US3524744A - Nickel base alloys and process for their manufacture - Google Patents
Nickel base alloys and process for their manufacture Download PDFInfo
- Publication number
- US3524744A US3524744A US518165A US3524744DA US3524744A US 3524744 A US3524744 A US 3524744A US 518165 A US518165 A US 518165A US 3524744D A US3524744D A US 3524744DA US 3524744 A US3524744 A US 3524744A
- Authority
- US
- United States
- Prior art keywords
- alloy
- nickel base
- alloys
- base alloys
- parikh
- 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.)
- Expired - Lifetime
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0433—Nickel- or cobalt-based alloys
-
- 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
- ABSTRACT OF THE DISCLOSURE Superalloys characterized by a uniformly dispersed ultrafine hardening phase and a very fine matrix phase having a composition by Weight consisting essentially of from 3.5 to 6 percent molybdenum, from 3.5 to 6.5 percent aluminum, from 12 to 17 percent chromium, iron up to 4 percent maximum, from 0.5 to 4 percent titanium, from 0 to 20 percent cobalt, carbon up to 0.20 percent maximum, boron up to 0.05 percent maximum, from 0 to 0.15 percent zirconium, manganese up to 0.25 percent maximum, silicon up to 0.50 percent maximum, 0 to 0.5 percent copper, balance nickel with incidental impurities.
- the present invention relates to a novel group of nickel base superalloys which are characterized by a new and unique microstructure and to a process whereby such nickel base alloys may be made. More especially my invention is based upon my discovery that by the practice of a molten metal atomizing process to yield the alloy powders followed by the consolidation thereof as herein taught there results very desirable structural alloys featuring the new microstructure.
- This alloy is commonly referred to as Inco 713C.
- Another of these nickel base superalloys commercially available has the following composition:
- This alloy is commonly referred to as Udimet 700.
- the as-cast nickel base alloys which correspond compositionally to the materials that I treat are characterized by either a very large acicular grain or relatively coarse dendritic structures. These acicular grains or dendritic structures, as the case may be, seriously detract from the physical and metallurgical properties of the materials but until the advent of my invention such materials could only be readily fabricated in their as-cast state and this resulted in these undesirable microstructures. Such acicular grains or dendritic structures also render these alloys brittle and extremely difficult to fabricate into useful shapes.
- the present nickel base alloys are characterized by a substantially uniformly dispersed hardening phase which hardening phase is of very, 'very small size and it is this combination of dispersion and size which leads to the desirable properties of the nickel base alloys herein described and claimed.
- a primary object of my invention is to provide nickel base alloys quite low in carbon content, which are characterized by a uniformly dispersed, ultra fine hardening phase and uniform, fine matrix grain size with resulting property improvement over known similar materials.
- the matrix grain size refers to the metallurgical grain structure.
- a more specific object of my invention is to provide an alloy consisting essentially of from 3 /2 to 6% molybdenum; from 3 /2 to 6.5% aluminum, from 12 to 17% chrominum, iron 4% maximum, from 0.5 to 4% titanium, from O to 20% cobalt, carbon up to 0.20% maximum, boron up to 0.05 maximum, from 0 to 0.15% zirconium, maganese 0.25% maximum, 0 to 0.5% copper, silicon 0.50% maximum, 1.8 to 2.8% columbium and tantalum, balance nickel with incidental impurities, which alloy is characterized by a substantially uniformly dispersed hardening phase of a size predominantly less than a few microns and a matrix grain size that is essentially less than about 50 microns.
- Another important object of my invention is to provide a process of making these nickel base alloys characterized by the unique microstructure aforesaid which includes the steps of atomizing a molten alloy charge to form powders thereof and consolidating said powders into structural alloy stock.
