EP1922427A2 - Materiaux a base de metaux durs pour applications a haute temperature - Google Patents

Materiaux a base de metaux durs pour applications a haute temperature

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Publication number
EP1922427A2
EP1922427A2 EP06813610A EP06813610A EP1922427A2 EP 1922427 A2 EP1922427 A2 EP 1922427A2 EP 06813610 A EP06813610 A EP 06813610A EP 06813610 A EP06813610 A EP 06813610A EP 1922427 A2 EP1922427 A2 EP 1922427A2
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EP
European Patent Office
Prior art keywords
binder
tic
hardmetals
hardmetal
hard particles
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Withdrawn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
EP06813610A
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German (de)
English (en)
Other versions
EP1922427A4 (fr
Inventor
Shaiw-Rong Scott Liu
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.)
Genius Metal Inc
Original Assignee
Genius Metal Inc
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Filing date
Publication date
Application filed by Genius Metal Inc filed Critical Genius Metal Inc
Publication of EP1922427A2 publication Critical patent/EP1922427A2/fr
Publication of EP1922427A4 publication Critical patent/EP1922427A4/fr
Withdrawn legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • 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
    • 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
    • C22C29/14—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on borides
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps

Definitions

  • Hardmetals include various composite materials and are specially designed to be hard and refractory, and exhibit strong resistance to wear. Examples of widely-used hardmetals include sintered or cemented carbides or carbonitrides, or a combination of such materials. Some hardmetals, called cermets, have compositions that may include processed ceramic particles (e.g., TiC) bonded with binder metal particles. Certain compositions of hardmetals have been documented in the technical literature. For example, a comprehensive compilation of hardmetal compositions is published in Brookes' World Dictionary and Handbook of Hardmetals, sixth edition, International Carbide Data, United Kingdom (1996) .
  • Hardmetals may be used in a variety of applications. Exemplary applications include cutting tools for cutting metals., stones, and other hard materials, wire-drawing dies, knives, mining tools for cutting coals and various ores and rocks, and drilling tools for oil and other drilling applications. In addition, such hardmetals also may be used to construct housing and exterior surfaces or layers for various devices to meet specific needs of the operations of the devices or the environmental conditions under which the devices operate. [0005] Many hardmetals may be formed by first dispersing hard, refractory particles of carbides or carbonitrides in a binder matrix and then pressing and sintering the mixture. The sintering process allows the binder matrix to bind the particles and to condense the mixture to form the resulting hardmetals. The hard particles primarily contribute to the hard and refractory properties of the resulting hardmetals . Summary
  • the hardmetal materials described below include materials comprising hard particles having a first material, and a binder matrix having a second, different material.
  • the hard particles are spatially dispersed in the binder matrix in a substantially uniform manner.
  • the first material for the hard particles may include, for example, materials based on tungsten carbide, materials based on titanium carbide, materials based on a mixture of tungsten carbide and titanium carbide, other carbides, nitrides, borides, suicides, and combinations of these materials.
  • the second material for the binder matrix may include, among others, rhenium, a mixture of rhenium and cobalt, a nickel-based superalloy, a mixture of a nickel-based superalloy and rhenium, a mixture of a nickel-based superalloy, rhenium and cobalt, and these materials mixed with other materials.
  • Tungsten may also be used as a binder matrix material in hardmetal materials.
  • the nickel-based superalloy may be in the ⁇ - ⁇ ' metallurgic phase.
  • the volume of the second material may be from about 3% to about 40% of a total volume of the material.
  • the binder matrix may comprise rhenium in an amount at or greater than 25% of a total weight of the binder matrix of the final material .
  • the second material may include a Ni-based superalloy.
  • the Ni-based superalloy may include Ni and other elements such as Re for certain applications.
  • Fabrication of the hardmetal materials of this application may be carried out by, according to one implementation, sintering the material mixture under a vacuum condition and performing a solid-phase sintering under a pressure applied through a gas medium. Such hardmetals may also be coated on surfaces using thermal spray methods to form either hardmetal coatings and hardmetal structures .
  • Advantages arising from various implementations of the described hardmetal materials may include one or more of the following: superior hardness in general, enhanced hardness at high temperatures, and improved resistance to corrosion and oxidation.
  • Additional material compositions and their application are disclosed.
  • a material can include hard particles comprising at least one carbide selected from at least one of TaC, HfC, NbC, ZrC, TiC, WC, VC, Al 4 C 3 , ThC 2 , Mo 2 C, SiC and B 4 C; and a binder matrix that binds the hard particles and comprises rhenium.
  • a material can include hard particles comprising at least one nitride selected from at least one of HfN, TaN, BN, ZrN, and TiN; and a binder matrix that binds the hard particles and comprises rhenium.
  • a material can include hard particles comprising at least one boride selected from at least one of HfB 2 , ZrB 2 , TaB 2 , TiB 2 , NbB 2 , and WB; and a binder matrix that binds the hard particles and comprises rhenium.
  • FIG. 1 shows one exemplary fabrication flow in making a hardmetal according to one implementation.
  • FIG. 2 shows an exemplary two-step sintering process for processing hardmetals in a solid state.
  • FIGS. 3, 4, 5, 6, 7, and 8 show various measured properties of selected exemplary hardmetals.
  • FIGS. 9 and 10 illustrate examples of the thermal spray methods . Detailed Description
  • compositions of hardmetals are important in that they directly affect the technical performance of the hardmetals in their intended applications, and processing conditions and equipment used during fabrication of such hardmetals.
  • the hardmetal compositions also can directly affect the cost of the raw materials for the hardmetals, and the costs associated with the fabrication processes. For these and other reasons, extensive efforts have been made in the hardmetal industry to develop technically superior and economically feasible compositions for hardmetals.
  • This application describes, among other features, material compositions for hardmetals with selected binder matrix materials that, together, provide performance advantages .
  • Material compositions for hardmetals of interest include various hard particles and various binder matrix materials.
  • the hard particles may be formed from carbides of the metals in columns IVB (e.g., TiC, ZrC, HfC), VB (e.g., VC, NbC, TaC), and VIB (e.g., Cr 3 C 2 , Mo 2 C, WC) in the Periodic Table of Elements.
  • nitrides formed by metals elements in columns IVB (e.g., TiN, ZrN, HfN) and VB (e.g., VN, NbN, and TaN) in the Periodic Table of Elements may also be used.
  • one material composition for hard particles that is widely used for many hardmetals is a tungsten carbide, e.g., the mono tungsten carbide
  • WC WC
  • Various nitrides may be mixed with carbides to form the hard particles. Two or more of the above and other carbides and nitrides may be combined to form WC-based hardmetals or WC-free hardmetals. Examples of mixtures of different carbides include but are not limited to a mixture of WC and TiC, and a mixture of WC, TiC, and TaC.
