EP0758407B1 - Cermet und verfahren zu seiner herstellung - Google Patents
Cermet und verfahren zu seiner herstellung Download PDFInfo
- Publication number
- EP0758407B1 EP0758407B1 EP95913058A EP95913058A EP0758407B1 EP 0758407 B1 EP0758407 B1 EP 0758407B1 EP 95913058 A EP95913058 A EP 95913058A EP 95913058 A EP95913058 A EP 95913058A EP 0758407 B1 EP0758407 B1 EP 0758407B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- mass
- cermet
- binder
- content
- pressure
- 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
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- 239000011195 cermet Substances 0.000 title claims abstract description 68
- 238000000034 method Methods 0.000 title claims description 16
- 239000011230 binding agent Substances 0.000 claims abstract description 46
- 239000002344 surface layer Substances 0.000 claims abstract description 30
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 38
- 238000005245 sintering Methods 0.000 claims description 24
- 239000000203 mixture Substances 0.000 claims description 19
- 229910052757 nitrogen Inorganic materials 0.000 claims description 17
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 16
- 238000010438 heat treatment Methods 0.000 claims description 16
- 238000001816 cooling Methods 0.000 claims description 15
- 229910052758 niobium Inorganic materials 0.000 claims description 15
- 239000000463 material Substances 0.000 claims description 14
- 229910052721 tungsten Inorganic materials 0.000 claims description 14
- 229910052715 tantalum Inorganic materials 0.000 claims description 13
- 229910052750 molybdenum Inorganic materials 0.000 claims description 11
- 239000010410 layer Substances 0.000 claims description 10
- 239000007789 gas Substances 0.000 claims description 9
- 230000035515 penetration Effects 0.000 claims description 9
- 229910052786 argon Inorganic materials 0.000 claims description 8
- 229910052720 vanadium Inorganic materials 0.000 claims description 8
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- 238000002844 melting Methods 0.000 claims description 5
- 230000008018 melting Effects 0.000 claims description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 4
- 239000011248 coating agent Substances 0.000 claims description 4
- 238000000576 coating method Methods 0.000 claims description 4
- 239000011261 inert gas Substances 0.000 claims description 4
- 238000004519 manufacturing process Methods 0.000 claims description 4
- 229910052751 metal Inorganic materials 0.000 claims description 4
- 239000002184 metal Substances 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 238000000227 grinding Methods 0.000 claims description 3
- 238000002156 mixing Methods 0.000 claims description 3
- 230000003746 surface roughness Effects 0.000 claims description 3
- 239000004020 conductor Substances 0.000 claims description 2
- 229910002804 graphite Inorganic materials 0.000 claims description 2
- 239000010439 graphite Substances 0.000 claims description 2
- 150000001247 metal acetylides Chemical class 0.000 claims description 2
- 150000004767 nitrides Chemical class 0.000 claims description 2
- 238000004452 microanalysis Methods 0.000 claims 2
- 206010026865 Mass Diseases 0.000 claims 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims 1
- 230000006835 compression Effects 0.000 claims 1
- 238000007906 compression Methods 0.000 claims 1
- 229910052593 corundum Inorganic materials 0.000 claims 1
- 239000004615 ingredient Substances 0.000 claims 1
- 239000002356 single layer Substances 0.000 claims 1
- 229910001845 yogo sapphire Inorganic materials 0.000 claims 1
- 239000010936 titanium Substances 0.000 description 14
- 238000005520 cutting process Methods 0.000 description 8
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 7
- 239000012298 atmosphere Substances 0.000 description 6
- 229910002091 carbon monoxide Inorganic materials 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 239000000758 substrate Substances 0.000 description 5
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical group [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 239000012299 nitrogen atmosphere Substances 0.000 description 3
- 238000003825 pressing Methods 0.000 description 3
- 238000011282 treatment Methods 0.000 description 3
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 229910001873 dinitrogen Inorganic materials 0.000 description 2
