WO2014122306A2 - Matériau en carbure métallique et son procédé de fabrication - Google Patents

Matériau en carbure métallique et son procédé de fabrication Download PDF

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Publication number
WO2014122306A2
WO2014122306A2 PCT/EP2014/052549 EP2014052549W WO2014122306A2 WO 2014122306 A2 WO2014122306 A2 WO 2014122306A2 EP 2014052549 W EP2014052549 W EP 2014052549W WO 2014122306 A2 WO2014122306 A2 WO 2014122306A2
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WIPO (PCT)
Prior art keywords
cemented carbide
around
carbide material
binder
phase
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PCT/EP2014/052549
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English (en)
Other versions
WO2014122306A3 (fr
Inventor
Igor Yurievich KONYASHIN
Bernd Heinrich Ries
Frank Friedrich Lachmann
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Element Six Gmbh
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Application filed by Element Six Gmbh filed Critical Element Six Gmbh
Priority to CN201480017790.2A priority Critical patent/CN105074029B/zh
Priority to US14/766,114 priority patent/US20150376744A1/en
Priority to JP2015556525A priority patent/JP6275750B2/ja
Priority to EP14703394.8A priority patent/EP2954082B1/fr
Publication of WO2014122306A2 publication Critical patent/WO2014122306A2/fr
Publication of WO2014122306A3 publication Critical patent/WO2014122306A3/fr
Priority to US16/283,129 priority patent/US20190368011A1/en
Priority to US17/222,982 priority patent/US20210222273A1/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B7/00—Working up raw materials other than ores, e.g. scrap, to produce non-ferrous metals and compounds thereof; Methods of a general interest or applied to the winning of more than two metals
    • C22B7/001—Dry processes
    • 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
    • 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
    • C22C29/067—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 comprising a particular metallic binder
    • 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
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
    • C22C2026/006—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes with additional metal compounds being carbides

Definitions

  • This disclosure is related to a cemented carbide material such as for use in high-pressure components for synthesis of diamond or c-BN or fabrication of poly-crystalline diamond or c-BN and a method of making same.
  • cemented carbides employed for high-pressure high-temperature (HPHT) components used for diamond synthesis and production of polycrystalline diamond (PCD), including anvils and dies, are subjected to high pressures, temperatures and loads. Such unfavorable conditions lead to their deformation and, if the deformation exceeds a certain level, the HPHT components fail. In this respect it is very important to have a cemented carbide material with a high level of Young's modulus to reduce the deformation at high pressures and consequently improve the deformation resistance and lifetime of the HPHT components.
  • cemented carbide material for use in the fabrication of high- pressure high-temperature components having improved resistance to deformation as well as high fracture toughness and strength.
  • a cemented carbide material comprising WC, Co and Re, wherein: the cemented carbide material comprises between around 3 to around 10 wt.% Co and between around 0.5 to around 8 wt.% Re;
  • the equivalent total carbon (ETC) content of the cemented carbide material with respect to WC being between around 6.3 wt.% to around 6.9 wt.%
  • the cemented carbide material being substantially free of eta-phase and free carbon.
  • a polycrystalline superhard construction comprising: a substrate comprising the cemented carbide material defined above; and a body of polycrystalline superhard material bonded to the substrate along an interface.
  • a cutter comprising a substrate comprising the cemented carbide material defined above bonded to a body of polycrystalline superhard material adapted for a rotary drill bit for boring into the earth.
  • a PCD element for a rotary shear bit for boring into the earth, for a percussion drill bit or for a pick for mining or asphalt degradation comprising a cutter element comprising a body of superhard polycrystalline material bonded to a body of cemented carbide material as defined above.
  • a drill bit or a component of a drill bit for boring into the earth comprising a PCD element as defined above.
  • a method of producing the cemented carbide material defined above comprising: milling a cemented carbide mixture containing WC and carbon with Re, Co, Ni and/or Fe and optionally grain growth inhibitors comprising one or more of V, Cr, Ta, Ti, Mo, Zr, Nb and Hf or a carbide thereof; pressing the cemented carbide article from the mixture; sintering the article at a temperature of above around 1450°C in vacuum for between around 1 to 10 minutes and a pressure of Ar (HIP) for around 5 to 120 minutes; and cooling the article from sintering the temperature to approximately 1300 degrees Centigrade (°C).
