, the Si content is limited to 1.0 % or less, and the Mn content is limited to 3.0 % or less. Preferably, the Si content is 0.5 % or less, and the Mn content is 1.0 % or less. More preferably, the Si content is 0.2 % or less, and the Mn content is 0.5 % or less.
  • Ni stabilizes the austenite phase of the matrix and enhances the high-temperature strength. Further, Ni is an indispensable additive element as a constituent of the ⁇ ' phase. When the Ni content is below 30 %, precipitation of the ⁇ ' phase is insufficient, thereby deteriorating the high-temperature strength. On the other hand, when the Ni content exceeds 49 %, JIS NCF751 as a resource-saving material becomes no longer advantageous in respect of the price. Consequently, the Ni content is limited to 30 to 49 %. Preferably, the Ni content is 30 to 45 %.
  • Cr is an indispensable element for providing an oxidation resistance property for an alloy, and at least 10 % Cr is required for ensuring the oxidation resistance property as heat-resistant parts for a motor vehicle or the like.
  • the Cr content exceeds 18 %, the alloy structure becomes unstable, and harmful embrittlement phases such as the ⁇ ' phase and the ⁇ phase rich in Cr are generated, thus deteriorating the creep rupture strength and normal-temperature ductility. Therefore, the Cr content is limited to 10 to 18 %.
  • the Cr content is 13 to 18 %. More preferably, it is 13.5 to 16 %.
  • Al is an indispensable element for precipitating the stable gamma prime phase, to thereby obtain a desired high-temperature strength, as described above, and at least 1.0 % Al is necessary.
  • the Al content is limited to 1.0 to 3.0 %.
  • such a high Al content serves to increase an amount of generation of Al 2 O 3 during high-temperature heating, and contributes to improvement of the oxidation resistance property.
  • the Al content is not less than 1.6 to 3.0 %, more preferably 1.8 to 2.4 %.
  • no alloy having such a high Al content has ever existed, and this is one of the most significant characteristics of the present invention.
  • elements of the Group IVa and the Va family in an invention alloy combine with Ni and precipitate the gamma prime phase so as to enhance the high-temperature strength. Totally not less than 1.5 % one or more of the elements of the Group IVa and the Group Va must be added. However, when the total additive amount of these elements exceeds 8.0 %, the gamma prime phase becomes unstable during high-temperature long-time heating, and intermetallic compounds of the ⁇ phase and the ⁇ phase which do not conform with the ⁇ phase are easily generated, and also, the hot workability is degraded. Consequently, totally 1.5 to 8.0 % one or more of the elements of the IVa family and the Va family are added. Preferably, the total additive amount is 3.0 to 5.0 %.
  • Ti is the most favorable element to be added, and preferably, the additive amount of Ti is 1.5 to 3.0 %. More preferably, it is 2.0 to 3.0 %.
  • Zr and Hf have lower solubility into the ⁇ phase than Ti, and can not be added as much as Ti. However, Zr and Hf partially segregate on or around crystal grain boundaries and serve to enhance the grain-boundary strength in a high temperature range.
  • Nb is the most favorable element to be added, and preferably, the additive amount of Nb is 0.3 to 2.5 %. More preferably, it is 0.5 to 1.5 %.
  • V vanadium
  • Ta performs solid-solution strengthening of the ⁇ ' phase more than Nb. However, Ta is a rare resource and increases the price by a large degree so that a large amount of Ta can not be added.
  • Mo and W are elements of the same VIa family as Cr, and both Mo and W perform solid-solution strengthening of the austenite matrix and serve to enhance the high-temperature fatigue strength and high-temperature creep rupture strength. Therefore, if necessary, one or both of 3 % or less Mo and 3 % or less W can be added. However, Mo is preferred in respect of the alloy price and the specific gravity, and the preferable Mo content in this case is 0.1 to 1.0 %.
  • the amount of Cr+Mo+W expressed by atomic percent is preferably 13 to 18. More preferably, it is 15.0 to 17.5.
  • Co dissolves in the austenite matrix and promotes solid solution of the ⁇ ' phase in a range for hot working, thereby improving the workability.
  • Co increases an amount of precipitation of the ⁇ ' phase and enhances the high-temperature strength. Consequently, Co can be added to be substituted for Ni, if necessary, in such a range that Ni+Co ⁇ 49.
  • Co is a more expensive element than Ni so that the upper limit is preferably 5.0 %.
  • the Group IVa elements and the Group Va elements must individually satisfy the foregoing respective ranges. Besides, it is important to realize the total amounts of these elements and the Al rate in proper ranges as the gamma prime constituent elements.
