MXPA00000983A - A cermet having a binder with improved plasticity, a method for the manufacture and use therof - Google Patents

Abstract

Cermets having a Co-Ni-Fe-binder, a method for the manufacture and use thereof are described. The Co-Ni-Fe-binder comprises about 40 wt.%to 90 wt.%Co, the remainder consisting of Ni, Fe and incidental impurities. The binder is unique in that even when subjected to plastic deformation, it substantially maintains its face centered cubic crystal structure and avoids stress and/or strain induced phase transformations. Stated differently, the Co-Ni-Fe-binder exhibits reduced work hardening. The cermets are used as tools for mining and construction, for machining materials, and as a screw head punch.

Description

A CERAMETAL THAT HAS AN AGGLUTINANT WITH IMPROVED PLASTICITY, A METHOD FOR THE MANUFACTURE AND USE OF THE SAME.

BACKGROUND Cerametals are composite materials comprised of a hard component, which may or may not be interconnected three-dimensionally, and a binder that binds or binds the hard component. An example of a traditional cerametal is a tungsten carbide (WC) cerametal (WC cermetal), also known as cemented tungsten carbide and WC-Co. Here, the hard component is WC while the binder is cobalt (Co-binder), such as, for example, a cobalt-tungsten-carbon alloy. This Co binder is approximately 98% by weight (% p) of cobalt. The cobalt is the main binder for cerametals. For example, approximately 15% of the world's annual primary cobalt market is used in the manufacture of hard materials including WC cerametals. Approximately 26% of the world's annual cobalt market is used in the manufacture of superalloins developed for advanced aircraft turbine engines - a factor that contributes to cobalt being cataloged as strategic material. Up to approximately 45% of the world's primary cobalt production is located in politically unstable regions. These factors not only contribute to the high cost of cobalt but also explain the erratic fluctuations in the cost of cobalt. Therefore, it would be desirable to reduce the amount of cobalt used as a binder in the cerametals. Prakash et al. They tried to achieve this goal in their work related to WC cerametals by replacing an iron-cobalt-nickel-iron-rich binder (Fe-Co-Ni binder) for the binder of the Co. (See for example, L.J. Prakash, Doctoral Thesis, Kernforschungszentrum Karisruhe, Germany, Institute Fuer Material- und Festkoeperforschung, 1980 and L.J. Prakash et. al., "The Influence Of The Binder Composition On The Properties Of WC-Fe / Co / Ni Cemented Carbides" Mod. Dev. Powder Metal (1981), 14, 225-268). Agree Prakash et. al-, WC-cerametals that have an iron-rich Fe-Co-Ni binder were reinforced by stabilizing a body-centered cubic structure (bcc) in the Fe-Co-Ni binder. This bcc structure was achieved by a martensitic transformation. Although Prakash et al. they focus on iron-rich martensitic binder alloys, reveal that the Co-Ni-Fe binder consists of 50 wt.% cobalt, 25 wt.% nickel and 25 wt.% iron.

Guilemany et al. studied the mechanical properties of WC cerametals that have a Co binder and WC cerametals with higher resistance to corrosion that have a Co-binder substituted with nickel-rich nickel-iron at high binder contents made by sintering followed by HIPping . (See, for example, Gúilemany et al., "Mechanical-Property Relationships of Co / WC and Co-Ni-Fe / WC Hard Metal Alloys," Int. J. of Refractory &Hard Materials (1993-1994) 12, 199 -206). Metallurgically, cobalt is interesting since it is allotropic - that is, at temperatures greater than about 417 ° C, the pure cobalt atoms are arranged in a face-centered cubic structure (fcc) and at temperatures less than about 417 ° C, the pure cobalt atoms are arranged in an almost hexagonal packed structure (hcp). Thus, at approximately 417 ° C, pure cobalt exhibits an allotropic transformation, ie, what? the fcc structure changes to the hcp structure (fcc hcp transformation). Alloying the cobalt can temporarily suppress the fcc hcp transformation by stabilizing the fcc structure. For example, it is known that alloying cobalt with tungsten and carbon to form an alloy of Co-W-C (Co-binder) temporarily stabilizes the fcc structure. (See, for example, W. Dawihl et al., Kobalt 22 (1964) 16). It is well known, however, we submit, an alloy of Co-W-C (Co binder) to stress and / or strain induces the fcc hcp transformation. (See, for example, Schleinkofer et al., Material Science and Engineering A194 (1995) 1 and Meterials Science and Engineering A194 (1996) 103). In WC cerametals that have a Co binder the stress and / or stress developed during the cooling of the cerametals after densification (eg vacuum sintering, pressure sintering, hot isostatic pressing ... etc.) can induce the transformation fcc hcp. Also, it is well known that the cyclic loading, such as the cyclic loading that can propagate the growth of subcritical fractures, of WC cerametals having a Co-binder induces the fcc hcp transformation. Applicants have determined that in cerametals the presence of the hcp structure in the binder can be harmful since this can result in embrittlement of the binder. In this way, it would be desirable to find a binder that not only provides cost savings and that costs are predictable but also exhibits embrittlement mechanisms such as local ffc-hcp transformations. For the above reasons, there is a need for a cerametal having a binder with greater plasticity compared to the Co-binder which can be manufactured cheaply.

BRIEF DESCRIPTION OF THE INVENTION Applicants have determined that the presence of the hcp structure in the binder of a cerametal can be harmful. The hcp structure results in embrittlement of the binder. Applicants have identified a solution to the problem that includes using a binder that has greater plasticity. The present invention is directed to a cerametal having a binder, preferably a binder having a fcc structure, with improved plasticity (the plastic binder has reduced work hardening) which is stable even under high stress conditions and / or tension. The cerametal of the present invention also satisfies the need for a low cost cerametal having predictable and improved costs. Cerametal comprises a hard component and a binder with improved plasticity that improves the fracture resistance of cerametal. Although in relation to a comparable cerametal having a Co-binder, the cerametal having the plastic binder may have lower hardness, the total hardness of the wax of the invention can be adjusted by varying the grain size distribution of the hard component and / or the amount of the hard component without sacrificing strength and / or robustness. Preferably, the amount of hard component is increased to increase the hardness of the metal without sacrificing the strength and / or strength of the metal. An advantage of the wax of the present invention includes improved resistance to fractures and reliability, which can be attributed to the plasticity of the binder, relative to a comparable wax having a binder of Co. Another advantage of the wax of the present invention includes improved corrosion resistance and / or oxidation resistance relative to a comparable cerametal having a Co-binder. The ceramide of the present invention comprises at least one hard component and a cobalt-nickel-iron binder (Co-Ni-Fe binder). The Co-Ni-Fe binder comprises about 40 wt% to 90 wt% cobalt, the rest of the binder consists of nickel and iron, and optionally, accidental impurities, with the nickel comprising at least 4 wt%, but not more than 36% by weight of the binder and the iron comprising at least 4% by weight but not more than 36% by weight of the binder, with the binder having a Ni: Fe ratio of about 1.5: 1 to 1: 1.5; with a cermet, however, desisting from that comprising a Co-Ni-Fe binder consisting of 50% by weight of cobalt, 25% by weight of nickel and 25% by weight in iron. Preferably, the Co-Ni-Fe binder substantially comprises a cubic crystal structure centered on the face (fcc) and does not undergo transformation in base induced by stress or strain when subjected to plastic deformation. Preferably, the Co-Ni-Fe binder is substantially austenitic. This cerametal having a Co-Ni-Fe binder can be produced at lower and less fluctuating costs than a cerametal having a Co-Ni binder. The advantages of cerametals having a Co-Ni-Fe binder include resistance to Improved fractures and reliability, and improved corrosion resistance and / or oxidation resistance, both in relation to comparable cerametals having a Co-binder. The plastic binder of the present invention is unique in that even when subjected to plastic deformation, the binder maintains its glass structure fcc and avoids stress-induced and / or stress-induced transformations. Applicants have measured resistance and fatigue performance in cerametals having Co-Ni-Fe binders up to about 2400 megapascal (MPa) for flexural strength and up to about 1550 MPa for cyclic fatigue (200,000 cycles in flexion at about room temperature). Applicants believe that phase transformations induced by substantial stress and / or stress in the Co-Ni-Fe binder occur at those levels of stress and / or leading to superior performance.

