EP2347025B1 - Verfahren zur herstellung eines teils, umfassend einen block aus dichtem material, bestehend aus harten teilchen und bindemittelphase, mit eigenschaftsgradient und resultierendes teil - Google Patents

Verfahren zur herstellung eines teils, umfassend einen block aus dichtem material, bestehend aus harten teilchen und bindemittelphase, mit eigenschaftsgradient und resultierendes teil Download PDF

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EP2347025B1
EP2347025B1 EP09755981A EP09755981A EP2347025B1 EP 2347025 B1 EP2347025 B1 EP 2347025B1 EP 09755981 A EP09755981 A EP 09755981A EP 09755981 A EP09755981 A EP 09755981A EP 2347025 B1 EP2347025 B1 EP 2347025B1
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Prior art keywords
block
binder phase
dense
temperature
dense material
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French (fr)
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EP2347025A1 (de
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Christophe Colin
Elodie Lefort
Alfazazi Dourfaye
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Varel Europe SAS
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Varel Europe SAS
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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
    • C22C29/02—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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12014—All metal or with adjacent metals having metal particles
    • Y10T428/12028—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, etc.]
    • Y10T428/12049—Nonmetal component

Definitions

  • a part comprising a block of dense material consisting of hard particles dispersed in a binder phase by a thermo-chemical treatment, the part having a property gradient.
  • Many parts in particular drill bit cutters or machining tools, consist of blocks of hardened carbide type material consisting of carbide particles dispersed in a metal binder phase. These materials, which are extremely hard, and therefore resistant to wear, can also be fragile. Also, in order to reinforce their toughness, they are subjected to treatments intended to introduce within them a ductile phase composition gradient with or without the formation of new phases whose hardness is different from the initial hardness of the block which results either in blocks whose outer surface, or at least a part thereof, is extremely hard and the inner part is more tenacious, either to blocks whose outer surface or at least a part is more tenacious and the inner part is harder .
  • non-dense cemented carbide blocks having a porosity gradient can be produced by powder metallurgy and infiltrated by a binder phase to improve their ductility to the core.
  • This method is poorly suited in particular to the WC-Co type system, because it leads to the partial destruction of the pre-existing carbide skeleton infiltration, and therefore does not achieve the desired properties for a cutter.
  • cemented carbides with a composition gradient by natural phase solid sintering of a multilayer component, each of the layers having a different composition.
  • this method does not completely densify the material and must be followed by an expensive treatment of hot isostatic compaction.
  • the preparation of the cemented carbide gradient composition is complex since it requires the realization of a succession of elementary layers that fit into each other.
  • this method has the disadvantage of not generating a continuous composition gradient.
  • cemented carbide blocks having a binder phase composition gradient over millimeter distances by enriching these cemented carbides by imbibition from the outside to from a liquid phase capable of penetrating (or migrating) into the cemented carbide.
  • This imbibition phenomenon corresponds to the migration of external liquid composition close to that of the solid / liquid system considered perfectly dense under the sole driving force of the migration pressure generated by a local imbalance of the volume fraction of the binder phase and / or the size and morphology of the solid grains.
  • This phenomenon concerns any system consisting of condensed phases (solid and liquid) which has an ability to adapt the shape of its solid grains by the absorption of liquid thus making it energetically more stable, that is to say which has a maturing Ostwald with modification of the shape of the hard particles without necessarily causing a magnification of these particles by the phenomenon of dissolution and re-precipitation.
  • the inventors have found that it is possible to generate binding phase concentration gradients over millimeter distances inside dense cemented carbide blocks, on the sole condition of depositing a suitable coating on all or part of the surface of the dense cemented carbide block and subject to a suitable heat treatment whose temperature must be at least equal to the temperature allowing the transition to the liquid state of the binder phase (solidus of the cemented carbide considered).
  • the material constituting the coating destabilizes (or dissociates) and one or more chemical elements constituting it, diffuse and react or not with the block material, thus generating a binder phase gradient in the block and / or the formation of phases whose hardness is different from the initial hardness of the block over greater or lesser distances, depending on the duration of the heat treatment applied.
  • the parameters of the heat treatment can be determined by those skilled in the art in particular depending on the shape of the desired gradient.
