EP0966550B1 - Corps fritte en metal dur ou cermet et son procede de production - Google Patents
Corps fritte en metal dur ou cermet et son procede de production Download PDFInfo
- Publication number
- EP0966550B1 EP0966550B1 EP98919052A EP98919052A EP0966550B1 EP 0966550 B1 EP0966550 B1 EP 0966550B1 EP 98919052 A EP98919052 A EP 98919052A EP 98919052 A EP98919052 A EP 98919052A EP 0966550 B1 EP0966550 B1 EP 0966550B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- sintering
- microwave
- platelets
- sintered body
- hard
- 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.)
- Expired - Lifetime
Links
- 229910052751 metal Inorganic materials 0.000 title claims abstract description 46
- 239000002184 metal Substances 0.000 title claims abstract description 46
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 16
- 239000011195 cermet Substances 0.000 title claims abstract description 10
- 238000000034 method Methods 0.000 title claims description 24
- 238000005245 sintering Methods 0.000 claims abstract description 57
- 239000011230 binding agent Substances 0.000 claims abstract description 10
- 150000002739 metals Chemical class 0.000 claims description 24
- 239000000843 powder Substances 0.000 claims description 24
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 19
- 239000000463 material Substances 0.000 claims description 18
- 238000009768 microwave sintering Methods 0.000 claims description 15
- 229910052721 tungsten Inorganic materials 0.000 claims description 15
- 239000010937 tungsten Substances 0.000 claims description 15
- 239000000203 mixture Substances 0.000 claims description 12
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 11
- 229910052799 carbon Inorganic materials 0.000 claims description 11
- 150000004767 nitrides Chemical class 0.000 claims description 5
- 239000007787 solid Substances 0.000 claims description 4
- 239000000126 substance Substances 0.000 claims description 4
- 239000003966 growth inhibitor Substances 0.000 claims description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims 4
- 230000015572 biosynthetic process Effects 0.000 claims 2
- 229910052757 nitrogen Inorganic materials 0.000 claims 2
- 229910017464 nitrogen compound Inorganic materials 0.000 claims 2
- 150000002830 nitrogen compounds Chemical class 0.000 claims 2
- 229910003470 tongbaite Inorganic materials 0.000 claims 2
- 239000012071 phase Substances 0.000 abstract description 13
- 239000007790 solid phase Substances 0.000 abstract 1
- 238000006243 chemical reaction Methods 0.000 description 27
- 238000010438 heat treatment Methods 0.000 description 10
- 230000008569 process Effects 0.000 description 10
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 9
- 230000005855 radiation Effects 0.000 description 9
- 229910017052 cobalt Inorganic materials 0.000 description 7
- 239000010941 cobalt Substances 0.000 description 7
- 239000002245 particle Substances 0.000 description 7
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 7
- 238000011161 development Methods 0.000 description 6
- 230000018109 developmental process Effects 0.000 description 6
- 239000012779 reinforcing material Substances 0.000 description 6
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 5
- 238000009770 conventional sintering Methods 0.000 description 5
- 239000013078 crystal Substances 0.000 description 5
- 238000005520 cutting process Methods 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 239000002131 composite material Substances 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 230000003993 interaction Effects 0.000 description 4
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 230000035515 penetration Effects 0.000 description 4
- 230000000737 periodic effect Effects 0.000 description 4
- 230000009467 reduction Effects 0.000 description 4
- 239000004065 semiconductor Substances 0.000 description 4
- 229910009043 WC-Co Inorganic materials 0.000 description 3
- 230000008901 benefit Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000011065 in-situ storage Methods 0.000 description 3
- 238000001878 scanning electron micrograph Methods 0.000 description 3
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 238000005056 compaction Methods 0.000 description 2
- 238000007571 dilatometry Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000005670 electromagnetic radiation Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 230000007246 mechanism Effects 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 229910052574 oxide ceramic Inorganic materials 0.000 description 2
- 239000011224 oxide ceramic Substances 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000004904 shortening Methods 0.000 description 2
- 238000002411 thermogravimetry Methods 0.000 description 2
- 238000007514 turning Methods 0.000 description 2
