EP2195473A1 - Outil - Google Patents

Outil

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Publication number
EP2195473A1
EP2195473A1 EP08758755A EP08758755A EP2195473A1 EP 2195473 A1 EP2195473 A1 EP 2195473A1 EP 08758755 A EP08758755 A EP 08758755A EP 08758755 A EP08758755 A EP 08758755A EP 2195473 A1 EP2195473 A1 EP 2195473A1
Authority
EP
European Patent Office
Prior art keywords
tool according
metal
binder
phase
coating
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.)
Withdrawn
Application number
EP08758755A
Other languages
German (de)
English (en)
Inventor
Benno Gries
Leo Prakash
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
HC Starck GmbH
Original Assignee
HC Starck 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.)
Filing date
Publication date
Application filed by HC Starck GmbH filed Critical HC Starck GmbH
Publication of EP2195473A1 publication Critical patent/EP2195473A1/fr
Withdrawn legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/067—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds comprising a particular metallic binder
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/08—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on tungsten carbide
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • C23C30/005—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
    • C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
    • C23C4/06—Metallic material
    • 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
    • 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
    • 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
    • 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
    • Y10T428/31504—Composite [nonstructural laminate]
    • Y10T428/31678—Of metal

Definitions

  • the present invention relates to a coated
  • Metal cutting tool with reduced adhesion wear and increased heat resistance in particular a hard metal tool for machining of alloys such as steels, cast iron, stainless steels and non-ferrous base alloys, such as superalloys.
  • Carbide tools for metal cutting are composites and consist of at least two phases, one of which is the metallic binder phase, and one or more the hard material phase (s).
  • hard materials are in particular carbides, nitrides and carbonitrides of refractory metals such as tungsten, molybdenum, titanium, zirconium, hafnium, chromium, vanadium, niobium and tantalum in question.
  • the binder phase generally consists of cobalt and, depending on the carbon activity during sintering, contains fractions of such refractory metals whose free formation enthalphes are low enough to partially decompose into the metallic form during sintering, in particular W, Cr and Mo.
  • the binder phase can also contain Fe and Ni 1 or even Fe and Ni and no cobalt.
  • Such binding systems show advantages in the field of toxicology, since they have less contact corrosion with carbides than with pure cobalt.
  • Fe and Ni there has been no shortage of attempts in the past to introduce FeCoNi or FeNi-based binding systems in carbide metal cutting tools, which has hitherto not been technically successful, unlike other hard metal applications.
  • the binder phase encloses in the sintered state, the hard material phase, which can have a determined by optical or electron-optical methods size between 10 and 0.05 microns after sintering - depending on Zerspanungsaufgabe. This size is mainly adjusted by the fineness of the hard powder used.
  • Cutting tools have a defined geometry, whose task is, for example, to use the tool in a cutting tool receiving the cutting forces frictionally to create the chip and deliberately break, and dissipate the resulting heat as possible with the expiring Span.
  • So-called indexable inserts have a basic geometry derived from a cuboid or a plate, often with a hole in the middle, and one or more cutting edges with a purposefully produced fillet.
  • the hot hardness of Fe, Co or Ni base alloys can be increased by alloying the elements of subgroup 6a of the periodic table.
  • carbide production with cobalt as a binder it is possible by controlling the carbon potential during sintering to alloy up to about 6 mol% tungsten to the binder, which leads to carbide tools with outstanding heat resistance or hot hardness.
  • FeCoNi-based binder systems with low cobalt contents, and more particularly FeNi-based as the cobalt content decreases, less and less tungsten dissolves, so that the hot strengths of these binder alloys are generally insufficient for machining.
  • the solubility of WC in Fe, Co or Ni is 7, 22 and 12 percent by weight, respectively, which additionally depends on the carbon supply. Therefore, it is believed by those skilled in the art that decreasing cobalt content is expected to result in decreasing hot hardness, and thus increasingly less suitable as a binder phase for carbide tools for metal cutting. Since the cost of the binder phase increases with increasing cobalt content, and also the health risk due to corresponding grinding dust during finishing, there is an interest in reducing the cobalt content of the binder phase as much as possible in the production of metal cutting tools. While hard metals with pure Fe and pure Co binder have a good course of the hot hardness, those with pure Ni binder are greatly inferior. The reason is the high ductility of the nickel.