DRAWINGS These and other features, aspects and advantages of the present invention will be better understood with reference to the following description, the appended claims and the accompanying drawings wherein: FIGURE 1 shows an optical photomicrograph of the microstructure of a WC-cerametal of the art above having a Co binder made by vacuum sintering at about 1550 ° C; FIGURE is shown in a black and white image of FIGURE 1 of the type used for the fraction analysis of the microstructure area of a prior art WC ceramide having a Co binder made by vacuum sintering at about 1550 ° C; FIGURE 2 shows (for comparison with FIGURE 1) an optical photomicrograph of the microstructure of a WC cermetal having a Co-Ni-Fe binder of the present invention made by vacuum sintering at about 1550 ° C; FIGURE 2a shows (for comparison with the FIGURE la) a black and white image of FIGURE 1 of the type used for the area fraction analysis of the WC cerametal microstructure having a Co-Ni-Fe binder of the present invention made by vacuum sintering to about 1550 ° C; FIGURE 3 shows an electron backscatter image (BEI) of the microstructure of a metal ceramide WC having a Co-Ni-Fe binder of the present invention made by vacuum sintering at about 1535 ° C; FIGURE 4 shows an elemental distribution map of energy dispersing spectroscopy (EDS) of tungsten (W) corresponding to the microstructure of the WC cerametal of FIGURE 3; FIGURE 5 shows an elemental distribution map of EDS for the carbon (C) that corresponds to the microstructure of the WC cerametal of FIGURE 3; FIGURE 6 shows an elemental distribution map of EDS for oxygen (O) that corresponds to the microstructure of WC cerametal of FIGURE 3; FIGURE 7 shows an elemental distribution map of EDS for cobalt (Co) that corresponds to the WC cerametal microstructure of FIGURE 3; FIGURE 8 shows an elemental distribution map of EDS for nickel (Ni) which corresponds to the microstructure of the WC cerametal of FIGURE 3; FIGURE 9 shows an elemental distribution map of EDS for iron (Fe) that corresponds to the microstructure of the WC cerametal of FIGURE 3; FIGURE 10 shows an elemental distribution map of EDS for the titanium (Ti) corresponding to the microstructure of the WC cerametal of FIGURE 3; FIGURE 11 shows a transmission electron microscopy (TEM) photomicrograph of a binder source in a prior art WC cerametal having a Co binder made by vacuum sintering at approximately 1535 ° C illustrating the high concentration of the stacking failure in those prior art ceramics; FIGURE 12 shows a photomicrog to TEM graph of another binder source in a prior art WC wax having a Co binder made by vacuum sintering at approximately 1535 ° C illustrating the high concentration of stacking failure present through those cerametals of the prior art; FIGURE 13 shows a comparative TEM photomicrograph of a binder source in a cerametal of the present invention, comprising a WC cermetal having a Co-Ni-Fe binder made by vacuum sintering at about 1535 ° C illustrating the absence of stacking faults; FIGURES 14, 14a and 14b show a comparative TEM photomicrograph, the results of the diffraction of the selected area (SAD) using TEM along the axis of the zone [031], and the results of the SAD using TEM along the axis of the zone [101] of a binder source in a WC cememetal having a Co-Ni-Fe binder of the present invention made by vacuum sintering at about 1535 ° C; FIGS. 15 and 15a show a TEM photomicrograph of a binder source in a prior art WC cememetal having a Co binder made by vacuum sintering at about 1535 ° C, illustrating the fracture mechanism caused by high concentrations of stacking failure; FIGS. 16 and 16a show, for comparison, a TEM photomicrograph of a binder source in a WC wax having a Co-Ni-Fe binder of the present invention made by vacuum sintering at about 1535 ° C illustrating the presence of plastic deformation and a high unrestrained dislocation density in those WC cerametals of the invention instead of the fracture mechanism caused by stacking failures in the prior art WC ceramics; FIGURE 17 shows Weibull distribution graphs of transverse rupture strengths (TRS) for a prior art WC cerametal having a Co binder (represented by open circles "O" and the line - - - - -) a WC-ceramic having a Co-Ni-Fe binder of the present invention (represented by "•" dots and the - - - - -) line, both made by vacuum sintering at about 1535 ° C; FIGURE 18 shows Weibull distribution charts of the TRS for a prior art WC cerametal having a Co binder (represented by open circles "O" and the line - - - - -) A comparative WC cerametal which has a Co-Ni-Fe binder of the present invention (represented by dots "•" and j_a line - - - - -), both made by vacuum sintering at about 1550 ° C; FIGURE 19 shows distribution graphs of Weibull of the TRS for a prior art WC cerametal having a Co binder (represented by "O" open circles and the - - - - - line) and a comparative WC cerametal having a Co-Ni binder -Faith of the present invention (represented by "•" points and the line -. - - -), both made by vacuum sintering at approximately 1550 ° C; FIGURE 20 shows performance data of flexural fatigue-strain amplitude (sma?) As a function of cycles to failure at about room temperature in the air - for a prior art WC wax having a Co-binder. (represented by ^ "O" open circles and the line - - - - -) and a comparative WC ceramide Co-Ni-Fe binder of the present invention (represented by "•" dots and the line - - - - -), both made by vacuum sintering at approximately 1550 ° C; FIGURE 21 shows performance data of flexural fatigue-strain amplitude (smax) as a function of the failure cycles tested at approximately 700 ° C in the air - for such a WC-cement of the prior art having a binder of Co (represented by open circles "O" and the line - - - - -) and a comparative WC wax-metal Co-Ni-Fe binder of the present invention (represented by "#" and "a" lines - - - - -), both made by vacuum sintering at approximately 1550 ° C, and FIGURE 22 shows the compression-low stress cycle of fatigue performance data by bending-amplitude of effort (smax) as a function of the cycles at fails approximately at room temperature in the air - for a prior art WC wax having a Co binder (represented by open circles "O" and the line - - - - -) and a Co-Ni-Fe binder WC comparative wax of the present invention (represent This is done by points "#" and the line - - - - -), both made by vacuum sintering at approximately 1550 ° C.

