EP0758407B1 - Cermet et son procede de production - Google Patents

Cermet et son procede de production Download PDF

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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
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Prior art keywords
mass
cermet
binder
content
pressure
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Expired - Lifetime
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EP95913058A
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German (de)
English (en)
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EP0758407A1 (fr
Inventor
Hans Werner Daub
Klaus Dreyer
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Widia GmbH
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Widia GmbH
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Priority claimed from DE4423451A external-priority patent/DE4423451A1/de
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/04—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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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
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Claims (10)

  1. Cermet avec une teneur en substance dure de 95 à 75 pour-cent en masse et de 5 à 25 pour-cent en masse de liant de Co et/ou de Ni, la phase de substance dure se composant de carbonitrures avec une structure B1 cristalline cubique et contenant de 30 à 60 pour-cent en masse de Ti, de 5 à 25 pour-cent en masse de W, de 5 à 15 pour-cent en masse de Ta dont jusqu'à 70 pour-cent en masse peuvent être remplacés par du Nb, de 0 à 12 pour-cent en masse de Mo, de 0 à 5 pour-cent en masse de V, de 0 à 2 pour-cent en masse de Cr, de 0 à 1 pour-cent en masse de Hf et/ou Zr, la teneur en (C+N) dans la phase de carbonitrure étant >80 pour-cent molaire, la teneur en azote N/(C+N) étant comprise entre 0,15 et 0,7 et, dans la phase liant, jusqu'à 2 pour-cent en masse de Al étant contenus et/ou du W, Ti, Mo, V et/ou Cr métalliques étant dissous, dans seulement une couche superficielle définie par une profondeur de pénétration de 0,01 à 3 µm, mesurable par une micro-analyse énergie-dispersive sur une surface de mesure >(0,5 x 0,5)mm2,
    1. la teneur en liant de Co et/ou de Ni par rapport aux zones de noyau de cermet situées là-dessous étant ≤30 pour-cent en masse
    2. la teneur en Ti étant de 110 à 130% par rapport aux zones de noyau de cermet situées là-dessous,
    une répartition uniforme de métal liant étant respectivement présente dans le noyau de cermet d'un côté et dans la couche superficielle de l'autre côté et
    3. la somme des teneurs en W, Ta ainsi que des teneurs possibles en Mo, Nb, V et/ou Cr dans la couche superficielle ayant une épaisseur de 0,01 à 3µm, étant comprise entre 70 et 100 pour-cent en masse par rapport aux zones de noyau de cermet situées là-dessous.
  2. Cermet avec une teneur en substance dure de 95 à 75 pour-cent en masse et de 5 à 25 pour-cent en masse de liant de Co et/ou de Ni, la phase de substance dure se composant de carbonitrures avec une structure B1 cristalline cubique et contenant de 30 à 60 pour-cent en masse de Ti, de 5 à 25 pour-cent en masse de W, de 5 à 15 pour-cent en masse de Ta dont jusqu'à 70 pour-cent en masse peuvent être remplacés par du Nb, de 0 à 12 pour-cent en masse de Mo, de 0 à 5 pour-cent en masse de V, de 0 à 2 pour-cent en masse de Cr, de 0 à 1 pour-cent en masse de Hf et/ou Zr, la teneur en (C+N) dans la phase de carbonitrure étant >80 pour-cent molaire, la teneur en azote N/(C+N) étant comprise entre 0,15 et 0,7 et, dans la phase liant, jusqu'à 2 pour-cent en masse de AI étant contenus et/ou du W, Ti, Mo, V et/ou Cr métalliques étant dissous, la teneur en liant de Co et/ou de Ni dans la couche superficielle avec une profondeur de pénétration de 0,01 à 3 µm, mesurable par le biais d'une micro-anlayse énergie-dispersive, par rapport aux couches situées là-dessous étant <90 pour-cent en masse, à une teneur en Ti comprise entre 100% et 120% par rapport à la zone de noyau, et la somme des teneurs en W, Ta ainsi que, le cas échéant, en Mo, Nb, V, Cr étant comprise entre 80 pour-cent en masse et 110 pour-cent en masse.
  3. Cermet selon la revendication 1 ou 2, caractérisé par le fait que les zones de noyau situées au-dessous de la couche superficielle présentent au moins pour l'essentiel une phase de substance dure avec une structure noyau-bord et/ou que, dans la couche superficielle, la phase de substance dure est exclusivement homogène.