- FIG. 1 schematically illustrates an atomizing chamber for use in the practice of the present invention
- FIG. 2 schematically illustrates atomizing apparatus for use herewith
- FIG. 3 is a photomicrograph of a commercially available, as-cast nickel base superalloy, Inco 713C, at a magnification of 150x;
- FIG. 4 is a photomicrograph of an alloy of the same composition as shown in FIG. 3 made by the process herein taught at a magnification of 320x;
- FIG. 5 is a photomicrograph of another nickel base alloy, Udimet 700, in its commercial as-cast condition at a magnification of 150x;
- FIG. 6 is a photomicrograph at a magnification of 500X of an alloy of the same chemical composition as that shown in FIG. 5 but made according to the teachings of this invention.
- FIG. 7 is a photomicrograph at a magnification of 200x of an alloy of the same chemical composition as that shown in FIG. 5 but made according to the teachings of this invention.
- the molten metal charge is then poured into a preheated (to prevent chilling) magnesia-lined pouring cup 26 placed at the top of the atomizing chamber 22.
- the melt passes first through a hole 21 at the bottom of the pouring cup through a refractory-lined nozzle 27.
- the molten charge enters the atomizing chamber 22.
- the molten stream is first broken up into fine particles and then quickly quenched by a high pressure inert gas stream entering the chamber 22 through the gas inlet port 23.
- a water reservoir 24 is provided at the bottom of the chamber which may operate in conjunction with the atomizing stream to rapidly quench the particles.
- a capped opening 25 is provided at the bottom of the chamber for metal powder removal.
- a gas exit port 28 is also provided. After the alloy powders are formed they are removed from the atomizing chamber, separated from the water and dried. Drying may be most simply accomplished by limited heating to drive off the water.
- the alloy powders were then canned in mild steel encapsulating material. Air was evacuated from the cans and they were then sealed. Such cans were then hotpressed to consolidate the atomized powders. In carrying out such hot-pressing it should be noted that great care should be taken to avoid melting the particles and at the same time contamination of the resulting sintered billets should also be avoided.
- the stainless steel alloys of my invention were sintered readily under an argon atmosphere to avoid the loss of volatile chromium among other things. Suitable sintering temperatures are between the range of 2550 to 2690 F.
- the alloy powders were sealed in 0.040 inch thick stainless steel cans, heated at 2190 F. and then hammer forged without side restraint. The height reduction was about 60%. Although the edges of the forged pieces were somewhat porous and cracked, I found that a slightly below such surfaces the forged pieces were dense.
- the most preferable mode of consolidating powders is by extrusion. Green compacts of the atomized powders, 1 /2 inch high by 1 inch diameter were sealed in close fitting mild steel cans under vacuum. These were then heated to 2200" F. in a resistance furnace, then dropped quickly into an extrusion die and rapidly loaded to 40 tons per square inch. Such load was maintained for 15 seconds, then the in plate was removed and the compact was pushed out of the die. 100% dense structures were thus obtained.
- FIG. 3 The advantages of my invention may most readily be seen by comparing FIG. 3 with FIG. 4 and FIGS. 6 and 7 with FIG. 5.
- the commercial materials are illustrated in FIGS. 3 and 5 and the fine-grained structure of the present alloys is readily shown in FIGS. 4, 6 and 7.
- both the oxygencontent and the nitrogen content should be maintained as low as possible, preferably below 1000 parts per million oxygen and below 100 parts per million nitrogen.
- the alloys made according to the present invention consist of very fine matrix phase and very fine hardening phase. Such alloys are characterized by high ductility and accordingly one may readily fabricate them into useful shapes. Such fabricating step is of the utmost importance from the economic as well as a property standpoint. As a result of the fine-grained size the alloys are not only readily fabricable but have considerably better tensile strengths as opposed to the coarse cast structures of the prior art. Alloys made as taught herein are characterized by tensile strengths of around 200,000 p.s.i. as compared with values of around 120,000 p.s.i. for the commercially available materials.