  • nitrides, carbonitrides, borides, and suicides may also be used as hard particles for hardmetals. Examples of various suitable hard particles are described in this application.
  • the binder matrix in addition to providing a matrix for bonding the hard particles together, can significantly affect the hard and refractory properties of the resulting hardmetals.
  • the binder matrix may include one or more transition metals in the eighth column of the Periodic Table of Elements, such as cobalt (Co) , nickel (Ni) , and iron (Fe) , and the metals in the 6B column such as molybdenum (Mo) and chromium (Cr) . Two or more of such and other binder metals may be mixed together to form desired binder matrices for bonding suitable hard particles.
  • Some binder matrices for example, use combinations of Co, Ni, and Mo with different relative weights.
  • the hardmetal compositions described here were developed in part based on a recognition that the material composition of the binder matrix may be specially configured and tailored to provide high-performance hardmetals to meet specific needs of various applications.
  • the material composition of the binder matrix has significant effects on other material properties of the resulting hardmetals, such as the elasticity, the rigidity, and the strength parameters (including the transverse rupture strength, the tensile strength, and the impact strength) .
  • the inventor recognized that it was desirable to provide the proper material composition for the binder matrix to better match the material composition of the hard particles and other components of the hardmetals in order to enhance the material properties and the performance of the resulting hardmetals.
  • these hardmetal compositions use binder matrices that include rhenium, a nickel-based superalloy or a combination of at least one nickel-based superalloy and other binder materials.
  • binder matrices that include rhenium, a nickel-based superalloy or a combination of at least one nickel-based superalloy and other binder materials.
  • Other suitable binder materials may include, among others, rhenium (Re) or cobalt.
  • a Ni-based superalloy exhibits a high material strength at a relatively high temperature .
  • the resulting hardmetal formed with such a binder material can benefit from the high material strength at high temperatures of rhenium and KTi-superalloy and exhibit enhanced performance at high temperatures.
  • compositions of the hardmetals described in this application may include the binder matrix material from about 3% to about 40% by volume of the total materials in the hardmetals so that the corresponding volume percentage of the hard particles is about from 97% to about 60%, respectively.
  • the binder matrix material in certain implementations may be from about 4% to about 35% by volume out of the volume of the total hardmetal materials.
  • compositions of the hardmetals may have from about 5% to about 30% of the binder matrix material by volume out of the volume of the total hardmetal materials.
  • the weight percentage of the binder matrix material in the total weight of the resulting hardmetals may be derived from the specific compositions of the hardmetals.
  • the binder matrices may be formed primarily by a nickel-based superalloy, and by various combinations of the nickel-based superalloy with other elements such as Re, Co, Ni, Fe, Mo, and Cr.
  • a Ni-based superalloy of interest may comprise, in addition to Ni, elements Co, Cr, Al, Ti, Mo, W, and other elements such as Ta, Nb, B, Zr and C.
  • Ni-based W superalloys may include the following constituent metals in weight percentage of the total weight of the superalloy: Ni from about 30% to about 70%, Cr from about 10% to about 30%, Co from about 0% to about 25%, a total of Al and Ti from about 4% to about 12%, Mo from about 0% to about 10%, W from about 0% to about 10%, Ta from about 0% to about 10%, Nb from about 0% to about 5%, and Hf from about 0% to about 5%.
  • Ni-based superalloys may also include either or both of Re and Hf, e.g., Re from 0% to about 10%, and Hf from 0% to about 5%.
  • Ni-based superalloy with Re may be used in applications under high temperatures.
  • a Ni-based super alloy may further include other elements, such as B, Zr, and C, in small amounts.
  • Compounds TaC and NbC have similar properties to a certain extent and may be used to partially or completely substitute or replace each other in hardmetal compositions in some implementations. Either one or both of HfC and NbC also may be used to substitute or replace a part or all of TaC in hardmetal designs.
  • Compounds WC, TiC, TaC may be produced individually and then mixed to form a mixture or may be produced in a form of a solid solution. When a mixture is used, the mixture may be selected from at least one from a group consisting of (1) a mixture of WC, TiC, and TaC,
  • hard particles may be selected from at least one from a group consisting of (1) a solid solution of WC, TiC, and TaC, (2) a solid solution of WC, TiC, and NbC, (3) a solid solution of WC, TiC, and at least one of TaC and NbC, and (4) a solid solution of WC, TiC, and at least one of HfC and NbC.
  • the nickel-based superalloy as a binder material may be in a ⁇ - ⁇ ' phase where the ⁇ ' phase with a FCC structure mixes with the ⁇ phase.
  • the strength increases with temperature within a certain extent .
  • Another desirable property of such a Ni-based superalloy is its high resistance to oxidation and corrosion.
  • the nickel-based superalloy may be used to either partially or entirely replace Co in various Co-based binder compositions.
  • rhenium and a nickel-based superalloy in a binder matrix of a hardmetal can W significantly improve the performance of the resulting hardmetal by- benefiting from the superior performance at high temperatures from presence of Re while utilizing the relatively low-sintering temperature of the Wi-based superalloy to maintain a reasonably low sintering temperature for ease of fabrication.
  • the relatively low content of Re in such binder compositions allows for reduced cost of the binder materials so that such materials be economically feasible.
  • Such a nickel-based superalloy may have a percentage weight from several percent to 100% with respect to the total weight of all material components in the binder matrix based on the specific composition of the binder matrix.
  • a typical nickel-based superalloy may primarily comprise nickel and other metal components in a ⁇ - ⁇ ' phase strengthened state so that it exhibits an enhanced strength which increases as temperature rises.
  • Various nickel-based superalloys may have a melting point lower than the common binder material cobalt, such as alloys under the trade names Rene-95, Udimet-700, Udimet-720 from Special Metals which comprise primarily Ni in combination with Co, Cr, Al, Ti, Mo, Nb, W, B, and Zr.
  • cobalt such as alloys under the trade names Rene-95, Udimet-700, Udimet-720 from Special Metals which comprise primarily Ni in combination with Co, Cr, Al, Ti, Mo, Nb, W, B, and Zr.
  • the nickel-based superalloy can be used in the binder to provide a high material strength and to improve the material hardness of the resulting hardmetals, at high temperatures near or above 500° C.
  • Tests of some fabricated samples have demonstrated that the material hardness and strength for hardmetals with a Ni-based superalloy in the binder can improve significantly, e.g., by at least 10%, at low operating temperatures in comparison with similar material compositions without Ni-based superalloy in the binder.
