US2798827A - Method of casting and heat treating nickel base alloys - Google Patents
Method of casting and heat treating nickel base alloys Download PDFInfo
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- US2798827A US2798827A US582948A US58294856A US2798827A US 2798827 A US2798827 A US 2798827A US 582948 A US582948 A US 582948A US 58294856 A US58294856 A US 58294856A US 2798827 A US2798827 A US 2798827A
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- 238000005266 casting Methods 0.000 title claims description 8
- 238000000034 method Methods 0.000 title claims description 7
- 229910045601 alloy Inorganic materials 0.000 title description 32
- 239000000956 alloy Substances 0.000 title description 32
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title description 31
- 229910052759 nickel Inorganic materials 0.000 title description 15
- 229910000990 Ni alloy Inorganic materials 0.000 claims description 15
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 14
- 238000010438 heat treatment Methods 0.000 claims description 12
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 9
- 229910052796 boron Inorganic materials 0.000 claims description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 7
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 7
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 7
- 229910052782 aluminium Inorganic materials 0.000 claims description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 7
- 229910052799 carbon Inorganic materials 0.000 claims description 7
- 229910052804 chromium Inorganic materials 0.000 claims description 7
- 239000011651 chromium Substances 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims description 7
- 239000011733 molybdenum Substances 0.000 claims description 7
- 229910052710 silicon Inorganic materials 0.000 claims description 7
- 239000010703 silicon Substances 0.000 claims description 7
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims description 3
- 238000002791 soaking Methods 0.000 description 8
- 238000005242 forging Methods 0.000 description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 6
- 238000002844 melting Methods 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- 239000010936 titanium Substances 0.000 description 6
- 229910052719 titanium Inorganic materials 0.000 description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 239000011572 manganese Substances 0.000 description 4
- 238000007711 solidification Methods 0.000 description 4
- 230000008023 solidification Effects 0.000 description 4
- 238000001816 cooling Methods 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 230000015556 catabolic process Effects 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 239000012634 fragment Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
Definitions
- alloys of this type appear to be associated with the high-temperature strength of the alloy and a preferential melting of segregated complex intermetallic bo-ride microconstituents, such as complex (MozCr, Ni) B, ata temperature considerably lower than the melting temperature in the predominant matrix phase.
- a preferential melting is conventionally referred to as hot shortness.
- the heat generated by metal deformation during forging blows of the hammer can cause temperatures in the metal to instantaneously rise to or beyond the melting point of the complex intermetallic boride phase causing complete breakdown of the material.
- the forgeability of cast nickel base alloys of the type described herein which contain boron as an essential alloying element may be greatly improved by a heat treatment which either completely diffuses the brittle microconstituents, existing in the alloy as cast, into the matrix or, in some cases, partially diffuses and breaks up the continuity of the intergranular network.
- the practice of my invention involves soaking a cast nickel base alloy of the type mentioned herein at an elevated temperature for a period of time suflicient to render the alloy forgeable. Superior results are obtained if the soaking or heat treatment is conducted at a temperature within the range of approximately 1900 F. to 2300 F. If a temperature substantially above 2300 F. is employed initially, certain difiiculties in forging are encountered because of the melting of the segregated microconstituents. However, in certain cases, after the diffusion of the microconstituents has begun, the soaking temperature may be increased without causing amelting of the microconstituents. If soaking temperatures substantially below 1900 F. are employed, an excessive length of time is required for the heat treatment.
- the cast nickel base alloy should beusoaked at a temperature within the above-mentioned temperature range for a time equal to at least one hour per inch of cross section of the cast nickel base alloy. I have found that in most instances when the soaking time exceeds about hours, no further improvement in the forgeability of the alloy is obtained. In practice, very beneficial results are obtained by soaking a cast nickel base alloy of the type described herein at an elevated temperature for a time within the range of 8 to 64 hours. At present the preferred heat treatment involves soaking the alloy for about 12 to 24 hours at a temperature within the range of approximately 1900 F. to 2300 F. In a typical heat treatment, the alloy is maintained at 2150 F. for 16 hours.
