EP0365716A1 - Nickel-cobalt base alloys - Google Patents
Nickel-cobalt base alloys Download PDFInfo
- Publication number
- EP0365716A1 EP0365716A1 EP88202205A EP88202205A EP0365716A1 EP 0365716 A1 EP0365716 A1 EP 0365716A1 EP 88202205 A EP88202205 A EP 88202205A EP 88202205 A EP88202205 A EP 88202205A EP 0365716 A1 EP0365716 A1 EP 0365716A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- nickel
- reduction
- cross
- cold worked
- 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.)
- Withdrawn
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
-
- 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
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
-
- 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%
-
- 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
- C22C19/07—Alloys based on nickel or cobalt based on cobalt
Definitions
- This invention relates to nickel-cobalt base alloys and particularly nickel-cobalt base alloys having excellent corrosion resistance combined with high strength and ductility at higher service temperatures.
- the Smith patent U.S. No. 3,356,542, issued December 5, 1967, discloses cobalt-nickel base alloys containing chromium and molybdenum.
- the alloys of the Smith patent are corrosion resistant and can be work strengthened under certain temperature conditions to have very high ultimate tensile and yield strength. These alloys can exist in one of two crystalline phases, depending on temperature. They are also characterized by a composition-dependent transition zone of temperatures in which transformation between phases occur. At temperatures above the upper transus, the alloy is stable in the face centered cubic (FCC) structure. At temperatures below the lower transus, the alloy is stable in the hexagonal close-packed (HCP) form.
- FCC face centered cubic
- HCP hexagonal close-packed
- the alloy of the present invention provides an alloy which retains satisfactory tensile and ductility levels and stress rupture properties at temperatures up to about 1300°F. This is a striking improvement in thermomechanical properties and is accomplished by modifying the composition so that the transus is raised to higher temperatures and the precipitation hardening effect is maximized. Thus, the iron and aluminum are reduced to incidental proportions, and titanium or columbium or both are increased to limits described below. Accordingly, as pointed out in my earlier patent, not all alloys whose composition falls within the ranges set out herein are encompassed by the present invention, since many of such compositions would include alloys containing embrittling phases.
- the calculation of the number uses the above formula except that the chemical symbol refers to the "effective atomic fraction" of the element in the alloy.
- This concept takes into account the postulated conversion of a portion of the metal atoms present, particularly nickel, into compounds of the type Ni3X, where X is titanium, columbium or aluminum. These compounds precipitate out of solid solution thus altering the composition of the remaining matrix to reduce the amount of nickel and effectively to increase the amount of the other transition elements.
- the remaining composition has an "effective atomic fraction" of these elements. Consequently many combinations of all the interacting elements can produce the same N v number (small effects on the N v due to carbon and boron are not significant and may be ignored in these calculations).
- the maximum of titanium when used without columbium and using the preferred analysis is 6%.
- the maximum for columbium without titanium is 10%.
- Either titanium or columbium may be used in this alloy, alone or in combination, but must be used so that the resulting N v number does not exceed 2.80.
- the alloy of this invention like those of Smith and my earlier patent is a multiphase alloy forming an HCP-FCC platelet structure.
- the alloys of the present invention broadly comprise the following chemical elements in the indicated weight percentage ranges: Carbon 0.05 max Cobalt 20-40 Molybdenum 6-11 Chromium 15-23 Iron 1.0 max Boron 0.005-0.020 Titanium 0-6 Columbium 0-10 Nickel Bal.
- the preferred aim analysis for melting the alloy of the invention is, in weight percent: Carbon 0.01 max Cobalt 36 Molybdenum 7.5 Chromium 19.5 Iron 1.0 max Boron 0.01 Titanium 3.8 Columbium 1.1 Nickel Bal.
- the alloy of this invention is melted by any appropriate technique such as vacuum induction melting and cast into ingots or formed into powder for subsequent formation into articles by an appropriate known powder metals technique. After casting as ingots, the alloy is preferably homogenized and then hot rolled into plates or other forms suitable for subsequent working.
- the alloy is preferably finally cold worked at ambient temperature to a reduction of cross-section of at least 5% and up to about 40%, although higher levels of cold work may be used but with some loss of thermomechanical properties. It may, however, be cold worked at any temperature below the HCP-FCC transformation zone.
- the alloys After cold working the alloys are preferably aged at a temperature between 800°F and 1350°F for about 4 hours. Following aging the alloys may be air cooled.