- SDGKUVSVPIIUCF-UHFFFAOYSA-N 2,6-dimethylpiperidine Chemical compound CC1CCCC(C)N1 SDGKUVSVPIIUCF-UHFFFAOYSA-N 0.000 description 1
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 244000052616 bacterial pathogen Species 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000002902 bimodal effect Effects 0.000 description 1
- 230000037396 body weight Effects 0.000 description 1
- 238000007707 calorimetry Methods 0.000 description 1
- 239000006229 carbon black Substances 0.000 description 1
- 238000005255 carburizing Methods 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 239000004020 conductor Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000001493 electron microscopy Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 239000012212 insulator Substances 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000002905 metal composite material Substances 0.000 description 1
- 229910001092 metal group alloy Inorganic materials 0.000 description 1
- 238000010327 methods by industry Methods 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 229910052575 non-oxide ceramic Inorganic materials 0.000 description 1
- 239000011225 non-oxide ceramic Substances 0.000 description 1
- 239000000615 nonconductor Substances 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 229920000620 organic polymer Polymers 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 210000002381 plasma Anatomy 0.000 description 1
- 229920000642 polymer Polymers 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000007669 thermal treatment Methods 0.000 description 1
- HHIQWSQEUZDONT-UHFFFAOYSA-N tungsten Chemical compound [W].[W].[W] HHIQWSQEUZDONT-UHFFFAOYSA-N 0.000 description 1
Images
Classifications
-
- 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
- B22F3/23—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces involving a self-propagating high-temperature synthesis or reaction sintering step
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/058—Mixtures of metal powder with non-metallic powder by reaction sintering (i.e. gasless reaction starting from a mixture of solid metal compounds)
-
- 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
Definitions
- the invention relates to a hard metal or cermet sintered body defined in claim 1, consisting of at least one hard material phase containing WC and a binder phase and embedded WC platelets (platelike reinforcing materials).
- the invention also relates to a method for producing a hard metal or cermet sintered body as defined in claim 4.
- a hard metal composite body made of hard material phases, such as tungsten carbide and / or carbides or nitrides of the elements of the IVa or Va group of the periodic table, of reinforcing materials and of a binder metal phase such as cobalt, iron or nickel is known from EP 0 448 572 B1, which as reinforcing materials either single-crystal platelet-shaped reinforcing material made of borides, carbides, nitrides or carbonitrides of the elements of the IVa or VIa group of the periodic table or mixtures thereof or of SiC, Si 3 N 4 , Si 2 N 2 O, Al 2 O 3 , ZrO 2 , AlN and / or BN or single-crystalline needle-shaped reinforcing materials made of SiC, Si 3 N 4 , Si 2 N 2 O, Al 2 O 3 , ZrO 2 , AlN and / or BN.
- the proportion of the reinforcing materials is 2 to 40% by volume, preferably 10 to 20% by volume.
- the US-A-3 which is at least 647 401 describes anisodimensional tungsten carbide platelets of maximum dimension between 0.1 to 50 ⁇ m and a largest dimension three times as large as the smallest dimension. These platelets are bound by cobalt, which is present in an amount of 1 to 30% based on the total body weight.
- the body has a density of 95% of the theoretical maximum density.
- CH 522 038 describes a cemented cemented carbide body containing tungsten carbide particles, the mean grain size of which is smaller than 1 ⁇ m , at least 60% of the particles being smaller than 1 ⁇ m .
- the metal phase content is between 1 to 30% and is composed of 8 to 33% by weight of tungsten and 67 to 62% by weight of cobalt.
- the largest areas of the anisodimensional WC particles should be oriented practically parallel to a reference line.
- WO 96/22399 describes a multiphase sintered body which has a first hard phase made of carbides, nitrides, carbonitrides or carbooxynitrides of the elements of the IVa, Va or VIa metals of the periodic table.
- the second phase consists of a solid solution with particle sizes of 0.01 to 1 ⁇ m of carbides, nitrides, carbonitrides and Carbooxinitriden of at least two elements of the IVa to VIa-group of the periodic system.
- the binder is composed of cobalt, nickel, iron, chromium, molybdenum and tungsten, as well as mixtures thereof.
- the sintered body can contain WC platelets made of tungsten carbide with a size between 0.1 and 0.4 ⁇ m , which are to be formed in situ.