  • the subject of the invention is a method for manufacturing a part comprising a block of dense material consisting of hard particles of the same or different nature dispersed in a binder phase, the material having a solidus temperature T s from of which the binder phase is liquid, characterized in that at least a portion of the surface of the dense material block is deposited with an active coating consisting of a material possibly capable of reacting chemically with the dense material but not providing any additional binder phase, when the assembly is carried beyond a minimum reaction temperature T r , and in that the block coated with the active coating is subjected to a heat treatment comprising heating and then holding for a time t m at a holding temperature T m greater than or equal to the minimum reaction temperature T r , followed by cooling to room temperature.
  • This method leads to variations of the binder phase inside the block over millimeter distances which are done without external binder phase input and thus without leading to the overall enrichment of the block in additional binder phase.
  • the holding temperature T m is greater than or equal to the solidus temperature T s of the dense material.
  • the holding temperature T m is less than or equal to T s + 200 ° C.
  • the holding time t m is between 1 min and 10 min.
  • the active coating can be deposited only on a part of the surface of the block.
  • the active coating can be deposited on the entire surface of the block.
  • the dense material is for example a cemented carbide consisting of metal carbide particles dispersed in a metal matrix.
  • the cemented carbide may further contain natural or synthetic diamond particles up to 1 mm in diameter.
  • the cemented carbide is for example of the WC-M type, M being one or more metals taken from Co, Ni and Fe, the sum of the contents by weight of these metals in the binder phase being greater than 50%.
  • the coating material capable of reacting with the dense material of the block is for example composed of at least one of nitride, boride, carbide, oxide, hydride, carbonitride, borocarbide and graphite compounds. This material may consist of any mixture of these different compounds.
  • the coating may be deposited by a PVD (Physical Vapor Deposition) or CVD (Chemical Vapor Deposition) method, or by a spraying, brushing, dipping or screen printing process.
  • PVD Physical Vapor Deposition
  • CVD Chemical Vapor Deposition
  • the block of dense material is for example a cutting or support block of a drill bit of a drilling tool or felling or machining of rocks or metals.
  • PDC Polycrystalline Diamond Compact
  • TSP Thermal Stable Polycrystalline diamond
  • the diamond plate can be attached to the block by soldering, after the treatment of the block.
  • This thermal process then has the advantage of very simply producing cemented carbide blocks having a property gradient suitable for use as a drill bit or cutting tool bit, or as a cutting bit support block. drilling tool or cutting tool.
  • the cutter for a rock size tool which comprises a block consisting of hard particles dispersed in a binder phase obtained by the process according to the invention may have a distance greater than 0.5 mm, better still greater than 1 mm, and better still higher at 3 mm, a continuous gradient of binder phase content, the difference in binder phase content between the richest zone and the less rich zone being greater than 1% by volume, better still greater than 2%, and better still, greater than 5%.
  • the cutting edge may comprise a PDC or TSP-type diamond insert having a thickness of between 0.4 mm and 5 mm.
  • the rock size tool may include at least one cutter or impregnated blade of a cemented carbide blend with natural or synthetic diamond particles (up to 1 mm in diameter).
  • blocks intended in particular to manufacture bits for drilling tools or more generally for cutting tools generally parallelepiped shape or cylindrical shape having dimensions of the order of a few millimeters or a few tens of millimeters .
  • These blocks obtained by powder metallurgy, consist of a dense material whose structure comprises on the one hand hard particles such as metal carbides, and in particular tungsten carbides, and on the other hand a binding phase consisting of mainly a metal or an alloy metallic.
  • this binder phase can form, at a suitable temperature, a eutectic whose melting temperature is lower both at the melting point of the carbides and at the melting point of the metal or of the metal alloy.
  • This metal or metal alloy which constitutes the binder phase is for example cobalt but may also be iron or nickel or a mixture of these metals, these elements represent at least 50% by weight of the binder phase.
  • This binder phase may also contain addition elements whose sum of the contents may reach at most 15% by weight but generally do not exceed 5%.
  • additive elements may be copper to improve electrical conductivity or silicon which has a surfactant effect with respect to the system consisting of carbides and the binder phase.
  • the alloying elements may also be of carbide-forming elements for forming carbides or mixed carbides of type M x C y other than tungsten carbide. These elements include manganese, chromium, molybdenum, vanadium, niobium, tantalum, titanium, zirconium and afnium.
  • the binder phase may comprise additive elements that change the shape and / or inhibit the magnification of hard particles and that those skilled in the art know.