- 238000001513 hot isostatic pressing Methods 0.000 description 2
- 238000012423 maintenance Methods 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 2
- 239000002347 wear-protection layer Substances 0.000 description 2
- UGFAIRIUMAVXCW-UHFFFAOYSA-N Carbon monoxide Chemical compound [O+]#[C-] UGFAIRIUMAVXCW-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000005229 chemical vapour deposition Methods 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- MWUXSHHQAYIFBG-UHFFFAOYSA-N nitrogen oxide Inorganic materials O=[N] MWUXSHHQAYIFBG-UHFFFAOYSA-N 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Images
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
- C22C29/02—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
-
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/26—Web or sheet containing structurally defined element or component, the element or component having a specified physical dimension
- Y10T428/263—Coating layer not in excess of 5 mils thick or equivalent
- Y10T428/264—Up to 3 mils
- Y10T428/265—1 mil or less
Definitions
- the invention relates to a cermet with a hard material content of 95 to 75% by mass and 5 to 25% by mass of binder as the balance Cobalt and / or nickel, the hard material phase consisting of carbonitrides with a cubic B1 crystal structure and 30 to 60 mass% Ti, 5 to 25 mass% W, 5 to 15 mass% Ta, of which up to 70% by mass can be replaced by Nb, 0 to 12 mass% Mo, 0 to 5 mass% V, 0 to 2 mass% Cr, 0 to Contains 1% by mass of Hf and / or Zr, the (C + N) content in the carbonitride phase > 80 mol%, the nitrogen content N / (C + N) is between 0.15 and 0.7 and in the binder phase up to 2% Al and / or metallic W, Ti, Mo, V and / or Cr dissolved are.
- the hard material phases essentially have a core-edge structure.
- the invention further relates to a method of manufacture of such a cermet by mixing, grinding, granulating and Pressing a starting mixture containing corresponding constituents and then sintering.
- EP 0 344 421 A1 proposes a cermet that either an average grain size of the hard material phase in the surface layer compared to a core with a penetration depth of 0.05 mm, which is between 0.8 to 1.2 times the average grain size of the hard material phase in the cermet core is or in the same penetration depth affects a binder phase that is 0.7 up to 1.2 times the average binder content of the cermet core or where the hardness in the aforementioned penetration depth between 0.95 and 1.1 times the average hardness of the Cermet core lies.
- the starting mixture is used to produce this cermet sintered after grinding, mixing and pre-pressing, in a first stage up to 1300 ° C or below is sintered under vacuum or an inert gas atmosphere while in a second stage above 1300 ° C at a nitrogen pressure is sintered from 0.1 to 20 torr, and wherein the Nitrogen pressure also increases with increasing temperature should.
- the cooling is also in the presence of nitrogen performed.
- EP 0 368 336 B1 describes a cermet substrate with a hard surface layer in which the region with the maximum Hardness at a depth between 5 ⁇ m and 50 ⁇ m from the substrate surface is present, and the substrate surface has a hardness of 20 to 90% of the maximum hardness.
- This Cermets becomes the pre-pressed mixture of an initial temperature increase to 1100 ° C in a vacuum, followed by an increase in temperature from 1100 ° C to a temperature range between 1400 ° C and 1500 ° C in a nitrogen atmosphere and one finally subjected to sintering in a vacuum.
- EP 0 374 358 B1 describes a process for producing a cermet with 7 to 20% by weight binder phase and a hard phase made of titanium carbide, titanium nitride and / or titanium carbonitride with 35 to 59% by weight Ti, 9 to 29% by weight W, 0.4 to 3.5% by weight Mo, 4 to 24% by weight of at least one metal from Ta, Nb, V and zirconium, 5.5 to 9.5% by weight N 2 and 4, 5 to 12 wt .-% C.
- the formulated mixed, dried and pre-pressed mass is sintered in such a way that the temperature is raised to 1350 ° C.
- the nitrogen atmosphere being set to 1 Torr at 1350 ° C.
- the nitrogen partial pressure together with the temperature increase from 1350 ° C. to the sintering temperature is gradually increased, the nitrogen atmosphere being set to 5 torr at the sintering temperature.
