Title of Invention	CEMENTED CARBIDE BODY CONTAINING ZIRCONIUM AND NIOBIUM AND METHOD OF MAKING THE SAME
Abstract	A sintered cemented carbide body (e.g., a cutting tool) and a method of making the same. The sintered cemented carbide body includes tungsten carbide, a binder phase of at least one metal of the iron group or an alloy thereof, and one or more solid solution phases. Each one of the solid solution phases has at least one of the carbides and carbonitrides of a combination of zirconium, niobium, and tungsten. The method includes the steps of providing a powder mixture that contains tungsten carbide, a binder metal powder comprising at least one metal of the iron group or an alloy thereof, and at least one of the carbides and carbonitrides of both zirconium and niobium including a powder of the carbides or carbonitrides of zirconium and niobium, forming a green compact of said powder mixture, and vacuum sintering or sinter-HIP said green compact at a temperature of from 1400 to 1560°C.

Title of Invention

CEMENTED CARBIDE BODY CONTAINING ZIRCONIUM AND NIOBIUM AND METHOD OF MAKING THE SAME

Abstract

A sintered cemented carbide body (e.g., a cutting tool) and a method of making the same. The sintered cemented carbide body includes tungsten carbide, a binder phase of at least one metal of the iron group or an alloy thereof, and one or more solid solution phases. Each one of the solid solution phases has at least one of the carbides and carbonitrides of a combination of zirconium, niobium, and tungsten. The method includes the steps of providing a powder mixture that contains tungsten carbide, a binder metal powder comprising at least one metal of the iron group or an alloy thereof, and at least one of the carbides and carbonitrides of both zirconium and niobium including a powder of the carbides or carbonitrides of zirconium and niobium, forming a green compact of said powder mixture, and vacuum sintering or sinter-HIP said green compact at a temperature of from 1400 to 1560°C.