  • HIP pressure of Ar
  • a method of recycling the cemented carbide material defined above comprising melting the carbide material in a protective atmosphere with liquid Zn, evaporating the Zn to form a resultant product; and milling the resulting product to recover Re from the product.
  • a method of recycling the cemented carbide material defined above comprising subjecting the cemented carbide material to an acid leaching mixture to remove the binder phase from the cemented carbide material; and chemically recovering Co and Re from the removed binder phase.
  • a method of recycling the cemented carbide material defined above comprising oxidation of the cemented carbide material to dissolve the carbide, Re and Co, and recovering the Re.
  • a cemented carbide material in a high- pressure component for synthesis of diamond or c-BN, or in fabrication of polycrystalline diamond or c-BN operating at a pressure of above 5 GPa and a temperature of above 1 100°C
  • the cemented carbide material comprises: a carbide of one or more metals in form of the second carbide phase, or dissolved in a binder phase in the material, said one or more metals comprising Ti, V, Cr, Mn, Zr, Nb, Mo, Hf and/or Ta; between around 0.5 to around 8 wt.% Re and between around 3 to around 10 wt.% Co; the equivalent total carbon (ETC) content of the cemented carbide material with respect to WC being between around 6.3 wt.% to around 6.9 wt.%
  • the cemented carbide material being substantially free of eta-phase and free carbon.
  • Figure 1 is an SEM image of a cemented carbide material according to a first example and comprising WC-Co-Re;
  • Figure 2 is an EBSD image of the WC-Co-Re cemented carbide material of Figure 1 ;
  • Figure 3 is an EBSD image showing the microstructure of conventional WC-Co cemented carbide material.
  • ETC equivalent total carbon
  • a "superhard material” is a material having a Vickers hardness of at least about 25GPa. Diamond and cubic boron nitride (cBN) material are examples of superhard materials.
  • a "superhard construction” means a construction comprising polycrystalline superhard material or superhard composite material, or comprising polycrystalline superhard material and superhard composite material bonded to a cemented carbide substrate.
  • polycrystalline diamond is a PCS material comprising a mass of diamond grains, a substantial portion of which are directly inter-bonded with each other and in which the content of diamond is at least about 80 volume percent of the material.
  • interstices between the diamond gains may be at least partly filled with a binder material comprising a catalyst for diamond.
  • interstices or "interstitial regions” are regions between the diamond grains of PCD material.
  • interstices or interstitial regions may be substantially or partially filled with a material other than diamond, or they may be substantially empty.
  • Embodiments of PCD material may comprise at least a region from which catalyst material has been removed from the interstices, leaving interstitial voids between the diamond grains.
  • polycrystalline cubic boron nitride (PCBN) material is a PCS material comprising a mass of cBN grains dispersed within a wear resistant matrix, which may comprise ceramic or metal material, or both, and in which the content of cBN is at least about 50 volume percent of the material.
  • the content of cBN grains is at least about 60 volume percent, at least about 70 volume percent or at least about 80 volume percent.
  • Embodiments of superhard material may comprise grains of superhard materials dispersed within a hard matrix, wherein the hard matrix preferably comprises ceramic material as a major component, the ceramic material preferably being selected from silicon carbide, titanium nitride and titanium carbo-nitride.
  • a cemented carbide material comprises a mass of grains of a hard material comprising a carbide phase and interstices between the hard grains which are filled with a binder material which constitutes the binder phase.
  • the carbide phase is WC and the binder phase comprises an alloy of Co and Re with some W and C dissolved in it.
  • Figure 3 shows, for comparison, a conventional cemented carbide material comprising WC as the carbide phase and Co as the binder phase.
  • the cemented carbide material further comprises a carbide of one or more metals in the form of a second carbide phase or dissolved in the binder phase, the one or more metals comprising Ti, V, Cr, Mn, Zr, Nb, Mo, Hf and/or Ta.
  • the cemented carbide material is substantially free of eta-phase and free carbon.
