EP0247577A1 - Alliage à base de nickel durcissable par vieillissement et résistant à la corrosion - Google Patents
Alliage à base de nickel durcissable par vieillissement et résistant à la corrosion Download PDFInfo
- Publication number
- EP0247577A1 EP0247577A1 EP87107651A EP87107651A EP0247577A1 EP 0247577 A1 EP0247577 A1 EP 0247577A1 EP 87107651 A EP87107651 A EP 87107651A EP 87107651 A EP87107651 A EP 87107651A EP 0247577 A1 EP0247577 A1 EP 0247577A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- molybdenum
- titanium
- weight percent
- niobium
- 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 95
- 239000000956 alloy Substances 0.000 title claims abstract description 95
- 230000007797 corrosion Effects 0.000 title claims abstract description 72
- 238000005260 corrosion Methods 0.000 title claims abstract description 72
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 105
- 239000010936 titanium Substances 0.000 claims abstract description 96
- 239000011651 chromium Substances 0.000 claims abstract description 94
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 90
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 89
- 239000010955 niobium Substances 0.000 claims abstract description 89
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 86
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 79
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 71
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 70
- 239000011733 molybdenum Substances 0.000 claims abstract description 70
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 67
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 66
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 52
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 45
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 32
- 238000005336 cracking Methods 0.000 claims abstract description 32
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 claims abstract description 11
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 claims abstract description 10
- 238000001953 recrystallisation Methods 0.000 claims abstract description 9
- 230000035882 stress Effects 0.000 claims description 32
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 28
- 229910052799 carbon Inorganic materials 0.000 claims description 24
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 17
- 230000002829 reductive effect Effects 0.000 claims description 17
- 230000032683 aging Effects 0.000 claims description 14
- 229910052742 iron Inorganic materials 0.000 claims description 14
- 238000003483 aging Methods 0.000 claims description 12
- 230000003247 decreasing effect Effects 0.000 claims description 12
- 239000011572 manganese Substances 0.000 claims description 11
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 10
- 230000007423 decrease Effects 0.000 claims description 10
- 229910052748 manganese Inorganic materials 0.000 claims description 9
- 230000009467 reduction Effects 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 9
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 6
- VNTLIPZTSJSULJ-UHFFFAOYSA-N chromium molybdenum Chemical compound [Cr].[Mo] VNTLIPZTSJSULJ-UHFFFAOYSA-N 0.000 claims description 6
- 239000010703 silicon Substances 0.000 claims description 6
- 238000011282 treatment Methods 0.000 claims description 6
- 238000000034 method Methods 0.000 claims description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- 238000004519 manufacturing process Methods 0.000 claims description 4
- 239000013067 intermediate product Substances 0.000 abstract description 2
- 239000000203 mixture Substances 0.000 description 47
- 239000004848 polyfunctional curative Substances 0.000 description 23
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 18
- 239000000243 solution Substances 0.000 description 13
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 11
- 238000010438 heat treatment Methods 0.000 description 11
- 238000001556 precipitation Methods 0.000 description 11
- 229910002092 carbon dioxide Inorganic materials 0.000 description 9
- 230000000694 effects Effects 0.000 description 9
- 239000000463 material Substances 0.000 description 9
- TWRXJAOTZQYOKJ-UHFFFAOYSA-L Magnesium chloride Chemical compound [Mg+2].[Cl-].[Cl-] TWRXJAOTZQYOKJ-UHFFFAOYSA-L 0.000 description 8
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 8
- 230000002411 adverse Effects 0.000 description 8
- 150000001805 chlorine compounds Chemical class 0.000 description 8
- 150000004763 sulfides Chemical class 0.000 description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 7
- 238000007792 addition Methods 0.000 description 7
- 229910052796 boron Inorganic materials 0.000 description 7
- 239000001569 carbon dioxide Substances 0.000 description 7
- 229910052802 copper Inorganic materials 0.000 description 7
- 239000010949 copper Substances 0.000 description 7
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 6
- 238000006243 chemical reaction Methods 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- 238000005482 strain hardening Methods 0.000 description 6
- 229910052717 sulfur Inorganic materials 0.000 description 6
- 239000011593 sulfur Substances 0.000 description 6
- 229910052721 tungsten Inorganic materials 0.000 description 6
- RWSOTUBLDIXVET-UHFFFAOYSA-N Dihydrogen sulfide Chemical compound S RWSOTUBLDIXVET-UHFFFAOYSA-N 0.000 description 5
- 229910021578 Iron(III) chloride Inorganic materials 0.000 description 5
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 5
- 238000009835 boiling Methods 0.000 description 5
- RBTARNINKXHZNM-UHFFFAOYSA-K iron trichloride Chemical compound Cl[Fe](Cl)Cl RBTARNINKXHZNM-UHFFFAOYSA-K 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 229910052698 phosphorus Inorganic materials 0.000 description 5
- 239000011574 phosphorus Substances 0.000 description 5
- 229910052726 zirconium Inorganic materials 0.000 description 5
- 239000010941 cobalt Substances 0.000 description 4
- 229910017052 cobalt Inorganic materials 0.000 description 4
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 4
- 235000019589 hardness Nutrition 0.000 description 4
- 229910000037 hydrogen sulfide Inorganic materials 0.000 description 4
- 229910001629 magnesium chloride Inorganic materials 0.000 description 4
- 229910052715 tantalum Inorganic materials 0.000 description 4
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 4
- 239000010937 tungsten Substances 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- 239000011777 magnesium Substances 0.000 description 3
- 229910052749 magnesium Inorganic materials 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- 230000004580 weight loss Effects 0.000 description 3
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 2
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 2
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000011575 calcium Substances 0.000 description 2
- 229910052791 calcium Inorganic materials 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 238000004140 cleaning Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000014509 gene expression Effects 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- QAOWNCQODCNURD-UHFFFAOYSA-N sulfuric acid group Chemical group S(O)(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- 238000010998 test method Methods 0.000 description 2
- 238000005303 weighing Methods 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910000967 As alloy Inorganic materials 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910000599 Cr alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910001122 Mischmetal Inorganic materials 0.000 description 1
- 229910001182 Mo alloy Inorganic materials 0.000 description 1
- 229910001257 Nb alloy Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- VVTSZOCINPYFDP-UHFFFAOYSA-N [O].[Ar] Chemical compound [O].[Ar] VVTSZOCINPYFDP-UHFFFAOYSA-N 0.000 description 1
- 239000001996 bearing alloy Substances 0.000 description 1
- 239000012267 brine Substances 0.000 description 1
- ZMIGMASIKSOYAM-UHFFFAOYSA-N cerium Chemical compound [Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce] ZMIGMASIKSOYAM-UHFFFAOYSA-N 0.000 description 1
- 238000001311 chemical methods and process Methods 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 230000002301 combined effect Effects 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000002939 deleterious effect Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000002803 fossil fuel Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- 229910001068 laves phase Inorganic materials 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 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 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 230000036961 partial effect Effects 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 239000003209 petroleum derivative Substances 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 239000011780 sodium chloride Substances 0.000 description 1
- HPALAKNZSZLMCH-UHFFFAOYSA-M sodium;chloride;hydrate Chemical compound O.[Na+].[Cl-] HPALAKNZSZLMCH-UHFFFAOYSA-M 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
- 239000012085 test solution Substances 0.000 description 1
- 125000000101 thioether group Chemical group 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-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
- 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
-
- E—FIXED CONSTRUCTIONS
- E21—EARTH OR ROCK DRILLING; MINING
- E21B—EARTH OR ROCK DRILLING; OBTAINING OIL, GAS, WATER, SOLUBLE OR MELTABLE MATERIALS OR A SLURRY OF MINERALS FROM WELLS
- E21B17/00—Drilling rods or pipes; Flexible drill strings; Kellies; Drill collars; Sucker rods; Cables; Casings; Tubings
-
- 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%
Definitions
- This invention relates to a nickel-base alloy and more particularly to such an alloy and products made therefrom having a unique combination of corrosion resistance and age or precipitation hardenability properties in the heat treated condition and without requiring working below the alloy's recrystallization temperature.