Full Text	CEMENTED CARBIDE BODY CONTAINING ZIRCONIUM AND NIOBIUM AND METHOD OF MAKING THE SAME BACKGROUND OF THE INVENTION [0001] The present invention provides sintered cemented carbide bodies having increased resistance to plastic deformation comprising tungsten carbide (WC), a binder metal phase and one or more solid solution phases comprising at least one of the carbides, nitrides and carbonitrides of at least one of the elements of groups IVb, Vb and VIb of the Periodic Table of Elements. The present invention also provides a method for producing these sintered cemented carbide bodies. These sintered cemented carbide bodies are useful in the manufacture of cutting tools, and especially indexable cutting inserts for the machining of steel and other metals or metal alloys. [0002] Sintered cemented carbide bodies and powder metallurgical methods for the manufacture thereof are known, for example, from U.S. Patent Re. 34,180 to Nemeth et al.. While cobalt has originally been used as a binder metal for the main constituent, tungsten carbide, a cobalt-nickel-iron alloy as taught by U.S Patent No. 6,024,776 turned out to be especially useful as a binder phase for tungsten carbide and other carbides, nitrides and carbonitrides of at least one of the elements titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum and tungsten, respectively. [0003] Numerous attempts have been made in order to modify the properties or characteristics of the sintered cemented carbide bodies prepared by powder metallurgical methods. These properties include, but are not limited to, hardness, wear resistance, plastic deformation at increased temperatures, density, magnetic properties, resistance to flank wear and resistance to cratering. In order to provide cutting tools having improved wear properties at high cutting speeds, it is known, for example, that the sintered cemented carbide bodies should have increased contents of titanium or tantalum and niobium. On the other hand, however, it is known that increasing contents of titanium or tantalum or niobium result in a noticeable reduction of strength as they form solid solution carbides with tungsten carbide, since the amount of tungsten carbide-phase which provides for the maximum strength in a sintered cemented carbide body decreases with the formation of solid solution carbides. [0004] Also well known to those skilled in the art is the fact that the addition of zirconium and hafnium increases the strength of sintered cemented carbide bodies both at room temperature and at higher temperatures. However, the increase in strength is combined with lower hardness and decreased wear resistance. In addition, a disadvantage of the addition of zirconium is its high affinity to oxygen and its poor wettability which impedes the sintering process used in the preparation of the sintered cemented carbide body. [0005] U.S. Patents Nos. 5,643,658 and 5,503,925, both hereby incorporated by reference herein, aim at improving hot hardness and wear resistance at higher temperatures of sintered cemented carbide bodies by means of adding zirconium and/or hafnium carbides, nitrides and carbonitrides to the powder mixture of tungsten carbide and a binder metal of the iron family. As a result thereof, the hard phases of at least one of zirconium and hafnium coexist with other hard phases of metals of groups IVb, Vb and VIb, but excluding zirconium and hafnium, with said hard phases forming, in each case, solid solutions with tungsten carbide. Due to the high affinity of zirconium for oxygen, either the starting powder materials have to be extremely low in oxygen, or the oxygen content has to be controlled by using a reducing sintering atmosphere. [0006] JP-A2-2002-356734, published on December 13, 2002, discloses a sintered cemented carbide body comprising WC, a binder phase consisting of at least one metal of the iron group, and one or more solid solution phases, wherein one of said solid solution phases comprises Zr and Nb while all solid solution phases other than the first one comprise at least one of the elements Ti, V, Cr, Mo, Ta and W, but must not comprise Zr and Nb. According to this Japanese patent document, the best cutting results are achieved at a tantalum content of less than 1% by weight of the total composition, calculated as TaC. [0007] The present invention aims at achieving new sintered cemented carbide bodies having increased resistance to plastic deformation at increased temperatures and, as a result thereof, having increased wear resistance. Besides, the present invention aims at providing a powder metallurgical method of producing said sintered cemented carbide bodies. More specifically, it is an object of the present invention to provide a sintered cemented carbide body having at least two co-existing solid solution phases containing zirconium and niobium or one single homogenous solid solution phase containing zirconium and niobium. [0008] Another object of the present invention consists in providing a method of producing said sintered cemented carbide body comprising the step of providing a powder mixture which upon sintering provides at least two co-existing solid solution phases or one single homogenous solid solution phase containing, in each case, zirconium and niobium, and providing improved sintering activity and wettability with hard constituents of elements of groups IVb, Vb, and VIb of the periodic table of elements. SUMMARY OF THE INVENTION [0009] In one form thereof, the invention is a sintered cemented carbide body that has increased resistance to plastic deformation. The sintered cemented carbide body includes tungsten carbide, and a binder phase that includes at least one metal of the iron group or an alloy thereof, and one or more solid solution phases wherein each one of the solid solution phases comprises at least one of the carbides and carbonitrides of a combination of zirconium, niobium, and tungsten. [0010] In another form thereof, the invention is a method of producing a sintered cemented carbide body comprising the steps of: providing a powder mixture comprising tungsten carbide, a binder metal powder comprising at least one metal of the iron group or an alloy thereof, and at least one of the carbides and carbonitrides of both zirconium and niobium; forming a green compact of said powder mixture; and vacuum sintering or sinter-HIP said green compact at a temperature of from 1400 to 1560 °C, wherein a powdered solid solution of the carbides or carbonitrides of zirconium and niobium is used to form said powder mixture. [0011] In yet another form thereof, the invention is a cutting tool that comprises a body that includes a rake face and a flank face wherein the rake face and the flank face intersect to form a cutting edge at the intersection thereof. The body comprises tungsten carbide, a binder phase comprising at least one metal of the iron group or an alloy thereof, and one or more solid solution phases each one of which comprising at least one of the carbides and carbonitrides of a combination of zirconium, niobium, and tungsten. [0012] In still another form thereof, the invention is a sintered cemented carbide body that has increased resistance to plastic deformation. The sintered cemented carbide body includes tungsten carbide, and a binder phase that includes at least one metal of the iron group or an alloy thereof, and one or more solid solution phases wherein each one of the solid solution phases comprises at least one of the carbides and carbonitrides of a combination consisting of zirconium, niobium, and tungsten BRIEF DESCRIPTION OF THEACCOMPANYING DRAWINGS [0013] The following is a brief description of the drawings that form a part of this patent application: [0014] FIG. 1 is an isometric view of a cutting tool of the present invention wherein the cutting tool is a CNMG style of cutting tool; [0015] FIGS. 2A is a photomicrograph that shows the unetched microstructure of Sample (A), which is a sintered cemented carbide body, at 1,500-fold magnification (10 micrometer scale) wherein Sample (A) was produced according to the present invention as disclosed hereinafter, and Sample (A) has a porosity of [0016] FIG. 2B is a photomicrograph that shows the unetched microstructures of Sample (B), which is a sintered cemented carbide body, at 1,500-fold magnification (10 micrometer scale) wherein Sample (B) was produced according to a conventional process as disclosed hereinafter, and Sample (B) has a residual porosity of A08 as shown in FIG. 2B; [0017] FIG. 3A is a photomicrograph of a sintered bending strength test rod, in cross section, which was made according to the present invention as described hereinafter and does not show sinter distortion; [0018] FIG. 3B is a photomicrograph of a sintered bending strength test rod, in cross section, which was made in a conventional fashion as described hereinafter and very clearly shows a sinter distortion; [0019] FIG. 4 is a photomicrograph (20 micrometer scale) showing the unetched microstructure of an embodiment of the sintered cemented carbide body of the present invention wherein there is shown a binder enriched surface zone free of solid solution carbide wherein the binder enriched surface zone begins at and extends inwardly from the surface of the substrate and one single homogeneous solid solution phase (MC); and [0020] FIG. 5 is a photomicrograph (20 micrometer scale) showing the unetched microstructure of an other embodiment of the sintered cemented carbide body of the present invention wherein there is shown a binder enriched surface zone free of solid solution carbide wherein the binder enriched surface zone begins at and extends inwardly from the surface of the substrate and underneath the binder enriched surface zone free of solid solution phase there is shown a zone in which a single phase MC1 exists (MC1 is light brown), and underneath the MC1 zone there is a zone that has two coexisting solid solution carbide phases wherein one solid solution phase is MC land it is light brown and the other solid solution phase is MC 2 and it is dark brown. DETAILED DESCRIPTION OF SPECIFIC EMBODIMENTS [0021] Referring to FIG. 1, there is shown a cutting tool, i.e., a sintered cemented carbide body, generally designated as 20. Cutting tool 20 has a rake face 22 and flank faces 24. There is a cutting edge 26 at the intersection of the rake face 22 and the flank faces 24. The cutting tool 20 further contains an aperture 28 by which the cutting tool 20 is secured to a tool holder. The style of cutting tool shown in FIG. 5 is a CNMG style of cutting tool. The illustration in FIG. 1 of a CNMG style of cutting tool should not be considered to limit the scope of the invention. It should be appreciated that the present invention is a new cemented carbide material that can be used as a cutting tool wherein the geometry of the cutting tool can be any known cutting tool geometry. [0022] In regard to the composition of the cutting tool, i.e., a sintered cemented carbide body, the composition contains tungsten carbide and a binder, as well as one or more solid solution phases that comprise the carbides and/or the carbonitrides of a combination of zirconium, niobium and tungsten as exemplified by the formulae (Zr,Nb,W)C and/or (Zr,Nb,W)CN. In one preferred embodiment of the composition, just one of the solid solution phases consists of a carbide or carbonitride of a combination of zirconium, niobium and tungsten. In another preferred embodiment of the composition, the solid solution phase consisting of a carbide or carbonitride of a combination of zirconium, niobium and tungsten is the sole solid solution phase of the body wherein no other element such as titanium, hafnium, vanadium, tantalum, chromium, and molybdenum is present in said solid solution phase. [0023] In yet another preferred embodiment of the composition, one of the solid solution phases comprises a carbide or carbonitride of a combination of zirconium, niobium and tungsten and at least one carbide, nitride or carbonitride of one or more of titanium, hafnium, vanadium, tantalum, chromium, and molybdenum wherein the solid solution phase may be either the sole solid solution phase of the body or one of two or more different solid solution phases. More specifically, there can be two or more different solid solution phases that are present with each solid solution phase comprising a carbide or carbonitride of a combination of zirconium, niobium and tungsten, and at least one carbide, nitride or carbonitride of one or more of titanium, hafnium, vanadium, tantalum, chromium and molybdenum, respectively. In those cases where the solid solution phase comprises a carbide or carbonitride of a combination of zirconium, niobium and tungsten, and at least one carbide, nitride or carbonitride comprising one or more other metals, it is even more preferred that said at least one other metal is one or more of titanium, tantalum and hafnium. [0024] According to the present invention, the binder alloy preferably comprises cobalt, a CoNi-alloy or a CoNiFe-alloy, each of which may or may not contain additional alloying elements such as chromium and tungsten. The binder alloy preferably comprises between about 3 weight percent to about to 15 weight percent of the total body. [0025] Preferably, the total contents of a carbide or carbonitride of a combination of zirconium, niobium and tungsten of the one or more solid solution phase(s) comprise between about 1 weight percent and about 15 weight percent of the total body. Also preferred are those embodiments of the present invention wherein the total content of the elements titanium, hafnium, vanadium, tantalum, chromium and molybdenum does not exceed about 8 weight percent of the total body. According to especially preferred embodiments of the present invention, titanium comprises between about 1 weight percent and about 8 weight percent of the total body, tantalum comprises between about 1 weight percent and about 7 weight percent of the total body, and hafnium comprises between about 1 weight percent and about 4 weight percent of the total body. [0026] If the cemented carbide body has a mass ratio Nb/(Zr + Nb) of greater than about 0.5, and more preferably greater than or equal to about 0.6, the formation of a single homogeneous solid solution phase or the formation of two or more coexisting solid solution phases within the sintered cemented carbide body is remarkably increased. [0027] According to still another aspect of the present