US3561934A - Sintered steel particles containing dispersed carbides - Google Patents

Sintered steel particles containing dispersed carbides Download PDF

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Publication number
US3561934A
US3561934A US666776A US3561934DA US3561934A US 3561934 A US3561934 A US 3561934A US 666776 A US666776 A US 666776A US 3561934D A US3561934D A US 3561934DA US 3561934 A US3561934 A US 3561934A
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Prior art keywords
tool
metal
austenitizing
high speed
article
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US666776A
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English (en)
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Gary Steven
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Crucible Materials Corp
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Crucible Inc
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Assigned to COLT INDUSTRIES OPERATING CORP. reassignment COLT INDUSTRIES OPERATING CORP. MERGER AND CHANGE OF NAME Assignors: CRUCIBLE CENTER COMPANY (INTO) CRUCIBLE INC. (CHANGED TO)
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Assigned to MELLON BANK, N.A. AS AGENT FOR MELLON BANK N.A. & MELLON FINANCIAL SERVICES CORPORATION, MELLON FINANCIAL SERVICES CORPORATION reassignment MELLON BANK, N.A. AS AGENT FOR MELLON BANK N.A. & MELLON FINANCIAL SERVICES CORPORATION SECURITY INTEREST (SEE DOCUMENT FOR DETAILS). 2ND Assignors: CRUCIBLE MATERIALS CORPORATION, A CORP. OF DE.
Assigned to MELLON BANK, N.A. FOR THE CHASE MANHATTAN BANK (NATIONAL ASSOCIATION) AND MELLON BANK N.A., CHASE MANHATTAN BANK, THE (NATIONAL ASSOCIATION) AS AGENT reassignment MELLON BANK, N.A. FOR THE CHASE MANHATTAN BANK (NATIONAL ASSOCIATION) AND MELLON BANK N.A. SECURITY INTEREST (SEE DOCUMENT FOR DETAILS). 1ST Assignors: CRUCIBLE MATERIALS CORPORATION, A CORP. OF DE.
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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
    • C22C1/00—Making non-ferrous alloys
    • C22C1/10—Alloys containing non-metals
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium

