US3837930A - Method of producing iron-chromium-aluminum alloys with improved high temperature properties - Google Patents

Method of producing iron-chromium-aluminum alloys with improved high temperature properties Download PDF

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US3837930A
US3837930A US00325313A US32531373A US3837930A US 3837930 A US3837930 A US 3837930A US 00325313 A US00325313 A US 00325313A US 32531373 A US32531373 A US 32531373A US 3837930 A US3837930 A US 3837930A
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powder
grain
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chromium
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R Cairns
J Benjamin
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Huntington Alloys Corp
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International Nickel Co Inc
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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
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
    • C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
    • C22C32/0026—Matrix based on Ni, Co, Cr or alloys thereof
    • 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
    • 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
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
    • B22F2003/208—Warm or hot extruding
    • 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
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B22F2003/248—Thermal after-treatment
    • 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
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • B22F2009/041—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by mechanical alloying, e.g. blending, milling
    • 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
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps

Definitions

  • ABSTRACT A powder metallurgy product comprising iron and chromium, and/or aluminum and characterized by elongated grains that are stable at elevated temperatures.
  • a method of producing such a product including mechanically alloying a suitable powder charge,
  • the product produced according to the present invention exhibits good oxidation resistance and good room temperature and elevated temperature strength and ductility.
  • the constituent metal particles of the starting powder charge are integrated together into dense composite particles without melting any of the constituents, this being done by dry milling the powder, usually in the presence of grinding media, e.g., balls, so as to apply to the powder charge, mechanical energy in the form of a plurality of repeatedlyapplied high energy, compressive forces.
  • grinding media e.g., balls
  • Such high energy forces result in the fracture, or comminution, of the original powder constituents and the welding together of the fragments so produced, as well as the repeated fracture and re-welding of the welded fragments, so that there is brought about a substantially complete codissemination of the fragments of the various constituents of the starting powder.
  • the mechanically alloyed composite powder particles produced in this manner are characterized metallographically by cohesive internal structures in which the constituents are intimately united to provide an interdispersion of comminuted fragments of the starting constituents. Very short distances across the areas corresponding to the fragments of initial materials in the composite particles can be created, e.g., on the order of 3 microns or 1 micron or less, and fine dispersoid particles present in the powder charge can be uniformly distributed throughout the composite particles at short interparticle spacings, e.g., one micron or less.
  • the mechanical alloying process may be conducted in a variety of equipment, including a stirred ball mill,
  • the attritive elements By maintaining the attritive elements in a highly activated state of mutual collision in a substantially dry environment and throughout substantially the whole mass, optimum conditions are provided for comminuting and cold welding the constituents, accompanied by particle growth, to produce within each composite particle, a mechanically alloyed structure of the constituents.
  • the resulting composite metal powder will be heavily cold worked and will reach a high hardness level, which becomes substantially constant (saturation hardness) after a minimum milling time due to impact compression of the particles arising from repeated collision of the attractive elements upon the metal particles, such hardness level providing stored energy to the composite powder particles.
  • milling is usually conducted beyond the point at which saturation hardness is reached.
  • FIG. 1 is a photomicrograph taken at 50 diameters of an iron-base product made according to the present invention, which product was cold-rolled 50 percent and grain coarsened by heating at 2,400F. for one hour.
  • P10. 2 is a photomicrograph taken at 100 diameters of a wire produced according to the present invention which wire was exposed to a temperature of 2400F. for 160 hours.
  • the present invention includes the mechanical alloying of powder charges containing by weight, about 10 percent to about 40 percent chromium; up to about 10 percent aluminum, e.g., about 1 percent to about 10 percent aluminum; up to about 20 percent cobalt; up to about 10 percent nickel; up to about 5 percent titanium; up to about 2 percent each of rare earth metal, yttrium, zirconium, columbium, hafnium, tantalum, silicon, and/or vanadium; up to about 6 percent each of tungsten and molybdenum; and the balance essentially iron, and further including by volume, up to about 10 percent finely divided dispersoid material consisting of oxides, nitrides, carbides, borides and other refractory materials, which dispersoid material has a melting point of at least about 2750F.; hot consolidating the mechanically alloyed powder to a substantially completely dense body (e.g., about 98 percent theoretical density or more); working the consolidated body at a temperature within the
  • the powder charge and consolidated material produced therefrom contain, by weight about l5 to 40 percent chromium, and even more preferably, about 18 percent to about 26 percent chromium; up to about 5 percent cobalt; up to about 6 percent nickel; about 1 percent to about 7 percent aluminum, e.g., about 3 to 7 percent aluminum; up to about 0.5 percent zirconium; up to about 1 percent titanium; about 0.1 percent to about 10 percent or more preferably, about 0.25 to 5 percent dispersoid in the form of a finely divided, well-distributed refractory dispersoid; such as a refractory oxide, including alumina, lanthana, yttria, ceria, titania, silica, zirconia, hafnia, for example; a metal carbide; and/or a metal nitride, such as zirconium nitride; and the balance essentially iron.