invention, the sintered cemented carbide body comprises at least one of said nitrides or carbonitrides and comprises an outermost zone being free of any solid solution phase but binder enriched up to a depth of about 50 micrometers (µm) from an uncoated surface of said body. Embodiments of this type are shown in FIGS. 4 and 5 hereof. [0028] As is acknowledged by those having ordinary skill in the art, binder enrichment and formation of a surface zone free of solid solution carbide (SSC) is induced during sintering once at least one nitride or carbonitride is present in the starting powder mixture. Due to the formation of free nitrogen during sintering, diffusion of binder metal from the bulk towards the surface, and diffusion of solid solution phase from the surface zone towards the bulk will take place, resulting in a binder enriched surface zone being free of any solid solution phase. Due to these diffusion processes, two or more coexisting different solid solution phases showing a concentration gradient between the surface and the center of the body are formed underneath of the binder enriched zone, according to a still more preferred embodiment of the present invention. In those cases, however, where just one single solution phase being homogeneous throughout the body is present, said one single and homogeneous solid solution phase will be located underneath of the binder enriched zone such that the single solid solution phase is homogeneous throughout said body, except in the binder enriched zone. [0029] According to still other preferred embodiments of the present invention, one or more wear resistant layers deposited according to well-known physical vapor deposition (PVD) or chemical vapor deposition (CVD) methods are coated over a surface of the sintered cemented carbide body. Preferably, these wear resistant coatings comprise one or more of the carbides, nitrides, carbonitrides, oxides or borides of a metal of the groups IVb, Vb and Ylb of the periodic table of elements, and alumina. [0030] Referring to the method aspects of the present invention, according to a preferred embodiment of the method of the present invention, a solid solution of a carbide or carbonitride of a combination of zirconium and niobium having a mass ratio Nb/(Zr + Nb) of greater than about 0.5, and preferably greater than or equal to about 0.6 or more, is used as the powdered solid solution of a carbide or carbonitride of a combination of zirconium and niobium. The powdered solid solution of a carbide or carbonitride of a combination of zirconium, niobium and tungsten preferably comprises between about 1 weight percent and about 15 weight percent of the total powder mixture. [0031] Preferably, cobalt powder, powders of cobalt and nickel or powders of cobalt and nickel and iron or powders of a cobalt-nickel alloy or powders of a cobalt-nickel-iron alloy are used as the binder metal powders, within the method of the present invention. Optionally, the binder metal powders may include additional elements, preferably one or more of chromium and tungsten. Preferably, the binder metal powder comprises between about 3 weight percent and about 15 weight percent of the total powder mixture. [0032] According to still another embodiment of the present invention, the powder mixture additionally comprises at least one carbide, nitride or carbonitride of one or more of titanium, hafnium, vanadium, tantalum, chromium, and molybdenum. Preferably, the powder mixture comprises at least one of the elements titanium, hafnium, vanadium, tantalum, chromium and molybdenum in an amount of between about 1 weight percent and about 8 weight percent of the total powder mixture. [0033] The present inventors have surprisingly found that due to the addition of zirconium and niobium in the form of a powdered solid solution of a carbide or carbonitride of a combination of zirconium and niobium to the starting powder mixture, instead of using zirconium carbide plus niobium carbide or zirconium carbonitride plus niobium carbonitride, each individually, either one single homogeneous solid solution phase comprising the carbides and/or the carbonitrides of a combination of zirconium, niobium and tungsten, or two or more coexisting solid solution phases comprising the carbides and/or the carbonitrides of a combination of zirconium, niobium and tungsten, and at least one carbide, nitride or carbonitride of one or more of titanium, hafnium, vanadium, tantalum, chromium and molybdenum, depending on the compounds added to the starting powder mixture, are formed during sintering according to the method of the present invention. [0034] Contrary to the documents mentioned herein above, upon sintering all elements added to the starting powder mixture are dissolved in each one of the coexisting solid solution phases, according to the present invention. For example, up to about 65 weight percent tungsten, up to about 75 weight percent niobium, up to about 60 weight percent zirconium, up to about 20 weight percent titanium, up to about 15 weight percent tantalum, and up to about 20 weight percent hafnium can be dissolved in the coexisting solid solution phases. [0035] Another advantage of the use of a powdered solid solution of a carbide or carbonitride of a combination of zirconium and niobium as part of the starting powder mixture according to the present invention is the fact that tantalum can be added to the composition for improving binder phase distribution and toughness in an amount of about 1 weight percent or more of the total starting powder mixture. [0036] The best results in terms of homogeneity of the solid solution phase(s) formed according to the present invention have been obtained if a powdered solid solution of a carbide or carbonitride of a combination of zirconium and niobium having a ratio of about 40 weight percent zirconium carbide and about 60 weight percent niobium carbide was added to the starting powder mixture. [0037] Referring to FIG. 2A and FIG. 2B, each one of these figures is a photomicrograph at 1500X (each photomicrograph as a 10 micrometer scale) that shows the unetched microstructures of two samples; namely, Sample (A) and Sample (B), respectively. Sample (A) was produced according to the present invention using (Zr,Nb)C in the starting powder mixture and whereas Sample (B) was conventionally made by using individual carbides; namely, ZrC and NbC instead of (Zr,Nb)C in the starting powder mixture. FIG. 2A shows that Sample (A) has a porosity of less than A02 and FIG. 2B shows that Sample (B) has a porosity of A08. In addition, as can be seen in FIG. 2A, the microstructure of Sample (A) obtained by using the (Zr,Nb)C solid solution in the starting powder is much more homogeneous in terms of porosity as compared with the microstructure (see FIG. 2B) of Sample (B), which is the conventionally prepared sintered cemented carbide body using ZrC + NbC as part of the starting powder mixture. [0038] Referring to FIG. 3A and FIG. 3B, these figures are photomicrographs of sintered bending strength test rods wherein each is in cross section. FIG. 3B shows the microstructure of Sample (B) that is made in a conventional fashion using ZrC and NbC in the starting powder mixture wherein there is a sinter distortion that can be seen very clearly. FIG. 3 A shows the microstructure of Sample (A) that was made according to the present invention using a solid solution carbide of zirconium and niobium (Zr,Nb)C wherein FIG. 3A does not show sinter distortion. This comparison shows that, with respect to sinter distortion, Sample (A) is much better with the present invention than with the conventional sample (B). [0039] As indicated earlier, a further advantage of using a powdered solid solution of a carbide or carbonitride of a combination of zirconium and niobium as part of the starting powder mixture consists in the lower affinity to oxygen, as compared to conventional methods of producing sintered cemented carbide bodies, whereby it is not necessary to have a reducing sintering atmosphere. Due to the avoidance of any controlling and monitoring of the reducing quality of the sintering atmosphere, sintering becomes easier and less expensive according to the present invention as compared to the prior art. [0040] Referring to FIG. 4, FIG. 4 is a photomicrograph of an embodiment of the sintered cemented carbide body of the present invention wherein there is shown a binder enriched surface zone free of solid solution carbide and one single homogeneous solid solution phase (MC). FIG. 4 shows that the present invention allows the production of sintered cemented carbide bodies having one single homogeneous solid solution phase. [0041] Referring to FIG. 5, FIG. 5 is a photomicrograph of an other embodiment of the sintered cemented carbide body of the present invention wherein there is shown a binder enriched surface zone free of solid solution carbide. Underneath the binder enriched surface zone free of solid solution phase there is shown a zone in which a solid solution phase MC1 exists. MC1 is light brown. Underneath the zone containing only MC1 solid solution phase, there is a zone that contains two coexisting solid solution phases. One solid solution phase is MC land it is light brown. The other solid solution phase is MC 2 and it is dark brown. FIG. 5 shows that the present invention allows the production of sintered cemented carbide bodies having different coexisting solid solution phases (MC1; (MC1+MC2)) visible by optical microscopy located underneath an outermost binder enriched zone being free of solid solution phase. [0042] Further details of the invention shall be described through the following examples. Table 1 sets forth the raw materials that were used in the examples that are set forth hereinafter. Table 1 - Raw Materials Used for the Examples [0043] In regard to the processing of the examples, for each one of the examples the specified raw materials were wet milled in an attritor for 10 hours and dried. Green compacts were pressed of the resulting powder mixtures and sintered according to the sintering conditions stated in the examples. In the examples the percentages are given in weight percent unless otherwise stated. [0044] As is well known to those skilled in the art of powder metallurgy, the element pairs tantalum and niobium as well as zirconium and hafnium in most cases of occurrence are associated with each other such that a complete separation often is difficult to obtain. This is why in commercial applications, small amounts or traces of niobium will be present in tantalum, and vice versa, and small amounts or traces of zirconium will be present in hafnium, and vice versa. This also is valid for the present disclosure, whenever these elements or compounds thereof are mentioned by their names or chemical formulae. Example 1: [0045] Powder mixtures A and B having the compositions (weight percent) given in Table 2 were prepared. TRS bars (ISO 3327, type B) were pressed from these powder mixtures to form green compacts. The compacts were sinter-HIPped at temperatures between 1430 and 1520 degrees Centigrade. The resulting sintered cemented carbide bodies were metallurgically tested. The results of these tests are shown in FIGS. 2A and 2B and FIGS. 3A and 3B. Sample A (according to the present invention) shows a porosity of whereas sample B (prior art comparative example) shows a high residual porosity (see FIG. 2B) and strong sinter distortion (see FIG. 3B). Table 2 - Starting Powder Mixtures for Samples (A) and (B) (weight percent) The resulting sintered cemented carbide bodies of Sample (A) and Sample (B) had the following properties as reported in Table 3 below. Table 3 Selected Properties for Sample (A) and Sample (B) In regard to the columns of Table 3, the density is reported in grams per cubic centimeter, the magnetic saturation is reported in . 1 micro testla cubic meter per kilogram, the coercive force (Hc) is reported in oersteds, the hardness is reported as a Vickers Hardness Number using a 30 kilogram load, and the porosity was ascertained per a visual inspection. The test methods used to determine the properties set forth in Table 3, as well as throughout the entire patent application, are described below. The method to determine density was according to ASTM Standard B311 -93(2002)el entitled "Test Method for Density Determination for Powder Metallurgy (P/M) Materials Containing Less Than Two Percent Porosity. The method used to determine the magnetic saturation was along the lines of ASTM Standard B886-03 entitled "Standard Test Methods for Determination of MAGNETIC Saturation (Ms) of Cemented Carbides. The method to determine coercive force was ASTM Standard B887-03 entitled "Standard Test Method for Determination of Coercivity (Hcs) for Cemented Carbides. The method to determine the Vickers hardness was along the lines of ASTM Standard E92- 82(2003)el entitled "Standard Test Method for VICKERS Hardness of Metallic Materials". The method used to determine the porosity was along the lines of ASTM Standard B276-91(2000) entitled "Standard Test Method for Apparent Porosity in Cemented Carbides". Example 2: [0046] Similar to Example 1, powder mixtures C through G were prepared, as given in Table 4 below. Table 4 - Starting Powder Mixtures for Samples C through G [0047] Cutting inserts were pressed from powder mixtures C to G in geometry CNMG120412-UN, then sintered (sinter-HIP 1505°C/85 min) and CVD coated to form a standard multilayer coating comprised of titanium carbonitride and alumina layers. All samples were coated equally. The resulting sintered bodies had the following properties as set forth in Table 5 below. Table 5 Selected Properties for Samples C through G [0048] These cutting inserts were subjected to deformation resistance turning tests under the following conditions: Workpiece material: 42CrMo4 (1.7225) - alloy steel Cutting speed: 500, 550m/min, from 550m/min in stages of 25m/min increasing up to failure of the insert due to plastic deformation because of thermal overloading. Cutting time: 15 sec. for each cutting speed Feed rate: 0.4 mm/rev. Cutting depth: 2.5 mm Coolant: none The results of these tests are set forth in Table 6 below. Table 6 Test Results for Examples C through G [0049] Further, CVD coated (same coatings as in Example 2) cutting inserts from powder mixtures C to G were subjected to a wear turning test under the following parameters: Workpiece material: 42CrMo4 (1.7225) - alloy steel Cutting speed: 320 and 340 