- EP 0 492 059 A3 describes a cermet body whose hardness is at a penetration depth of not less than 1 mm higher than in the interior of the cermet, wherein the binder content can be minimized in a layer thickness of 0.5 to 3 ⁇ m compared to the core substrate.
- the cermet should have a hard material coating in a thickness of 0.5 to 20 ⁇ m made of carbides, nitrides, oxides and borides of titanium and Al 2 O 3 .
- a green compact is first heated to a temperature between 1100 ° C. and 1400 ° C. under vacuum, then nitrogen gas is admitted to a pressure at which the partial nitrogen pressure is between 5 and 10 torr, so that the substrate surface is denitrified.
- the sintering and the final cooling are carried out under a non-oxidizing atmosphere, such as a vacuum or an inert gas atmosphere.
- the body is coated using CVD or PVD.
- EP 0 499 223 A1 proposes that the relative concentration of the binder in a 10 ⁇ m thick layer near the surface be 5 to 50% of the average mean content of binder in the cermet core and in the layer below it from 10 ⁇ m to 100 ⁇ m Penetration depth to set the binder content to 70 to 100% relative to the cermet core, whereby compressive stresses of 30 kgf / mm 2 and more exist on the surface.
- the sintering is carried out under nitrogen gas at a constant pressure of 5 to 30 torr and the cooling under vacuum at a cooling rate of 10 to 20 ° C./min.
- EP 0 515 340 A3 describes a cermet with one Binder-enriched zone near the surface.
- EP 0 519 895 A1 discloses a cermet with a three-layered edge zone, in which the first layer is TiN-rich to a depth of 50 ⁇ m, the next layer from 50 to 150 ⁇ m penetration depth with a binder enrichment and the next layer from 150 ⁇ m to 400 ⁇ m is formed with a binder depletion relative to the interior of the cermet core.
- the sintered body is in an atmosphere of N 2 and / or NH 3 , possibly in combination with CH 4 , CO, CO 2 at 1100 ° C to 1350 ° C for one to 25 hours under atmospheric pressure or a pressure above 1.1 bar treated.
- the cermets known from the prior art have the surface either different binder levels what is recognizable by spotty appearance, or tend to stick of the binder with the sinter pad, what because of that related reactions to changes in composition in the Contact zone leads.
- Other disadvantages of the previous one Cermets known in the prior art are sometimes high Surface roughness as well as with increased binder metal contents in poor adhesion to the surface from there Wear protection layers. If nickel content in the Surface is increased, is not a CVD coating at all possible.
- the disadvantages mentioned speak in particular against the use of the cermet as a cutting insert for cutting Editing.
- the core areas under the surface layer mentioned have at least essentially one hard material phase a core edge structure.
- the hard phase in the surface layer only homogeneously or with the core edge structure intended for the core may also be partially available.
- the further preferably low roughness depths R T 6 6 ⁇ m or R Z 5 5 ⁇ m have an effect.
- the hardness HV30 is preferably constant in the surface area.
- the cermet can have one or more wear protection layers, which consist of titanium carbide or nitride and / or Al 2 O 3 , preferably applied by the CVD method.
- the cermet described is produced by the method set out in claim 8. Thereafter, a mixture containing the constituents determined according to claim 1 or 3 to 7 is ground, granulated and pre-pressed and then sintered, preferably in sintering furnaces with graphite heating conductors. After pressing, the green body is first heated to the melting temperature of the binder phase under vacuum with a pressure ⁇ 10 -1 mbar, then further heated to the sintering temperature, which is between 1450 to 1530 ° C, where the temperature is 0.2 to 2 hours held and then the body is cooled to 1200 ° C.
- the last heating, holding and cooling is carried out in a gas mixture of N 2 and CO with an N 2 / (N 2 + CO) ratio between 0.1 and 0.9 under an average pressure of 10% to 80% of the mean alternately in a period between 40 and 240 sec, preferably 40 to 180 sec.
- the sintered Body after sintering under a hot isostatic press Argon at temperatures close to the sintering temperature and pressures be subjected to above 30 bar.