  • the ratio of Al/(Al+Ti+Zr+Hf+V+Nb+Ta) expressed by atomic percent is increased to stabilize the ⁇ ' phase.
  • the ratio of Al/(Al+Ti+Zr+Hf+V+Nb+Ta) is 0.45 to 0.75. More preferably, it is 0.50 to 0.60.
  • the amount of (Al+Ti+Zr+Hf+V+Nb+Ta) expressed by atomic percent is preferably controlled in a proper range.
  • this value is below 6.5 atom. %, the strength is not as high as the strength of the conventional Fe-Ni-Cr-base superalloy having more than 50 % Ni, and when it exceeds 10 atom. %, hot working for engine valves and the like becomes difficult.
  • the amount of (Al+Ti+Zr+Hf+V+Nb+Ta) expressed by atomic percent is controlled in a range of 6.5 to 10.0 which is higher than the conventional forging alloy, so as to improve the short-time high-temperature strength.
  • the more preferable range is 7.0 to 8.5 atom. %.
  • Such a high calculated ⁇ ' amount has never been realized in a forging alloy for engine valves and the like. In this respect, it is quite a novel invention. In the case of an Ni-base superalloy having 50 % or more Ni, the ⁇ ' phase is stable up to a high temperature, and with this level of ⁇ ' amount, hot working for strength of engine valves and the like is difficult.
  • B boron
  • B boron
  • the upper limit of B is preferably 0.015 %.
  • Mg and Ca enhance purification of the alloy as strong deoxidizing, desulfurizing elements, and serve to improve the ductility during high-temperature tension, creep deformation and hot working. Consequently, an appropriate amount of one or both of Mg and Ca can be added. The effect starts to take place from addition of a small amount. However, when the additive amount of each of Mg and Ca exceeds 0.02 %, the solidus temperature during heating is lowered, and the hot workability is degraded. Therefore, the upper limit of each of Mg and Ca is preferably 0.02 %.
  • Y and REM are effective for enhancing the high-temperature oxidation resistance property, and an appropriate amount of one or both of Y and REM can be added.
  • the effect starts to take place from addition of a small amount.
  • the additive amount of each of Y and REM exceeds 0.1 %, the solidus temperature during heating is lowered, and the hot workability is degraded. Therefore, the upper limit of each of Y and REM is preferably 0.1 %. It is easy to use an invention alloy as a base and to derive the optimum additive amount of elements of the lanthanoid group so as to enhance the oxidation resistance property up to the limit, and such an operation does not exceed the range of this invention.
  • Re dissolves in the austenite matrix to strengthen the same. Also, Re promotes precipitation of the ⁇ ' phase, and it advantageously improves the alloy in high-temperature wear resistance property. Therefore, up to 2.0 % Re may be added to the invention alloy. Since Re is a rare resource and increases the alloy price by a large degree, excessive addition is not necessary.
  • Fe is an effective element for forming the austenite matrix which is inexpensive for a resource-saving alloy. Further, Fe softens the matrix in a higher temperature range than Ni, and consequently, hot working can be conducted even if the alloy includes the above-mentioned amounts of strengthening alloy elements. For the foregoing reasons, Fe is the balance of the composition except unavoidable impurities.
  • the following elements may be included in an invention alloy if their additive amounts are within the following ranges: P ⁇ 0.04 %, S ⁇ 0.02 %, O ⁇ 0.02 %, N ⁇ 0.05 % more preferably, P ⁇ 0.02 %, S ⁇ 0.005 %, O ⁇ 0.01 %, N ⁇ 0.01 %
  • the above-described Fe-Ni-Cr-base superalloys are subjected to vacuum melting alone or vacuum melting and the subsequent refining process of electroslag remelting, vacuum arc remelting or the like, and the ingots thus obtained are processed through hot forging, hot rolling or the like, and finished as primary products.
  • the impact value after heating at 800°C for 400 hours as a material for valves of a motor vehicle engine is less than 0.5 MJ/m 2 , the valves whose toughness is inadequate might be broken when, for example, the engine after long-term use is quickly rotated up to a high temperature in a cold place. Therefore, if necessary, the impact value of the invention alloy after heating at 800°C for 400 hours is preferably limited to 0.5 MJ/m 2 or more.
  • the invention alloys can satisfy such fatigue strength under the optimum heat treatment condition.
  • the invention alloys can realize both the excellent normal-temperature toughness and the high high-temperature fatigue strength after high-temperature long-time heating. This is the performance which could not be achieved by the conventional Fe-Ni-Cr-base superalloys, and the above-mentioned value specifically shows the excellent properties of the invention alloys.
