WO2004065045A1 - Outil de coupe en ceramique dote d'une zone peripherique, procede de fabrication et utilisation associes - Google Patents

Outil de coupe en ceramique dote d'une zone peripherique, procede de fabrication et utilisation associes Download PDF

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Publication number
WO2004065045A1
WO2004065045A1 PCT/EP2004/000243 EP2004000243W WO2004065045A1 WO 2004065045 A1 WO2004065045 A1 WO 2004065045A1 EP 2004000243 W EP2004000243 W EP 2004000243W WO 2004065045 A1 WO2004065045 A1 WO 2004065045A1
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WIPO (PCT)
Prior art keywords
edge
ceramic
cutting tool
sintering
edge zone
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PCT/EP2004/000243
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German (de)
English (en)
Inventor
Wolfgang Hintze
Gerold Schneider
Arndt PÜSCHEL
Nils Claussen
Marie-Helene Berger
Christian Nedess
Original Assignee
Technische Universität Hamburg-Harburg
Tuhh Technologie Gmbh
Priority date (The priority date 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 date listed.)
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Publication date
Priority claimed from DE2003207478 external-priority patent/DE20307478U1/de
Application filed by Technische Universität Hamburg-Harburg, Tuhh Technologie Gmbh filed Critical Technische Universität Hamburg-Harburg
Priority to US10/542,479 priority Critical patent/US20110094363A1/en
Priority to EP04702300A priority patent/EP1585610A1/fr
Publication of WO2004065045A1 publication Critical patent/WO2004065045A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
    • C04B41/45—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements
    • C04B41/52—Multiple coating or impregnating multiple coating or impregnating with the same composition or with compositions only differing in the concentration of the constituents, is classified as single coating or impregnation
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
    • C04B41/45—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements
    • C04B41/50—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements with inorganic materials
    • C04B41/5053—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements with inorganic materials non-oxide ceramics
    • C04B41/5057—Carbides
    • C04B41/5061—Titanium carbide
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
    • C04B41/45—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements
    • C04B41/50—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements with inorganic materials
    • C04B41/5053—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements with inorganic materials non-oxide ceramics
    • C04B41/5062—Borides, Nitrides or Silicides
    • C04B41/5068—Titanium nitride
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
    • C04B41/80—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone of only ceramics
    • C04B41/81—Coating or impregnation
    • C04B41/85—Coating or impregnation with inorganic materials
    • C04B41/87—Ceramics
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
    • C04B41/80—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone of only ceramics
    • C04B41/81—Coating or impregnation
    • C04B41/89—Coating or impregnation for obtaining at least two superposed coatings having different compositions

