EP2606996A1 - Verfahren zum Sinter von Metallmatrixverbundmaterialien - Google Patents

Verfahren zum Sinter von Metallmatrixverbundmaterialien Download PDF

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Publication number
EP2606996A1
EP2606996A1 EP11195717.1A EP11195717A EP2606996A1 EP 2606996 A1 EP2606996 A1 EP 2606996A1 EP 11195717 A EP11195717 A EP 11195717A EP 2606996 A1 EP2606996 A1 EP 2606996A1
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EP
European Patent Office
Prior art keywords
phase
metal
powders
vol
carbide
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EP11195717.1A
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English (en)
French (fr)
Inventor
Alessandro Fais
Serena Bonetti
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EPoS Srl
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EPoS Srl
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Priority to EP11195717.1A priority Critical patent/EP2606996A1/de
Priority to PCT/IB2012/057550 priority patent/WO2013093847A2/en
Publication of EP2606996A1 publication Critical patent/EP2606996A1/de
Withdrawn legal-status Critical Current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
    • C22C1/00—Making non-ferrous alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
    • 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
    • C22C1/1084—Alloys containing non-metals by mechanical alloying (blending, milling)
    • 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
    • C22C29/02—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
    • 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
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • B22F2009/042—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling using a particular milling fluid
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/08—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on tungsten carbide
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • 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
    • C22C29/10—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 titanium carbide