  • the chemical composition of these materials includes unavoidable impurities that result from the processes of making.
  • the block 1 made of dense material is coated with a layer 2 of thickness generally between approximately 50 ⁇ m and 2 mm, made of a material capable of chemically reacting with the binder phase and / or the carbide phase of the dense material.
  • This coating is carried out by spraying, PVD (Physical Vapor Deposition) or CVD (Chemical Vapor Deposition) deposit if this coating material is supplied in gaseous form, or by brush, dip or dipping. silkscreen if the coating material is brought in liquid form.
  • the holding temperature T m must be greater than or equal to the minimum reaction temperature T r which is the temperature above which the outer coating or one of its elements begins to react (in particular formation of solid phases) or diffuse without reacting (no formation of solid phases but can lead locally to a change in the composition of the binding phase of the dense block) significantly within the block.
  • This reaction temperature T r must be greater than or equal to the solidus temperature T s of the cemented carbide which constitutes the block.
  • This solidus temperature is the minimum temperature at which the binder phase of the cemented carbide is in the liquid state. This condition is desirable so that the coating or one of its constituent elements can rapidly diffuse and then react or not depending on the coating considered with the constituents (solid grains or liquid phase) of the block being treated.
  • the reaction temperature T r is greater than or equal to the destabilization or dissociation temperature T d of the compound which is not necessarily greater than the solidus temperature T s of the cemented carbide.
  • the reaction temperatures T r , of destabilization T d and the solidus temperature T s depend on the nature of the material of which the coating consists and of the material of which the block is made. Those skilled in the art know how to determine these temperatures.
  • reaction temperature Tr which has just been defined is greater than or equal to the solidus temperature Ts so that the diffusion takes place in the binder phase in the liquid state in order to obtain a sufficient diffusion rate.
  • the holding temperature T m must not be too high. Preferably, it should remain below T s + 200 ° C and better, below T s + 100 ° C, and better still, below T s + 50 ° C.
  • the holding time t m must be adapted to the shape and amplitude of the desired gradient and is deduced from the experiment. It is usually of the order of a few minutes.
  • the coating material capable of destabilizing or dissociating and / or reacting with the material constituting the dense block to be treated is, for example, a metalloid nitride or metal nitride such as boron nitride, aluminum nitride, titanium nitride, or a boride such as titanium boride, a metalloid carbide or metal such as boron carbide, titanium carbide, or a hydride such as titanium hydride or graphite or an oxide refractory such as alumina or a carbonitride or borocarbide metal or a mixture of such materials.
  • a metalloid nitride or metal nitride such as boron nitride, aluminum nitride, titanium nitride, or a boride such as titanium boride, a metalloid carbide or metal such as boron carbide, titanium carbide, or a hydride such as titanium hydride or graphite or an oxide
  • the materials used to make the coating of the block to be treated must be active or in some cases reactive above the solidus temperature T s , but it is preferable that they remain stable, that is to say, do not dissociate, below this temperature.
  • the property gradient obtained may result from a relative hardening of the surface of the block relative to the core, or on the contrary, a softening.
  • the heat treatment comprises, as shown in figure 4 , a rise in temperature up to the holding temperature T m , then a hold for a holding time t m at this temperature and cooling to room temperature.
  • the holding time t m and the holding temperature T m are adapted according to the dimensions of the block to be treated and the property gradient that is to be obtained.
  • the heat treatment can be carried out in a resistance furnace, or an induction furnace, or a microwave oven, under a protective atmosphere or under empty.
  • the protective atmosphere is for example argon or a mixture of argon and hydrogen but generally any neutral atmosphere such as argon, nitrogen, hydrogenated argon, hydrogenated nitrogen, hydrogen or possibly a primary or secondary vacuum.
  • the block thus treated has a composition, in particular a binder phase content, which varies from outside to inside.
  • the figure shows iso-concentration Ci curves in the binder phase, the outermost zone 10 being the poorest in the binder phase and therefore the hardest, and the intermediate zone 11 having an intermediate concentration and the the richest zone 12 binder phase being the least hard and therefore the most tenacious.
  • the variation in the binder phase content takes place over several millimeters.
  • the extent of the area affected by the variation of the binder phase content depends both on the maximum holding temperature T m , the holding time t m and the thickness of the coating material.