Definitions

  • the invention relates to a ceramic cutting tool or a cutting ceramic with an edge zone or edge layer with improved wear resistance, toughness, strength and hardness, a method for its production and use.
  • Cutting ceramics are naturally hard materials based on oxide or nitride.
  • oxide ceramics are divided into so-called white oxide ceramics based on corundum (Al 2 O 3 ) with additives, mainly zirconium oxide (ZrO 2 ), and so-called black mixed ceramics with relatively high proportions of titanium carbide or titanium carbonitride. They are manufactured by sintering, hot isostatic pressing or hot pressing at temperatures from 1500 ° to 2000 ° C. The hardness of these materials only drops sharply at higher temperatures. As a result of high wear resistance, low tendency to diffusion and resistance to oxidation, oxide ceramics enable very high cutting speeds.
  • Ceramic composite bodies consisting of a basic structure and an outer edge layer are known from DE 41 19 705. These ceramic composite bodies have a gas-tight outer layer, which consists entirely of wear-resistant ceramic, in particular oxides, carbides, nitrides and / or borides of aluminum and zirconium, an inner structure made of metallic and ceramic phases (cermet) and an intermediate layer, which contains the ceramic Connects outer layer with the inner structure and forms a continuous transition from the outer layer to the metal-containing inner structure.
  • This ceramic body is said to be characterized by high strength, wear resistance as well as high thermal shock resistance and an outer layer that does not tend to flake off.
  • the grading of hard metals is also known; it enables a defined variation of the structural, thermal and functional properties of hard metals (Lengauer, W .; Dreyer, K .: Functionally graded hardmetals, Journal of Alloys and Compounds 338 (2002) 194-212, and Ucakar, V .; Kral, C; Dreyer, K .; Lengauer, W .: Near-surface microstructural modification of (Ti, W) (C, N) -based compacts with nitrogen, 15 th International Plansee Seminar, Eds. Kneringer, G .; Rödhammer , P. and Wildner, H .; Plansee Holding AG, Reuttle (2001) Vol. 2).
  • Coatings can also be used to improve the performance properties of hard metal and ceramic cutting materials.
  • the hardness, the coefficient of friction and the resistance to oxidation can be varied depending on the main application (DE 197 09 980 C1 and DE 36 08 734 C1).
  • whisker-reinforced ceramic cutting tools are known (EP 0 861 219).
  • Cutting ceramics made of Al 2 O 3 and TiC are known from US 3,580,708.
  • a disadvantage in the production of known cutting ceramics is the use of pure, preferably high-purity starting materials, for example oxygen-free TiC, likewise high sintering temperatures are necessary for the production of cutting ceramics according to the prior art, which require high energy expenditure and thus lead to high production costs for known mixing ceramics.
  • Another disadvantage is wear resistance that can be improved and, like hard metals, can be increased by coatings. Due to the process technologies used, there is an abrupt (non-graded) mass transfer from the material to be coated to the layer material which only allows a weak layer adhesion and can lead to flaking when used. In addition, with increasing layer thicknesses (also in multiple layers), the cutting edge is rounded, so that the cutting edge geometry previously worked out, usually worked out with diamond tools, is lost.
  • Known coating methods also require complex charging due to the process.
  • the functional behavior of the cutting ceramics is to be improved in particular in the finishing of hardened steels and the machining of cast materials.
  • an edge zone or edge layer which does not tend to flake off, in which the cutting edge geometry is retained, in particular sharp-edged cutting edges are not to be rounded.
  • the charging of the inserts for edge zone production / coating is to be simplified.
  • the ceramic cutting tool according to the invention is a multi-phase ceramic (starting ceramic), which consists of a basic ceramic and a sacrificial phase as well as optionally additives and primary hard material phases and a wear-resistant, hard, not deposited, possibly multi-layered edge zone or edge layer of at least one hard material phase, the edge zone being intimate with the original ceramic is growing, and is formed by aging the original ceramic in a defined atmosphere.
  • start ceramic consists of a basic ceramic and a sacrificial phase as well as optionally additives and primary hard material phases and a wear-resistant, hard, not deposited, possibly multi-layered edge zone or edge layer of at least one hard material phase, the edge zone being intimate with the original ceramic is growing, and is formed by aging the original ceramic in a defined atmosphere.
  • the multiphase cutting ceramic according to the invention consist in the use of inexpensive raw materials and low sintering temperatures due to the process.
  • the ceramic body is subjected to a temperature treatment, preferably pressure-assisted, after the hard machining to produce the cutting edge geometry, which is carried out in a reducing atmosphere and / or reducing sintered bed, the characteristic elements of the layer material, which are specified in more detail below, not being provided by secondary sources become.