  • the following table show measured hardness parameters of samples P65 and P46A with Ni-based superalloy in the binder in comparison with samples P49 and P47A with pure Co as the binder, where the compositions of the samples are listed in Table 4. Effects of Ni-based Superalloy (NS) in Binder
  • hardmetal samples with Ni-based superalloy in the binder can exhibit a material hardness that is significantly higher than that of similar hardmetal samples without having a Ni-based superalloy in the binder.
  • Ni-based superalloy as a binder material can also improve the resistance to corrosion of the resulting hardmetals or cermets in comparison with hardmetals or cermets using the conventional cobalt as the binder.
  • a nickel-based superalloy may be used alone or in combination with other elements to form a desired binder matrix.
  • Other elements that may be combined with the nickel-based superalloy to form a binder matrix include but are not limited to, another nickel-based superalloy, other non-nickel-based alloys, Re, Co, Ni, Fe, Mo, and Cr.
  • Rhenium as a binder material may be used to provide strong bonding of hard particles and in particular can produce a high melting point for the resulting hardmetal material.
  • the melting point of rhenium is about 3180° C, much higher than the melting point of 1495° C of the commonly-used cobalt as a binder material.
  • This feature of rhenium partially contributes to the enhanced performance of hardmetals with binders using Re, e.g., the enhanced hardness and strength of the resulting hardmetals at high temperatures.
  • Re also has other desired properties as a binder material. For example, the hardness, the transverse rapture strength, the fracture toughness,
  • •Mfl and the melting point of the hardmetals with Re in their binder matrices can be increased significantly in comparison with similar hardmetals without Re in the binder matrices.
  • a hardness Hv over 2600 Kg/mm 2 has been achieved in exemplary WC-based hardmetals with Re in the binder matrices.
  • the melting point of some exemplary WC- based hardmetals, i.e., the sintering temperature has shown to be greater than 2200° C.
  • the sintering temperature for WC-based hardmetals with Co in the binders in Table 2.1 in the cited Brookes is below 1500° C.
  • a hardmetal with a high sintering temperature allows the material to operate at a high temperature below the sintering temperature.
  • tools based on such Re-containing hardmetal materials may operate at high speeds to reduce the processing time and the overall throughput of the processing.
  • the use of Re as a binder material in hardmetals may present limitations in practice.
  • the desirable high-temperature property of Re generally leads to a high sintering temperature for fabrication.
  • the oven or furnace for the conventional sintering process needs to operate at or above the high sintering temperature.
  • Ovens or furnaces capable of operating at such high temperatures, e.g., above 2200° C, can be expensive and may not be widely available for commercial use.
  • 5,476,531 discloses a use of a rapid omnidirectional compaction (ROC) method to reduce the processing temperature in manufacturing WC-based hardmetals with pure Re as the binder material from 6% to 18% of the total weight of each hardmetal.
  • This ROC process is still expensive and is generally not suitable for commercial fabrication.
  • One potential advantage of the hardmetal compositions and the composition methods described here is that they may provide or allow for a more practical fabrication process for fabricating hardmetals with either Re or mixtures of Re with other binder materials in the binder matrices.
  • this two-step process makes it possible to fabricate hardmetals where Re is at or more than 25% of the total weight of the binder matrix of the resulting hardmetal.
  • Such hardmetals with Re at or more than 25% may be used to achieve a high hardness and a high material strength at high temperatures .
  • W rapid omnidirectional compaction
  • Another limitation of using pure Re as a binder material for hardmetals is that Re oxidizes severely in air at or above about 35O 0 C. This poor oxidation resistance may dramatically reduce the use of pure Re as binder for any application above about 300 0 C. Since Ni-based superalloy has exceptionally strength and oxidation resistance under 1000 "C, a mixture of a Ni-based superalloy and Re where Re is the dominant material in the binder may be used to improve the strength and oxidation resistance of the resulting hardmetal using such a mixture as the binder.
  • the addition of Re into a binder primarily comprised of a Ni-based superalloy can increase the melting range of the resulting hardmetal, and improve the high temperature strength and creep resistance of the Ni-based superalloy binder.
  • the percentage weight of the rhenium in the binder matrix should be between a several percent to essentially 100% of the total weight of the binder matrix in a hardmetal.
  • the percentage weight of rhenium in the binder matrix should be at or above 5%.
  • the percentage weight of rhenium in the binder matrix may be at or above 10% of the binder matrix.
  • the percentage weight of rhenium in the binder matrix may be at or above 25% of the total weight of the binder matrix of the resulting hardmetal.
  • Hardmetals with such a high concentration of Re may be fabricated at relatively low temperatures with a two-step process described in this application.
  • cost should be considered in designing binder matrices that include rhenium. Some of the examples given below reflect this consideration.
  • a hardmetal composition includes dispersed hard particles having a first material, and a binder matrix having a second, different material that includes rhenium, where the hard particles are spatially dispersed in the binder matrix in a substantially uniform manner.
  • the binder matrix may be a mixture of Re and other binder materials to reduce the total content of Re to in part reduce the overall cost of the raw materials and in part to explore the presence of other binder materials to enhance the performance of the binder matrix.
  • binder matrices having mixtures of Re and other binder materials include, mixtures of Re and at least one Ni-based superalloy, mixtures of Re, Co and at least one Ni.-based superalloy, mixtures of Re and Co, and others.
  • Cermets TiC particles bound by a mixture of KTi and Mo or a mixture of Ni and Mo 2 C are cermets. Cermets as described here further include hard particles formed by mixtures of TiC and TiN, of TiC, TiN, WC, TaC, and NbC with the binder matrices formed by the mixture of Ni and Mo or the mixture of Ni and Mo 2 C. For each hardmetal composition, three different weight percentage ranges for the given binder material in the are listed. As an example, the binder may be a mixture of a Ni-based superalloy and cobalt, and the hard particles may a mixture of WC, TiC, TaC, and NbC.
  • the binder may be from about 2% to about 40% of the total weight of the hardmetal. This range may be set to from about 3% to about 35% in some applications and may be further limited to a smaller range from about 4% to about 30% in other applications .
  • Fabrication of hardmetals with Re or a nickel-based superalloy in binder matrices may be carried out as follows. First, a powder with desired hard particles such as one or more carbides or carbonitrides is prepared. This powder may include a mixture of different carbides or a mixture of carbides and nitrides. The powder is mixed with a suitable binder matrix material that includes Re or a nickel-based superalloy. In addition, a pressing lubricant, e.g., a wax, may be added to the mixture.
  • a pressing lubricant e.g., a wax
  • the mixture of the hard particles, the binder matrix material, and the lubricant is mixed through a milling or attriting process by milling or attriting over a desired period, e.g., hours, to fully mix the materials so that each hard particle is coated with the binder matrix material to facilitate the binding of the hard particles in the subsequent processes.