DESCRIPTION The cerametal of the present invention has a binder with improved plasticity (a plastic binder exhibiting reduced work hardening) comprising at least one hard component and a binder which, when combined with at least one hard component, possesses improved properties including, for example, improved resistance to growth of subcritical fractures under cycle fatigue, improved strength, and, optionally, improved oxidation resistance and / or improved corrosion resistance. Optionally, the cerametal of the present invention may exhibit corrosion resistance and / or oxidation resistance in an environment (eg, a solid, a liquid, a gas, or any combination of the foregoing) due to (1) the chemical inertness of the cerametal, (2) formation of a protective barrier over the cerametal against the interactions of the environment and the cerametal, or (3) both. A more preferred composition of the Co-Ni-Fe binder comprises a Ni: Fe ratio of about 1: 1. An even more preferred composition of the Co-Ni-Fe binder comprises a cobalt: nickel: iron ratio of about 1.8: 1.1. It will be appreciated by those skilled in the art that the Co-Ni-Fe binder may optionally comprise accidental impurities emanating from the starting materials, metallurgical spraying processes, machining and / or sintering, as well as environmental influences. It will be appreciated by those skilled in the art that the binder content of the cerametals of the present invention depends on factors such as the composition and / or geometry of the hard component, the use of the ceramide, the composition of the binder. For example, when the cerametal of the invention comprises a WC wax having a Co-Ni-Fe binder, the binder content may comprise from about 0.2 wt% to 35 wt% (preferably 3% by weight). weight at 30% by weight), and when the cerametal of the invention comprises a TiCN cerametal having a Co-Ni-Fe binder, the binder content may comprise from about 0.3 wt% to 25 wt% (preferably 3 wt%) to 20% by weight). As a further example, when a WC wax of the invention having Co-Ni-Fe binder is used as a peak-type tool for mining and construction, the binder content may comprise from about 5% by weight to 27% by weight (preferably from about 5% by weight to 19% by weight); and when a WC wax of the invention having Co-Ni-Fe binder is used as a revolving tool for mining and construction, the binder content may comprise from about 5% by weight to 19% by weight (so preferable from about 5% by weight to 15% by weight); and when a WC wax of the invention having a Co-Ni-Fe binder is used as a screw head punch, the binder content may comprise about 8% by weight up to 30% by weight (so preferable from about 10% by weight to 25% by weight); and when a ceramide of the invention having a Co-Ni-Fe binder is used as a cutting tool for chips formed from the machining of workpiece materials, the binder content may comprise about 2% by weight to 19% by weight (preferably from about 5% by weight to 14% by weight); and when a ceramide of the invention having Co-Ni-Fe binder is used as an elongated rotating tool for machining materials, the binder content may comprise from about 0.2 wt% to 19 wt% (preferably from about 5% by weight to 16% by weight). A hard component may comprise at least one of the borides, carbides, nitrides, carbonitrides, oxides, silicides, their mixtures, their solid solutions or combinations thereof. The metal of at least one of the borides, carbides, nitrides, oxides or silicides may include one or more metals of the groups 2,3, (including the lanthanides, actinides), 4, 5, 6, 7, 8, 9, 10, 11, 12, 13 and 14 of the International Union of Pure and Applied Chemistry (IUPAC). Preferably, at least one hard component may comprise carbides, nitrides, carbonitrides, their mixtures, their solid solutions, or any combination thereof. The metal of the carbides, nitrides and carbonitrides may comprise one or more metals of groups 3, including the lanthanides and actinides, 4, 5 and 6 of the IUPAC; and more preferably, one or more of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum and tungsten. In this context, the waxes of the invention can be referred to by the composition constituting the majority of the hard component. For example, if a hard component majority comprises carbide, the cermet can be designated as a carbide cermet. If a majority of the hard component comprises tungsten carbide (WC), the cermet can be designated as tungsten carbide cerametal or WC cermetal. Similarly, the ceramides may be named, for example, boride wax metals, nitride wax metals, oxide wax metals, silicide wax metals, carbonitride wax metals, oxynitride wax metals. For example, if a majority of the hard components comprise titanium carbonitride (TiCN), the wax can be designated as a titanium carbonitride wax or TiCN cermet. This nomenclature should not be limited by the above examples and instead form the basis that leads to a common understanding to those skilled in the art. Dimensionally, the grain size of the hard component of the cerametal having a high plasticity binder can range in size from the order of submicrons to about 100 micrometers (μm) or more. The submicrometers include nanostructured materials that have structural characteristics ranging from about 1 nanometer to about 100 nanometers (0.1 μm) or more. It will be appreciated by those skilled in the art that the grain size of the hard component of the cerametals of the present invention depends on factors such as the composition and / or geometry of the hard component, the use of the ceramide, and the composition of the binder. For example, the applicants believe that when the wax of the invention comprises a WC wax having a Co-Ni-Fe binder., the grain size of the hard component may comprise from about 0.1 μm to about 40 μm, and when the cermet of the invention comprises a TiCN cermet having a Co-Ni-Fe binder, in particle size of the component Hard can comprise from about 0.5 μm to about 6 μm. As an example, applicants believe that when the WC-based wax of the invention having Co-Ni-Fe binder is used as a peak-type tool or as a rotating tool for mining and construction, the grain size of the component hard can comprise from about 1 μm to about 30 μm (preferably from about 1 μm to about 25 μm); and when a WC wax of the invention having Co-Ni-Fe binder is used as a screw head punch, the grain size of the hard component can comprise from about 1 μm to about 25 μm (preferably about 1 μm to about 15 μm); and when a cerametal of the invention having Co-Ni-Fe binder is used as a cutting tool for chips formed during the machining of workpiece materials, the grain size of the hard component may comprise about 0.1 μm. up to 40 μm (preferably from about 0.5 μm to 10 μm); and when a cerametal of the invention having a Co-Ni-Fe binder is used as an elongated rotating tool for machining material, the grain size of the hard component can comprise from about 0.1 μm to 12 μm (preferably about 8 μm and smaller). The applicants contemplate that each increment between the end points of the ranges described herein, for example, the binder content, the binder composition, the Ni: Fe ratio, the grain size of the hard component, the hard component content, ... etc., is covered here as if it were specifically established. For example, a range of binder content of about 0.2% by weight to 35% by weight encompasses increases of about 1% by weight, specifically including therefore about 0.2% by weight, 1% by weight, 2% by weight , 3% by weight, ..., 33% by weight, 34% by weight and 35% by weight of the binder. While, for example, for a binder composition, the range of the cobalt content from about 40 wt% to 90 wt% encompasses increases of about 1 wt%, whereby specifically 40 wt% is included, 41% by weight, 42% by weight, ... 88% by weight, 89% by weight, and 90% by weight, while the nickel and iron ranges from approximately 4% to 36% by weight each encompass increments of about 1% by weight, including therefore specifically 4% by weight, 5% by weight, 6% by weight, ... 34% by weight, 35% by weight and 36% by weight. In addition, for example, a range of the Ni: Fe ratio of about 1.5: 2.1 to 1: 1.5 encompasses increments of about 0.1, thus specifically including 1.5: 1, 1.4: 1, ... 1: 1,. .. 1: 1.4, and 1: 1.5). In addition, for example, a grain size range of the hard component of about 0.1 μm to about 40 μm encompasses increments of about 1 μm, thus specifically including about 1 μm, 2 μm, 3 μm, ... 38 μm, 39 μm, and 40 μm. A wax of the present invention may be used with or without a coating depending on the use of the wax metals. If the ceramide is to be used with a coating, then the ceramide is coated with a coating that exhibits suitable properties, such as, for example, lubricity, wear resistance, satisfactory adhesion to the metal, chemical inertness with the materials of the workpiece. work at the temperatures of use, and a coefficient of thermal expansion that is compatible with that of the cerametal (that is, compatible with thermophysical properties). The coating can be applied via CVD and / or PVD techniques. Examples of coating material, which may comprise one or more layers of one or more different components, may be selected from the following, which are not intended to be wholly exclusive: alumina, zirconia, aluminum oxynitrile, silicon oxynitrile, SiAlON, the borides of the elements of groups 4, 5 and 6 of the IUPAC, the carbonitrides of the elements of groups 4, 5 and 6 of the IUPAC, including titanium carbonitride, the nitrides of the elements of groups 4, 5 and 6 of the IUPAC including the titanium nitride, the carbides of the elements of groups 4, 5 and 6 of the IUPAC, including titanium carbide, cubic boron carbide, silicon nitride, carbon nitride, nitride aluminum, diamond, diamond like coal, titanium nitride and aluminum. The cerametals of the present invention can be made from a pulverized mixture comprising a pulverized hard component and a pulverized binder which can be consolidated by any forming means including, for example, pressing, for example, uniaxial, biaxial, triaxial, hydrostatic, or wet bag (e.g., isostatic pressing) either at room temperature or at elevated temperature (e.g., hot pressing, hot isostatic pressing), casting, injection molding; extrusion; molding in the form of tape; casting or molding in suspension; casting or sliding molding; or any combination of the above. Some of those methods are discussed in U.S. Patent Nos. 4,491,559; 4,249,955; 3,888,662; and 3,850,368, the subject matter of which is incorporated herein by reference in its entirety in the present invention. In any case, whether or not a pulverized mixture is consolidated, its solid geometry can include any conceivable by one skilled in the art. To achieve a shape or combinations of shapes, the spray mixture can be formed before, during, and / or after densification. The formation techniques before densification can include any of the aforementioned means, as well as the raw or plastic machining that forms the raw body or its combinations. Formation techniques after densification can include any such machining operations, such as grinding, electronic discharge machining, brush rectification, cutting, etc. A raw body comprising a spray mixture can then be classified by Any means which are compatible with the manufacture of a ceramide of the present invention Preferred means comprise liquid phase sintering Such means include vacuum sintering, sintering under pressure (also known as sinter-HIP), isostatic pressing (HIPping), etc. These media operate at a temperature and / or pressure sufficient to produce an article in substantially dense theory having minimal porosity. For example, for WC cememetal having a Co-Ni-Fe binder, such temperatures can include temperatures ranging from about 1300 ° C (2373 ° F), to about 1760 ° C (3200 ° F) and so preferable, from about 1400 ° C (2552 ° F) to about 1600 ° C (2912 ° F). The densification pressures may range from about zero (0) kPa (zero (0) psi) to about 206 MPa (0 ksi). For carbide cerametal, pressure sintering (also known as sinter-HIP) can be carried out from about 1.7 MPa (250 psi) to about 13.8 MPa (2 ksi) at temperatures from about 1370 ° C (2498 ° F) to about 1600 ° C (2912 ° F), while HIPping can be carried out from about 68 MPa (10 ksi) to about 206 MPa '(30 ksi) at temperatures of about 1,310 ° C (2373 ° F) to about 1760 ° C (3200 ° F). The densification can be carried out in the absence of an atmosphere, that is, under vacuum; or in an inert atmosphere, for example, one or more gases of group 18 of the IUPAC; in carburizing atmospheres; nitrogen atmospheres, for example, nitrogen, formation gas (96% nitrogen, 4% hydrogen), ammonia etc .; or a reducing gas mixture, for example, H2 / H20, CO / C02, CON / H2 / C02 / H20, etc .; or any combination of the above.