  • the cemented carbide material comprises between around 0.5 to around 8 wt% Re.
  • the cemented carbide material comprises between around 3 to around 10 wt.% Co.
  • the cemented carbide material comprises between around 0.5 to around 6 wt.% Re.
  • the WC in the cemented carbide material may, for example, have a mean grain size below around 0.6 microns.
  • the equivalent total carbon (ETC) content with respect to WC lies between around 6.3 wt% to around 6.9 wt%.
  • the magnetic properties of the cemented carbide material may be related to important structural and compositional characteristics and is understood to be an indication of the carbon content in the cemented carbide material.
  • the most common technique for measuring the carbon content in cemented carbides is indirectly, by measuring the concentration of tungsten dissolved in the binder to which it is indirectly proportional. The higher the content of carbon dissolved in the binder the lower the concentration of tungsten dissolved in the binder.
  • the magnetic saturation 4 ⁇ or magnetic moment ⁇ of a hard metal, of which cemented tungsten carbide is an example, is defined as the magnetic moment or magnetic saturation per unit weight.
  • the magnetic moment, ⁇ , of pure Co is 16.1 micro-Tesla times cubic metre per kilogram ⁇ T.m 3 /kg), and the induction of saturation, also referred to as the magnetic saturation, 4 ⁇ , of pure Co is 201.9 ⁇ . ⁇ 3 ⁇ .
  • the following formula may be used to relate magnetic saturation, Ms, to the concentrations of W and C in the binder:
  • cemented carbide material have an associated magnetic saturation of at least around 40 percent to around 80 percent of the magnetic saturation of nominally pure Co.
  • the mean grain size of carbide grains may be determined by examination of micrographs obtained using a scanning electron microscope (SEM) or light microscopy images of metallurgically prepared cross-sections of a cemented carbide material body, applying the mean linear intercept technique, for example.
  • the mean size of the WC grains may be estimated indirectly by measuring the magnetic coercivity of the cemented carbide material, which indicates the mean free path of Co intermediate the grains, from which the WC grain size may be calculated using a simple formula well known in the art. This formula quantifies the inverse relationship between magnetic coercivity of a Co-cemented WC cemented carbide material and the Co mean free path, and consequently the mean WC grain size. Magnetic coercivity has an inverse relationship with MFP.
  • the "mean free path" (MFP) of a composite material such as cemented carbide is a measure of the mean distance between the aggregate carbide grains cemented within the binder material.
  • the mean free path characteristic of a cemented carbide material may be measured using a micrograph of a polished section of the material. For example, the micrograph may have a magnification of about 1500x.
  • the MFP may be determined by measuring the distance between each intersection of a line and a grain boundary on a uniform grid.
  • the matrix line segments, Lm are summed and the grain line segments, Lg, are summed.
  • the mean matrix segment length using both axes is the "mean free path". Mixtures of multiple distributions of tungsten carbide particle sizes may result in a wide distribution of MFP values for the same matrix content.
  • the grain sizes are expressed in terms of Equivalent Circle Diameter (ECD) according to the ISO FDIS 13067 standard.
  • ECD Equivalent Circle Diameter
  • the carbide phase of the cemented carbide material is formed of carbide grains having a mean grain size of at least around 0.1 ⁇ to at most around 10 ⁇ and the cemented carbide material may have an associated magnetic coercive force varying from around 2kA/m to around 70 kA/m.
  • the carbide phase comprises WC and the cemented carbide material has a coercive force He in kA/m as a function of the WC mean grain size D wc in ⁇ determined on the basis of EBSD images of the carbide microstructure equal to or less than values given by the equation:
  • the carbide phase comprises WC and the binder phase comprises Co and Re.
  • the binder phase of the cemented carbide material may, for example, be a solid solution of Re, carbon and W and one of more of Fe, Co, and Ni.
  • the binder phase comprises at least about 0.1 weight percent to at most about 5 weight percent of one or more of V, Cr, Ta, Ti, Mo, Zr, Nb and Hf in solid solution and/or in the form of carbide compounds.
  • the material comprises at least about 0.01 weight percent and at most about 2 weight percent of one or more of Ru, Rh, Pd, Os, Ir and Pt.