- the heat treatment of the present invention preferably is employedto render forgeable a cast nickel base alloy having a composition, expressed in weight percent, within the following composition range:
- Example I Carbon 0.10 Manganese 0.10 max. Silicon 0.52 Chromium 15.20 Molybdenum 4.95 Titanium 1.93 Aluminum 2.14 Boron 0.015 Iron 13.70 Nickel Balance
- Example III Carbon 0.10 Manganese 0.01 max. Silicon 0.31 Chromium 15.20 Molybdenum 4.71 Iron Q.
- Nickel base alloys of the type contemplated herein generally are cast at temperatures Within the range of approximately 2700 F. to 3200 F. In most instances, superior castings are obtained ifthe alloy is cast at a temperature within the range of approximately 2750 F. to 3000 F.
- the nickel base alloy is cast and the resulting ingots preferably are allowed to cool to permit inspection and scarfing.
- the ingots are then heated to a temperature within the range of approximately 1900" F. to 2300 F. and are maintained at a temperature within this range for the desired length of time to cause diffusion of the brittle microconstituents.
- the cast alloy ingots need not be allowed to completely cool before heat treatment; if desired, the ingots may be allowed to cool from the casting temperature to a temperature within the desired soaking temperature range and thereafter maintained at a temperature within this range to produce the forgeable structure.
- the cast nickel alloy may be allowed to cool before it is forged or, if desired, it may be forged or otherwise hot Worked directly from the heat treatment with no intermediate cooling.
- the alloy may be forged or hot worked with any conventional forging equipment. In most cases, superior results are obtained if the cast nickel alloy is forged or hot worked at a temperature within the range of approximately 1900 F. to 2300 F.
- alloys employed in the practice of the present invention are singularly adaptable for use in applications which not only require a high corrosion and oxidation re-, sistance but a high strength and dimensional stability as well.
- a method which comprises the steps of casting an alloy consisting essentially of 0 to .35% carbon, 0 to 1.00% manganese, 0 to 1.00% silicon, 10 to 20% chromium, 2 to 24% molybdenum, 1 to 4% titanium, 1 to 5% aluminum, 0.01 to 18% iron, 0.01 to 0.50% boron, and the balance nickel and, after said cast nickel alloy has solidified, heating said cast nickel alloy to a temperature within the range of approximately 1900 F. to 2300 F. for a time of at least one hour per inch of cross-section of said cast nickel alloy to improve the hot working characteristics of said cast nickel alloy.
- a method which comprises the steps of casting an alloy consisting essentially of 0 to 0.25% carbon, 0 to 1.00% manganese, 0 to 1.00% silicon, 13 to 17% chromium, 4 to 6% molybdenum, 1.50 to 3.00% titanium, 1 to 4% aluminum, 8 to 12% iron, 0.01 to 0.10% boron, and the balance nickel and, after said cast nickel alloy has solidified, heating said cast nickel alloy to a temperature within the range of approximately 1900 F. to 2300 F. for a time of at least one hour per inch of cross-section of said cast nickel alloy to improve the hot Working characteristics of said cast nickel alloy.
Description
United States Patent METHOD OF CASTING AND HEAT TREATING NICKEL BASE ALLOYS Dean K. Hanink, Indianapolis, 11111., assignor to General Motors Corporation, Detroit, Mich, a corporation of Delaware No Drawing. Continuation of application Serial No. 324,833, December 8, 1952. This application May 7, 1956, Serial No. 582,948
2 Claims. (Cl. 1483) This application is a continuation of application Serial No. 324,833, filed December 8, 1952.
range heretofore have been readily cast but have exhibited poor forging characteristics, which, prior to my invention, have precluded forging or other hot working of these alloys in large scale operations. The poor forgeability of alloys of this type appears to be associated with the high-temperature strength of the alloy and a preferential melting of segregated complex intermetallic bo-ride microconstituents, such as complex (MozCr, Ni) B, ata temperature considerably lower than the melting temperature in the predominant matrix phase. Such a preferential melting is conventionally referred to as hot shortness.
