EP2527480B1 - Liant NiFe ayant une application universelle - Google Patents

Liant NiFe ayant une application universelle Download PDF

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Publication number
EP2527480B1
EP2527480B1 EP11167901.5A EP11167901A EP2527480B1 EP 2527480 B1 EP2527480 B1 EP 2527480B1 EP 11167901 A EP11167901 A EP 11167901A EP 2527480 B1 EP2527480 B1 EP 2527480B1
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EP
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Prior art keywords
weight
binder alloy
alloy
hardness
base
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EP11167901.5A
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German (de)
English (en)
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EP2527480A1 (fr
Inventor
Dr. Benno Gries
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Hoganas Germany GmbH
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HC Starck GmbH
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Application filed by HC Starck GmbH filed Critical HC Starck GmbH
Priority to ES11167901.5T priority Critical patent/ES2628422T3/es
Priority to EP11167901.5A priority patent/EP2527480B1/fr
Priority to PL11167901T priority patent/PL2527480T3/pl
Priority to RU2013158048A priority patent/RU2623545C2/ru
Priority to PCT/EP2012/059748 priority patent/WO2012163804A1/fr
Priority to US14/122,246 priority patent/US9821372B2/en
Priority to CN201280025581.3A priority patent/CN103562422B/zh
Priority to KR1020137032074A priority patent/KR102079325B1/ko
Priority to JP2014513132A priority patent/JP6124877B2/ja
Publication of EP2527480A1 publication Critical patent/EP2527480A1/fr
Priority to IL229654A priority patent/IL229654B/en
Publication of EP2527480B1 publication Critical patent/EP2527480B1/fr
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Priority to US15/730,747 priority patent/US11207730B2/en
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    • 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
    • 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
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
    • B22F1/105—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material containing inorganic lubricating or binding agents, e.g. metal salts
    • 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
    • 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
    • C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides 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
    • 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
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel

Definitions

  • the invention relates to a process for producing a composite material obtainable by sintering a composition containing a hard carrier and a FeCoNi or FeNi based base binder alloy. Moreover, the invention relates to a sintered composite material, which is obtainable according to the method and its use for tools or components, in particular forming or comminution tools.
  • Cemented carbide is a sintered composite of hardeners, such as carbides and a binder alloy.
  • Carbides are used in many different ways and are used, for example, for processing practically all known materials. Carbides may also be used, for example, as a structural component, as a forming or comminution tool or for a variety of other purposes, where it depends particularly on wear resistance, mechanical strength or high temperature resistance.
  • a common field of application is the cutting of metallic materials. Due to machining, forming and friction processes locally limited temperatures up to 800 ° C. In other cases, forming operations of metallic workpieces are performed at high temperatures, such as forging, wire drawing or rolling. The tool is under mechanical stress, which can lead to deformation of the carbide tool.
  • high-temperature creep resistance in practice, the hot hardness is usually determined as a substitute
  • the fracture toughness K 1 C
  • the wear resistance, the hot hardness, the fracture toughness and the related strength can be adjusted by the size of the carbide phase and its proportion of the hard metal composition.
  • the present invention relates to novel hard metals having a FeNi or FeCoNibas striving binder alloy, which in hardness (Vickers hardness according to ISO 3878), fracture toughness (K 1 C, calculated according to the formal of Shetty from the crack lengths and the size of the Vickershärteeindrucks) and hot hardness the properties of those hitherto conventional hard metals correspond to a Co-based binder alloy.
  • base alloy instead of cobalt as the base alloy, other base alloys are used in special hard metals.
  • base binder alloying is meant also pure metals with inevitable impurities, e.g. available as commercially available nickel and cobalt metal powders.
  • Ni metal powders are used as a base alloy for the production of corrosion-resistant, oxidation-resistant or non-magnetisable hard metals.
  • the sintering in the liquid phase leads to the formation of a binding alloy based on Ni.
  • This binder alloy contains elements such as W, Co, Cr, Mo, or others added to the hard metal batch as a metal powder or carbide, for example, and their contents in the pure Ni by alloying in the liquid phase sintering to the resulting Ni-base alloy. These elements lead to a better corrosion resistance compared to pure nickel.
  • Hard metals with Ni as a binder-based alloy are not universally used because of their low hardness values compared to those bound with Co-base alloys.
  • hard metals bonded with Ni-base alloys are characterized by comparatively low thermal hardness. Therefore, they are not used in the machining of metallic materials.
  • FeCoNi-based alloys are known as carbide binders.
  • their disadvantages are their low K 1 C values, which is proportional to the strength according to the Griffith equation up to binder contents of about 12% by weight.
  • the K 1 C values of a hard metal are based on tungsten carbide (average powder diameter: 0.6 ⁇ m) with 7.5% FeCoNi 40/20/40 at values between 8.2 and 9.5 MPa m 1/2 while a cemented carbide having the same volume fraction of cobalt (corresponding to 8 wt% due to the higher density of cobalt compared to FeCoNi 40/20/40) reaches a K 1 C of 9.5 MPa m 1/2 .
  • the hot curing of hard metals with FeCoNi base alloys as binders are usually lower at higher temperatures than those bound with cobalt base alloys.
  • FeNi-based alloys are also known as binders.
  • WO-A1-2002 / 0112896 describes FeNi alloys based on 35 to 65% Ni and 65 to 35% Fe.
  • the strength of the described base alloy FeNi 50/50 at room temperature, however, is comparatively low;
  • a carbide with 7.4% FeNi 50/50 volume fraction of the binder corresponding to 8 wt .-% cobalt due to the lower density of FeNi 50/50
  • hard metals are with a FeNi 50/50 base alloy having a tungsten solubility in the binder alloy of at most 19.4% equivalent to a cobalt base alloy (maximum 20% W in the binder alloy) in terms of the thermal hardness.
  • tungsten carbides with Ni-base alloys are inferior to both of the above with respect to the hot hardness, and therefore are not used for applications where it comes to high hot hardness such as in metal cutting.
  • EP-B1-1 488 020 FeCoNi base alloys with 10 to 75% _Co are known as fcc-structured carbide binders for special machining tasks designed to reduce the adhesive wear that occurs when machining special steels.
  • the hot curing of such hard metals with austenitic FeCoNi base alloys are clearly inferior to those with cobalt-based alloys. It is also believed that, in addition, the strength values of hard metals from these austenitic binder alloys will be lower compared to those hard metals bonded with a cobalt-based alloy.
  • WO-A2-2010 / 046224 describes the use of molybdenum-doped FeCoNi-, Co-, Ni- and Ni-based powdered metal powders alloyed with molybdenum.
  • the hot curing of a WC and 8% Co is not quite reached with 82% of the maximum magnetic saturation ( FIG. 2 of the WO-A2-2010 / 046224 ).
  • the K 1 C is very much dependent on the carbon content of the cemented carbide (Example 4 of the WO-A2-2010 / 046224 ), which tends to fluctuate in industrial sintering practice.
  • the safe achievement of the required properties hardness, K 1 C and hot hardness sensitive depends on the control of the carbon balance, which is not always ensured under industrial conditions.
  • cemented carbide lung In the current production of cemented carbide via powder metallurgical production processes, i. Pressing and sintering of powdered tungsten carbide formulations releases respirable dusts due to the process. If grinding is used in the sintered or pre-sintered state of the hard metal, very fine, breathable dusts (grinding dusts) are also produced.