- An alloy composition according to this invention was prepared having the composition by weight: C Co Mo Cr Fe B Ti Cb Ni 0.006% 36.3% 7.35% 19.4% 1.04% 0.008% 3.79% 1.20% BAL
- This alloy was hot rolled and divided into two portions, one of which was cold worked to 36% and the other to 48%, aged at 1300°F and formed into test pieces identified by the terms "specimens” which are plain, cylindrical test specimens and “studs” which are threaded test specimens.
- this invention provides unique thermomechanical properties at temperatures in the neighborhood of 1300°F where presently available alloys are no longer serviceable. This provides service temperatures for jet engine fasteners and other parts for higher temperature service, thus making it possible to construct such engines and other equipment for higher operating temperatures and greater efficiency than heretofore possible.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Materials For Medical Uses (AREA)
Abstract
A work hardened nickel-cobalt alloy having high strength and ductility at temperatures of about 1300°F is provided consisting essentially by weight of about 0.05% max carbon, about 20%-40% cobalt, about 6%-11% molybdenum, about 15%-23% chromium, about 1.0% max iron, about 0.0005%-0.020% boron, about 0%-4% titanium, about 0%-2% columbium and the balance nickel, the alloy having been cold worked at a temperature below the HCP-FCC phase transformation zone to a reduction in cross-section between 5% and 50%.
Description
- This invention relates to nickel-cobalt base alloys and particularly nickel-cobalt base alloys having excellent corrosion resistance combined with high strength and ductility at higher service temperatures.
- There has been a continuing demand in the metallurgical industry for alloy compositions which have excellent corrosion resistance combined with high strength and ductility at higher and higher service temperatures.
- The Smith patent, U.S. No. 3,356,542, issued December 5, 1967, discloses cobalt-nickel base alloys containing chromium and molybdenum. The alloys of the Smith patent are corrosion resistant and can be work strengthened under certain temperature conditions to have very high ultimate tensile and yield strength. These alloys can exist in one of two crystalline phases, depending on temperature. They are also characterized by a composition-dependent transition zone of temperatures in which transformation between phases occur. At temperatures above the upper transus, the alloy is stable in the face centered cubic (FCC) structure. At temperatures below the lower transus, the alloy is stable in the hexagonal close-packed (HCP) form. By cold working metastable face centered cubic material at a temperature below the lower limit of the transformation zone, some of the alloy is transformed into the hexagonal close-packed phase which is dispersed as platelets through the matrix of face centered cubic material. It is this cold working and phase transformation which appears to be responsible for the excellent ultimate tensile and yield strength of the alloy of the Smith patent. The alloy is further strengthened by precipitation hardening. This alloy, however, has stress rupture properties which make it not suitable for temperatures above about 800°F.
- In my earlier U.S. Patent No. 3,767,385 I provide an alloy which is an improvement on the Smith patent and which has stress rupture properties suitable for service temperatures to about 1100°F. In the patent I disclosed my discovery that modifying the Smith composition by including elements which I believe form compounds resulting in additional precipitation hardening of the alloy, supplementing the hardening effect due to conversion of FCC to HCP phase, made it possible to provide higher tensile strength and ductility with a lower amount of cold work. This in turn raised the tensile strength and ductility level at higher temperatures. However, above 1100°F neither the alloy of Smith nor the alloy of my earlier patent wil provide the thermomechanical properties of the present allow.
- The alloy of the present invention provides an alloy which retains satisfactory tensile and ductility levels and stress rupture properties at temperatures up to about 1300°F. This is a striking improvement in thermomechanical properties and is accomplished by modifying the composition so that the transus is raised to higher temperatures and the precipitation hardening effect is maximized. Thus, the iron and aluminum are reduced to incidental proportions, and titanium or columbium or both are increased to limits described below. Accordingly, as pointed out in my earlier patent, not all alloys whose composition falls within the ranges set out herein are encompassed by the present invention, since many of such compositions would include alloys containing embrittling phases.
- The formation of these embrittling phases in the transition elements bears a close relationship to the electron vacancies in their sub bands as was predicted by Linus Pauling many years ago ("The Nature of Interatomic Forces in Metals", Physical Review, vol. 54, December 1, 1938). Paul Beck and his coworkers (S. P. Rideout and P. A. Beck, NASA TN 2638) showed how the formation of pure sigma phase in ternary alloys could be related to the atomic percentages of their constituent elements by a formula of the type: Nv = 0.61 Ni + 1.71 CO + 2.66 Fe + 4.66 Cr + 5.66 Mo where Nv is the average number of electron vacancies per 100 atoms of the alloy and the chemical symbols refer to the atomic fraction of that element in the alloy. There is a critcal Nv number above which 100% of sigma can be exerted to form. In engineering alloys however, the presence of a small amount of the sigma phase can render an alloy brittle. The first onset of sigma can be predicted at a lower Nv number which varies with different alloys. In my earlier patent 3,767,385 I describe this variation with the percentage of iron in the alloy. However, in the present alloy, a limit of only 1% iron is imposed and so only one critical Nv number is specified, namely 2.80.
