US3556780A - Process for producing carbide-containing alloy - Google Patents
Process for producing carbide-containing alloy Download PDFInfo
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- US3556780A US3556780A US518058A US3556780DA US3556780A US 3556780 A US3556780 A US 3556780A US 518058 A US518058 A US 518058A US 3556780D A US3556780D A US 3556780DA US 3556780 A US3556780 A US 3556780A
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Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
-
- 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
- C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
-
- 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
-
- 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
- Y10S75/956—Producing particles containing a dispersed phase
Definitions
- T-l steels The nominal composition of such T-l steels is normally given as iron-18%; tungsten-4%; chromium- 1%; vanadiumapproximately 0.8% carbon.
- a primary object of my invention is to provide a new and improved group of iron base tool steels which may have a relatively high carbide content and which are characterized by a uniformly dispersed carbide phase of ultra fine particle size, i.e., from 0.5 to 3 microns and where optionally but preferably there is an ultra-fine matrix grain size, i.e., substantially all of the matrix grains are on the order of 5 microns or less.
- Another object of my invention is to provide a new group of steels having special utility for tool purposes which are characterized by a relatively high concentration of carbide phase, in fact the carbide phase is of approximately twice the volume of conventional M-2 steels, which carbide phase is uniformly distributed throughout the ferrous matrix and is of ultra fine size.
- Another object of my invention is to provide a wrought tool steel of relatively high carbide volume.
- a further object of my invention is to provide a method of preparing tool steels which includes the steps of atomizing and consolidating powders of certain of said steels and whereby no serious oxidation occurs and substantially no deleterious oxides are formed.
- Still another object of my invention is to provide a method of making such steels whereby the carbide content thereof is readily and accurately controlled.
- a further primary object of my invention is to provide a new group of alloy steels characterized by a fine-grained,
- uniformly dispersed carbide phase consisting of from 2.5 to 16% chromium, from to 20% cobalt, from 0.8 to 12.2% vanadium, from 0 to 10% molybdenum, from 0 to 20% tungsten, from 0.6 to 4% carbon, balance substantially iron with the usual other impurities and minor additions in commercial steels and wherein the total of the molybdenum content plus one-half of the tungsten content is a value greater than 4 but less than 15 with the further requirement that there be adequate carbon present to permit the alloy to be hardened to a Rockwell C level of at least 60.
- a more specific object of my invention is to provide novel ferrous base alloys having a chemical composition of from 0 to 20% tungsten; from 2.5 to 16% chromium; from 0 to 10% molybdenum; from 2 to 12.2% vanadium; and from 0.6 to 4% carbon, along with incidental impurities which composition is characterized by a substantially uniformly dispersed carbide phase in the major phase (ferrous) matrix and having a carbide phase, substantially all of which has a grain size of less than 3 microns.
- Still another object of my invention is to provide a novel group of tool steels characterized by a unique microstructure which are fabricated by the consolidation of prealloyed powders.
- 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 at a magnification of 2000, unetched, of a consolidated alloy made as herein taught;
- FIG. 4 is a photomicrograph at 2000 magnification showing the structure of an atomized and consolidated alloy made as herein taught;
- FIG. 5 is a photomicrograph at 2000 magnification showing the structural commercial M2 steel as hardened and tempered.
- FIG. 6 is a photomicrograph at a magnification of 500 of a consolidated alloy made as herein taught
- FIG. 7 is a graph showing turning test data for one of the alloys made as herein taught in comparison with other steels.
- FIG. 8 is a graph of turning test data for another of the alloys made as herein taught in comparison with other steels.
- atomized metal powders I preferably commence with an atomization process, although, of course, other methods of producing prealloyed powders which in turn, upon consolidation as herein taught, yield the present novel microstructures may be used.
- the apparatus for atomization is schematically illustrated in FIGS. 1 and 2 although it will be understood that other similar apparatus may be likewise employed.
- An appropriate alloy charge of the desired composition was first weighed up, melted in a suitable crucible and then the molten alloy was poured through the orifice 21 at the top of the atomizing chamber 22. In such chamber 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.
- atomized metal powders I provide at the bottom of the apparatus a water reservoir 24 which may operate in conjunction with the atomizing stream to quench the particles.
