US3502463A - Nickel base alloys and process for their manufacture - Google Patents
Nickel base alloys and process for their manufacture Download PDFInfo
- Publication number
- US3502463A US3502463A US518145A US3502463DA US3502463A US 3502463 A US3502463 A US 3502463A US 518145 A US518145 A US 518145A US 3502463D A US3502463D A US 3502463DA US 3502463 A US3502463 A US 3502463A
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- US
- United States
- Prior art keywords
- alloys
- nickel base
- alloy
- base alloys
- nickel
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- 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
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10S75/00—Specialized metallurgical processes, compositions for use therein, consolidated metal powder compositions, and loose metal particulate mixtures
- Y10S75/95—Consolidated metal powder compositions of >95% theoretical density, e.g. wrought
Definitions
- Nickel base alloys having a relatively large quantity of carbide phase exhibit improved metallurgical and physical properties.
- Novel alloys disclosed have a composition by weight consisting essentially of from 10 to 20 percent tungsten, from 8 to 12 percent cobalt, from 8 to 20 per cent chromium, from 2 to 4 percent titanium, from 1.5 to 3 percent aluminum, from 1 to 3 percent carbon, balance nickel with incidental impurities.
- nickel base alloys and especially highly alloyed nickel base alloys normally contain about 0.1% carbon and accordingly have a relatively small quantity of carbide phase.
- carbon content along with an increase in the amount of carbide forming materials, I have been able to provide high strength nickel base alloys which need not be aged to bring out their excellent strength features. Even without aging and by mere cold working following powder consolidation the present alloys illustrate excellent strength features. Part of this stems from the considerable increase in carbide volume contained therein.
- both the metallurgical and physical properties of the present nickel base alloys with the concurrent increase in the carbide content thereof may be readily achieved by practicing the atomization and metal powder consolidation process which is hereinafter described.
- the carbide phase is of a grain size ranging from 0.5 to 3 microns. It should be understood that in some cases a very small amount of such carbides may be slightly larger than 3 microns and so long as the number of these slightly larger carbides is quite small, e.g., less than of total carbide, the detrimental effect is minimal.
- the advantages of the present alloys and their excellent strength retention at elevated temperatures lies in the presence of a large volume of thermally stable carbide phase and especially as shown in the attached photomicrographs of a fine carbide phase uniformly distributed throughout the major alloy matrix.
- the presently available nickel base alloys containing the low amount of carbon referred to above rely upon solid solution strengthening by such elements as chromium, tungsten, molybdenum and cobalt together with additional strengthening produced by precipitates of compounds resulting from the minor additions of titanium and aluminum.
- the latter compounds are finely dispersed and are relatively stable up to about 1800 or 1900 F. but at above these temperatures the nickeltitaniurn-aluminum compounds dissolve and lose their effectiveness as dispersion strengtheners.
- the carbides remain stable at temperatures approaching 2200 F. and since the alloys of my invention contain large quantities of carbon and as a result of the interactions with the carbide forming elements therein large volumes of carbide phase result.
- the hard carbide constituent maintains its efiiciency as a strengthener at temperatures which cause a significant loss of strength in the present commercial products. Strengthening by the carbide phase apparently is due to not only its ultra fine size and uniform distribution but the fact that these factors restrict grain growth of the nickel alloy matrix and provide barriers to the movement of slip planes within the grains.
- a primary object of my invention is to provide a new group of nickel base structural alloys of relatively high carbide content which are characterized by a uniformly dispersde carbide phase of ultra fine particle size, i.e., predominantly less than 3 microns.
- a more specific object of my invention is to provide a new group of nickel base alloys characterized as aforesaid which consist of 10 lo 20% tungsten, 8 to 12% cobalt, 8 to 20% chromium, 2 to 4% titanium, 1.5 to 3% aluminum, 1 to 3% carbon, with incidental impurities.
- Another object of my invention is to provide a new group of wrought nickel base alloys for structural use.
- a further object of my invention is to provide a method of preparing such nickel base alloys which includes the steps of atomizing, rapidly quenching and consolidating such nickel base materials.
- FIGURE 1 schematically illustrates an atomizing chamber for use in the practice of the present invention
- FIGURE 2 schematically illustrates atomizing apparatus for use herewith
- FIGURE 3 is a photomicrograph at a magnification of 2000 of a consolidated alloy made as herein taught.