- the respective value x represents the relative nitrogen content in the cermet, namely the ratio N / (C + N) and the value y the setting of the gas mixture N 2 / (N 2 + CO).
- the limit values are specified by cermet nitrogen contents between 0.15 and 0.7, to which settings of the gas mixture of 0.1 and 0.9 are assigned. All values in between can be seen in the graphical representation, whereby fluctuations up or down of 10% are permitted. The same applies to the representation according to FIG. 2, where the ordinate y represents the mean pressure in bar and the abscissa represents the binder content x in mass%.
- the mean pressure to be set is 20 mbar, with a binder content of 5% by mass 6 mbar, with deviations from the mean value of up to 10% being permitted here as well.
- the pressures set in the sintering furnace then fluctuate around a constant mean pressure, alternating upwards and downwards at least 10%.
- step 3 with the proviso that no CO was blown in and the set N 2 pressure was constant at 20 mbar.
- Example 1 Cermet according to the invention Comparative cermet Ti (surface layer) / Ti (core): 1.3 1.4 Binder (surface layer) / Binder (core) 0.12 0.6 Total (W, Mo, Ta, Nb) (surface) / Total (W, Mo, Ta, Nb) (core) 0.9 0.6 Edge layer thickness 0.5 ⁇ m 10 ⁇ m Zone below the surface layer with a porosity ⁇ A02 and ⁇ B02 200 ⁇ m 250 ⁇ m and a porosity in the core ⁇ A06 and ⁇ B02 surface roughness R T 5 ⁇ m 15 ⁇ m R Z 3.8 ⁇ m 11 ⁇ m
- Example 2 Cermet according to the invention Comparative cermet Ti (surface layer) / Ti (core) 1.23 1.00 Binder (surface layer) / Binder (core) 0.15 1.20 Total (W, Mo, Ta, Nb) (surface) / Total (W, Mo, Ta, Nb) (core) 0.98 0.8 Porosity throughout ⁇ A02 and ⁇ B02 all other values as in example 1.
- a comparison body was subjected to the same process steps 1, 2 and 4, but process step 3 with the proviso that no CO was blown in and the N 2 pressure was constant at 20 mbar.
- Example 3 Cermet according to the invention Comparative cermet Ti (surface layer) / Ti (core) 1.32 1.00 Binder (surface layer) / Binder (core) 0.27 0.50 Total (W, Ta, Nb) (surface) / Total (W, Ta, Nb) (core) 0.82 1.5 Edge layer thickness 0.3 ⁇ m 5 ⁇ m Zone below the surface layer with a porosity ⁇ A02 and ⁇ B02 100 ⁇ m 120 ⁇ m Porosity in the core ⁇ A08 and ⁇ B02 roughness depth R T 3.5 ⁇ m 13 ⁇ m R Z 2.8 ⁇ m 9 ⁇ m
- Example 4 Cermet according to the invention Comparative cermet Ti surface layer / Ti core 1.21 1.00 Binder surface layer / binder core 0.69 1.60 Total amount (W, Ta, Nb) surface / total amount (W, Ta, Nb) core 0.78 0.4 Porosity throughout ⁇ A02 and ⁇ B02 all other values as in example 3.
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Description
- Fig. 1
- den linearen Zusammenhang zwischen dem Verhältnis N/(C+N) im Cermet und der Einstellung des Gehaltes N2/(N2+CO) im Gasgemisch und
- Fig. 2
- die Abhängigkeit der Einstellung des mittleren Druckes vom Bindemetallgehalt in der Ausgangsmischung bzw. im Cermet.