The specific influence which these complex intermetallic boride constituents play in forgeability is related to the necessary high forging temperature of 19002150 F.
required for hot working alloys of very high hot strength. V
The heat generated by metal deformation during forging blows of the hammer can cause temperatures in the metal to instantaneously rise to or beyond the melting point of the complex intermetallic boride phase causing complete breakdown of the material.
ature and during forging. Metal fragments have indicated selective or preferential melting asdesdribed above. The formation of these boride microconstituents isinherent to the complete solidification of the alloy from the molten state. This is indicated by the shape and distribution of the phases in the microstruct'ure which indicate they are the last to freeze during solidification and are the first to melt when the alloy is reheated to a temperature above approximately 2300" F. A rapid cooling of such an alloy by quenching into water from the molten state will slightly reduce the amount of the intermetallic phase present within the general microstructure. On the other hand, a very slow rate of solidification produces a greater amount of the intermetallic phase. Slow cooling rates generally are properly representative of the solidification occurring in large cast ingots used in production forge shops. efiect on the forgeability of the cast alloy, even in section thicknesses of one inch. Hence, a mere reduction in ingot size or the casting of ingots in the form of thin This breakdown is indicated by fractures in all directions while at the high temper However, the cooling rate has but a negligible 2,798,827 Patented July 9, 1957 ice slabs for use of the rolling of sheet stock will not produce practicably forgeable materials. Hence, up to the present time, alloys of the type contemplated herein have remained highly impracticable to forge or otherwise hot work.
Accordingly, it is the principal object of this invention to improve the forgeability of cast nickel base alloys of the type mentioned herein which contain boron as an essential alloying element. Other objects and advantages of the invention will appear more fully in the description which follows.
According to the present invention, the forgeability of cast nickel base alloys of the type described herein which contain boron as an essential alloying element may be greatly improved by a heat treatment which either completely diffuses the brittle microconstituents, existing in the alloy as cast, into the matrix or, in some cases, partially diffuses and breaks up the continuity of the intergranular network.
The practice of my invention involves soaking a cast nickel base alloy of the type mentioned herein at an elevated temperature for a period of time suflicient to render the alloy forgeable. Superior results are obtained if the soaking or heat treatment is conducted at a temperature within the range of approximately 1900 F. to 2300 F. If a temperature substantially above 2300 F. is employed initially, certain difiiculties in forging are encountered because of the melting of the segregated microconstituents. However, in certain cases, after the diffusion of the microconstituents has begun, the soaking temperature may be increased without causing amelting of the microconstituents. If soaking temperatures substantially below 1900 F. are employed, an excessive length of time is required for the heat treatment.
Generally speaking, the cast nickel base alloy should beusoaked at a temperature within the above-mentioned temperature range for a time equal to at least one hour per inch of cross section of the cast nickel base alloy. I have found that in most instances when the soaking time exceeds about hours, no further improvement in the forgeability of the alloy is obtained. In practice, very beneficial results are obtained by soaking a cast nickel base alloy of the type described herein at an elevated temperature for a time within the range of 8 to 64 hours. At present the preferred heat treatment involves soaking the alloy for about 12 to 24 hours at a temperature within the range of approximately 1900 F. to 2300 F. In a typical heat treatment, the alloy is maintained at 2150 F. for 16 hours.
The heat treatment of the present invention preferably is employedto render forgeable a cast nickel base alloy having a composition, expressed in weight percent, within the following composition range:
Illustrative of specific cast nickel alloys which may be rendered forgeable by the present process are the following where the several ingredients are expressed by weight:
in percent 3 I Example I Carbon 0.10 Manganese 0.10 max. Silicon 0.52 Chromium 15.20 Molybdenum 4.95 Titanium 1.93 Aluminum 2.14 Boron 0.015 Iron 13.70 Nickel Balance Example [I 7 Carbon 0.18 Manganese 0.07 Silicon 0.29 Chromium 15.20 Molybdenum 5 .07 Iron 9.20 Aluminum 2.39 Titanium 1.86 Boron 0.046 Nickel Balance Example III Carbon 0.10 Manganese 0.01 max. Silicon 0.31 Chromium 15.20 Molybdenum 4.71 Iron Q. 9.81 Aluminum 2.68 Titanium 2.47 Boron 0.036 Nickel Balance Example IV Carbon 0.11 Manganese 0.03 Silicon 0.14 Chromium 15.50 Molybdenum 5.91 Iron 9.90 Aluminum 3.16 Titanium 2.28 Boron 0.017 Nickel Balance Cast nickel 'alloys having compositions as shown in the foregoing examples, when soaked at a temperature within the range of approximately 1900 F. to 2300 F. for varying times sufiicient to cause difiusion of the brittle intergranular network into the matrix phase, were readily forged.