  • the cemented carbide has an associated hardness and, in some embodiments, the hardness decrease at 300°C is at most 20%, or, in some other embodiments, is at most 17%.
  • Hardness measurements were carried out according to the DIN ISO 3878 on metallurgical cross-sections at a load of 30 kgf at room temperature as well as at 300°C, 500°C and 800°C in an Ar atmosphere. After achieving the elevated temperatures the cross-section was annealed for 10 min, after which a Vickers indentation was made under the load of 30 kgf and the load was applied for 15 sec.
  • the cemented carbide material may, for example, have a hardness decrease at 500°C of at most 30% or, in some other embodiments, at most 27%.
  • the hardness-toughness coefficient may be calculated by multiplying the Vickers hardness in GPa and indentation fracture toughness in MPa m 2 , and, in some embodiments, this is above 150.
  • the cemented carbide material has a Vickers hardness
  • the binder phase of the cemented carbide material has one or more residual compressive stresses and these may, for example, be between around -5 MPa to around 100 MPa.
  • An embodiment of a cemented carbide material may be made by a method including milling a cemented carbide mixture containing carbides with Re, Co, Ni and/or Fe and optionally grain growth inhibitors including V, Cr, Ta, Ti, Mo, Zr,, Nb and Hf or their carbides and then pressing a cemented carbide article from the mixture.
  • the article is then sintered at temperatures of above 1450°C in vacuum for 1 to 10 min and afterwards under pressure of Ar (HIP) for 5 to 120 min.
  • the article is then cooled from the sintering temperatures to approximately 1300 degrees Centigrade (°C) in an atmosphere comprising inert gases, nitrogen, hydrogen or a mixture thereof, or in a vacuum, at a cooling rate of approximately 0.2 to 2 degrees per minute.
  • Tungsten carbide powder wherein the WC grains had an average grain size of about 0.6 ⁇ with carbon content of 6.13 wt.%, was milled with 5.5%Re powder and 3.7%Co powder.
  • the Co grains had an average grain size of about 1 ⁇ .
  • the powder mixture was produced by milling the powders together for 24 hours using a ball mill in a milling medium comprising hexane with 2 wt.% paraffin wax, and using a powder-to-ball ratio of 1 :6. After milling 0.35 wt.% carbon black was added and additional milling was performed for 1 hr resulting in the fact that the equivalent total carbon (ETC) content with respect to WC of the mixture was equal to 6.51 wt.%.
  • ETC equivalent total carbon
  • a control batch of conventional WC-Co cemented carbides without Re was made from the same WC powder batch and 6 wt.% Co, which corresponds to the same volume percentage of binder as in the WC-Co-Re material, without adding carbon black.
  • the batch was milled in the same way as the WC-Co-Re carbide and sintered at 1440°C for 1 hr including 30 sintering vacuum and 30 min sintering under pressure (HIP).
  • the carbon content was measured on sintered samples in the same way as for the WC-Co-Re cemented carbides and found to be equal to 5.77 wt.% providing evidence that the equivalent total carbon (ETC) content with respect to WC is equal to 6.13 wt%.
  • Metallurgical cross-sections of the WC-Co-Re and WC-Co cemented carbides were made and examined by optical microscopy and SEM.
  • the hardness (HV20), indentation fracture toughness (Kic), transverse rupture strength (TRS), compressive strength and Young's modulus as well as coercive force and magnetic moment (saturation) of the sintered bodies were examined.
  • the WC mean grain size was measured on the basis of the EBSD image of the cross-sections according to the procedure described in: K.P. Mingard, B. Roebuck a, E.G. Bennett , M.G. Gee, H. Nordenstrom, G. Sweetman, P. Chan . Comparison of EBSD and conventional methods of grain size measurement of hard metals. Int. Journal of Refractory Metals & Hard Materials 27 (2009) 213-223.
  • Figures 1 and 2 show SEM and EBSD images respectively of the WC-Co-Re cemented carbide formed according to Example 1
  • Figure 3 shows the microstructure of the conventional WC- Co cemented carbides without Re and having the Equivalent Total Carbon content with respect to WC of 6.13 wt.%.