  • Prakash Leo J. Prakash, University of Düsseldorf 1979,
  • binder alloys based on FeCoNi with cobalt contents lower than 40% achieved without alloying with other elements quite heat curing which are similar to those of pure cobalt binder from 400 to 800 0 C equal or even superior to, for example, FeCoNi 70/15/15, 65 / 20/15 and 25/25/50 or 50/25/25, despite the lower bond densities compared to cobalt and thus higher binder contents in the cemented carbide. Therefore, such binder alloys are in principle suitable to withstand the stresses on the cutting edge as well as cobalt, or even clearly superior in the case of the latter alloy.
  • thermal shock resistance When carbide tools with intermittent engagement, as happens when interrupted rotation or milling, also plays the thermal shock resistance a role. This size depends on physical parameters such as coefficient of expansion, thermal conductivity and tensile strength at high temperatures. Lack of thermal shock resistance manifests itself in so-called comb cracks on the cutting edge.
  • the invention relates to carbide tools, in particular
  • a carbide tool with a geometry suitable for metal cutting, a coating suitable for metal cutting, at least one hard material phase and a single- or multi-phase Binder phase characterized in that the proportion of the elements iron (Fe), cobalt (Co) and nickel (Ni) in the total amount of these elements in the binder phase for Co between 0 and 40 wt .-%, preferably from 5 to 40 wt. %, Fe between 20 and 90 wt .-% and for Ni between 5 and 75 wt .-%, wherein the proportions add up to 100%.
  • Hard metal tool according to item 1 characterized in that the binder phase is alloyed as a result of sintering with tungsten to a content that neither eta phases nor carbon precipitations are included.
  • carbide tool according to item 1 or 2 characterized in that the binder phase is alloyed to the maximum extent as a result of sintering with Cr and / or Mo, that no eta-phase occurs.
  • a cemented carbide tool according to one or more of items 1 to 3, wherein the cobalt content is less than 5%, and is alloyed with molybdenum at most to the solubility limit, wherein the molybdenum content is generated by introducing its metal, nitride or oxide.
  • a cemented carbide tool according to one or more of the items 1 to 4, wherein the binder phase contains one, two or three phases in the mixture selected from austenitic phase, martensitic phase and tetragonal distorted martensitic phase.
  • a cemented carbide tool according to one or more of the items 1 to 5, wherein the binder phase additionally contains 5 to 30 wt .-% chromium and the sum of the percentages of the metals Co, Ni, Cr and Fe is less than or equal to 100 wt .-%.
  • carbide tool according to one or more of the items 1 to 6, wherein the binder phase additionally contains up to 5 percent by mass V, Mo and / or Al and / or Ti 1 W, Ta / Nb, Zr and / or Hf in each case in one part less than or equal to the solubility limit of the respective substance and / or up to 15 mass% Mn.
  • the content of carbon in the binder phase is set so that no precipitates of unbound carbon are present.
  • Hard metal tool according to one or more of the items 1 to 9, wherein the coating comprises or consists of at least one refractory metal nitride, boron nitride, diamond, oxide, sulfides or mixtures thereof.
  • cemented carbide tool according to one or more of items 1 to 10, wherein the coating comprises or consists of titanium nitride, titanium aluminum nitride TiAIN, TiCN, aluminum oxide, TiTaNbC, tungsten carbon or mixtures thereof.
  • the coating has a layer sequence TiN / TiCN / Al 2 O 3 / TiN or TiN / TiCN / Al 2 O 3 / TiN.
  • the thickness of the coating is between 0.5 ⁇ m and 100 ⁇ m, preferably between 1 ⁇ m and 50 ⁇ m, advantageously between 2 ⁇ m and 20 ⁇ m, in particular 3 ⁇ m and 10 ⁇ m
  • the mean grain size of the hard material phase is between 0.1 and 10 ⁇ m, preferably between 0.2 and 7 ⁇ m, in particular between 0.3 and 4 ⁇ m or 0.5 to 4 ⁇ m or 1 to 3 ⁇ m.
  • Hard metal tool according to one or more of the items 1 to 17, wherein the hard material phase tungsten carbide or their mixed crystals.
  • Hard metal tool according to item 18 wherein additionally at least one further cubic carbide phase or mixed carbide phase is contained and the proportion of cubic carbide phase can be up to 30% by weight.