- U.S. Patent No. 3,160,500 granted December 8, 1964 to H.L. Eiselstein and J. Gadbut relates to a matrix- stiffened alloy described as having high strength containing 55-62% Ni, 7 to 11% Mo, 3 to 4.5% Nb, 20-24% Cr, up to 8% W, 0.1% Max. C, 0.5% Max. Si, 0.5% Max. Mn, 0.015% Max. B, 0.40% Max of a deoxidizer selected from the group consisting of Al and Ti and the balance essentially Fe but not more than 20%.
- percent is given as weight percent (w/o) unless otherwise indicated.
- the alloy is further characterized as having at least about 60 ksi 0.2% YS (414 MN/m2) at room temperature and being essentially non-age hardenable, non-age hardenable being defined in the 3,160,500 patent as a maximum increase in yield strength of 20 ksi (138 MN/m2) when subjected to a heat treatment at a temperature of about 1100 to 1300 F as compared to the yield strength of the alloy in the annealed condition. According to the patent, the total amount of aluminum plus titanium present in the alloy is not to exceed 0.4% "as otherwise the alloys tend to become age hardenable" (Col. 2, lines 45-49).
- Alloys 1-3 exemplifying the claimed subject matter of the patent and two alloys (identified here as Alloys A and B) described as outside the patented invention, are set forth in Table I where the 0.2% YS (ksi) at room temperature in the annealed condition (1900 F, 1 hour) as reported in the patent are also given. With regard to Table I it is to be noted that tungsten was reported only in connection with Alloy 2. Alloy A was described as being “similar in composition” to Alloy 1 except as indicated (Pat., col. 4, lines 10 & 11). Alloy B was characterized as having "age hardened strongly but had a yield strength at room temperature of only 49,500 psi, . . . when tested after a 1900 F anneal.”
- Type 625 alloy as well as other compositions of the 3,160,500 patent are characterized by outstanding corrosion resistance particularly resistance to chlorides, sulfides and carbon dioxide, combined with stability at elevated temperatures, this combination of properties was achieved by eliminating age or precipitation hardening for all practical purposes because of the prohibitively long time required at the elevated temperature required for age hardening.
- a preferred composition contains 0.03% C, 0.18% Mn, 0.27% Si, 21% Cr, 0.6% Al, 0.6% Ti, 4% Nb, 3% Mo, 0.009% B, 53% Ni and balance Fe.
- iron is limited to 20% Max. with 60-75% Ni + Co, Co ⁇ 40%. While an alloy within the range of this patent has been available as Pyromet 718 (trademark of the applicant) characterized by high strength, stress rupture life and ductility at elevated temperatures, it and other compositions of the 3,046,108 patent have not provided the desired corrosion resistance in environments containing chlorides, sulfides and carbon dioxide at elevated temperatures required for use in sour wells.
- European Patent Application No. 92,397 published October 26, 1983, on the other hand is expressly directed to providing an alloy suitable for use in sour gas wells where corrosion resistance is required to sulfides, carbon dioxide, methane and brine (chlorides) at temperatures up to 300 C.
- This publication suggests that the most likely causes of failure under such conditions are sulfide stress corrosion cracking, chloride stress corrosion cracking, pitting and general corrosion.
- Alloys A-X there are six compositions outside the claimed subject matter of the 92,397 application, Alloys F-L, containing 1.9-3.1% Nb but only Alloy K contains a significant amount of Ti for consideration here.
- patents and the Japanese publication specify the composition set forth therein as containing 0.5-4% of at least one of Nb, Ti, Zr, Ta, and V.
- the 4,400,210 and 4,400,211 patents (Col. 6) and presumably also the Japanese publication state the elements Nb, Ti, Zr, Ta and V are equivalent to each other in providing precipitation (age) hardening due to the formation of an intermetallic compound with Ni.
- EPA Publication No. 82-56480 published July 28, 1982 relates to a nickel base alloy having resistance to stress corrosion cracking in contact with water at elevated temperature as in boiling water nuclear reactors or pressurized water reactors.
- the proposed alloy is described as consisting essentially of 15-25% Cr, 1-8% Mo, 0.4-2% Al, 0.7-3% Ti, 0.7-4.5% Nb and the balance Ni, strengthened by gamma prime and/or gamma double prime.
- the gamma prime phase is defined as an intermetallic compound of Ni3(Al, Ti) and the gamma double prime phase as an intermetallic compound of Ni3Nb.