  • the hard particles should also be coated with the lubricant material to lubricate the materials to facilitate the mixing process and to reduce or eliminate oxidation of the hard particles.
  • pressing, pre- sintering, shaping, and final sintering are subsequently performed to the milled mixture to form the resulting hardmetal.
  • the sintering process is a process for converting a powder material into a continuous mass by heating to a temperature that is below the melting temperature of the hard particles and may be performed after preliminary compacting by pressure. During this process, the binder material is densified to form a continuous binder matrix to bind hard particles therein. One or more additional coatings may be further formed on a surface of the resulting hardmetal to enhance the performance of the hardmetal.
  • FIG. 1 is a flowchart for this implementation of the fabrication process.
  • the manufacture process for cemented carbides includes wet milling in solvent, vacuum drying, pressing, and liquid-phase sintering in vacuum.
  • the temperature of the liquid-phase sintering is between melting point of the binder material (e.g., Co at 1495°C) and the eutectic temperature of the mixture of hardmetal (e.g., WC-Co at 1320 0 C).
  • the sintering temperature of cemented carbide is in a range of 1360 to 1480 0 C.
  • manufacture process is same as conventional cemented carbide process.
  • the principle of liquid phase sintering in vacuum is applied in here.
  • the sintering temperature is slightly higher than the eutectic temperature of binder alloy and carbide.
  • the sintering condition of P17 25% of Re in binder alloy, by weight
  • the sintering condition of P17 25% of Re in binder alloy, by weight
  • FIG. 2 shows a two-step fabrication process based on a solid-state phase sintering for fabricating various hardmetals described in this application.
  • hardmetals that can be fabricated with this two-step sintering method include hardmetals with a high concentration of Re in the binder matrix that would otherwise require the liquid-phase sintering at high temperatures.
  • This two-step process may be implemented at relatively low temperatures, e.g., under 2200° C, to utilize commercially feasible ovens and to produce the hardmetals at reasonably low costs.
  • the liquid phase sintering is eliminated in this two-step process because the liquid phase sintering may not be practical due to the generally high eutectic temperatures of the binder alloy and carbide.
  • the first step of this two-step process is a vacuum sintering where the mixture materials for the binder matrix and the hard particles are sintered in vacuum.
  • the mixture is initially processed by, e.g., wet milling, drying, and pressing, as performed in conventional processes for fabricating cemented carbides.
  • This first step of sintering is performed at a temperature below the eutectic temperature of the binder alloy and the hard particle materials to remove or eliminate the interconnected porosity.
  • the second step is a solid phase sintering at a temperature below the eutectic temperature and under a pressured condition to remove and eliminate the remaining porosities and voids left in the sintered mixture after the first step.
  • a hot isostatic pressing (HIP) process may be used as this second step sintering. Both heat and pressure are applied to the material during the sintering to reduce the processing temperature which would otherwise be higher in absence of the pressure.
  • a gas medium such as an inert gas may be used to apply and transmit the pressure to the sintered mixture. The pressure may be at or over 1000 bar. Application of pressure in the HIP process lowers the required processing temperature and allows for use of conventional ovens or furnaces .
  • the temperatures of solid phase sintering and HIPping for achieving fully condensed materials are generally significantly lower than the temperatures for liquid phase sintering.
  • the sample P62 which uses pure Re as the binder may be fully densified by vacuum sintering at 2200 0 C for one to two hours and then HIPping at about 2000 0 C under a pressure of 30,000 PSI in the inert gas such as Ar for about one hour.
  • the use of ultra fine hard particles with a particulate dimension less than 0.5 micron can reduce the sintering temperature for fully densifying the hardmetals (fine particles are several microns in size) .
  • TABLE 3 further lists compositions of the above three exemplary nickel-based superalloys, Udimet720 (U720) , Rene' 95 (R-95) , and Udimet700 (U700) , respectively.
  • TABLE 4 lists compositions of exemplary hardmetals, both with and without rhenium or a nickel-based superalloy in the binder matrices.
  • the material composition for Lot P17 primarily includes 88 grams of T32 (WC) , 3 grams of 132 (TiC) , 3 grams of A31 (TaC), 1.5 grams of Hl (Re) and 4.5 grams of L2 (R-95) as binder, and 2 grams of a wax as lubricant.
  • Lot P58 represents a hardmetal with a nickel-based superalloy L2 as the only binder material without Re. These hardmetals were fabricated and tested to illustrate the effects of either or both of rhenium and a nickel- based superalloy as binder materials on various properties of the resulting hardmetals. TABLES 5-8 further provide summary information of compositions and properties of different sample lots as defined above . [0044] FIGS. 3 through 8 show measurements of selected hardmetal samples of this application. FIGS. 3 and 4 show measured toughness and hardness parameters of some exemplary hardmetals for the steel cutting grades. FIGS. 5 and 6 show measured toughness and hardness parameters of some exemplary hardmetals for the non-ferrous cutting grades.
  • FIG. 7 shows measurements of the hardness as a function of temperature for some samples.
  • FIGS. 7 and 8 also show measurements of commercial C2 and C6 carbides under the same testing conditions, where FIG. 7 shows the measured hardness and FIG. 8 shows measured change in hardness from the value at the room temperature (RT) .
  • RT room temperature
  • the exemplary categories of hardmetal compositions are described below to illustrate the above general designs of the various hardmetal compositions to include either of Re and Nickel- based superalloy, or both.
  • the exemplary categories of hardmetal compositions are defined based on the compositions of the binder matrices for the resulting hardmetals or cermets.
  • the first category uses a binder matrix having pure Re
  • the second category uses a binder matrix having a Re-Co alloy
  • the third category uses a binder matrix having a Ni-based superalloy
  • the fourth category uses a binder matrix having an alloy having a Ni-based superalloy in combination with of Re with or without Co.
  • hard and refractory particles used in hardmetals of interest may include, but are not limited to, carbides, nitrides, carbonitrides, borides, and suicides.
  • Carbides include WC, TiC, TaC, HfC, NbC, Mo 2 C, Cr 2 C 3 , VC, ZrC, B 4 C, and SiC.
  • Nitrides include TiN, ZrN, HfN, VN, NbN, TaN, and BN.
  • Examples of Carbonitrides include Ti (C,N), Ta (C,N), Nb(CN), Hf(CN), Zr(C,N), and V(C 7 N).
  • Examples of Borides include TiB 2 , ZrB 2 , HfB 2 , TaB 2 , VB 2 , MoB 2 , WB, and W 2 B.
  • examples of Suicides are TaSi 2 , Wsi 2 , NbSi 2 , and MoSi 2 .