  • a refractory oxide including alumina,
  • the dispersoid particles preferably have a particle size of about 50A. to 5000A., more preferably about 100A. to 1000A., and have average interparticle spacings of about 500A. to about 2500A, more preferably, about 660A. to about 1800A.
  • the mechanical alloying operation is carried out in a stirred ball mill, e.g., a Szegvari attritor, provided with an attrition medium comprising balls having an average diameter of 0.1 to 0.5 inches and running at an impeller speed of about 50 to 350 RPM.
  • the halls are present in an amount sufficient to provide a ball-topowder ratio, preferably, of about from 4 to 1 to about 50 to i.
  • the respective impeller speeds can be about 300 to 400 RPM and about 70 to 100 RPM.
  • the mechanical alloying operation preferably is carried out for a time sufficient, in the particular milling device employed, to ensure the substantial homogeneity of the final composite particles and to impart substantial saturation hardness to the composite particles.
  • milling times of about 10 to about hours, e.g., about 15 to about 20 hours, are usually sufficient in a high energy mill such as the attritor.
  • the mechanical alloying operation be conducted in an inert atmosphere such as argon and, preferably at a flow rate sufficient to prevent substantial infiltration of air into the mill, e.g., about 5 cu. ft. of argon per hr. in a mill having an internat volume of 10 to 15 gallons, so that the uncontrolled pickup of gases such as oxygen and nitrogen in the powders is minimized. It appears that the presence of excessive oxygen, and possibly also nitrogen, in the mill atmosphere during milling can hinder the welding factor which desirably occurs during mechanical alloying, may lead to the production of undesirably fine powders and contribute to inhomogeneity.
  • an inert atmosphere such as argon and, preferably at a flow rate sufficient to prevent substantial infiltration of air into the mill, e.g., about 5 cu. ft. of argon per hr. in a mill having an internat volume of 10 to 15 gallons
  • the amount of nitrogen and of oxygen in the powder does not exceed about 0.4 percent oxygen and 0.2 percent nitrogen.
  • Satisfactory composite powders generally have average particle sizes in the range 10 to 1000 microns, e.g., about 20 to 200 microns.
  • the dispersoid ingredient is present in the powder in a total amount of, by volume, about 0.1 to 10 percent and is well distributed throughout the composite at average interparticle distances from about 500 to 2,500 Angstroms.
  • the composite powder is dense and substantially devoid of internal porosity such that it withstands penetration by a diamond pyramid indenter, Generally, milling is continued substantially beyond the point at which substantial saturation hardness is achieved in the composite powder for the purpose of further improving the homogeneity of the powder with beneficial results in terms of strength and ductility in consolidated powders made therefrom, as well as avoidance of segregated areas in the consolidated material made therefrom.
  • the powder charges that can be converted to mechanically alloyed powders having the compositional requirements set forth herein may include iron powder, e. g., sponge iron, reduced mill scale, decarburized carbonyl iron powder, etc., generally having a particle size not exceeding 100 mesh.
  • Chromium may be introduced into the charge as chromium powder, e.g., electrolytic chromium having a particle size not exceeding 100 mesh, or ferrochromium powder containing about to percent chromium and not more than about 0.2 percent carbon, and the balance iron, having a particle size not exceeding mesh.
  • Aluminum may be introduced as an iron-aluminum master alloy powder containing 50 to 80 percent aluminum and the balance iron and other desired ingredients, e.g., iron, chromium, aluminum, etc. Additionally, the chromium and the aluminum, when desired, can be incorporated into the initial powder mixture as an iron-chromiumaluminum master alloy powder. It is preferred that the nitrogen content of the initial'powder charge be sufficiently low to provide mechanically alloyed powder containing less than 0.2 weight per cent nitrogen.