  • hot rolled bars made of the invention alloys are cut into a required size and shaped into engine valves for motor vehicles through hot upset forging or hot extrusion.
  • engine valves are inexpensive resource-saving valves which are excellent in high-temperature fatigue strength, high-temperature hardness, stability of alloy structure, the oxidation resistance property and normal- and high-temperature strength after long-time heating, and which do not require building-up on valve face portions.
  • the engine valves can greatly contribute to the economic aspect of production of motor vehicles.
  • These engine valves can be subjected to various treatments for surface nitrogenization and various kinds of hard plating before practical use.
  • various kinds of heat-resistant steel and high-hardness alloy tool steel are welded on the axial portions of the engine valves, and they can be used as connection valves. Further, when the engine valves are processed in various manners and used as hollow engine valves, their durability is further improved.
  • hot rolled bars made of the invention alloys after solid solution heat treatment are subjected to cold or warm working and annealing repeatedly, worked into wire having a diameter of about 0.2 mm at the minimum, and shaped into a knitted mesh supporter for supporting a ceramic carrier of exhaust gas catalyzer.
  • This knitted mesh supporter has more excellent oxidation resistance property and high-temperature strength than stainless steel of SUS310S and so forth which is a conventional knitted mesh material, so that a knitted mesh supporter having higher reliability and excellent durability can be obtained.
  • Alloys of the compositions shown in Table 1 were formed into ingots of 10 kg through vacuum induction melting, and then, the ingots were shaped into bars of 30 mm square through hot working (REM was added as misch metal).
  • the bars were subjected to solid solution heat treatment in which they were maintained at 1050°C for 30 minutes and then water-cooled, and aging treatment in which they were maintained at 750°C for 4 hours and then air-cooled. After this normal heat treatment or after maintaining the bars of this condition at 800°C for 400 hours, normal-temperature hardness, normal-temperature Charpy impact tests, normal-temperature and 800°C tension tests and rotary bending fatigue tests under the condition of 800°C-294 MPa were performed.
  • oxidation resistance properties when the bars were heated at 850°C for 400 hours were inspected. Normal-temperature hardness was measured by Rockwell hardness meters.
  • the Charpy impact tests were performed at a temperature of 20°C with 2U-notch test pieces No. 3 in accordance with the JIS method.
  • the tension tests were performed with a parallel-portion diameter of 6.35 mm and an elongation of 4D in accordance with the ASTM method.
  • the rotary bending fatigue tests were performed with test pieces having a parallel-portion diameter of 8 mm at a rotational speed of 3600 in accordance with the JIS Z2274, and the number of testing operations until each test piece was ruptured was counted.
  • Nos. 1 to 21 are invention alloys, Nos. 31 to 33 are comparative alloys, and No. 41 is a conventional alloy disclosed in JP-B2-4-11613.
  • Values A, B and C appended to the various chemical compositions in Table 1 are, respectively, an amount of Al+Ti+Zr+Hf+V+Nb+Ta, a ratio of Al/(Al+Ti+Zr+Hf+V+Nb+Ta) and an amount of Cr+Mo+W which are expressed by atomic percent.
  • an atomic weight of La was used as a representative value of the REM content. Further, the relationship between the values A and B is shown in Fig. 1.
  • the various kinds of mechanical properties and acid resistance properties of the invention alloys were as excellent as or more excellent than those of the conventional alloy No. 41 including 60 % Ni. It was confirmed that the invention alloys were superior resource-saving heat-resistant alloys.
  • the invention alloy No. 2 shown in Table 1 was further subjected to hot forging and cutting and grinding work, and finished as a round bar having a diameter of 6 mm. Then, one end of this round bar was formed into a shape of an engine valve through hot upset forging.
  • This engine valve and a mass-production engine valve made of the conventional alloy disclosed in JP-B2-4-11613 were subjected to the normal heat treatment described in Example 1, and bench tests were carried out with engine testers for lead-free gasoline. Test conditions as high-speed high-temperature continuous durability tests were selected in such a manner that the maximum temperature of the valve would be 780 to 830°C, and continuous operation for 400 hours was performed. After finishing the tests, shape changes and cross-sectional wear states of the engine valves made of the invention alloy and the conventional alloy were observed, and it was confirmed that both the engine valves had such qualities that they could be provided for practical use without any problems.