- An alloy consisting essentially of from 3.5 to 6% molybdenum; from 3.5 to 6.5% aluminum; from 12 to 17% chrominum; iron 4% maximum; from 0.5 to 4% titanium; from 0 to 20% cobalt; carbon up to 0.20% maximum; boron up to 0.05% maximum; from O to 0.15% zirconium; manganese 0.25% maximum; silicon 0.50% maximum; 0 to 0.5% copper, balance nickel, said alloy being characterized by a substantially uniformly dispersed hardening phase in the major phase matrix, said hardening phase being essentially of a size less than a few microns and the said matrix phase being essentially less than about 50 microns.
Description
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US51816566A | 1966-01-03 | 1966-01-03 |
Publications (1)
Publication Number | Publication Date |
---|---|
US3524744A true US3524744A (en) | 1970-08-18 |
Family
ID=24062843
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US518165A Expired - Lifetime US3524744A (en) | 1966-01-03 | 1966-01-03 | Nickel base alloys and process for their manufacture |
Country Status (7)
Country | Link |
---|---|
US (1) | US3524744A (en) |
JP (1) | JPS5620345B1 (en) |
AT (1) | AT291610B (en) |
DE (1) | DE1558507A1 (en) |
FR (1) | FR1507140A (en) |
GB (1) | GB1166686A (en) |
SE (1) | SE393402B (en) |
Cited By (17)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3639116A (en) * | 1970-01-06 | 1972-02-01 | Cabot Corp | Lanthanum-containing powders for making oxidation-resistant metallics, method of making same, and metallic products made therefrom |
US3639179A (en) * | 1970-02-02 | 1972-02-01 | Federal Mogul Corp | Method of making large grain-sized superalloys |
US3648343A (en) * | 1968-12-10 | 1972-03-14 | Federal Mogul Corp | Method of making a composite high-temperature valve |
US3649257A (en) * | 1970-02-18 | 1972-03-14 | Latrobe Steel Co | Fully dense consolidated-powder superalloys |
US3902862A (en) * | 1972-09-11 | 1975-09-02 | Crucible Inc | Nickel-base superalloy articles and method for producing the same |
US4066449A (en) * | 1974-09-26 | 1978-01-03 | Havel Charles J | Method for processing and densifying metal powder |
US4168967A (en) * | 1978-04-17 | 1979-09-25 | The International Nickel Company, Inc. | Nickel and cobalt irregularly shaped granulates |
US4240824A (en) * | 1979-10-04 | 1980-12-23 | Scm Corporation | Process of making nickel or cobalt powder with precipitates |
DE3234090A1 (en) * | 1981-09-14 | 1983-04-28 | United Technologies Corp., 06101 Hartford, Conn. | SINGLE CRYSTAL ITEM FROM A NICKEL-BASED SUPER ALLOY |
US4530727A (en) * | 1982-02-24 | 1985-07-23 | The United States Of America As Represented By The Department Of Energy | Method for fabricating wrought components for high-temperature gas-cooled reactors and product |
US4919718A (en) * | 1988-01-22 | 1990-04-24 | The Dow Chemical Company | Ductile Ni3 Al alloys as bonding agents for ceramic materials |
US5015290A (en) * | 1988-01-22 | 1991-05-14 | The Dow Chemical Company | Ductile Ni3 Al alloys as bonding agents for ceramic materials in cutting tools |
US5298052A (en) * | 1991-07-12 | 1994-03-29 | Daido Metal Company, Ltd. | High temperature bearing alloy and method of producing the same |
EP2913418A1 (en) * | 2014-02-28 | 2015-09-02 | Daido Steel Co.,Ltd. | Turbine wheel of automotive turbocharger and method for producing the same |