  • T m the maximum holding temperature
  • t m the holding time
  • the thickness of the coating material At equal thickness of the coating layer, the higher the temperature T m is and the longer the time t m is, the more the affected area is extended; that is, the deeper the block is affected.
  • the block as just described is covered on all sides with an active material. But, the active material can be deposited only on a part of the outer surface of the block and thus can lead to hardening or softening that areas of the block located under the coating and therefore have respectively a softened area or hardened core that can extend to the outer surface of the block that is not coated.
  • the variation in hardness that can reach several hundred Vickers can be over distances greater than 0.5mm, and can extend throughout the block.
  • the first block, spotted 10 at the figure 5 was spray-coated with a layer 11 of boron nitride BN, covering the upper face and the side faces of the block, and then treated under vacuum.
  • the direction of migration of the binder phase is indicated by the arrow and by the increasing direction of the iso-concentrations (C1 ⁇ C2 ⁇ C3 ⁇ C4).
  • the second block, spotted 20 at the figure 7 was also coated with a layer 21 of boron nitride BN, but this was deposited on only one half of the block.
  • the block was treated under a hydrogenated argon atmosphere.
  • the binder phase concentration gradient obtained leads to a hardness amplitude of 120 HV, only the zone 22 beneath the coating being cured, the remainder 23 not being hardened.
  • the direction of migration of the binder phase is indicated by the arrow and the increasing direction of the iso-concentrations (C1 ⁇ C2 ⁇ C3).
  • the third block, spotted 30 at the figure 9 was coated with a layer 31 of aluminum oxide Al 2 O 3 deposited in the form of liquid paste with a brush on the upper face and on the side faces of the block and treated under vacuum.
  • the binder phase concentration gradient obtained is dome-shaped, but, contrary to what was obtained with the first block, the zone 32 close to the surface has been softened so that their hardness is 150 HV less than that of the core zone 33.
  • the direction of migration of the binder phase is indicated by the arrow and by the increasing direction of the insulation. concentrations (C1 ⁇ C2 ⁇ C3 ⁇ C4) whose meaning is opposite to the two previous cases.
  • the boron nitride makes it possible to harden the zone of the block close to the coating layer, whereas the alumina makes it possible to soften it.
  • the furnace atmosphere (vacuum or argon-hydrogenated) used to carry out the treatments has no effect on the result.
  • the blocks thus treated may constitute bits of drilling tool or cutting tool and may have dimensions of a few millimeters or even more since it is conceivable to produce cutting blades having dimensions of several centimeters and which can be hardened by this process.
  • a cutter for a rock cutting tool or tool for cutting refractory or machining metals consisting of a cemented carbide support block 20 made using the method according to the invention, the lateral surface of which is hard and the tenacious core (C1 ⁇ C2 ⁇ C3 ⁇ C4) and whose underside has not been coated before heat treatment and whose upper face after treatment has been reported a plate 21 of natural or synthetic diamond of greater thickness at 0.4 mm according to the HPHT (High Pressure - High Temperature) process of the PDC (Polycrystalline Diamond Compact) or TSP (Thermally Stable Polycrystalline diamond) type.
  • HPHT High Pressure - High Temperature
  • PDC Polycrystalline Diamond Compact
  • TSP Thermally Stable Polycrystalline diamond
  • the support block 20 treated according to the invention can be assembled after the HPHT process by soldering for example according to the process known under the name of "LS Bond” and described in US Pat. US 4,225,322 and US 5,111,895 without this operation leading to a drastic change in the binder phase concentration gradient in the block.