  • the mechanically alloyed composite powders are thereafter hot consolidated as, for example, by canning (in a can which may be mild steel, stainless steel, nickel, etc., and which is welded shut after filling with powder) and hot extruding the powder, or by other hot compaction steps.
  • Powder extrusion can be carried out at an elevated temperature up to 1600F. or higher, e.g., 2000F. or 2400F., the extrusion ratio preferably being about 5:1 to 50:1 or higher.
  • the consolidated powder products can then be fabricated into various shapes; for example, the consolidated powder products can be hot and/or cold rolled to plate or sheet, or rolled, swaged or drawn to bar, rod or wire.
  • Such fabrication can be carried out at elevated temperatures, e.g., up to about 2000F. or even higher, or at ambient temperature, intermediate anneals preferably being utilized in the latter case (i.e., fabrication at ambient temperature) after reductions of about 50 percent.
  • the consolidated product is then worked (i.e., drawn, forged, rolled, etc.) at temperatures not exceeding about 1600F. to 1700F. so as to permit the production of coarse, elongated grains on subsequent heat treatment.
  • Heat treatment of the consolidated product without post-consolidation working thereof generally does not result in coarse, elongated grains.
  • the required amount of working of the consolidated product generally decreases with increasing dispersoid content thereof and is preferably about to 12 percent reduction or more; for example, a cold-working reduction of about 16 percent to about percent or more can be employed with a consolidated product having a total dispersoid content of up to about 1 to 2 volume percent.
  • the amount of working of the consolidated product before the grain-coarsening, or secondary recrystallization, heat treatment and the graincoarsening heat-treatment temperature that are required to achieve elongated, relatively coarse grains are a function of the amount of stored energy in the consolidated product.
  • higher amounts of such stored energy can be produced by mechanically alloying for longer periods of time and/or consolidating, e.g., by extrusion, the mechanically-alloyed powder at lower temperatures and/or with greater amounts of working or deformation of the powder.
  • the amount of working before the graincoarsening heat treatment be sufficient to induce strains, i.e., provide stored energy, throughout the consolidated product so that coarse, elongated grains can subsequently be generated substantially completely throughout the product.
  • the product is subjected to a grain-coarsening heat treatment at an elevated temperature which may be about 2,200F. up to a temperature below the incipient melting point of the alloy.
  • an elevated temperature which may be about 2,200F. up to a temperature below the incipient melting point of the alloy.
  • the grain-coarsening heat treatment can be conducted at significantly lower temperatures, e.g., temperatures as low as 1600F.
  • temperatures e.g., temperatures as low as 1600F.
  • stressrupture properties it appears that no significant difference results whether grain coarsening occurs at a relatively low temperature or at a higher temperature. Grain coarsening is itself the significant parameter and the phenomenon does not occur unless work is imparted to the material after hot consolidation. It is generally found that higher temperatures are required where the product includes about 0.5 percent or more, by weight, zirconium, or where the powder is mechanically alloyed for relatively short periods, e.g., about 15 hours.
  • Such heating results in grain growth, wherein the grains of the product grow to a definite desired size that is not substantially exceeded even after subsequent sustained exposure to temperatures approaching the melting point of the alloy, e.g., about 2,350F. to 2,400F. for 100 hours or more, which grains are elongated in the direction or directions of working and generally have dimensions in the range of about 10 to l00-microns wide and about 50 to 2000 microns long, when viewed two-dimensionally.
  • Such larger grains provide significant improvement in high temperature tensile and stress-rupture strengths.
  • Products made according to the invention also exhibit elevated temperature grain stability, room temperature workability, comparatively high room-temperature tensile strength, and reduced tendency for embrittlement at ambient temperatures after extended exposure to elevated temperature.
  • such dispersoid particles can be produced by adding precursor material to the initial powder charge and thereafter converting such precursor material to the appropriate dispersoid composition.
  • precursor material for example, there can be added to the initial powder charge particles of zirconium metal and/or misch metal, after which the zirconium and/or misch metal is converted to the oxide form (i.e., zirconia, lanthana, ceria, etc.).
  • oxide form i.e., zirconia, lanthana, ceria, etc.
  • Such conversion to the dispersoid composition can be achieved, for example, by introducing controlled amounts of oxygen into the charge before or during the mechanical alloying operation.
  • a readily reducible metal oxide such as iron oxide, nickel oxide, etc., having a negative free energy of formation substantially below kilocalories per gram atom of oxygen at 25C.