The present invention is illustrated by the following. This is provided to demonstrate and clarify various aspects of the present invention: however, the following should not be construed as limiting the scope of the claimed invention. Table 1 summarizes the nominal binder content in% by weight, the Co: Ni: Fe ratio, the cerametal type, the% by weight of the 1st hard component, the size of the 1st hard component (μm), the% by weight of the 2nd hard component, the size of the 2nd hard component (μm), the% by weight of the 3rd hard component, the size of the 3rd hard component (μm), the method of machining or milling (where WBM = wet grinding in a mill) of balls and AT = ground by wear), the grinding time (hr), and the densification method (Dnsfctn *) (where VS = vacuum sintering, HIP = isostatically hot pressing, and PS = pressure sintering [also known as sinter-HIP], temperature (temp), and tierrtpo (hr) for a number of WC cerametals and TiCN cerametals within the scope of the present invention.These materials were produced using conventional powder metallurgical technology as described in, for example, "World Directory and Handbook of HARDMETALS AND HARD MATERIALS "Sixth Edition, by Kenneth J. A. Brookes, International Carbide DATA (1996); "PRINCIPLES OF TUNGSTEN CARBIDE ENGINEERING" Second Edition, by George Schneider, Society of Carbide and Tool Engineers (1989); "Cermet-Handbook, Hertel AG, Werzeuge + Hartstoffe, Fuerth, Bavaria, Germany (1993), and" CEMENTED CARBIDES ", by P. Schwarzkopf &R. Kieffer, The Macmillan Company (1960) - the subject matter of which it is incorporated herein by reference in its entirety in the present application.