CN106435279A (en) * | 2016-10-24 | 2017-02-22 | 四川六合锻造股份有限公司 | Highstrength oxidationresistant hightemperature alloy and heat treatment technique and application thereof |
US10378087B2 (en) | 2015-12-09 | 2019-08-13 | General Electric Company | Nickel base super alloys and methods of making the same |
CN110643856A (en) * | 2018-06-26 | 2020-01-03 | 中南大学 | Nickel-based alloy, preparation method thereof and manufactured article |
Families Citing this family (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4631013A (en) * | 1984-02-29 | 1986-12-23 | General Electric Company | Apparatus for atomization of unstable melt streams |
IL74267A (en) * | 1984-02-29 | 1988-01-31 | Gen Electric | Method of atomization of melt from a closely coupled nozzle,apparatus and product formed |
FR2643085B1 (en) * | 1989-02-10 | 1991-05-10 | Onera (Off Nat Aerospatiale) | NICKEL-BASED SUPERALLOY FOR INDUSTRIAL TURBINE BLADES |
GB0024031D0 (en) | 2000-09-29 | 2000-11-15 | Rolls Royce Plc | A nickel base superalloy |
CN103894599B (en) * | 2014-03-14 | 2016-04-13 | 华南理工大学 | A kind of Ni based powder metallurgy repair materials and application thereof |
US10577679B1 (en) | 2018-12-04 | 2020-03-03 | General Electric Company | Gamma prime strengthened nickel superalloy for additive manufacturing |
Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3244506A (en) * | 1964-09-08 | 1966-04-05 | Allegheny Ludhum Steel Corp | Cutting tool material |
-
1966
- 1966-01-03 US US518165A patent/US3524744A/en not_active Expired - Lifetime
- 1966-12-28 SE SE6617819A patent/SE393402B/en unknown
- 1966-12-29 GB GB58083/66A patent/GB1166686A/en not_active Expired
- 1966-12-29 JP JP8573666A patent/JPS5620345B1/ja active Pending
-
1967
- 1967-01-02 DE DE19671558507 patent/DE1558507A1/en active Pending
- 1967-01-02 AT AT3667A patent/AT291610B/en not_active IP Right Cessation
- 1967-01-03 FR FR89778A patent/FR1507140A/en not_active Expired
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3244506A (en) * | 1964-09-08 | 1966-04-05 | Allegheny Ludhum Steel Corp | Cutting tool material |
Cited By (22)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3648343A (en) * | 1968-12-10 | 1972-03-14 | Federal Mogul Corp | Method of making a composite high-temperature valve |
US3639116A (en) * | 1970-01-06 | 1972-02-01 | Cabot Corp | Lanthanum-containing powders for making oxidation-resistant metallics, method of making same, and metallic products made therefrom |
US3639179A (en) * | 1970-02-02 | 1972-02-01 | Federal Mogul Corp | Method of making large grain-sized superalloys |
US3649257A (en) * | 1970-02-18 | 1972-03-14 | Latrobe Steel Co | Fully dense consolidated-powder superalloys |
US3902862A (en) * | 1972-09-11 | 1975-09-02 | Crucible Inc | Nickel-base superalloy articles and method for producing the same |
US4066449A (en) * | 1974-09-26 | 1978-01-03 | Havel Charles J | Method for processing and densifying metal powder |
US4168967A (en) * | 1978-04-17 | 1979-09-25 | The International Nickel Company, Inc. | Nickel and cobalt irregularly shaped granulates |
US4240824A (en) * | 1979-10-04 | 1980-12-23 | Scm Corporation | Process of making nickel or cobalt powder with precipitates |
DE3234090A1 (en) * | 1981-09-14 | 1983-04-28 | United Technologies Corp., 06101 Hartford, Conn. | SINGLE CRYSTAL ITEM FROM A NICKEL-BASED SUPER ALLOY |