m/min Cutting time: 2 min for each cutting speed Feed rate: 0.3 mm/rev. Cutting depth: 2.5 mm Coolant: none The results are set forth in Table 7 below that report the amount of flank wear in millimeters. Table 7 Results of Testing of Samples C through G [0050] Test pieces were pressed and sintered with powder mixtures D, C, F and G. These test pieces were subjected to a hot hardness test (Vickers hardness) under the following conditions: Test weight: 1000 grams Test temperatures: room temperature RT, 400, 600, 800 and 900°C The results of the hardness testing are set forth in Table 8 below. Table 8 Results of Vickers Hardness Testing for Samples D, C, F and G [0051 ] Just as with the hot hardness turning tests, the Vickers hardness (hot hardness) test shows for the sintered bodies according to the present invention a clearly increased resistance against plastic deformation at higher temperatures as compared to the prior art. [0052] The compositions of the solid solution carbide (SSC) phase of samples C, D, E and F were analyzed by scanning electron microscopy (SEM) with the assistance of EDAX. In samples D, E and F two different SSC-phases could be identified by optical microscopy, whereas sample C showed one single SSC-phase, only. Where two different SSC-phases were present, the darker one was richer in tungsten and lower in zirconium, as compared with the lighter one. The results of the above determination are reported in Table 9 below that presents the composition of the solid solution carbides (as sintered) in weight percent. Table 9 Compositions of Solid Solution Phases for Samples C, D, E and F Example 3 [0053] Similar to Example 1, powder mixtures H through K as given in Table 10 were prepared: Table 10 Starting Powder Mixtures for Samples H through K * Mixture of WC1 and WC2: 75% WC1, 25% WC2 as (W, Ti)C 50/50 From powder mixtures H, I, J and K (prior art), cutting inserts having the geometry CNMG120412-UN were manufactured, pressed, sintered/sinter-HIP (1505°C/85 min) and CVD coated. The resulting sintered bodies had the following properties as reported in Table 11. Table 11 Selected properties of Samples H through K [0054] These cutting inserts were subjected to hot hardness tests under the following conditions: Workpiece material: 42CrMo4 (1.7225) - alloy steel Cutting speed: increasing from 450m/min in stages of 25m/min until failure of the inserts due to plastic deformation because of thermal overloading. Cutting time: 15 sec. for each cutting speed Feed rate: 0.4 mm/rev. Cutting depth: 2.5 µm Coolant: none The results of these cutting tests are set forth in Table 12 below. Table 12 Results of Cutting Tests for Samples K through J A review of these test results show a tool life improvement between about 20 percent and about 67 percent. [0055] Further inserts made from mixtures H to K and CVD coated. These coated inserts were subjected to a wear turning test with increasing cutting speeds under the following parameters: Workpiece material: 42CrMo4 (1.7225) - alloy steel Cutting speed: 260, 300, 320 and 340 m/min Cutting time: 2 min each cutting speed Feed rate: 0.5 mm/rev. Cutting depth: 1.5 mm Coolant: none The results are set forth in Table 13. Table 13 Results of Cutting Tests for Coated Samples K through J Example 4: [0056] Powder mixtures L and M (prior art) were prepared according to the compositions given in Table 14 (the compositions are set forth in weight percent below: Table 14 Starting Powder Mixtures for Samples L and M as (Ta,Nb)C 70/30 as (W,Ti)C 50/50 Cutting inserts were pressed from powder mixtures L and M in geometry CNMG120412-UN, then sintered (sinter-HIP 1505°C/85 min) and CVD coated. The resulting sintered bodies had the following properties as reported in Table 15. In addition to the properties reported for the above examples, Table 15 also reports the depth of the cobalt-enriched SSC-free zone in micrometers and the volume percent of cubic carbides present except for tungsten carbide. Table 15 Selected Properties of Cutting Inserts of Samples L and M These cutting inserts were subjected to a toughness test (interrupted cutting test) with the following conditions: Workpiece material: Ck60 (1.1221) - carbon steel Cutting speed: 200 m/min Cutting depth: 2.5 mm Feed rate: 0.3, 0.4, 0.5 mm/rev., 100 impacts per feed rate. Coolant: none The feed was increased according to the mentioned increments until breakage occurred. Table 16 below sets forth the results of the toughness test. Table 16 Results of Toughness Test (Interrupted Cutting) for Samples L and M Additional cutting inserts were subjected to a deformation resistance turning test under following conditions: Workpiece material: 42CrMo4 (1.7225) - alloy steel Cutting speed: 400, 430, 460 m/min in stages of 30 m/min increasing up to failure of the insert due to plastic deformation because of thermal overloading Cutting time: 5 sec. for each cutting speed Cutting depth: 2.5 mm Feed rate: 0.3 mm/rev. Coolant: none Table 17 sets for the results of these deformation resistance turning tests. Table 17 Results of Deformation Resistance Turning Tests for Samples L and M [0057] Further cutting inserts were subjected to a wear turning test under the following conditions: Workpiece material: 42CrMo4 (1.7225) - alloy steel Cutting speed: 208 m/min Cutting depth: 2.5 mm Feed rate: 0.4 mm/rev. Coolant: none The results of the wear turning test are reported in Table 18 below. Table 18 Results of Wear Turning Tests for Samples L and M Example 5 [0058] Powder mixtures N and O were prepared having the compositions (in weight percent) given in Table 19. Table 19 Starting Powder Compositions for Samples N and O tas (W,Ti)C 50/50 From starting powder mixtures N and O, green compacts were pressed (TRS bars, ISO 3327, type B) and vacuum sintered at 1530°C/60min. The as sintered properties of Samples N and O are set forth in Table 20 below: Table 20 Selected Properties of Samples N and O [0059] An analysis of the sintered bodies revealed that Sample N shows two different coexisting solid solution phases that were identified by optical microscopy. By optical microscopy Sample O showed one single homogeneous solid solution phase. The compositional results of the analysis of Samples N and O are set forth in Table 21 below. Table 21 Composition of solid solution carbides (as sintered) in Samples N and O (components are set forth in weight percent) ) Thickness of SSCl-zone: about 80 to 120 µm [0060] The problems of the prior art mentioned above are overcome by the present invention which provides a sintered cemented carbide body having increased resistance to plastic deformation, comprising tungsten carbide, a binder phase comprising at least one metal of the iron group or an alloy thereof, and one or more solid solution phases each one of which comprising at least one of the carbides and carbonitrides of a combination of zirconium, niobium, and tungsten. Further, the problems of the prior art are overcome by the method of the present invention wherein this method is a method of producing said sintered cemented carbide body, according to the present invention, comprises the steps of: (a) providing a powder mixture comprising tungsten carbide, a binder metal powder comprising at least one metal of the iron group or an alloy thereof, and at least one of the carbides and carbonitrides of both, zirconium and niobium; (b) forming a green compact of said powder mixture; (c) vacuum sintering or sinter-HIP said green compact at a temperature of from 1400 to 1560°C; wherein in step (a) a powdered solid solution of the carbides or carbonitrides of zirconium and niobium is used to form said powder mixture. The sintered cemented carbide bodies of the present invention have increased resistance to plastic deformation, resulting in improved wear resistance and extended life time of cutting tools produced from said sintered cemented carbide bodies. Besides, a considerable minimization of porosity and sinter distortion as compared to prior art sintered cemented carbide bodies, is obtained by the present invention. [0061] There is also a considerable advantage of the method of the present invention which, according to a preferred embodiment thereof, uses a powdered solid solution of (Zr,Nb)C instead of the conventionally used single carbides ZrC and NbC. This advantage is due to the lower affinity of the solid solution of (Zr,Nb)C to oxygen that results in that neither a reducing sintering atmosphere is necessary nor a continuous control of the reducing force of the sinter atmosphere is necessary. [0062] The patents and other documents identified herein are hereby incorporated by reference herein. Other embodiments of the invention will be apparent to those skilled in the art from a consideration of the specification or a practice of the invention disclosed herein. It is intended that the specification and examples are illustrative only and are not intended to be limiting on the scope of the invention. WE CLAIM 1. A sintered cemented carbide body having increased resistance to plastic deformation, comprising tungsten carbide, a binder phase comprising at least one metal of the iron group or an alloy thereof, and a solid solution phase comprising at least one of the carbides and carbonitrides of a combination of zirconium, niobium, and tungsten, wherein said body has a mass ratio Nb/(Zr+Nb) of at least 0.5, and wherein said solid solution phase is the sole solid solution phase of said body and (i) consists of a carbide or carbonitride of a combination of zirconium, niobium and tungsten or (ii) comprises a carbide or carbonitride of a combination of zirconium, niobium and tungsten, and at least one carbide, nitride or carbonitride of one or more of titanium, hafnium, vanadium, tantalum, chromium, and molybdenum. 2. The body of claim 1, wherein said at least one carbide, nitride or carbonitride is of one or more of titanium, tantalum and hafnium. 3. The body of claims 1 or 2, wherein said binder phase comprises cobalt, a CoNi-alloy or a CoNiFe-alloy. 4. The body of claim 3, wherein said binder phase additionally comprises one or more of chromium and tungsten. - 5. The body of any one of claims 1 to 4, wherein said binder phase comprises 3 to 15% of the total weight of said body. 6. The body of any one of claims 1 to 5, wherein the total contents of a carbide or carbonitride of a combination of zirconium, niobium and tungsten of said solid solution phase comprise 1 to 15% of the total weight of said body. 7. The body of any one of claims 1 to 6, wherein the total content of the elements titanium, hafnium, vanadium, tantalum, chromium, and molybdenum does not exceed 8% of- the total weight of said body. 8. The body of claim 7 wherein titanium comprises 1 to 8 % of the total weight of said body. 9. The body of claim 7, wherein tantalum comprises 1 to 7 % of the total weight of said body. 10. The body of claim 7 wherein hafnium comprises 1 to 4 % of the total weight of said body. 11. The body of any one of claims 1 to 10, wherein the mass ratio Nb/(Zr+Nb) is 0.6 or more. 12. The body of any one of claims 1 to 11, wherein said body comprises at least one of said nitrides or carbonitrides and comprises an outermost zone being free of any solid solution phase, but binder enriched, up to a depth of about 50 µm from an uncoated surface of said body. 13. The body of claim 12 having, underneath of said binder enriched zone, one single solid solution phase being homogeneous throughout said body except said binder enriched zone. 14. The body of any one of claims 1 to 13, wherein one or more wear resistant PVD- or CVD-layers are coated over a surface of said body. 15. A method of producing the sintered cemented carbide body of any one of claims 1 to 13 comprising the steps of (a) providing a powder mixture comprising tungsten carbide, a binder metal powder comprising at least one metal of the iron group or an alloy thereof, and at least one of the carbides and carbonitrides of both, zirconium and niobium; (b) forming a green compact of said powder mixture; (c) vacuum sintering or sinter-HIP said green compact at a temperature of from 1400 to 1560°C; characterized in that in step (a) a powdered solid solution of the carbides or carbonitrides of zirconium and niobium having a mass ratio Nb/(Zr + Nb) of at least 0.5 is used to form said powder mixture. 16. The method of claim 15, wherein a powdered solid solution of a carbide or carbonitride of a combination of zirconium and niobium having a mass ratio Nb/(Zr + Nb) of 0.6 or more is used. 17. The method of claims 15 or 16, wherein cobalt, a powdered CoNi-alloy or a t > powdered CoNiFe-alloy is used as said binder metal powder. 18. The method of claim 17, wherein said binder metal powder additionally comprises at least one of chromium and tungsten. 19. The method of any one of claims 15 to 18, wherein said binder metal powder comprises 3 to 15% of the total weight of said powder mixture. 20. The method of any one of claims 15 to 19, wherein said powder mixture additionally comprises at least one carbide, nitride or carbonitride of one or more of titanium, hafnium, vanadium, tantalum, chromium, and molybdenum. 21. The method of any one of claims 15 to 20, wherein said powdered solid solution of a carbide or carbonitride of a combination of zirconium and niobium comprises 1 to 15% of the total weight of said powder mixture. 22. The method of any one of claims 15 to 21, wherein said powder mixture comprises at least one of the elements titanium, hafnium, vanadium, tantalum, chromium and molybdenum in an amount of 1 to 8 % of the total weight of said powder mixture. A sintered cemented carbide body (e.g., a cutting tool) and a method of making the same. The sintered cemented carbide body includes tungsten carbide, a binder phase of at least one metal of the iron group or an alloy thereof, and one or more solid solution phases. Each one of the solid solution phases has at least one of the carbides and carbonitrides of a combination of zirconium, niobium, and tungsten. The method includes the steps of providing a powder mixture that contains tungsten carbide, a binder metal powder comprising at least one metal of the iron group or an alloy thereof, and at least one of the carbides and carbonitrides of both zirconium and niobium including a powder of the carbides or carbonitrides of zirconium and niobium, forming a green compact of said powder mixture, and vacuum sintering or sinter-HIP said green compact at a temperature of from 1400 to 1560°C.