These cerametals were made using commercially available ingredients (as described in, for example, "World Directory and Handbook of HARDMETALS AND HARD MATERIALS" Sixth Edition). For example, material -8, a WC wax from Table 1, was made from a batch of approximately 10 kilograms (kg) of initial powders comprising approximately 89.9% by weight WC (macrocrystalline tungsten carbide (mesh) -80 + 400 [particle size between about 38 μm and 180 μm] of Kennametal Inc. Fallon, Nevada [] this was also the initial WC for material 5 and 8-12 in table 1]), approximately 4.5% by weight of commercially available extra-fine cobalt powder, approximately 2.5% by weight of commercially available nickel powder (INCO Grade 255, INCO International, Canada), 2.5% by weight of commercially available iron powder (Carbonyl Iron Powder CN, BASF Corporation , Mount Olive, New Jersey) and approximately 0.6% by weight of tungsten metal powder (particle size of approximately 1 μm from Kennametal Inc. Fallon, Nevada) This lot, to which was added approximately 2.1% by weight of cexa. "paraffin and about 0.3% by weight of surfactant, was combined with about 4.5 liters of naphtha (the petroleum distillate "LACOLENE", Ashland, Chemical, Columbus, OH) for wet milling in a ball mill for about 16 hours. The milled mixture was dried in a sigma knife dryer, dry milled using a Fritzmill mill, and granulated to produce a pressed powder having a Scott density of approximately 25 x 106 kg / m3 (63.4 grams / inch3). The pressed powder exhibited good flow characteristics during formation in raw bodies in the form of square plates (based on inserts of type SNG433) by pressing. The raw bodies were placed in a vacuum sintering furnace or a dedicated baking device for densification. The furnace and its contents, in an atmosphere of hydrogen evacuated to about 0.9 kilopascals (kPa) [7 torr], were heated from about room temperature to about 180 ° C (350 ° F) at about 9/12 of an hour under empty and they were kept for about 3/12 of an hour; they were heated to approximately 370 ° C (700 ° F) at approximately 9/12 of an hour and maintained for approximately 4/12 of an hour; they were heated to about 430 ° C (800 ° F) in about 5/12 of an hour and maintained for about 4/12 of an hour; they were heated to about 540 ° C (1000 ° F) in about 5/12 of an hour and remained for about 2/12 of an hour; heated to approximately 590 ° C (110 ° F) in about 4/12 of an hour, then with the interrupted hydrogen jgas there is a heating to approximately 1120 ° C (2050 ° F) in about 16/12 of a hour and were maintained for about 4/12 of an hour under vacuum ranging from about 15 micrometers to about 23 micrometers; they were heated to about 1370 ° C (2500 ° F) in about 9/12 of an hour and maintained for about 4/12 of an hour while introducing argon at about 1,995 kPa (15 torr); they were heated at approximately 1550 ° C (2825 ° F) at approximately 9/12 of an hour while the argon was maintained at approximately 1995 cPa (15 torr) and maintained for approximately 9/12 of an hour; and then the powder for the oven was interrupted and the oven and its contents were allowed to cool to approximately room temperature. As anyone skilled in the art understands, Material 8 of Table 1 was made by known techniques. In this regard, the ability to use known techniques, and in particular vacuum sintering is an advantage of the present invention and is contrary to the teachings of the art. In a manner similar to Material 8, Materials 1-7 and 9-12 of Table 1 were formed, consolidated and densified using substantially stable techniques. The dosing of materials 1-4, 6, 7, 11 and 12 was carried out using pressure sintering (also known as sinter-HIP) with the pressure of the atmosphere in the sintering furnace being raised to approximately 4.MPa ( 40 bar) for the last approximately 10 minutes at the temperature shown in Table 1. In addition, comparative materials of the prior art were made which only have Co binders for materials 2, 4-6, and 9-12, and At the same time comparative materials of the prior art having a Co-Ni binder (Co: Ni = 2: 1) were made for Material 7. The results of the mechanical, physical and microstructural properties for materials 1-8 of the Table 1 with the comparative materials of the prior art are summarized in Table 2. In particular, Table 2 summarizes the density (g / cm3), the magnetic saturation (0.1 μTm3 / kg), the coercive force (Oe, substantially measured according to the norm a International ISO 3326: Determination of coercivity of hard metals (magnetization), the subject matter of which is hereby incorporated as a reference in its entirety in the present application) hardness (Hv3o, measured substantially in accordance with the international ISO standard 3878 :. Vickers hardness test of hard metals the subject matter of which is incorporated herein by reference in its entirety in the present application), the resistance to transverse rupture (MPa, measured substantially in accordance with international standard ISO 3327 / Type B : Determination of the force to the transverse breaking of hard metals, the subject matter of which is hereby incorporated as a reference in its entirety in the present application), and the porosity (measured substantially according to the International Standard ISO 4505: Metallographic Determination of the porosity of hard metals and non-combined carbon, the subject matter of which is incorporated herein by reference in its entirety in the present application).

An in-depth characterization of Materials 9-12 and comparative materials of the prior art was made and summarized in Tables 3, 4, 5 and 6. The data include density (g / cm3), magnetic saturation (Tm3 / kg ,), coercive force (He, oersteds), Vickers hardness (HV30), Rockwell hardness (HRA), fracture resistance (K? C square root of megapascals meters [Mpam1 2], determined substantially according to the Designation ASTM: Standard Test Method C1161-90 for Flexure Resistance and Advanced Ceramics at Room Temperature, American Society for Testing and Materials, Philadelphia, PA the subject matter of which is incorporated herein by reference in its entirety in the present invention ), binding ratio (% by weight of Co:% by weight of Ni:% by weight of Fe determined from the results of the chemical analysis), binder content (percent by weight of cermet), resistance to rupture transversal (TRS, megapas lime (MPa), determined substantially according to the method described by Schleinkofer et al. in Materials Science and Engineering, A194 (1995), 1-8 for Table 4 and by ISO 3327 of Tables 3, 5 and 6, the subject matter of which is incorporated herein by reference in its entirety in the present application ), thermal conductivity (cond. ter., calories / centimeter-second-degree-centigrade (cal / (cm.s. ° C), determined substantially using a pulse laser technique), Vickers Hardness at 20 ° Hot C, 200 ° C, 400 ° C, 600 ° C and 800 ° C (HV100 / 10, determined by injecting cermet samples at temperature using a load of approximately 100 grams for approximately 10 seconds), and chemical analysis of the binder (% by weight, determined using fluorescence x [only Co, Ni, and Fe are from the binder, it was assumed that Ta, Ti, Nb and Cr are carbides and thus part of the hard components, the rest up to 100% by weight is WC or TiCN as given in Table 1 for the respective material- #, plus accidental impurities, if the there are] ) .