- age hardenable compositions as exemplified by said U.S. Patent No. 3,046,108 though age hardenable to a desirably high strength, leave much to be desired with regard to corrosion resistance, particularly resistance to cracking under stress in media containing sulfides, chlorides and carbon dioxide as encountered in sour wells.
- the problem to which the application is directed is to provide an age hardenable nickel base chromium-molybdenum-containing alloy and articles made therefrom which without being warm or cold worked will have a unique combination of strength and corrosion resistance particularly to pitting and crevice corrosion and resistance to stress corrosion cracking under high stress in severely corrosive environments.
- the alloy and articles made therefrom should have high resistance to pitting and crevice corrosion and to stress corrosion cracking in the presence of chlorides, sulfides and/or carbon dioxide at elevated pressures and temperatures while being hardenable by heat treatment to a 0.2% yield strength greater than about 100 ksi (about 690MN/m2) without the need for working below the recrystallization temperature, that is warm or cold working.
- the alloy and articles made therefrom are moreover to be highly resistant to such corrosion in the chloride-, sulfide-, and carbon dioxide- bearing media at the elevated pressures and temperatures, e.g., up to about 500 F (about 260 C) encountered in deep sour oil and/or gas wells.
- the foregoing problem is solved in accordance with the invention by providing a nickel base, chromium-molybdenum-containing alloy which in weight percent consists essentially of the composition set forth in Table II below.
- the balance of the composition is at least 55% nickel, the sum of the percent chromium and molybdenum being not greater than 31, and the sum of the percent niobium, titanium and aluminum being such that the total atomic percent thereof is about 3.5 a/o to 5 a/o when calculated as 0.64(w/o Nb) + 1.24(w/o Ti) + 2.20(w/o Al).
- Other elements can be present which aid in making and processing the alloy or which do not objectionably detract from the desired properties.
- the broad range of one or more elements may be used with the preferred ranges of other elements.
- the stated broad maximum or minimum of one or more elements can be used with their preferred maximums or minimums respectively in Table II and hereinafter.
- niobium it is intended by reference to niobium to include the usual amount of tantalum found in commercially available niobium bearing alloys used in making alloying additions of niobium to commercial alloys.
- nickel-base composition in addition to nickel the essential elements are chromium, molybdenum, niobium, titanium and aluminum. Optional elements and the usual incidental impurities may also be present.
- Carbon and nitrogen are not considered to be desirable additions in this composition because each can have an adverse effect upon corrosion resistance and because each interferes with the desired hardening reaction, carbon by tying up niobium and titanium, and nitrogen by tying up titanium.
- carbon is limited to no more than about 0.1% and preferably to no more than about 0.03% or better yet to no more than about 0.02%.
- Nitrogen is limited to no more than about 0.04% or even to a maximum of about 0.03% and is preferably limited to no more than about 0.01%.
- the hardener elements, niobium and titanium are present in the larger amounts indicated by their ranges. While better results can be attained with extremely low levels of carbon present, e.g. less than about 0.005% or less than about 0.003%, the cost of reducing carbon below 0.01% makes that a practical minimum for carbon when the added cost would not be warranted.
- Manganese may be present in amounts up to about 5% but it is preferably kept low, to no more than about 2%, better yet to no more than about 0.5% or even no more than about 0.2%, because manganese increases the tendency for grain boundary precipitation and reduces intergranular corrosion resistance, and pitting and crevice corrosion resistance.
- the larger amounts of manganese when present are at the expense of the larger amounts of iron contemplated in this alloy.
- silicon While silicon may be present it is preferably kept low because it promotes the formation of unwanted Laves phase and excessive amounts of silicon can affect weldability and hot workability. Thus, silicon is limited to no more than about 1%, preferably no more than about 0.5% and better yet no more than about 0.2%. Phosphorus and sulfur are considered impurities in this alloy because both adversely affect hot workability and cleanliness of the alloy and promote hydrogen embrittlement. Therefore, phosphorus and sulfur are kept low, less than about 0.03% each. Preferably phosphorus is limited to 0.015% Max. and sulfur to 0.010% Max.
- cobalt contributes to corrosion resistance when present in this composition and to that end may replace nickel on a weight-for-weight basis.
- the cost of cobalt is now and is expected to continue to be greater than nickel so that the extent of the benefit gained from a given addition of cobalt must be weighed against the cost thereof. For that reason, cobalt is limited to a maximum of 5% and nickel is at least 55%. Preferably, at least 57%, better yet at least 59% nickel is present.
- tungsten can be substituted for its equivalent percent molybdenum, that is about 2% by weight tungsten for each 1% by weight molybdenum replaced, when it may be beneficial but at least about 7% molybdenum must be present.
- Boron up to a maximum of about 0.02% may be present in this alloy. Even though many of the advantages of the present alloy can be attained without a boron addition, it is preferred for consistent best results that a small amount of boron of about 0.001% to about 0.006% Max. be present. Also to aid in refining the alloy, up to about 0.50% Max. preferably not more than 0.08% Max. zirconium may be present and from a few hundredths up to about a tenth of a percent of other elements such as magnesium, calcium or one or more of the rare earths may be added.
- Copper may be present in this alloy when it may be exposed to sulfuric acid-bearing media or it is desired to ensure maximum resistance to chloride and sulfide stress corrosion cracking at elevated temperature when its adverse effect, if any, on pitting, crevice and intergranular corrosion resistance can be tolerated. To that end, up to about 3%, preferably no more than 2.0%, copper may be present.
- Iron also is not an essential element in this composition and, if desired, may be omitted. Because commercially available alloying materials contain iron it is preferred to reduce melting costs by using them. It is also believed that iron contributes to resistance to room temperature sulfide stress-cracking. Thus, up to about 20% Max. iron may be present but about 2% to no more than about 14% is preferred.
- Chromium, molybdenum, niobium, titanium, aluminum and nickel are critically balanced to provide the uniquely outstanding combination of strength and corrosion resistance properties characteristic of the alloy provided by the present invention.
- the maximum tolerable molybdenum is proportionately reduced on a one-for-one weight percent basis from 12% to 7%. Because the larger amounts of chromium ( ⁇ 22%) or molybdenum (>11%) may result in the precipitation of deleterious phases, they are preferably avoided with only about 55% nickel and a minimum of 57% or better yet 59% nickel is preferred.