- the atomizing chamber which is fabricated of a steel shell, water-cooled, is approximately three feet in diameter and approximately two feet in height. Obviously, other dimensions may be employed without departing from the spirit or scope of my invention. At the bottom the chamber is slightly conical and at 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 atomized powders were finer than 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 a significant increase in powder density for-most alloys, apparently because of the spheroidal shape and extreme harness 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 minutes prior to upset Appelr forging on a 250-pound capacity mechanical forge unit. Forging was used to produce pancake ingots approximately /2 inch thick. After forging, the canned billets were hot rolled to approximately 0.22 to 0.24 inch using a 10% reduction per pass, this representing a total reduction in thickness of 90 to 92% of the original billet thickness. The canning material was then removed and the rolled plate stock sectioned for metallurgical examination and mechanical property evaluations. It should be noted that the consolidation of the powders into wrought stock was accomplished without resorting to conventional sintering techniques and without adding carbon in any manner to the powders.
- Alloy Number 1 is commercial M-2 stock.
- the other alloys which are presented represented novel compositions in that they are greatly enriched in carbon and carbide forming elements, especially vanadium.
- alloy powders resulting from the atomization technique were canned they were heated to temperatures ranging from l850 to 2150 F. and hammer forged and then hot rolled to consolidate. It should be noted that press forging or extrusion into solid shapes or other means of consolidating said powders may be employed.
- the present alloys are preferentially treated by the steps involving hot working, annealing, machining to shape, austenitizing and tempering.
- the carbon content of an atomized high-speed steel decreases substantially when annealed and sintered in so-called pure dry hydrogen, thus requiring large additions to the powders of carbon in the form of lampblack, graphite, or a carbonaceous gas. A portion of this carbon loss occurs during the lengthy annealing treatment which is necessary to soften the atomized powders so that they may be cold pressed.
- the method taught herein utilizes direct working in sealed cans, for example, of the atomized powders which prevents further oxidation when the powders are heated for consolidation by forging or other powder Working methods.
- the atomized powders are annealed and sintered as taught in the prior art, the amount of carbon in the final product is extremely dilficult to control.
- Deleterious oxides are those which, by their morphology (such as continuous or semicontinuous films on the prealloyed powder particles), render the powders ditlicult to consolidate, cause structural weakness of the consolidated product, or require an excessive amount of mechanical working of the product to break up and disperse such films so that they do not adversely affect the strength properties.
- the present alloy compositions are consolidated in the hot state to substantially fully dense stock by plastic deformation of the prealloyed powders.
- Table II presents Rockwell C harness data of some of the present alloys treated as shown in the table.
- Table III presents some room temperature transverse rupture data of the present alloys.
- FIG. 3 there is illustrated the fine carbide phase and the uniform distribution thereof as is found in the present alloy systems. This particular photomicrograph is unetched.
- FIG. 4 is a photomicrograph of the atomized consolidated alloys made as taught by my process and it is apparent that the carbide phase is uniformly distributed and is very fine size ranging up to 3 microns. The matrix at the same time is quite fine, ranging up to 5 microns.
- the commercial M-2 alloys as shown in FIG. 5 have a matrix grain size of greater than 10 microns, the carbide phase is not uniformly dispersed therein and the carbide phase is of relatively large grain size.
- the matrix grain size is less than 5 microns although it is possible but somewhat less desirable by the practice of my invention to have the matrix grain size somewhat larger than is found in the preferred embodiment hereof.
- Alloy Number 32 was fabricated into one-quarter inch diameter stub length twist drills. To provide appropriate comparison a drill of similar geometry was fabricated from commercial RC-70 steel, the best presently available high speed steel. Both such twist drill materials were then employed to drill holes in AISI 4340 stock quenched and tempered to a Rockwell C hardness of 37. Alloy 32 produced 29 holes whereas the commercial RC7-O drill produced only 17 holes before excessive corner wear and chipping prevented further drilling. The toughness of Alloy 32 was demonstrated by the absence of chipping or breakage.
- FIG. 7 shows some turning test data for Alloy 32 and compares the results with three commercially available tool steels.
- the tests which are charted on that graph were run on AISI 4340 steel having a Rockwell C hardness of 50 to 52.
- RC-70 as indictaed above, is considerd the best commercially available tool steel.
- Alloy 32 is far superior to it. For example, as a cutting speed of feet per minute Alloy 32 had a tool life of 17 minutes compared to RC-s 4 minutes. At 50 f.p.m. the difference is 39 minutes compared to only 10 minutes. The important implications and advantages of this will be immediately apparent to those skilled in this art.
- FIG. 8 compares Alloy 25 with two other commercial steels noted on the graph. This is lathe turning test data on AISI 4340 steel of Rockwell C hardness 38 to 40. At 100 feet per minute, for example, Alloy 25 had a tool life more than double both RC-70 and commercial M1 steels (22 minutes versus 10 for the others).