  • the above-identified four categories of hardmetals or cermets can also use these and other hard and refractory particles.
  • the Re may be approximately from 5% to 40% by volume of all material compositions used in a hardmetal or cermet. For example, the sample with a lot No.
  • P62 in TABLE 4 has 10% of pure Re, 70%of WC, 15% of TiC, and 5% of TaC by volume. This composition approximately corresponds to 14.48% of Re, 75.43% of WC, 5.09% of TiC and 5.0% of TaC by weight.
  • the Specimen P62-4 was vacuum sintered at 2100° C for about one hour and 2158° C for about one hour. The density of this material is about 14.51g/cc, where the calculated density is 14.50 g/cc.
  • the average hardness Hv is 2627+35 Kg/mm 2 for 10 measurements taken at the room temperature under a load of 10 Kg.
  • the measured surface fracture toughness K sc is about 7.4 xlO 5 Pa-m 1/2 estimated by Palmvist crack length at a load of 10 Kg.
  • P66 in TABLE 4 This sample has about 20% of Re, 60% of WC, 15% of TiC, and 5% of TaC by volume in composition. In the weight percentage, this sample has about 27.92% of Re, 62.35% of WC, 4.91% of TiC, and 4.82% of TaC.
  • the Specimen P66-4 was first processed with a vacuum sintering process at about 2200° C for one hour and was then sintered in the solid-phase with a HIP process to remove porosities and voids.
  • the density of the resulting hardmetal is about 14.40g/cc compared to the calculated density of 15.04g/cc.
  • the average hardness Hv is about 2402 ⁇ 44 Kg/mm 2 for 7 different measurements taken at the room temperature under a load of 10 Kg.
  • the surface fracture toughness K sc is about 8.1 xl ⁇ s Pa-m 1/2 .
  • the sample P66 and other compositions described here with a high concentration of Re with a weight percentage greater than 25%, as the sole binder material or one of two or more different binder materials in the binder, may be used for various applications at high operating temperatures and may be manufactured by using the two-step process based on solid-phase sintering.
  • microstructures and properties of Re bound multiples types of hard refractory particles may provide advantages over Re-bound WC material.
  • Re bound WC-TiC-TaC may have better crater resistance in steel cutting than Re bound WC material.
  • materials formed by refractory particles of Mo 2 C and TiC bound in a Re binder are examples of hard refractory particles.
  • the Re-Co alloy may be about from 5 to 40 Vol% of all material compositions used in the composition.
  • the Re-to-Co ratio in the binder may vary from 0.01 to 0.99 approximately.
  • Inclusion of Re can improve the mechanical properties of the resulting hardmetals, such as hardness, strength and toughness special at high temperature compared to Co bounded hardmetal . The higher Re content is the better high temperature properties are for most materials using such a binder matrix.
  • the sample P31 in TABLE 4 is one example within this category with 2.5% of Re, 7.5% of Co, and 90% of WC by volume, and 3.44% of Re, 4.40% of Co and 92.12% of WC by weight.
  • the Specimen P31-1 was vacuum sintered at 1725C for about one hour, slight under sintering with some porosities and voids.
  • the density of the resulting hardmetal is about 15.16 g/cc (calculated density at 15.27 g/cc).
  • the average hardness Hv is about 1889+18 Kg/mm 2 at the room temperature under 10 Kg and the surface facture toughness K sc is about 7.7 xlO 6 Pa-m 1/2 .
  • the Specimen P31-1 was treated with a hot isostatic press (HIP) process at about 1600C / 15Ksi for about one hour after sintering.
  • HIP hot isostatic press
  • the HIP reduces or substantially eliminates the porosities and voids in the compound to increase the material density.
  • the measured density is about 15.25g/cc (calculated density at 15.27 g/cc) .
  • the measured hardness Hv is about 1887+12 Kg/mm 2 at the room temperature under 10 Kg.
  • the surface fracture toughness K sc is about 7.6 xlO 6 Pa-m 1/2 .
  • P32 in TABLE 4 with 5.0% of Re, 5.0% of Co, and 90% of WC in volume (6.75% of Re, 2.88% of Co and 90.38% of WC in weight) .
  • the Specimen P32-4 was vacuum sintered at 1800C for about one hour.
  • the measured density is about 15.58 g/cc in comparison with the calculated density at 15.57 g/cc.
  • the measured hardness Hv is about 2065 Kg/mm 2 at the room temperature under 10 Kg.
  • the surface fracture toughness K sc is about 5.9 xlO 6 Pa-m 1/2 .
  • the Specimen P32-4 was also HIP at 1600C / 15Ksi for about one hour after Sintering.
  • the measured density is about 15.57g/cc (calculated density at 15.57 g/cc) .
  • the average hardness Hv is about 2010+12 Kg/mm 2 at the room temperature under 10 Kg.
  • the surface fracture toughness K sc is about 5.8 xlO 6 Pa-m 1/2 .
  • the third example is P33 in TABLE 4 which has 7.5% of Re, 2.5% of Co, and 90% of WC by volume and 9.93% of Re, 1.41% of Co and 88.66% of WC by weight.
  • the Specimen P33-7 was vacuum sintered at 1950C for about one hour and was under sintering with porosities and voids.
  • the measured density is about 15.38 g/cc (calculated density at 15.87 g/cc).
  • the measured hardness Hv is about 2081 Kg/mm 2 at the room temperature under a force of 10 Kg.
  • the surface fracture toughness Ksc is about 5.6 xlO 6 Pa-m 1/2 .
  • the Specimen P33-7 was HIP at 1600C / 15Ksi for about one hour after Sintering.
  • the average hardness Hv is measured at about 2039+18 Kg/mm 2 at the room temperature under 10 Kg.
  • the surface fracture toughness Ksc is about 6.5 xlO 6 Pa-m 1/2 .
  • the third category is based on binder matrices with Ni-based superalloys from 5 to 40% in volume of all materials in the resulting hardmetal.
  • Ni-based superalloys are a family of high temperature alloys with ⁇ ' strengthening. Three different strength alloys, Rene' 95, Udimet 720, and Udimet 700 are used as examples to demonstrate the effects of the binder strength on mechanical properties of the final hardmetals.
  • the Ni-based superalloys have a high strength specially at elevated temperatures. Also, these alloys have good environmental resistance such as resistance to corrosion and oxidation at elevated temperature.
  • Ni- based superalloys can be used to increase the hardness of Ni-based superalloy bound hardmetals when compared to Cobalt bound hardmetals.
  • the tensile strengths of the Ni-based superalloys are much stronger than the common binder material cobalt as shown by TABLE 6. This further shows that Ni-based superalloys are good binder materials for hardmetals.
