EP2855399A1 - Compact fritté extra-dur pour applications d'outils de coupe et son procédé de fabrication - Google Patents

Compact fritté extra-dur pour applications d'outils de coupe et son procédé de fabrication

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Publication number
EP2855399A1
EP2855399A1 EP13730401.0A EP13730401A EP2855399A1 EP 2855399 A1 EP2855399 A1 EP 2855399A1 EP 13730401 A EP13730401 A EP 13730401A EP 2855399 A1 EP2855399 A1 EP 2855399A1
Authority
EP
European Patent Office
Prior art keywords
superhard
sintered
milling
superhard compact
compact
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.)
Withdrawn
Application number
EP13730401.0A
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German (de)
English (en)
Inventor
Gerold Weinl
Torbjorn Selinder
Rui SHAO
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.)
Diamond Innovations Inc
Original Assignee
Diamond Innovations Inc
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Filing date
Publication date
Application filed by Diamond Innovations Inc filed Critical Diamond Innovations Inc
Publication of EP2855399A1 publication Critical patent/EP2855399A1/fr
Withdrawn legal-status Critical Current

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    • 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
    • C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
    • 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
    • B22F3/02—Compacting only
    • 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
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
    • C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
    • C04B35/58007—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides
    • C04B35/58014—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides based on titanium nitrides, e.g. TiAlON
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
    • C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
    • C04B35/58007—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides
    • C04B35/58014—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides based on titanium nitrides, e.g. TiAlON
    • C04B35/58021—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides based on titanium nitrides, e.g. TiAlON based on titanium carbonitrides
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
    • C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
    • C04B35/583—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on boron nitride
    • C04B35/5831—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on boron nitride based on cubic boron nitrides or Wurtzitic boron nitrides, including crystal structure transformation of powder
    • 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
    • C22C1/1026—Alloys containing non-metals starting from a solution or a suspension of (a) compound(s) of at least one of the alloy constituents
    • 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
    • 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
    • C22C29/04—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 carbonitrides
    • 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
    • C22C29/16—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on nitrides
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
    • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
    • C04B2235/38—Non-oxide ceramic constituents or additives
    • C04B2235/3804—Borides
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
    • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
    • C04B2235/38—Non-oxide ceramic constituents or additives
    • C04B2235/3804—Borides
    • C04B2235/3813—Refractory metal borides
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
    • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
    • C04B2235/38—Non-oxide ceramic constituents or additives
    • C04B2235/3852—Nitrides, e.g. oxynitrides, carbonitrides, oxycarbonitrides, lithium nitride, magnesium nitride
    • C04B2235/386—Boron nitrides
    • 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
    • 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
    • C22C2026/007—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes with additional metal compounds being nitrides
    • 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
    • C22C2026/008—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes with additional metal compounds other than carbides, borides or nitrides