- the carbide volumes of some of the present alloys were increased by forming other carbides in addition to vanadium carbide.
- the carbon content of these alloys ranges from 0.6 to 4.0% by weight.
- Some of the carbon in the charge combines with the carbide-forming additives such as vanadium to produce hard carbide particles. Additional carbon is required to permit the iron-rich matrix to be hardened to the extent that the alloy can be hardened to at least Rockwell C 60 by using standard hardening techniques. Amounts of carbon greatly in excess of that required to harden the matrix and to form hard carbides with alloying constituents may lead to the formation of other carbide phases as well as excessive retained austenite after heat treating, either of which may be undesirable.
- the tungsten and molybdenum concentrations in the present alloys are so related whereby the total of the molybdenum plus one-half of the tungsten content should be greater than 4 but less than 15 with the molybdenum ranging from to 10% and the tungsten from 0 to 20%. Accordingly, when the tungsten content is high, there can be no, or small amounts of molybdenum. At the same time, a high molybdenum content can permit the elimination of tungsten.
- the amount of chromium that can be used herein ranges from 2.5 to 16%. If greater oxidation resistance is desired the chromium content will approach the higher end of the range.
- Cobalt is an optional alloying additive. This element acts as a solid solution strengthening agent and by adding it to the present alloy system one increases the elevated temperature strength.
- Vanadium is the most important carbide forming element used in this alloy system. All or a portion of the vanadium may be replaced by other strong carbide elements selected from the group, titanium columbium, tantalum, zirconium and hafnium taken singly or in combination in amounts up to by weight. The use of these materials is optional. When these elements are used the vanadium content can range from 0 to 12.2% and the Ti, Cb, Ta, Zr and Hf can range from 0 to 5% with the proviso that the total vanadium plus one, a group, or all of these others total at least 0.8% and not be be greater than 12.2%.
- Achieving a fine, uniformly dispersed carbide phase permits the incorporation of a substantially larger volume of this hard, wear-resistant component than is found in prior art materials without a concurrent reduction in strength or toughness.
- Conventionally processed tool steels and other ferrous alloys are melted and then poured into ingot molds which are of such size, shape and characterized by such a thermal conductivity that the metal requires at least sevral minutes before solidification is complete.
- Dur- '10 ing this time interval the carbide phase nucleates and then grows to appreciable size. Subsequent hot working of the ingots causes some break up of the carbides but they remain relatively coarse and tend to be aligned in the direction of hot working.
- the alloys which are made as taught in this invention are cooled from the molten state in the form of the fine droplets (mostly less than 0.007 inch in diameter) which solidify in a fraction of a second. This extremely short time interval does not permit the carbide phase to grow appreciably.
- the atomized powders are then heated for consolidation and for subsequent heat treatment of the solid stock. It should be noted that this heating is done at a temperature below that at which there is an undue coarsening or agglomeration of the carbide phase. Because of the extreme fineness of the hard carbide particles the atomized and consolidated present alloys may be hot worked at temperatures similar to or even lower than those used for conventionally produced tool steels and the alloys do not contain large carbide particles which would act as sites for crack initiation and propagation. Thus another advantage of the present alloys and the herein-described method of making them is that greater carbide volumes may be had without impairing alloy workability.
- the atomized and consolidated alloys of my invention may be heat treated by methods commonly employed for conventional tool steels. After hot working the consolidated alloys may be annealed or softened for subsequent machining by heating to temperatures of 1500" or 1600 F. followed by slow cooling such as furnace cooling. After the appropriate finished shape has been machined from the softened stock it may then be hardened by standard commercial practices.
- the hardening or austenitizing is most readily accomplished by first heating the alloy to a temperature of approximately 2100 or 2200 F., holding at this temperature for sufficient length of time to permit adequate solution of carbides into the matrix, and then cooling by immersion in oil or by air cooling. Following this quenching the alloys are then tempered by reheating to a temperature near 950 to 1100 F. for one or two hours; this tempering treatment may be performed two or three times (cooling to room temperature between each heating cycle) to impart additional toughness to the alloy.
- the heat treatments employed during annealing, austenitizing and tempering are conducted at temperatures which do not permit excessive growth or agglomeration of the carbide phase during the heating periods for such atomized and consolidated alloys.