Nickel base alloys of the type contemplated herein generally are cast at temperatures Within the range of approximately 2700 F. to 3200 F. In most instances, superior castings are obtained ifthe alloy is cast at a temperature within the range of approximately 2750 F. to 3000 F.
In carrying out the method of the present invention, the nickel base alloy is cast and the resulting ingots preferably are allowed to cool to permit inspection and scarfing.
The ingots are then heated to a temperature within the range of approximately 1900" F. to 2300 F. and are maintained at a temperature within this range for the desired length of time to cause diffusion of the brittle microconstituents.
The cast alloy ingots need not be allowed to completely cool before heat treatment; if desired, the ingots may be allowed to cool from the casting temperature to a temperature within the desired soaking temperature range and thereafter maintained at a temperature within this range to produce the forgeable structure.
Following the heat treatment, the cast nickel alloy may be allowed to cool before it is forged or, if desired, it may be forged or otherwise hot Worked directly from the heat treatment with no intermediate cooling. The alloy may be forged or hot worked with any conventional forging equipment. In most cases, superior results are obtained if the cast nickel alloy is forged or hot worked at a temperature within the range of approximately 1900 F. to 2300 F.
The alloys employed in the practice of the present invention are singularly adaptable for use in applications which not only require a high corrosion and oxidation re-, sistance but a high strength and dimensional stability as well.
Various changes and modifications of the embodiments of the invention described herein may be made by those skilled in the art without departing from the spirit and principles of the invention.
I claim:
'1. A method which comprises the steps of casting an alloy consisting essentially of 0 to .35% carbon, 0 to 1.00% manganese, 0 to 1.00% silicon, 10 to 20% chromium, 2 to 24% molybdenum, 1 to 4% titanium, 1 to 5% aluminum, 0.01 to 18% iron, 0.01 to 0.50% boron, and the balance nickel and, after said cast nickel alloy has solidified, heating said cast nickel alloy to a temperature within the range of approximately 1900 F. to 2300 F. for a time of at least one hour per inch of cross-section of said cast nickel alloy to improve the hot working characteristics of said cast nickel alloy.
2. A method which comprises the steps of casting an alloy consisting essentially of 0 to 0.25% carbon, 0 to 1.00% manganese, 0 to 1.00% silicon, 13 to 17% chromium, 4 to 6% molybdenum, 1.50 to 3.00% titanium, 1 to 4% aluminum, 8 to 12% iron, 0.01 to 0.10% boron, and the balance nickel and, after said cast nickel alloy has solidified, heating said cast nickel alloy to a temperature within the range of approximately 1900 F. to 2300 F. for a time of at least one hour per inch of cross-section of said cast nickel alloy to improve the hot Working characteristics of said cast nickel alloy.
References Cited in the file of this patent UNITED STATES PATENTS
Claims (1)
1.A METHOD WHICH COMPRISES THE STEPS OF CASTING AN ALLOY CONSISTING ESSENTIALLY OF 0 TO .35% CARBON, 0 TO 1.00% MANGANESE, 0 TO 1.00% SILICON, 10 TO 20% CHROMIUM, I TO 24% MOLYBDENUM, 1 TO 4% TUTANIUM, 1 TO 5% ALUMINUM 0.02 TO 18% IRON, 0.01 TO 0.50% BORON, AND THE BALANCE NICKEL AND, AFTER SAID CAST NICKEL ALLOY HAS SOLIDIFIED, HEATING SAID CAST NICKEL ALLOY TO A TEMPERATURE WITHIN THE RANGE OF APPROXIMATELY 1900*F. TO 2300*F. FOR A TIME OF AT LEAST ONE HOUR PER INCH OF CROSS-SECTION OF SAID CAST NICKEL ALLOY TO IMPROVE THE HOT WORKING CHARACTERISTICS OF SAID CAST NICKEL ALLOY.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US582948A US2798827A (en) | 1956-05-07 | 1956-05-07 | Method of casting and heat treating nickel base alloys |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US582948A US2798827A (en) | 1956-05-07 | 1956-05-07 | Method of casting and heat treating nickel base alloys |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US2798827A true US2798827A (en) | 1957-07-09 |