35,2 | TiC | 9,0 | TaC |
15,1 | TiN | 1,0 | NbC |
19,2 | WC | 4,8 | Ni |
7,1 | MO2C | 8,6 | Co |
Beispiel 1: | erfindungsgemäßer Cermet | Vergleichs Cermet |
Ti-(Oberflächenschicht) / Ti-(Kern): | 1,3 | 1,4 |
Binder-(Oberflächenschicht) / Binder-(Kern) | 0,12 | 0,6 |
Gesamtmenge (W,Mo,Ta,Nb) (Oberfläche) / Gesamtmenge (W,Mo,Ta,Nb) (Kern) | 0,9 | 0,6 |
Dicke der Randschicht | 0,5 µm | 10 µm |
Zone unterhalb der Randschicht mit einer Porosität ≤A02 und <B02 | 200 µm | 250 µm |
und einer Porosität im Kern <A06 und <B02 Rauhtiefe der Oberfläche RT | 5 µm | 15 µm |
RZ | 3,8 µm | 11 µm |
Beispiel 2: | erfindungsgemäßer Cermet | Vergleichs Cermet |
Ti-(Oberflächenschicht) / Ti-(Kern) | 1,23 | 1,00 |
Binder-(Oberflächenschicht) / Binder-(Kern) | 0,15 | 1,20 |
Gesamtmenge (W,Mo,Ta,Nb) (Oberfläche) / Gesamtmenge (W,Mo,Ta,Nb) (Kern) | 0,98 | 0,8 |
Porosität durchgehend ≤A02 und <B02 alle übrigen Werte wie im Beispiel 1. |
26,1 | TiC | 1,1 | NbC |
27,1 | TiN | 8,2 | Ni |
20,1 | WC | 8,7 | Co |
8,7 | TaC |
Beispiel 3: | erfindungsgemäßer Cermet | Vergleichs Cermet |
Ti-(Oberflächenschicht) / Ti-(Kern) | 1,32 | 1,00 |
Binder-(Oberflächenschicht) / Binder-(Kern) | 0,27 | 0,50 |
Gesamtmenge (W,Ta,Nb) (Oberfläche) / Gesamtmenge (W,Ta,Nb) (Kern) | 0,82 | 1,5 |
Dicke der Randschicht | 0,3 µm | 5 µm |
Zone unterhalb der Randschicht mit einer Porosität ≤A02 und <B02 | 100 µm | 120 µm |
Porosität im Kern <A08 und <B02 Rauhtiefe RT | 3,5 µm | 13 µm |
RZ | 2,8 µm | 9 µm |
Beispiel 4: | erfindungsgemäßer Cermet | Vergleichs Cermet |
Ti-Oberflächenschicht / Ti-Kern | 1,21 | 1,00 |
Binder-Oberflächenschicht / Binder-Kern | 0,69 | 1,60 |
Gesamtmenge (W,Ta,Nb) Oberfläche / Gesamtmenge (W,Ta,Nb) Kern | 0,78 | 0,4 |
Porosität durchgehend ≤A02 und <B02 alle übrigen Werte wie in Beispiel 3. |
Drehen im glatten Schnitt, trocken
Schnittgeschwindigkeit Vc = 140 m/min
Schnittiefe ap = 2 mm
Vorschub f = 0,3 mm
Beispiel | Standzeit (min) | |
erfindungsgemäßer Cermet | Vergleichs-Cermet | |
1 | 16 | 5 |
2 | 18 | 9 |
3 | 25 | 12 |
4 | 32 | 13 |
Claims (10)
- Cermet mit einem Hartstoffanteil von 95 bis 75 Massen-% und 5 bis 25 Massen-% Co- und/oder Ni-Binder, wobei die Hartstoffphase aus Carbonitriden mit kubischer B1 Kristallstruktur besteht und 30 bis 60 Massen-% Ti, 5 bis 25 Massen-% W, 5 bis 15 Massen-% Ta, wovon bis zu 70 Massen-% durch Nb ersetzt sein können, 0 bis 12 Massen-% Mo, 0 bis 5 Massen-% V, 0 bis 2 Massen-% Cr, 0 bis 1 Massen-% Hf und/oder Zr enthält, der (C+N)-Gehalt in der Carbonitridphase >80 Mol% beträgt, der Stickstoffanteil N/(C+N) zwischen 0,15 und 0,7 liegt und in der Binderphase bis zu 2 Massen-% Al enthalten und/oder metallisches W, Ti, Mo, V und/oder Cr gelöst ist, wobei nur in einer durch eine Eindringtiefe von 0,01 bis 3 µm bestimmten Oberflächenschicht, meßbar durch eine energiedispersive Mikroanalyse auf einer Meßfläche >(0,5 x 0,5)mm2,1. der Gehalt an Co- und/oder Ni-Binder in bezug auf die darunterliegenden Cermet-Kernbereiche ≤30 Massen-%2. der Ti-Gehalt 110 bis 130 % relativ zu den darunterliegenden Cermet-Kernbereichen3. die Summe der Gehalte an W, Ta sowie etwaige Anteile an Mo, Nb, V und/oder Cr in der 0,01 bis 3 µm dicken Oberflächenschicht relativ zu den darunterliegenden Cermet-Kernbereichen 70 bis 100 Massen-% beträgt.
