cBN SINTERED COMPACT

Abstract

A cBN sintered compact includes a binder phase that contains a TiAl alloy containing at least one of the Si, Mg, and Zn elements, Ti.sub.2CN, TiB.sub.2, AlN, and Al.sub.2O.sub.3; the ratio I.sub.Ti2CN/I.sub.TiAl is 2.0 or more and 30.0 or less, wherein I.sub.Ti2CN represents the intensity of the Ti.sub.2CN peak appearing at 2? from 41.9? to 42.2? and I.sub.TiAl represents the intensity of the TiAl alloy peak appearing at 2? from 39.0? to 39.3? in XRD; and, in the mapped image of each element of Ti, Al, Si, Mg, and Zn by Auger electron spectroscopy, the ratio S.sub.TiAlM/S.sub.TiAl, is 0.05 or more and 0.98 or less wherein S.sub.TiAlM represents the average area of the portions wherein Ti, Al and at least one selected from the group consisting of Si, Mg, and Zn overlap and S.sub.TiAl represents the average area of the portions where Ti and Al overlap.

Claims

1. A cBN sintered compact comprising: cubic boron nitride crystal grains; and a binder phase, wherein 1) the binder phase comprises; a TiAl alloy, Ti.sub.2CN, TiB.sub.2, AlN, and Al.sub.2O.sub.3, the TiAl alloy containing at least one element selected from the group consisting of Si, Mg, and Zn, 2) a ratio I.sub.Ti2CN/I.sub.TiAl is 2.0 or more and 30.0 or less, where I.sub.Ti2CN represents the intensity of the Ti.sub.2CN peak appearing at 2? from 41.9? to 42.2? and I.sub.TiAl represents the intensity of the TiAl alloy peak appearing at 2? from 39.0? to 39.3? in XRD, and 3) in a mapped image of each element of Ti, Al, Si, Mg, and Zn by Auger electron spectroscopy, the ratio S.sub.TiAlM/S.sub.TiAl, is 0.05 or more and 0.98 or less wherein S.sub.TiAlM represents the average area of the portions where Ti, Al and at least one selected from the group consisting of Si, Mg, and Zn overlap and S.sub.TiAl represents the average area of the portions where Ti and Al overlap.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0018] FIG. 1 is a schematic diagram illustrating overlapping portions of the Ti and Al elements based on elemental mapping of Example sintered compact 1 by Auger electron spectroscopy.

[0019] FIG. 2 is a schematic diagram illustrating overlapping portions of the Ti, Al, and Si elements based on elemental mapping of Example sintered compact 1 by Auger electron spectroscopy.

DETAILED DESCRIPTION OF THE INVENTION

[0020] The present inventor has focused on cBN sintered compacts as hard composite materials and has extensively studied to produce a cBN sintered compact that has excellent fatigue wear resistance and abrasive wear resistance and is resistant to damaging factors, such as fracture due to impacts and vibrations for breaking rocks in use as a drilling tool.

[0021] As a result, the inventor has obtained the knowledge that a predetermined relationship holds between XRD peaks of Ti.sub.2CN and the TiAl alloy in the binder phase in the cBN sintered compact, and a TiAl alloy containing at least one of Si, Mg, and Zn in the binder phase has excellent fatigue wear resistance and abrasion resistance, and also has resistance to damage factors such as fracture due to impact and vibration in use as a drilling tool.

[0022] The following detailed description will focus on application of the cBN compact in accordance with embodiments of the present invention to drilling tools.

[0023] The expression A to B or A-B (A and B are both numerical values) on the numerical range throughout the specification and claims is synonymous with A or above and B or below, and the range includes the upper limit value (B) and the lower limit value (A). In the case that only the upper limit (B) is followed by a unit, the unit for the upper limit (B) should also be applied to the lower limit (A).

1. Cubic Boron Nitride (cBN) Grains

[0024] The average size of cBN grains and the content of cBN grains in the cBN sintered compact will now be described.