Claims (17)

  1. Verfahren zur Herstellung eines Teils mit einem Block (1) aus dichtem Material, welches aus harten Teilchen besteht, welche derselben oder unterschiedlicher Art sind, und welche in einer Bindemittelphase dispergiert sind, wobei das Material eine Festzustandstemperatur Ts aufweist, ab welcher die Bindemittelphase flüssig ist, dadurch gekennzeichnet, dass auf zumindest einen Teil der Oberfläche des Blockes aus dichtem Material (1) eine aktive Beschichtung (2) aufgebracht wird, die aus einem Material besteht, das eventuell mit dem dichten Material chemisch reagieren kann, wenn die gesamte Anordnung auf eine Temperatur jenseits einer minimalen ReaktionstemperaturTr gebracht wird, und dass der mit der aktiven Beschichtung (2) beschichtete Block (1) einer thermischen Behandlung unterzogen wird, welche ein Aufheizen und dann ein Halten während einer Zeit tm auf einer Haltetemperatur Tm umfasst, welche höher als oder gleich der minimalen Reaktionstemperatur Tr ist, gefolgt von einer Abkühlung auf die Umgebungstemperatur, wobei dieses Verfahren zu Veränderungen der Bindemittelphase im inneren des Blocks über Millimeterdistanzen führt, welche ohne äußere Zugabe von Bindemittelphase stattfinden und somit nicht zu einer Gesamtanreicherung an zusätzlicher Bindemittelphase in dem Block führen
  2. Verfahren gemäß Anspruch 1, dadurch gekennzeichnet, dass die Haltetemperatur Tm hoher als oder gleich der Festzustandstemperatur Ts des dichten Materials ist.
  3. Verfahren gemäß Anspruch 2, dadurch gekennzeichnet, dass die Haltetemperatur Tm niedriger als oder gleich Ts + 200°C ist.
  4. Verfahren gemäß irgendeinem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Haltezeit tm zwischen 1 min und 10 min beträgt.
  5. Verfahren gemäß irgendeinem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass die aktive Beschichtung nur auf einen Teil der Oberfläche des Blocks aufgebracht wird.
  6. Verfahren gemäß irgendeinem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass die aktive Beschichtung auf die gesamte Oberfläche des Blocks aufgebracht wird.
  7. Verfahren gemäß irgendeinem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass das dichte Material ein einsatzgehärtetes Karbid ist, das aus metallischen Karbidteilchen besteht, die in einer Metallmatrix dispergiert sind.
  8. Verfahren gemäß Anspruch 7, dadurch gekennzeichnet, dass das einsatzgehärtete Karbid außerdem natürliche oder künstliche Diamantpartikel enthält, welche eine Größe von bis zu 1mm Durchmesser aufweisen.
  9. Verfahren gemäß Anspruch 7 oder Anspruch 8, dadurch gekennzeichnet, dass das einsatzgehärtete Karbid von der Art WC-M ist, wobei M aus einem oder mehreren Metallen besteht, welche aus Co, Ni und Fe genommen sind, wobei die Summe der Gewichtsgehalte dieser Metalle in der Bindemittelphase mehr als 50% beträgt.
  10. Verfahren gemäß irgendeinem der Ansprüche 1 bis 9, dadurch gekennzeichnet, dass das Beschichtungsmaterial, welches mit dem dichten Material des Blocks reagieren kann, aus zumindest einer Verbindung besteht, welche aus den Verbindungen der Art Nitrid, Karbid, Oxid, Hydrid, Karbonitrid, Borokarbid, Graphit oder irgendeinem Gemisch dieser verschiedenen Verbindungen genommen ist.
  11. Verfahren gemäß irgendeinem der Ansprüche 1 bis 10, dadurch gekennzeichnet, dass die Beschichtung mit einem Verfahren der Art PVD (Physical Vapor Deposition) oder CVD (Chemical Vapor Deposition) oder mit einem Sprühverfahren oder mit dem Pinsel oder im Tauchbad oder durch Serigraphie aufgebracht wird.
  12. Verfahren gemäß irgendeinem der Ansprüche 1 bis 11, dadurch gekennzeichnet, dass der Block aus dichtem Material eine Schneide oder ein Tragblock für eine Schneide eines Bohr- oder Abbau- oder maschninellen Bearbeitungswerkzeugs (Steinblöcke/ Metalle) ist.
  13. Verfahren gemäß Anspruch 12, dadurch gekennzeichnet, dass außerdem ein diamantbesetztes Plättchen der Art PDC (Polycrystalline Diamond Compact) oder TSP (Thermally Stable Polycrystalline diamond) auf einer Seite des Tragblocks angeordnet wird.
  14. Verfahren gemäß Anspruch 13, dadurch gekennzeichnet, dass das diamantbesetzte Plättchen nach Bearbeitung des Blocks durch Löten auf eine Seite des Blocks aufgebracht wird.