- Cermet mit einem Hartstoffanteil von 95 bis 75 Massen-% und 5 bis 25 Massen-% Co- und/oder Ni-Binder, wobei die Hartstoffphase aus Carbonitriden mit kubischer B1 Kristallstruktur besteht und 30 bis 60 Massen-% Ti, 5 bis 25 Massen-% W, 5 bis 15 Massen-% Ta, wovon bis zu 70 Massen-% durch Nb ersetzt sein können, 0 bis 12 Massen-% Mo, 0 bis 5 Massen-% V, 0 bis 2 Massen-% Cr, 0 bis 1 Massen-% Hf und/oder Zr enthält, der (C+N)-Gehalt in der Carbonitridphase >80 Mol% beträgt, der Stickstoffanteil N/(C+N) zwischen 0,15 und 0,7 liegt und in der Binderphase bis zu 2 Massen-% Al enthalten und/oder metallisches W, Ti, Mo, V und/oder Cr gelöst ist, wobei der Co- und/oder Ni-Bindergehalt in der Oberflächenschicht mit einer Eindringtiefe von 0,01 bis 3 µm, meßbar durch eine einergiedispersive Mikroanalyse, relativ zu den darunterliegenden Schichten <90 Massen-% bei einem Ti-Gehalt zwischen 100 % bis 120 % relativ zum Kernbereich beträgt und die Summe der Gehalte an W, Ta sowie ggf. Mo, Nb, V, Cr zwischen 80 Massen-% und 110 Massen-% liegt.
- Cermet nach Anspruch 1 oder 2, dadurch gekennzeichnet, daß die unter der Oberflächenschicht liegenden Kernbereiche, zumindest im wesentlichen eine Hartstoffphase mit einer Kern-Rand-Struktur aufweisen und/oder daß in der Oberflächenschicht die Hartstoffphase ausschließlich homogen vorliegt.
- Cermet nach einem der Ansprüche 1 oder 3, dadurch gekennzeichnet, daß die Zone unmittelbar unter der Oberflächenschicht bis zu einer Tiefe von mindestens 50 µm, maximal 600 µm, eine Porosität ≤A02 und <B02 (nach ISO4505) und im darunterliegenden Kern <A08 und <B04 aufweist.
- Cermet nach Anspruch 2 oder 3, dadurch gekennzeichnet, daß der Körper eine durchgehende Porosität ≤A02 und <B02 aufweist.
- Cermet nach einem der Ansprüche 1 bis 5, dadurch gekennzeichnet, daß die Oberflächenrauhtiefe RT ≤ 6 µm oder RZ ≤ 5 µm beträgt und/oder daß die Härte HV 30 im Oberflächenbereich konstant ist.
- Cermet nach einem der Ansprüche 1 bis 6, gekennzeichnet durch eine ein- oder mehrlagige Beschichtung aus Carbiden oder Nitriden des Ti und/oder aus Al2O3, vorzugsweise nach dem CVD-Verfahren aufgetragen.