  • a method for producing a cemented carbide tool according to one or more of items 1 to 19, comprising the steps of: providing a binder metal powder of the composition according to one or more of the preceding claims; Providing a hard material powder; - mixing hard material and binder metal powder to obtain a first mixture; Pressing the first mixture into a blank; -Sintering the blank to sintering -if possibly mechanical post-processing of the sintering-applying the coating according to one or more of the preceding claims.
  • the metal workpiece is a workpiece made of steels, cast iron, stainless steels and non-ferrous base alloys such as superalloys, aluminum, brass, titanium, or plastics, fiber composites.
  • the cemented carbide tool according to the present invention therefore has the following features: 1) a coating, [0019] and [0020] 2) a) an austenitic at room temperature at least proportionally
  • FeCoNi-based binder phase with 5 to 40% Co, 90 to 20% Fe, Ni min. 5% to max. 75% (regardless of the other components of the Binders the sum is always to be expected 100%), in addition also W and / or C as a result of sintering as a binder for cemented carbides, possibly also Cr and / or Mo when using corresponding carbide, nitride or metal powders containing
  • the claimed range for cobalt is a compromise between the rising above 40% inhalation toxicity of the powdery binder alloy in contact with WC on the one hand, and the decreasing cobalt content solubility of tungsten in the binder on the other. Below 5% cobalt, the tungsten solubility becomes too small to have to be replaced by the more soluble molybdenum, but this does not take the form of carbide molybdenum compounds, which undesirably mix carbides with e.g.
  • Hard metal tool according to the present invention have a defined geometry, whose task is, for example, to force fit the tool in a cutting forces receiving tool holder, create the chip and selectively break, and the resulting heat as possible with the expiring span dissipate.
  • Suitable are conventional geometries of so-called indexable inserts. These often have a basic geometry derived from a cuboid or plate, often with a hole in the middle, and one or more cutting edges with a purposefully made fillet, such as four-hexagonal or octagonal platelets.
  • Other cutting tools, such as for cutting are self-retaining thanks to their geometry and have only one cutting edge. Often the surface indicates also nubs or reliefs to minimize the contact surface of the chip with the cutting tool.
  • the binder alloy may be both austenitic (face-centered cubic) and martensitic (body-centered cubic, possibly distorted tetragonal) as well as the mentioned two or three phases contained in the mixture.
  • austenitic face-centered cubic
  • martensitic body-centered cubic, possibly distorted tetragonal
  • a high proportion of austenite is preferred because of the good thermal behavior of the temperature, which can be adjusted by the ratio of the components Fe, Co and Ni in the binder phase.
  • the hard metal tool consists of a hard metal or cermet cutting material for machining metal workpieces (such as steels, cast irons, stainless steels, and nonferrous base alloys such as superalloys) with a hard material phase containing carbides, nitrides, and / or carbonitrides Binder phase of iron, cobalt and nickel, which contains 5 to 40% cobalt, 90-20% iron and 5 to 75% nickel, wherein the proportions add up to 100%, and a coating.
  • a hard metal or cermet cutting material for machining metal workpieces such as steels, cast irons, stainless steels, and nonferrous base alloys such as superalloys
  • Binder phase of iron, cobalt and nickel which contains 5 to 40% cobalt, 90-20% iron and 5 to 75% nickel, wherein the proportions add up to 100%, and a coating.
  • the amount of binder phase present in the cemented carbide tool is from 3 to 40% by weight, advantageously from 5 to 20% by weight, and the hard material phase, both phases being complementary to 100% by weight.
  • the hard material phase both phases being complementary to 100% by weight.
  • diamond, intermetallic phases or an oxide reinforcement may be present.
  • the invention further relates to the use of the hard metal tool for the machining machining of metal workpieces.
  • the binder serves to form a liquid phase at sintering temperature which can be in equilibrium with and wet the hard material phase.
  • the liquid binder phase should have a considerable solubility for the hard material phase with the sintering temperature, but should excrete it on cooling again.
  • the binder phase should have mechanical properties which correspond to the intended use and the prevailing temperatures in such a way that the binder for a hard and tough as possible cohesion of the hard metal or cermet body leads.
  • machining operations such as turning, milling or drilling steel grades, especially austenitic steels
  • a gluing of the hard metal or cermet cutting material with the steel workpiece is often noted despite suitable geometry, which is due to the resulting increased wear of the cutting tool and the poor quality machining on the workpiece is undesirable.