(1) Mean Grain Size

[0025] The cBN grains used in this embodiment may have any mean grain size. The preferred mean grain size ranges from 0.5 or more to 30.0 or less ?m.

[0026] The reason for limiting the range of the mean grain size is as follows: In addition to an improvement in fracture resistance by hard cBN grains contained in the sintered compact, a mean grain diameter of 0.5 to 30.0 ?m leads to, for example, not only suppressing in breakage and chipping originating from the uneven shape of the cutting edge caused by detachment of cBN grains from the surface of a drilling tool during use, but also suppressing in cracks propagating from the interface between the cBN grains and the binder phase by stresses applied to the cutting edge of the drilling tool during use or suppressing in propagation of cracking of the cBN grains.

[0027] The mean diameter of cBN grains can be determined as follows:

[0028] The cross section of a sintered cBN is mirror-finished, and the microstructure on the mirror-finished surface is observed by scanning electron microscopy (SEM) to capture a secondary electron image. A portion of cBN grains in the captured image is extracted by image processing, and the mean grain diameter (described below) is calculated based on the maximum length of each grain determined by image analysis.

[0029] The extraction of the portions of cBN grains in the image by the image processing comprises the steps of: displaying the image in monochrome of 256 gradations including 0 in black and 255 in white to clearly distinguish the cBN grains from the binder phase; and binarizing the image using a threshold calculated with an expression (w?v)/2+v where v represents the peak pixel value of each portion of cBN grains and w represents the peak pixel value of each portion of the binder phases.

[0030] It is preferable to determine pixel values of at least three different cBN particles within the same image area and to define the average of the three pixel values as the peak pixel value of the cBN grain. The region for determining the pixel values of each cBN grain has dimensions of, for example, about 0.5 ?m by 0.5 ?m. It is preferable to determine pixel values of at least three different bonding-phase grains within the same image area and to define the average of the three pixel values as the peak value of the bonding phase. The region for determining the pixel values of each bonding phase has dimensions of about 0.2 ?m by 0.2 ?m to 0.5 ?m by 0.5 ?m. [0021]

[0031] After the binarization process, the cBN grains are separated from each other by a process that separates the contact portions of the cBN grains, for example, by watershed analysis.

[0032] The black portions corresponding to cBN grains in the image after the binarization process are subjected to grain analysis, and the maximum length of each cBN grain is defined as a diameter of the grain. For grain analysis to determine the maximum length, a larger one of the two lengths obtained by calculating the Feret diameter of one cBN grain is a maximum length, and this value is defined as a diameter of each cBN grain.

[0033] Each cBN grain is then assumed to be an ideal sphere with this diameter, to calculate the cumulative volume as a volume of the grain. Based on this cumulative volume, a graph is drawn with the vertical axis as volume percentage (%) and the horizontal axis as diameter (?m). The diameter at 50% volume fraction corresponds to the mean diameter of cBN grains. This treatment is performed for three observation areas, and the mean thereof is defined as a mean grain diameter D50 of cBN (?m).

[0034] Prior to the grain analysis, a length (?m) per pixel is preliminarily determined with a standard scale in a SEM image. Preferably, at least 30 cBN grains are observed in an observation area. For example, in the case that the average size of the cBN grains is about 3 ?m, the observation area is preferably about 15 ?m by 15 ?m.

(2) Content

[0035] The cBN compact may contain any amount (% by volume) of cBN grains. A preferred content range between 65.0% by volume or more and 93.0% by volume or less for the following reasons.

[0036] A content below 65.0% by volume leads to a reduced amount of hard material (cBN grains) in the cBN sintered compact, which may result in reduced fracture resistance in use, for example, as a drilling tool. A content above 93.0% by volume leads to formation of voids in the cBN sintered compact, which voids may work as origins of cracks and thus may result in reduced fracture resistance.