  15. Verfahren gemäß irgendeinem der Ansprüche 1 bis 14, dadurch gekennzeichnet, dass das Teil eine Schneide zum Zerkleinern von Steinblöcken ist, mit einem Block, der aus harten Partikeln besteht, welche in einer Bindemittelphase dispergiert sind, die über eine größere Distanz als 0,5 mm einen kontinuierlichen Gradienten an Bindemittelphasengehalt aufweist, wobei der Unterschied des Gehalts an Bindemittelphase zwischen der reichsten Zone und der am wenigsten reichen Zone mehr als 1 Vol.-% beträgt.
  16. Verfahren gemäß Anspruch 15, dadurch gekennzeichnet, dass die Schneide ein aufgesetztes diamantbesetztes Plattchen der Art PDC oder TSP mit einer größeren Dicke als 0,4 mm aufweist.
  17. Verfahren gemäß Anspruch 15 oder Anspruch 16, dadurch gekennzeichnet, dass das Teil ein Schneidwerkzeug für Steinblöcke mit zumindest einer Schneide oder einer Klinge ist.
EP09755981A 2008-10-07 2009-10-07 Verfahren zur herstellung eines teils, umfassend einen block aus dichtem material, bestehend aus harten teilchen und bindemittelphase, mit eigenschaftsgradient und resultierendes teil Active EP2347025B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR0856771A FR2936817B1 (fr) 2008-10-07 2008-10-07 Procece pour fabriquer une piece comprenant un bloc en materiau dense du type carbure cemente, presentant un grandient de proprietes et piece obtenue
PCT/FR2009/051910 WO2010040953A1 (fr) 2008-10-07 2009-10-07 Procede de fabrication d'une piece comprenant un bloc en materiau dense constitue de particules dures et de phase liante presentant un grandient de proprietes, et piece ainsi obtenue

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EP2347025A1 EP2347025A1 (de) 2011-07-27
EP2347025B1 true EP2347025B1 (de) 2013-01-16

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US (1) US8602131B2 (de)
EP (1) EP2347025B1 (de)
JP (1) JP5622731B2 (de)
CN (1) CN102282278A (de)
FR (1) FR2936817B1 (de)
WO (1) WO2010040953A1 (de)

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US9428822B2 (en) 2004-04-28 2016-08-30 Baker Hughes Incorporated Earth-boring tools and components thereof including material having hard phase in a metallic binder, and metallic binder compositions for use in forming such tools and components
US8858871B2 (en) 2007-03-27 2014-10-14 Varel International Ind., L.P. Process for the production of a thermally stable polycrystalline diamond compact
FR2914206B1 (fr) * 2007-03-27 2009-09-04 Sas Varel Europ Soc Par Action Procede pour fabriquer une piece comprenant au moins un bloc en materiau dense constitue de particules dures dispersees dans une phase liante : application a des outils de coupe ou de forage.
FR2936817B1 (fr) * 2008-10-07 2013-07-19 Varel Europ Procece pour fabriquer une piece comprenant un bloc en materiau dense du type carbure cemente, presentant un grandient de proprietes et piece obtenue
WO2011146752A2 (en) 2010-05-20 2011-11-24 Baker Hughes Incorporated Methods of forming at least a portion of earth-boring tools, and articles formed by such methods
CA2799911A1 (en) 2010-05-20 2011-11-24 Baker Hughes Incorporated Methods of forming at least a portion of earth-boring tools, and articles formed by such methods
US8522900B2 (en) 2010-09-17 2013-09-03 Varel Europe S.A.S. High toughness thermally stable polycrystalline diamond
JP6809918B2 (ja) * 2017-01-31 2021-01-06 三菱重工業株式会社 金属成形品の熱処理方法及び製造方法
TWI652352B (zh) * 2017-09-21 2019-03-01 國立清華大學 共晶瓷金材料
JP6762331B2 (ja) * 2018-03-09 2020-09-30 三菱重工業株式会社 金属成形品の製造方法
EP4017676A4 (de) * 2019-09-26 2023-10-11 Worldwide Machinery, Ltd Trägermaterial zum schweissen
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JP5622731B2 (ja) 2014-11-12
US20110174550A1 (en) 2011-07-21
US8602131B2 (en) 2013-12-10
FR2936817A1 (fr) 2010-04-09
WO2010040953A1 (fr) 2010-04-15
EP2347025A1 (de) 2011-07-27
CN102282278A (zh) 2011-12-14
JP2012505306A (ja) 2012-03-01
FR2936817B1 (fr) 2013-07-19

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