  • the binder phase has 0 mass% to 40 mass% Co, 5 mass% to 75 mass% Ni, 20 mass% to 90 mass% Fe.
  • the binder phase may also contain 5 mass% to 30 mass% Cr, wherein the sum of the metals Co, Ni, Cr and Fe does not exceed 100%.
  • cobalt-free binder metals cobalt can occur as an inevitable impurity.
  • the binder phase may additionally contain up to 5 mass% V, Mo and / or Al, up to the solubility limit Ti, W, Ta / Nb, Zr and / or Hf and up to 15 mass% Mn.
  • oxygen, nitrogen and / or boron can be present in the binder to the maximum solubility.
  • the content of carbon in the cutting material is adjusted so that at best traces of eta phases and no precipitations of unbound carbon are present.
  • the binder phase has no hexagonal proportions.
  • the binder phase in the tool according to the invention is obtained by using a binder metal powder having the desired composition for producing the tool.
  • the binder metal powder used to make the tool can be obtained by conventional methods such as mixing the elemental powders of the metals in the binder metal powder or by atomizing a molten alloy of the desired composition.
  • Particularly suitable for this purpose are prealloyed powders which can be obtained in the desired composition by precipitation of metal salt solutions in suitable precipitants and subsequent reduction, as for example in WO 97/21844, US Pat. No. 5,102,454, US Pat. No. 5,912,399, WO 00/23 631, EP1079950 described.
  • pre-alloyed alloy powders may be used in admixture with elemental powders as binder metal powder, as described in WO2008 / 034903.
  • the hard material phase it is possible to use generally known carbides, nitrides and / or carbonitrides, preferably those of the refractory metals, and mixtures thereof and mixed crystals with cubic carbides, for example TiTaNbC. Tungsten carbide is particularly advantageous here.
  • the hard material phase is generally used in the form of powders.
  • the average particle sizes (according to ASTM-B-330, FSSS) of the hard powder used are usually about 0.3 ⁇ m to 10 ⁇ m, advantageously 0.4 ⁇ m to 7 ⁇ m or 0.5 ⁇ m to 4 ⁇ m.
  • the hard material powders used have BET surface areas of generally less than 0.1 m 2 / g to 4 m 2 / g.
  • hard material powder with BET surface areas of 0.1 m 2 / g to 8 m 2 / g, advantageously from 0.2 m 2 / g to 6 m 2 / g, in particular from 0.25 r ⁇ v7g to 4.5 m 2 / g, or from 0.3 m 2 / g to 4 m 2 / g or 5 r ⁇ v7g be used.
  • tungsten carbide powder having a mean grain size of 1 ⁇ m mixed with a tungsten carbide powder having a mean grain size of 5 ⁇ m e.g. a tungsten carbide powder having a mean grain size of 1 ⁇ m mixed with a tungsten carbide powder having a mean grain size of 5 ⁇ m.
  • a mixture of tungsten carbide (WC) and tungsten carbide (W2C) is used as the hard material phase.
  • the mixture can be present as a powder mixture or as a mixture of both substances within the powder particles.
  • hard material powder in particular tungsten carbide, with BET surface areas of 1 nfVg to 8 m 2 / g, advantageously from 2 m 2 / g to 6 m 2 / g, in particular from 2.5 m 2 / g to 4.5 m 2 / g, or from 3 nrVg to 4 m 2 / g or 5 m 2 / g.
  • the coating consists of a refractory metal nitride, boron nitride,
  • Titanium nitride TiN titanium aluminum nitride TiAIN 1 TiCN, TiAISiN, TiTaNbC 1 MoS2, or mixtures thereof.
  • some metastable or amorphous coatings are suitable, such as TiAIN or tungsten / carbon.
  • multilayer coatings are also possible which contain different layer thicknesses and coating materials.
  • Possible layer sequences are e.g. For example, TiN / TiCN / AbOa / TiN, TiN / TiCN / AbOs / TiN.
  • Usual thicknesses of the coating are between a few microns and several 100 microns.
  • the total thickness of the coatings is usually from 1 .mu.m to 50 .mu.m, advantageously from 2 .mu.m to 20 .mu.m and in particular from 3 .mu.m to 10 .mu.m.
  • CVD chemical vapor deposition
  • PVD physical vapor deposition
  • the cemented carbide substrate is modified superficially or near the surface in the composition before application of the coating by sintering or subsequent treatments in such a way that the layer adhesion is optimal.
  • the coating is generally adapted very specifically to the material to be machined and to the hard metal.
  • the coating is under compressive stress; Tensile stresses often cause tearing and flaking.
  • cemented carbide tools according to the invention find use for machining metal workpieces or non-metal workpieces.
  • chromium-containing metal workpieces wherein the proportion of chromium in the binder phase of the cutting material, ie the material from which the hard metal tool according to the invention consists, is not greater than the chromium content in the steel alloy of the workpiece.
  • it may be a workpiece made of steels, cast iron,
  • Non-metallic materials may also be processed, such as fiber composites or thermoplastic or thermosetting plastics, which may also be reinforced with fibers such as glass or carbon fibers, fillers or other reinforcing agents, such as glass fibers. Nanocomposites.