- ultra-fine grain alloys Especially in the production of ultra-fine grain alloys but ultrafine and nano-fine starting powders also become clearly that the conventional production process due to problems with processing powders and grain enlargement apparently reach its limits during sintering.
- microwaves describes electromagnetic radiation in the frequency range from approx. 10 8 to 10 11 Hz (corresponding to a wavelength in a vacuum of around 1 mm to 1 m).
- Commercially available microwave generators generate monochromatic radiation, ie waves with a certain frequency. Generators with 2.45 ⁇ 10 9 Hz are widespread, which corresponds to a wavelength of 12 cm.
- thermal radiation (Planckian radiation) has a very large frequency bandwidth and in typical sintering processes it has its energy maximum at a wavelength of 1 to 2 ⁇ m . Matter, which is exposed to electromagnetic radiation, can heat up due to the interaction with the field and thereby withdraw energy from the wave field. Since this interaction is strongly frequency-dependent, matter is also heated in the microwave field and by thermal radiation due to various heating mechanisms.
- the interaction of matter with a microwave field takes place via the electrical dipoles or free charges present in the material.
- the range of absorption properties of materials for microwaves ranges from transparent (oxide ceramics, some organic polymers) to partially transparent (oxide ceramics, non-oxide ceramics, filled polymers, semiconductors) to reflective (metals).
- the behavior of a material in the microwave field depends on the microwave frequency and to a large extent on the temperature: material that is microwave-transparent at room temperature can absorb or reflect strongly at elevated temperatures. For most substances, the penetration depth of the microwaves is much greater than that for infrared radiation, which, depending on the sample size, has the result that the material - in contrast to "skin heating" with infrared radiation - can be heated in volume with microwaves.
- the penetration depth of microwaves with a frequency of 2.45 GHz at a temperature of 20 ° C differs for different substances and has the following values: 1.7 ⁇ m for aluminum, 2.5 ⁇ m for Cobalt (as an example for metals), 4.7 ⁇ m for WC and 8.2 ⁇ m for TiC (as example for solid semiconductors), 10 m for Al 2 O 3 and 1.3 cm for H 2 O (as example for insulators) and 7.5 cm for WC with 6 M% Co, 31 cm for Al 2 O 3 with 10 M% Al and 36 cm for Al 2 O 3 with 30 M% TiC (as an example for powder metal green parts).
- Fig. 1 shows schematically the structure of a suitable one Oven.
- the microwave with a frequency of 2.45 GHz is from generated a magnetron and into the metallic resonator housing guided. Inside the resonator is the cemented carbide batch, the one with a microwave-transparent, thermal Insulation is surrounded. With appropriate interpretation of the The resonators are in a homogeneous magnetic field and is heated homogeneously. The measurement of the batch temperature and the coupled microwave power are used for Control of the microwave sintering process with a microprocessor. Compare the sintering profiles to microwave sintering conventional sintering in comparable sized furnaces have shown that the sintering cycle (without the cooling phase) shortened by a factor of 3 in microwave sintering can be.
- the consumption of electrical energy the microwave sintering technology here is due to the process time reduction and because of the lower heating output during of sintering is only a fraction of the values for the conventional sintering technology.
- a microwave sintering hard metals and also cermets with a high binder metal content (e.g. 25% by mass) as well as with a low binder metal content (for example 4% by mass) at temperatures, 50 to 100 K below that of conventional sintering lying, sintering without pressure.
- the comparison with a conventional one Sintering shows that the bulk of the compaction in microwave sintering at much lower temperatures still takes place below the eutectic temperature.
- the improved Compression behavior can also be seen in the simultaneous Reduction of open and closed porosity in Microwave sintering. Because of the shorter sintering times and the microwave sintered show lower sintering temperatures Hard metals have a finer structure and thus an increase in hardness up to 10 %. In use as a cutting tool when turning The microwave sintered version of cast iron showed advantages in the open area wear behavior.
- Tungsten powder no longer in a separate process step be carburized, but in that the carburizing in the Sintering process is integrated.
- the compacts are on the usual way of shaping made by instead of Tungsten carbide-cobalt powder mixture from a mixture of Tungsten, carbon and cobalt powder is assumed.
