EP0244520A1 - Alliages résistant aux températures élevées - Google Patents
Alliages résistant aux températures élevées Download PDFInfo
- Publication number
- EP0244520A1 EP0244520A1 EP86303435A EP86303435A EP0244520A1 EP 0244520 A1 EP0244520 A1 EP 0244520A1 EP 86303435 A EP86303435 A EP 86303435A EP 86303435 A EP86303435 A EP 86303435A EP 0244520 A1 EP0244520 A1 EP 0244520A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- heat resistant
- temperature
- rem
- based heat
- 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.)
- Granted
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 50
- 239000000956 alloy Substances 0.000 title claims abstract description 50
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 claims abstract description 19
- 239000012535 impurity Substances 0.000 claims abstract description 9
- 238000003483 aging Methods 0.000 claims description 8
- 239000006104 solid solution Substances 0.000 claims description 8
- 238000000034 method Methods 0.000 claims 7
- 230000007797 corrosion Effects 0.000 abstract description 17
- 238000005260 corrosion Methods 0.000 abstract description 17
- 239000000463 material Substances 0.000 abstract description 5
- 238000002485 combustion reaction Methods 0.000 abstract description 3
- 238000001556 precipitation Methods 0.000 description 14
- 238000010438 heat treatment Methods 0.000 description 10
- 229910052761 rare earth metal Inorganic materials 0.000 description 10
- 238000005242 forging Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 239000000126 substance Substances 0.000 description 6
- 230000000930 thermomechanical effect Effects 0.000 description 6
- 229910052720 vanadium Inorganic materials 0.000 description 6
- 206010037660 Pyrexia Diseases 0.000 description 5
- 230000009467 reduction Effects 0.000 description 5
- 230000006872 improvement Effects 0.000 description 4
- 229910052758 niobium Inorganic materials 0.000 description 4
- 230000003014 reinforcing effect Effects 0.000 description 4
- 229910052721 tungsten Inorganic materials 0.000 description 4
- 230000032683 aging Effects 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 230000000452 restraining effect Effects 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- GNTDGMZSJNCJKK-UHFFFAOYSA-N divanadium pentaoxide Chemical compound O=[V](=O)O[V](=O)=O GNTDGMZSJNCJKK-UHFFFAOYSA-N 0.000 description 2
- 239000000446 fuel Substances 0.000 description 2
- 238000000265 homogenisation Methods 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 230000002787 reinforcement Effects 0.000 description 2
- 229910052715 tantalum Inorganic materials 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- PMZURENOXWZQFD-UHFFFAOYSA-L Sodium Sulfate Chemical compound [Na+].[Na+].[O-]S([O-])(=O)=O PMZURENOXWZQFD-UHFFFAOYSA-L 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- 229910001235 nimonic Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 229910052938 sodium sulfate Inorganic materials 0.000 description 1
- 235000011152 sodium sulphate Nutrition 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
Definitions
- This invention relates to an Fe-Ni based heat resistant alloy having an excellent high-temperature corrosion resistance, and high toughness and strength, and more particularly to a high strength Fe-Ni based heat resistant alloy useful as a material for heat resistant components in internal combustion engine such as exhaust valve, heat resistant spring, heat resistant bolt and the like.
- the reinforcing mechanism of this Fe-Ni based heat resistant alloy is due to the precipitation of ⁇ -phase [Ni3(Al, Ti)] likewise in case of the Ni based heat resistant alloy.
- the precipitation at grain boundary of ⁇ -phase [Ni3Ti] not contributing to the reinforcement is liable to occur in the Fe-Ni based heat resistant alloy, so that the reduction of strength and ductility is not avoided.
- the addition amount of Al, Ti or the like as a reinforcing element is limited to a relatively narrow range from a viewpoint of the structure stability.
- the addition of B is effective for restraining the grain boundary precipitation of ⁇ -phase, but in this case, it is required to add a great amount of B.
- B considerably reduces the incipient melting temperature of the grain boundary, so that the addition of the great amount of B causes a problem of damaging hot workability. Therefore, the addition amount of B is restricted to an extent of causing no damage of hot warkability.
- the increase of Al amount is effective for restraining the grain boundary precipitation of ⁇ -phase.
- the reinforcing action based on the precipitation of ⁇ -phase is produced by strain energy based on the difference in crystal lattice constant between the precipitated ⁇ -phase and matrix, so that it is necessary to increase the lattice constant of ⁇ -phase as far as possible in order to provide a large strength.
