EP2010687B1 - Corps en métal dur et procédé de son production - Google Patents

Corps en métal dur et procédé de son production Download PDF

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Publication number
EP2010687B1
EP2010687B1 EP07724394.7A EP07724394A EP2010687B1 EP 2010687 B1 EP2010687 B1 EP 2010687B1 EP 07724394 A EP07724394 A EP 07724394A EP 2010687 B1 EP2010687 B1 EP 2010687B1
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Prior art keywords
phase
sintering
metals
mass
carbon
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EP07724394.7A
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German (de)
English (en)
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EP2010687A2 (fr
Inventor
Walter Lengauer
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TUTEC GmbH
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TUTEC GmbH
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Classifications

    • 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
    • C22C29/06—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 based on carbides, but not containing other metal compounds
    • C22C29/08—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 based on carbides, but not containing other metal compounds based on tungsten carbide
    • 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
    • C22C1/053—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor with in situ formation of hard compounds
    • 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
    • B22F3/10—Sintering only
    • B22F3/1003—Use of special medium during sintering, e.g. sintering aid
    • B22F3/1007—Atmosphere
    • 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
    • B22F3/12—Both compacting and sintering
    • B22F3/14—Both compacting and sintering simultaneously
    • B22F3/15—Hot isostatic pressing
    • 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
    • B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
    • B22F2005/001—Cutting tools, earth boring or grinding tool other than table ware
    • 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
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy

Definitions

  • the invention relates to the method defined in the claims for producing a cemented carbide body with a uniform structure, with a single- or multi-phase hard material phase
  • the invention further relates to the carbide body defined in the claims.
  • the grain size of hard metal bodies and their distribution in the hard metal are determined by many factors, including the starting materials, the composition and the production conditions, in particular the grinding and the sintering temperature.
  • the carbon balance of the hard metal approach plays a significant role.
  • a lower growth tendency is generally observed than for carbides with stoichiometric or superstoichiometric carbon content.
  • Additions of tantalum, vanadium, chromium or even titanium carbide can serve as Kom growth inhibitors for WC.
  • the grain size and in particular the grain size distribution of a hard metal has a great influence on the mechanical properties.
  • coarse-grained WC-Co hard metals are generally tougher than fine-grained ones Wear resistance and hardness for it is higher. Mixed crystal phases in multi-carbide alloys can be used to improve toughness.
  • additional carbides such as VC, Cr 3 C 2 , TaC, NbC, (Ta, Nb) C, or TiC
  • the additional carbides are added either in the form of a WC pre-doped with additional carbides or during the production of the hard metal batch, ie during mixing and grinding.
  • the aim is a uniform distribution of additional carbides as possible.
  • the mixture produced represents a mixture of WC and the additional carbides, which, however, is still inhomogeneous.
  • the additional carbides can not be incorporated into the crystal lattice of the WC on this production route.
  • WC agglomerates pose a particular problem, since these agglomerates are difficult to break up by grinding and thus the additional carbides are distributed irregularly on the WC crystallites and do not reach all crystallite surfaces. This leads to an undesirable inhomogeneous grain growth of the cemented carbide.
  • the US-A 4,649,084 describes a method for improving the adhesion of an oxide coating to a WC-based substrate having a composition of WC, Co and at least one carbide, nitride or carbonitride of titanium and at least one carbide, nitride or carbonitride of tantalum, niobium or mixtures thereof.
  • the substrate body is to be sintered in gaseous nitrogen at a temperature at or above the melting point of the cobalt phase for a sufficiently long period of time to cause the formation of a B1-phase enriched layer on the surface of the sintered substrate. Subsequently, the surface of the substrate is oxidized before the oxide wear layer is applied.
  • the present invention is based on the idea that the hard metal is produced by reactive sintering a powder mixture containing a W-Co-C phase in the form that the additional carbides incorporated in the crystal lattice of the W-Co-C phase, that is dissolved are or is homogeneously alloyed with these metals.