  • a round bar of 6 mm made of the invention alloy No. 2 in Example 2 was subjected to cold drawing and annealing repeatedly and worked into wire having a diameter of 0.25 mm, and thereafter, the wire is shaped into a knitted mesh supporter of a ceramic carrier for an exhaust gas catalyzer.
  • This catalyzer unit was joined in the bench tests in Example 2, and its performance as the knitted mesh supporter was inspected. Although the temperature of the knitted mesh supporter was higher than that of the valve, the knitted mesh supporter made of the invention alloy did not cause creep deformation nor abnormal oxidization after finishing the tests, and it was found that the invention alloy exhibited an excellent performance in the form of the exhaust gas knitted mesh supporter as well.

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Claims (17)

  1. Fe-Ni-Cr-Basis-Superlegierung, die gewichtsmäßig aus bis zu 0,15 % C, bis zu 1,0 % Si, bis zu 3,0 % Mn, 30-49 % Ni, 10-18 % Cr, 1,0-3,0 % Al, einem oder mehreren aus den Gruppen IVa und Va gewählten Elementen in einer Menge oder Gesamtmenge von 1,5-8,0 %, wahlweise einem oder beiden von bis zu 3 % Mo und bis zu 3 % W, wahlweise bis zu 5 % Co in einem solchen Bereich, daß Ni+Co ≤ 49 %, wahlweise bis zu 0,015 % B, wahlweise einem oder beiden von bis zu 0,02 % Mg und bis zu 0,02 % Ca, wahlweise einem oder beiden von bis zu 0,1 % Y und bis zu 0,1 % SEM, wahlweise bis zu 2,0 % Re, und Rest Fe und unvermeidlichen Verunreinigungen besteht,
    wobei Al ein unerläßliches Zusatzelement ist und ein oder mehrere aus den Gruppen IVa und Va gewählten Elemente den folgenden Formeln in Atomprozent genügen: 0,45 ≤ Al/(Al+Ti+Zr+Hf+V+Nb+Ta) ≤ 0,75
    Figure imgb0011
     6,5 ≤ Al+Ti+Zr+Hf+V+Nb+Ta ≤ 10,0.
    Figure imgb0012
  2. Fe-Ni-Cr-Basis-Superlegierung nach Anspruch 1, die gewichtsmäßig aus bis zu 0,15 % C, bis zu 1,0 % Si, bis zu 3,0 % Mn, 30-49 % Ni, 10-18 % Cr, 1,6-3,0 % Al, einem oder mehreren aus den Gruppen IVa und Va gewählten Elementen in einer Menge oder Gesamtmenge von 1,5-8,0 %, und Rest Eisen und unvermeidlichen Verunreinigungen besteht.
  3. Fe-Ni-Cr-Basis-Superlegierung nach Anspruch 1, die gewichtsmäßig aus bis zu 0,15 % C, bis zu 1,0 % Si, bis zu 3,0 % Mn, 30-49 % Ni, 10-18 % Cr, einem oder beiden von bis zu 3 % Mo und bis zu 3 % W, 1,6-3,0 % Al, einem oder mehreren aus den Gruppen IVa und Va gewählten Elementen in einer Menge oder Gesamtmenge von 1,5-8,0 %, und Rest Eisen und unvermeidlichen Verunreinigungen besteht.
  4. Fe-Ni-Cr-Basis-Superlegierung nach Anspruch 1, die gewichtsmäßig aus bis zu 0,08 % C, bis zu 0,5 % Si, bis zu 1,0 % Mn, 30-49 % Ni, 13-18 % Cr, 1,6-3,0 % Al, 1,5-3,0 % Ti, 0,3-2,5 % Nb, und Rest Fe und unvermeidlichen Verunreinigungen besteht.
  5. Fe-Ni-Cr-Basis-Superlegierung nach Anspruch 1, die gewichtsmäßig aus bis zu 0,08 % C, bis zu 0,5 % Si, bis zu 1,0 % Mn, 30-49 % Ni, 13-18 % Cr, einem oder beiden von bis zu 3 % Mo und bis zu 3 % W, 1,6-3,0 % Al, 1,5-3,0 % Ti, 0,3-2,5 % Nb, und Rest Fe und unvermeidlichen Verunreinigungen besteht.
  6. Fe-Ni-Cr-Basis-Superlegierung nach Anspruch 1, die gewichtsmäßig aus bis zu 0,08 % C, bis zu 0,5 % Si, bis zu 1,0 % Mn, 30-49 % Ni, 13-18 % Cr, bis zu 3 % Mo, 1,6-3,0 % Al, 1,5-3,0 % Ti, 0,3-2,5 % Nb, und Rest Fe und unvermeidlichen Verunreinigungen besteht.