  • P58 in TABLE 4 which has 7.5% of Rene'95, 0.6% of VC, and 91.9% of WC in weight and compares to cobalt bound P54 in TABLE 4 (8% of Co, 0.6% of VC, and 91.4% of WC) .
  • the hardness of P58 is significant higher than P54 as shown in TABLE 7.
  • the fourth category is Ni-based superalloy plus Re as binder, e.g., approximately from 5% to 40 % by volume of all materials in the resulting hardmetal or cermet. Because addition of Re increases the melting point of binder alloy of Ni-based superalloy plus Re, the processing temperature of hardmetal with Ni- based superalloy plus Re binder increases as the Re content increases. Several hardmetals with different Re concentrations are listed in TABLE 8. TABLE 9 further shows the measured properties of the hardmetals in TABLE 8.
  • Ni-based superalloy plus Re and Co as binder which is also about 5% to 40% by volume .
  • Exemplary compositions of hardmetals bound by Ni-based superalloy plus Re and Co are list in TABLE 10 .
  • Ni-based superalloys not only exhibit excellent strengths at elevated temperatures but also possess outstanding resistances to oxidation and corrosion at high temperatures.
  • Ni- based superalloys have complex microstructures and strengthening mechanisms. In general, the strengthening of Ni-based superalloys is primarily due to precipitation strengthening of ⁇ - ⁇ ' and solid- solution strengthening. The measurements the selected samples demonstrate that Ni-based superalloys can be used as a high- performance binder materials for hardmetals.
  • TABLE 11 lists compositions of selected samples by their weight percentages of the total weight of the hardmetals.
  • the WC particles in the samples are 0.2 ⁇ m in size.
  • TABLE 12 lists the conditions for the two-step process performed and measured densities, hardness parameters, and toughness parameters of the samples.
  • the sample P54 uses the conventional binder consisting of Co.
  • the Ni-superalloy R-95 is used in the sample P58 to replace Co as the binder in the sample P54.
  • the Hv increases from 2090 of P54 to 2246 of P58.
  • the mixture of Re and Co is used to replace Co as binder and the corresponding Hv increases from 2090 of P54 to 2133 of P5S.
  • the samples P72, P73, P74 have the same Re content but different amounts of Co and R95.
  • the mixtures of Re, Co, and R95 are used in samples P73 and P74 to replace the binder having a mixture of Re and Co as the binder in the sample 72.
  • the hardness Hv increases from 2041 (P72) to 2217 (P73) and 2223 (P74) .
  • TABLE 15 further shows measured hardness parameters under various temperatures for the selected samples, where the Knoop hardness H k were measured under a load of 1 Kg for 15 seconds on a Nikon QM hot hardness tester and R is a ratio of H k at an elevated testing temperature over H k at 25°C.
  • the hot hardness specimens of C2 and C6 carbides were prepared from inserts SNU434 which were purchased from MSC Co. (Melville, WY) .
  • each measured value at a given temperature is an averaged value of
  • Inclusion of Re in the binder matrices of the hardmetals increases the melting point of binder alloys that include Co-Re, Ni superalloy-Re, Ni superalloy-Re-Co.
  • the melting point of the sample P63 is much higher than the temperature of 2200 0 C used for the solid-phase sintering process.
  • Hot hardness values of such hardmetals with Re in the binders e.g., P17 to P63
  • the above measurements reveal that an increase in the concentration of Re in the binder increases the hardness at high temperatures.
  • the sample P62A with pure Re as the binder has the highest hardness.
  • the sample P63 with a binder composition of 94% of Re and 6 % of the Ni-based superalloy R95 has the second highest hardness.
  • the samples P40A(71.9%Re- 29.1%R95), P49(69.9%Re-30.1%R95) , P51 (88.5%Re-ll .5%R95) , and P50 (71.9%Re-28.1%R95) are the next group in their hardness.
  • the sample P48 with 62.5% of Re and 37.5% of R95 in its binder has the lowest hardness at high temperatures among the tested materials in part because its Re content is the lowest.
  • a hardmetal or cermet may include TiC and TiN bonded in a binder matrix having Ni and Mo or Mo 2 C.
  • the binder Ni of cermet can be fully or partially replaced by Re, by Re plus Co, by Ni-based superalloy, by Re plus Ni-based superalloy, and by Re plus Co and Ni-based superalloy.
  • Samples P38 and P39 are examples of Ni-bound cermets.
  • the sample P34 is an example of Rene95-bound Cermet.
  • TABLES 17-29 list additional compositions with 3 exemplary composition ranges 1, 2, and 3 which may be used for different applications.
  • compositions that use Ni -based superalloy (NBSA) in a binder for binding a nitride from nitrides of IVb &Vb columns of the Periodic Table .
  • NBSA Ni -based superalloy
  • compositions that use Re and Ni-based superalloy (Re+NBSA) in a binder for binding a carbide from carbides of IVb, Vb, & VIb or a nitride from nitrides of IVb & Vb.
  • the range of the binder is from l%Re + 99% superalloy to 99% Re + 1% superalloy.
  • the range of Binder is from l%Re + 99% Co to 99% Re + l%Co.
  • compositions that use Ni-based superalloy (NBSA) and Co in a binder for binding a carbide from carbides of IVb, Vb, & VIb or a nitride from nitrides of IVb & Vb.
  • the range of Binder is from 1%NBSA + 99% Co to 99%NBSA + l%Co.
  • NBSA+Co NBSA 0.03 to 0.02 to 0.04 to 0.027 to 0.05 to 29.7 0.03 to 39.6 31 34.7 27 22
  • VN Co 0.03 to 0.04 to 0.04 to 0.055 to 0.05 to 29.7 0.066 to 39.6 44 34.7 40 34
  • compositions that use Re, Ni-based superalloy (NBSA), and Co in a binder for binding a carbide from carbides of IVb, Vb, & VIb or a nitride from nitrides of IVb & Vb.
  • the range of Binder is from 0.5%Re + 0.5% Co+ 99% superalloy to 99% Re + 0.5% Co + 0.5% Superalloy to 0.5%Re + 99% Co+ 0.5% Superalloy
  • TABLK 25 Compositions that use Re and Ni-based superalloy (NBSA) in a binder for binding WC+TiC or WC+TaC or WC+TiC+TaC
  • compositions that use Re , Ni-based superalloy (NBSA) 7 and Co in a binder for binding WC+TiC or WC+TaC or WC+TiC+TaC .
  • the range of Binder is from 0 . 5%Re + 99 . 5% superalloy to 99 . 5% Re + 0 . 5% Superalloy to 0 . 5%Re + 0 . 5% Superalloy+ 99% Co .