Full Text

CEMENTED CARBIDE BODY CONTAINING ZIRCONIUM AND NIOBIUM
AND METHOD OF MAKING THE SAME
BACKGROUND OF THE INVENTION
[0001] The present invention provides sintered cemented carbide bodies
having increased resistance to plastic deformation comprising tungsten carbide
(WC), a binder metal phase and one or more solid solution phases comprising at
least one of the carbides, nitrides and carbonitrides of at least one of the elements
of groups IVb, Vb and VIb of the Periodic Table of Elements. The present
invention also provides a method for producing these sintered cemented carbide
bodies. These sintered cemented carbide bodies are useful in the manufacture of
cutting tools, and especially indexable cutting inserts for the machining of steel
and other metals or metal alloys.
[0002] Sintered cemented carbide bodies and powder metallurgical
methods for the manufacture thereof are known, for example, from U.S. Patent
Re. 34,180 to Nemeth et al.. While cobalt has originally been used as a binder
metal for the main constituent, tungsten carbide, a cobalt-nickel-iron alloy as
taught by U.S Patent No. 6,024,776 turned out to be especially useful as a binder
phase for tungsten carbide and other carbides, nitrides and carbonitrides of at least
one of the elements titanium, zirconium, hafnium, vanadium, niobium, tantalum,
chromium, molybdenum and tungsten, respectively.
[0003] Numerous attempts have been made in order to modify the
properties or characteristics of the sintered cemented carbide bodies prepared by
powder metallurgical methods. These properties include, but are not limited to,
hardness, wear resistance, plastic deformation at increased temperatures, density,
magnetic properties, resistance to flank wear and resistance to cratering. In order
to provide cutting tools having improved wear properties at high cutting speeds, it
is known, for example, that the sintered cemented carbide bodies should have
increased contents of titanium or tantalum and niobium. On the other hand,
however, it is known that increasing contents of titanium or tantalum or niobium
result in a noticeable reduction of strength as they form solid solution carbides
with tungsten carbide, since the amount of tungsten carbide-phase which provides
for the maximum strength in a sintered cemented carbide body decreases with the
formation of solid solution carbides.
[0004] Also well known to those skilled in the art is the fact that the
addition of zirconium and hafnium increases the strength of sintered cemented
carbide bodies both at room temperature and at higher temperatures. However, the
increase in strength is combined with lower hardness and decreased wear
resistance. In addition, a disadvantage of the addition of zirconium is its high
affinity to oxygen and its poor wettability which impedes the sintering process
used in the preparation of the sintered cemented carbide body.
[0005] U.S. Patents Nos. 5,643,658 and 5,503,925, both hereby
incorporated by reference herein, aim at improving hot hardness and wear
resistance at higher temperatures of sintered cemented carbide bodies by means of
adding zirconium and/or hafnium carbides, nitrides and carbonitrides to the
powder mixture of tungsten carbide and a binder metal of the iron family. As a
result thereof, the hard phases of at least one of zirconium and hafnium coexist
with other hard phases of metals of groups IVb, Vb and VIb, but excluding
zirconium and hafnium, with said hard phases forming, in each case, solid
solutions with tungsten carbide. Due to the high affinity of zirconium for oxygen,
either the starting powder materials have to be extremely low in oxygen, or the
oxygen content has to be controlled by using a reducing sintering atmosphere.
[0006] JP-A2-2002-356734, published on December 13, 2002, discloses
a sintered cemented carbide body comprising WC, a binder phase consisting of at
least one metal of the iron group, and one or more solid solution phases, wherein
one of said solid solution phases comprises Zr and Nb while all solid solution
phases other than the first one comprise at least one of the elements Ti, V, Cr, Mo,
Ta and W, but must not comprise Zr and Nb. According to this Japanese patent
document, the best cutting results are achieved at a tantalum content of less than
1% by weight of the total composition, calculated as TaC.
[0007] The present invention aims at achieving new sintered cemented
carbide bodies having increased resistance to plastic deformation at increased
temperatures and, as a result thereof, having increased wear resistance. Besides,
the present invention aims at providing a powder metallurgical method of
producing said sintered cemented carbide bodies. More specifically, it is an object
of the present invention to provide a sintered cemented carbide body having at
least two co-existing solid solution phases containing zirconium and niobium or
one single homogenous solid solution phase containing zirconium and niobium.
[0008] Another object of the present invention consists in providing a
method of producing said sintered cemented carbide body comprising the step of
providing a powder mixture which upon sintering provides at least two co-existing
solid solution phases or one single homogenous solid solution phase containing, in
each case, zirconium and niobium, and providing improved sintering activity and
wettability with hard constituents of elements of groups IVb, Vb, and VIb of the
periodic table of elements.
SUMMARY OF THE INVENTION
[0009] In one form thereof, the invention is a sintered cemented carbide
body that has increased resistance to plastic deformation. The sintered cemented
carbide body includes tungsten carbide, and a binder phase that includes at least
one metal of the iron group or an alloy thereof, and one or more solid solution
phases wherein each one of the solid solution phases comprises at least one of the
carbides and carbonitrides of a combination of zirconium, niobium, and tungsten.
[0010] In another form thereof, the invention is a method of producing a
sintered cemented carbide body comprising the steps of: providing a powder
mixture comprising tungsten carbide, a binder metal powder comprising at least
one metal of the iron group or an alloy thereof, and at least one of the carbides and
carbonitrides of both zirconium and niobium; forming a green compact of said
powder mixture; and vacuum sintering or sinter-HIP said green compact at a
temperature of from 1400 to 1560 °C, wherein a powdered solid solution of the
carbides or carbonitrides of zirconium and niobium is used to form said powder
mixture.
[0011] In yet another form thereof, the invention is a cutting tool that
comprises a body that includes a rake face and a flank face wherein the rake face
and the flank face intersect to form a cutting edge at the intersection thereof. The
body comprises tungsten carbide, a binder phase comprising at least one metal of
the iron group or an alloy thereof, and one or more solid solution phases each one
of which comprising at least one of the carbides and carbonitrides of a
combination of zirconium, niobium, and tungsten.
[0012] In still another form thereof, the invention is a sintered cemented
carbide body that has increased resistance to plastic deformation. The sintered
cemented carbide body includes tungsten carbide, and a binder phase that includes
at least one metal of the iron group or an alloy thereof, and one or more solid
solution phases wherein each one of the solid solution phases comprises at least
one of the carbides and carbonitrides of a combination consisting of zirconium,
niobium, and tungsten
BRIEF DESCRIPTION OF THEACCOMPANYING DRAWINGS
[0013] The following is a brief description of the drawings that form a
part of this patent application:
[0014] FIG. 1 is an isometric view of a cutting tool of the present
invention wherein the cutting tool is a CNMG style of cutting tool;
[0015] FIGS. 2A is a photomicrograph that shows the unetched
microstructure of Sample (A), which is a sintered cemented carbide body, at
1,500-fold magnification (10 micrometer scale) wherein Sample (A) was
produced according to the present invention as disclosed hereinafter, and Sample
(A) has a porosity of [0016] FIG. 2B is a photomicrograph that shows the unetched
microstructures of Sample (B), which is a sintered cemented carbide body, at
1,500-fold magnification (10 micrometer scale) wherein Sample (B) was
produced according to a conventional process as disclosed hereinafter, and
Sample (B) has a residual porosity of A08 as shown in FIG. 2B;
[0017] FIG. 3A is a photomicrograph of a sintered bending strength test
rod, in cross section, which was made according to the present invention as
described hereinafter and does not show sinter distortion;
[0018] FIG. 3B is a photomicrograph of a sintered bending strength test
rod, in cross section, which was made in a conventional fashion as described
hereinafter and very clearly shows a sinter distortion;
[0019] FIG. 4 is a photomicrograph (20 micrometer scale) showing the
unetched microstructure of an embodiment of the sintered cemented carbide body
of the present invention wherein there is shown a binder enriched surface zone
free of solid solution carbide wherein the binder enriched surface zone begins at
and extends inwardly from the surface of the substrate and one single
homogeneous solid solution phase (MC); and
[0020] FIG. 5 is a photomicrograph (20 micrometer scale) showing the
unetched microstructure of an other embodiment of the sintered cemented carbide
body of the present invention wherein there is shown a binder enriched surface
zone free of solid solution carbide wherein the binder enriched surface zone
begins at and extends inwardly from the surface of the substrate and underneath
the binder enriched surface zone free of solid solution phase there is shown a zone
in which a single phase MC1 exists (MC1 is light brown), and underneath the
MC1 zone there is a zone that has two coexisting solid solution carbide phases
wherein one solid solution phase is MC land it is light brown and the other solid
solution phase is MC 2 and it is dark brown.
DETAILED DESCRIPTION OF SPECIFIC EMBODIMENTS
[0021] Referring to FIG. 1, there is shown a cutting tool, i.e., a sintered
cemented carbide body, generally designated as 20. Cutting tool 20 has a rake
face 22 and flank faces 24. There is a cutting edge 26 at the intersection of the
rake face 22 and the flank faces 24. The cutting tool 20 further contains an
aperture 28 by which the cutting tool 20 is secured to a tool holder. The style of
cutting tool shown in FIG. 5 is a CNMG style of cutting tool. The illustration in
FIG. 1 of a CNMG style of cutting tool should not be considered to limit the scope
of the invention. It should be appreciated that the present invention is a new
cemented carbide material that can be used as a cutting tool wherein the geometry
of the cutting tool can be any known cutting tool geometry.
[0022] In regard to the composition of the cutting tool, i.e., a sintered
cemented carbide body, the composition contains tungsten carbide and a binder,
as well as one or more solid solution phases that comprise the carbides and/or the
carbonitrides of a combination of zirconium, niobium and tungsten as exemplified
by the formulae (Zr,Nb,W)C and/or (Zr,Nb,W)CN. In one preferred embodiment
of the composition, just one of the solid solution phases consists of a carbide or
carbonitride of a combination of zirconium, niobium and tungsten. In another
preferred embodiment of the composition, the solid solution phase consisting of a
carbide or carbonitride of a combination of zirconium, niobium and tungsten is the
sole solid solution phase of the body wherein no other element such as titanium,
hafnium, vanadium, tantalum, chromium, and molybdenum is present in said solid
solution phase.
[0023] In yet another preferred embodiment of the composition, one of
the solid solution phases comprises a carbide or carbonitride of a combination of
zirconium, niobium and tungsten and at least one carbide, nitride or carbonitride
of one or more of titanium, hafnium, vanadium, tantalum, chromium, and
molybdenum wherein the solid solution phase may be either the sole solid
solution phase of the body or one of two or more different solid solution phases.
More specifically, there can be two or more different solid solution phases that are
present with each solid solution phase comprising a carbide or carbonitride of a
combination of zirconium, niobium and tungsten, and at least one carbide, nitride
or carbonitride of one or more of titanium, hafnium, vanadium, tantalum,
chromium and molybdenum, respectively. In those cases where the solid solution
phase comprises a carbide or carbonitride of a combination of zirconium, niobium
and tungsten, and at least one carbide, nitride or carbonitride comprising one or
more other metals, it is even more preferred that said at least one other metal is
one or more of titanium, tantalum and hafnium.
[0024] According to the present invention, the binder alloy preferably