- the elements niobium, titanium, and aluminum take part in the age hardening reaction by which the present composition is strengthened by heat treatment and without requiring warm or cold working.
- This invention in part stems from the discovery that the elements niobium and titanium together with smaller amounts of aluminum in the critical proportions specified herein in relation to each other and to the elements chromium, molybdenum and nickel provide a high 0.2% yield strength combined with a high level of corrosion resistance suitable for use under a wide variety of conditions and, when balanced as indicated to be preferred herein, provide a composition suitable for use under the rigorous conditions to be encountered in deep sour wells.
- compositions strengthened primarily with niobium and titanium differ from those strengthened with titanium or titanium and aluminum in that the titanium and the titanium plus aluminum strengthened material showed extensive intergranular precipitation of chromium-rich carbides (M23C6) during aging which occurred independent of the chromium and molybdenum content.
- the hardener elements niobium, titanium and aluminum must be carefully balanced if the high strength of this composition provided by the age hardening reaction is not to result in an unwanted reduction in corrosion resistance. While the broad range for niobium has been stated as about 2-6% and for titanium about 0.50-2.5%, for better corrosion resistance a preferred niobium range is about 2.5-5% or better yet 2.75-4.25% and a preferred titanium range is about 0.6 to 2% or even better yet about 0.7 to 2.0%.
- the total hardener content should range from 3.5 a/o up to about 5 a/o and better yet should not exceed about 4.5 a/o for a better all around combination of properties as described herein.
- nickel should be increased whenever the hardener content is increased with the ratio of the atomic percent increase in nickel to the atomic percent increase in hardener content being 3 to 1 to compensate for the additional nickel removed from the alloy matrix. In this way, the adverse effect of undesired phases, such as sigma phase, and their attendant adverse effect can be avoided.
- aluminum is beneficial in stabilizing the desired intragranular precipitate and relatively small amounts are found advantageous. It has also been noted that above about 0.25%, that is at about 0.35% and above, aluminum does not appear to add to but rather to detract from the yield strength at room temperature. Therefore, while up to about 1% aluminum can be present, for better results, particularly higher yield strength, aluminum is limited to no more than 0.5%. In this regard, it is also to be noted that when the larger amounts of aluminum objectionably affect the room temperature yield strength, the strength of the composition can be increased by using a lower solution or a higher primary aging temperature. Also, if the tolerable maximum amounts of niobium and/or titanium are not already present then one or both may be increased. Therefore, aluminum amounts in excess of 0.35% (0.77 a/o) are not to be included in atomic percent determinations throughout this specification but only insofar as room temperature yield strength is concerned.
- the alloy of this invention can be melted and hot worked using techniques that are well known and conventionally used in the commercial production of nickel-base alloys.
- a double melting practice is preferred such as melting in the electric arc furnace plus argon-oxygen decarburization or vacuum induction melting, to prepare a remelt electrode followed by remelting, e.g. consumable remelting.
- Deoxidation and desulfurization with magnesium and/or calcium when used contributes to hot workability.
- Additions of rare earths, e.g. in the form of misch metal which is primarily a mixture of cerium and lanthanum, or yttrium may also be beneficial.
- Small amounts of boron and/or zirconium also stabilize grain boundaries and may contribute to hot workability.
- the elements present in this composition are balanced to provide an austenitic microstructure in which the strengthening elements niobium, titanium and aluminum react during appropriate heat treatment with nickel to form one or more strengthening phases in the form of an intragranular precipitate by age or precipitation hardening.
- the composition of those phases is generalized as Ni3(Nb,Ti,Al) and may include gamma prime and/or gamma double prime.
- the age-hardenable corrosion resistant nickel-base chromium, molybdenum, niobium, titanium and aluminum alloy of the present invention is readily fabricated into a wide variety of parts following practices utilized in connection with other nickel base alloys. It is well suited to be produced in the form of billets, bars, rod, strip and plate as well as a variety of semi-finished and finished articles for use where its outstanding combination of strength and corrosion resistance in the heat treated condition is desired without requiring working below the recrystallization temperature. Homogenization and hot working is carried out from a temperature of about 2050-2200 F (about 1120-1200 C).
- solutioning and recrystallization is carried out by heating to a solution treating temperature of about 1800-2200 F (about 980 - 1200 C).
- An optimum solution treating temperature is 1900 F (1038 C) and preferably should be no higher than about 1950 F (about 1065 C) because higher temperature tends to reduce strength and pitting and crevice corrosion resistance, and to increase intergranular precipitation during the aging heat treatment.
- Lower solution treating temperatures than the recrystallization temperature are preferably not used to avoid an adverse effect on corrosion resistance and microstructure though higher strength may result. While care is to be exercised in selecting the solution and aging treating temperatures, the temperatures to be used for optimum results are readily determined.
- a single step age hardening heat treatment may be used if desired but to provide optimum strength and corrosion resistance a two-step aging treatment is preferred.
- the initial or primary aging treatment can be at about 1250 F (677 C) to 1450 F (788 C), preferably between about 1300 and 1400 F (about 700 - 760 C), e.g. 1350 F (732 C), followed by secondary aging at about 1100 - 1250 F (about 590 - 675 C). It is to be noted that in this composition, the use of higher primary aging temperatures result in increased strength but contributes to intergranular precipitation.
- Table III The examples set forth in Table III are exemplary of the present invention and in addition to the amounts indicated under each element contained from 0.001-0.006% boron. Other elements when present in more than what is considered a residual or incidental amount in keeping with good commercial practice are indicated in the footnote to the table.
- Examples 1-52 were vacuum induction melted as small laboratory heats and, unless otherwise noted, contained ⁇ 0.2% manganese, ⁇ 0.2% silicon, ⁇ 0.015% phosphorus, ⁇ 0.010% sulfur, and ⁇ 0.01% nitrogen. An addition of 0.05% magnesium was made to each to complete desulphurization and/or deoxidation before being cast as an ingot.
- the ingots were homogenized at 2185 F (1195 C) for an extended period (about 60-70 hours) and then forged from a starting temperature of about 2100 F (about 1150 C), with intermediate reheats as required, to bars .75 in ⁇ 1.25 or 1.5 in (1.9 ⁇ 3.2 or 3.8 cm). Sections of forged bar from each example were then formed into .125 in (.32 cm) thick strip.