  • the charging of the cutting bodies is very simple.
  • the edge zone is ideally connected to the structure of the multi-phase cutting ceramic, so that there is little tendency to flake off.
  • the wear and wear properties of the cutting ceramic are improved by the hard material edge layers produced according to the invention (cf.
  • the cutting edge geometry is generated in the green state of the ceramic cutting body, in order to simultaneously produce an edge zone during the sintering and thus further reduce the production costs.
  • a favorable composition of the multi-phase cutting ceramic also makes it possible to produce multi-layer coatings for a further advantageous embodiment of the cutting tool, in terms of improving its wear, friction and usage properties.
  • the multi-phase cutting tool according to the invention consists of a starting ceramic, which is composed of a basic ceramic with at most 50% by volume of one or more sacrificial phases and with at most 40% by volume additives and with at most 50% by volume of one or more primary hard material phases, as well as an edge zone ( or boundary layer or edge area).
  • the edge zone has grown into the base material / starting ceramic. Compared to the base material, the edge zone has no or a significantly reduced proportion of starting ceramics, in particular basic ceramics, and is realized after the usually last production step, the hard machining of ceramic cutting plates, by means of a subsequent, optionally pressure-assisted temperature treatment in a reducing atmosphere.
  • the base ceramic is a ceramic, preferably aluminum oxide, based on one or more metallic or semi-metallic compounds Aen with oxygen and / or nitrogen.
  • the sacrificial phase is the oxide and / or an oxygen-containing compound made of carbon and / or nitrogen and / or boron, one or more characteristic elements, especially titanium oxycarbide and / or titanium oxycarbonitride.
  • the characteristic elements are preferably elements of the 3rd or 4th or 5th period, the IV or V or VI subgroup of the periodic table of the elements and / or boron and / or silicon, preferably titanium and / or zirconium and / or vanadium and / or Tungsten and / or boron and / or silicon, especially titanium and / or zirconium.
  • Additives denote desired or tolerated, but also inevitably present additives in the form of additives, sintering aids and impurities which are contained in the starting powders, added to the powder versa or added as a result of the powder preparation or caused by abrasion; preferably ZrO 2 .
  • the primary hard material phase is the carbide and / or nitride and / or boride, and / or carbonitride and / or carboboride and / or boron nitride and / or Carbobomitride of one or more characteristic elements, preferably titanium carbide and / or titanium carbonitride, especially titanium carbide.
  • the edge zone consists of one or more hard material phase (s), the carbide and / or nitride and / or boride and / or their mixtures of one or more characteristic elements, is constructed in one or more layers and has no or a significantly reduced proportion compared to the base material on basic ceramics.
  • the starting ceramic used in the ceramic cutting tool is provided by an aluminothermic production and / or conventional, pressure-free, possibly vacuum-assisted sintering and / or hot-isostatic pressing and / or hot pressing and / or microwave sintering and / or laser sintering in a reducing atmosphere.
  • the multiphase ceramic consists of at least two characteristic structural components (phases), preferably Al 2 O 3 (as basic ceramic) and a sacrificial phase, preferably an oxide and / or oxy-nitride and / or oxynitride and / or oxy-boride and / or oxy-carbonitride and / or oxy-carboboride and / or Oxiborn trid and / or Oxikarbobomitrid, especially an Oxikarbid and / or Oxin trid and / or Oxikarbonitrid, whereby the following phases, preferably Al 2 O 3 (as basic ceramic) and a sacrificial phase, preferably an oxide and / or oxy-nitride and / or oxynitride and / or oxy-boride and / or oxy-carbonitride and / or oxy-carboboride and / or Oxiborn trid and / or Oxikarbobomitrid, especially an Oxikarbid and
  • Al 2 O 3 phase preferably made of Al 2 O 3 without impurities, especially high-purity Al 2 O 3 .
  • the multiphase ceramic which is preferably based on Al 2 O 3 , has a structure which has an average grain size between 100 nm and 10 ⁇ m, preferably between 300 nm and 5 ⁇ m, especially between 500 nm and 3 ⁇ m.
  • the edge zone of the cutting tool has a thickness between 0.1 ⁇ m and 20 ⁇ m, preferably between 0.5 ⁇ m and 8 ⁇ m, especially between 1 ⁇ m and 4 ⁇ m; a transition zone with a thickness of 50 nm to 5 ⁇ m is formed with the base material.
  • the sacrificial phase consists in particular of titanium oxycarbide and / or titanium oxynitride and / or titanium oxycarbonitride and, in a preferred embodiment, has a lower nanohardness than AI 2 O 3 , at most 26 GPa (measured with Berkovichindenter, at 3 mN), preferably at most 25 GPa, exactly 23 GPa.