comprises cobalt, a CoNi-alloy or a CoNiFe-alloy, each of which may or may not
contain additional alloying elements such as chromium and tungsten. The binder
alloy preferably comprises between about 3 weight percent to about to 15 weight
percent of the total body.
[0025] Preferably, the total contents of a carbide or carbonitride of a
combination of zirconium, niobium and tungsten of the one or more solid solution
phase(s) comprise between about 1 weight percent and about 15 weight percent of
the total body. Also preferred are those embodiments of the present invention
wherein the total content of the elements titanium, hafnium, vanadium, tantalum,
chromium and molybdenum does not exceed about 8 weight percent of the total
body. According to especially preferred embodiments of the present invention,
titanium comprises between about 1 weight percent and about 8 weight percent of
the total body, tantalum comprises between about 1 weight percent and about 7
weight percent of the total body, and hafnium comprises between about 1 weight
percent and about 4 weight percent of the total body.
[0026] If the cemented carbide body has a mass ratio Nb/(Zr + Nb) of
greater than about 0.5, and more preferably greater than or equal to about 0.6, the
formation of a single homogeneous solid solution phase or the formation of two or
more coexisting solid solution phases within the sintered cemented carbide body
is remarkably increased.
[0027] According to still another aspect of the present invention, the
sintered cemented carbide body comprises at least one of said nitrides or
carbonitrides and comprises an outermost zone being free of any solid solution
phase but binder enriched up to a depth of about 50 micrometers (µm) from an
uncoated surface of said body. Embodiments of this type are shown in FIGS. 4
and 5 hereof.
[0028] As is acknowledged by those having ordinary skill in the art,
binder enrichment and formation of a surface zone free of solid solution carbide
(SSC) is induced during sintering once at least one nitride or carbonitride is
present in the starting powder mixture. Due to the formation of free nitrogen
during sintering, diffusion of binder metal from the bulk towards the surface, and
diffusion of solid solution phase from the surface zone towards the bulk will take
place, resulting in a binder enriched surface zone being free of any solid solution
phase. Due to these diffusion processes, two or more coexisting different solid
solution phases showing a concentration gradient between the surface and the
center of the body are formed underneath of the binder enriched zone, according
to a still more preferred embodiment of the present invention. In those cases,
however, where just one single solution phase being homogeneous throughout the
body is present, said one single and homogeneous solid solution phase will be
located underneath of the binder enriched zone such that the single solid solution
phase is homogeneous throughout said body, except in the binder enriched zone.
[0029] According to still other preferred embodiments of the present
invention, one or more wear resistant layers deposited according to well-known
physical vapor deposition (PVD) or chemical vapor deposition (CVD) methods
are coated over a surface of the sintered cemented carbide body. Preferably, these
wear resistant coatings comprise one or more of the carbides, nitrides,
carbonitrides, oxides or borides of a metal of the groups IVb, Vb and Ylb of the
periodic table of elements, and alumina.
[0030] Referring to the method aspects of the present invention,
according to a preferred embodiment of the method of the present invention, a
solid solution of a carbide or carbonitride of a combination of zirconium and
niobium having a mass ratio Nb/(Zr + Nb) of greater than about 0.5, and
preferably greater than or equal to about 0.6 or more, is used as the powdered
solid solution of a carbide or carbonitride of a combination of zirconium and
niobium. The powdered solid solution of a carbide or carbonitride of a
combination of zirconium, niobium and tungsten preferably comprises between
about 1 weight percent and about 15 weight percent of the total powder mixture.
[0031] Preferably, cobalt powder, powders of cobalt and nickel or
powders of cobalt and nickel and iron or powders of a cobalt-nickel alloy or
powders of a cobalt-nickel-iron alloy are used as the binder metal powders, within
the method of the present invention. Optionally, the binder metal powders may
include additional elements, preferably one or more of chromium and tungsten.
Preferably, the binder metal powder comprises between about 3 weight percent
and about 15 weight percent of the total powder mixture.
[0032] According to still another embodiment of the present invention,
the powder mixture additionally comprises at least one carbide, nitride or
carbonitride of one or more of titanium, hafnium, vanadium, tantalum, chromium,
and molybdenum. Preferably, the powder mixture comprises at least one of the
elements titanium, hafnium, vanadium, tantalum, chromium and molybdenum in
an amount of between about 1 weight percent and about 8 weight percent of the
total powder mixture.
[0033] The present inventors have surprisingly found that due to the
addition of zirconium and niobium in the form of a powdered solid solution of a
carbide or carbonitride of a combination of zirconium and niobium to the starting
powder mixture, instead of using zirconium carbide plus niobium carbide or
zirconium carbonitride plus niobium carbonitride, each individually, either one
single homogeneous solid solution phase comprising the carbides and/or the
carbonitrides of a combination of zirconium, niobium and tungsten, or two or
more coexisting solid solution phases comprising the carbides and/or the
carbonitrides of a combination of zirconium, niobium and tungsten, and at least
one carbide, nitride or carbonitride of one or more of titanium, hafnium,
vanadium, tantalum, chromium and molybdenum, depending on the compounds
added to the starting powder mixture, are formed during sintering according to the
method of the present invention.
[0034] Contrary to the documents mentioned herein above, upon
sintering all elements added to the starting powder mixture are dissolved in each
one of the coexisting solid solution phases, according to the present invention.
For example, up to about 65 weight percent tungsten, up to about 75 weight
percent niobium, up to about 60 weight percent zirconium, up to about 20 weight
percent titanium, up to about 15 weight percent tantalum, and up to about 20
weight percent hafnium can be dissolved in the coexisting solid solution phases.
[0035] Another advantage of the use of a powdered solid solution of a
carbide or carbonitride of a combination of zirconium and niobium as part of the
starting powder mixture according to the present invention is the fact that
tantalum can be added to the composition for improving binder phase distribution
and toughness in an amount of about 1 weight percent or more of the total starting
powder mixture.
[0036] The best results in terms of homogeneity of the solid solution
phase(s) formed according to the present invention have been obtained if a
powdered solid solution of a carbide or carbonitride of a combination of
zirconium and niobium having a ratio of about 40 weight percent zirconium
carbide and about 60 weight percent niobium carbide was added to the starting
powder mixture.
[0037] Referring to FIG. 2A and FIG. 2B, each one of these figures is a
photomicrograph at 1500X (each photomicrograph as a 10 micrometer scale) that
shows the unetched microstructures of two samples; namely, Sample (A) and
Sample (B), respectively. Sample (A) was produced according to the present
invention using (Zr,Nb)C in the starting powder mixture and whereas Sample (B)
was conventionally made by using individual carbides; namely, ZrC and NbC
instead of (Zr,Nb)C in the starting powder mixture. FIG. 2A shows that Sample
(A) has a porosity of less than A02 and FIG. 2B shows that Sample (B) has a
porosity of A08. In addition, as can be seen in FIG. 2A, the microstructure of
Sample (A) obtained by using the (Zr,Nb)C solid solution in the starting powder is
much more homogeneous in terms of porosity as compared with the
microstructure (see FIG. 2B) of Sample (B), which is the conventionally prepared
sintered cemented carbide body using ZrC + NbC as part of the starting powder
mixture.
[0038] Referring to FIG. 3A and FIG. 3B, these figures are
photomicrographs of sintered bending strength test rods wherein each is in cross
section. FIG. 3B shows the microstructure of Sample (B) that is made in a
conventional fashion using ZrC and NbC in the starting powder mixture wherein
there is a sinter distortion that can be seen very clearly. FIG. 3 A shows the
microstructure of Sample (A) that was made according to the present invention
using a solid solution carbide of zirconium and niobium (Zr,Nb)C wherein FIG.
3A does not show sinter distortion. This comparison shows that, with respect to
sinter distortion, Sample (A) is much better with the present invention than with
the conventional sample (B).
[0039] As indicated earlier, a further advantage of using a powdered
solid solution of a carbide or carbonitride of a combination of zirconium and
niobium as part of the starting powder mixture consists in the lower affinity to
oxygen, as compared to conventional methods of producing sintered cemented
carbide bodies, whereby it is not necessary to have a reducing sintering
atmosphere. Due to the avoidance of any controlling and monitoring of the
reducing quality of the sintering atmosphere, sintering becomes easier and less
expensive according to the present invention as compared to the prior art.
[0040] Referring to FIG. 4, FIG. 4 is a photomicrograph of an
embodiment of the sintered cemented carbide body of the present invention
wherein there is shown a binder enriched surface zone free of solid solution
carbide and one single homogeneous solid solution phase (MC). FIG. 4 shows
that the present invention allows the production of sintered cemented carbide
bodies having one single homogeneous solid solution phase.
[0041] Referring to FIG. 5, FIG. 5 is a photomicrograph of an other
embodiment of the sintered cemented carbide body of the present invention
wherein there is shown a binder enriched surface zone free of solid solution
carbide. Underneath the binder enriched surface zone free of solid solution phase
there is shown a zone in which a solid solution phase MC1 exists. MC1 is light
brown. Underneath the zone containing only MC1 solid solution phase, there is a
zone that contains two coexisting solid solution phases. One solid solution phase
is MC land it is light brown. The other solid solution phase is MC 2 and it is dark
brown. FIG. 5 shows that the present invention allows the production of sintered
cemented carbide bodies having different coexisting solid solution phases (MC1;
(MC1+MC2)) visible by optical microscopy located underneath an outermost
binder enriched zone being free of solid solution phase.
[0042] Further details of the invention shall be described through the
following examples. Table 1 sets forth the raw materials that were used in the
examples that are set forth hereinafter.
Table 1 - Raw Materials Used for the Examples
[0043] In regard to the processing of the examples, for each one of the
examples the specified raw materials were wet milled in an attritor for 10 hours
and dried. Green compacts were pressed of the resulting powder mixtures and
sintered according to the sintering conditions stated in the examples. In the
examples the percentages are given in weight percent unless otherwise stated.
[0044] As is well known to those skilled in the art of powder metallurgy,
the element pairs tantalum and niobium as well as zirconium and hafnium in most
cases of occurrence are associated with each other such that a complete separation
often is difficult to obtain. This is why in commercial applications, small amounts
or traces of niobium will be present in tantalum, and vice versa, and small
amounts or traces of zirconium will be present in hafnium, and vice versa. This
also is valid for the present disclosure, whenever these elements or compounds
thereof are mentioned by their names or chemical formulae.
Example 1:
[0045] Powder mixtures A and B having the compositions (weight
percent) given in Table 2 were prepared. TRS bars (ISO 3327, type B) were
pressed from these powder mixtures to form green compacts. The compacts were
sinter-HIPped at temperatures between 1430 and 1520 degrees Centigrade. The
resulting sintered cemented carbide bodies were metallurgically tested. The results
of these tests are shown in FIGS. 2A and 2B and FIGS. 3A and 3B. Sample A
(according to the present invention) shows a porosity of whereas sample B (prior art comparative example) shows a high residual porosity
(see FIG. 2B) and strong sinter distortion (see FIG. 3B).
Table 2 - Starting Powder Mixtures for Samples (A) and (B) (weight percent)