Definitions

  • the present invention relates to a method for sintering metal-matrix composite materials and to the corresponding materials that can be obtained by the aforesaid method.
  • Metal-matrix composite (MMC) materials are very widespread in all applications that are subject to phenomena of abrasion, high temperatures, erosion, and impact, such as for example cutting tools and tools for die-forming of metal materials.
  • the combination of hardness and toughness is obtained thanks to the combination of the properties of a well-distributed metal phase and of a ceramic phase or even a combination of ceramic phases.
  • High speed steels which historically have been used up to the advent of cemented carbides as materials for cutting tools, are still today competitive in industrial applications thanks to their high values of toughness combined with a hardness sufficient for a vast number of uses.
  • the ceramic phase usually comprises tungsten carbide (WC) as single component, but also carbides of titanium (TiC), tantalum (TaC), vanadium (VC), molybdenum (Mo 2 C), chromium (Cr 3 C 2 ), and hafnium (HfC) are used both as single component or in different combinations and proportions thereof.
  • WC tungsten carbide
  • TiC titanium
  • TaC tantalum
  • VC vanadium
  • Mo 2 C molybdenum
  • Cr 3 C 2 chromium
  • hafnium hafnium
  • step iii) to iv) may last, including cooling, up to 20 hours in order to reduce or at least prevent the thermal stresses inside the sintered components.
  • the ceramic phase grows in size and assumes a peculiar faceted shape due to the high orientation dependent free energy of the surfaces.
  • the ECAS sintering apparatus used In order to achieve a contained sintering time, the ECAS sintering apparatus used must be rapidly heated and cooled progressively, but as fast possible.
  • the object of the present invention is to overcome the technical problems described previously; namely:
  • the obj ects of the invention are achieved by a method for sintering a composite material including at least one metal phase and at least one ceramic phase, the method comprising the steps of:
  • the steps that make up a method for sintering metal-matrix composite materials according to a preferred embodiment of the invention will now be described.
  • the composite material that can be obtained using the method according to the invention comprises at least one metal phase and at least one ceramic phase.
  • a monophase metal, a multiphase metal, a single metal element or a metal alloy can be used as metal phase.
  • Providing the at least one metal phase in the form of powders of pre-alloyed metal material (or materials) and providing the at least one ceramic phase, which is also in the form of powders of ceramic material (or materials) are initial steps.
  • the pre-alloyed metal material By providing the pre-alloyed metal material, the possibility of formation of the final metal phase from a mixture of metal elements during sintering is excluded. This is necessary since, as will be seen hereinafter, on account of the high velocities of the sintering process, it is not possible to form the alloy during sintering.
  • the powders of metal material are provided in amounts sufficient to obtain a composite material in which the metal phase has a volume percentage of between 2 vol% and 40 vol%.
  • the average size of the particles of the powders of the (at least one) ceramic phase can range from 1 nm to 500 ⁇ m and can be mono-modal or multi-modal, but it is preferable to have an average size of the particles of less than 5 ⁇ m.
  • a further constraint concerning the metal phase exists, namely, the coefficient of thermal expansion.
  • the method according to the invention envisages that one or more metal phases have a coefficient of thermal expansion of between 0 K -1 and 6 ⁇ 10 -6 K -1 at room temperature.
  • the method according to the invention yields optimal results when each metal phase (in particular, in the case of multiphase metal matrix) has a coefficient of thermal expansion of between 0 K -1 and 6 ⁇ 10 -6 K -1 at room temperature.
  • the metal matrix comprises a single metal phase it is envisaged that this has a coefficient of thermal expansion of between 0 K -1 and 6 ⁇ 10 -6 K -1 at room temperature.
  • metal phase that satisfies said condition is that of an Fe-Ni alloy with a weight percentage of nickel of between 32 wt% and 42 wt%.
  • the operations proceed with mixing of the aforesaid powders (of the metal and ceramic phases), possibly combined with a dry or wet grinding operation, which can be performed at the same time as the mixing step or even prior to this. Grinding becomes necessary in the case where the powders have an average size excessive for the final characteristics that it is intended to bestow on the sintered component.
  • the mixing and/or milling operation can be carried out with the contribution of a mixing agent that is in the liquid phase at room temperature and pressure and that is preferably chosen in a group comprising ethanol, alkanes - preferably heptane, hexane - cyclohexane, water, or polymeric mixing agents, for example silicone or silicone-based compounds.