- the exothermic carburization reaction of tungsten and carbon to tungsten carbide, with a heat tone of 38 kJ / mol, takes place after the binder expulsion of the compact at Temperature of around 930 ° C instead.
- Fig. 2 is thermogravimetry (TG, DTG), dilatometry (DIL, DDIL) and dynamic differential calorimetry (DSC) a reaction sintering of a WC-6 M% Co hard metal for temperatures shown from 500 ° C.
- the DSC signal is above 750 ° C endothermic reduction of the oxides present in the tungsten powder recognize that with the corresponding mass decrease in thermogravimetry and a first shrinkage stage of the sample in Dilatometer signal corresponds.
- TG thermogravimetry
- DIL dilatometry
- DSC dynamic differential calorimetry
- the reaction sintering is done using microwave radiation implemented (MWRS), on the one hand is a further refinement of the structure possible, on the other hand the remaining porosity can be compared the conventional reaction sintering (RS) clearly be humiliated.
- MWRS microwave radiation implemented
- RS conventional reaction sintering
- HV30 Vickers hardness was after the conventional one Sintering 1560, after microwave sintering 1630, after conventional reaction sintering 1720 and after microwave reaction sintering 1770.
- reaction sintering In addition to the material-specific advantages of reaction sintering mentioned, especially microwave reaction sintering, this method offers great potential for simplification and shortening the process flow and saving energy in the production of hard metals. Except at high temperatures carburization that occurs also falls before and after Process steps such as mixing, breaking, crushing etc. continue. A process time gain can also be achieved in this way become.
- WC-6 M% Co hard metals with differently fine tungsten powders were manufactured using conventional (RS) and microwave heating (MWRS).
- the tungsten powders used had an average grain size of 0.4 ⁇ m , 1 ⁇ m and 2.4 ⁇ m (in each case FSSS) with doping of 0.2 M% VC or missing VC.
- FSSS microwave heating
- the influence of the VC content on the structure is evident most clearly with the fine tungsten powders.
- the WC crystals especially in the case of the RS samples, apparently have sufficient time to grow out during the sintering phase in the absence of VC.
- the invention has for its object a simultaneous Increase in hardness and toughness in hard metal or Cemert sintered bodies to bring about the type mentioned.
- the manufacture the method according to such a sintered body Claim 4 used.
- the method according to the invention is in no way limited to one limited possible unimodal initial grain size distribution, rather, it can also be used with powders with a wide or bimodal Size distribution to be worked.
- the reaction sintering of powders, both tungsten and Contain carbon, but also in the starting mixture WC may contain, completely or as a partial Reaction sintering is carried out, the partial proportions of the reaction sintering between 1% and 100% (based on the complete sintering process).
- the grain growth in the sintered body can be controlled.
- WC platelet growth can also be controlled via the partial share of reaction sintering, thereby reducing the platelet concentration is controllable in the sintered body.
- the volume fraction of the WC platelets on the total sintered body volume is preferably up to 25 vol%.
- the platelet content should be measured as a proportion of the area of a metallographic cut max. 20% amount, with all WC crystals with a length / width ratio, the so-called aspect ratio of greater than 3 be counted.
- the maximum aspect ratio is preferably Max. 10 ⁇ 1.
- the rate of growth to be controlled.
- microwave reaction sintering is that a more homogeneous structure, better compaction, i.e. a smaller residual porosity can be achieved as well as shorter ones Sintering times and lower sintering temperatures. Resulting from this lower manufacturing costs.
- 0.4 ⁇ m W powder, 0.2% addition of VC, 6% co-powder with a grain size of 1.6 ⁇ m and a stoichiometric addition of carbon in the form of Carbon black mixed and adding acetone for 36 hours in one Ball mill has been ground before then using 2% wax Pressing aids have been added, distilled off and granulated are.
- the granules were pressed into green bodies by means of die presses and in the microwave sintering oven at 500 ° C / hour to 900 ° C heated up and then with the onset of the carburization reaction to the sintering temperature within 10 min using microwaves heated from 1350 ° C. After a waiting time of 20 min the sample is cooled by turning off the microwave heater.