  7. Fe-Ni-Cr-Basis-Superlegierung nach Anspruch 1, die gewichtsmäßig aus bis zu 0,08 % C, bis zu 0,2 % Si, bis zu 0,5 % Mn, 30-45 % Ni, 13,5-16 % Cr, 0,1-1,0 % Mo, 1,8-2,4 % Al, 2,0-3,0 % Ti, 0,5-1,5 % Nb, und Rest Fe und unvermeidlichen Verunreinigungen besteht.
  8. Fe-Ni-Cr-Basis-Superlegierung nach irgendeinem der Ansprüche 1-7, die gewichtsmäßig bis zu 5 % Co in einem solchen Bereich enthält, daß Ni+Co ≤ 49.
  9. Fe-Ni-Cr-Basis-Superlegierung nach Anspruch 1, wobei Al ein unerläßliches Zusatzelement ist und ein oder mehrere aus den Gruppen IVa und Va gewählten Elemente den folgenden Formeln in Atomprozent genügen: 6,5 ≤ Al+Ti+Zr+Hf+V+Nb+Ta ≤ 8,5
    Figure imgb0013
     0,50 ≤ Al/(Al+Ti+Zr+Hf+V+Nb+Ta) ≤ 0,60.
    Figure imgb0014
  10. Fe-Ni-Cr-Basis-Superlegierung nach irgendeinem der Ansprüche 1-9, wobei Cr ein unerläßliches Zusatzelement ist und eines oder beide von Mo und W in einem solchen Bereich enthalten sind, daß 13 ≤ Cr+Mo+W ≤ 18 in Atomprozent gilt.
  11. Fe-Ni-Cr-Basis-Superlegierung nach irgendeinem der Ansprüche 1-10, die gewichtsmäßig bis zu 0,015 % B enthält.
  12. Fe-Ni-Cr-Basis-Superlegierung nach irgendeinem der Ansprüche 1-11, die gewichtsmäßig eines oder beide von bis zu 0,02 % Mg und bis zu 0,02 % Ca enthält.
  13. Fe-Ni-Cr-Basis-Superlegierung nach irgendeinem der Ansprüche 1-12, die gewichtsmäßig eines oder beide von bis zu 0,1 % Y und bis zu 0,1 % SEM enthält.
  14. Fe-Ni-Cr-Basis-Superlegierung nach irgendeinem der Ansprüche 1-13, wobei der Charpy-U-Kerbschlagwert nach 400-stündigem Erhitzen auf 800 °C nicht unter 0,5 MJ/m2 ist.
  15. Fe-Ni-Cr-Basis-Superlegierung nach irgendeinem der Ansprüche 1-14, wobei die Bruchfestigkeit beim 800 °C-294 MPa-Drehbiegeermüdungstest nach 400-stündigem Erhitzen auf 800 °C nicht unter 0,5 x 106 Malen ist.
  16. Motorventil für ein Kraftfahrzeug, das aus einer Fe-Ni-Cr-Basis-Superlegierung nach irgendeinem der Ansprüche 1-15 hergestellt ist.
  17. Kettengewirkter Netzwerkträgerkörper für einen Abgaskatalysator, der aus einer Fe-Ni-Cr-Basis-Superlegierung nach irgendeinem der Ansprüche 1-15 hergestellt ist.
EP94112923A 1993-08-19 1994-08-18 Fe-Ni-Cr-Basis-Superlegierung, Motorenventil und kettengewirkter Netzwerkträgerkörper für einen Abgaskatalysator Expired - Lifetime EP0639654B1 (de)

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JP20494093 1993-08-19
JP6056219A JP3058794B2 (ja) 1993-08-19 1994-03-25 Ｆｅ−Ｎｉ−Ｃｒ基超耐熱合金、エンジンバルブおよび排ガス触媒用ニットメッシュ
JP56219/94 1994-03-25

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JPH09279309A (ja) * 1996-04-12 1997-10-28 Daido Steel Co Ltd Ｆｅ−Ｃｒ−Ｎｉ系耐熱合金
EP0838533B1 (de) * 1996-10-25 2002-02-13 Daido Tokushuko Kabushiki Kaisha Hitzebeständige Legierung für Auslassventile und Verfahren zur Herstellung derartiger Auslassventile
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EP0639654A2 (de) 1995-02-22
DE69406511D1 (de) 1997-12-04
JPH07109539A (ja) 1995-04-25
EP0639654A3 (de) 1995-10-11
DE69406511T2 (de) 1998-03-26

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