  • TaC 0.5 to 0.5 to 24 1 to 20 O. ⁇ 3 to 21 2 to 18 1. 8 tol9 22
  • TABLES 30-41 list exemplary cermet compositions with 3 exemplary composition ranges 1, 2, and 3 which may be used for different applications.
  • NBSA Ni-based superalloy
  • TaC O L to 15 0 25 to 0 15 to 0.4 to 0.2 to 0.5 to 36 12 30 10 26
  • NBSA Re and Ni-based superalloy
  • TABLK 34 Compositions that use Re and Co in a binder for binding TiC+ Mo 2 C, or TiN+ Mo 2 C, or TiC+TiN+ Mo 2 C, or TiC+TiN+Mo 2 C+WC+TaC+VC+Cr 2 C 3
  • Re+Co Re 0.03 to 0.1 tc 64 0.04 to 0.13 to 0.05 to 0.16 to 29.7 26.73 60 24.75 57
  • NBSA Ni-based superalloy
  • compositions that use Re, Co, and Ni-based superalloy (NBSA) in a binder for binding TiC and Mo 2 C, or TiN and Mo 2 C, or TiC, TiN, and Mo 2 C, or TiC, TiN, Mo 2 C, WC, TaC, VC, and Cr 2 C 3
  • NBSA Ni-based superalloy
  • TABLK 38 Compositions that use Re , Ni , and Ni-based superalloy (NBSA) in a binder for binding TiC+ Mo 2 C, or TiN+ Mo 2 C, or TiC+TiN+ Mo 2 C, or TiC+TiN+Mo 2 C+WC+TaC+VC+Cr 2 C 3
  • NBSA Ni-based superalloy
  • NBSA Ni-based superalloy
  • compositions that use Re, Ni, Co, and Ni-based superalloy (NBSA) in a binder for binding TiC+ Mo 2 C, or TiN+ Mo 2 C, or TiC+TiN+ Mo 2 C, or TiC+TiN+Mo 2 C+WC+TaC+VC+Cr 2 C 3
  • NBSA Ni-based superalloy
  • TABLES 42-51 list additional examples of various compositions with 3 exemplary composition ranges 1, 2, and 3 which may be used for different applications. Similar to some compositions described above, some compositions in TABLES 42-51 may be particularly useful for applications at high temperatures as indicated in the last row under "estimated melting points.”
  • binder matrix materials with rhenium, a nickel-based superalloy or a combination of both can enhance material performance at high temperatures.
  • Tungsten is typically- used as a constituent element in various hard particles such as carbides, nitrides, carbonitrides, borides, and suicides.
  • tungsten can significantly raise the melting point of the final hardmetal materials to the range of about 2500 to about 3500 0 C.
  • hardmetals using W-based binder matrix materials can be used in applications at high temperatures that may not be possible with other materials.
  • certain compositions that use a binder matrix based on tungsten (W) shown in TABLES 43-48 show expected high melting points around 3500 0 C.
  • each nitride may be substituted by a combination of a nitride and carbide as the hard particle material .
  • a material under this design includes hard particles comprising at least one nitride from nitrides of IVB and VB columns in the periodic table and one carbide from carbides of IVB, VB and VIB columns in the periodic table, and a binder matrix that binds the hard particles and comprises rhenium and cobalt.
  • Re Re 3 to 40 9.5 to 4 to 35 12.5 to 5 to 30 15 to 1800 to Bound 69.5 65 60 2200
  • Re Re Re 3 to 40 7.5 to 4 to 35 10 to 5 to 30 12.5 to 2000 to Bound 64 59 54 2400
  • TaSi 2 TaSi 2 60 to 97 38 to 65 to 96 43 to 70 to 95 49 to 93 91 88
  • W bound a carbide from carbides of IVb , Vb , & VIb or a nitride from nitrides of IVb & Vb .
  • Re and W (Re+W) bound a carbide from carbides of IVb, Vb, & VIb or a nitride from nitrides of IVb & Vb.
  • the range of Binder is from l%Re + 99% W to 99% Re + 1%W.
  • Re and W (Re+W) bound a boride from borides of IVb , Vb, & VIb or a suicide from suicides of IVb & Vb .
  • the range of Binder is from l%Re + 99% W to 99% Re + 1%W
  • Re and Co (Re+Co) bound a carbide from carbides of IVb, Vb, & VIb or a nitride from nitrides of IVb & Vb.
  • the range of Binder is from l%Re + 99% Co to 99% Re + l%Co.
  • Re and Co (Re+Co) bound a boride from borides of IVb, Vb, & VIb or a suicide from suicides of IVb & Vb.
  • the range of Binder is from l%Re + 99% Co to 99% Re + l%Co.
  • Re and Mo (Re+Mo) bound a carbide from carbides of IVb, Vb, & VIb.
  • the range of Binder is from l%Re + 99% Mo to 99% Re + l%Mo.
  • Re and Ni (Re+Ni) bound a carbide from carbides of IVb, Vb, & VIb.
  • the range of Binder is from l%Re + 99% Ni to 99% Re + l%Ni.
  • Re and Cr (Re+Cr) bound a carbide from carbides of IVb, Vb, S- VIb .
  • the range of Binder is from l%Re + 99% Cr to 99% Re + l%Cr .
  • compositions for hardmetals or cermets may be used for a variety of applications.
  • a material as described above may be used to form a wear part in a tool that cuts, grinds, or drills a target object by using the wear part to remove the 0 material of the target object.
  • a tool may include a support part made of a different material, such as a steel. The wear part is then engaged to the support part as an insert.
  • the tool may be designed to include multiple inserts engaged to the support part.
  • some mining drills may include multiple button bits made of a hardmetal material . Examples of such a tool includes a drill, a cutter such as a knife, a saw, a grinder, and a drill.
  • hardmetals descried here may be used to form the entire head of a tool as the wear part for cutting, drilling or other machining operations.
  • the hardmetal particles may also be used to form abrasive grits for polishing or grinding various materials.
  • such hardmetals may also be used to construct housing and exterior surfaces or layers for various devices to meet specific needs of the operations of the devices or the environmental conditions under which the devices operate.
  • the hardmetals described here may be used to manufacture cutting tools for machining metals, alloys, composite materials, plastic materials, wooden materials, and others.
  • the cutting tools may include indexable inserts for turning, milling, boring and drilling, drills, end mills, reamers, taps, hobs and milling cutters.
  • the hardmetal compositions for high-temperature operating conditions described above may have special advantages when used in such cutting tools, e.g., extended tool life and improved productivity by such tools by increasing the cutting speed.