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- Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
Claims (7)
- Corps fritté en métal dur ou cermet, se composant d'au moins une phase de matière dure contenant du WC et d'une phase liant ainsi que de platelets de WC enrobés,
caractérisé par le fait
que les métaux nécessaires à la formation de la ou bien des phase(s) dure(s), le carbone et les proportions de tungstène et de carbone nécessaires à la formation des platelets de WC, ainsi que, le cas échéant, d'autres métaux, carbures et nitrures métalliques et/ou des composés d'azote solides en tant que fournisseurs pour carbone et/ou azote ont été précomprimés au moins en partie respectivement en forme de poudre en un corps formé et ont été soumis ensuite au moins temporairement à un frittage-réaction dans un champ à micro-ondes ayant une densité de flux d'énergie de 0,01 à 10 W/cm3. - Corps fritté en métal dur ou cermet selon la revendication 1, caractérisé par le fait qu'il contient jusqu'à 12 %, de préférence 8 % de VC et/ou de Cr3C2 par rapport à la phase liant.
- Corps fritté en métal dur ou cermet selon la revendication 1 ou 2, caractérisé par le fait que les platelets de WC présentent un rapport diamètre/épaisseur de ≥3, de préférence de ≥5, et/ou que la proportion des platelets de WC - par rapport au volume total - est < 25 pourcent volumétrique.
- Procédé de fabrication d'un corps fritté en métal dur ou cermet selon l'une des revendications 1 à 3, caractérisé par le fait que les métaux nécessaires à la formation de la ou bien des phase(s) dure(s), le carbone et les proportions de tungstène et de carbone nécessaires à la formation des platelets de WC, ainsi que, le cas échéant, d'autres métaux, carbures et nitrures métalliques et/ou des composés d'azote solides en tant que fournisseurs pour carbone et/ou azote sont précomprimés au moins en partie respectivement en forme de poudre en un corps formé et sont soumis ensuite au moins temporairement à un frittage-réaction dans un champ à micro-ondes ayant une densité de flux d'énergie de 0,01 à 10 W/cm3.
- Procédé selon la revendication 4, caractérisé par le fait que la fraction de matière produite par fittage-réaction, en particulier le WC, est comprise entre 1 % et 100 %, les fractions restantes ont été ajoutées dans la forme chimique dans laquelle elles existent plus tard dans le corps fritté fini.
- Procédé selon l'une des revendications 4 ou 5, caractérisé par le fait que la croissance des platelets de WC est commandée par la part du frittage-réaction à micro-ondes par rapport à l'ensemble du processus de frittage à micro-ondes.
- Procédé selon l'une des revendications 4 à 6, caractérisé par le fait que l'on ajoute au mélange de départ des inhibiteurs de croissance de grains, de préférence jusqu'à 12 %, en outre de préférence jusqu'à 8 % de VC et/ou de Cr3C2.
Applications Claiming Priority (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE19709527 | 1997-03-10 | ||
DE19709527 | 1997-03-10 | ||
DE19725914 | 1997-06-19 | ||
DE19725914A DE19725914A1 (de) | 1997-03-10 | 1997-06-19 | Hartmetall- oder Cermet-Sinterkörper und Verfahren zu dessen Herstellung |
PCT/DE1998/000674 WO1998040525A1 (fr) | 1997-03-10 | 1998-03-06 | Corps fritte en metal dur ou cermet et son procede de production |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0966550A1 EP0966550A1 (fr) | 1999-12-29 |
EP0966550B1 true EP0966550B1 (fr) | 2001-10-04 |
Family
ID=26034637
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP98919052A Expired - Lifetime EP0966550B1 (fr) | 1997-03-10 | 1998-03-06 | Corps fritte en metal dur ou cermet et son procede de production |
Country Status (4)