- Verfahren zur Herstellung eines Cermets nach einem der Ansprüche 1 oder 3 bis 7 durch Mischen, Mahlen, Granulieren und Pressen einer entsprechenden die Bestandteile enthaltenden Ausgangsmischung und anschließendem Sintern, vorzugsweise in Sinteröfen mit Graphitheizleitern, gekennzeichnet durch ein Aufheizen bis zum Schmelzpunkt der Binderphase unter Vakuum mit einem Druck ≤10-1 mbar, weiteres Aufheizen von der Schmelztemperatur der Binderphase bis zur Sintertemperatur, 0,2- bis 2-stündiges Halten der Sintertemperatur und anschließendes Abkühlen auf 1200°C, wobei das weitere Aufheizen, Halten und Abkühlen in einem Gasgemisch aus N2 und CO mit N2/(N2+CO)-Verhältnis zwischen 0,1 und 0,9 unter einem um einen mittleren Druck von 10 % bis 80 % des Mittelwertes alternierend in einer Periodendauer zwischen 40 und 240 sec, vorzugsweise 40 bis 180 sec, mit einem mittleren Druck, der bestimmt ist durch den linearen Zusammenhang y = ( 7 / 10 x + 2,5) ± 10 %, wobei y = mittlerer Druck (mbar) und x = Bindergehalt in Massen-% sind,
und einem N2/(N2+CO)-Verhältnisy , das bestimmt ist durchy = ( 16 / 11x - 0,12) ± 10 % mitx = N/(C+N) im Cermet, und anschließender Abkühlung unter Inertgas, wie Argon, Stickstoff oder unter Vakuum. - Verfahren nach Anspruch 8, dadurch gekennzeichnet, daß bei der Aufheizung im Schmelzpunktbereich (Ts ± 80°C) unter Einlaß von Stickstoff ein Druck von 0,2 mbar geregelt wird, wobei vorzugsweise der gepreßte Körper zunächst auf 1020°C unter Vakuum mit einem Druck ≤0,1 mbar aufgeheizt wird, bevor während des Aufheizens von 1020°C bis 1370°C unter Einlaß von Stickstoff ein Druck von 0,2 mbar geregelt wird.
- Verfahren zur Herstellung eines Cermets nach einem der Ansprüche 2, 3, 5 oder 6 oder 8, 9, dadurch gekennzeichnet, daß nach dem Sintern ein heißisostatisches Pressen unter Argon bei Temperaturen nahe der Sintertemperatur und Drücken oberhalb von 30 bar durchgeführt wird.
Applications Claiming Priority (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE4415454 | 1994-05-03 | ||
DE4415454 | 1994-05-03 | ||
DE4423451 | 1994-07-05 | ||
DE4423451A DE4423451A1 (de) | 1994-05-03 | 1994-07-05 | Cermet und Verfahren zu seiner Herstellung |
PCT/DE1995/000434 WO1995030030A1 (de) | 1994-05-03 | 1995-03-29 | Cermet und verfahren zu seiner herstellung |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0758407A1 EP0758407A1 (de) | 1997-02-19 |
EP0758407B1 true EP0758407B1 (de) | 1998-02-11 |
Family
ID=25936212
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP95913058A Expired - Lifetime EP0758407B1 (de) | 1994-05-03 | 1995-03-29 | Cermet und verfahren zu seiner herstellung |
Country Status (6)
Country | Link |
---|---|
US (1) | US5856032A (de) |
EP (1) | EP0758407B1 (de) |
JP (1) | JPH09512308A (de) |
AT (1) | ATE163203T1 (de) |
ES (1) | ES2112053T3 (de) |
WO (1) | WO1995030030A1 (de) |
Families Citing this family (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US6017488A (en) | 1998-05-11 | 2000-01-25 | Sandvik Ab | Method for nitriding a titanium-based carbonitride alloy |
SE9701859D0 (sv) * | 1997-05-15 | 1997-05-15 | Sandvik Ab | Titanium based carbonitride alloy with nitrogen enriched surface zone |