  • solubility of the ternary subcarbide for doping carbides is given to a suitable Total doping level to achieve in the finished sintered carbide.
  • additional carbides can be incorporated in a uniform distribution.
  • the hard metal is formed by reactive sintering of a batch of a corresponding powder, for example W 9 CO 3 C 4 together with carbon, which after the phase reaction W 9 CO 3 C 4 + 5C ⁇ 9 WC + 3 Co responding.
  • This cemented carbide has about 9 mass% Co when no additional phases are incorporated.
  • the additional carbides are not included in the above reaction equation;
  • the metals of the additional carbides are in W 9 Co 3 C 4 as well as in all other W-Co-C phases either at the position of the W atoms and / or Co atoms in which these metals are substituted, or they are installed at other point locations in the crystal lattice.
  • these metals can be deposited as free carbides in the cemented carbide, optionally on WC crystallites and / or they are dissolved in the binder phase.
  • the metals of the additional carbides are incorporated into the unit cell of the ternary phases, they are already present at the points where WC forms in the ternary W-Co-C phase by reactions with carbon, in accordance with the above reaction equation
  • the metals are separated by a distance of less lattice planes so that they occur in the best possible distribution.
  • an optimum effect of the doping carbides is achieved not only with respect to the inhomogeneous grain growth to be suppressed, but also ensures economical use since the doping carbides are added only to the extent necessary.
  • an overdoping of such additional carbides in the hard metal and thus embrittlement of the hard metal can thus be prevented.
  • a starting powder which not only has pure W-Co-C phases to which a growth inhibitor such as Cr 3 C 2 is added, but from the outset an alloyed W-Co-C Phase used in which individual tungsten or cobalt atoms by Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, Ni, Fe, Sc, Y, La, Ce, Re, Ru, Rh, Pt such that these metals are contained in a ternary W-Co-C phase in dissolved form.
  • the growth inhibitors are located in the same lattice as the tungsten, which reacts with WC in the presence of carbon.
  • At least one of the metals Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, of which in particular V, Cr or Ta, and at least one of the metals Sc, Y, La, Ce, Re, Ru, Rh, Pt are preferred contained in dissolved form.
  • the starting mixture contains an amount of said ternary W-Co-C phase which corresponds to at least 10% by volume of the WC-sintered cemented carbide body.
  • the carbon necessary for the reaction sintering can be added to the batch in solid form as graphite, carbon black or another carbon modification (carbon nanotubes, Buckminster fullerenes) or in the form of another organic or inorganic carbon donor.
  • carbon nanotubes carbon nanotubes, Buckminster fullerenes
  • a part of the carbon required for reactive sintering is added by gas phase treatment with a carbon-containing gas in the pre-sintering or sintering process.
  • the desired total composition, in particular the 10 vol % of alloyed ternary phase corresponds, with at least two of the metals Ti, Zr, Hf, V, Nb, Ta, Cr, Mo or at least two oxides, carbides, oxicarbides, carbonitrides or oxicarbonitrides of these metals or an organic compound of these metals such Acetate, oxalate or citrate or another inorganic compound such as a fluoride or chloride and mixed by subsequent annealing in bulk or compressed form at temperatures up to a maximum of 1900 ° C for up to 168 hours under vacuum, inert gas, C-containing Treated gases or hydrogen.
  • the starting mixture can be processed by reaction with carbon either by C-containing gases and / or by addition of carbon in solid form to a powder of the composition WC + Co + doping carbides by a controlled temperature control, preferably in a corresponding total composition necessary for the carbide to be produced ,
  • known sintering cycles which are tuned to a controlled uniform nucleation of the WC during heating, can be used, wherein the temperature is kept constant in the heating phase, the cooling phase and / or after reaching the maximum sintering temperature in hold times over periods ⁇ 5 min or the temperature change is reduced.
  • the starting mixture may additionally contain Al. The same applies to the powders according to claims 9 to 11 as explained for the above method.