- it is effective to make a large ratio of Ti/Al by decreasing the Al amount. Therefore, the increase of Al does not quite contribute to the reinforcement of the Fe-Ni based heat resistant alloy, so that the amount of Al becomes limited low.
- the inventors have made various studies in order to provide Fe-Ni based heat resistant alloys which can restrain the precipitation of ⁇ -phase by adding proper amounts of B and Al and to improve the strength even if the Al amount is limited low, and further to improve high-temperature corrosion resistance, and as a result, the invention has been accomplished.
- a hith strength, high toughness, high corrosion resistant Fe-Ni based heat resistant alloy comprising, on a weight ratio, 0.01-0.2% of C, not more than 2% of Si, not more than 2% of Mn, 25-50% of Ni, 13-23% of Cr, 1.5-3.5% of Ti, 0.1-0.7% of Al, 0.001-0.05% of B, 0.001-0.01% of Ca, 0.001-0.1% of REM (at least one rare earth element), and if necessary,0.003-0.05% of N, and further at least one of 0.005-0.05% of Zr, 0.05-1% of V, 0.05-3% of Nb+Ta (inclusive of a case that either is zero), 0.05-3% of Mo and 0.05-3% of W, and the remainder being Fe and inevitable impurities.
- the heat resistant alloy having a high strength and a remarkably excellent high-temperature corrosion resistance is provided without the damage of the toughness by subjecting the alloy of the above chemical composition to a solid solution treatment at a temperature of not less than 1050°C as a usual heat treatment and further to an age hardening treatment at 650-850 °C, and if necessary, subjecting to a working heat treatment wherein the homogenization is carried out at a high temperature of not less than 1050 °C and residual strain is given by working at a temperature of not more than 1000 °C and an age hardening treatment is carried out at 650-850 °C, whereby the precipitation in grain of ⁇ -phase [(Ni3(Al, Ti)] is promoted and the precipitation of harmful ⁇ -phase [Ni3Ti] is restrained.
- C is an effective element for enhancing high-temperature strength by bonding with Cr and Ti to form carbides. In order to obtain such an effect, it is necessary to add not less than 0.01% of C. However, if the amount is too large, the toughness and ductility are degraded and if it is applied, for example, to an exhaust valve, the performances are deteriorated, so that the upper limit should be 0.2%.
- Si is mainly added as a deoxidizer in melting process. However, if the amount is too large, the toughness and ductility lower, so that it is limited to not more than 2%.
- Mn is added as a deoxidizer likewise Si and desulfurizer in melting. However, if the amount is too large, the oxidation resistance at high temperature lowers, so that it is limited to not more than 2%.
- Ni is an element required for stabilizing austenite structure and simultaneously forming ⁇ -phase [Ni3(Al, Ti)].
- ⁇ -phase ⁇ -phase
- brittle phase such as ⁇ -phase or the like is formed in use at high temperature to degrade high-temperature properties, while when it is too large, the improvement of high-temperature properties is not so expected and the cost is rather increased, so that the Ni amount is limited to 25-50%.
- Cr is an effective element for ensuring corrosion resistance and oxidation resistance required in the heat resistant alloy. In order to obtain such an effect, it is necessary to add not less than 13% of Cr. However, if the amount is too large, ⁇ -phase is formed to degrade toughness and ductility, so that it is limited to not more than 23%.
- Ti is an element necessary for bonding with Ni and Al to form ⁇ -phase [Ni3 (Al, Ti)] effective for the increase of high-temperature strength. For this purpose, not less than 1.5% of Ti is added. However, if the amount is too large, ⁇ -phase [Ni3 Ti] is precipitated to degrade high-temperature properties, so that it is limited to not more than 3.5%.
- Al is an element necessary for the formation of ⁇ -phase likewise Ti. For this purpose, not less than 0.1% of Al is added. However, if the amount is too large, the ratio of Ti/Al decreases and the strength is reduced, so that it is limited to not more than 0.7%.
- B is an effective element for restraining the precipitation of ⁇ -phase. In order to obtain such an effect, it is necessary to add not less than 0.001% of B. However, if the amount is too large, local melting temperature of grain boundary is considerably reduced and hot workability is damaged, so that it should be limited to not more than 0.05%.
- Ca is an effective element for fixing S to enhance hot workability and controlling distribution form of carbides to enhance toughness and ductility, and contributes to enhance the strength even if the Al amount is limited low. For this purpose, not less than 0.001% of Ca is added. However, if the amount is too large, the workability lowers, so that it should be limited to not more than 0.01%.