  4. Cermet selon l'une des revendications 1 ou 3, caractérisé par le fait que la zone située directement au-dessous de la couche superficielle jusqu'à une profondeur de 50 µm du moins, de 600 µm au maximum, présente une porosité ≤A02 et <B02 (selon ISO4505) et <A08 et <B04 dans le noyau situé là-dessous.
  5. Cermet selon la revendication 2 ou 3, caractérisé par le fait qu'à travers l'ensemble du corps, la porosité est ≤A02 et <B02.
  6. Cermet selon l'une des revendications 1 à 5, caractérisé par le fait que la profondeur de rugosité de la surface est égale à RT ≤6 µm ou RZ ≤5 µm et/ou que la dureté HV 30 est constante dans la zone de la surface.
  7. Cermet selon l'une des revendications 1 à 6, caractérisé par un revêtement à une seule couche ou à plusieurs couches en carbures ou nitrures du Ti et/ou en Al2O3, appliqué de préférence selon le procédé CVD.
  8. Procédé de fabrication d'un cermet selon l'une des revendications 1 ou 3 à 7 par mélange, broyage, granulation et pressage d'un mélange de départ correspondant contenant les composants et par un frittage subséquent, de préférence dans des fours de frittage avec des conducteurs chauffants en graphite, caractérisé par un échauffement jusqu'au point de fusion de la phase liant sous vide avec une pression ≤10-1 mbar, par un autre échauffement de la température de fusion de la phase liant jusqu'à la température pour le frittage, par le maintien de la température pour le frittage pendant une durée de 0,2 à 2 heures et par un refroidissement subséquent à une température de 1200°C, l'autre échauffement, le maintien et le refroidissement étant effectués dans un mélange gazeux de N2 et CO avec un rapport de N2/(N2+CO) compris entre 0,1 et 0,9, sous une pression moyenne alternant d'une pression moyenne de 10% à 80% de la valeur moyenne, dans une durée de période entre 40 et 240 secondes, de préférence de 40 à 180 secondes, avec une pression moyenne qui est déterminée par la relation linéaire
    Figure 00240001
    où y = la pression moyenne (mbar) et x = la teneur en liant en pour-cent en masse, et avec un rapport y de N2/(N2+CO) qui est détérminé par
    Figure 00240002
    avec x =N/(C+N) dans le cermet, et par un refroidissement subséquent sous gaz inerte tel qu'argon, azote ou sous vide.
  9. Procédé selon la revendication 8, caractérisé par le fait qu'une pression de 0,2 mbar est réglée lors de l'échauffement dans le domaine de point de fusion (TS±80°C) avec l'admission de l'azote, de préférence, le corps pressé étant d'abord échauffé à une température de 1020°C sous vide avec une pression ≤0,1 mbar, avant qu'une pression de 0,2 mbar soit réglée durant l'échauffement de 1020°C à 1370°C avec l'admission de l'azote.
  10. Procédé de fabrication d'un cermet selon l'une des revendications 2, 3, 5 ou 6 ou 8, 9, caractérisé par le fait que l'on effectue, après le frittage, une compression isostatique à température élevée sous argon, à des températures prés de la température pour le frittage et des pressions supérieures à 30 bar.
EP95913058A 1994-05-03 1995-03-29 Cermet et son procede de production Expired - Lifetime EP0758407B1 (fr)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
DE4415454 1994-05-03
DE4415454 1994-05-03
DE4423451A DE4423451A1 (de) 1994-05-03 1994-07-05 Cermet und Verfahren zu seiner Herstellung
DE4423451 1994-07-05
PCT/DE1995/000434 WO1995030030A1 (fr) 1994-05-03 1995-03-29 Cermet et son procede de production

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EP0758407A1 EP0758407A1 (fr) 1997-02-19
EP0758407B1 true EP0758407B1 (fr) 1998-02-11

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US (1) US5856032A (fr)
EP (1) EP0758407B1 (fr)
JP (1) JPH09512308A (fr)
AT (1) ATE163203T1 (fr)
ES (1) ES2112053T3 (fr)
WO (1) WO1995030030A1 (fr)

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SE511846C2 (sv) * 1997-05-15 1999-12-06 Sandvik Ab Sätt att smältfassintra en titanbaserad karbonitridlegering
SE9701859D0 (sv) * 1997-05-15 1997-05-15 Sandvik Ab Titanium based carbonitride alloy with nitrogen enriched surface zone
US6017488A (en) * 1998-05-11 2000-01-25 Sandvik Ab Method for nitriding a titanium-based carbonitride alloy
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

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* Cited by examiner, † Cited by third party
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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

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EP0758407A1 (fr) 1997-02-19
ES2112053T3 (es) 1998-03-16
US5856032A (en) 1999-01-05
WO1995030030A1 (fr) 1995-11-09
ATE163203T1 (de) 1998-02-15
JPH09512308A (ja) 1997-12-09

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