  • the edge zone of the ceramic cutting tool or the cutting ceramic consists in particular of titanium carbide and / or titanium carbonitride and has a higher nanohardness than Al 2 O 3 , preferably in the range from 27 GPa to 35 GPa (measured with Berkovich indenter at 3 mN), especially 29 GPa up to 32 GPa.
  • a further embodiment of the ceramic cutting tool provides that the edge zone is produced like a coating or a coating scheme (multi-layer coating from the same and / or different materials) or, by means of chemical and / or physical deposition, influences the properties of the cutting tool, preferably the hardness and changed the wear resistance, especially the usage properties improved.
  • the cutting ceramic according to the invention is u. a. used as a cutting tool for processing metallic materials with a hardness greater than 50 HRC, preferably hardened steel and / or cast materials.
  • the cutting edge of the cutting ceramic is formed by a rake face and a free face when the rake face and the free face meet; it is preferably chamfered.
  • a transition zone of between 50 nm and 5 ⁇ m is formed between the edge zone and the starting material, in which they are intimately grown.
  • the structure of the multiphase starting ceramic has an average grain size between 100 nm and 10 ⁇ m, preferably between 300 nm and 5 ⁇ m, especially between 500 nm and 3 ⁇ m.
  • the sacrificial phase consists of titanium oxycarbide and has a lower nanohardness (measured with Berkovichindenter, at 3 mN) than Al 2 O 3 , at most 26 GPa, preferably 23 GPa.
  • the edge zone or edge layer mainly contains titanium carbide, which has a higher nanohardness (measured with Berkovichindenter, at 3 mN) than Al 2 O 3 , preferably between 27 GPa to 35 GPa, especially 29 GPa to 32 GPa.
  • a single-layer or multi-layer coating is applied to the edge zone or the edge region by means of physical and / or chemical deposition from the same and / or different materials, the performance properties of the cutting tool being improved.
  • the method according to the invention for producing the cutting tool comprises the following steps:
  • the starting powders are prepared, green bodies are produced and compressed into semi-finished products using known sintering processes;
  • the method comprises the following steps:
  • the starting powders are prepared and green bodies are produced using known powder metallurgical processes
  • a third embodiment of the method according to the invention for producing the ceramic cutting body with improved wear resistance, toughness, strength and hardness of the edge zone or the edge layer consists in that a multiphase starting ceramic / base material is provided which consists of at most 50% by volume of sacrificial phase and at most 40 % By volume of additives and at most 50% by volume of primary hard material phase, and the rest of the base ceramic consists of
  • a hard machining of the sintered ceramic body is carried out, preferably by grinding, in particular the rake face, protective chamfer and free face, and
  • the starting powders are prepared and green bodies are produced using known powder metallurgical processes; the composition of the starting powders is preferably chosen with regard to reaction sintering, especially with regard to aluminothermic reaction sintering;
  • Pre-sintering of the green body preferably below the intended maximum sintering temperature, preferably in the temperature range from 200 ° and 1500 ° C., especially 300 and 800 ° C., preferably at a pressure between 0.001 mbar and 1 bar, especially between 0.01 mbar and 100 mbar, preferably using a purge gas, especially argon, preferably in a defined atmosphere, preferably in a reducing, especially in a carbon-containing atmosphere;
  • Second sintering or dense sintering of the pre-sintered and hard-worked semi-finished product with simultaneous or subsequent aging in a defined atmosphere to produce an edge zone or edge layer.
  • the sintering or the pre-sintering and / or the second sintering of the ceramic cutting body is carried out by means of aluminothermic or reactive or conventional pressure-less, possibly vacuum-assisted Sintering and / or by means of hot isostatic pressing and / or hot pressing and / or microwave sintering and / or laser sintering.
  • the edge zone is formed by thermal, optionally pressure-supported outsourcing or sintering of the cutting body.
  • the edge zone can also be formed by aging in a defined, preferably reducing, especially carbon-containing atmosphere, preferably in an oven with heating elements containing carbon or carbon. Furthermore, the formation of the edge zone is possible by aging in a defined, preferably reducing, especially nitrogen-containing atmosphere.
  • the edge zone is preferably by aging at maximum temperatures between 1000 ° C and 2500 ° C, preferably between 1300 ° C and 2000 ° C, especially between 1550 ° and 1650 ° C and by thermal or thermal pressure-supported aging at a pressure of between 0.001 mbar and 4000 bar, preferably at a pressure between 100 bar and 3000 bar.
  • the edge zone is preferably formed by aging using purging and / or compressed gases, preferably argon and / or nitrogen, especially argon.