- the total of the molybdenum content plus one-half of the tungsten content is greater than 4 but less than 15, and wherein the carbon content is at least sufiicient to allow said alloy to be hardened to a Rock-well C value of at least 60,
- alloy metal stock being characterized by having a substantially uniformly dispersed carbide phase in a major iron-rich matrix, said carbide phase predominantly having a particle size of less than 3 microns.
- Mo 0 to 10 W 0 to 20 Element selected from the group consisting of Ti, Cb, Ta, Zr, Hf and mixtures thereof 0 to 5 C 0.6 to 4.0
- alloy metal stock being characterized by having a substantially uniformly dispersed carbide phase in a major iron-rich matrix, said carbide phase predominantly having a particle size of less than 3 microns.
- a method for producing solid iron-base alloys characterized by a substantially uniformly dispersed carbide phase in a major iron-rich matrix, said carbide phase predominantly having a particle size of less than 3 microns, from prealloyed powders consisting essentially of the following ingredients in substantially the proportions stated:
- the improvement comprises,
Abstract
Description
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
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US51805866A | 1966-01-03 | 1966-01-03 |
Publications (1)
Publication Number | Publication Date |
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US3556780A true US3556780A (en) | 1971-01-19 |
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US518058A Expired - Lifetime US3556780A (en) | 1966-01-03 | 1966-01-03 | Process for producing carbide-containing alloy |
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Cited By (22)
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 |
JPS4994515A (en) * | 1972-10-24 | 1974-09-07 | ||
US3853537A (en) * | 1969-12-20 | 1974-12-10 | F Thummler | Sintering alloy |
US3887667A (en) * | 1970-07-15 | 1975-06-03 | Special Metals Corp | Method for powder metal production |
US3988084A (en) * | 1974-11-11 | 1976-10-26 | Carpenter Technology Corporation | Atomizing nozzle assembly for making metal powder and method of operating the same |
US4032302A (en) * | 1974-12-23 | 1977-06-28 | Hitachi Metals, Ltd. | Carbide enriched high speed tool steel |
JPS54116318A (en) * | 1978-03-01 | 1979-09-10 | Kobe Steel Ltd | Highly wear resistant powder high speed steel |
JPS5538961A (en) * | 1978-09-11 | 1980-03-18 | Kobe Steel Ltd | Powder high speed steel of superior abrasion resistance and toughness |
US4194900A (en) * | 1978-10-05 | 1980-03-25 | Toyo Kohan Co., Ltd. | Hard alloyed powder and method of making the same |
US4272463A (en) * | 1974-12-18 | 1981-06-09 | The International Nickel Co., Inc. | Process for producing metal powder |
US4640711A (en) * | 1983-09-26 | 1987-02-03 | Metals Ltd. | Method of object consolidation employing graphite particulate |
US4667497A (en) * | 1985-10-08 | 1987-05-26 | Metals, Ltd. | Forming of workpiece using flowable particulate |
US4808226A (en) * | 1987-11-24 | 1989-02-28 | The United States Of America As Represented By The Secretary Of The Air Force | Bearings fabricated from rapidly solidified powder and method |
US4853178A (en) * | 1988-11-17 | 1989-08-01 | Ceracon, Inc. | Electrical heating of graphite grain employed in consolidation of objects |
US4915605A (en) * | 1989-05-11 | 1990-04-10 | Ceracon, Inc. | Method of consolidation of powder aluminum and aluminum alloys |
US4933140A (en) * | 1988-11-17 | 1990-06-12 | Ceracon, Inc. | Electrical heating of graphite grain employed in consolidation of objects |
US5238482A (en) * | 1991-05-22 | 1993-08-24 | Crucible Materials Corporation | Prealloyed high-vanadium, cold work tool steel particles and methods for producing the same |
US5290507A (en) * | 1991-02-19 | 1994-03-01 | Runkle Joseph C | Method for making tool steel with high thermal fatigue resistance |
US5294382A (en) * | 1988-12-20 | 1994-03-15 | Superior Graphite Co. | Method for control of resistivity in electroconsolidation of a preformed particulate workpiece |
US20090252636A1 (en) * | 2008-04-08 | 2009-10-08 | Christopherson Jr Denis B | Powdered metal alloy composition for wear and temperature resistance applications and method of producing same |