  • oxygen gas can be included in a mixture with argon during milling, so as to form a fine dispersoid oxide by diffusion and internal oxidation when the resulting powder is hot consolidated.
  • desired dispersoid particles are nitrides, (e.g. ZrN)
  • controlled amounts of nitrogen can be introduced into the mill in the form of nitrogen gas mixed with argon, for example.
  • oxide and nitride compounds have been mentioned as dispersoid particle compositions, other types of dispersoid materials can also be used in the present invention, e.g., up to about 10 percent of one or more hard phases, such as carbides, borides, and the like.
  • Refractorycompounds which may be included in the powder mix or produced in situ include oxides, carbides, nitrides, borides of such refractory metals as thorium, zirconium,,hafnium, titanium, and even such refractory oxides as those of silicon, aluminum, yt-
  • the refractory dispersoid material has a preferred melting point of at least about 2750F.
  • the refractory oxides generally include the oxides of those metals whose negative free energy of formation of the oxide per gram mole of oxygen at about 1000C. is at "least about 150 kilocalories.
  • the refractory nitrides include those metal nitrides having a negative free energy of formation of at least about 25 kilocalories per gram mole of nitrogen at 1000C. and the refractory carbides include metal carbides having a negative free energy of formation of at least about l kilocalories per gram atom of carbon at 1000C.
  • EXAMPLE 1 8.5 kilograms of a powder mixture comprising, by weight, 28.7 percent minus 100 mesh ferrochromium powder, 1 percent cobalt powder, having an average particle size of 5 microns, 61 percent minus 100 mesh iron powder, 6 percent minus 100 mesh ferroaluminum including 65 percent aluminum, 2.5 percent 100 mesh ferroaluminum including 65 percent aluminum and 10 percent cerium-free misch metal, 0.3 percent of ferrocolumbium including 67 percent columbium and 0.5 percent of ferrozirconium including 10 percent zirconium, was mechanically alloyed for a period of 18 hours in a IO-gallon capacity Szegvari attritor. The mechanical alloying was carried out with 380 lbs.
  • a portion of the extruded bar was subsequently bar rolled at room temperature to a strain of 40 percent reduction in area, and annealed for one hour at 2400F.
  • the bar exhibited grain growth as evidenced by grains having average dimensions of about 100 microns in width and about 1000 microns in length.
  • EXAMPLE 11 I An extrusion having the same composition as that described in Example I was produced with a powder mixture and under the processing conditions similar to those described in Example I, except that the mechanical alloying time in this instance was 12 hours.
  • the wire was annealed at 2400F.
  • the wire grains, after each of the annealing times being elongated in the working directions and being, on the average, about 200 microns long and about 20 microns wide, as illustrated in FIG. 2, which is the grain structure of the 160 hour annealed wire.
  • the relative uniformity of grain size of the wires annealed at the various temperatures indicates the grain stability that is present therein at elevated temperatures.
  • the commercial wire which had an average initial grain size of about 40 microns, exhibited very extensive, uncontrolled grain growth as a result of the high temperature heating, the grown grains of the commercial wire being essentially equiaxed and having an average size of 1200 microns.
  • Example III A portion of the mechanically alloyed powder described in Example I was canned and hot compacted in a closed extrusion container at 2100F. to form a 3 /2 inch diameter compact having fine grain size. The compact was heated to 2100F. and rolled from 3 /2 inch diameter round to a 3-inch square and then to a 2 inch thick rectangle which was cross-rolled to l-inch thick plate. The plate was reheated to 2100F. and rolled to 0.25-inch plate. The plate was annealed at 1800F.
  • the sheet exhibits the same type of grain structure as that described in Example II, i.e., elongated grains of relatively large size (about 200 microns long and 20 microns wide) produced by grain growth.
  • Each mechanically alloyed powder was canned in a 3 /2 inch diameter mild steel can and consolidated without evacuation of the can by extruding at 2000F. to %-inch diameter bars, which were then turned to 0.664-inch diameter.
  • portions of the bars were heated at 2400F. for /2 hour in an attempt to achieve grain coarsening therein, no grain coarsening resulted.
  • Bars produced from Powder Nos. 1,2,3, 6 and 7 were then individually rolled at room temperature to various reductions of 16 to 41 percent. A portion of each bar was removed after each reduction step, each of these portions then being heated at 2400F. for 16 hour and inspected for grain coarsening, the results being given in Table IV, where the consolidated products are assigned the same numbers as their corresponding powclers.