  • End product is a hard metal body with a hard material phase of 60 to 100% by mass of WC (proportion of the hard material phase), up to 40% by mass (proportion of the hard material phase ) of a carbide, nitride, carbonitride or oxycarbonitride of at least one of the metals Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, wherein at least 10% by volume of the WC have been formed by reaction of a ternary W-Co-C phase with carbon and this ternary phase before sintering at least two of the metals Ti, Zr, Hf , V, Nb, Ta, Cr, Mo, Fe, Ni, Sc, Y, La, Ce, Re, Ru, Rh, Pt in dissolved form and a binder phase of 4-20 mass% (hard metal content) of Co or Co with up to 50 mass% (proportion of the binder phase) Fe, Ni and / or Cr.
  • Nitrogen may also be present in bound form in the powdery starting mixture, in particular as nitride or carbonitride. This nitrogen has a further refining effect in the further production of the cemented carbide body in the finished product.
  • the solubility limit for V, Ta and Cr in addition to tungsten carbide, tungsten and cobalt powder, tantalum, vanadium and chromium carbide powder, 0.9 mass% Ta, 0, 4% by mass of VC and 0.4% by mass of Cr 3 C 2 are weighed into a mixture of the formula (W, Ta, V, Cr) 2.51 Co 0.82 C, homogenized in the planetary ball mill in cyclohexane for 20 minutes by means of carbide grinding bodies and ground. After drying, cylindrical molds were pressed at a pressure of 150 MPa and placed in a graphite crucible.
  • tungsten carbide, tungsten, cobalt, tantalum carbide, vanadium carbide and chromium carbide powder were weighed in Ta content based on the total Weighing 0.9% by mass and the V and Cr content in each case 0.4% by mass.
  • the powders were homogenized in the planetary ball mill in cyclohexane for 20 minutes using carbide grinding media and ground.
  • the dried and sieved powder mixture was placed in a molybdenum boat under a hydrogen atmosphere at a rate of 5 ° C / min heated to 1350 ° C and held the temperature there for 100 min. The cooling rate was initially 12 ° C / min, from 800 ° C 3 ° C / min.
  • the result was a X-ray single-phase powder of (W, Ta, V, Cr) 2.51 Co 0.82 C.
  • tungsten carbide, tungsten and cobalt powders, tantalum, vanadium and chromium carbide powders and yttrium nitride 0.6 mass% TaC, 0.3 Mass% VC, 0.3 mass% Cr 3 C 2 and 0.1 mass% YN, again using the general formula (W, Ta, V, Cr, Y) 2.51 Co 0.82 C.
  • YN donates Y by elimination of nitrogen, which dissolves as well as V, Ta, and Cr in the alloyed subcarbide phase.
  • This mixture was homogenized in the planetary ball mill in cyclohexane for 20 minutes using HarlmetallmahlSystemn and ground.
  • the dried and sieved powder mixture was heated in a molybdenum boat under hydrogen atmosphere at 5 ° C / min to 1350 ° C and held the temperature there for 100 min.
  • the cooling curve was initially 12 ° C / min, from 800 ° C 3 ° C / min.
  • Example 1 Sintering hard metals with carbon black addition, Example 1
  • cylindrical molds were pressed at a pressure of 150 MPa, placed in a graphite crucible, and heated to 1280 ° C under vacuum at a rate of 5 ° C / min. The temperature was held there for 30 min and added 20 mbar Ar as protective gas at the end of this holding plateau. It was then heated at a rate of 5 ° C / min to 1400 ° C and cooled at a holding plateau of 30 min at a rate of 5 ° C / min.
  • cylindrical molds were pressed at a pressure of 150 MPa, placed in a graphite crucible and heated under vacuum at 1290 ° C at a rate of 5 ° C per minute. The temperature was held there for 30 min and at the end of this holding plateau 20 mbar Ar was added as a protective gas. It was then heated at a rate of 5 ° C / min to 1450 ° C and cooled to a holding plateau of 45 min at a rate of 5 ° C per minute.