  • the WC-Co-Re carbide shown in Figure 1 and Figure 2 has a WC mean grain size of 0.44 ⁇ . It will be seen that there is neither eta-phase nor free carbon nor porosity in the microstructure of both carbide materials shown in Figures 1 and 2.
  • Table 1 shows the grain size distribution in the microstructure of the WC-Co-Re cemented carbide shown in Figures 1 and 2.
  • the magnetic moment of the WC-Co-Re carbide material of Figure 1 and Figure 2 was equal to 4.7 Gcm 3 /g, which is 64% of the theoretical value for cemented carbide with 3.7 % of nominally pure Co providing evidence for its specific magnetic saturation in per cent (SMS).
  • the hardness-toughness coefficient calculated by multiplying the Vickers hardness in GPa and fracture toughness in MPa m 2 was therefore equal to 195.
  • the compressive strength of the WC-Co-Re cemented carbide was determined to be 6020 MPa and its Young's modules to be equal to 712 GPa. Its hot hardness was found to be equal to 16.9 GPa at 300°C and 14.9 GPa at 500°C providing evidence that the hardness decrease at the elevated temperatures was about 9.1 % and 19.8% correspondingly. The compressive strength almost did not change when increasing the temperatures from room temperature to 300°C and 500°C.
  • the residual stress in the Co-Re binder phase of the WC-Co-Re cemented carbide was measured using a Bruker D8 Discover d iff racto meter using the Cu- ⁇ radiation. This wavelength of X-ray typically obtained diffraction information from a depth of around 5 ⁇ .
  • the diffracted beam was collected using a Braun Position Sensivite Detector with a bin size of 0.01059°.
  • the residual stress measurement was performed by use of the Co (21 1 ) peak at an angle of 146.6° using a step size of 0.01059° and a count time of 10 sec. per step.
  • the residual stress measurements were performed using the standard iso. inclination ⁇ 2 ⁇ technique in accordance with the ref. "Fitzpatrick M, Fry T, Holdway P, et al. NPL Good Practice Guide No. 52: Determination of Residual Stresses by X-ray Diffraction - Issue 2. September 2005".
  • Young's modulus is a type of elastic modulus and is a measure of the uni-axial strain in response to a uni-axial stress, within the range of stress for which the material behaves elastically.
  • a method of measuring the Young's modulus E is by means of measuring the transverse and longitudinal components of the speed of sound through the material using ultrasonic waves.
  • the longitudinal and transverse speeds of sound may be measured using ultrasonic waves, as is well known in the art.
  • the cemented carbide material of one or more embodiments may find particular application in use in high-pressure components for synthesis of diamond or c-BN, or in fabrication of poly- crystalline diamond or c-BN operating at pressures of above 5 GPa and temperatures of above 1 100°C.
  • PCD composite compact elements may comprise a PCD structure bonded along an interface to an embodiment of a cemented carbide substrate comprising particles of a metal carbide and the binder material described above.
  • An embodiment of a PCD composite compact element may be made by a method including providing the cemented carbide substrate, contacting an aggregated, substantially unbonded mass of diamond particles against a surface of the substrate to form an pre-sinter assembly, encapsulating the pre-sinter assembly in a capsule for an ultra-high pressure furnace and subjecting the pre-sinter assembly to a pressure of at least about 5.5 GPa and a temperature of at least about 1 ,250 degrees centigrade, and sintering the diamond particles to form a PCD composite compact element comprising a PCD structure integrally formed on and joined to the cemented carbide substrate.
  • the pre-sinter assembly may be subjected to a pressure of at least about 6 GPa, at least about 6.5 GPa, at least about 7 GPa or even at least about 7.5 GPa.
  • the hardness of cemented tungsten carbide substrate may be enhanced by subjecting the substrate to an ultra-high pressure and high temperature, particularly at a pressure and temperature at which diamond is thermodynamically stable.
  • the magnitude of the enhancement of the hardness may depend on the pressure and temperature conditions.