  • the dispersoid particles generally ranged in size from about 150A. to about 500A., with average interparticle spacings of about 1 100A. for Bar No. 1, about 800A. for Bar Nos. 2,4 and 5, and about 650A. for Bar Nos. 3,6 and 7, these values occurring in both the extrusions and in the grain-coarsened products.
  • a method of producing a powder metallurgy product comprising:
  • yttrium, zirconium, columbium, hafnium, tantalum, silicon, and/or vanadium up to about 6 percent each of tungsten and molybdenum, and the balance iron, further comprising up to about It) volume percent dispersoid material having a melting point of at least 2750F., and working the consolidated product at a temperature not higher than the temperature range of about 1600F. to about 1700F. to achieve therein a reduction of at least about 10 percent, such that the resulting worked material will undergo grain coarsening when subjected to an elevated grain coarsening temperature.

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US00325313A 1972-01-17 1973-01-22 Method of producing iron-chromium-aluminum alloys with improved high temperature properties Expired - Lifetime US3837930A (en)

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US4075010A (en) * 1976-02-05 1978-02-21 The International Nickel Company, Inc. Dispersion strengthened ferritic alloy for use in liquid-metal fast breeder reactors (LMFBRS)
US4111685A (en) * 1976-11-04 1978-09-05 Special Metals Corporation Dispersion-strengthened cobalt-bearing metal
US4391634A (en) * 1982-03-01 1983-07-05 Huntington Alloys, Inc. Weldable oxide dispersion strengthened alloys
US4404023A (en) * 1981-04-07 1983-09-13 Eckart-Werke Standard Bronzepulver-Werke Carl Eckart Process for the production of a metal or metal alloy powder
US4619699A (en) * 1983-08-17 1986-10-28 Exxon Research And Engineering Co. Composite dispersion strengthened composite metal powders
US4627959A (en) * 1985-06-18 1986-12-09 Inco Alloys International, Inc. Production of mechanically alloyed powder
DE3714239A1 (de) * 1987-04-29 1988-11-17 Krupp Gmbh Verfahren zur herstellung von pulvern und formkoerpern mit einem gefuege nanokristalliner struktur
US5002834A (en) * 1988-04-01 1991-03-26 Inco Alloys International, Inc. Oxidation resistant alloy
US5209772A (en) * 1986-08-18 1993-05-11 Inco Alloys International, Inc. Dispersion strengthened alloy
US5496419A (en) * 1993-07-30 1996-03-05 The Foundation: The Research Institute Of Electric And Magnetic Alloys Wear-resistant high permeability magnetic alloy and method of manufacturing the same
US20030021715A1 (en) * 2001-01-15 2003-01-30 Wolfgang Glatz Powder-metallurgic method for producing highly dense shaped parts
US20030215349A1 (en) * 2002-02-28 2003-11-20 Hitachi Unisia Automotive, Ltd. Production method of high density iron based forged part
GB2394960A (en) * 2002-11-04 2004-05-12 Doncasters Ltd Hafnium oxide dispersion hardened nickel-chromium-iron alloys
US20100048322A1 (en) * 2008-08-21 2010-02-25 Ryo Sugawara Golf club head, face of the golf club head, and method of manufacturing the golf club head
US20100175508A1 (en) * 2002-11-04 2010-07-15 Dominique Flahaut High temperature alloys

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DE2838850C2 (de) * 1978-09-06 1983-12-15 Gränges Nyby AB, Nybybruk Verfahren zum Herstellen kaltverformter Rohre aus auf pulvermetallurgischem Weg erzeugten stranggepreßten rostfreien Stahlrohren
GB2156854B (en) * 1984-04-06 1987-03-11 Atomic Energy Authority Uk Titanium nitride dispersion strengthened alloys
JPS61173758U (hu) * 1985-04-17 1986-10-29
GB2181454B (en) * 1985-10-10 1990-04-04 Atomic Energy Authority Uk Processing of high temperature alloys