  • a homogeneous cubic phase Ti, Ta, Nb, Cr, W, V
  • the atmosphere was pumped to a rotary pump vacuum (about 0.01 mbar) and then filled to 100 mbar Ar. It was then heated at a rate of 5 ° C / min to 1400 ° C and cooled at a holding plateau of 30 min at a rate of 5 ° C / min.
  • the improved characteristics are due to a more uniform hard metal structure resulting from a uniform distribution of the grain growth inhibiting metals V, Ta and / or Cr.
  • the significantly improved properties are due to the uniform distribution of Co, which originates entirely from the subcarbide in the cited embodiments. Only by using alloyed subcarbide phases in the approach, this distribution is ideal, since W, Co and the grain growth inhibitors are dissolved in the same crystal lattice of the precursor.
  • the addition of rare earth elements such as Y additionally increases the connection of the interfaces of the WC to Co.
  • the use of nitrogen already in the heating phase and even in the presence of the open-pore structure of the green compacts additionally refines the hard metal structure. This indicates a solution of nitrogen in the alloyed subcarbide phases, which can already be achieved in powder production.
  • Tungsten carbide, tungsten, cobalt, tantalum carbide, vanadium carbide and chromium carbide powders having average grain sizes in the range of 0.6-1.7 microns were weighed into a powder of total composition Co 0.82 (W 2.4 Ta 0.02 V 0.04 Cr 0.04 ) 2.51 C.
  • the starting mixture was homogenized in the planetary ball mill in cyclohexane for 20 min and ground.
  • the dried and sieved powder mixture was heated in a molybdenum boat under hydrogen atmosphere at 5 ° C / min to 1350 ° C and held the temperature there for 100 min. Up to 800 ° C was cooled at 11 ° C / min, then at 3 ° C / min.
  • soot was weighed to obtain a stoichiometric amount of carbon, this mixture was homogenized and ground in the planetary ball mill in hard metal grinding bowls using tungsten carbide balls in cyclohexane for 20 minutes. After drying and granulation were washed with a Pressure of 150 MPa cylindrical molds pressed in a carbide die placed in a graphite crucible.
  • the hardness HV30 of this cemented carbide was 1690 and the fracture toughness according to Palmqvist / Shetty was 10.6 MPa.m -1/2 .
  • Tungsten carbide, tungsten, cobalt, tantalum carbide, vanadium carbide and chromium carbide powders of average grain sizes in the range 0.6-1.7 microns were weighed into a powder of total composition Co 0.82 (W 2.42 V 0.04 Cr 0.04 ) 2.51 C.
  • the mixture of the starting powders was homogenized in the planetary ball mill in cyclohexane for 20 min and ground.
  • the dried and sieved powder mixture was heated in a molybdenum boat under hydrogen atmosphere at 5 ° C / min to 1350 ° C and held the temperature there for 100 min. Up to 800 ° C was cooled at 11 ° C / min, then at 3 ° C / min.
  • carbon black was weighed to a theoretical (W, Cr, V) / C ratio of 0.94, homogenized and ground in the planetary ball mill in hard metal grinding jars using hard metal balls in cyclohexane for 20 minutes.
  • cylindrical molds were pressed in a carbide die at a pressure of 150 MPa and placed in a graphite crucible.
  • the green compacts were heated at 5 ° C / min to 930 ° C. There, a holding plateau of 45 min was inserted and then also heated at 5 ° C / min to 1280 ° C on.
  • the temperature was maintained for 30 min and then 20mbar argon added as a protective gas.
  • the hardness HV30 of this cemented carbide was 1430 and the fracture toughness according to Palmqvist / Shetty 15.5 MPa.m -1/2 .