- The calculation of the number uses the above formula except that the chemical symbol refers to the "effective atomic fraction" of the element in the alloy. This concept takes into account the postulated conversion of a portion of the metal atoms present, particularly nickel, into compounds of the type Ni3X, where X is titanium, columbium or aluminum. These compounds precipitate out of solid solution thus altering the composition of the remaining matrix to reduce the amount of nickel and effectively to increase the amount of the other transition elements. Thus, the remaining composition has an "effective atomic fraction" of these elements. Consequently many combinations of all the interacting elements can produce the same Nv number (small effects on the Nv due to carbon and boron are not significant and may be ignored in these calculations). Thus, the maximum of titanium when used without columbium and using the preferred analysis is 6%. Similarly , the maximum for columbium without titanium is 10%. Either titanium or columbium may be used in this alloy, alone or in combination, but must be used so that the resulting Nv number does not exceed 2.80. The alloy of this invention, like those of Smith and my earlier patent is a multiphase alloy forming an HCP-FCC platelet structure.
- The alloys of the present invention broadly comprise the following chemical elements in the indicated weight percentage ranges:
Carbon 0.05 max Cobalt 20-40 Molybdenum 6-11 Chromium 15-23 Iron 1.0 max Boron 0.005-0.020 Titanium 0-6 Columbium 0-10 Nickel Bal. - The preferred aim analysis for melting the alloy of the invention is, in weight percent:
Carbon 0.01 max Cobalt 36 Molybdenum 7.5 Chromium 19.5 Iron 1.0 max Boron 0.01 Titanium 3.8 Columbium 1.1 Nickel Bal. - The alloy of this invention is melted by any appropriate technique such as vacuum induction melting and cast into ingots or formed into powder for subsequent formation into articles by an appropriate known powder metals technique. After casting as ingots, the alloy is preferably homogenized and then hot rolled into plates or other forms suitable for subsequent working.
- The alloy is preferably finally cold worked at ambient temperature to a reduction of cross-section of at least 5% and up to about 40%, although higher levels of cold work may be used but with some loss of thermomechanical properties. It may, however, be cold worked at any temperature below the HCP-FCC transformation zone.
- After cold working the alloys are preferably aged at a temperature between 800°F and 1350°F for about 4 hours. Following aging the alloys may be air cooled.
- The unique properties and advantages of the alloy of this invention can perhaps be best understood by referring to the following examples:
- An alloy composition according to this invention was prepared having the composition by weight:
C Co Mo Cr Fe B Ti Cb Ni 0.006% 36.3% 7.35% 19.4% 1.04% 0.008% 3.79% 1.20% BAL - This alloy was hot rolled and divided into two portions, one of which was cold worked to 36% and the other to 48%, aged at 1300°F and formed into test pieces identified by the terms "specimens" which are plain, cylindrical test specimens and "studs" which are threaded test specimens.
- These specimens were subjected to mechanical testing at elevated temperatures as set out in Tables I, II and III hereafter.