  • the edge zone is further formed by aging with holding times between 1 min and 300 min, preferably between 5 min and 180 min, especially between 10 min and 60 min, at a pressure selected according to claim 23 and / or a temperature selected according to claim 22.
  • the aging takes place in a sintered bed, preferably a carbon-containing sintered bed.
  • the outsourcing creates an outer zone that is discolored, preferably a golden yellow on the surface.
  • the invention provides for the use of a ceramic cutting tool with improved wear resistance, toughness, strength and hardness of the edge zones or edge layer, as part according to one of claims 1 to 13 in apparatus and machine construction, in particular as a cutting plate.
  • a ceramic cutting tool is created which has high wear resistance, toughness, strength and hardness, in particular in the edge zone or edge layer.
  • the wear resistance of such mixed ceramic cutting materials is increased, with the lowest possible production outlay being achieved.
  • the functional behavior of the cutting ceramic is improved, in particular when finishing hardened steels and machining cast materials.
  • a sharp-edged cutting edge and an edge zone or edge layer or edge area which is not prone to flaking is achieved.
  • the charging of the inserts for edge zone production / coating is simplified.
  • phase inventory sacrificial phase
  • simple charging the marginal zone production / coating is simplified.
  • the method according to the invention offers the possibility or the cutting bodies according to the invention offer the advantage that the hardness / wear and toughness / bending strength properties of base material and surface layer can be optimized separately. For example, the free-space wear that determines the tool life in hard finishing can be reduced without reducing the toughness.
  • Show it: 1 is a schematic view of the composition and structure of a ceramic cutting body with a specially designed edge zone,
  • FIG. 3 shows an exemplary embodiment of the process sequence for producing a ceramic cutting body in a schematic illustration with process parameters
  • FIG. 4 shows a more general schematic representation of the exemplary embodiment of the method sequences for producing a ceramic cutting body shown in FIG. 3, FIG.
  • FIG. 5 is a scanning electron micrograph of an oblique grinding of the edge zone of a ceramic cutting body with basic structure, hard material layer (TiC), transition zone (hard material layer base material) and cutting body surface (posthip surface),
  • FIG. 6 shows a scanning electron microscopic representation of the structure of a ceramic cutting body, with an element mapping on a cross section of a cutting body with a specially designed edge zone, and
  • the ceramic cutting body shown in FIGS. 1 and 2 has a wear-resistant edge zone 20, which is present in full, with increased wear resistance. Furthermore, the phase inventory of the ceramic is exemplified in FIG. 1. 2 shows in the micrograph the starting ceramic 10 consisting of Al 2 O 3 , ZrO 2 and Ti (0, C) as well as the through a high content of TIC marked edge zone 20, which has grown together with the original ceramic and has a thickness of about 2-3 microns.
  • the process is initially based on an exothermic reduction of a metal oxide by metallic aluminum with the formation of Al 2 O 3 in situ.
  • Various mixed ceramics can be produced by adding primary ceramic hard material phases, eg TiC, Ti (C, N), TiN, to the starting powder mixture.
  • the aluminothermic production of mixed ceramics is shown schematically in FIGS. 3 and 4.
  • the powder batch (A) is composed of reactive and inert components.
  • the reactive components aluminum and TiO 2 realize the in situ formation of Al 2 O 3 .
  • the reactants are not in a stoichiometric ratio, so that no metallic titanium remains, but a titanium mixed phase of a titanium oxycarbide or titanium oxycarbonate from the primary constituents TiO 2 and the carbon of the furnace atmosphere, from the graphite heating elements of the furnace or one of them Sample surrounding graphite or graphite-containing sintered bed, as well as the optionally used primary hard material, for example. TiC, Ti (C, N) or TiN is formed.
  • the sintered cutting plate blanks are preferably hard-machined by grinding on the flank face, rake face and cutting edge (F) and provided with the desired cutting edge geometry.
  • edge zones are formed from hard materials such as TiC x with a significantly reduced Al 2 ⁇ 3 content.
  • 5 shows the edge zone 20 in the oblique section of a cutting body with a significantly reduced Al 2 O 3 content compared to the basic structure 10, and the transition zone in which the basic structure and edge zone have grown together intimately.
  • 6 shows SEM images of a cross section as well as distributions of the elements Al, O, Ti and Zr in the starting ceramic 10 and the edge zone 20.
  • edge zone or the top layer of a multi-layer edge zone favorable friction behavior and, due to the color, a clear detection of the cutting edge wear is achieved.
  • the advantage of the method for producing mixed ceramic cutting materials with an edge zone or edge layer is a simple charging of the cutting bodies for edge zone or layer production.