Country | Link |
---|---|
US (1) | US6293986B1 (fr) |
EP (1) | EP0966550B1 (fr) |
AT (1) | ATE206481T1 (fr) |
WO (1) | WO1998040525A1 (fr) |
Families Citing this family (63)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2002058437A1 (fr) * | 2001-01-17 | 2002-07-25 | The Penn State Research Foundation | Traitement par hyperfrequences au moyen de couches de materiau en poudre absorbant les micro-ondes |
CA2409433A1 (fr) * | 2002-10-23 | 2004-04-23 | Consolidated Civil Enforcement Inc. | Methode de traitement cryogenique de carbure de tungstene contenant du cobalt |
US7175687B2 (en) * | 2003-05-20 | 2007-02-13 | Exxonmobil Research And Engineering Company | Advanced erosion-corrosion resistant boride cermets |
US7384443B2 (en) * | 2003-12-12 | 2008-06-10 | Tdy Industries, Inc. | Hybrid cemented carbide composites |
US20050211475A1 (en) | 2004-04-28 | 2005-09-29 | Mirchandani Prakash K | Earth-boring bits |
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 |
US20080101977A1 (en) * | 2005-04-28 | 2008-05-01 | Eason Jimmy W | Sintered bodies for earth-boring rotary drill bits and methods of forming the same |
US8637127B2 (en) | 2005-06-27 | 2014-01-28 | Kennametal Inc. | Composite article with coolant channels and tool fabrication method |
US7687156B2 (en) | 2005-08-18 | 2010-03-30 | Tdy Industries, Inc. | Composite cutting inserts and methods of making the same |
US7597159B2 (en) | 2005-09-09 | 2009-10-06 | Baker Hughes Incorporated | Drill bits and drilling tools including abrasive wear-resistant materials |
US7997359B2 (en) | 2005-09-09 | 2011-08-16 | Baker Hughes Incorporated | Abrasive wear-resistant hardfacing materials, drill bits and drilling tools including abrasive wear-resistant hardfacing materials |
US7703555B2 (en) | 2005-09-09 | 2010-04-27 | Baker Hughes Incorporated | Drilling tools having hardfacing with nickel-based matrix materials and hard particles |
US8002052B2 (en) | 2005-09-09 | 2011-08-23 | Baker Hughes Incorporated | Particle-matrix composite drill bits with hardfacing |
US7776256B2 (en) * | 2005-11-10 | 2010-08-17 | Baker Huges Incorporated | Earth-boring rotary drill bits and methods of manufacturing earth-boring rotary drill bits having particle-matrix composite bit bodies |
US7784567B2 (en) | 2005-11-10 | 2010-08-31 | Baker Hughes Incorporated | Earth-boring rotary drill bits including bit bodies comprising reinforced titanium or titanium-based alloy matrix materials, and methods for forming such bits |
US7802495B2 (en) | 2005-11-10 | 2010-09-28 | Baker Hughes Incorporated | Methods of forming earth-boring rotary drill bits |
US7807099B2 (en) | 2005-11-10 | 2010-10-05 | Baker Hughes Incorporated | Method for forming earth-boring tools comprising silicon carbide composite materials |
US8770324B2 (en) | 2008-06-10 | 2014-07-08 | Baker Hughes Incorporated | Earth-boring tools including sinterbonded components and partially formed tools configured to be sinterbonded |
US7913779B2 (en) | 2005-11-10 | 2011-03-29 | Baker Hughes Incorporated | Earth-boring rotary drill bits including bit bodies having boron carbide particles in aluminum or aluminum-based alloy matrix materials, and methods for forming such bits |
US20070151769A1 (en) * | 2005-11-23 | 2007-07-05 | Smith International, Inc. | Microwave sintering |
US20070138706A1 (en) * | 2005-12-20 | 2007-06-21 | Amseta Corporation | Method for preparing metal ceramic composite using microwave radiation |
ES2386626T3 (es) | 2006-04-27 | 2012-08-23 | Tdy Industries, Inc. | Cabezas perforadoras de suelos modulares con cuchillas fijas y cuerpos de cabezas perforadoras de suelos modulares con cuchillas fijas |