  • an acute inhalation toxicity may additionally occur during the grinding of pre-sintered hard metals or also sintered hard metals.
  • An object of the present invention was therefore to improve the safety of work, hard metals, i. To provide sintered composites that have a reduced acute toxic effect.
  • base binder alloys comprising 66 to 90% by weight, preferably 70 to 90% by weight of nickel.
  • Base binder alloys having 10 to 34 wt% iron are preferred. Particularly preferred is an iron content in the base binder alloy of 10 to 30 wt .-%.
  • Essentially free in the sense of the present invention means that the element in an amount of less than 0.5 wt .-%, preferably less than 0.1 wt .-%, more preferably less than 0.08 wt .-% and in particular less than 0.02 wt .-% and in particular less than 0.001 wt .-%, for example less than 0.005 wt .-%, each based on the total weight of the base binder alloy, is present.
  • the base binder alloy contains less than 0.1% by weight, preferably less than 0.08% by weight, in particular less than 0.02% by weight, in particular less than 0.01 Wt .-% molybdenum.
  • the hardness carrier is selected from the group consisting of carbides, nitrides, borides and carbonitrides. These particularly preferably contain one or more elements of the 4th, 5th or 6th subgroup of the periodic table.
  • He comprises at least 50% by weight of the binary hardener tungsten carbide, based on the total weight of the hardness carriers, and may also contain further hardeners, such as ternary hardeners, such as tantalum-niobium mixed carbide, titanium carbonitride or tungsten-titanium carbide or even quaternary, such as tungsten-titanium-carbonitride or tungsten-titanium-niobium-tantalum carbide.
  • ternary hardeners such as tantalum-niobium mixed carbide, titanium carbonitride or tungsten-titanium carbide or even quaternary, such as tungsten-titanium-carbonitride or tungsten-titanium-niobium-tantalum carbide.
  • the hardness carriers are preferably in powder form.
  • the powders have an average particle diameter of 0.01 to 150, preferably 0.1 to 100 microns.
  • the average particle diameter is determined according to ASTM B330.
  • the hardness carriers preferably have a hardness above 800 kg / mm 2 , in particular above 1000 kg / mm 2 (measured in accordance with ISO 6507, Part 2).
  • compositions used in the process according to the invention may optionally also contain other components as additives, such as metals, for example selected from the group consisting of rhenium, molybdenum, chromium and aluminum.
  • additives such as metals, for example selected from the group consisting of rhenium, molybdenum, chromium and aluminum.
  • elemental tungsten or elemental carbon may be preferably used since it is suitable for correcting the carbon content of the composite after sintering.
  • intermetallic compounds such as Ni 3 Al or chromium nitride decomposing during sintering can also be added to the compositions to be sintered.
  • additives may constitute up to 20% by weight, preferably up to 10% by weight, the weight data being based on the total weight of the composition.
  • the composition contains 3 to 50 wt .-% of the base binder alloy, preferably 4 to 40 wt .-%, in particular 4 to 30 wt .-% of the base binder alloy, each based on the total weight of the composition.
  • the sintering is preferably carried out at temperatures above 1000 ° C, more preferably above 1100 ° C and in particular at temperatures between 1150 ° C and 1600 ° C.
  • the sintering is in the presence of liquid phase.
  • the base binder alloy is completely or partially present in liquid form during the sintering process.
  • step a) The provision of the dispersion described in step a) is carried out in a preferred embodiment by adding a solvent to a pulverulent composition containing a hardness carrier and base binder alloy powder.
  • Preferred solvents are those which have a boiling point of ⁇ 250 ° C at 1 bar.
  • alcohols in particular aliphatic alcohols, for example ethanol, and water or mixtures thereof, such as mixtures of water and organic Solvents, especially water and alcohols.
  • organic solvents in particular selected from the group consisting of ketones and hydrocarbons, for example acetone and aliphatic hydrocarbons, such as heptane and hexane.
  • the milling of the dispersion prepared in step a) can be carried out using milling tools familiar to the person skilled in the art.
  • the milling of the dispersion is carried out in a ball mill or an attritor, which are particularly preferably equipped with hard metal balls.
  • the dispersion may optionally additionally contain organic auxiliaries, such as waxes, dispersion aids, inhibitors, adhesives or emulsifiers, before the drying step.
  • organic auxiliaries such as waxes, dispersion aids, inhibitors, adhesives or emulsifiers
  • step b) is followed by preparing a powder by drying the dispersion.
  • the dispersion may, for example, be spray-dried or dried under reduced pressure.
  • the solvent low-boiling solvent which can be easily distilled off under reduced pressure.
  • the dried powder from step c) is used to produce compacts or extrudates.
  • the pressing of the dried powder is preferably carried out in suitable tools, or isostatically.
  • step e) the compact or the extrudate is sintered.
  • the sintering is carried out in the presence of a protective gas atmosphere or under reduced pressure.
  • the sintered composites are further densified at elevated pressure in a separate or integrated post-densification step.
  • the pressing and the sintering are carried out simultaneously and preferably by additional application of electric fields or currents. These can provide an elevated temperature during sintering and compression.