  • the present invention also relates to a method for producing a cemented carbide tool according to one or more of the preceding claims, comprising the steps:
  • the binder metal powder may be provided by preparing a pre-alloyed metal powder of the desired composition described in WO 97/21844, US 5,102,454, US 5,912,399, WO 00/23 631, EP1079950, to which reference is made.
  • the binding metal powder can be provided by mixing a prealloyed metal powder with one or more elemental powders, ie metal powders which consist only of a metal as described in WO2008 / 034903, to which reference is made.
  • the hard material powder advantageously has a mean particle size of 0.3 to 10 .mu.m, preferably 0.5 to 7 .mu.m, in particular 1 to 4 microns.
  • the hard material powder has a BET surface area of 0.1 m 2 / g to 8 m 2 / g, advantageously from 0.2 m 2 / g to 6 m 2 / g or 0.1 m 2 / g to 4 m 2 / g, in particular from 0.25 m 2 / g to 4.5 m 2 / g, or from 0.3 m 2 / g to 4 m 2 / g or 5 m 2 / g.
  • hard material tungsten carbide tungsten carbide or a mixture of these substances can be used advantageously.
  • the first mixture may also contain pressing or sintering aids, such as waxes, long-chain carboxylic acids, their esters or salts, or polymers such as polyethylene glycol or polyacrylates.
  • pressing or sintering aids such as waxes, long-chain carboxylic acids, their esters or salts, or polymers such as polyethylene glycol or polyacrylates.
  • the compression to a blank is usually designed as uniaxial pressing and generally carried out at pressures of 50-250 MPa.
  • the sintering takes place usually at temperatures of about 1200 0 C to 1600 0 C, in particular 1250 0 C to 1550 0 C in an inert atmosphere or in vacuo instead.
  • a hard metal powder mixture consisting of 94 wt.% WC with a
  • the carbon content of the mixture was adjusted so that the cemented carbide does not contain any harmful third phases such as free carbon or carbon deficit phases ("eta phases") after sintering
  • Hard metal carbide inserts with a geometry according to CNMG120408 were made by axial dry pressing a compression was produced and then vacuum sintered in a graphite sintering furnace for one hour at 1450 ° C.
  • the metallographic examination of the carbide semi-finished products showed that the cemented carbide had a uniform microstructure with a WC particle size of about 0.6 microns good and very few coarse grains of coarse grains up to a grain size of 3 microns were seen was 1920 kg / mm 2 (Vickers hardness at 10 kg load, "HV10")
  • the X-ray examination showed that the binder consists mainly of martensite and some retained austenite.
  • the hard metal insert blanks were ground to size, the
  • Comparative Example 1 The service life of a conventional WC-Co cemented carbide of the same geometry, the same coating and the same composition, but purely cobalt-bound, was 5 minutes in comparison, while with the WC-70Fe12Co18Ni cemented carbide in Example 1 a service life of 6 Minutes under the same cutting conditions.
  • the criterion for the end of service life was a wear mark width ("VBmax.") Of 0.2 mm.
  • a hard metal powder mixture consisting of 94 wt.% WC with a
  • Reversible inserts of the same composition exhibited a life of 6 minutes in uncoated form with the WC-50Fe25Co25Ni PVD coated insert showing a life of 8.5 minutes and the CVD coated insert with the same substrate exhibiting a life of 8.0 minutes.
  • Criterion for the end of life was a wear mark width VBmax of 0.2 mm.
  • the lower service life of the WC-Co insert was due to a higher plastic deformation of the cutting edge and a correspondingly poorer surface finish of the workpiece.
  • a hard metal powder mixture consisting of 83.5 wt.% WC with a particle size of 1, 1 .mu.m, a mixed carbide consisting of TiTaNbC of 8% and a binder content of 8.5 wt% consisting of 70Fe12Co18Ni present as mixed crystal was prepared by wet milling in produced an attritor and processed into granules in a conventional spray dryer. The carbon content of the mixture was adjusted so that the cemented carbide does not contain any harmful third phases such as free carbon or etaphases after sintering.
  • the hard metal insert blanks were ground to size, the cutting edges rounded and then provided with a conventional CVD multilayer coating based on TiN / TiCN / Al2O3 / TiN with a total layer thickness of 8 microns. Standstill tests were when turning without coolant insert with a cutting speed of 200 m / min, feed 0.32 mm / rev, cutting depth 2 mm in a 42CrMo4 low alloy steel.
  • the conventional cobalt-bonded cemented carbide tool showed a pronounced plastic deformation of the cutting edge at the end of its life, while the FeCoNi-bonded cemented carbide tool showed only a few crevice and flank wear.
  • the coating showed signs of wear but was still intact. There were no signs of adhesive wear.