Definitions

  • the present disclosure relates to a sintered superhard material made from powdered composition suitable for use in the manufacture of superhard abrasive compacts, and specifically to a sintered body containing cubic boron nitride (cBN) which may be used in cutting tools for hard part turning applications with enhanced toughness and good consistency.
  • cBN cubic boron nitride
  • PcBN Polycrystalline cubic boron nitride
  • diamond and diamond composite materials are commonly used to provide a superhard cutting surface for cutting tools such as those used in metal machining.
  • a sintered superhard compact body may comprise superhard particles; and a binder phase bonding the superhard particles together, wherein the weight percent ratio of W/Co in the sintered compact falls between 1 .0 and 2.0, and sum of weight percent of W and Co in the sintered compact is in a range from about 2 to about 20.
  • a sintered superhard compact body may comprise superhard particles; and a binder phase bonding the superhard particles together, wherein the binder phase comprises tungsten and cobalt derived from milling debris, wherein the binder phase comprises stoichiometric or substoichiometric carbides, nitrides, oxides, or sums thereof from aluminum, titanium or other transition metals of group IV, V, or VI in the periodic table of elements.
  • a method of making a superhard compact may comprise steps of providing milling bodies; milling a powder mixture of superhard powder and a binder material, and fluids with the milling bodies; and incorporating W and Co from the milling bodies into the superhard compact.
  • FIG. 1 is a backscattered scanning electron micrograph (BSE) image of a microstructure of a sintered superhard compact body made from a roll mill using cemented carbide milling bodies;
  • BSE backscattered scanning electron micrograph
  • FIG. 2 is a backscattered scanning electron micrograph (BSE) image of a microstructure of a sintered superhard compact body made from a roll mill using cermet milling bodies;
  • BSE backscattered scanning electron micrograph
  • FIG. 3 is a backscattered scanning electron micrograph (BSE) image of a microstructure of a sintered superhard compact body made from an attritor mill using cermet milling bodies according to an embodiment
  • FIG 4 is a graph of flank wear progression for a cutting tool made from materials milled by an attritor mill with cermet milling bodies, compared with a commercial grade;
  • FIG 5 is a graph of crater wear progression for a cutting tool made from materials milled by an attritor mill with cermet milling bodies, compared with a commercial grade;
  • FIG 6 is a graph of toughness test result for a cutting tool made from materials milled by an attritor mill with cermet milling bodies, compared with a commercial grade.
  • An embodiment provides a sintered superhard compact body with a defined weight percent ratio of W/Co and its manufacturing method.
  • the superhard particles may be selected from a group of cubic boron nitride, diamond, and diamond composite materials.
  • the composition of starting material used in producing the polycrystalline cBN compact comprises cBN and a binder phase, in powder or particular form.
  • the binder phase may at least partially melt and react with cBN and form bonding by reaction sintering during high pressure and high temperature (HPHT) sintering.
  • An embodiment may improve the toughness of a cBN material with an increased wear resistance and a reduction of variability of tool life for a given application area.
  • a superhard sintered compact and a method for its production that provides significantly improved microstructural homogeneity and better toughness than other superhard sintered compacts.
  • Embodiments use milling bodies, such as cermet milling bodies.
  • Cermet milling bodies may be made from a raw material powder blend which comprises 18% hexagonal close-packed (HCP) WC by weight, 16% HCP Co, and balanced face centered cubic (FCC) TiCN. After sintering, the cermet milling bodies may contain W in a range from 15% to 20%, which may be dissolved in (FCC) (Ti, W) (C, N). The cermet material may also contain up to 15% cobalt, which, in turn, may contain up to 12% dissolved tungsten.
  • HCP hexagonal close-packed
  • FCC balanced face centered cubic
  • Dispersion of cBN particles is mainly accomplished during the milling step.
  • Milling in general, as a means of comminution and dispersion, is well known in the art.
  • Commonly used milling techniques in grinding ceramic powder include conventional ball mills, tumbling ball mills, planetary ball mills, attritor mills, and agitated ball mills.
  • the energy input is determined by the size and density of the milling media, the diameter of the milling pot and the speed of rotation. Since the method requires that the balls tumble, rotational speeds, and therefore energy are limited.
  • Conventional ball milling is well suited for milling powders with low to medium particle strength.
  • conventional ball milling is used where powders are to be milled to a final particle size around 1 micron or more.
  • Attritor mills consist of an enclosed grinding chamber with an agitator that rotates at high speeds in either a vertical or horizontal configuration. Milling bodies are typically in the size ranging from 0.2 to 15 mm and, where comminution is the objective, milling media typically are high density cemented carbide. The high rotational speeds of the agitator, coupled with high density, small diameter milling bodies, provide high energy.
  • Attritor mill results in high shear in the slurry, which provides for very successful co-dispersion, or blending of powders. Attritor mill typically achieves finer particles and better homogeneity of materials in the sintered compact than the other methods mentioned.