  • the process enables the cutting bodies to be packed / charged tightly in the process of creating edge zones.
  • the cutting bodies can be stacked directly on top of one another, so that the diffusion reactions which produce the edge zones only take place at the accessible areas near the cutting edges and, accordingly, the edge zones are preferably formed in the area of the cutting edges.
  • cutting bodies can be used to further increase the use properties with known variants of conventional coating processes, e.g. PVD and / or CVD can be coated subsequently.
  • a cutting body is produced in the stages shown in FIG. 3, reference being made to the respective process conditions indicated in FIG. 3, which represent an exemplary embodiment.
  • the powder batch is produced, ie for example a mixture of 35% by volume Al 2 O 3 , 15% by volume TiC, 21.5% by volume A1 and 28.5% by volume TiO 2 .
  • stage B powder preparation by attrition.
  • the powder batch is attracted for 7 hours at 700 rpm in acetone using Y-TZP grinding balls and Y-TZP grinding disks in an Al 2 ⁇ 3 container.
  • stage C powder conditioning takes place by drying and sieving with a mesh size of 200 ⁇ m.
  • stage D the base body is first produced by uniaxal pressing at 5 MPa and then cold isostatic pressing at 900 MPa.
  • Stage E includes reaction sintering in a vacuum (after argon purge) in a graphite-heated gas sintering furnace, the sintering program includes the following heating rates and holding times:
  • step F is followed in step F by hard machining by means of grinding, and finally, in accordance with the method according to the invention, step G is followed by hot isostatic pressing, especially at 1625 ° C., with argon as compressed gas, especially at 200 MPa, in a heated with graphite elements hot isostatic press over a period of 10 minutes, so that a ceramic cutting body with the properties specified above is obtained in the edge zone or edge layer.
  • step G is followed by hot isostatic pressing, especially at 1625 ° C., with argon as compressed gas, especially at 200 MPa, in a heated with graphite elements hot isostatic press over a period of 10 minutes, so that a ceramic cutting body with the properties specified above is obtained in the edge zone or edge layer.
  • 5 and 6 show an oblique cut of an edge zone according to the invention.
  • stage E The process stages specified in FIG. 3 are shown as a schematic sequence in FIG. 4, stage E with the reaction sintering illustrating the sequence of sintering via the phase development of the starting powder.
  • stage E The temperature and pressure ranges and process times indicated in FIGS. 3 and 4 do not represent a range limitation; process conditions deviating from the specified value ranges are also possible; compressed gases other than those specified can also be used.
  • a further embodiment of the process processes for producing a cutting body according to the invention according to FIGS. preparation of the green body before process step (E), for example by grinding the rake face, free surface and protective chamfer to form a cutting edge, in which case process step (F) can be dispensed with.
  • process steps (E) and (G) can be combined, thereby reducing process times and costs.
  • the green body is preferably pre-sintered in a first sintering process below the intended maximum sintering temperature.
  • This presintering preferably takes place in a vacuum and in a reducing atmosphere.
  • the semi-finished product is then hard-machined, taking into account any porosity that may still be present, and is densely sintered in a second sintering process at maximum temperatures in the range from 1550-1650 ° C and a holding time of 30-60 min in an evacuated, preferably graphite-heated, sintering furnace and then or subsequently in a defined atmosphere thermally outsourced.
  • the sealing sintering is followed by hot isostatic pressing in a defined atmosphere.
  • the atmosphere is reducing, preferably containing carbon and / or nitrogen.
  • This variant enables a reduction in hard machining costs by generating the geometry of the cutting body on a semi-finished product of lower strength, whereby in comparison to green body processing, smaller shrinkage-related dimensional deviations, higher cutting edge qualities and a lower sensitivity of the semi-finished products during handling are achieved due to the presintering.
  • the green body is reactively presintered in a first sintering process in a temperature range of 500-800 ° C., preferably at a heating rate of 1 K / min between 550 and 700 ° C., whereby the aluminothermic reaction is at least partially or completely completed.
  • the semi-finished product is hard-machined taking into account the existing porosity, subjected to a second sintering process or hot-isostatically pressed and thermally aged or subsequently in a defined atmosphere.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Ceramic Engineering (AREA)
  • Materials Engineering (AREA)
  • Structural Engineering (AREA)
  • Organic Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Compositions Of Oxide Ceramics (AREA)