SE511846C2 (sv) * | 1997-05-15 | 1999-12-06 | Sandvik Ab | Sätt att smältfassintra en titanbaserad karbonitridlegering |
SE512133C2 (sv) * | 1997-07-10 | 2000-01-31 | Sandvik Ab | Metod att framställa titanbaserade karbonitridlegeringar fria från bindefasytskikt |
JP2948803B1 (ja) * | 1998-03-31 | 1999-09-13 | 日本特殊陶業株式会社 | サーメット工具及びその製造方法 |
SE514053C2 (sv) * | 1999-05-03 | 2000-12-18 | Sandvik Ab | Metod för tillverkning Ti(C,N)-(Ti,Ta,W) (C,N)-Co legeringar för skärverktygstillämpningar |
SE525745C2 (sv) * | 2002-11-19 | 2005-04-19 | Sandvik Ab | Ti(C-(Ti,Nb,W)(C,N)-Co-legering för svarvskärtillämpningar för finbearbetning och medelfin bearbetning |
DE10342364A1 (de) * | 2003-09-12 | 2005-04-14 | Kennametal Widia Gmbh & Co.Kg | Hartmetall-oder Cermetkörper und Verfahren zu seiner Herstellung |
DE102008048967A1 (de) * | 2008-09-25 | 2010-04-01 | Kennametal Inc. | Hartmetallkörper und Verfahren zu dessen Herstellung |
US8834594B2 (en) | 2011-12-21 | 2014-09-16 | Kennametal Inc. | Cemented carbide body and applications thereof |
CN116162838B (zh) * | 2023-04-26 | 2023-06-30 | 崇义章源钨业股份有限公司 | 一种金属陶瓷及其制备方法 |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61281835A (ja) * | 1985-06-07 | 1986-12-12 | Sumitomo Electric Ind Ltd | サ−メツトの焼結法 |
JPH0643622B2 (ja) * | 1985-12-04 | 1994-06-08 | 住友電気工業株式会社 | 窒素含有サ−メツトの製造法 |
JPH01152228A (ja) * | 1987-12-10 | 1989-06-14 | Sumitomo Electric Ind Ltd | 窒素含有サーメットの製造法 |
JPH02131803A (ja) * | 1988-11-11 | 1990-05-21 | Mitsubishi Metal Corp | 耐欠損性のすぐれた耐摩耗性サーメット製切削工具 |
SE467257B (sv) * | 1989-06-26 | 1992-06-22 | Sandvik Ab | Sintrad titanbaserad karbonitridlegering med duplexa strukturer |
SE500047C2 (sv) * | 1991-05-24 | 1994-03-28 | Sandvik Ab | Sintrad karbonitridlegering med höglegerad bindefas samt sätt att framställa denna |
SE9101865D0 (sv) * | 1991-06-17 | 1991-06-17 | Sandvik Ab | Titanbaserad karbonitridlegering med slitstarkt ytskikt |
SE9201928D0 (sv) * | 1992-06-22 | 1992-06-22 | Sandvik Ab | Sintered extremely fine-grained titanium based carbonitride alloy with improved toughness and/or wear resistance |
SE470481B (sv) * | 1992-09-30 | 1994-05-24 | Sandvik Ab | Sintrad titanbaserad karbonitridlegering med hårdämnen med kärna-bård-struktur och sätt att tillverka denna |
JPH1152228A (ja) * | 1997-08-05 | 1999-02-26 | Nikon Corp | 広角レンズ |
-
1995
- 1995-03-29 US US08/716,340 patent/US5856032A/en not_active Expired - Fee Related
- 1995-03-29 JP JP7527925A patent/JPH09512308A/ja active Pending
- 1995-03-29 EP EP95913058A patent/EP0758407B1/de not_active Expired - Lifetime
- 1995-03-29 ES ES95913058T patent/ES2112053T3/es not_active Expired - Lifetime
- 1995-03-29 AT AT95913058T patent/ATE163203T1/de not_active IP Right Cessation
- 1995-03-29 WO PCT/DE1995/000434 patent/WO1995030030A1/de active IP Right Grant
Also Published As
Publication number | Publication date |
---|---|
JPH09512308A (ja) | 1997-12-09 |
WO1995030030A1 (de) | 1995-11-09 |
US5856032A (en) | 1999-01-05 |
ES2112053T3 (es) | 1998-03-16 |
EP0758407A1 (de) | 1997-02-19 |
ATE163203T1 (de) | 1998-02-15 |
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