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Claims (12)

  1. Procédé de fabrication d'un corps en métal dur ayant une structure dont les cristallites de WC anisotropes représentent moins de 20 % du nombre total des cristallites de WC,
    - avec une phase de substance dure qui contient entre 60 % en masse et 100 % en masse de WC, jusqu'à 40 % en masse d'un carbure, nitrure, carbonitrure ou oxycarbonitrure libre de l'un des éléments Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, et
    - avec une phase liant en Co ou en Co et jusqu'à 50 % en masse de Ni, Fe ou Cr, qui possède une part comprise entre 4 et 20 % en masse à l'ensemble du métal dur,
    dans lequel on compose un mélange initial pulvérulent correspondant à la composition souhaitée et on soumet celui-ci à un frittage réactif en présence de carbone,
    caractérisé par le fait que ledit mélange initial pulvérulent comprend au moins une phase W-Co-C en principe ternaire dans laquelle sont contenus, sous forme dissoute, au moins deux des métaux Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, Ni, Fe, Sc, Y, La, Ce, Re, Ru, Rh, Pt.
  2. Procédé selon la revendication 1, caractérisé par le fait que l'un des métaux Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, de préférence V, Cr ou Ta, et au moins l'un des métaux Sc, Y, La, Ce, Re, Ru, Rh, Pt sont contenus sous forme dissoute et/ou que ledit mélange initial contient une quantité de ladite phase W-Co-C en principe ternaire, qui correspond à au moins 10 % volumétrique du WC dans le corps fritté en métal dur.
  3. Procédé selon la revendication 1 ou 2, caractérisé par le fait que le carbone nécessaire au frittage réactif est ajouté à la préparation sous forme solide en graphite, suie ou une autre modification de carbone ou un autre donneur organique ou inorganique de carbone ou de mélanges des substances précitées, et/ou qu'une partie du carbone nécessaire au frittage réactif est ajoutée lors du processus de pré-frittage ou de frittage, par traitement en phase gazeuse avec un gaz carboné.
  4. Procédé selon l'une quelconque des revendications 1 à 3, caractérisé par le fait que, pour la réalisation de ladite phase W-Co-C en principe ternaire dans le mélange initial, on mélange une sélection de W, WC, W2C, oxydes de tungstène, Co, WxCoy et C qui correspond à la composition souhaitée, en particulier à la part de 10 % volumétrique en phase W-Co-C ternaire alliée, avec au moins deux des métaux Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, Fe, Ni, Sc, Y, La, Ce, Re, Ru, Rh, Pt ou au moins deux oxydes, carbures, oxycarbures, carbonitrures ou oxycarbonitrures de ces métaux ou deux composés organiques de ces métaux, tels que l'acétate, l'oxalate ou le citrate, ou un autre composé inorganique, tel qu'un fluorure ou un chlorure, ou au moins deux des métaux précités sont contenus sous forme dissoute, et on la traite en vrac ou sous forme compactée par recuit subséquent à des températures allant jusqu'à 1900 °C au maximum, pour une durée allant jusqu'à 168 heures, sous vide, gaz protecteur, gaz carbonés ou hydrogène, de préférence de telle sorte que le mélange initial soit converti par une gestion contrôlée de température, par des réactions avec du carbone, que ce soit par des gaz carbonés et/ou par addition de carbone sous forme solide, en une poudre de la composition WC + Co + carbure de dopage ou en une poudre WC + Co(Me), où Co(Me) signifie un alliage Co de deux au moins des éléments Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, Fe, Ni, Sc, Y, La, Ce, Re, Ru, Rh, Pt, de préférence dans une composition totale nécessaire correspondant au métal dur à produire.
  5. Procédé selon l'une quelconque des revendications 1 à 4, caractérisé par le fait que de l'azote est présent sous forme liée, en particulier en tant que nitrure ou carbonitrure, dans le mélange initial pulvérulent.
  6. Procédé selon l'une quelconque des revendications 1 à 5, caractérisé par le fait que durant le frittage, dans la phase d'échauffement, dans la phase de refroidissement et/ou après avoir atteint la température maximale de frittage, la température est maintenue constante ou le changement de température est réduit dans des temps de palier sur des espaces de temps supérieurs ou égaux à 5 minutes.
  7. Procédé selon l'une quelconque des revendications 1 à 6, caractérisé par le fait que ledit mélange initial contient en sus de l'Al.