  • the hardmetals described here may be used to manufacture tools for wire drawing, extrusion, forging and cold heading. Also as mold and Punch for powder process. In addition, such hardmetals may be used as wear-resistant material for rock drilling and mining.
  • the hardmetal materials described in this application may be fabricated in bulk forms or as coatings on metal surfaces.
  • Coatings with such new hardmetal materials may be advantageously used to form a hard layer on a metal surface to achieve desired hardness that would otherwise be difficult to achieve with the underlying metal material.
  • Bulk hardmetal materials based on the compositions in this application may be expensive and hence the use of coatings on less expensive metals with lower hardness may be used to reduce the costs of various components or parts with high hardness.
  • a number of powder processes for producing commercial hardmetals may be used to manufacture the hardmetals of this application. As an example, a binder alloy with Re higher than 85% in weight may be fabricated by the process of solid phase sintering to eliminate open porosities then HIP replaces liquid phase sintering.
  • FIG. 9 shows a flowchart for several fabrication methods for materials or structures from the above hardmetal compositions.
  • alloy powders for the binders and the hard particle powders may be mixed with a milling liquid in a wet mixing process with or without a lubricant (e.g., wax).
  • the fabrication flows on the left hand side of FIG. 9 are for fabricating hardmetals with lubricated wet mixing.
  • the mixture is first dried by vacuum drying or spray drying process to produce lubricated grade powder.
  • the lubricated grade power is shaped into a bulky material via pill pressing, extruding, or cold isostatic press (CIP) and shaping.
  • CIP cold isostatic press
  • the bulky material is then heated to remove the lubricant and is sintered in a presintering process.
  • the material may be processed via several different processes.
  • the material may be processed via a liquid phase sintering in vacuum or hydrogen and then further processed by a HIP process to form the final hardmetal parts.
  • the material after the presintering may go through a solid phase sintering to eliminate open porosity and then a HIP process to form the final hardmetal parts .
  • the unlubricated grade power after the drying process may be processed in two different ways to form the final hardmetal parts.
  • the first way as illustrated simply uses hot pressing to complete the fabrication.
  • the second way uses a thermal spray forming process to form the grade powder on a metal substrate in vacuum.
  • the metal substrate is removed to leave the structure by the thermal spray forming as a free-standing material as the final hardmetal part.
  • the free-standing material may be further processed by a HIP process to reduce the porosities if needed.
  • a thermal spray process may be used under a vacuum condition to produce large parts coated with hardmetal materials. For example, surfaces of steel parts and tools may be coated to improve their hardness and thus performance.
  • FIG. 10 shows an exemplary flow chart of a thermal spray process.
  • thermal spray processes are known for coating metal surfaces.
  • ASM Handbook Vol. 7 (P408, 1998) describes the thermal spray as a family of particulate/droplet consolidation processes capable of forming metals, ceramics, intermetallics, composites, and polymers into coatings or freestanding structures.
  • powder, wire, or rods can be injected into combustion or arc-heated jets, where they are heated, melted or softened, accelerated, and directed toward the surface, or substrate, being coated.
  • the particles or droplets rapidly solidify, cool, contract, and incrementally build up to form a deposit on a target surface.
  • a thermal spray process may use chemical (combustion) or electrical (plasma or arc) energy to heat feed materials injected into hot-gas jets to create a stream of molten droplets that are accelerated and directed toward the substrates being coated.
  • chemical (combustion) or electrical (plasma or arc) energy to heat feed materials injected into hot-gas jets to create a stream of molten droplets that are accelerated and directed toward the substrates being coated.
  • Various thermal spray processes are shown in Figure 3 and 4 in ASM Handbook Vol. 7, pages 409-410.
  • Selected hardmetal compositions described here can maintain high material strength and hardness at high temperatures at or above 1500 0 C.
  • certain high-power engines operate at such high temperatures such as various jet and/or rocket engines used in various flying devices and vehicles. More specifically, jet and/or rocket nozzles, including non-erosive nozzle throats and low-erosive nozzle throats, in these and other engines may be partially or entirely made of the selected hardmetal materials described in this application.
  • hardmetals based on one or more of (1) one or more carbides, (2) one or more nitrides, (3) one or more borides and (4) a combination of two or more of (1) , (2) and (3) with a binder material which is either pure Re or a composite binder material with Re as one component.
  • the melting points of various carbides, nitrides, and borides in this application are above 2400 0 C.
  • suitable carbides for the present high-temperature hardmetal materials include TaC, HfC, NbC, ZrC, TiC, WC, VC, Al 4 C 3 , ThC 2 , Mo 2 C, SiC and B 4 C.
  • nitrides for the present high-temperature hardmetal materials include HfN, TaN, BN, ZrN, and TiN.
  • suitable borides for the present high- temperature hardmetal materials include HfB 2 , ZrB 2 , TaB 2 , TiB 2 , NbB 2 , and WB.
  • Two examples of the composite binder material with Re as one component are (1) W and Re and (2) Ta and Re.

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Abstract

La présente invention se rapporte à des compositions de métaux durs comportant chacune des particules dures comprenant une première matière et une matrice de liant contenant une seconde matière différente à base de rhénium ou d'un super alliage au nickel. Du tungstène peut également être utilisé en tant que matière pour la matrice de liant. Un processus de frittage en deux étapes peut être utilisé pour fabriquer ces métaux durs à des températures de frittage relativement faibles dans une phase à l'état solide pour produire des métaux durs quasiment entièrement densifiés. Un revêtement ou une structure à base d'un métal dur peut être formé sur une surface par mise en oeuvre d'un procédé de pulvérisation thermique.
EP06813610A 2005-08-19 2006-08-21 Materiaux a base de metaux durs pour applications a haute temperature Withdrawn EP1922427A4 (fr)

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US71001605P 2005-08-19 2005-08-19
PCT/US2006/032654 WO2007022514A2 (fr) 2005-08-19 2006-08-21 Materiaux a base de metaux durs pour applications a haute temperature

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EP1922427A2 true EP1922427A2 (fr) 2008-05-21
EP1922427A4 EP1922427A4 (fr) 2009-03-18

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CN102815971B (zh) * 2012-08-22 2013-08-21 中南大学 一种Hf(Ta)C超高温复相涂层及其制备方法
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CN101316941A (zh) 2008-12-03
IL189288A0 (en) 2008-06-05
EP1922427A4 (fr) 2009-03-18
WO2007022514A3 (fr) 2008-08-07
CA2617945A1 (fr) 2007-02-22
JP2009504926A (ja) 2009-02-05
AU2006280936A1 (en) 2007-02-22
BRPI0615027A2 (pt) 2011-04-26
WO2007022514A2 (fr) 2007-02-22
KR20080053468A (ko) 2008-06-13

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