TABLE II Stud Tensile Strength Aged 1300°F - 4 hours 36% Cold Work TEST TEMP. °F TEST STEEL AREA in² LOAD POUNDS STRESS psi 70 5/16" studs .06397 16,220 253,556 16,140 252,305 16,180 ± 57 252,930 ± 885 1100 13,720 214,476 13,420 209,786 13,570 ± 212 212,131 ± 3316 1200 13,820 216,039 13,640 213,225 13,730 ± 127 214,632 ± 1990 1350 12,840 200,719 12,500 195,404 12,670 ± 240 198,062 ± 3758 70 3/8" studs .09506 25,025 263,255 24,500 257,732 24,762 ± 371 260,494 ± 3905 1100 20,050 210,919 19,550 205,659 19,800 ± 354 208,289 ± 3719 1200 20,150 211,971 19,950 209,867 20,050 ± 141 210,919 ± 1488 1350 19,475 204,871 19,540 204,608 19,462 ± 18 204,739 ± 186 TABLE III Specimen Tensile Properties Aged 1300°F - 4 hours 36% Cold Work TEST TEMP. °F UTS .2% YS E RA. UTS .2% YS ELONG. RED. OF AREA 70 253,507 242,485 14.0 42.6 208,918 185,371 23.0 53.5 242,441 + 29,585 226,625 + 36,044 16.7 + 5.5 47.7 + 5.5 264,898 252,020 13.0 46.9 1100 213,131 196,969 12.0 34.0 196,692 179,860 17.0 37.1 204,912 + 11,623 188,414 + 12,098 14.5 + 3.5 35.6 + 2.2 1200 216,364 197,980 11.0 33.3 208,417 189,379 15.0 42.0 212,390 + 5,619 193,679 + 6,082 13.0 + 2.8 37.7 + 6.2 1350 194,949 16,192 10.0 20.4 194,589 172,345 11.0 23.0 194,769 + 255 170,768 + 2,230 10.5 + 0.7 21.7 + 1.8 - A comparison of the properties of the alloys of the Smith patent, may earlier patent and the present invention are set out hereafter on the attached table:
TABLE IV Treatment Smith 3,356,542 Slaney 3,767,385 Present Invention % Cold Work 51% 48% 36% Age 1050°F 1225°F 1300°F Properties Room Temp. 1200°F 1300°F Room Temp. 1200°F 1300°F Room Temp. 1200°F 1300°F Ultimate Tensile Strength (KSI)* 310 Not suitable Not suitable 275 222 Not suitable 242.4 212.4 194.8 0.2 Yield Strength (KSI) 290 Above Above 265 210 Above 226.6 193.7 170.8 Elongation 11 800°F 800°F 8 7 1100°F 16.7 13.0 10.5 Reduction in Area 52 35 22 47.7 37.7 21.7 Stress Not suitable Not suitable 106.4 KSI @1300°F 101.9 hrs. Rupture Above 800°F Above 1100°F 96.0 KSI @1300°F 98.2 hrs. 96.0 KSI @1300°F 79.1 hrs. *KSI = kilopounds/in² = 1,000 psi - From the foregoing data it can be seen that this invention provides unique thermomechanical properties at temperatures in the neighborhood of 1300°F where presently available alloys are no longer serviceable. This provides service temperatures for jet engine fasteners and other parts for higher temperature service, thus making it possible to construct such engines and other equipment for higher operating temperatures and greater efficiency than heretofore possible.
- In the foregoing specification I have set out certain preferred practices and embodiments of this invention, however, it will be understood that this invention may otherwise be embodied within the scope of the following claims.
Claims (8)
1. A nickel-cobalt alloy having high strength and ductility at service temperatures of about 1300°F consisting essentially of the following elements by weight percent: and having a maximum electron vacancy number (Nv) of 2.80, said alloy having been cold worked at a temperature below the lower temperature limit of the HCP-FCC phase transformation zone to a reduction in cross-section between 5% and 50%.
2. An alloy as claimed in claim 1 having been cold worked to a reduction in cross-section between 10% and 40%.
4. An alloy as claimed in any of the preceding claims having been aged at a temperature of about 800°F to 1350°F for about 4 hours after cold working.
5. An alloy as claimed in any of the preceding claims, which has been cold worked at ambient temperature.
6. An alloy as claimed in any of the preceding claims having been aged at about 1350°F for about 4 hours after cold working.
7. An alloy as claimed in any of the preceding claims having been cold worked to a reduction in cross-section of about 36%.
8. An alloy as claimed in any of the preceding claims having been cold worked to a reduction in cross-section of about 36%.
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US63898584A | 1984-08-08 | 1984-08-08 |
Publications (1)
Publication Number | Publication Date |
---|---|
EP0365716A1 true EP0365716A1 (en) | 1990-05-02 |
Family
ID=24562268
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP88202205A Withdrawn EP0365716A1 (en) | 1984-08-08 | 1988-10-04 | Nickel-cobalt base alloys |
Country Status (3)
Country | Link |
---|---|
EP (1) | EP0365716A1 (en) |
JP (1) | JPH02145738A (en) |
SE (1) | SE465037B (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1329528A1 (en) * | 2000-09-19 | 2003-07-23 | NHK Spring Co., Ltd. | Co-ni base heat-resistant alloy and method for production thereof |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5736140B2 (en) * | 2010-09-16 | 2015-06-17 | セイコーインスツル株式会社 | Co-Ni base alloy and method for producing the same |
Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB710413A (en) * | 1951-03-15 | 1954-06-09 | Mond Nickel Co Ltd | Improvements relating to alloys |
US3069258A (en) * | 1958-08-08 | 1962-12-18 | Int Nickel Co | Nickel-chromium casting alloy with niobides |
US3356542A (en) * | 1967-04-10 | 1967-12-05 | Du Pont | Cobalt-nickel base alloys containing chromium and molybdenum |
FR2149935A5 (en) * | 1971-08-06 | 1973-03-30 | Wiggin & Co Ltd Henry | |
US3767385A (en) * | 1971-08-24 | 1973-10-23 | Standard Pressed Steel Co | Cobalt-base alloys |
FR2183353A5 (en) * | 1972-05-04 | 1973-12-14 | Creusot Loire | |
EP0074603A1 (en) * | 1981-09-11 | 1983-03-23 | Hitachi, Ltd. | Gas turbine nozzle having superior thermal fatigue resistance |
-
1988
- 1988-10-04 EP EP88202205A patent/EP0365716A1/en not_active Withdrawn
- 1988-10-06 SE SE8803555A patent/SE465037B/en not_active IP Right Cessation
- 1988-11-24 JP JP29716188A patent/JPH02145738A/en active Pending
Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB710413A (en) * | 1951-03-15 | 1954-06-09 | Mond Nickel Co Ltd | Improvements relating to alloys |
US3069258A (en) * | 1958-08-08 | 1962-12-18 | Int Nickel Co | Nickel-chromium casting alloy with niobides |
US3356542A (en) * | 1967-04-10 | 1967-12-05 | Du Pont | Cobalt-nickel base alloys containing chromium and molybdenum |
FR2149935A5 (en) * | 1971-08-06 | 1973-03-30 | Wiggin & Co Ltd Henry | |
US3767385A (en) * | 1971-08-24 | 1973-10-23 | Standard Pressed Steel Co | Cobalt-base alloys |
FR2183353A5 (en) * | 1972-05-04 | 1973-12-14 | Creusot Loire | |
EP0074603A1 (en) * | 1981-09-11 | 1983-03-23 | Hitachi, Ltd. | Gas turbine nozzle having superior thermal fatigue resistance |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1329528A1 (en) * | 2000-09-19 | 2003-07-23 | NHK Spring Co., Ltd. | Co-ni base heat-resistant alloy and method for production thereof |
EP1329528A4 (en) * | 2000-09-19 | 2005-09-07 | Nhk Spring Co Ltd | Co-ni base heat-resistant alloy and method for production thereof |
Also Published As
Publication number | Publication date |
---|---|
JPH02145738A (en) | 1990-06-05 |
SE8803555A (en) | 1990-04-07 |
SE465037B (en) | 1991-07-15 |
SE8803555D0 (en) | 1988-10-06 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP1507879B1 (en) | Nickel-base alloy | |
US5403547A (en) | Oxidation resistant low expansion superalloys | |
US5637159A (en) | Nickel-cobalt based alloys | |
US4066447A (en) | Low expansion superalloy | |
EP0455752B1 (en) | Iron aluminide alloys with improved properties for high temperature applications | |
US4772342A (en) | Wrought Al/Cu/Mg-type aluminum alloy of high strength in the temperature range between 0 and 250 degrees C. | |
EP0361524A1 (en) | Ni-base superalloy and method for producing the same | |
EP0312966B1 (en) | Alloys containing gamma prime phase and process for forming same | |
US4386976A (en) | Dispersion-strengthened nickel-base alloy | |
JP2004010963A (en) | HIGH STRENGTH Ti ALLOY AND ITS PRODUCTION METHOD | |
US5283032A (en) | Controlled thermal expansion alloy and article made therefrom | |
EP0593824A1 (en) | Nickel aluminide base single crystal alloys and method | |
KR101835408B1 (en) | Titanium alloy with excellent mechanical property and method for manufacturing the same | |
US4795504A (en) | Nickel-cobalt base alloys | |
JPH0440418B2 (en) | ||
US3668023A (en) | Tantalum-containing precipitation-strengthened nickel-base alloy | |
EP0043576B1 (en) | Molybdenum-based alloy | |
EP0387976A2 (en) | New superalloys and the methods for improving the properties of superalloys | |
US3802934A (en) | Precipitation strengthened alloys | |
JP2909089B2 (en) | Maraging steel and manufacturing method thereof | |
Guo et al. | Improving thermal stability of alloy 718 via small modifications in composition | |
EP0365716A1 (en) | Nickel-cobalt base alloys | |
KR102163011B1 (en) | Nickel base superalloy for high temperature fastening member and method for manufacturing the same | |
CA2010147A1 (en) | Tantalum-containing superalloys | |
CN113322396A (en) | Copper-nickel-based medium-entropy alloy with excellent comprehensive mechanical properties and preparation method thereof |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AT CH DE FR GB IT LI NL |
|
17P | Request for examination filed |
Effective date: 19900625 |
|
17Q | First examination report despatched |
Effective date: 19911223 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN |
|
18D | Application deemed to be withdrawn |
Effective date: 19930504 |