The resulting sintered cemented carbide bodies of Sample (A) and Sample (B) had
the following properties as reported in Table 3 below.
Table 3 Selected Properties for Sample (A) and Sample (B)

In regard to the columns of Table 3, the density is reported in grams per cubic
centimeter, the magnetic saturation is reported in . 1 micro testla cubic meter per
kilogram, the coercive force (Hc) is reported in oersteds, the hardness is reported
as a Vickers Hardness Number using a 30 kilogram load, and the porosity was
ascertained per a visual inspection. The test methods used to determine the
properties set forth in Table 3, as well as throughout the entire patent application,
are described below. The method to determine density was according to ASTM
Standard B311 -93(2002)el entitled "Test Method for Density Determination for
Powder Metallurgy (P/M) Materials Containing Less Than Two Percent Porosity.
The method used to determine the magnetic saturation was along the lines of
ASTM Standard B886-03 entitled "Standard Test Methods for Determination of
MAGNETIC Saturation (Ms) of Cemented Carbides. The method to determine
coercive force was ASTM Standard B887-03 entitled "Standard Test Method for
Determination of Coercivity (Hcs) for Cemented Carbides. The method to
determine the Vickers hardness was along the lines of ASTM Standard E92-
82(2003)el entitled "Standard Test Method for VICKERS Hardness of Metallic
Materials". The method used to determine the porosity was along the lines of
ASTM Standard B276-91(2000) entitled "Standard Test Method for Apparent
Porosity in Cemented Carbides".
Example 2:
[0046] Similar to Example 1, powder mixtures C through G were prepared, as
given in Table 4 below.
Table 4 - Starting Powder Mixtures for Samples C through G

[0047] Cutting inserts were pressed from powder mixtures C to G in geometry
CNMG120412-UN, then sintered (sinter-HIP 1505°C/85 min) and CVD coated to
form a standard multilayer coating comprised of titanium carbonitride and
alumina layers. All samples were coated equally. The resulting sintered bodies
had the following properties as set forth in Table 5 below.
Table 5
Selected Properties for Samples C through G

[0048] These cutting inserts were subjected to deformation resistance
turning tests under the following conditions:
Workpiece material: 42CrMo4 (1.7225) - alloy steel
Cutting speed: 500, 550m/min, from 550m/min in stages of
25m/min increasing up to failure of the insert due to
plastic deformation because of thermal overloading.
Cutting time: 15 sec. for each cutting speed
Feed rate: 0.4 mm/rev.
Cutting depth: 2.5 mm
Coolant: none
The results of these tests are set forth in Table 6 below.
Table 6
Test Results for Examples C through G

[0049] Further, CVD coated (same coatings as in Example 2) cutting
inserts from powder mixtures C to G were subjected to a wear turning test under
the following parameters:
Workpiece material: 42CrMo4 (1.7225) - alloy steel
Cutting speed: 320 and 340 m/min
Cutting time: 2 min for each cutting speed
Feed rate: 0.3 mm/rev.
Cutting depth: 2.5 mm
Coolant: none
The results are set forth in Table 7 below that report the amount of flank wear in
millimeters.
Table 7
Results of Testing of Samples C through G

[0050] Test pieces were pressed and sintered with powder mixtures D, C,
F and G. These test pieces were subjected to a hot hardness test (Vickers
hardness) under the following conditions:
Test weight: 1000 grams
Test temperatures: room temperature RT, 400, 600, 800 and 900°C
The results of the hardness testing are set forth in Table 8 below.
Table 8
Results of Vickers Hardness Testing for Samples D, C, F and G

[0051 ] Just as with the hot hardness turning tests, the Vickers hardness
(hot hardness) test shows for the sintered bodies according to the present
invention a clearly increased resistance against plastic deformation at higher
temperatures as compared to the prior art.
[0052] The compositions of the solid solution carbide (SSC) phase of
samples C, D, E and F were analyzed by scanning electron microscopy (SEM)
with the assistance of EDAX. In samples D, E and F two different SSC-phases
could be identified by optical microscopy, whereas sample C showed one single
SSC-phase, only. Where two different SSC-phases were present, the darker one
was richer in tungsten and lower in zirconium, as compared with the lighter one.
The results of the above determination are reported in Table 9 below that presents
the composition of the solid solution carbides (as sintered) in weight percent.
Table 9
Compositions of Solid Solution Phases for Samples C, D, E and F

Example 3
[0053] Similar to Example 1, powder mixtures H through K as given in
Table 10 were prepared:
Table 10
Starting Powder Mixtures for Samples H through K

* Mixture of WC1 and WC2: 75% WC1, 25% WC2
as (W, Ti)C 50/50
From powder mixtures H, I, J and K (prior art), cutting inserts having the
geometry CNMG120412-UN were manufactured, pressed, sintered/sinter-HIP
(1505°C/85 min) and CVD coated. The resulting sintered bodies had the
following properties as reported in Table 11.
Table 11
Selected properties of Samples H through K

[0054] These cutting inserts were subjected to hot hardness tests under
the following conditions:
Workpiece material: 42CrMo4 (1.7225) - alloy steel
Cutting speed: increasing from 450m/min in stages of 25m/min
until failure of the inserts due to plastic deformation
because of thermal overloading.
Cutting time: 15 sec. for each cutting speed
Feed rate: 0.4 mm/rev.
Cutting depth: 2.5 µm
Coolant: none
The results of these cutting tests are set forth in Table 12 below.
Table 12
Results of Cutting Tests for Samples K through J

A review of these test results show a tool life improvement between about 20
percent and about 67 percent.
[0055] Further inserts made from mixtures H to K and CVD coated.
These coated inserts were subjected to a wear turning test with increasing cutting
speeds under the following parameters:
Workpiece material: 42CrMo4 (1.7225) - alloy steel
Cutting speed: 260, 300, 320 and 340 m/min
Cutting time: 2 min each cutting speed
Feed rate: 0.5 mm/rev.
Cutting depth: 1.5 mm
Coolant: none
The results are set forth in Table 13.
Table 13
Results of Cutting Tests for Coated Samples K through J

Example 4:
[0056] Powder mixtures L and M (prior art) were prepared according to
the compositions given in Table 14 (the compositions are set forth in weight
percent below:
Table 14
Starting Powder Mixtures for Samples L and M

*as (Ta,Nb)C 70/30
as (W,Ti)C 50/50
Cutting inserts were pressed from powder mixtures L and M in geometry
CNMG120412-UN, then sintered (sinter-HIP 1505°C/85 min) and CVD coated.
The resulting sintered bodies had the following properties as reported in Table 15.
In addition to the properties reported for the above examples, Table 15 also
reports the depth of the cobalt-enriched SSC-free zone in micrometers and the
volume percent of cubic carbides present except for tungsten carbide.
Table 15
Selected Properties of Cutting Inserts of Samples L and M

These cutting inserts were subjected to a toughness test (interrupted cutting test)
with the following conditions:
Workpiece material: Ck60 (1.1221) - carbon steel
Cutting speed: 200 m/min
Cutting depth: 2.5 mm
Feed rate: 0.3, 0.4, 0.5 mm/rev., 100 impacts per feed rate.
Coolant: none
The feed was increased according to the mentioned increments until breakage
occurred. Table 16 below sets forth the results of the toughness test.
Table 16
Results of Toughness Test (Interrupted Cutting) for Samples L and M

Additional cutting inserts were subjected to a deformation resistance turning test
under following conditions:
Workpiece material: 42CrMo4 (1.7225) - alloy steel
Cutting speed: 400, 430, 460 m/min in stages of 30 m/min
increasing up to failure of the insert due to
plastic deformation because of thermal
overloading
Cutting time: 5 sec. for each cutting speed
Cutting depth: 2.5 mm
Feed rate: 0.3 mm/rev.
Coolant: none
Table 17 sets for the results of these deformation resistance turning tests.
Table 17
Results of Deformation Resistance Turning Tests for Samples L and M

[0057] Further cutting inserts were subjected to a wear turning test under
the following conditions:
Workpiece material: 42CrMo4 (1.7225) - alloy steel
Cutting speed: 208 m/min
Cutting depth: 2.5 mm
Feed rate: 0.4 mm/rev.
Coolant: none
The results of the wear turning test are reported in Table 18 below.
Table 18
Results of Wear Turning Tests for Samples L and M

Example 5
[0058] Powder mixtures N and O were prepared having the compositions
(in weight percent) given in Table 19.
Table 19
Starting Powder Compositions for Samples N and O

tas (W,Ti)C 50/50
From starting powder mixtures N and O, green compacts were pressed (TRS bars,
ISO 3327, type B) and vacuum sintered at 1530°C/60min. The as sintered
properties of Samples N and O are set forth in Table 20 below:
Table 20
Selected Properties of Samples N and O