  • the composite materials obtained according to the method according to the invention are optionally subsequently ground to the required shape, with tools for metal cutting usually by means of chemical vapor deposition techniques (CVD) or physical vapor deposition (PVD) or combined methods can be further coated.
  • CVD chemical vapor deposition techniques
  • PVD physical vapor deposition
  • the composite materials according to the invention include as binder alloy one or more elements of the group Fe, Ni and optionally Co.
  • the base alloy may already contain such elements. However, the final composition of the binder alloy does not become established until sintering and subsequent cooling of the cemented carbide.
  • the binder alloy may also contain one or more elements selected from the group consisting of W, Mo, Cr, V, Ta, Nb, Ti, Zr, Hf, Re, Ru, Al, Mn, C.
  • These elements have limited solubility both in the FeNi base alloy as well as in other base alloys, and their contents are adjusted during sintering and cooling due to their temperature-dependent solubility in addition to the carbon content according to the principle of solubility of the carbides depending on their thermodynamic stability.
  • the sum of these elements in the binder alloy according to the invention is therefore generally less than 30 wt .-%, based on the total weight of the binder alloy of the sintered composite material.
  • the binder alloy of the sintered composite of the invention comprises up to 30% by weight of one or more elements selected from the group consisting of W, Mo, Cr, V, Ta, Nb, Ti, Zr, Hf, Re, Ru , Al, Mn, B, N and C.
  • the selection and contents of the above elements have an influence on the properties of the binder alloy.
  • W, Cr and Mo increase the hot hardness due to their solubilities on the order of not more than 5 to 25% by weight. Therefore, it is desirable in industrial practice to set the carbon of the cemented carbide so low that the contents of these elements in the binder alloy are as high as possible without causing harmful carbon deficiency phases (so-called eta phases).
  • the actual dissolved tungsten content in hard metals with Co base alloys is determined by the magnetic saturation. If the magnetic saturation of the Co content of pure WCCo hard metals is less than 70% that of pure cobalt, eta phases are formed. For industrial reasons, however, a safety margin is kept to this limit for reasons of process safety.
  • carbide parts may also be in a preferred manner but also carbide parts further and arbitrary geometry and application, such as forging tools, forming tools, countersinks, components, knives, peeling plates, rollers, stamping tools, pentagonal drill bits for soldering, mining chisel, milling tools for milling processing of concrete and asphalt , Mechanical seals and any other geometry and application.
  • the sintered composite material according to the invention can be used for forming or comminution tools.
  • the tool is a tool for cutting metallic tools or for forming metallic workpieces at high temperatures, for example a tool for forging, wire drawing or rolling.
  • the ethanol was separated by distillation in vacuo, and pressed the obtained hard metal powder axially at 150 MPa and sintered at 1420 ° C.
  • the plate-shaped hard metal pieces were ground, polished and examined for their properties. Both batches showed no eta phases or carbon precipitates as sinters.
  • the different carbon content after sintering and the consequent different tungsten content in the binder metal alloy is the result of mass transfer during sintering.
  • the binder metal alloy in the base is cobalt, with proportions of tungsten and possibly carbon.
  • the hot hardnesses were determined as before (see results FIG. 1 ).
  • new sintered bodies were made from the existing hard metal approaches.
  • a density of 14.81 g / cm 3 and a magnetic saturation of 54 to 55 Gcm 3 / g was achieved with the "low carbon” variant.
  • Densities between 14.77 and 14.79 g / m 3 and magnetic saturations between 70.5 and 72.5 Gcm 3 / g were achieved with the "high carbon” variant.
  • the limit for the eta phase is below 51 Gcm 3 / g, the limit for carbon excretion at about 75 Gcm 3 / g.
  • the sintered pieces were thus free from eta-phase and carbon precipitations.
  • the two sinter batches were in the middle and in the high, but not in the low range for the carbon content, which would have been conducive to a high hot hardness.
  • the resulting cemented carbides containing neither eta phase nor carbon precipitates had an HV30 between 1626 and 1648.
  • the K 1 C values were for the most part between 8.5 and 8.9 MPa m 1/2 . Only in a very narrow range with high carbon contents at the boundary to the area of carbon precipitation, values of 9.3 to 9.5 for the K 1 C were found.
  • hard metals with a FeCoNi 40/20 / 40A base binding in terms of K 1 C and hot hardness are inferior to those which are bound with cobalt as a base for the binder alloy.
  • carbides with a FeNi 50/50 based alloy have at least equal hot hardness, but show comparatively low K 1 C values, which means carbides bonded in this way can not be used universally ( Fig. 3 ).
  • carbides with this binder-based alloy can be used for turning metal, but not for milling because of their low K 1 C value, since the mechanical shock resistance is insufficient.
  • Table 3 Fe / Ni ratio HV30 K1C density Magnetic saturation (kg / mm 2 ) (MPa m 1/2 ) (g / cm 3 ) (G cm 3 / g) 35/65 * 1618 9.2 14.75 102 25/75 * 1626 9.3 14.67 94.7 15/85 * 1608 9.4 14,74 98.4 10/90 * 1618 11.3 14.84 42.3 5/95 1541 10.7 14.79 38.2 0/100 1478 12.4 14.81 42.7
  • FIGS 2 and 3 illustrate the results of Example 4 and Examples 1 and 4 in comparison.
  • the hardness barely drops from 50% Ni to unexpectedly high Ni contents of 90%.
  • the course of the hardness is surprisingly almost constant up to values of 90% Ni, then drop off abruptly. It can be interpolated that the required hardness level, which results from the lower hardness value of Comparative Example 1, is achieved at Ni contents of up to 93%.