  • An embodiment may use attritor or other mills with milling bodies made from cemented carbide hard metal, also known as WC/Co hard metal, containing 85- 90% HCP WC, and 7-15% Co.
  • the desirable form of milling debris may allow for a longer milling time and improved dispersion.
  • milling debris refers to any materials produced from milling bodies or the linings of a mill due to the friction between abrasive particles, milling bodies and linings. The dispersion of the different phases during milling is critical. The maximum possible dispersion is limited in prior art, by the fact that the cemented carbide milling bodies wear and produce milling debris containing high WC content.
  • cemented carbide has much higher W content than cermet, the tolerable milling time for cemented carbide milling bodies is much lower than that for cermet milling bodies, which greatly restricts the level of dispersion that can be achieved through milling using cemented carbide milling bodies.
  • cermet hard metal milling bodies may comprise a composition of (Ti,W)(C,N).
  • the composition may be beneficial to add as a part of the final blank composition.
  • W and/or Co containing raw materials may be added to achieve the desired final material composition.
  • the tungsten and cobalt are from milling debris.
  • the cermet milling bodies By using the cermet milling bodies, a more favorable form of milling debris may be formed, where the milling debris is actually a part of the raw material blend.
  • the advantage of using cermet milling debris as raw material is that the mill debris contains (Ti,W)(C,N) and Co with the right proportion of W/Co and they are always together.
  • the W in the (Ti,W)(C,N) is reduced to metallic W, which dissolves in molten Co during HPHT sintering. Therefore, molten Co may help distribute W uniformly around particles and helps increase homogeneity of the reactions between Co, W, and Al with cBN and binder phase particles.
  • molten Co may help distribute W uniformly around particles and helps increase homogeneity of the reactions between Co, W, and Al with cBN and binder phase particles.
  • superhard particles may comprise 31 wt% cBN, wherein the binder phase includes 5 wt% Al, 32 wt% Ti(Co .6 N 0 4 ), 32 wt%
  • the materials are milled by using cermet bodies in an attritor mill giving an addition of 3.1 +/- 1 wt% W and 2.2 +/-1 wt% Co from the milling bodies
  • a ratio of tungsten to cobalt may be in a range of 1 .0 to 2.0. In another embodiment, a ratio of tungsten to cobalt may be in a range of 1 .0 to1 .8. In yet another embodiment, a ratio of tungsten to cobalt may be in a range of 1 .0-1 .5.
  • PCBN based materials for hard part turning typically comprise sintered bodies having a volume share in the range of 35 to 85 vol. % cBN particles, and a ceramic binder phase which comprises carbides, nitrides, oxides, or sums thereof of aluminum, titanium or any other transition metal group IV, V, or VI in the periodic table of elements.
  • the cBN based material is sintered in a high pressure, high temperature (HPHT) process. Phase transitions during the HPHT process result in generating new phases, such as, borides, nitrides and carbonitrides, for example. Small amounts of inevitable contaminants may be present in these materials, which may be generated in certain process steps, such as, milling, which gives rise to tungsten and cobalt content originating in the milling bodies.
  • raw superhard materials such as cBN
  • fluids and ceramic materials which comprises stoichiometric or substoichiometric carbides, nitrides, oxides, or sums thereof from aluminum, titanium or other transition metals of group IV, V, or VI in the periodic table of elements.
  • An embodiment may further include steps of preparing granules from a mixture of superhard powders, ceramic powders, organic binder materials, and fluids; pre-compacting the granules to form a soft green part of defined shape; heating the soft green part in a vacuum furnace to form a hard green part; inserting one or more the hard green parts in a container.
  • An embodiment may further include steps of sintering the hard greens in the container in a pressure cell at a predetermined pressure and temperature; removing the container from the pressure cell to reveal the superhard compact.
  • PCBN may be typically made by HPHT sintering of a powder blend of cBN, ceramic phase and aluminum or aluminum compound, and may be often formed in the shape of a large PCBN disc or "blank".
  • two phases attributable to the cBN and binder phase material may be selected from a group of AI2O3, TiB 2 , AIN, for example.
  • at least one boride containing W, Co, or W-Co alloy phases may be detected by an X-Ray Diffraction (XRD), such as WB 2 , Co 2 B, or CoW 2 B 2 .
  • the W phase is not detected in the blank.
  • the PCBN blank may also be made from HPHT sintering of pre- compacted hard green discs.
  • hard greens have intermediary phases that may include AI 3 Ti, Ti 2 AIN, W, CoAI, AIB 2 that are produced in the pre-sintering step.
  • Example A Powders of cBN (39% by weight), substoichiometric TiN (ssTiN) (56% by weight) and Al (5% by weight) were milled in a roll mill with cemented carbide milling bodies in isopropyl alcohol for 2 hours. The slurry was then dried in an oven in air to remove the alcohol. Then the powder was dispersed in ethanol (99.6% pure), which was mixed with a polyethylene glycol (PEG) solution. The slurry was then spray dried into spherical granules, which is pre-compacted into round discs. The discs were fired in hydrogen at about 400 °C and then pre-sintered at 900 °C in vacuum. After pre-sintering, the hard green discs were loaded in a cell and HPHT sintered at temperature around 1300 to 1450 °C with pressure of at least 2 GPa.
  • ssTiN substoichiometric TiN
  • Al 5% by weight