- Tensile and corrosion test specimens were prepared from bar and/or strip material of the examples and heats of Tables III and IIIA and were tested in the solution treated (recrystallized) plus age hardened condition unless otherwise stated.
- Room temperature tensile and hardness data are set forth in Tables IV and IVA.
- the 0.2% yield strength (“0.2% YS") is given as the average of two tests in “ksi” and “(MN/m2)" as is also the ultimate tensile strength ("UTS").
- the percent elongation in four diameters or widths depending on whether from bar or strip specimens is indicated as "El.(%)".
- the percent reduction in area is indicated as "RA(%)”.
- the average room temperature hardness on the Rockwell C scale is indicated as "HRC”.
- the alloy of the present invention in the solution treated and age hardened condition is brought to a high yield strength with a minimum hardener content (Nb+Ti+Al) of 3.5 a/o without requiring warm or cold working for that purpose.
- Yield strengths greater than 100 ksi (690 MN/m2), that is at least about 105 ksi (about 724.9 MN/m2) are consistently provided with hardener contents greater than 3.5 a/o with niobium ⁇ 3.0 w/o.
- the minimum weight percent titanium is proportionately increased from about 0.8 w/o to about 2.0 w/o, that is, a reduction of a predetermined amount in the niobium content should be accompanied by 1.2 times that amount of an increase in the weight percent titanium present in the alloy.
- a reduction of a predetermined amount in the niobium content should be accompanied by 1.2 times that amount of an increase in the weight percent titanium present in the alloy.
- Preferably in making this and the following adjustments in niobium and titanium with regard to yield strength only up to about 0.35 w/o (0.77 a/o) aluminum is present.
- niobium and titanium are adjusted proportionately in relation to each other so that as the percent by weight niobium is decreased from about 3.9 w/o to 3.0 w/o the minimum weight percent titanium is increased proportionately from 0.50 w/o to about 1.1 w/o, that is, the ratio of an increase in titanium to a decrease in niobium is equal to about 2/3. As the weight percent niobium is decreased from 3.0% to 2.75% the minimum weight percent titanium is increased proportionately from about 1.1% to 1.6%, that is, a ratio of an increase in titanium to the accompanying decrease in niobium of 2.
- the weight percent niobium is decreased from about 4.5 w/o to about 3.5 w/o the weight percent titanium is increased proportionately from 0.50 to 1.5 w/o, then a minimum 0.2% yield strength of about 140 ksi (about 965 MN/M2) is attainable.
- the carbon content exceeds about 0.03%, the effect of carbon on strength can be offset by increasing hardener content, particularly niobium, so as to compensate for the amount tied up by carbon and thereby rendered unavailable for the desired hardening reaction. Because carbon tends toward increased intergranular precipitation and an attendant reduction in corrosion resistance, the higher carbon contents contemplated herein, e.g. greater than 0.06% are to be avoided when its affect on corrosion resistance cannot be tolerated.
- Example 27 illustrates that with about 0.06% carbon the average yield strength was 99.5 (101.0 and 98.0) ksi.
- the strength of Ex. 27 can be increased by increasing the hardener content or by using a lower solution treating temperature, the Al heat treatment.
- processing of the material should be such as to provide a grain size in the age hardened material of about ASTM 5 or finer.
- V-notch Charpy impact strength 40 ft-lb (54.2 J)
- a maximum of about 11% molybdenum is preferred with about 16-18% chromium.
- the maximum molybdenum is proportionately reduced from 11% to 9%, and as chromium is increased from 22.0% to 24%, %Cr + %Mo ⁇ 31.
- Ex. 40 specimens had a V-notch Charpy impact strength of 34.5 as heat treated B1 and 23.5 ft-lb (31.9 J) exposed.
- Heats 910, 914 and 967 (%Cr + %Mo > 31) as B1 heat treated had impact strengths, respectively, of 66.5 ft-lb (90.2 J), 30.5 ft-lb (41.4 J) and 42 ft-lb (56.9 J), and in the exposed condition they had, respectively, 33.5 ft-lb (45.4 J), 17 ft-lb (23 J) and 24.5 ft-lb (33.2 J).
- the preferred composition of the present invention as set forth in Table II hereinabove is characterized by a minimum Charpy V-notch impact strength of 40 ft-lb (54.2 J).
- Molybdenum is about four times as effective as chromium (in weight percent) in improving pitting and crevice corrosion resistance when tested at 40 C in 6% ferric chloride (FeCl3) plus 1% hydrochloric acid (HCl).
- a preferred composition provides a higher level of resistance in FeCl3-HCl, that is, an average weight loss of no more than 1 mg/cm2 when tested with a standard crevice (ASTM G-48) at 40 C for 72 hours.
- ASTM G-48 standard crevice
- this composition there is preferably a minimum of about 17% chromium and the percent chromium plus four times the percent molybdenum is not less than about 52%.
- This preferred composition also consistently provides freedom from the onset of pitting below the temperature at which the test medium boils, about 100 C, however, no more than about 11% molybdenum should be used with 17% chromium. From the worst case data obtained with the crevice corrosion test specimens exposed at 55 C, it is apparent good pitting and crevice corrosion resistance is preferably maintained with a minimum of about 59% nickel and by limiting the molybdenum content to no more than about 10%. The molybdenum and chromium contents are also preferably balanced in relation to each other so that at about 16% chromium the molybdenum is about 8.5-10%.
- the minimum weight percent of molybdenum preferred is proportionately reduced to 7.0% but the maximum remains at about 10%.
- the preferred weight percent molybdenum is about 7-10% but not greater than about [31 - (% Cr)].
- a chromium content of about 18.0% it is preferred to use a molybdenum content of about 8.5 to 9.7%.
- the preferred minimum weight percent molybdenum is proportionately reduced from 8.5% to 8.0% and the preferred maximum weight percent is proportionately reduced to 9.4%.
- the weight percent chromium is increased from 20.5% to a preferred maximum of about 22.0% the minimum weight percent molybdenum is proportionately reduced from 8.0 to 7.7% and the maximum weight percent molybdenum is preferably reduced so that with a chromium content of about 22.0%, the maximum molybdenum is about 8.2%.
