EP0330913A2 - Procédé de préparation d'un métal dur fritté et métal dur fritté ainsi obtenu - Google Patents

Procédé de préparation d'un métal dur fritté et métal dur fritté ainsi obtenu Download PDF

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Publication number
EP0330913A2
EP0330913A2 EP89102623A EP89102623A EP0330913A2 EP 0330913 A2 EP0330913 A2 EP 0330913A2 EP 89102623 A EP89102623 A EP 89102623A EP 89102623 A EP89102623 A EP 89102623A EP 0330913 A2 EP0330913 A2 EP 0330913A2
Authority
EP
European Patent Office
Prior art keywords
aluminum
nitride
carbide
added
hard metal
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP89102623A
Other languages
German (de)
English (en)
Other versions
EP0330913B1 (fr
EP0330913A3 (en
Inventor
Hans Kolaska
P. Prof. Dr. Ettmayer
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Widia GmbH
Original Assignee
Krupp Widia GmbH
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Krupp Widia GmbH filed Critical Krupp Widia GmbH
Priority to AT89102623T priority Critical patent/ATE89329T1/de
Publication of EP0330913A2 publication Critical patent/EP0330913A2/fr
Publication of EP0330913A3 publication Critical patent/EP0330913A3/de
Application granted granted Critical
Publication of EP0330913B1 publication Critical patent/EP0330913B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • 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
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy

Definitions

  • titanium carbide and titanium carbonitride hard metal can only be used to a limited extent as cutting tools, especially at high cutting speeds and with cyclical thermal loads (such as during milling); under the effect of the high temperatures occurring at the cutting edge, the binder metal loses its strength and tends to undergo plastic deformation under the influence of the cutting forces.
  • the significantly lower thermal conductivity of TiC-Mo, Ni and Ti (C, N) -Mo, Ni hard metals compared to tungsten carbide leads to heat build-up, especially at the most stressed point.
  • Aluminum-containing complex carbides or complex nitrides should preferably be used, furthermore those complex carbides or complex nitrides which contain substances which have the same or similar effects to aluminum.
  • the substances NbCrN, TaCrN, V5Si3N 1-x , Mo5Si3C 0.6 offer.
  • aluminum-containing complex carbides and / or nitrides from the family of the H phases and / or Chi phases and / or Kappa phases are used.
  • the aluminum-containing complex carbides and nitrides are produced by reaction of the nitride or carbide of aluminum with the powdery transition metals or by reaction of the nitrides or carbides of the transition metals with aluminum. They become common in the carbide industry Chen crushing methods pulverized and processed with the other alloy components of the hard metal in a conventional manner to a sintered hard metal body - in particular to cutting tools or cutting plates.
  • the aluminum content of the binder metal is between 2 and 8% by mass.
  • the monocarbides and nitrides of the transition metals which form during the reaction of the complex carbides and nitrides with the liquid binder metal are epitaxially deposited on the surface of the hard material particles and completely envelop the hard material particle.
  • sintering temperatures between 1350 ° C and 1550 ° C and sintering times of up to 2 hours, the diffusion rates in the hard material particles are not sufficient to bring about a metallurgical equilibrium between the hard material particle in question and its shell made of monocarbides or nitrides of the transition metals.