US4530727A (en) * | 1982-02-24 | 1985-07-23 | The United States Of America As Represented By The Department Of Energy | Method for fabricating wrought components for high-temperature gas-cooled reactors and product |
US4919718A (en) * | 1988-01-22 | 1990-04-24 | The Dow Chemical Company | Ductile Ni3 Al alloys as bonding agents for ceramic materials |
US5015290A (en) * | 1988-01-22 | 1991-05-14 | The Dow Chemical Company | Ductile Ni3 Al alloys as bonding agents for ceramic materials in cutting tools |
US5298052A (en) * | 1991-07-12 | 1994-03-29 | Daido Metal Company, Ltd. | High temperature bearing alloy and method of producing the same |
EP2913418A1 (en) * | 2014-02-28 | 2015-09-02 | Daido Steel Co.,Ltd. | Turbine wheel of automotive turbocharger and method for producing the same |
US20150247221A1 (en) * | 2014-02-28 | 2015-09-03 | Daido Steel Co., Ltd. | Turbine wheel of automotive turbocharger and method for producing the same |
US9738954B2 (en) * | 2014-02-28 | 2017-08-22 | Daido Steel Co., Ltd. | Turbine wheel of automotive turbocharger and method for producing the same |
US10378087B2 (en) | 2015-12-09 | 2019-08-13 | General Electric Company | Nickel base super alloys and methods of making the same |
US10801088B2 (en) | 2015-12-09 | 2020-10-13 | General Electric Company | Nickel base super alloys and methods of making the same |
CN106435279A (en) * | 2016-10-24 | 2017-02-22 | 四川六合锻造股份有限公司 | Highstrength oxidationresistant hightemperature alloy and heat treatment technique and application thereof |
CN106435279B (en) * | 2016-10-24 | 2018-06-15 | 四川六合锻造股份有限公司 | A kind of high-strength, antioxidant high temperature alloy and its heat treatment process and application |
CN110643856A (en) * | 2018-06-26 | 2020-01-03 | 中南大学 | Nickel-based alloy, preparation method thereof and manufactured article |
CN110643856B (en) * | 2018-06-26 | 2021-11-30 | 中南大学 | Nickel-based alloy, preparation method thereof and manufactured article |
Also Published As
Publication number | Publication date |
---|---|
DE1558507A1 (en) | 1972-02-17 |
FR1507140A (en) | 1967-12-22 |
AT291610B (en) | 1971-07-26 |
GB1166686A (en) | 1969-10-08 |
SE393402B (en) | 1977-05-09 |
JPS5620345B1 (en) | 1981-05-13 |
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Legal Events
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Owner name: COLT INDUSTRIES OPERATING CORP. Free format text: MERGER AND CHANGE OF NAME;ASSIGNOR:CRUCIBLE CENTER COMPANY (INTO) CRUCIBLE INC. (CHANGED TO);REEL/FRAME:004120/0308 Effective date: 19821214 |
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Owner name: MELLON BANK, N.A. FOR THE CHASE MANHATTAN BANK (NA Free format text: SECURITY INTEREST;ASSIGNOR:CRUCIBLE MATERIALS CORPORATION, A CORP. OF DE.;REEL/FRAME:004490/0452 Effective date: 19851219 Owner name: CHASE MANHATTAN BANK, THE (NATIONAL ASSOCIATION) A Free format text: SECURITY INTEREST;ASSIGNOR:CRUCIBLE MATERIALS CORPORATION, A CORP. OF DE.;REEL/FRAME:004490/0452 Effective date: 19851219 Owner name: MELLON FINANCIAL SERVICES CORPORATION Free format text: SECURITY INTEREST;ASSIGNOR:CRUCIBLE MATERIALS CORPORATION, A CORP. OF DE.;REEL/FRAME:004490/0410 Effective date: 19851219 Owner name: MELLON BANK, N.A. AS AGENT FOR MELLON BANK N.A. & Free format text: SECURITY INTEREST;ASSIGNOR:CRUCIBLE MATERIALS CORPORATION, A CORP. OF DE.;REEL/FRAME:004490/0410 Effective date: 19851219 |