- a minimum of about 0.8% to 0.9% titanium is required to attain the outstanding crevice corrosion resistance at 55° C.
- a minimum of about 1.1% Ti and of about 2.75% Nb is preferred.
- Room temperature sulfide stress cracking test specimens were prepared from strip which, after heat treatment had been heated at 550 F (287.8 C) for 30 days and air cooled to simulate deep well aging (well aged).
- Longitudinal U-bend test specimens 3-7/8 ⁇ 3/8 ⁇ 1/8 in (9.8 ⁇ 1 ⁇ .3 cm) from well aged strip were machined to a 120 grit surface finish and bent in accordance with ASTM G-30 (Fig. 5) to a 1 in (2.54 cm) inside diameter.
- a steel bolt was attached to each leg of each U-bend specimen using nuts and washers at each end.
- transverse specimens were also prepared and processed as described in connection with the U-bend test specimens except that the transverse specimens were about 1-3/8 in (3.5 cm) long and while exposed to the test solution each specimen was anchored at its opposite ends in engagement with iron sleeves and bent to a predetermined deflection by a force applied midway between its ends. After cleaning the specimens were exposed to the solution specified in NACE Test Method TM-01-77 (approved July 1, 1977). Each specimen was examined at 20 ⁇ magnification for cracks after intervals of about 240, 504, 648, and 1000 hours. The time after which cracking was detected or "NC" for no cracks is indicated in Table VI and VIA under "NACE".
- the U-bend data is grouped as longitudinal specimens under "Long.” and the transverse specimens under “Trans.” in Tables VI and VIA.
- “longitudinal” and “transverse” serve to identify the axis of the specimen in relation to the direction in which the parent material, from which the specimen was prepared, was worked.
- the NACE TM-01-77 test data in Tables VI and VIA show that the present composition is resistant to sulfide stress-cracking at room temperature. For best results, the highest levels of molybdenum, niobium and titanium should be avoided. In this regard, 24% chromium is used with 7% molybdenum. As the amount of chromium is decreased from 23%, the maximum amount of molybdenum can be increased from 8%, with the ratio of the reduction in the chromium weight percent to the increase in the tolerable molybdenum weight percent being equal to about 2.
- a decrease in chromium content from about 22% to 20% results in an increase from about 8.5% to about 9.5% in the maximum amount of molybdenum that is preferably used when optimum resistance to sulfide stress-cracking is desired. Also indicated is a reduction to about 16% chromium when the molybdenum content is at about 11.5%.
- the amount of niobium and titanium should be carefully controlled. With about 4.5% niobium present, titanium should not be greater than about 0.50%. As the weight percent niobium is reduced from 4.5% to about 3.0%, the maximum amount of titanium present can be proportionately increased to about 2.0%.
- the maximum weight percent of niobium is 4.25% with which no more than about 0.50% titanium is used.
- the maximum weight percent titanium is proportionately increased from about 0.50% to about 1.75%.
- the ratio of an increase in the weight percent of titanium to the accompanying decrease in niobium is 1.0 in both these instances.
- the present alloy and age hardened products made therefrom have good resistance to chloride stress-cracking as demonstrated by exposure to the severe environment of boiling 45% MgCl2.
- nickel below about 60%
- the lower chromium and molybdenum contents provide better results.
- nickel should be present.
- the minimum nickel to be present is correspondingly increased or decreased above or below 60% with the amount of the change in nickel content being three times the change in hardener content.
- the nickel content should be correspondingly increased or decreased by 1.5 a/o.
- copper also contributes to stress-cracking resistance in boiling MgCl2 and for this purpose it is desirable to include up to about 3% copper to compensate for lower nickel than about 60% or when the hardener content is greater than 4.0 a/o. Up to about 2.0% copper is effectively used in compositions containing 60% nickel and above.
- the specimens were ground to 120 grit finish, bent to 1 in (2.54 cm) inside diameter and were stressed.
- Tables VII-IX the number of hours of exposure following which the specimen showed a stress crack or NC for no crack is given.
- the examples of the present invention and of the heats in Tables VII-IX were exposed to saturated (25%) sodium chloride, 0.5 g/l elemental sulfur and 1300-1440 psig partial pressure of hydrogen sulfide test medium under three different conditions. As indicated in Table VII, the examples and heats there listed were tested for 648h at 400 F (204.4 C) made up of two 160h periods and one period of 328h and if no cracks were observed the test was continued for 328h at 450 F.
- the autoclave test data demonstrate the outstanding resistance to corrosion and stress cracking under extremely severe conditions. Analysis of the data shows that in this composition molybdenum in weight percent is about four times as effective as chromium in improving resistance to stress cracking as measured in the autoclave test in the 400-450 F temperature range. For best resistance to cracking in the 400-450 F range, the percent chromium plus four times the percent molybdenum should not be less than about 47%, that is, % Cr + 4(%Mo) ⁇ 47% Eq.
- the percent chromium plus four times the percent molybdenum should not be less than about 49.5%, that is, % Cr + 4(%Mo) ⁇ 49.5% Eq. 4
- the percent chromium plus the percent molybdenum should not be less than 30%, that is, % Cr + % Mo ⁇ 30% Eq. 5
- the hardener content is preferably no greater than about 4.5 a/o. For exposures at temperatures below 500 F a hardener content up to about 5 a/o gives good resistance to stress-cracking.
- aluminum is preferably no more than 0.35% (no more than 0.77 a/o) to maximize strength. Copper also contributes to improved resistance to stress cracking in the autoclave test and for this purpose up to 3% can be used. As hardener content is increased above 4.0 a/o, copper preferably up to 2.0% is used effectively in improving resistance to stress cracking in the autoclave test.
- Example 53 was prepared using a double melting practice as a heat weighing about 10,000 pounds (4,545.5 kg) and forged to 4 in (10.16 cm) round bar which was heat treated.
- the composition of Example 53 is set forth in Table X.
- the composition of Heat A, representative of commercial Type 625 alloy (also about a 10,000 lb heat) is also given in Table X. Each contained less than 0.01% phosphorus and less than 0.01% sulfur. Though not indicated, Heat A also contained about 0.004% boron.
- the alloy of the present invention by its unusual combination of strength and corrosion resistance properties is well suited for a wide variety of uses in the chemical, petroleum and nuclear industries.