Definitions

  • the invention relates generally to powdered'metal articles and method for producing the same.
  • the invention relates to powdered metal articles produced from high speed tool and die steel compositions by hot compacting particles of said compositions.
  • the particles range in size from about -30 or finer standard mesh and contain a reactive metal component such as titanium, vanadium, zirconium, columbium, molybdenum, tungsten or tantalum.
  • the reactive metal component is reacted with a non-metal, which may be carbon, oxygen or nitrogen, to produce a nonmetallic dispersion of said reactive metal and non-metal.
  • the article is capable of hardening treatment by conventional austenitizing, quenching and tempering to hardness levels above about 58 R for die steels and 64 R for high speed steels. Austenitizing to these high hardness levels may be achieved in very short times on the order of two minute or less. In addition during hardening treatment the symmetry or out-of-roundness of the article remains substantially unchanged.
  • any change in symmetry or out-of-roundness after the hardening treatment would require a subsequent grinding operation.
  • any nonuniformity in size after hardening treatment would also have to be in some measure corrected by additional grinding.
  • this grinding operation after hardening treatment is rendered more ditficult and expensive because of the increased hardness of the material.
  • both tool and die articles must be subjected to a machining operation during the course of manufacture.
  • machining operation To permit easy machining, and particularly with cutting tools, maintenance of the machined cutting edge during use, it is desirable to have a relatively fine-grained micro-structure in the final article.
  • a more specific object of the invention is to provide tool and die steel articles produced from metal particles by a powder metallurgy technique, whereby improved properties and economies of manufacture are achieved.
  • Another object of the invention is to provide articles of high speed tool or die steel that are subject to substantially no out-of-roundness, or loss of symmetry after hardening treatment by conventional austenitizing, quenching and tempering.
  • a further, more specific object of the invention is to provide hot-compacted articles of high speed tool and die steel particles that are characterized by a hardness of at least about 58 R for die steels and 64 R for high speed steels and a substantially uniform dispersion of carbon, oxygen or nitrogen nonmetallic compounds.
  • Yet another object of the invention is to provide a hotcompacted article of high speed tool steel, such as a cylindrical hob or die, wherein all the machining and finishing operation of the article may be done prior to hardening by austenitizing, quenching and tempering; thi may be accomplished because the article is not subject to any substantial change of symmetry or nonuniform dimensional change as a result of the hardening treatment.
  • FIGS. 1A and 1B are photomicrographs showing annealed longitudinal microstructures of compacts of M28 tool steel in accordance with the present invention
  • FIG. 2 is a photomicrograph showing the microstructure of a slice cut from a conventional bar of material of the same composition and size as that of the compacts of FIGS. 1A and 113;
  • FIG. 3 is a graph comparing the austenitizing times required to achieve various hardnesses with campacts in accordance with the invention and samples of conventional material, all samples being austenitized at 2200 F., oil quenched and tempered 2+2+2 hours at 1025 F.
  • FIGS. 4A and 4B are photomicrographs of samples in accordance with the invention.
  • FIGS. 5A and 5B are photomicrographs of samples of conventional bar products of the same composition as the samples of FIGS. 4A and 4B.
  • particles of a high speed toolor die-steel composition containing a metal component capable of reacting with a non-metal, such as carbon, oxygen or nitrogen are provided.
  • Each of the particles has a non-metallic compound of the reactive metal and non-metal such as carbides, nitrides or oxides substantially evenly dispersed throughout the particle.
  • a charge of the metal particles is heated preferably in the substantial absence of oxygen to an elevated temperature and is then subjected to pressure application to compact the same in accordance with any suitable powder metallurgy technique to a final density of at least about 99 percent.
  • the compacting and heating of the particles may be achieved by placing the same in an evacuated envelope or container which is heated to temperature in a furnace and then placed in a die wherein the pressure necessary for compacting is applied by the use of a ram; alternately, the envelope containing the powdered metal charge to be compacted may be placed in a fluidpressure vessel, commonly termed an autoclave, for compacting and the charge may be heated either in the autoclave or in a furnace prior to being placed in the autoclave.
  • the heating and compacting operation can be conducted in the substantial absence of oxygen to insure the maintenance of an oxide-free particle surface for the purpose of good particle bonding during compacting and the maintenance of final product cleanliness.
  • the size of the particles of the high speed tool or die steel used in the practice of the invention preferably should be in the size range of standard mesh or finer.
  • the particle size influences the ultimate carbide size characterizing the final product.
  • Suitable reactive metals are titanium, vanadium, zirconium, columbium, molybdenum, tungsten and tantalum.
  • the grain size of the article may typically be 12 Snyder-Graft or finer. This fine grain size is believed to contribute toughness to the article.
  • the grain size is almost completely dependent upon the amount of working imparted to the article.
  • the coarser would be the grain structure thereof.