Table 3: Comparison of the Properties of the Materials - vacuum sintering at 1535 ° C Magnetic Saturation Coercive Force Vickers Hardness **** Rockwell Hardness Binder Ratio (Co: Ni: Fe) ## total binder content in the material ### Resistance to Transversal Rupture (value determined by the distribution of Weibull) #### Thermal Conductivity f Vickers Hardness in Hot Chemical Analysis in Table 4: Comparison of the Properties of the Materials - vacuum sintered at 1550 ° C Magnetic Saturation Coercive Strength Vickers Hardness Rockwell Hardness # Binder Ratio (Co: Ni: Fe) ## total binder content in the material ### Resistance to Transversal Rupture (value determined by the distribution of Weibull) #### Thermal Conductivity: Hardness of Hot Vickers Chemical Analysis in% Table 5: Comparison of the Properties of the Materials - Sintered pressure at 1485 ° C Magnetic Saturation Coercive Force Vickers Hardness * *** Rockwell Hardness # Binder Ratio (Co: Ni: Fe) ## total binder content in the material M # Resistance to Transversal Rupture (value determined by the distribution of Weibull) MM Thermal Conductivity! Hardness of Vickers in Hot Chemical Analysis in% Table 6: Comparison of the Properties of the Materials - Sintered by Pressure at 1550 ° C Magnetic Saturation Coercive Strength Vickers hardness Rockwell hardness Binder ratio (Co: Ni: Fe) ## total binder content in the material ### Resistance to Transversal Rupture (value determined by the distribution of Weibull) #### Thermal Conductivity Hardness of Hot Vickers Chemical Analysis in% Briefly, the data demonstrate that WC-cerametals having Co-Ni-Fe binder have properties that are at least comparable toand, in general, better than those of the WC cerametals having Co binders. To better quantify the WC cerametals of the invention having an additional microstructural characterization of Co-Ni-Fe binders, they were carried out including optical microscopy, transmission electron microscopy and scanning electron microscopy. Figure 1 is a photomicrograph of the microstructure of a prior art WC ceramide having a hard component of tungsten carbide 4 and a Co-2 binder made by vacuum sintering at about 1550 ° (Material 10 of the Art. Previous). Figure 2 is an optical photomicrograph of the microstructure of a WC ceramide having a free tungsten carbide 4 component and a Co-Ni-Fe 6 binder also made by vacuum sintering at about 1550 ° C (Material 10). The microstructures appear to be substantially the same. The volume percent of the binder (determined substantially by measuring the percent of the black area) in the Material 10 of the Prior Art and the Material 10 measured approximately 12.8 and 11.9 at approximately 1875 X (6.4 μm), illustrated in the Figures la and 2a, respectively. Additional values measured approximately 13.4 and 14.0 to approximately 1200 X (10 μm), respectively. The percent of the area of the binder for "Prior Art Material 9 and Material -9 measured approximately 15.3 and 15.1 to approximately 1200 X (10 μm), respectively." The percent of the binder area of the Material 11 of the Prior Art and Material 11 measured 14.6, . 1 to approximately 1200 X (10 μm), respectively. These data confirm that the WC-cerametal having Co-Ni-Fe binder has substantially the same distribution, on a volume percent basis, of hard component and binder as a prior art WC wax having a binder. Co, when both were produced from batches of powder formulated on substantially the same base in percent by weight hard component and binder. Figures 3 to 10 correlate with the distribution of the elements (determined in an electron microscope by energy disperser spectroscopy using a scanning electron microscope JSM-6400 (Model No. ISM65-3, JEOL LTD, Tokyo, Japan) equipped with a LaBe cathodic electron gun system and an energy disperser x-ray system, a lithium-silicon detector (Oxford Instruments Inc., Analytical System Division, Microanalysis Group, Bucks, England) in a sample of Material 9 for its characteristics microstructural structures Figure 3 is an electronic retroinspection image (BEI) of the microstructure of Material 9 comprising a Co-Ni-Fe 6 binder, the hard component of WC 4, and a hard component of titanium carbide 10. The Figures 4 through 10 are maps of "distribution of the elements for tungsten (W), carbon (C), oxygen (0), cobalt (Co), nickel (Ni), iron (Fe), and titanium (Ti), respectively, which correspond to the microstructure of Figure 3. The coincidence of Co, Ni, and Fe demonstrate their presence as the binder. The mismatch of Co, Ni, and Fe with W demonstrates that Co-Ni-Fe binders cemented tungsten carbide. The area of Figure 10 showing a concentration of Ti in combination with the same area in the BEI of Figure 3 suggests the presence of a carbide containing titanium. Transmission electron microscopy (TEM) studies of Material 11 of the Prior Art and Material 11 were conducted. Samples of both materials were prepared substantially according to the method described in "Fatigue of Hard Metals and Cerametals under Cyclically Varied Efforts" presented by Uwe Schleinkofer as a Doctoral Thesis at the Faculty of the Erlangen-Nuernberg University, Germany (1995), the subject matter of which is hereby incorporated by reference in its entirety in the present application. The studies were performed using an electron microscope transmission scan Phillips Electronics E; 400T (STEM) equipped with an energy dispersing x-ray system with a silicon and aluminum detector (Oxford Instruments Inc., Analytical System, Division, Microanalysis Group, Bucks, England). FIGURE 11 shows a TEM image of the Co 2 binder of Material 11 of the Prior Art. Flat stacking faults 12 are observed through the Co 2 binder with regions of high concentration of stacking faults 14. Each stacking fault represents a thin layer of Co binder transformed fcc - »hcp. Those regions of high concentration of stacking faults represent transformed binder fcc - > hcp significantly. One explanation for flat stacking faults is that the Co binder has a low stacking fault energy. Consequently, the imposition of an effort and / or tension induces the transformation of a fcc structure in other circumstances to an hcp structure, hardening the binder of Co. FIGURE 12 shows a TEM image of another area of the Co 2 binder near a hard tungsten carbide component 4 of the Material 11 of the Prior Art. As with FIGURE 11, flat stacking faults ~ 12 are observed throughout the Co 2 binder with regions of high concentration of stacking faults 14. In contrast, FIGURE 13 shows a TEM image of the Co-Ni binder -Fe 2 of Material 11. In addition to a hard component of tungsten carbide 4, FIGURE 13 shows dislocations 16. Unlike material 11 of the prior art, applicants believe that the Co-Ni-Fe binder of Material 11 has a high stacking failure energy that suppresses stacking failure formation. flat In addition, applicants believe that the energy of the stacking fault is at a level that allows unrestricted displacement movement. FIGURES 14, 14a and 14b show a photomicrograph of comparative TEM, the results of the diffraction of the selected area (SAD) to along the axis of the zone [031], and the results of the SAD along the axis of the zone [101] for the Co-Ni-Fe binder of the Material 11. The results of the SAD of FIGURES 14a and 14b are characteristic of a fcc structure in the absence of the hcp structure. Consequently, the imposition of an effort and / or stress on the binder of Co-Ni-Fe generated non-flat defects such as dislocation 16. • Such behavior indicates that there is greater plastic deformation of the Co-Ni-Fe binder than in the binder of Co. The consequences of the limited plastic deformation in the binder of Co are shown dramatically in FIGS. 15 and 15a. These TEM images show a fracture 22 that formed in the Co 4 binder, the orientation of the fracture 20 and 20 ', and its coincidence with the orientation of the stacking fault 18 and 18'. In contrast, the benefits of the plasticity of the Co-Ni-Fe binder are shown in FIGS. 16 and 16a. These TEM images show a single dislocation 38, the slip marks of the displacement 26 on the surface of a thin section of the TEM, and the high density of unrestricted, non-planar dislocations, which is characteristic for a high plastic deformation. 24 of the Co-Ni-Fe binder 6. The transverse rupture resistances (TRS) measured for Material 9 of the Prior Art and Material 9 were analyzed using Weibull statistics. FIGURE 17 represents the Weibull distribution chart of the TRS for the Material 9 of the Prior Art having a binder of Co represented by open circles "O" and Material 9 (represented by dots "•"). Material 9 of the prior art had a Weibull modulus of approximately 20.4 and a mean TRS (flexural strength) of approximately 1949 MPa, both of which were determined from the linear least squares fit equation ln (ln (1 / (1-F))) = 20-422 • ln (s / MPa) -154.7 represented in the figure by the line - - - - -). In this equation F = (i-0.5) / Ni, where i is the sample number and Ni is the total number of samples tested and s is the measure of the flexural strength of the material. Material 9 had a Weibull modulus of approximately 27.9 and a mean TRS (flexural strength) of approximately 2050 MPa, both of which were determined from the least-squares fit equation, linear ln (ln (l / (lF))) = 27.915- In (s / MPa) -212.87 (represented in the figure by the line - - - - - -). The TRS measurements for Material 10 of the Prior Art and Material 9 were analyzed using Weibull statistics. FIGURE 18 represents the Weibull distribution chart of the TRS for the Material 10 of the Prior Art having a binder of Co represented by open circles "O" and the material 10 (represented by points "•"). Material 10 of the Technique Previous had a Weibull modulus of approximately 32.4 and a mean TRS (flexural strength) of approximately 1942 MPa, both of which were determined from the linear least squares fit equation ln (ln (l / (lF) )) = 32.4189-ln (s / MPa) -245.46 represented in the figure by the line - - - - -). Material 10 had a Weibull modulus of approximately 9.9 and a mean TRS (flexural strength) of approximately 2089 MPa, both of which were determined from the least squares fit equation, linear ln (ln (1 / (1-F))) = 9.9775 • ln (s / MPa) -75.509 (represented in the figure by the line - - - - - -).