Abstract

L'invention concerne un outil de coupe en céramique à plusieurs phases, dont la zone ou couche périphérique est plus résistante à l'usure. Cet outil consiste en une céramique de base et en une phase sacrificielle, il est éventuellement doté d'additifs et de phases de substance dure primaires, ainsi que d'une zone ou couche périphérique dure, résistante à l'usure, non séparée et éventuellement en plusieurs couches, cette couche périphérique étant dotée d'au moins une phase de substance dure. A la suite de processus de diffusion et de transposition, la zone périphérique est intimement liée à la céramique de départ et formée par transfert de la céramique de départ dans une atmosphère déterminée.
PCT/EP2004/000243 2003-01-17 2004-01-15 Outil de coupe en ceramique dote d'une zone peripherique, procede de fabrication et utilisation associes WO2004065045A1 (fr)

Priority Applications (2)

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US10/542,479 US20110094363A1 (en) 2003-01-17 2004-01-15 Ceramic cutting tool with an edge area, method for the production and use thereon
EP04702300A EP1585610A1 (fr) 2003-01-17 2004-01-15 Outil de coupe en ceramique dote d'une zone peripherique, procede de fabrication et utilisation associes

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DE20300823.5 2003-01-17
DE20300823 2003-01-17
DE20307478.5 2003-05-14
DE2003207478 DE20307478U1 (de) 2003-01-17 2003-05-14 Keramisches Schneidwerkzeug mit einer Randzone

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WO2004065045A1 true WO2004065045A1 (fr) 2004-08-05

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Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4447263A (en) * 1981-12-22 1984-05-08 Mitsubishi Kinzoku Kabushiki Kaisha Blade member of cermet having surface reaction layer and process for producing same
JPH04289002A (ja) * 1991-03-13 1992-10-14 Mitsubishi Materials Corp 硬質層被覆アルミナ系セラミックス切削工具
JPH05208304A (ja) * 1992-01-28 1993-08-20 Mitsubishi Materials Corp アルミナー炭窒化チタン系セラミックス切削工具
US5275981A (en) * 1990-02-23 1994-01-04 Mitsubishi Material Corporation Al2 O3 based ceramic

Patent Citations (4)

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Publication number Priority date Publication date Assignee Title
US4447263A (en) * 1981-12-22 1984-05-08 Mitsubishi Kinzoku Kabushiki Kaisha Blade member of cermet having surface reaction layer and process for producing same
US5275981A (en) * 1990-02-23 1994-01-04 Mitsubishi Material Corporation Al2 O3 based ceramic
JPH04289002A (ja) * 1991-03-13 1992-10-14 Mitsubishi Materials Corp 硬質層被覆アルミナ系セラミックス切削工具
JPH05208304A (ja) * 1992-01-28 1993-08-20 Mitsubishi Materials Corp アルミナー炭窒化チタン系セラミックス切削工具

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Title
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PATENT ABSTRACTS OF JAPAN vol. 017, no. 648 (M - 1518) 2 December 1993 (1993-12-02) *
SCHEPPOKAT S ET AL: "RBAO Composites Containing TiN and TiN/TiC", JOURNAL OF THE EUROPEAN CERAMIC SOCIETY, ELSEVIER SCIENCE PUBLISHERS, BARKING, ESSEX, GB, vol. 16, no. 9, 1996, pages 919 - 927, XP004047393, ISSN: 0955-2219 *

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