- the alloy lends itself to the production of a large variety of sizes and shapes.
- Intermediate products in any desired form such as billets, bars, strip and sheet as well as powder metallurgy products can be provided from which an even wider range of finished products can be made.
- the compositions set forth herein are advantageously used to provide parts for use in the exploration for, and exploitation of, petroleum products such as those intended for exposure under stress and/or under elevated temperatures.
- such parts include subsurface safety valves, hangers, valve and packer components, and other parts used above or below ground.
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Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
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AT87107651T ATE67795T1 (de) | 1986-05-27 | 1987-05-26 | Korrosionsbestaendige aushaertbare legierung auf nickelbasis. |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
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US86780386A | 1986-05-27 | 1986-05-27 | |
US867803 | 1986-05-27 | ||
US869138 | 1986-05-30 | ||
US06/869,138 US5556594A (en) | 1986-05-30 | 1986-05-30 | Corrosion resistant age hardenable nickel-base alloy |
Publications (2)
Publication Number | Publication Date |
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EP0247577A1 true EP0247577A1 (fr) | 1987-12-02 |
EP0247577B1 EP0247577B1 (fr) | 1991-09-25 |
Family
ID=27128018
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Application Number | Title | Priority Date | Filing Date |
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EP87107651A Expired - Lifetime EP0247577B1 (fr) | 1986-05-27 | 1987-05-26 | Alliage à base de nickel durcissable par vieillissement et résistant à la corrosion |
Country Status (7)
Country | Link |
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EP (1) | EP0247577B1 (fr) |
JP (1) | JP2729480B2 (fr) |
KR (1) | KR870011268A (fr) |
CA (1) | CA1336945C (fr) |
DE (1) | DE3773261D1 (fr) |
IL (1) | IL82587A0 (fr) |
NO (1) | NO872215L (fr) |
Cited By (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0262673A2 (fr) * | 1986-10-01 | 1988-04-06 | Inco Alloys International, Inc. | Alliage à base de nickel, résistant à la corrosion et possédant des caractéristiques mécaniques élevées |
EP0424277A1 (fr) * | 1989-10-20 | 1991-04-24 | Tecphy | Procédé d'amélioration de la résistance à la corrosion d'un alliage à base de nickel et alliage ainsi réalisé |
FR2786419A1 (fr) * | 1998-12-01 | 2000-06-02 | Imphy Sa | Electrode de soudage en alliage base nickel et alliage correspondant |
EP1078190A1 (fr) * | 1998-05-01 | 2001-02-28 | Grant Prideco, Inc | Tige de forage a parois epaisses |
EP1852517A3 (fr) * | 2002-05-15 | 2008-02-27 | Kabushiki Kaisha Toshiba | Lame de coupe composée d'un alliage Ni-Cr-Al |
EP2222884A1 (fr) * | 2007-11-19 | 2010-09-01 | Huntington Alloys Corporation | Alliage de résistance ultra élevée pour des environnements difficiles de pétrole et de gaz et procédé de préparation |
US8313593B2 (en) | 2009-09-15 | 2012-11-20 | General Electric Company | Method of heat treating a Ni-based superalloy article and article made thereby |
EP2730670A1 (fr) * | 2012-11-07 | 2014-05-14 | Hitachi Ltd. | Alliage de moulage à base de Ni et pièce de coulée de turbine à vapeur l'utilisant |
CN104674144A (zh) * | 2015-02-28 | 2015-06-03 | 钢铁研究总院 | 核电堆用大尺寸高强细晶镍基高温合金锻件热处理方法 |
EP3431222A1 (fr) * | 2014-04-04 | 2019-01-23 | Special Metals Corporation | Soudure et procédé de fabrication d'une soudure |
CN111094603A (zh) * | 2017-08-01 | 2020-05-01 | 切佩茨基机械厂股份公司 | 耐腐蚀合金 |
WO2022053353A1 (fr) * | 2020-09-09 | 2022-03-17 | Nv Bekaert Sa | Matériau d'alliage à base de ni |
CN115961178A (zh) * | 2022-11-15 | 2023-04-14 | 重庆材料研究院有限公司 | 一种超高强韧镍基耐蚀合金 |
WO2023129703A1 (fr) * | 2021-12-30 | 2023-07-06 | Huntington Alloys Corporation | Alliages durcissables par précipitation à base de nickel présentant une résistance améliorée à la fragilisation par l'hydrogène |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
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JPS63137133A (ja) * | 1986-11-28 | 1988-06-09 | Sumitomo Metal Ind Ltd | 高耐食性析出硬化型Ni基合金 |
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FR2154871A5 (fr) * | 1971-09-28 | 1973-05-18 | Creusot Loire | |
FR2277901A2 (fr) * | 1974-07-12 | 1976-02-06 | Creusot Loire | Perfectionnements aux alliages a base de nickel-fer-chrome, a durcissement structural obtenu par un traitement thermique approprie |
EP0056480A2 (fr) * | 1980-12-24 | 1982-07-28 | Hitachi, Ltd. | Application d'un alliage à base de nickel, possédant une résistance élevée à la corrosion fissurante sous tension |
EP0066361A2 (fr) * | 1981-04-17 | 1982-12-08 | Inco Alloys International, Inc. | Alliage à base de nickel, résistant à la corrosion et possédant des caractéristiques mécaniques élevées |
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ZA832119B (en) * | 1982-04-05 | 1984-04-25 | Teledyne Ind | Corrosion resistant nickel base alloy |
JPS602653A (ja) * | 1983-06-20 | 1985-01-08 | Sumitomo Metal Ind Ltd | 析出強化型ニツケル基合金の製造法 |
-
1987
- 1987-05-19 IL IL82587A patent/IL82587A0/xx unknown
- 1987-05-26 DE DE8787107651T patent/DE3773261D1/de not_active Expired - Lifetime