US9162285B2 (en) | 2008-04-08 | 2015-10-20 | Federal-Mogul Corporation | Powder metal compositions for wear and temperature resistance applications and method of producing same |
US9624568B2 (en) | 2008-04-08 | 2017-04-18 | Federal-Mogul Corporation | Thermal spray applications using iron based alloy powder |
-
1966
- 1966-01-03 US US518058A patent/US3556780A/en not_active Expired - Lifetime
Cited By (29)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3853537A (en) * | 1969-12-20 | 1974-12-10 | F Thummler | Sintering alloy |
US3655458A (en) * | 1970-07-10 | 1972-04-11 | Federal Mogul Corp | Process for making nickel-based superalloys |
US3887667A (en) * | 1970-07-15 | 1975-06-03 | Special Metals Corp | Method for powder metal production |
JPS4994515A (en) * | 1972-10-24 | 1974-09-07 | ||
JPS5427817B2 (en) * | 1972-10-24 | 1979-09-12 | ||
US3988084A (en) * | 1974-11-11 | 1976-10-26 | Carpenter Technology Corporation | Atomizing nozzle assembly for making metal powder and method of operating the same |
US4272463A (en) * | 1974-12-18 | 1981-06-09 | The International Nickel Co., Inc. | Process for producing metal powder |
US4032302A (en) * | 1974-12-23 | 1977-06-28 | Hitachi Metals, Ltd. | Carbide enriched high speed tool steel |
JPS54116318A (en) * | 1978-03-01 | 1979-09-10 | Kobe Steel Ltd | Highly wear resistant powder high speed steel |
JPS5937740B2 (en) * | 1978-03-01 | 1984-09-11 | 株式会社神戸製鋼所 | High wear resistance sintered high speed steel |
JPS5538961A (en) * | 1978-09-11 | 1980-03-18 | Kobe Steel Ltd | Powder high speed steel of superior abrasion resistance and toughness |
JPS5937741B2 (en) * | 1978-09-11 | 1984-09-11 | 株式会社神戸製鋼所 | Sintered high-speed steel with excellent wear resistance and toughness |
US4194900A (en) * | 1978-10-05 | 1980-03-25 | Toyo Kohan Co., Ltd. | Hard alloyed powder and method of making the same |
US4640711A (en) * | 1983-09-26 | 1987-02-03 | Metals Ltd. | Method of object consolidation employing graphite particulate |
US4667497A (en) * | 1985-10-08 | 1987-05-26 | Metals, Ltd. | Forming of workpiece using flowable particulate |
US4808226A (en) * | 1987-11-24 | 1989-02-28 | The United States Of America As Represented By The Secretary Of The Air Force | Bearings fabricated from rapidly solidified powder and method |
US4933140A (en) * | 1988-11-17 | 1990-06-12 | Ceracon, Inc. | Electrical heating of graphite grain employed in consolidation of objects |
US4853178A (en) * | 1988-11-17 | 1989-08-01 | Ceracon, Inc. | Electrical heating of graphite grain employed in consolidation of objects |
US5294382A (en) * | 1988-12-20 | 1994-03-15 | Superior Graphite Co. | Method for control of resistivity in electroconsolidation of a preformed particulate workpiece |
US4915605A (en) * | 1989-05-11 | 1990-04-10 | Ceracon, Inc. | Method of consolidation of powder aluminum and aluminum alloys |
US5290507A (en) * | 1991-02-19 | 1994-03-01 | Runkle Joseph C | Method for making tool steel with high thermal fatigue resistance |
US5238482A (en) * | 1991-05-22 | 1993-08-24 | Crucible Materials Corporation | Prealloyed high-vanadium, cold work tool steel particles and methods for producing the same |
US5344477A (en) * | 1991-05-22 | 1994-09-06 | Crucible Materials Corporation | Prealloyed high-vanadium, cold work tool steel particles |
US20090252636A1 (en) * | 2008-04-08 | 2009-10-08 | Christopherson Jr Denis B | Powdered metal alloy composition for wear and temperature resistance applications and method of producing same |
US9162285B2 (en) | 2008-04-08 | 2015-10-20 | Federal-Mogul Corporation | Powder metal compositions for wear and temperature resistance applications and method of producing same |
US9546412B2 (en) * | 2008-04-08 | 2017-01-17 | Federal-Mogul Corporation | Powdered metal alloy composition for wear and temperature resistance applications and method of producing same |
US9624568B2 (en) | 2008-04-08 | 2017-04-18 | Federal-Mogul Corporation | Thermal spray applications using iron based alloy powder |
US20200156156A1 (en) * | 2008-04-08 | 2020-05-21 | Tenneco Inc. | Powder metal material for wear and temperature resistance applications |
US10926334B2 (en) * | 2008-04-08 | 2021-02-23 | Tenneco Inc. | Powder metal material for wear and temperature resistance applications |
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