- REM at least one earth element: 0.001-0.1%
- REM is an element for considerably improving adhesion property of oxide film, and is effective for the improvement of high-temperature corrosion resistance. Particularly, the effect by the addition of REM is considerably developed when the variation of service temperature is large. In order to obtain such an effect, not less than 0.001% of REM is added. However, when the REM amount exceeds 0.1%, the hot workability is apt to be degraded.
- Zr, V, Nb, Ta, Mo and W are effective elements for forming carbides to enhance high-temperature strength and toughness, and among them, Zr is also an effective element for reinforcing grain boundary. If necessary, at least one of Zr, V, Nb, Ta Mo and W may be added for obtaining the above effect. However, if the amount is too large, the toughness and hot workability are degraded, so that it should be limited to the above defined range.
- N is an element effective for controlling the growth of crystal grains to make the structure fine, not less than 0.003% of N may be added, if necessary. However, if the amount is too large, stringers due to agglomeration of nitride are formed to degrade ductility, so that it should be limited to not more than 0.05%.
- Fe-Ni based heat resistant alloys having high strength, high toughness and improved high-temperature corrosion resistance have a chemical composition as defined above. It has been found that it is more desirable that the above chemical composition alloy is subjected to a solid solution treatment at a temperature of not less than 1050 C as a usual heat treatment and further to an age hardening treatment at 650-850 °C. Furthermore, it has been confirmed that the above treated alloy is homogenized at a high temperature of not less than 1050 °C, subjected to a working strain at a temperature of not more than 1000 °C, and then age-hardened at a temperature of 650-850 °C. Thus, the precipitation of ⁇ -phase in grain is promoted, and the precipitation of harmful ⁇ -phase is restrained to thereby provide high strength and considerably improve high-temperature corrosion resistance without the damage of toughness.
- An alloy having a chemical composition as shown in the following Table 1 was melted in a high frequency induction furnace of 50kg capacity to form an ingot of 30kg. Then, the ingot was subjected to a homogenization treatment at 1150°C for 16 hours, and forged to to a billet of 40mm square.
- thermo-mechanical treatment a part of the billets was subjected to a thermo-mechanical treatment, and the remaining billets were subjected to the usual heat treatment (solid solution and aging), to measure mechanical properties thereof.
- the conditions of the thermo-mechanical treatment were as follows. That is, the billet was soaked at 1000°C and rapidly forged to a reduction ratio of 50% through an air hammer, and immediately quenched, and then subjected to an aging at 750 °C for 16 hours.
- the usual heat treatment was carried out by subjecting to a solid solution treatment at 1000°C for 1 hour, quenching, and aging at 750 °C for 16 hours. The thus measured results are also shown in Table 2.
- the limit reduction ratio producing cracks is only 47% in the comparative alloy A, but is as high as 60-72% in the alloys B-F according to the invention, from which it is apparent that the addition of Ca is effective.
- the alloys B-F according to the invention are superior in the strength and toughness to the comparative alloy A. Particularly, it has been found that the thermo-mechanically treated alloys are higher in the strength as compared with the usually heat treated alloy, and are sufficiently high in the toughness.
- An alloy having a chemical composition as shown in the following Table 3 was melted in an electric furnace to form an ingot of 1 ton, which was drawn by forging into a billet of 180mm in diameter, from which an exhaust valve for large vessel was manufactured.
- the forging of the exhaust valve was divided into the forging of shaft and the shaping of valve head.
- the forging of the shaft was conducted by heating at 1000 °C with 3 heat cycles so as to render the diameter into 70mm, wherein the forging ratio at the third heat cycle was 30%, and the finish temperature was about 900 °C.
- the forging of the valve head was conducted to a diameter of about 300mm by heating at 1000°C at one heat, wherein the finish temperature was about 850°C, at the valve face, and about 900 °C at teh central part in the top of the valve head. And also, the forging ratio of the valve face was about 60% at maximum.
- valve was subjected to an age hardening treatment at 750°C for 16 hours as a thermo-mechanical treatment, or to a usual heat treatment wherein the valve was solid soluted at 1000 °C for 1 hour, cooled with water, and aged at 750 °C for 16 hours. Thereafter, the tensile properties of the shaft and the hardness of the vave face were examined and the results obtained are shown in Table 4.
- the valves after the thermo-mechanical treatment are better than the usual heat treatment.
- the thermo-mechanicaly treated valve is compared with the usual heat treated valve, the tensile strength and yield stress of the shaft portion and the hardness of the valve face are superior, and the ductility of the shaft portion is sufficient in practical use.