- the atomizing chamber which is illustrated is fabricated of a steel shell, water-cooled and is approximately 3 feet in diameter and approximately 2 feet in height. Obviously other dimensions may be employed without departing from the spirit or scope of my invention.
- the bottom of the chamber is slightly conical and in the center thereof I provide a capped opening 25 for metal powder and water removal.
- I also provide an exhaust port 28 for argon exit.
- the alloy powders were withdrawn from the atomizing chamber and dried. Approximately 75 to 85% of the resulting atomized powders were finer than 80 mesh and from 15 to 30% were finer than 325 mesh.
- the atomized alloy powders were next consolidated into solid stock.
- the powders were first canned in Inconel cylinders that were lined with molybdenum foil to permit easy stripping of the canning material from the hot worked ingot. After the bottom. of the cylinder was welded on the alloy powders were poured into the Inconel cans and pressed at pressures ranging from 5 to 30 tons per square inch. I found that the higher pressures did not produce significant increases in powder density for most alloys apparently because of the spheroidal shape and the extreme hardness of the powder particles. Accordingly a major portion of the compositions were pressed at from 5 to 15 t.s.i.
- the welded cans were heated to forging temperatures in air and soaked approximately for 10 minutes prior to upset hammer forging on a 250 pound capacity forge unit. Forging was used to produce pancake ingots approximately A2 inch thick. After forging the canned billets where hot rolled to approximately 0.22 to 0.24 inch using a 10% reduction per pass, this representing a total reduction in thickness of to 92% of the original billet thickness. The canning material was then removed and the rolled plates stock sectioned for metallurgical examination and physical property evaluations.
- Table II presents some room temperature transverse rupture data of the alloy compositions listed in Table I:
- An alloy consisting essentially of from 10 to 20% tungsten; from 8 to 12% cobalt; from 8 to 20% chromium; from 2 to 4% titanium; from 1.5 to 3% aluminum; from 1 to 3% carbon, balance nickel with incidental impurities.
- the alloy as defined in claim 1 characterized by a substantially uniformly dispersed carbide phase in the major phase matrix and by a carbide phase grain size of predominantly less than 3 microns.
Description
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US51814566A | 1966-01-03 | 1966-01-03 |
Publications (1)
Publication Number | Publication Date |
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US3502463A true US3502463A (en) | 1970-03-24 |
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Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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US518145A Expired - Lifetime US3502463A (en) | 1966-01-03 | 1966-01-03 | Nickel base alloys and process for their manufacture |
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Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3655458A (en) * | 1970-07-10 | 1972-04-11 | Federal Mogul Corp | Process for making nickel-based superalloys |
US3916497A (en) * | 1973-02-16 | 1975-11-04 | Mitsubishi Metal Corp | Heat resistant and wear resistant alloy |
US3917463A (en) * | 1973-02-16 | 1975-11-04 | Mitsubishi Metal Corp | Nickel-base heat resistant and wear resistant alloy |
US4240824A (en) * | 1979-10-04 | 1980-12-23 | Scm Corporation | Process of making nickel or cobalt powder with precipitates |
US20040256603A1 (en) * | 2001-10-18 | 2004-12-23 | Cesur Celik | Powder for laminated ceramic capacitor internal electrode |
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 US518145A patent/US3502463A/en not_active Expired - Lifetime
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 (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3655458A (en) * | 1970-07-10 | 1972-04-11 | Federal Mogul Corp | Process for making nickel-based superalloys |
US3916497A (en) * | 1973-02-16 | 1975-11-04 | Mitsubishi Metal Corp | Heat resistant and wear resistant alloy |
US3917463A (en) * | 1973-02-16 | 1975-11-04 | Mitsubishi Metal Corp | Nickel-base heat resistant and wear resistant alloy |
US4240824A (en) * | 1979-10-04 | 1980-12-23 | Scm Corporation | Process of making nickel or cobalt powder with precipitates |
US20040256603A1 (en) * | 2001-10-18 | 2004-12-23 | Cesur Celik | Powder for laminated ceramic capacitor internal electrode |
US7277268B2 (en) * | 2001-10-18 | 2007-10-02 | Candian Electronic Powers Corporation | Laminated ceramic capacitor |
US7857886B2 (en) | 2001-10-18 | 2010-12-28 | Canadian Electronic Powders Corporation | Powder for laminated ceramic capacitor internal electrode |
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