  • a mixing agent that is in the liquid phase at room temperature and pressure and that is preferably chosen in a group comprising ethanol, alkanes - preferably heptane, hexane - cyclohexane, water, or polymeric mixing agents, for example silicone or silicone-based compounds.
  • the method according to the invention yields optimal results in the case where the steps of mixing of the powders and the possible steps of milling are carried out in the absence of any process-control polymeric agent that at room temperature is in the solid state, such as wax and paraffin.
  • the mixed powders of the (at least one) metal phase and of the (at least one) ceramic phase are then inserted in a mould of sintering equipment.
  • the method according to the invention yields optimal results if the sintering is performed using an electric-current-assisted sintering (ECAS) apparatus.
  • ECAS electric-current-assisted sintering
  • the powders within the mould are then subjected to sintering with a duration of the cycle, comprising a heating step and a cooling step, of between 10 -4 s and 60 s.
  • a duration of the cycle comprising a heating step and a cooling step, of between 10 -4 s and 60 s.
  • the result is that of a composite material with a density of between 90% and 100% of the theoretical density (an ECAS method is described in the document No. WO-A-2010/070623 filed in the name of the present applicant).
  • the method according to the invention yields optimal results in the case where the sintering operation is performed in the absence of protective atmosphere (which for these applications is typically a gaseous protective atmosphere).
  • the sintered material thus obtained has unprecedented values of toughness with high hardness and presents a better performance in the applications of machining with chip removal as compared to known materials.
  • the inventors have moreover found that very satisfactory results in terms of mechanical properties of the sintered composite material are obtained by conducting the heating step in a time range of between 1 ms and 500 ms.
  • the time interval concerned by the heating step is chosen between 1 ms and 100 ms because the effects just mentioned are further amplified.
  • ceramic phase a single phase, for example tungsten carbide (WC), titanium carbide (TiC), titanium nitride (TiN), or titanium carbo-nitride (TiCN), or alternatively a mixture of two or more ceramic phases in different percentages can be provided.
  • WC tungsten carbide
  • TiC titanium carbide
  • TiN titanium nitride
  • TiCN titanium carbo-nitride
  • the usable ceramic phases can comprise at least one carbide of a metal chosen in the group comprising tungsten (WC), titanium (TiC), tantalum (TaC), hafnium (HfC), molybdenum (Mo 2 C), niobium (NbC and Nb 2 C), zirconium (ZrC), vanadium (VC), chromium (Cr 3 C 2 ).
  • the aforesaid ceramic phases can alternatively comprise also the family of the nitrides of the same metals, i.e., tungsten (WN and WN 2 ), titanium (TiN), tantalum (TaN), hafnium (HfN), molybdenum (Mo 2 N), niobium (NbN), zirconium (ZrN), vanadium (VN), chromium (CrN), or carbo-nitrides TiC(1-x)Nx where x is comprised between 0 and 1.
  • Metal particles constituted by an Fe-Ni alloy with 42 wt% of nickel and a coefficient of thermal expansion at room temperature of 6 ⁇ 10 -6 K-1 obtained by a process of mechanical alloying and sifted through a 150- ⁇ m sieve (102 mesh) are mixed without polymer additives in an industrial mixer with powder of tungsten carbide (WC) and titanium carbide (TiC).
  • the weight percentages of each powder are the following: 9.77 wt% of Fe-Ni alloy with 42 wt% of nickel, 79.53 wt% of tungsten carbide, and 10.7 wt% of titanium carbide.
  • the Vickers hardness at 30 kgf and the Palmquist toughness are respectively: 1464 ⁇ 98 HV30 and 24.49 ⁇ 1.58 MPa ⁇ m -0.5 .
  • the grain size of the titanium-carbide phase in the composite material is approximately 2 ⁇ m, whilst the grain size of the tungsten-carbide phase is approximately 1 ⁇ m.
  • the cylinders were ground and polished in order to create a cutting insert with a nose radius of 0.8 mm and an end relief angle of 5° that enables the metal chip to break off during machining.
  • Figure 1A presents a comparison with a similar cutting insert obtained starting from a commercial tool of degree P20 (ISO standard) with a value of Vickers hardness at 30 kgf of 1481 ⁇ 18 HV30 and a value of Palmquist toughness of 16.78 ⁇ 0.5 MPa ⁇ m -0.5 .
  • the insert was brazed on a tool holder and used on a lathe for machining normalized C40 steel with a Brinnel hardness of 210 HB.
  • the cutting speed considered was 120 m/min.
  • the abscissae represent the cutting time expressed in minutes, and the ordinates represent the parameter of wear of the tool VB B according to ISO 3685, expressed in millimetres.