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Claims (15)

  1. Procédé de fabrication d'un matériau composite comprenant la préparation d'une composition contenant :
    a) 50 à 97 % en poids d'au moins un élément d'alliage favorisant la dureté, comprenant au moins 50 % en poids de carbure de tungstène, par rapport au poids total de l'élément d'alliage favorisant la dureté, et
    b) 50 à 3 % en poids d'un alliage liant de base, comprenant :
    α) 66 à 93 % en poids de nickel,
    β) 34 à 7 % en poids de fer, et
    γ) 0 à 9 % en poids de cobalt,
    l'alliage liant de base présentant un rapport en poids fer:nickel de 1:2 à 1:13, et
    la somme des proportions en poids α), β) et γ) de l'alliage liant de base étant de 100 % en poids, et
    c) jusqu'à 30 % en poids d'un ou de plusieurs des éléments choisis dans le groupe constitué par W, Mo, Cr, V, Ta, Nb, Ti, Zr, Hf, Re, Ru, Al, Mn, B, N et C,
    le poids total de l'alliage liant de base, de l'élément d'alliage favorisant la dureté et éventuellement d'additifs présents étant de 100 % en poids,
    et le frittage de cette composition.
  2. Procédé selon la revendication 1, caractérisé en ce que l'alliage liant de base présente un rapport en poids fer:nickel de 1:2,5 à 1:12, de préférence de 1:3 à 1:10, et notamment de 1:3 à 1:9, de manière particulièrement préférée de 1:4 à 1:8, par exemple de 1:4 à 1:7.
  3. Procédé selon la revendication 1 ou 2, caractérisé en ce que l'alliage liant de base comprend 66 à 90 % en poids, de préférence 70 à 90 % en poids de nickel.
  4. Procédé selon au moins l'une quelconque des revendications 1 à 3, caractérisé en ce que l'alliage liant de base contient moins de 8 % en poids de cobalt, de préférence moins de 5 % en poids de cobalt.
  5. Procédé selon au moins l'une quelconque des revendications 1 à 4, caractérisé en ce que l'alliage liant de base comprend moins de 0,1 % en poids de molybdène, de préférence moins de 0,08 % en poids, notamment moins de 0,02 % en poids de molybdène.
  6. Procédé selon au moins l'une quelconque des revendications 1 à 5, caractérisé en ce que l'élément d'alliage favorisant la dureté est choisi dans le groupe constitué par les carbures, les nitrures, les borures et les carbonitrures.
  7. Procédé selon au moins l'une quelconque des revendications 1 à 6, caractérisé en ce que l'élément d'alliage favorisant la dureté comprend un ou plusieurs éléments des groupes de transition 4, 5 et 6 du tableau périodique.
  8. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que l'alliage liant de base se présente sous la forme d'une poudre d'alliage.
  9. Procédé selon au moins l'une quelconque des revendications précédentes, comprenant les étapes suivantes :
    a) la préparation d'une dispersion comprenant une composition contenant un élément d'alliage favorisant la dureté et une poudre d'alliage liant de base dans un solvant,
    b) le broyage de la dispersion,
    c) la fabrication d'une poudre par séchage de la dispersion,
    d) la fabrication de corps comprimés par compression de la poudre ou par extrusion de la poudre à l'aide d'agents plastifiants, et
    e) le frittage du corps comprimé ou de l'extrudeuse.
  10. Matériau composite fritté contenant au moins un élément d'alliage favorisant la dureté et un alliage liant,
    l'élément d'alliage favorisant la dureté comprenant au moins 50 % en poids de carbure de tungstène, par rapport au poids total de l'élément d'alliage favorisant la dureté,
    l'alliage liant étant constitué par :
    les éléments Fe et Ni et éventuellement Co, et
    jusqu'à 30 % en poids d'un ou de plusieurs des éléments choisis dans le groupe constitué par W, Mo, Cr, V, Ta, Nb, Ti, Zr, Hf, Re, Ru, Al, Mn, B, N et C, l'alliage liant pouvant être obtenu à partir d'un alliage liant de base comprenant 66 à 93 % en poids de nickel, 7 à 34 % en poids de fer et 0 à 9 % en poids de cobalt, et présentant un rapport en poids fer:nickel de 1:2 à 1:13.
  11. Matériau composite fritté selon la revendication 10, caractérisé en ce que l'alliage liant de base contient moins de 0,5 % en poids de cobalt.
  12. Matériau composite fritté selon la revendication 10 ou 11, caractérisé en ce que l'alliage liant de base présente un rapport en poids fer:nickel de 1:2,5 à 1:12, de préférence de 1:3 à 1:10, et notamment de 1:3 à 1:9, de manière particulièrement préférée de 1:4 à 1:8, par exemple de 1:4 à 1:7.
  13. Utilisation du matériau composite fritté selon l'une quelconque des revendications 10 à 12 pour des outils ou des composants.
  14. Utilisation selon la revendication 13, caractérisée en ce que les outils sont des outils de déformation ou de broyage.
  15. Utilisation selon la revendication 13 ou 14, caractérisée en ce que l'outil est un outil pour l'usinage d'outils métalliques ou pour la déformation de pièces métalliques à des températures élevées, par exemple un outil pour le forgeage, le tréfilage ou le cylindrage.
EP11167901.5A 2011-05-27 2011-05-27 Liant NiFe ayant une application universelle Active EP2527480B1 (fr)