The TRS measurements for Material 12 of the Prior Art and Material 12 were analyzed using Weibull statistics. FIGURE 19 represents the Weibull distribution graph of transverse rupture strength (TRS) for Material 12 of the prior art having a binder of Co represented by open circles "O" and Material 12 (represented by dots "•"). The Material 12 of the Prior Art had a Weibull modulus of about 35.1 and a mean transverse breaking strength (flexural strength) of about 2085 MPa, both of which were determined from the least squares fit equation ln (ln (1 / (1-F))) 35,094 • In (s / MPa) -268.2 (represented in the figure by the line - - - - -) Material 12 had a Weibull modulus of approximately 17.2 and a mean transverse breaking strength (bending strength) of approximately 2110 MPa, both of which were determined from the least squares fit equation, linear ln (ln (1 / (1-F))) = 17.202 • In (s / MPa) -131.67 (represented in the figure by the line - - - - - -) Performance in fatigue of Material 10 of the Technique Anterior and Material 10 were evaluated at about room temperature, at about 700 ° C in the air (both determined substantially according to the method described in U. Schleinkofer, HG Sockel.

P. Sclund, K. Górting, W. Heinrich, Mat. Sci. Eng. A194 (1995) 1; U. Schleinkofer, Doctoral Thesis, University of Erlangen-Nürnberg, Erlangen, 1995; U. Schleinkofer, H. G.

Sockel, K. Górting, W. Heinrich, Mat. Sci. Eng. A209 (1996) 313; and U. Schleinkofer, H. G. Sockel, K. Gorting, W.

Heinrich, Int. J. of Refractory Metals & Hard Materials 15 (1997) 103 the subject matter of which is incorporated herein by reference in its entirety in the present application), and at about 700 ° C in an atmosphere of argon (determined substantially according to B. Roebuck, M. G.

Gee, Mat. Sci. Eng. A209 (1996) 358 the subject matter "of which is incorporated herein by reference in its entirety in the present application) and is shown in FIGURES 20, 21 and 22, respectively, FIGURE 20 shows in particular the amplitude of the effort (smax) as a function of the cycles to failure at room temperature in the air for the Material 10 of the Prior Art (represented by open circles "O") and the Material 10 (represented by points "•") FIGURE 21 shows the amplitude of the effort { Smax) as a function of the cycles up to the failure tested at 700 ° C in the air of the prior art, comparative for the Material 10 of the Prior Art "(represented by open circles). "O") and Material 10 (represented by "•" points). FIGURE 22 shows the low cycle fatigue performance data (effort amplitude [smax] as a function of the cycles up to the failure tested) at 700 ° C in an argon atmosphere for the Material 10 of the Prior Art (shown by open circles "O") and Material 10 (represented by "•" points). In all three tests, Material 10 had at least one life to fatigue as long as Material 10 of the Prior Art and generally an improved life. As seen in FIGURE 20, Material 10 possesses a life until superior fatigue. In particular, three tests (designated as "- •" in FIGURE 20) were performed at the infinite life time "defined as 200,000 cycles.Furthermore, FIGURE 22 clearly demonstrates that Materials 10 have a longer life to fatigue for the same level of stress at elevated temperatures The patents or other documents identified herein are incorporated by reference in their entirety in the present application Other embodiments of the invention will be apparent to those skilled in the art upon consideration of the specification or practice of the invention described herein For example, the waxes of the present invention can be used for handling or removal of materials including, for example, mining, construction, agricultural and metal removal applications Some examples of agricultural applications include sowing boots, inserts for agricultural tools, discoidal blades, cutters or shredders lumber, lumbering tools and tools to work the land. Some examples of applications in mining and construction include cutting tools or excavators, earth augers, mineral or rock drills, construction equipment blades, rotary cutters, ground tools, crushing machines and digging tools. Some examples of material removal applications include drills, milling cutters, reamers, threading tools, material cutters and grinding inserts, material cutters or grinding inserts that incorporate chip control features, and material cutters or grinding inserts that they comprise a coating applied by either chemical vapor deposition (CVD), vapor pressure deposition (PVD), conversion coating, etc. A specific example of the use of the cerametals of the present invention includes the use of Material 3 of Table 1 as a screw head punch. Cerametals used as screw head punches must possess high impact resistance. The Material 3, a WC wax comprising approximately 22% by weight of Co-Ni-Fe binder was tested against Material 4 of the Prior Art, a WC-based wax comprising approximately 27% by weight of binder, of Co. The punches Screw head made of Material 3 work consistently better than screw head punches made of Prior Art Material 4 - producing 60,000-90,000 screws versus 30,000-50,000 screws. In addition, it was noted that the material was machined more easily (e.g., in the form of a microcircuit) than Material 4 of the Prior Art. It is intended that the specification and examples be considered as illustrative only, with the true scope and spirit of the invention being indicated by the following claims.