  • the sintered hard metal according to the invention combines the favorable properties of the carbides of the transition metals in the peripheral zone, which are readily wettable by the conventional binder metals, with the high wear resistance of the nitrides in the core and, due to the content of titanium and aluminum in the binder metal, has such a high wear resistance that the cutting tools produced therefrom or cutting inserts have significantly improved cutting performance.
  • Another advantage of the hard metal according to the invention is that during the implementation of the complex carbides and -ni tride with the liquid binder metal forming monocarbides and nitrides of the transition metals are epitaxially deposited on the surface of the hard material particles and thus prevent a further change in the hard material core under the effect of the liquid binder metal.
  • the existing carbides and / or mixed carbides and / or nitrides and / or mixed nitrides encased with a diffusion-inhibiting layer thus indicate from their structure that an equilibrium in the metallurgical sense has been avoided between the different hard materials within the hard material particle. This deliberately created imbalance condition results in the abovementioned improved wear resistance - even under extreme working conditions.
  • the conventional hard metal used for comparison (see FIG. 1, left blocks) consists of 57% Tic, 10% TiN, 10% WC, 2% VC, 10% Mo as well as 5.5% Ni and 5.5% Co.
  • the hard metals according to the invention with complex nitride-modified binder metal (cf. the blocks in the middle and on the right-hand side of FIG. 1) were made from the same base material with the addition of 0.6% or 2.2% Ti2AlN while simultaneously reducing the nickel and Cobalt content to 5.2% and 4.4% in a manner known per se; in the sintered hard metal, the associated aluminum content in the binder is about 2 or slightly more than 7%.
  • the milling tests were carried out on a shaft made of tempered steel 42CrMo4 at a cutting speed of 250 m / min; the associated product of depth of cut, chip cross-section and feed per tooth is 1.0 x 120 x 0.1 mm / tooth.
  • the improved wear resistance - which makes the hard metals according to the invention also interesting for other areas of application - is based on the fact that the starting mixture for producing the hard metal or hard metal body is composed in such a way that certain chemical reactions are initiated very quickly at the beginning of the melting of the binding phase, which result in the formation of a diffusion-inhibiting layer around the surface of the hard material particles of the starting mixture.
  • the deliberate selection of the constituents forming the starting powder mixture therefore means that no metallurgical equilibrium can be established in the finished hard metal or hard metal body. This ensures that the optimum properties of the different hard material particles for the intended applications - such as the known wear resistance of the titanium nitride and the known excellent hardness of the titanium carbide - are retained in the finished hard metal.
  • the metallurgical equilibrium which is usually given according to the prior art, these individual properties of the hard material particles according to the invention would at least partially be lost.
  • FIG. 4 shows a table with eight exemplary embodiments for the composition of the starting powder mixture of the hard metal body according to the invention.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Ceramic Products (AREA)
EP89102623A 1988-03-02 1989-02-16 Procédé de préparation d'un métal dur fritté et métal dur fritté ainsi obtenu Expired - Lifetime EP0330913B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT89102623T ATE89329T1 (de) 1988-03-02 1989-02-16 Verfahren zur herstellung eines gesinterten hartmetallkoerpers und gesinterter hartmetallkoerper.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE3806602 1988-03-02
DE3806602A DE3806602A1 (de) 1988-03-02 1988-03-02 Hartmetallkoerper