CA2662966C (fr) | 2006-08-30 | 2012-11-13 | Baker Hughes Incorporated | Procedes permettant d'appliquer un materiau resistant a l'usure aux surfaces externes d'outils de forage dans le sol et structures resultantes |
US7541561B2 (en) * | 2006-09-01 | 2009-06-02 | General Electric Company | Process of microwave heating of powder materials |
US7326892B1 (en) | 2006-09-21 | 2008-02-05 | General Electric Company | Process of microwave brazing with powder materials |
BRPI0717332A2 (pt) | 2006-10-25 | 2013-10-29 | Tdy Ind Inc | Artigos tendo resistência aperfeiçoada à rachadura térmica |
US7775416B2 (en) * | 2006-11-30 | 2010-08-17 | General Electric Company | Microwave brazing process |
US8272295B2 (en) * | 2006-12-07 | 2012-09-25 | Baker Hughes Incorporated | Displacement members and intermediate structures for use in forming at least a portion of bit bodies of earth-boring rotary drill bits |
US7775287B2 (en) | 2006-12-12 | 2010-08-17 | Baker Hughes Incorporated | Methods of attaching a shank to a body of an earth-boring drilling tool, and tools formed by such methods |
US20080138533A1 (en) * | 2006-12-12 | 2008-06-12 | General Electric Company | Microwave process for forming a coating |
US8574686B2 (en) * | 2006-12-15 | 2013-11-05 | General Electric Company | Microwave brazing process for forming coatings |
US8409318B2 (en) * | 2006-12-15 | 2013-04-02 | General Electric Company | Process and apparatus for forming wire from powder materials |
US7946467B2 (en) * | 2006-12-15 | 2011-05-24 | General Electric Company | Braze material and processes for making and using |
US7841259B2 (en) | 2006-12-27 | 2010-11-30 | Baker Hughes Incorporated | Methods of forming bit bodies |
US8512882B2 (en) | 2007-02-19 | 2013-08-20 | TDY Industries, LLC | Carbide cutting insert |
US20080202814A1 (en) * | 2007-02-23 | 2008-08-28 | Lyons Nicholas J | Earth-boring tools and cutter assemblies having a cutting element co-sintered with a cone structure, methods of using the same |
US20080210555A1 (en) * | 2007-03-01 | 2008-09-04 | Heraeus Inc. | High density ceramic and cermet sputtering targets by microwave sintering |
US7846551B2 (en) | 2007-03-16 | 2010-12-07 | Tdy Industries, Inc. | Composite articles |
US20090139607A1 (en) * | 2007-10-28 | 2009-06-04 | General Electric Company | Braze compositions and methods of use |
US8790439B2 (en) | 2008-06-02 | 2014-07-29 | Kennametal Inc. | Composite sintered powder metal articles |
JP2011523681A (ja) | 2008-06-02 | 2011-08-18 | ティーディーワイ・インダストリーズ・インコーポレーテッド | 超硬合金−金属合金複合体 |
US7703556B2 (en) | 2008-06-04 | 2010-04-27 | Baker Hughes Incorporated | Methods of attaching a shank to a body of an earth-boring tool including a load-bearing joint and tools formed by such methods |
US8261632B2 (en) | 2008-07-09 | 2012-09-11 | Baker Hughes Incorporated | Methods of forming earth-boring drill bits |
US8025112B2 (en) | 2008-08-22 | 2011-09-27 | Tdy Industries, Inc. | Earth-boring bits and other parts including cemented carbide |
US8322465B2 (en) | 2008-08-22 | 2012-12-04 | TDY Industries, LLC | Earth-boring bit parts including hybrid cemented carbides and methods of making the same |
US8272816B2 (en) | 2009-05-12 | 2012-09-25 | TDY Industries, LLC | Composite cemented carbide rotary cutting tools and rotary cutting tool blanks |
US8201610B2 (en) | 2009-06-05 | 2012-06-19 | Baker Hughes Incorporated | Methods for manufacturing downhole tools and downhole tool parts |
US8308096B2 (en) | 2009-07-14 | 2012-11-13 | TDY Industries, LLC | Reinforced roll and method of making same |
US8440314B2 (en) | 2009-08-25 | 2013-05-14 | TDY Industries, LLC | Coated cutting tools having a platinum group metal concentration gradient and related processes |