  • Example B Powders of cBN (39% by weight), ssTiN (56% by weight) and Al (5% by weight) were milled in a roll mill with cermet milling bodies. ssTiN and Al powders were milled in ethanol (99.6% pure) for 15 hours, and then cBN powders were added to the slurry and milled for another 10 hours. Then the slurry was mixed with a PEG solution after milling. The following spray drying, pre-compaction, pre- sintering and HPHT processes were the same as described in Example A.
  • Example C Powders of cBN (39% by weight), ssTiN (27% by weight), TiCN (28% by weight), and Al (6% by weight) were milled together in ethanol in an attritor mill with cermet milling bodies for 3 hours.
  • the cermet milling bodies had the composition of (weight%):W 17.36, Co 17.47, Ti 50.65, N 4.84, and C 9.83.
  • the slurry was mixed with a PEG solution after milling.
  • the following spray drying, pre- compaction, pre-sintering and HPHT processes were the same as described in Example A.
  • Table 1 shows the W and Co contents by X-Ray Fluorescence (XRF) and the calculated W/Co ratios and sum of W and Co contents of Examples A, B and C. All three examples had the same W level (4.2 to 4.5% by weight), but the Co level was much higher in Example C than in the other two cases.
  • XRF X-Ray Fluorescence
  • Example C the attritor milling action determined that the wearing between milling bodies was much more severe than from the mill jar. As a result, even though the attritor milling jar was made of stainless steel, there was not much mill debris from the attritor milling jar. The iron content in the final blend was only about 0.3% by weight. The mill debris in attritor milling with cermet milling bodies mainly came from the milling bodies, which resulted in the low W/Co ratio.
  • FIG. 1 , 2 and 3 show the back scattered electronic (BSE) micrographs of examples A, B and C.
  • FIG. 1 shows the BSE image of example A with 39 wt% cBN which was roll milled with cemented carbide milling bodies for two hours.
  • FIG. 2 illustrates the BSE image of example B with 39 wt% cBN which was roll milled with cermet milling bodies for 25 hours.
  • FIG. 3 illustrates the BSE image of example C with 39wt% cBN which was attritor milled with cermet milling bodies for three hours. It can be seen that with the same W level, dispersion in Example A is not very good. Dispersions in Example B and C much improved compared to Example A. It should be noted that in both Examples A and B, because of the excess W, large mill debris (white spots in the micrographs) were visible, whereas in example C, because W was dissolved in Co and uniformly distributed in the microstructure, large mill debris was scarce.
  • Table 2 shows a number of other material blends which were milled using different milling bodies (cermet or cemented carbide) and different mills (roll mill or attritor mill).
  • the lining of the roll mills might be stainless steel (ss) or cemented carbide (cc). All materials had a good dispersion of the constituents except for mill D, which was milled for too short duration.
  • the W/Co ratio was the highest (over 10) in the case of milling with cemented carbide bodies, because the W/Co ratio was high in the milling body material.
  • Powders of aluminum (5 wt%%), TiCN (32 wt%), ssTiN (32 wt%), and cBN (31 wt%) were milled in an attritor mill with cermet milling bodies in ethanol for 5 hours. After milling, the slurry was mixed with a PEG solution and the material was spray dried, pre-compacted, pre-sintered and HPHT sintered in the same way as described in Example 1 . Then tips were Electrical Discharge Machining (EDM) cut from HPHT sintered discs and standard cutting tools were made and machining tests were conducted together with a commercial hard part turning grade, which was referred to as "comparison grade” or "Comparison” in the following text, FIG. 4, 5 and 6 and Table 4.
  • EDM Electrical Discharge Machining
  • Table 3 shows the XRD data after pre-sintering and HPHT for Example 3. Co and W had reacted to form several different reaction products. In the material after HPHT, cBN, TiCN, AI2O3, and TiB 2 were detected, as expected traditionally. The new phases were some boron-containing tungsten, cobalt, or tungsten-cobalt phases, such as WB 2 , Co 2 B, or CoW 2 B 2 . Most notably, the intermediary phases after pre-sintering, such as AIB 2 , Ti 2 AIN, W, were not visible after HPHT. The TiN peak detectable after pre-sintering also disappeared after HPHT due to solid state diffusion and homogenization between the TiCN/TiN binders during HPHT sintering.
  • FIGS 4 and 5 show the flank wear and crater wear test results on Example 3 compared with the comparison grade.
  • the test was conducted on 8620 steel with continuous cutting. Cutting was stopped every 2 to 4 minutes, and flank wear and crater wear were measured and recorded. It could be seen that Example 3 had similar crater wear to the comparison grade, but much lower flank wear than the comparison grade.
  • Table 4 shows a series of wear test by cutting 8620 steel on Example 3 compared with the comparison grade.
  • Flank wear was measured every 4 minutes and tool life was determined based on 0.15 mm of flank wear.
  • Different cutting speeds 240 and 180 m/min
  • feeds 0.1 and 0.15 mm/rev
  • depth of cut 0.1 to 0.2 mm/doc
  • FIG. 6 shows the toughness test result on Example 3 compared with the comparison grade.
  • the test was conducted on 52100 steel with hardness of Rc 60 to 62. Four samples of each were tested and the failing feed of each sample was recorded.
  • toughness increases with cBN content.
  • Example 3 had much lower cBN content than the comparison grade, 38 vol% in Example 3 and 50 vol% in the comparison grade, it had the same toughness level as the comparison grade, and much better consistency. This could be attributed to the higher Co content and more uniform distribution of mill debris.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Ceramic Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Structural Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Ceramic Products (AREA)