  • the set of data designated by the reference N1 corresponds to a tool using a composite material corresponding to the one described in this example (which will at times be referred to hereinafter for brevity as "tool N1"), whilst the set of data designated by PA refers to the tool of degree P20 mentioned above (which will at times be referred to hereinafter for brevity as "tool PA"). From the comparison, it is immediately evident that already at low cutting speeds the reduction of wear of the cutting edge is appreciable, with obvious benefits in terms of costs and of reduction of machine downtime for replacing the tool. Even more eloquent is the subsequent Figure 1B , which illustrates the same comparison between the tool N1 and the tool PA but performed with a cutting speed increased to 140 m/min.
  • the tool PA shows a wear that is approximately twice that of the cutting edge of the tool N1 made of the material of Example 1.
  • the increase in wear is moreover rather contained as compared to the wear observable on the tool PA, where, assuming as reference the cutting instants corresponding to three minutes and six minutes, there is noted an increase of the wear up to approximately six times the initial value, whilst with the tool N1 the wear presents an increase that reaches approximately three times the initial value.
  • Metal particles constituted by an Fe-Ni alloy with 42 wt% of nickel, with a coefficient of thermal expansion at room temperature of 6 ⁇ 10 -6 K-1 obtained by a process of mechanical alloying and sifted through a 150- ⁇ m sieve (102 mesh) are mixed without polymer additives in an industrial mixer with powder of tungsten carbide (WC) and titanium carbide (TiC).
  • the weight percentages of each powder are the following: 18.65 wt% of Fe-Ni alloy with 42 wt% of nickel and 81.35 wt% of titanium carbide.
  • cylinders of sintered material are obtained with a diameter of 10 mm, a height of 3.56 ⁇ 0.04 mm, and a density of 4.93 ⁇ 0.04 g/cm 3 .
  • the Vickers hardness at 30 kgf and the Palmquist toughness are 1613 ⁇ 48 HV30 and 18.82 ⁇ 3.02 MPa ⁇ m -0.5 respectively.
  • the grain size of the titanium-carbide phase in the composite material is approximately 2 ⁇ m.
  • Figure 2 is similar to Figures 1A and 1B but comprises in just one diagram four sets of data, namely:
  • Metal particles constituted by Fe-Ni alloy with 42 wt% of nickel with a coefficient of thermal expansion at room temperature of 6 ⁇ 10 -6 K -1 obtained by a process of mechanical alloying and sifted through a 150- ⁇ m sieve (102 mesh) are mixed without polymer additives in an industrial mixer with powders of tungsten carbide and titanium carbide.
  • the weight percentages for each powder are the following: 11.81 wt% of Fe-Ni alloy with 42 wt% of nickel, 67.11 wt% of tungsten carbide, and 21.07 wt% of titanium carbide.
  • the grain size of the tungsten-carbide phase in the composite material is approximately 2 ⁇ m, whilst the grain size of tungsten carbide is approximately 1 ⁇ m.
  • Metal particles consisting of Fe-Ni alloy at 36 wt% of nickel with a coefficient of thermal expansion at room temperature of 2 ⁇ 10 -6 K -1 are obtained by a process of atomization and with a maximum size of 45 ⁇ m.
  • the weight percentages for each powder are the following: 11.5 ⁇ 0.5 wt% of Fe-Ni alloy with 42 wt% of nickel, 67.5 ⁇ 0.5 wt% of tungsten carbide, and 21.5 ⁇ 0.5 wt% of titanium carbide.
  • the Vickers hardness at 30 kgf and the Palmquist toughness are, respectively, 1716 ⁇ 27 HV30 and 20.03 ⁇ 0.64 MPa ⁇ m -0.5 .
  • the grain size of the tungsten-carbide phase in the composite material is approximately 2 ⁇ m, whilst the grain size of tungsten carbide is approximately 1 ⁇ m.
  • Figure 3 illustrates a comparison of the performance of the tool PA with tools having a cutting insert made of the material described in Example 3 and Example 4, respectively.
  • Example 3 The difference between the material of Example 3 and that of Example 4 lies in the use of atomized powders instead of powders obtained by mechanical milling.
  • the values of the wear parameter VB B settle substantially on values that are close to each other in the case of the tools N3 and N4, in a way somewhat independent of the cutting speed. Even more evident is the gap with respect to the tools obtained with known materials.
  • Figure 4 illustrates a comparative diagram where the abscissae represent the values of Vickers hardness (HV30) and the ordinates represent the values of Palmquist toughness (K IC ), the latter being expressed in MPa ⁇ m -0.5 , for different materials, namely:
  • the method according to the invention enables materials to be obtained, the properties of which in terms of combination of toughness and hardness fall in an area of the diagram substantially without data regarding known materials obtained with known methods and where there coexist values of toughness and hardness that are unattainable in combination by the aforesaid known sintered materials using known methods.
EP11195717.1A 2011-12-23 2011-12-23 Verfahren zum Sinter von Metallmatrixverbundmaterialien Withdrawn EP2606996A1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP11195717.1A EP2606996A1 (de) 2011-12-23 2011-12-23 Verfahren zum Sinter von Metallmatrixverbundmaterialien
PCT/IB2012/057550 WO2013093847A2 (en) 2011-12-23 2012-12-20 A method for sintering metal-matrix composite materials