JP2011051841A (ja) * | 2009-09-02 | 2011-03-17 | Ismanj:Kk | シリコン合金焼結体の製造方法 |
US9643236B2 (en) | 2009-11-11 | 2017-05-09 | Landis Solutions Llc | Thread rolling die and method of making same |
CN103003010A (zh) | 2010-05-20 | 2013-03-27 | 贝克休斯公司 | 形成钻地工具的至少一部分的方法,以及通过此类方法形成的制品 |
US8490674B2 (en) | 2010-05-20 | 2013-07-23 | Baker Hughes Incorporated | Methods of forming at least a portion of earth-boring tools |
CN102985197A (zh) | 2010-05-20 | 2013-03-20 | 贝克休斯公司 | 形成钻地工具的至少一部分的方法,以及通过此类方法形成的制品 |
US8800848B2 (en) | 2011-08-31 | 2014-08-12 | Kennametal Inc. | Methods of forming wear resistant layers on metallic surfaces |
US9016406B2 (en) | 2011-09-22 | 2015-04-28 | Kennametal Inc. | Cutting inserts for earth-boring bits |
EP3055272B1 (fr) | 2013-10-10 | 2021-08-11 | Raytheon Technologies Corporation | Régulation de microstructure de matériau inorganique par chauffage indirect à l'aide d'un rayonnement électromagnétique |
EP3057924B1 (fr) | 2013-10-14 | 2019-10-30 | United Technologies Corporation | Procédé de pyrolyse d'un matériau polymère précéramique à l'aide d'un rayonnement électromagnétique |
ES2769895T3 (es) * | 2013-12-17 | 2020-06-29 | Hyperion Materials & Tech Sweden Ab | Composición para una nueva calidad para herramientas de corte |
CN104190942B (zh) * | 2014-08-19 | 2016-08-31 | 天津市华辉超硬耐磨技术有限公司 | 一种硬质合金的微波烧结方法 |
RU2625922C1 (ru) * | 2016-01-29 | 2017-07-19 | Вазген Эдвардович Лорян | Реактор для получения самораспространяющимся высокотемпературным синтезом тугоплавких неорганических соединений |
DE102016207028A1 (de) * | 2016-04-26 | 2017-10-26 | H.C. Starck Gmbh | Hartmetall mit zähigkeitssteigerndem Gefüge |
EP3577242B1 (fr) | 2017-01-31 | 2022-10-12 | Tallinn University of Technology | Procédé de production d'un matériau composite de carbure cémenté-tungstène bimodal à double structure |
Family Cites Families (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3451791A (en) | 1967-08-16 | 1969-06-24 | Du Pont | Cobalt-bonded tungsten carbide |
US3647401A (en) | 1969-06-04 | 1972-03-07 | Du Pont | Anisodimensional tungsten carbide platelets bonded with cobalt |
JPS6039137A (ja) * | 1983-08-12 | 1985-02-28 | Mitsubishi Metal Corp | 炭化タングステン基超硬合金の製造法 |
JPH04502347A (ja) | 1988-12-16 | 1992-04-23 | クルップ・ヴィディア・ゲゼルシャフト・ミト・ベシュレンクテル・ハフツング | 硬質金属複合体およびその製造方法 |
US5451365A (en) | 1993-05-24 | 1995-09-19 | Drexel University | Methods for densifying and strengthening ceramic-ceramic composites by transient plastic phase processing |
DE4340652C2 (de) * | 1993-11-30 | 2003-10-16 | Widia Gmbh | Verbundwerkstoff und Verfahren zu seiner Herstellung |
US5580666A (en) | 1995-01-20 | 1996-12-03 | The Dow Chemical Company | Cemented ceramic article made from ultrafine solid solution powders, method of making same, and the material thereof |
DE69525248T2 (de) | 1995-08-23 | 2002-09-26 | Toshiba Tungaloy Co. Ltd., Kawasaki | Flächen-kristallines Wolframkarbid enthaltendes Hartmetall, Zusammensetzung zur Herstellung von flächen-kristallines Wolframkarbid und Verfahren zur Herstellung des Hartmetalls |
DE19601234A1 (de) | 1996-01-15 | 1997-07-17 | Widia Gmbh | Verbundkörper und Verfahren zu seiner Herstellung |
-
1998
- 1998-03-06 AT AT98919052T patent/ATE206481T1/de active
- 1998-03-06 US US09/367,004 patent/US6293986B1/en not_active Expired - Lifetime
- 1998-03-06 EP EP98919052A patent/EP0966550B1/fr not_active Expired - Lifetime
- 1998-03-06 WO PCT/DE1998/000674 patent/WO1998040525A1/fr active IP Right Grant
Also Published As
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US6293986B1 (en) | 2001-09-25 |
WO1998040525A1 (fr) | 1998-09-17 |
ATE206481T1 (de) | 2001-10-15 |
EP0966550A1 (fr) | 1999-12-29 |
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