  • the articles of the invention are characterized further by a homogeneous, non-directional carbide structure. It has been demostrated, as will be shown in detail hereinafter, that change in symmetry, shape, or out-of-roundness is a direct function of the directionality of the carbide structure. Specifically, upon austenitizing, quenching and tempering, the article will tend to change in size in the direction of carbide orientation. This is substantially eliminated with the present invention because of the homogeneous, non-directional carbide structure.
  • compositions may be sulfurized to improve machinability.
  • the average carbide size is desirably 5 microns maximum and preferably 1 to 2 microns. Large carbides may necessitate austenitizing times at temperatures that are excessive and therefore uneconomical. It has been found that the average carbide size of 5 microns maximum is desirable to achieve the desired hardness in high speed steels of 64 R and greater depending upon the specific metallurgical composition of the steel, at austenitizing times at temperature of two minutes or less. In addition, in cutting-tool applications the presence of large carbides, which may be present in cutting edges of the tools, may cause increased chipping of the cutting edges during use of the tool. In
  • the nonmetallic compounds of the reactive metal and the carbon, oxygen or nitrogen, as described hereinabove may be produced in the high speed tool or die steel particles by either of two practices.
  • the nonmetallic product may be present in the melt from which the particles are made.
  • the particles may be manufactured in the substantially pure reactive metal form and thereafter the non-metal may be reacted with the reactive metal by placing the particles in an environment of said non-metal, e.g., carbon, oxygen or nitrogen environment causing the reaction to take place, and thereafter diffusing the' nonmetallic reaction compound substantially uniformly throughout the particle.
  • a hob is a cylindrical, rotating cutting tool having helical before the hob has been hardened as by austenitizing, quenching, and tempering. Prior to this invention, during the hardening treatment the hob would become unsymmetrical or be characterized by out-of-roundness. This necessitated, after hardening treatment, a grinding operation to return the cylindrical hob blank to the required symmetry.
  • the homogeneous, nondirectional carbide structure and the resulting absence of substantial out-of-roundness upon hardening treatment eliminate the need for grinding to return the hob to symmetry after the hardening treatment. It is well known that such grinding adversely affects tool life.
  • high-carbon M high speed steel was used in accordance with the present invention in the manufacture of'bars from 3 to 6 inches in diameter, which are of the type used extensively for conventional gear hobs and special end mill cutters.
  • the composition of the steel from which these bars were made as well as that of a commercial 5-inch diameter bar used for comparison purposes is presented in Table III:
  • Table IV describes the preparation of the metal parby a milling operation, gear teeth, spline keys and the 40 ticles and vacuum hot-pressing cycles for the compacts like.
  • the cutting action is achieved by rotating the hob While feeding the same into the workpiece.
  • the compacts identified as 29958 and 30054 in Tables III and IV had a hardness after compacting of 32 R
  • the annealing cycles used these samples as well as the conventional sample 6l338 was a full anneal at 1600 F., furnace cooled at 25 F. per hour to 1200 F. and air cooled to room temperature.
  • the annealed microstructures of the 5-inch diameter compacts have a fine, even distribution of residual carbides edge-to-center.
  • the sample 61-33 8 which represents commercial product, shows extremely heavy segregation of relatively larger residual carbides at its mid-radius location. It is obvious from a comparipresence of increased section size.
  • Test specimens cut radially from 5 inch diameter slice of bars 61-338 and compact 300-54.
  • FIGS. 1A and 1B son of FIGS. 1A and 1B with FIG. 2 that the carbides formed during cooling are noticeably finer in the powder compacts in accordance with the present invention than in the commercial product.
  • This favorable carbide size and distribution of the compact in accordance with the present invention allows it to be heat treated with shorter austenitizing times to achieve full hardness than is the case with commercial material.
  • FIG. 3 shows the effect of austenitizing times at 2200 F. on the as-tempered hardness of the compact of the invention and commercial product. Tempering was effected at 1025 F. for 2+2+2 hours.
  • M2S tool samples were heat treated (2200 F. for 4 minutes, oil quenched, tempered at 1050" F. for 2+2 hours), surface ground on all sides and then standard tool tip geometry applied to one end.
  • Table IX lists the as-quenched grain size, average residual carbide size and the hardness after oil quenching from 2200 F. minute to 4 minutes at temperature) and tempering at 1025" F. for 2+2+2 hours. It may be (expressed in number impacts on the unsupported slot edges) is as follows:
  • the ratio of average tool life of the product of the invention to that of a conventional tool is 2.5 to 1.
  • composition of said metal body consists of, in percent, 0.80 to 3.00 carbon, up to 2 manganese, up to 1 silicon, up to 0.5 sulfur, up to 18.0 tungsten, up to 10.0 chromium, up to 12 molybdenum, up to 5 vanadium, up to 12 cobalt and balance iron, with tungsten+molybdenum+chromium +vanadium being equal to at least 10 percent.
  • composition of said metal body consists of, in percent, 0.97 to 1.02 carbon, 0.20 to 0.40 manganese, 0.20 to 0.40 silicon, 0.10 to 0.15 sulfur, 6 to 6.5 tungsten, 4 to 4.5 chromium, 4.75 to 5.25 molybdenum, 1.8 to 2.20 vanadium and balance iron, said article being characterized by a hardness after hardening treatment of at least 64 R 4.
  • said compacted particles are of a metal composition consisting of, in percent, 0.97 to 1.02 carbon, 0.20 to 0.40 manganese, 0.20 to 0.40 silicon, 0.10 to 0.15 sulfur, 6 to 6.5 tungsten, 4 to 4.5 chromium, 4.75 to 5.25 molybdenum, 1.8 to 2.20 vanadium, and balance iron, said hob having a hardness of at least 64 R 6.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
US666776A 1967-09-11 1967-09-11 Sintered steel particles containing dispersed carbides Expired - Lifetime US3561934A (en)