Publications (3)

Publication Number Publication Date
EP0330913A2 true EP0330913A2 (fr) 1989-09-06
EP0330913A3 EP0330913A3 (en) 1990-06-13
EP0330913B1 EP0330913B1 (fr) 1993-05-12

Family

ID=6348548

Family Applications (1)

Application Number Title Priority Date Filing Date
EP89102623A Expired - Lifetime EP0330913B1 (fr) 1988-03-02 1989-02-16 Procédé de préparation d'un métal dur fritté et métal dur fritté ainsi obtenu

Country Status (7)

Country Link
US (1) US4944800A (fr)
EP (1) EP0330913B1 (fr)
JP (1) JPH0711042B2 (fr)
AT (1) ATE89329T1 (fr)
DD (1) DD279031A5 (fr)
DE (2) DE3806602A1 (fr)
ES (1) ES2054893T3 (fr)

Families Citing this family (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AT392929B (de) * 1989-03-06 1991-07-10 Boehler Gmbh Verfahren zur pulvermetallurgischen herstellung von werkstuecken oder werkzeugen
SE467257B (sv) * 1989-06-26 1992-06-22 Sandvik Ab Sintrad titanbaserad karbonitridlegering med duplexa strukturer
US5552108A (en) * 1990-12-21 1996-09-03 Sandvik Ab Method of producing a sintered carbonitride alloy for extremely fine machining when turning with high cutting rates
SE9004118D0 (sv) * 1990-12-21 1990-12-21 Sandvik Ab Saett foer framstaellning av en sintrad karbonitridlegering foer fin till medelgrov fraesning
SE469386B (sv) * 1990-12-21 1993-06-28 Sandvik Ab Saett att framstaella en sintrad karbonitridlegering foer skaerande bearbetning
SE469384B (sv) * 1990-12-21 1993-06-28 Sandvik Ab Saett att framstaella en sintrad karbonitridlegering foer finfraesning
US5581798A (en) * 1990-12-21 1996-12-03 Sandvik Ab Method of producing a sintered carbonitride alloy for intermittent machining of materials difficult to machine
SE9101385D0 (sv) * 1991-05-07 1991-05-07 Sandvik Ab Sintrad karbonitridlegering med styrd korn- storlek
US5447549A (en) * 1992-02-20 1995-09-05 Mitsubishi Materials Corporation Hard alloy
US5451365A (en) * 1993-05-24 1995-09-19 Drexel University Methods for densifying and strengthening ceramic-ceramic composites by transient plastic phase processing
JPH06346184A (ja) * 1993-06-11 1994-12-20 Hitachi Metals Ltd ベーン用材料およびその製造方法
DE9402109U1 (de) * 1994-02-09 1994-03-31 Maartens Kleinmetaal B.V., Haarlem Rotationsschneidwerkzeug
WO1997027965A1 (fr) * 1996-01-16 1997-08-07 Drexel University Synthese de produits a phases h
US6228484B1 (en) 1999-05-26 2001-05-08 Widia Gmbh Composite body, especially for a cutting tool
US7572313B2 (en) * 2004-05-26 2009-08-11 Drexel University Ternary carbide and nitride composites having tribological applications and methods of making same
US20080035567A1 (en) * 2006-08-08 2008-02-14 Sabottke Craig Y Enhanced membrane separation system
US8778259B2 (en) 2011-05-25 2014-07-15 Gerhard B. Beckmann Self-renewing cutting surface, tool and method for making same using powder metallurgy and densification techniques
US10407757B2 (en) 2013-03-14 2019-09-10 Massachusetts Institute Of Technology Sintered nanocrystalline alloys
US10794210B2 (en) 2014-06-09 2020-10-06 Raytheon Technologies Corporation Stiffness controlled abradeable seal system and methods of making same
US11644288B2 (en) 2015-09-17 2023-05-09 Massachusetts Institute Of Technology Nanocrystalline alloy penetrators
CN114150176A (zh) * 2021-12-02 2022-03-08 常州市博斯特精密机械有限公司 一种抗冲击性能好的钻头生产工艺

Family Cites Families (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2967349A (en) * 1959-06-22 1961-01-10 Ford Motor Co Metallic compositions
US3507682A (en) * 1967-06-19 1970-04-21 Ncr Co Process and apparatus for coating thin film substrates
BE756565A (fr) * 1969-09-30 1971-03-01 Ugine Carbone Alliages durs a base de nitrures
BE794383A (fr) * 1972-02-14 1973-07-23 Teledyne Ind Alliages de carbures pour outils de coupe
US4402744A (en) * 1973-03-12 1983-09-06 Union Carbide Corporation Chemically bonded aluminum coating for carbon via monocarbides
US4347083A (en) * 1973-03-12 1982-08-31 Union Carbide Corporation Chemically bonded aluminum coating for carbon via monocarbides
US3971656A (en) * 1973-06-18 1976-07-27 Erwin Rudy Spinodal carbonitride alloys for tool and wear applications
US3994692A (en) * 1974-05-29 1976-11-30 Erwin Rudy Sintered carbonitride tool materials
US4049876A (en) * 1974-10-18 1977-09-20 Sumitomo Electric Industries, Ltd. Cemented carbonitride alloys
AU501073B2 (en) * 1974-10-18 1979-06-07 Sumitomo Electric Industries, Ltd. Cemented carbonitride alloys
US4019874A (en) * 1975-11-24 1977-04-26 Ford Motor Company Cemented titanium carbide tool for intermittent cutting application
JPS5823457B2 (ja) * 1977-08-11 1983-05-16 三菱マテリアル株式会社 強靭サ−メット
GB2048956B (en) * 1979-03-29 1983-02-16 Sumitomo Electric Industries Sintered compact for a machining tool
GB2063922A (en) * 1979-11-20 1981-06-10 Metallurg Inc Sintered hard metals
GB2070646B (en) * 1980-03-04 1985-04-03 Metallurg Inc Sintered hardmetals

Also Published As

Publication number Publication date
DD279031A5 (de) 1990-05-23
EP0330913B1 (fr) 1993-05-12
DE58904302D1 (de) 1993-06-17
ATE89329T1 (de) 1993-05-15
JPH01294842A (ja) 1989-11-28
JPH0711042B2 (ja) 1995-02-08
DE3806602A1 (de) 1988-07-07
EP0330913A3 (en) 1990-06-13
ES2054893T3 (es) 1994-08-16
DE3806602C2 (fr) 1991-04-04
US4944800A (en) 1990-07-31

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