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP11195717.1A EP2606996A1 (de) 2011-12-23 2011-12-23 Verfahren zum Sinter von Metallmatrixverbundmaterialien

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3862110A1 (de) * 2020-02-07 2021-08-11 EPoS S.r.L. Magnetische verbundmaterialien und verfahren zu ihrer herstellung
US20220023944A1 (en) * 2020-03-27 2022-01-27 Magotteaux International S.A. Composite wear component
CN114346238A (zh) * 2022-01-14 2022-04-15 中国科学院兰州化学物理研究所 一种超高温自润滑抗磨复合材料及其制备方法和应用

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103710561B (zh) * 2013-12-23 2016-02-10 上海应用技术学院 一种可调节基体相和增强相组成的多孔陶瓷/金属双连续相复合材料的制备方法

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WO1997003775A1 (en) * 1995-07-19 1997-02-06 Osprey Metals Limited Silicon alloys for electronic packaging
WO1999000524A1 (en) * 1997-06-30 1999-01-07 Massachusetts Institute Of Technology Minimal thermal expansion, high thermal conductivity metal-ceramic matrix composite
WO2003039790A2 (en) * 2001-10-09 2003-05-15 Washington University Tightly agglomerated non-oxide particles and method for producing the same
WO2007101282A2 (de) * 2006-03-09 2007-09-13 Austrian Research Centers Gmbh - Arc Verbundwerkstoff und verfahren zu seiner herstellung
EP1837103A1 (de) * 2004-12-28 2007-09-26 Nippon Light Metal, Co., Ltd. Verfahren zur herstellung von aluminiumverbundwerkstoff
JP2008066379A (ja) * 2006-09-05 2008-03-21 Sumitomo Electric Ind Ltd 複合材料
US20080079021A1 (en) * 2006-09-29 2008-04-03 Reinhold Bayerer Arrangement for cooling a power semiconductor module
WO2010070623A2 (en) 2008-12-19 2010-06-24 Epos S.R.L. Sintering process and corresponding sintering system

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1997003775A1 (en) * 1995-07-19 1997-02-06 Osprey Metals Limited Silicon alloys for electronic packaging
WO1999000524A1 (en) * 1997-06-30 1999-01-07 Massachusetts Institute Of Technology Minimal thermal expansion, high thermal conductivity metal-ceramic matrix composite
WO2003039790A2 (en) * 2001-10-09 2003-05-15 Washington University Tightly agglomerated non-oxide particles and method for producing the same
EP1837103A1 (de) * 2004-12-28 2007-09-26 Nippon Light Metal, Co., Ltd. Verfahren zur herstellung von aluminiumverbundwerkstoff
WO2007101282A2 (de) * 2006-03-09 2007-09-13 Austrian Research Centers Gmbh - Arc Verbundwerkstoff und verfahren zu seiner herstellung
JP2008066379A (ja) * 2006-09-05 2008-03-21 Sumitomo Electric Ind Ltd 複合材料
US20080079021A1 (en) * 2006-09-29 2008-04-03 Reinhold Bayerer Arrangement for cooling a power semiconductor module
WO2010070623A2 (en) 2008-12-19 2010-06-24 Epos S.R.L. Sintering process and corresponding sintering system

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
REPORT ON CARCINOGENS, BACKGROUND DOCUMENT FOR COBALT-TUNGSTEN CARBIDE: POWDERS AND HARD METALS, 2009

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3862110A1 (de) * 2020-02-07 2021-08-11 EPoS S.r.L. Magnetische verbundmaterialien und verfahren zu ihrer herstellung
US20220023944A1 (en) * 2020-03-27 2022-01-27 Magotteaux International S.A. Composite wear component
CN114346238A (zh) * 2022-01-14 2022-04-15 中国科学院兰州化学物理研究所 一种超高温自润滑抗磨复合材料及其制备方法和应用
CN114346238B (zh) * 2022-01-14 2022-08-26 中国科学院兰州化学物理研究所 一种超高温自润滑抗磨复合材料及其制备方法和应用

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WO2013093847A2 (en) 2013-06-27

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