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US66677667A 1967-09-11 1967-09-11

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US (1) US3561934A (zh)
JP (1) JPS6238402B1 (zh)
DE (1) DE1758626A1 (zh)
FR (1) FR1573501A (zh)
GB (1) GB1237244A (zh)

Cited By (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3715792A (en) * 1970-10-21 1973-02-13 Chromalloy American Corp Powder metallurgy sintered corrosion and wear resistant high chromium refractory carbide alloy
US4121927A (en) * 1974-03-25 1978-10-24 Amsted Industries Incorporated Method of producing high carbon hard alloys
DE2846122A1 (de) * 1977-10-27 1979-05-03 Nippon Piston Ring Co Ltd Legierung zur herstellung von gleitelementen fuer antriebsmaschinen
DE3001761A1 (de) * 1979-05-03 1980-11-13 Crucible Inc Pulvermetallurgisch hergestellter vanadiumhaltiger wolfram-hochgeschwindigkeitsstahl
US4365997A (en) * 1979-05-15 1982-12-28 Fried. Krupp Gesellschaft Mit Beschrankter Haftung Wear resistant compound material, method for manufacturing it and use of such compound material
US4469514A (en) * 1965-02-26 1984-09-04 Crucible, Inc. Sintered high speed tool steel alloy composition
US4576642A (en) * 1965-02-26 1986-03-18 Crucible Materials Corporation Alloy composition and process
US4667497A (en) * 1985-10-08 1987-05-26 Metals, Ltd. Forming of workpiece using flowable particulate
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
US5290507A (en) * 1991-02-19 1994-03-01 Runkle Joseph C Method for making tool steel with high thermal fatigue resistance
US20090303590A1 (en) * 2008-06-06 2009-12-10 Canon Kabushiki Kaisha Optical filter and imaging apparatus
CN110157938A (zh) * 2019-05-15 2019-08-23 左其福 利用难熔金属废旧硬质合金直接制造硬质合金类材料的方法
WO2020084352A1 (en) * 2018-10-26 2020-04-30 Erasteel Sas A method of producing a high speed steel alloy

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3809541A (en) * 1972-10-24 1974-05-07 G Steven Vanadium-containing tool steel article
JPS57181367A (en) * 1981-04-08 1982-11-08 Furukawa Electric Co Ltd:The Sintered high-v high-speed steel and its production
SE446277B (sv) * 1985-01-16 1986-08-25 Kloster Speedsteel Ab Vanadinhaltigt verktygsstal framstellt av metallpulver och sett vid dess framstellning
DE3507332A1 (de) * 1985-03-01 1986-09-04 Seilstorfer GmbH & Co Metallurgische Verfahrenstechnik KG, 8092 Haag Stahlmatrix-hartstoff-verbundwerkstoff
JPH02105503U (zh) * 1989-02-07 1990-08-22
GB9500503D0 (en) * 1995-01-11 1995-03-01 Saveker Jonathan J High speed cutting tool

Cited By (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4469514A (en) * 1965-02-26 1984-09-04 Crucible, Inc. Sintered high speed tool steel alloy composition
US4576642A (en) * 1965-02-26 1986-03-18 Crucible Materials Corporation Alloy composition and process
US3715792A (en) * 1970-10-21 1973-02-13 Chromalloy American Corp Powder metallurgy sintered corrosion and wear resistant high chromium refractory carbide alloy
US4121927A (en) * 1974-03-25 1978-10-24 Amsted Industries Incorporated Method of producing high carbon hard alloys
DE2846122A1 (de) * 1977-10-27 1979-05-03 Nippon Piston Ring Co Ltd Legierung zur herstellung von gleitelementen fuer antriebsmaschinen
DK156076B (da) * 1979-05-03 1989-06-19 Colt Ind Operating Corp Anvendelse af et koboltfrit hurtigstaal til skaerevaerktoej.
DE3001761A1 (de) * 1979-05-03 1980-11-13 Crucible Inc Pulvermetallurgisch hergestellter vanadiumhaltiger wolfram-hochgeschwindigkeitsstahl
US4276087A (en) * 1979-05-03 1981-06-30 Crucible Inc. Powder-metallurgy vanadium-containing tungsten-type high-speed steel
US4365997A (en) * 1979-05-15 1982-12-28 Fried. Krupp Gesellschaft Mit Beschrankter Haftung Wear resistant compound material, method for manufacturing it and use of such compound material
US4667497A (en) * 1985-10-08 1987-05-26 Metals, Ltd. Forming of workpiece using flowable particulate
US4853178A (en) * 1988-11-17 1989-08-01 Ceracon, Inc. Electrical heating of graphite grain employed in consolidation of objects
US4933140A (en) * 1988-11-17 1990-06-12 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
US5290507A (en) * 1991-02-19 1994-03-01 Runkle Joseph C Method for making tool steel with high thermal fatigue resistance
US20090303590A1 (en) * 2008-06-06 2009-12-10 Canon Kabushiki Kaisha Optical filter and imaging apparatus
WO2020084352A1 (en) * 2018-10-26 2020-04-30 Erasteel Sas A method of producing a high speed steel alloy
EP3870730A4 (en) * 2018-10-26 2022-07-20 Erasteel SAS PROCESS FOR THE PRODUCTION OF A HIGH SPEED STEEL ALLOY
CN110157938A (zh) * 2019-05-15 2019-08-23 左其福 利用难熔金属废旧硬质合金直接制造硬质合金类材料的方法

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Publication number Publication date
FR1573501A (zh) 1969-07-04
DE1758626A1 (de) 1972-04-06
JPS6238402B1 (zh) 1987-08-18
GB1237244A (en) 1971-06-30

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