Abstract

La présente invention concerne un procédé et une composition de compact fritté extra-dur. Le corps du compact fritté extra-dur peut comprendre des particules extra-dures et une phase liante. La phase liante peut lier les particules extra-dures entre elles. La phase liante comprend du tungstène et du cobalt. Le rapport du tungstène au cobalt est entre 1 et 2 et la somme du W et du Co dans le compact fritté extra-dur se situe dans une plage d'environ 2 à environ 20 pour cent en poids.
EP13730401.0A 2012-05-31 2013-05-31 Compact fritté extra-dur pour applications d'outils de coupe et son procédé de fabrication Withdrawn EP2855399A1 (fr)

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US201261653779P 2012-05-31 2012-05-31
PCT/US2013/043600 WO2013181525A1 (fr) 2012-05-31 2013-05-31 Compact fritté extra-dur pour applications d'outils de coupe et son procédé de fabrication

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CN104962793B (zh) * 2015-06-23 2017-04-26 中南钻石有限公司 一种具有良好导电性能的金刚石聚晶复合片及其制备方法
US9719742B2 (en) * 2015-08-10 2017-08-01 Bryan Zeman Empty ammunition magazine bolt hold open device
EP3814041A1 (fr) * 2018-06-28 2021-05-05 Diamond Innovations, Inc. Compact fritté en pcbn
CN116987943B (zh) * 2018-09-19 2025-10-10 住友电气工业株式会社 立方氮化硼烧结体以及包括该立方氮化硼烧结体的切削工具
CN114430704A (zh) * 2019-09-18 2022-05-03 住友电工硬质合金株式会社 金刚石切削工具
US12528744B2 (en) * 2020-03-13 2026-01-20 Mitsubishi Materials Corporation Hard composite material
WO2022210771A1 (fr) * 2021-03-31 2022-10-06 三菱マテリアル株式会社 Embout d'excavation, et outil d'excavation

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GB201011574D0 (en) * 2010-07-09 2010-08-25 Element Six Ltd PCBN material
KR102181845B1 (ko) * 2012-05-31 2020-11-23 하이페리온 매터리얼즈 앤드 테크놀로지스 (스웨덴) 에이비 Cbn 재료의 제조 방법

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JP2015523954A (ja) 2015-08-20
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KR20150024325A (ko) 2015-03-06
CN104350028A (zh) 2015-02-11

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