Priority Applications (11)

Application Number Priority Date Filing Date Title
ES11167901.5T ES2628422T3 (es) 2011-05-27 2011-05-27 Aglutinante de FeNi con aplicabilidad universal
EP11167901.5A EP2527480B1 (fr) 2011-05-27 2011-05-27 Liant NiFe ayant une application universelle
PL11167901T PL2527480T3 (pl) 2011-05-27 2011-05-27 Spoiwo NiFe o uniwersalnym zastosowaniu
CN201280025581.3A CN103562422B (zh) 2011-05-27 2012-05-24 通用型FeNi-粘结剂
PCT/EP2012/059748 WO2012163804A1 (fr) 2011-05-27 2012-05-24 Liants feni ayant une aptitude à la mise en oeuvre universelle
US14/122,246 US9821372B2 (en) 2011-05-27 2012-05-24 FeNi binder having universal usability
RU2013158048A RU2623545C2 (ru) 2011-05-27 2012-05-24 FeNi - СВЯЗУЮЩИЙ АГЕНТ С УНИВЕРСАЛЬНЫМИ ВОЗМОЖНОСТЯМИ ИСПОЛЬЗОВАНИЯ
KR1020137032074A KR102079325B1 (ko) 2011-05-27 2012-05-24 보편적 유용성을 갖는 FeNi 결합제
JP2014513132A JP6124877B2 (ja) 2011-05-27 2012-05-24 汎用性を有するＦｅＮｉバインダー
IL229654A IL229654B (en) 2011-05-27 2013-11-27 A universally useful iron-nickel binder
US15/730,747 US11207730B2 (en) 2011-05-27 2017-10-12 FeNi binder having universal usability

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP11167901.5A EP2527480B1 (fr) 2011-05-27 2011-05-27 Liant NiFe ayant une application universelle

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EP2527480A1 EP2527480A1 (fr) 2012-11-28
EP2527480B1 true EP2527480B1 (fr) 2017-05-03

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EP (1) EP2527480B1 (fr)
JP (1) JP6124877B2 (fr)
KR (1) KR102079325B1 (fr)
CN (1) CN103562422B (fr)
ES (1) ES2628422T3 (fr)
IL (1) IL229654B (fr)
PL (1) PL2527480T3 (fr)
RU (1) RU2623545C2 (fr)
WO (1) WO2012163804A1 (fr)

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CN103562422B (zh) 2016-02-10
CN103562422A (zh) 2014-02-05
US11207730B2 (en) 2021-12-28
JP2014519553A (ja) 2014-08-14
RU2623545C2 (ru) 2017-06-27
ES2628422T3 (es) 2017-08-02
IL229654A0 (en) 2014-01-30
JP6124877B2 (ja) 2017-05-10
US20180029118A1 (en) 2018-02-01
KR20140032414A (ko) 2014-03-14
RU2013158048A (ru) 2015-07-10
KR102079325B1 (ko) 2020-02-19
IL229654B (en) 2018-12-31
EP2527480A1 (fr) 2012-11-28
WO2012163804A1 (fr) 2012-12-06
US20140086782A1 (en) 2014-03-27
US9821372B2 (en) 2017-11-21
PL2527480T3 (pl) 2017-12-29

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