- 1987-05-26 NO NO872215A patent/NO872215L/no unknown
- 1987-05-26 CA CA000538031A patent/CA1336945C/fr not_active Expired - Lifetime
- 1987-05-26 EP EP87107651A patent/EP0247577B1/fr not_active Expired - Lifetime
- 1987-05-27 KR KR870005353A patent/KR870011268A/ko not_active Application Discontinuation
- 1987-05-27 JP JP62131042A patent/JP2729480B2/ja not_active Expired - Fee Related
Patent Citations (4)
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FR2154871A5 (fr) * | 1971-09-28 | 1973-05-18 | Creusot Loire | |
FR2277901A2 (fr) * | 1974-07-12 | 1976-02-06 | Creusot Loire | Perfectionnements aux alliages a base de nickel-fer-chrome, a durcissement structural obtenu par un traitement thermique approprie |
EP0056480A2 (fr) * | 1980-12-24 | 1982-07-28 | Hitachi, Ltd. | Application d'un alliage à base de nickel, possédant une résistance élevée à la corrosion fissurante sous tension |
EP0066361A2 (fr) * | 1981-04-17 | 1982-12-08 | Inco Alloys International, Inc. | Alliage à base de nickel, résistant à la corrosion et possédant des caractéristiques mécaniques élevées |
Cited By (26)
Publication number | Priority date | Publication date | Assignee | Title |
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EP0262673A2 (fr) * | 1986-10-01 | 1988-04-06 | Inco Alloys International, Inc. | Alliage à base de nickel, résistant à la corrosion et possédant des caractéristiques mécaniques élevées |
EP0262673B1 (fr) * | 1986-10-01 | 1995-04-26 | Inco Alloys International, Inc. | Alliage à base de nickel, résistant à la corrosion et possédant des caractéristiques mécaniques élevées |
EP0424277A1 (fr) * | 1989-10-20 | 1991-04-24 | Tecphy | Procédé d'amélioration de la résistance à la corrosion d'un alliage à base de nickel et alliage ainsi réalisé |
FR2653451A1 (fr) * | 1989-10-20 | 1991-04-26 | Tecphy | Procede d'amelioration de la resistance a la corrosion d'un alliage a base de nickel et alliage ainsi realise. |
EP1078190A1 (fr) * | 1998-05-01 | 2001-02-28 | Grant Prideco, Inc | Tige de forage a parois epaisses |
EP1078190A4 (fr) * | 1998-05-01 | 2003-04-09 | Grant Prideco Inc | Tige de forage a parois epaisses |
FR2786419A1 (fr) * | 1998-12-01 | 2000-06-02 | Imphy Sa | Electrode de soudage en alliage base nickel et alliage correspondant |
EP1005946A1 (fr) * | 1998-12-01 | 2000-06-07 | Ugine-Savoie Imphy | Electrode de soudage en alliage base nickel et alliage correspondant |
US6447716B1 (en) | 1998-12-01 | 2002-09-10 | Ugine-Savoie Imphy | Welding electrode made of a nickel-based alloy and the corresponding alloy |
EP1852517A3 (fr) * | 2002-05-15 | 2008-02-27 | Kabushiki Kaisha Toshiba | Lame de coupe composée d'un alliage Ni-Cr-Al |
US7682474B2 (en) | 2002-05-15 | 2010-03-23 | Kabushiki Kaisha Toshiba | Cutter composed of Ni-Cr-Al Alloy |
US7740719B2 (en) | 2002-05-15 | 2010-06-22 | Kabushiki Kaisha Toshiba | Cutter composed of Ni-Cr alloy |
EP2222884A1 (fr) * | 2007-11-19 | 2010-09-01 | Huntington Alloys Corporation | Alliage de résistance ultra élevée pour des environnements difficiles de pétrole et de gaz et procédé de préparation |
EP2845916A3 (fr) * | 2007-11-19 | 2015-05-06 | Huntington Alloys Corporation | Alliage de résistance ultra élevée pour des environnements difficiles de pétrole et de gaz et procédé de préparation |
EP2222884A4 (fr) * | 2007-11-19 | 2012-02-22 | Huntington Alloys Corp | Alliage de résistance ultra élevée pour des environnements difficiles de pétrole et de gaz et procédé de préparation |
US8313593B2 (en) | 2009-09-15 | 2012-11-20 | General Electric Company | Method of heat treating a Ni-based superalloy article and article made thereby |
US9464343B2 (en) | 2012-11-07 | 2016-10-11 | Mitsubishi Hitachi Power Systems, Ltd. | Ni-based casting alloy and steam turbine casting part using the same |
EP2730670A1 (fr) * | 2012-11-07 | 2014-05-14 | Hitachi Ltd. | Alliage de moulage à base de Ni et pièce de coulée de turbine à vapeur l'utilisant |
EP3431222A1 (fr) * | 2014-04-04 | 2019-01-23 | Special Metals Corporation | Soudure et procédé de fabrication d'une soudure |
CN104674144A (zh) * | 2015-02-28 | 2015-06-03 | 钢铁研究总院 | 核电堆用大尺寸高强细晶镍基高温合金锻件热处理方法 |
CN111094603A (zh) * | 2017-08-01 | 2020-05-01 | 切佩茨基机械厂股份公司 | 耐腐蚀合金 |
EP3663422A4 (fr) * | 2017-08-01 | 2021-01-20 | Stock Company "Chepetsky Mechanical Plant"(SC CMP) | Alliage résistant à la corrosion |
CN111094603B (zh) * | 2017-08-01 | 2021-12-07 | 切佩茨基机械厂股份公司 | 耐腐蚀合金 |
WO2022053353A1 (fr) * | 2020-09-09 | 2022-03-17 | Nv Bekaert Sa | Matériau d'alliage à base de ni |
WO2023129703A1 (fr) * | 2021-12-30 | 2023-07-06 | Huntington Alloys Corporation | Alliages durcissables par précipitation à base de nickel présentant une résistance améliorée à la fragilisation par l'hydrogène |
CN115961178A (zh) * | 2022-11-15 | 2023-04-14 | 重庆材料研究院有限公司 | 一种超高强韧镍基耐蚀合金 |
Also Published As
Publication number | Publication date |
---|---|
NO872215D0 (no) | 1987-05-26 |
DE3773261D1 (de) | 1991-10-31 |
NO872215L (no) | 1987-11-30 |
EP0247577B1 (fr) | 1991-09-25 |
CA1336945C (fr) | 1995-09-12 |
IL82587A0 (en) | 1987-11-30 |
KR870011268A (ko) | 1987-12-22 |
JP2729480B2 (ja) | 1998-03-18 |
JPS63145740A (ja) | 1988-06-17 |
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