Family
ID=24331066
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US582948A Expired - Lifetime US2798827A (en) | 1956-05-07 | 1956-05-07 | Method of casting and heat treating nickel base alloys |
Country Status (1)
| Country | Link |
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| US (1) | US2798827A (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2977223A (en) * | 1957-12-10 | 1961-03-28 | Westinghouse Electric Corp | Stabilized and precipitation-hardened nickel-base alloys |
| US3010201A (en) * | 1958-12-29 | 1961-11-28 | Owens Corning Fiberglass Corp | Process for fabricating a centrifuge for handling molten glass |
| US3047381A (en) * | 1958-02-03 | 1962-07-31 | Gen Motors Corp | High temperature heat and creep resistant alloy |
| US3151417A (en) * | 1962-09-10 | 1964-10-06 | Pangborn Corp | Throwing wheel vane |
| US3228650A (en) * | 1963-03-04 | 1966-01-11 | Gen Motors Corp | Die and method for its manufacture |
| EP0068628A2 (en) * | 1981-06-12 | 1983-01-05 | Special Metals Corporation | Castable nickel base alloy |
| DE3445768A1 (en) * | 1983-12-27 | 1985-07-04 | United Technologies Corp., Hartford, Conn. | METHOD FOR FORGING SUPER ALLOYS |
| US4717432A (en) * | 1986-04-09 | 1988-01-05 | United Technologies Corporation | Varied heating rate solution heat treatment for superalloy castings |
| US4877465A (en) * | 1986-03-18 | 1989-10-31 | Electicite De France (Service National) | Structural parts of austenitic nickel-chromium-iron alloy |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB583841A (en) * | 1941-12-17 | 1947-01-01 | Mond Nickel Co Ltd | Improvements relating to heat-resisting alloys |
| US2570193A (en) * | 1946-04-09 | 1951-10-09 | Int Nickel Co | High-temperature alloys and articles |
| US2688536A (en) * | 1951-01-27 | 1954-09-07 | Gen Motors Corp | High-temperature creep resistant alloy |
| US2712498A (en) * | 1948-06-01 | 1955-07-05 | Rolls Royce | Nickel chromium alloys having high creep strength at high temperatures |
-
1956
- 1956-05-07 US US582948A patent/US2798827A/en not_active Expired - Lifetime
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB583841A (en) * | 1941-12-17 | 1947-01-01 | Mond Nickel Co Ltd | Improvements relating to heat-resisting alloys |
| US2570193A (en) * | 1946-04-09 | 1951-10-09 | Int Nickel Co | High-temperature alloys and articles |
| US2712498A (en) * | 1948-06-01 | 1955-07-05 | Rolls Royce | Nickel chromium alloys having high creep strength at high temperatures |
| US2688536A (en) * | 1951-01-27 | 1954-09-07 | Gen Motors Corp | High-temperature creep resistant alloy |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2977223A (en) * | 1957-12-10 | 1961-03-28 | Westinghouse Electric Corp | Stabilized and precipitation-hardened nickel-base alloys |
| US3047381A (en) * | 1958-02-03 | 1962-07-31 | Gen Motors Corp | High temperature heat and creep resistant alloy |
| US3010201A (en) * | 1958-12-29 | 1961-11-28 | Owens Corning Fiberglass Corp | Process for fabricating a centrifuge for handling molten glass |
| US3151417A (en) * | 1962-09-10 | 1964-10-06 | Pangborn Corp | Throwing wheel vane |
| US3228650A (en) * | 1963-03-04 | 1966-01-11 | Gen Motors Corp | Die and method for its manufacture |
| EP0068628A2 (en) * | 1981-06-12 | 1983-01-05 | Special Metals Corporation | Castable nickel base alloy |
| EP0068628A3 (en) * | 1981-06-12 | 1983-02-02 | Special Metals Corporation | Castable nickel base alloy |
| DE3445768A1 (en) * | 1983-12-27 | 1985-07-04 | United Technologies Corp., Hartford, Conn. | METHOD FOR FORGING SUPER ALLOYS |
| US4877465A (en) * | 1986-03-18 | 1989-10-31 | Electicite De France (Service National) | Structural parts of austenitic nickel-chromium-iron alloy |
| US4717432A (en) * | 1986-04-09 | 1988-01-05 | United Technologies Corporation | Varied heating rate solution heat treatment for superalloy castings |
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