- the actual exhaust valve is required to not only be excellent in the strength and toughness, but also have a resistance against high -temperature corrosion induced by V and S compounds in the fuel residue from a viewpoint of the performance of the exhaust valve. Further, even if the change of the service temperture as in the exhaust valve is remarkable, it is required to have a considerably excellent adhesion of oxide film. Therefore, vanadium attack test was made with respect to a specimen cut out from the face of the exhaust valve in Example 2.
- the specimen was immersed in a molten mixed salt of vanadium pentoxide and sodium sulfate held at 800 °C, and then the corrosion weight loss was measured to obtain results as shown in the figure 1.
- the exhaust valve after the thermo-mechanical treatment of the alloy in Table 3 has an excellent high-temperature corrosion resistance substantially equal to that of the usual heat treated valve, which is almost equal to that of Nimonic 80A as the usually used expensive Ni based heat resistant alloy.
- the Fe-Ni based heat resistant alloy comprises, on a wight ratio, of 0.01-0.2% of C, not more than 2% of Si, not more than 2% of Mn, 25-50% of Ni, 13-23% of Cr, 1.5-3.5% of Ti, 0.1-0.7% of Al, 0.001-0.05% of B, 0.001-0.01% of Ca, 0.001-0.1% of REM (at least one rare earth element), and if necessary, 0.003-0.05% of N, and further at least one of 0.005-0.05% of Zr, 0.05-1% of V, 0.05-3% of Nb+Ta (inclusive of a case that either is zero), 0.05-3% of Mo and 0.05-3% of W, and the remainder being Fe and inevitable impurities.
- the addition of Ni and Cr improves the heat resistance and corrosion resistance
- the addition of Ti and Al produces the formation of ⁇ -phase effective for the improvement of high-temperature strength
- the addition of B and Al restrains the precipitation of ⁇ -phase
- the addition of Ca improves the hot workability
- the addition of REM improves high- temperature corrosion resistance
- the addition of Zr, V, Nb, Ta, Mo and W more improves the strength, and further the addition of N makes the structure finer.
- the alloy is used by subjecting to the usual heat treatment or the thermo-mechanical treatment, the precipitation of ⁇ -phase effective for the improvement of high-temperature strength is promoted in the crystal grains, and also the precipitation in grain boundary of ⁇ -phase harmful for the strength and notch susceptibility can be restrained , so that the strength and toughness become higher, and the high-temperature corrosion resistance is considerably excellent. Consequently, the invention can provide Fe-Ni based heat resistant alloys cheaper than Ni based heat resistant alloy, and has a remarkable merit that the alloy is suitable as a material for heat resistant components in internal combustion engine such as exhaust valve, heat resistant spring, heat resistant bolt and so on.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60079414A JPS61238942A (ja) | 1985-04-16 | 1985-04-16 | 耐熱合金 |
| DE8686303435T DE3662917D1 (en) | 1985-04-16 | 1986-05-06 | Heat resistant alloys |
| EP86303435A EP0244520B1 (fr) | 1985-04-16 | 1986-05-06 | Alliages résistant aux températures élevées |
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60079414A JPS61238942A (ja) | 1985-04-16 | 1985-04-16 | 耐熱合金 |
| EP86303435A EP0244520B1 (fr) | 1985-04-16 | 1986-05-06 | Alliages résistant aux températures élevées |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| EP0244520A1 true EP0244520A1 (fr) | 1987-11-11 |
| EP0244520B1 EP0244520B1 (fr) | 1989-04-19 |
Family
ID=39628919
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP86303435A Expired EP0244520B1 (fr) | 1985-04-16 | 1986-05-06 | Alliages résistant aux températures élevées |
Country Status (3)
| Country | Link |
|---|---|
| EP (1) | EP0244520B1 (fr) |
| JP (1) | JPS61238942A (fr) |
| DE (1) | DE3662917D1 (fr) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0657558A1 (fr) * | 1993-12-07 | 1995-06-14 | Hitachi Metals, Ltd. | Superalliage à base de Fe |
| EP0669405A2 (fr) * | 1994-02-24 | 1995-08-30 | Daido Tokushuko Kabushiki Kaisha | Aciers résistant aux températures élevées |