US4732622A (en) * 1985-10-10 1988-03-22 United Kingdom Atomic Energy Authority Processing of high temperature alloys
AU600009B2 (en) * 1986-08-18 1990-08-02 Inco Alloys International Inc. Dispersion strengthened alloy
JP2579393B2 (ja) * 1990-09-12 1997-02-05 川崎製鉄株式会社 耐酸化性の優れたＦｅ−Ｃｒ−Ａｌ系急冷合金箔
US5167728A (en) * 1991-04-24 1992-12-01 Inco Alloys International, Inc. Controlled grain size for ods iron-base alloys
AUPP042597A0 (en) * 1997-11-17 1997-12-11 Ceramic Fuel Cells Limited A heat resistant steel
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US4075010A (en) * 1976-02-05 1978-02-21 The International Nickel Company, Inc. Dispersion strengthened ferritic alloy for use in liquid-metal fast breeder reactors (LMFBRS)
US4111685A (en) * 1976-11-04 1978-09-05 Special Metals Corporation Dispersion-strengthened cobalt-bearing metal
US4404023A (en) * 1981-04-07 1983-09-13 Eckart-Werke Standard Bronzepulver-Werke Carl Eckart Process for the production of a metal or metal alloy powder
US4391634A (en) * 1982-03-01 1983-07-05 Huntington Alloys, Inc. Weldable oxide dispersion strengthened alloys
US4619699A (en) * 1983-08-17 1986-10-28 Exxon Research And Engineering Co. Composite dispersion strengthened composite metal powders
US4647304A (en) * 1983-08-17 1987-03-03 Exxon Research And Engineering Company Method for producing dispersion strengthened metal powders
US4627959A (en) * 1985-06-18 1986-12-09 Inco Alloys International, Inc. Production of mechanically alloyed powder
US5209772A (en) * 1986-08-18 1993-05-11 Inco Alloys International, Inc. Dispersion strengthened alloy
DE3714239A1 (de) * 1987-04-29 1988-11-17 Krupp Gmbh Verfahren zur herstellung von pulvern und formkoerpern mit einem gefuege nanokristalliner struktur
US5002834A (en) * 1988-04-01 1991-03-26 Inco Alloys International, Inc. Oxidation resistant alloy
US5496419A (en) * 1993-07-30 1996-03-05 The Foundation: The Research Institute Of Electric And Magnetic Alloys Wear-resistant high permeability magnetic alloy and method of manufacturing the same
US20030021715A1 (en) * 2001-01-15 2003-01-30 Wolfgang Glatz Powder-metallurgic method for producing highly dense shaped parts
US7390456B2 (en) * 2001-01-15 2008-06-24 Plansee Aktiengesellschaft Powder-metallurgic method for producing highly dense shaped parts
US20030215349A1 (en) * 2002-02-28 2003-11-20 Hitachi Unisia Automotive, Ltd. Production method of high density iron based forged part
GB2394960A (en) * 2002-11-04 2004-05-12 Doncasters Ltd Hafnium oxide dispersion hardened nickel-chromium-iron alloys
GB2394960B (en) * 2002-11-04 2007-04-25 Doncasters Ltd High temperature alloys
US20100175508A1 (en) * 2002-11-04 2010-07-15 Dominique Flahaut High temperature alloys
US20100048322A1 (en) * 2008-08-21 2010-02-25 Ryo Sugawara Golf club head, face of the golf club head, and method of manufacturing the golf club head
US8475294B2 (en) * 2008-08-21 2013-07-02 Seiko Instruments Inc. Golf club head, face of the golf club head, and method of manufacturing the golf club head

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IE37465L (en) 1973-07-17
JPS5736343B2 (hu) 1982-08-03
PL75811B1 (hu) 1974-12-31
BE794142A (fr) 1973-07-17
FR2168401B1 (hu) 1977-02-04
ES410670A1 (es) 1976-01-01
CA977587A (en) 1975-11-11
IE37465B1 (en) 1977-08-03
SE389820B (sv) 1976-11-22
IT976876B (it) 1974-09-10
AT337230B (de) 1977-06-27
FR2168401A1 (hu) 1973-08-31
JPS4881713A (hu) 1973-11-01
DE2301137B2 (de) 1976-03-25
CH579636A5 (hu) 1976-09-15
LU66828A1 (hu) 1973-07-24
NL7300538A (hu) 1973-07-19
GB1407867A (en) 1975-09-24
IL41195A0 (en) 1973-02-28
DD101582A5 (hu) 1973-11-12
IL41195A (en) 1975-10-15
ZA73308B (en) 1973-11-28
RO67589A (ro) 1982-05-10
DE2301137A1 (de) 1973-08-16
ATA34373A (de) 1976-10-15

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