Claims (33)

CHAPTER CLAIMEDICATORÍO Having described the invention, it is considered as a novelty and, therefore, the content is claimed in the following CLAIMS:

1. A cermet, characterized in that it comprises: at least one hard component and a Co-Ni-Fe binder comprising from about 40% by weight to 90% by weight cobalt, the rest of the binder is made of nickel and iron, and optionally , accidental impurities, with the nickel comprising at least 4% by weight, but not more than 36% by weight of the binder and the iron comprising at least 4% by weight but not more than 36% by weight of the binder, with the binder having a Ni: Fe ratio of about 1.5: 1 to 1: 1.5; with the exclusion, however, of a cerametal comprising a Co-Ni-Fe binder consisting of 50% by weight of cobalt, 25% by weight of nickel and 25% by weight in iron.

2. Cerametal according to claim 1, characterized in that the Co-Ni-Fe binder has substantially a face-centered cubic structure (fcc) and does not undergo phase transformation induced by stress or strain when subjected to plastic deformation.

3. The cerametal according to claim 1 or claim 2, characterized in that the Co-Ni-Fe binder is substantially austenitic.

The cerametal according to any of claims 1 to 3, characterized in that the binder has a Ni: Fe ratio of about 1: 1.

The cerametal according to any of claims 1 to 4, characterized in that the binder has a cobalt: nickel: iron ratio of about 1.8: 1: 1.

6. The cerametal according to any of claims 1 to 5, characterized in that the binder comprises 0.2 to 35% by weight of the cermet.

The cerametal according to claim 6, characterized in that the binder comprises from 3 to 30% by weight of the cermet.

The cerametal according to any of claims 1 to 7, characterized in that at least one hard component comprises at least one of carbides, nitrides, carbonitrides, their mixtures and their solid solutions.

9. The cerametal according to any of claims 1 to 8, characterized in that at least one hard component comprises at least one carbide of at least one of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum and tungsten.

The cerametal according to any of claims 1 to 9, characterized in that at least one hard component comprises at least one carbonitride of at least one of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum and tungsten .

11. The cerametal according to any of claims 8 to 10, characterized in that at least one of the carbides is tungsten carbide (WC).

The WC-ceramic according to claim 11, characterized in that it also comprises at least one carbide of at least one of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium and molybdenum.

The WC-ceramic according to claim 11 to claim 12, characterized in that it also comprises at least one carbonitride of at least one of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum and tungsten.

The cerametal according to any of claims 8 to 10, characterized in that at least one of the carbonitrides is titanium carbonitride (TiCN).

15. The TiCN cerametal according to claim 14, characterized in that it comprises at least one carbide of at least one of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum and tungsten.

16. The TiCN cerametal according to claim 14 to claim 15, characterized in that it also comprises at least one carbonitride of at least one of zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum and tungsten. .

17. A method for manufacturing a cement according to any of claims 1 to 16, characterized in that it comprises the steps of: providing at least one hard component; • combining a binder with at least one hard component to form a pulverized mixture, the binder comprises from about 40% by weight to 90% by weight cobalt, the rest of the binder consists of nickel and iron, and optionally, impurities " accidental, with the nickel comprising at least 4% by weight, but not more than 36% by weight of the binder and the iron comprising at least 4% by weight but not more than 36% by weight of the binder, with the binder having a Ni: Fe ratio of about 1.5: 1 to 1: 1.5, with the exclusion, however, of a binder composition consisting of 50% by weight of cobalt, 25% by weight of nickel and 25% by weight in iron, and densify the pulverized mixture to produce a cerametal 18.

The method according to the claim 17, characterized in that the densification comprises at least one of vacuum sintering and pressure sintering.

The method according to claim 17 or claim 18, characterized in that the binder comprises a mixture of cobalt, nickel and iron.

The method according to claim 17 or claim 18, characterized in that the binder comprises an alloy of cobalt, nickel and iron.

The method according to any of claims 17 to 20, characterized in that at least one hard component comprises at least one of the carbides, nitrides, carbonitrides, their mixtures and their solid solutions.

22. The method according to any of claims 17 to 20, characterized in that at least one hard component comprises at least one carbide of at least one of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum and tungsten.

23. The method according to any of claims 17 to 22, characterized in that at least one hard component comprises at least one carbonitride, of at least one of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum and tungsten.

24. The use of the cerametal according to any of claims 1 to 13 and of a cerametal comprising a Co-Ni-Fe binder having 50% by weight of cobalt, 25% by weight of nickel, and 25% by weight iron weight, where the binder comprises from about 5% by weight to 27% by weight of the cermet, as a tool of the peak type for mining and construction.

25. The use according to claim 24, wherein the binder comprises from about 5% by weight to 19% by weight of the cermet.

26. The use of the cerametal according to any of claims 1 to 13 and of a cerametal comprising a Co-Ni-Fe binder having 50% by weight of cobalt, 25% by weight of nickel, and 25% by weight of iron, where the binder comprises from about 5% by weight to 19% by weight of the cermet, as a rotary tool for mining and construction.

27. The use according to claim 26, wherein the binder comprises from about 5% by weight to 15% by weight of the cermet.

28. The use of the cerametal according to any of claims 1 to 13 and of a cerametal comprising a Co-Ni-Fe binder having 50% by weight of cobalt, 25% by weight of nickel, and 25% by weight iron weight-, where the binder comprises from about 8% by weight to 30% by weight of the cermet, such as a screw head punch.

29. The use according to claim 28, wherein the binder comprises from about 10% by weight to 25% by weight of the cermet.

30. The use of the cerametal according to any of claims 1 to 16 and of a cerametal comprising a Co-Ni-Fe binder having 50% by weight of cobalt, 25% by weight of nickel, and 25% in weight of iron > wherein the binder comprises from about 2% by weight to 19% by weight of the metal, as a cutting tool for the machining with shavings of the materials of the workpiece.

31. The use according to claim 30, wherein the binder comprises from about 5% by weight to 14% by weight of the cermet.

32. The use of the cerametal according to any of claims 1 to 16 and of a cerametal comprising a Co-Ni-Fe binder having 50% by weight of cobalt, 25% by weight of nickel, and 25% by weight of iron, where the binder comprises from about 0.2% by weight to 19% by weight of the cermet, as an elongated rotating tool for machining materials.

33. The use according to claim 32, wherein the binder comprises from about 5% by weight to 16% by weight of the cermet.