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  • Physics & Mathematics (AREA)
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  • Cutting Tools, Boring Holders, And Turrets (AREA)
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Abstract

La présente invention se rapporte à un outil revêtu, servant à l'usinage de métaux par enlèvement de copeaux, présentant une usure par adhésion réduite ainsi qu'une résistance à la chaleur renforcée.
EP08758755A 2007-10-02 2008-05-26 Outil Withdrawn EP2195473A1 (fr)

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PL2527480T3 (pl) * 2011-05-27 2017-12-29 H.C. Starck Gmbh Spoiwo NiFe o uniwersalnym zastosowaniu
TWI521090B (zh) * 2012-04-16 2016-02-11 財團法人工業技術研究院 複合刀具
CN103790520B (zh) * 2012-11-02 2018-03-20 喜利得股份公司 钻头和用于钻头的制造方法
CN103526101A (zh) * 2013-09-27 2014-01-22 无锡阳工机械制造有限公司 一种金属切削刀具及其制备方法
DE102018111101A1 (de) * 2018-05-09 2019-11-14 Tribo Hartstoff Gmbh Werkstück aus einem Hartmetallwerkstoff und Verfahren zu dessen Herstellung
CN112313354B (zh) * 2018-06-29 2022-05-10 山特维克科洛曼特公司 具有替代性粘结剂的硬质合金
CN109371306A (zh) * 2018-12-15 2019-02-22 宇龙精机科技（浙江）有限公司 一种五轴联动加工的机床
AT522605B1 (de) * 2019-05-23 2021-02-15 Boehlerit Gmbh & Co Kg Hartmetalleinsatz
JP7410383B2 (ja) * 2019-12-27 2024-01-10 株式会社Moldino 被覆切削工具

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5102454A (en) * 1988-01-04 1992-04-07 Gte Products Corporation Hydrometallurgical process for producing irregular shaped powders with readily oxidizable alloying elements
JPH0215159A (ja) * 1988-07-01 1990-01-18 Mitsubishi Metal Corp 表面被覆サーメット製切削工具の製造法
US5328763A (en) * 1993-02-03 1994-07-12 Kennametal Inc. Spray powder for hardfacing and part with hardfacing
US5912399A (en) * 1995-11-15 1999-06-15 Materials Modification Inc. Chemical synthesis of refractory metal based composite powders
AU8890498A (en) * 1997-08-26 1999-03-16 Microscreen B.V. Rapid detection and identification of micro-organisms
US6010283A (en) 1997-08-27 2000-01-04 Kennametal Inc. Cutting insert of a cermet having a Co-Ni-Fe-binder
DE19822663A1 (de) * 1998-05-20 1999-12-02 Starck H C Gmbh Co Kg Sinteraktive Metall- und Legierungspulver für pulvermetallurgische Anwendungen und Verfahren zu deren Herstellung und deren Verwendung
US6214247B1 (en) * 1998-06-10 2001-04-10 Tdy Industries, Inc. Substrate treatment method
FR2784691B1 (fr) * 1998-10-16 2000-12-29 Eurotungstene Poudres Poudre metallique prealliee micronique a base de metaux de transition 3d
SE521488C2 (sv) * 2000-12-22 2003-11-04 Seco Tools Ab Belagt skär med järn-nickel-baserad bindefas
DE10213963A1 (de) * 2002-03-28 2003-10-09 Widia Gmbh Hartmetall- oder Cermet-Schneidwerkstoff sowie Verfahren zur zerspanenden Bearbeitung von Cr-haltigen Metallwerkstücken
DE102006045339B3 (de) * 2006-09-22 2008-04-03 H.C. Starck Gmbh Metallpulver

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO2009046777A1 *

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CN101809203A (zh) 2010-08-18
WO2009046777A1 (fr) 2009-04-16
US20100239855A1 (en) 2010-09-23
DE102007047312A1 (de) 2009-04-09
WO2009046777A8 (fr) 2009-07-23
KR20100074140A (ko) 2010-07-01

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