  8. Procédé selon l'une quelconque des revendications 1 à 7, caractérisé par le fait que le frittage est mis en oeuvre en appliquant des cycles de frittage sous vide conventionnels, des cycles de frittage à atmosphère réductrice ou atmosphère de gaz protecteur, ou des cycles de frittage HIP conventionnels, jusqu'à des températures de 1500 °C, dans lequel on observe des taux d'échauffement et de refroidissement de 2 à 15 °C/min. et dans lequel la plage de température allant de 1100 à 1350 °C peut comprendre au moins une section isotherme de température d'une durée de 10 à 100 minutes, lors de l'échauffement.
  9. Procédé selon l'une quelconque des revendications 1 à 8, caractérisé par l'application de cycles de frittage jusqu'à des températures de 1500 °C qui sont accordés au frittage réactif de telle manière que l'on tienne compte d'une germination de WC homogène contrôlée ou d'une décomposition contrôlée de la phase W-Co-C lors de l'échauffement de telle manière que la section du cycle de frittage où se décompose la phase de sous-carbure, de préférence dans la plage comprise entre 750 et 1100 °C, soit parcourue à un taux d'échauffement inférieur à 2 °C/min., de préférence avec 0,1 à 2 °C/min., ou que l'on y règle un ou plusieurs temps de palier supplémentaire(s), de préférence d'une durée comprise entre 10 minutes et 2 heures.
  10. Procédé selon l'une quelconque des revendications 1 à 9, caractérisé par le fait que l'on ajoute à la préparation, outre la poudre ternaire alliée selon les revendications 4 à 6, une part supplémentaire de l'un au moins des métaux Al, Co, Ni, Fe, Sc, Y, La, Ce, Re, Ru, Rh, Pt ou d'un carbure, oxyde, carbonitrure ou oxycarbonitrure des métaux Al, Co, Ni, Fe, Sc, Y, La, Ce, Re, Ru, Rh, Pt.
  11. Procédé selon l'une quelconque des revendications 1 à 10, caractérisé par le fait que le frittage est mis en oeuvre en utilisant une atmosphère d'azote ou une atmosphère azotée, de préférence à une pression de 1 à 7 x 104 Pa, de préférence dans la plage comprise entre 800 et 1200 °C où se produit la réaction de phase solide de la phase W-Co-C et que, ainsi, cette réaction et le bilan de carbone du métal dur peuvent être influencés.
  12. Corps en métal dur comprenant une phase liant de 4 à 20 % en masse, qui contient de préférence du Co ou du Co et jusqu'à 50 % en masse, en particulier entre 0,5 et 50 % en masse de Fe, Ni et/ou de Cr, ainsi qu'une phase de substance dure qui contient jusqu'à 40 % en masse, de préférence entre 5 % en masse et 25 % en masse d'un carbure, nitrure, carbonitrure ou oxycarbonitrure de l'un au moins des métaux Ti, Zr, Hf, V, Ta, Cr, Mo, reste WC, caractérisé par le fait que 10 % volumétrique au moins du WC étaient produits par réaction d'une phase W-Co-C en principe ternaire avec du carbone, cette phase W-Co-C ternaire contenant, avant le frittage, au moins deux des métaux Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, Fe, Ni, Sc, Y, La, Ce, Re, Ru, Rh, Pt sous forme dissoute.
EP07724394.7A 2006-04-24 2007-04-20 Corps en métal dur et procédé de son production Not-in-force EP2010687B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102006018947A DE102006018947A1 (de) 2006-04-24 2006-04-24 Verfahren zur Herstellung eines Hartmetallkörpers, Pulver zur Herstellung eines Hartmetalls und Hartmetallkörper
PCT/EP2007/003457 WO2007121931A2 (fr) 2006-04-24 2007-04-20 Procédé de production d'un corps en métal dur, poudre servant à la production d'un métal dur et corps en métal dur

Publications (2)

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EP2010687A2 EP2010687A2 (fr) 2009-01-07
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EP2010687A2 (fr) 2009-01-07
DE102006018947A1 (de) 2007-10-25
WO2007121931A2 (fr) 2007-11-01

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