  • the hardness enhancement may increase the higher the pressure. Whilst not wishing to be bound by a particular theory, this is considered to be related to the Co drift from the substrate into the PCD during press sintering, as the extent of the hardness increase is directly dependent on the decrease of Co content in the substrate.
  • the cemented carbide material forming the substrate may comprise between around 2 to around 9 wt.% Re, and around 3 to around 9 wt.%Co, with the remainder being WC.
  • the working temperature on the surface of the high-pressure components may be at least around 200°C and at most around 800°C.
  • the cemented carbide contains cobalt (Co) and rhenium (Re) and the proportion of Re and Co lies in a certain range it may be possible to improve significantly the Young's modulus of the cemented carbide material.
  • the cemented carbide hot hardness at temperatures dramatically of up to 800°C.
  • the recycling procedure may comprise melting the cemented carbide material in a protective atmosphere with liquid Zn with consequent evaporation of Zn from the mixture, and milling the resulting product.
  • the cemented carbide material may be subjected to an acid leaching treatment to remove the binder phase of the cemented carbide article and chemically recover the Co and Re.
  • a further method of recycling the cemented carbide material may comprise oxidation of the cemented carbides articles with consequent dissolution of carbides, Re and Co and their recovery.

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  • Engineering & Computer Science (AREA)
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Abstract

L'invention porte sur un matériau en carbure métallique comprenant du WC, entre environ 3 et environ 10 % en poids de Co et entre environ 0,5 et environ 8 % en poids de Re. La teneur totale équivalente en carbone (ETC) du matériau en carbure métallique par rapport au WC est comprise entre environ 6,3 % en poids et environ 6,9 % en poids et le matériau en carbure métallique est pratiquement exempt de phase êta et exempt de carbone. L'invention porte également sur un procédé de production d'un tel matériau et sur l'utilisation d'un tel matériau.
PCT/EP2014/052549 2013-02-11 2014-02-10 Matériau en carbure métallique et son procédé de fabrication WO2014122306A2 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
CN201480017790.2A CN105074029B (zh) 2013-02-11 2014-02-10 烧结碳化物材料及其制备方法
US14/766,114 US20150376744A1 (en) 2013-02-11 2014-02-10 Cemented carbide material and method of making same
JP2015556525A JP6275750B2 (ja) 2013-02-11 2014-02-10 超硬合金材料およびそれを作製する方法
EP14703394.8A EP2954082B1 (fr) 2013-02-11 2014-02-10 Matériau en carbure de tungstène, son procédé de fabrication et son utilisation
US16/283,129 US20190368011A1 (en) 2013-02-11 2019-02-22 Cemented carbide material and method of making same
US17/222,982 US20210222273A1 (en) 2013-02-11 2021-04-05 Cemented carbide material and method of making same

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US201361763343P 2013-02-11 2013-02-11
GB1302345.2 2013-02-11
GBGB1302345.2A GB201302345D0 (en) 2013-02-11 2013-02-11 Cemented carbide material and method of making same
US61/763,343 2013-02-11

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CN105154747B (zh) * 2015-09-14 2017-04-12 江西耀升钨业股份有限公司 一种复合碳化钨硬质合金棒材及其制备方法
TWI617380B (zh) * 2015-09-26 2018-03-11 京瓷股份有限公司 棒狀體及切削工具
TWI619571B (zh) * 2015-09-29 2018-04-01 京瓷股份有限公司 棒狀體及切削工具
US11821062B2 (en) 2019-04-29 2023-11-21 Kennametal Inc. Cemented carbide compositions and applications thereof

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US20150376744A1 (en) 2015-12-31
EP2954082A2 (fr) 2015-12-16
GB201302345D0 (en) 2013-03-27
US20190368011A1 (en) 2019-12-05
WO2014122306A3 (fr) 2015-04-09
JP6275750B2 (ja) 2018-02-07
GB2512983A (en) 2014-10-15
CN105074029A (zh) 2015-11-18
JP2016513177A (ja) 2016-05-12
GB2512983B (en) 2017-11-15
EP2954082B1 (fr) 2020-07-22
US20210222273A1 (en) 2021-07-22
CN105074029B (zh) 2019-08-06
GB201402248D0 (en) 2014-03-26

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