| EP0812926A1 (fr) * | 1996-06-13 | 1997-12-17 | Inco Alloys International, Inc. | Alliages à base de nickel pour applications dans la pyrolyse d'éthylène |
| EP1340825A2 (fr) * | 2002-02-27 | 2003-09-03 | Daido Tokushuko Kabushiki Kaisha | Alliage à base de nickel, ressort en cet alliage résistant à haute température et procédé de fabrication de ce ressort |
| EP2806047A1 (fr) * | 2013-05-21 | 2014-11-26 | Daido Steel Co.,Ltd. | Alliage FE-NI durci par précipitation |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3058794B2 (ja) | 1993-08-19 | 2000-07-04 | 日立金属株式会社 | 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 |
| US5660938A (en) * | 1993-08-19 | 1997-08-26 | Hitachi Metals, Ltd., | Fe-Ni-Cr-base superalloy, engine valve and knitted mesh supporter for exhaust gas catalyzer |
| CN103526124B (zh) * | 2013-10-28 | 2015-10-21 | 江西省萍乡市三善机电有限公司 | 一种新型高耐热涡轮增压器密封环及其制备方法 |
| CN116445766A (zh) * | 2023-02-17 | 2023-07-18 | 河钢股份有限公司 | 一种镍铬合金 |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1082739B (de) * | 1953-05-29 | 1960-06-02 | Nyby Bruk Ab | Verwendung nicht ausscheidungshaertender, ueberhitzungsunempfindlicher Legierungen |
| GB999439A (en) * | 1962-05-10 | 1965-07-28 | Allegheny Ludlum Steel | Improvements in or relating to an austenitic alloy |
| US3575734A (en) * | 1968-07-26 | 1971-04-20 | Carpenter Technology Corp | Process for making nickel base precipitation hardenable alloys |
| US3865581A (en) * | 1972-01-27 | 1975-02-11 | Nippon Steel Corp | Heat resistant alloy having excellent hot workabilities |
| EP0092623A1 (fr) * | 1982-04-21 | 1983-11-02 | Westinghouse Electric Corporation | Superalliages austénitiques à durcissement par précipitation |
-
1985
- 1985-04-16 JP JP60079414A patent/JPS61238942A/ja active Pending
-
1986
- 1986-05-06 DE DE8686303435T patent/DE3662917D1/de not_active Expired
- 1986-05-06 EP EP86303435A patent/EP0244520B1/fr not_active Expired
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1082739B (de) * | 1953-05-29 | 1960-06-02 | Nyby Bruk Ab | Verwendung nicht ausscheidungshaertender, ueberhitzungsunempfindlicher Legierungen |
| GB999439A (en) * | 1962-05-10 | 1965-07-28 | Allegheny Ludlum Steel | Improvements in or relating to an austenitic alloy |
| US3575734A (en) * | 1968-07-26 | 1971-04-20 | Carpenter Technology Corp | Process for making nickel base precipitation hardenable alloys |
| US3865581A (en) * | 1972-01-27 | 1975-02-11 | Nippon Steel Corp | Heat resistant alloy having excellent hot workabilities |
| EP0092623A1 (fr) * | 1982-04-21 | 1983-11-02 | Westinghouse Electric Corporation | Superalliages austénitiques à durcissement par précipitation |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0657558A1 (fr) * | 1993-12-07 | 1995-06-14 | Hitachi Metals, Ltd. | Superalliage à base de Fe |
| EP0669405A2 (fr) * | 1994-02-24 | 1995-08-30 | Daido Tokushuko Kabushiki Kaisha | Aciers résistant aux températures élevées |
| EP0669405A3 (fr) * | 1994-02-24 | 1995-11-15 | Daido Steel Co Ltd | Aciers résistant aux températures élevées. |
| EP0812926A1 (fr) * | 1996-06-13 | 1997-12-17 | Inco Alloys International, Inc. | Alliages à base de nickel pour applications dans la pyrolyse d'éthylène |
| EP1340825A2 (fr) * | 2002-02-27 | 2003-09-03 | Daido Tokushuko Kabushiki Kaisha | Alliage à base de nickel, ressort en cet alliage résistant à haute température et procédé de fabrication de ce ressort |
| EP1340825A3 (fr) * | 2002-02-27 | 2003-10-08 | Daido Tokushuko Kabushiki Kaisha | Alliage à base de nickel, ressort en cet alliage résistant à haute température et procédé de fabrication de ce ressort |
| US6918972B2 (en) | 2002-02-27 | 2005-07-19 | Daido Tokushuko Kabushiki Kaisha | Ni-base alloy, heat-resistant spring made of the alloy, and process for producing the spring |
| EP2806047A1 (fr) * | 2013-05-21 | 2014-11-26 | Daido Steel Co.,Ltd. | Alliage FE-NI durci par précipitation |
Also Published As
| Publication number | Publication date |
|---|---|
| EP0244520B1 (fr) | 1989-04-19 |
| DE3662917D1 (en) | 1989-05-24 |
| JPS61238942A (ja) | 1986-10-24 |
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