[0059] An analysis of the sintered bodies revealed that Sample N shows
two different coexisting solid solution phases that were identified by optical
microscopy. By optical microscopy Sample O showed one single homogeneous
solid solution phase. The compositional results of the analysis of Samples N and
O are set forth in Table 21 below.
Table 21
Composition of solid solution carbides (as sintered) in Samples N and O
(components are set forth in weight percent)

*) Thickness of SSCl-zone: about 80 to 120 µm
[0060] The problems of the prior art mentioned above are overcome by
the present invention which provides a sintered cemented carbide body having
increased resistance to plastic deformation, comprising tungsten carbide, a binder
phase comprising at least one metal of the iron group or an alloy thereof, and one
or more solid solution phases each one of which comprising at least one of the
carbides and carbonitrides of a combination of zirconium, niobium, and tungsten.
Further, the problems of the prior art are overcome by the method of the present
invention wherein this method is a method of producing said sintered cemented
carbide body, according to the present invention, comprises the steps of:
(a) providing a powder mixture comprising tungsten carbide, a binder
metal powder comprising at least one metal of the iron group or an
alloy thereof, and at least one of the carbides and carbonitrides of both,
zirconium and niobium;
(b) forming a green compact of said powder mixture;
(c) vacuum sintering or sinter-HIP said green compact at a temperature of
from 1400 to 1560°C;
wherein in step (a) a powdered solid solution of the carbides or carbonitrides of
zirconium and niobium is used to form said powder mixture. The sintered
cemented carbide bodies of the present invention have increased resistance to
plastic deformation, resulting in improved wear resistance and extended life time
of cutting tools produced from said sintered cemented carbide bodies. Besides, a
considerable minimization of porosity and sinter distortion as compared to prior
art sintered cemented carbide bodies, is obtained by the present invention.
[0061] There is also a considerable advantage of the method of the
present invention which, according to a preferred embodiment thereof, uses a
powdered solid solution of (Zr,Nb)C instead of the conventionally used single
carbides ZrC and NbC. This advantage is due to the lower affinity of the solid
solution of (Zr,Nb)C to oxygen that results in that neither a reducing sintering
atmosphere is necessary nor a continuous control of the reducing force of the
sinter atmosphere is necessary.
[0062] The patents and other documents identified herein are hereby
incorporated by reference herein. Other embodiments of the invention will be
apparent to those skilled in the art from a consideration of the specification or a
practice of the invention disclosed herein. It is intended that the specification and
examples are illustrative only and are not intended to be limiting on the scope of
the invention.
WE CLAIM
1. A sintered cemented carbide body having increased resistance to plastic
deformation, comprising tungsten carbide, a binder phase comprising at least one metal of
the iron group or an alloy thereof, and a solid solution phase comprising at least one of the
carbides and carbonitrides of a combination of zirconium, niobium, and tungsten, wherein
said body has a mass ratio Nb/(Zr+Nb) of at least 0.5, and wherein said solid solution phase
is the sole solid solution phase of said body and (i) consists of a carbide or carbonitride of a
combination of zirconium, niobium and tungsten or (ii) comprises a carbide or carbonitride of
a combination of zirconium, niobium and tungsten, and at least one carbide, nitride or
carbonitride of one or more of titanium, hafnium, vanadium, tantalum, chromium, and
molybdenum.
2. The body of claim 1, wherein said at least one carbide, nitride or carbonitride is of
one or more of titanium, tantalum and hafnium.
3. The body of claims 1 or 2, wherein said binder phase comprises cobalt, a CoNi-alloy
or a CoNiFe-alloy.
4. The body of claim 3, wherein said binder phase additionally comprises one or more
of chromium and tungsten. -
5. The body of any one of claims 1 to 4, wherein said binder phase comprises 3 to
15% of the total weight of said body.
6. The body of any one of claims 1 to 5, wherein the total contents of a carbide or
carbonitride of a combination of zirconium, niobium and tungsten of said solid solution phase
comprise 1 to 15% of the total weight of said body.
7. The body of any one of claims 1 to 6, wherein the total content of the elements
titanium, hafnium, vanadium, tantalum, chromium, and molybdenum does not exceed 8% of-
the total weight of said body.
8. The body of claim 7 wherein titanium comprises 1 to 8 % of the total weight of said
body.
9. The body of claim 7, wherein tantalum comprises 1 to 7 % of the total weight of said
body.
10. The body of claim 7 wherein hafnium comprises 1 to 4 % of the total weight of said
body.
11. The body of any one of claims 1 to 10, wherein the mass ratio Nb/(Zr+Nb) is 0.6 or
more.
12. The body of any one of claims 1 to 11, wherein said body comprises at least one of
said nitrides or carbonitrides and comprises an outermost zone being free of any solid
solution phase, but binder enriched, up to a depth of about 50 µm from an uncoated surface
of said body.
13. The body of claim 12 having, underneath of said binder enriched zone, one single
solid solution phase being homogeneous throughout said body except said binder enriched
zone.
14. The body of any one of claims 1 to 13, wherein one or more wear resistant PVD- or
CVD-layers are coated over a surface of said body.
15. A method of producing the sintered cemented carbide body of any one of claims 1 to
13 comprising the steps of
(a) providing a powder mixture comprising tungsten carbide, a binder metal powder
comprising at least one metal of the iron group or an alloy thereof, and at least one
of the carbides and carbonitrides of both, zirconium and niobium;
(b) forming a green compact of said powder mixture;
(c) vacuum sintering or sinter-HIP said green compact at a temperature of from 1400 to
1560°C;
characterized in that in step (a) a powdered solid solution of the carbides or carbonitrides
of zirconium and niobium having a mass ratio Nb/(Zr + Nb) of at least 0.5 is used to form
said powder mixture.
16. The method of claim 15, wherein a powdered solid solution of a carbide or
carbonitride of a combination of zirconium and niobium having a mass ratio Nb/(Zr + Nb) of
0.6 or more is used.
17. The method of claims 15 or 16, wherein cobalt, a powdered CoNi-alloy or a
t >
powdered CoNiFe-alloy is used as said binder metal powder.
18. The method of claim 17, wherein said binder metal powder additionally comprises at
least one of chromium and tungsten.
19. The method of any one of claims 15 to 18, wherein said binder metal powder
comprises 3 to 15% of the total weight of said powder mixture.
20. The method of any one of claims 15 to 19, wherein said powder mixture additionally
comprises at least one carbide, nitride or carbonitride of one or more of titanium, hafnium,
vanadium, tantalum, chromium, and molybdenum.
21. The method of any one of claims 15 to 20, wherein said powdered solid solution of a
carbide or carbonitride of a combination of zirconium and niobium comprises 1 to 15% of the
total weight of said powder mixture.
22. The method of any one of claims 15 to 21, wherein said powder mixture comprises
at least one of the elements titanium, hafnium, vanadium, tantalum, chromium and
molybdenum in an amount of 1 to 8 % of the total weight of said powder mixture.

A sintered cemented carbide body (e.g., a cutting tool) and a method of
making the same. The sintered cemented carbide body includes tungsten carbide,
a binder phase of at least one metal of the iron group or an alloy thereof, and one
or more solid solution phases. Each one of the solid solution phases has at least
one of the carbides and carbonitrides of a combination of zirconium, niobium, and
tungsten. The method includes the steps of providing a powder mixture that
contains tungsten carbide, a binder metal powder comprising at least one metal of
the iron group or an alloy thereof, and at least one of the carbides and
carbonitrides of both zirconium and niobium including a powder of the carbides
or carbonitrides of zirconium and niobium, forming a green compact of said
powder mixture, and vacuum sintering or sinter-HIP said green compact at a
temperature of from 1400 to 1560°C.

Documents:

108-KOLNP-2006-(09-09-2011)-CORRESPONDENCE.pdf

108-KOLNP-2006-(09-09-2011)-PA.pdf

108-KOLNP-2006-(10-10-2011)-OTHER PATENT DOCUMENTS.pdf

108-KOLNP-2006-CORRESPONDENCE 1.1.pdf

108-KOLNP-2006-CORRESPONDENCE 1.2.pdf

108-KOLNP-2006-CORRESPONDENCE 1.3.pdf

108-KOLNP-2006-CORRESPONDENCE.pdf

108-KOLNP-2006-FORM 13.pdf

108-KOLNP-2006-FORM 27-1.1.pdf

108-KOLNP-2006-FORM 27-1.2.pdf

108-KOLNP-2006-FORM 27.pdf

108-kolnp-2006-granted-abstract.pdf

108-kolnp-2006-granted-claims.pdf

108-kolnp-2006-granted-correspondence.pdf

108-kolnp-2006-granted-description (complete).pdf

108-kolnp-2006-granted-drawings.pdf

108-kolnp-2006-granted-examination report.pdf

108-kolnp-2006-granted-form 1.pdf

108-kolnp-2006-granted-form 18.pdf

108-kolnp-2006-granted-form 2.pdf

108-kolnp-2006-granted-form 26.pdf

108-kolnp-2006-granted-form 3.pdf

108-kolnp-2006-granted-form 5.pdf

108-kolnp-2006-granted-reply to examination report.pdf

108-kolnp-2006-granted-specification.pdf

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Patent Number

234232

Indian Patent Application Number

108/KOLNP/2006

PG Journal Number

20/2009

Publication Date

15-May-2009

Grant Date

12-May-2009

Date of Filing

12-Jan-2006

Name of Patentee

KENNAMETAL INC.

Applicant Address

1600 TECHNOLOGY WAY LATROBE, PA

Inventors:

#	Inventor's Name	Inventor's Address
1	HANS-WILM HEINRICH	BODENSEERING 103, 95445 BAYREUTH
2	DIETER SCHMIDT	HOFFMANN-VON-FALLERSLEBEN-STRASSE 32, 95445 BAYREUTH
3	MANFRED WOLF	RATHAUSSTRASSE 12B, 95488 ECKERSDORF

PCT International Classification Number

B23B 27/14

PCT International Application Number

PCT/EP2004/011170

PCT International Filing date

2004-10-06

PCT Conventions:

#	PCT Application Number	Date of Convention	Priority Country
1	103 56 470.5	2003-12-03	Germany