[0037] The content of the cBN grains in the cBN sintered compact can be determined as follows: A cross-sectional microstructure of the cBN sintered compact is observed by SEM, the portions of cBN grains in the observed secondary electron image are extracted by image processing, and then the area occupied by the cBN grains is calculated by image analysis. This procedure is repeated in at least three observation regions, and the average of the resulting areas is defined as a cBN grain content (% by volume). Preferably, at least 30 cBN grains are observed in an observation area. For example, in the case that the average size of the cBN grains is about 3 ?m, the observation area is preferably about 15 ?m by 15 ?m.

2. Binder Phase

[0038] The binder phase of the present embodiment preferably contains Ti.sub.2CN, TiB.sub.2, AlN and Al.sub.2O.sub.3 in addition to a TiAl alloy containing at least one selected from the group consisting of Si, Mg, and Zn.

[0039] At least one selected from the group consisting of Si, Mg and Zn includes any one, any two, and any three (all) of the Si, Mg, and Zn elements.

[0040] It is preferable that the XRD peak intensities of Ti.sub.2CN and the TiAl alloy contained in the binder phase have a predetermined relation. Specifically, the ratio I.sub.Ti2CN/I.sub.TiAl of the peak intensities is preferably 2.0 or more and 30.0 or less where I.sub.Ti2CN represents the intensity of the Ti.sub.2CN peak appearing at 2? of 41.9? to 42.2? in XRD and I.sub.TiAl represents the intensity of the TiAl alloy peak appearing at 2? of 39.0? to 39.3?. At a ratio of peak intensities within this range, the resulting cBN sintered compact has excellent wear resistance and abrasive wear resistance, and is highly resistant to damage factors such as chipping due to impact and vibration during rock excavation, for the following reasons.

[0041] At a ratio I.sub.Ti2CN/I.sub.TiAl of less than 2.0, an excess amount of TiAl alloy present in the cBN sintered compact causes cBN grains to react with the TiAl alloy to form coarse TiB.sub.2 and causes an excess amount of AlN to be formed. The TiB.sub.2 and AlN work as starting points for fracture during rock excavation, for example. At a ratio I.sub.Ti2CN/I.sub.TiAl of greater than 30.0, the content of TiAl alloy in the cBN sintered compact decreases, resulting in reductions in adhesion between the cBN particles and the binder phase and toughness of the cBN sintered compact.

[0042] The peak intensity I.sub.Ti2CN of Ti.sub.2CN and the peak intensity I.sub.TiAl of the TiAl alloy were determined by XRD using CuK? rays, where the peak of the (111) diffraction line of cBN at 2?=43.3 is defined as a standard peak, the peak between 41.9? and 42.2? at 2? angle is defined as Ti.sub.2CN, and the peak between 39.0? and 39.3? at 2? angle is defined as TiAl alloy. After background noise removal, these peaks are confirmed through peak search.

[0043] One or more elements of the Si, Mg, and Zn elements are dispersed together in the TiAl alloy in the binder phase. In the mapping image by Auger electron spectroscopy (hereinafter AES) of the Ti, Al, Si, Mg, and Zn elements, the ratio S.sub.TiAlM/S.sub.TiAl preferably ranges from 0.05 to 0.98, where S.sub.TiAlM represents the average area where one or more elements of the Ti and Al elements and one or more elements of the Si, Mg, and Zn elements overlap with each other and S.sub.TiAl represents the average area where the Ti and Al elements overlap with each other.

[0044] The observation area by AES is preferably about 15 ?m by 15 ?m.

[0045] As examples of elemental mapping Example sintered compact 1 (will be described later) by AES, FIG. 1 illustrates positions where the Ti and Al elements overlap with each other, while FIG. 2 illustrates positions where the Ti, Al, and Si elements overlap with each other. In comparison of these drawings, the overlapping positions in FIG. 2 are distinctly parts of the overlapping positions in FIG. 1.

[0046] Although the reason why the presence of one or more elements of the Si, Mg, and Zn elements together with the TiAl alloy reduces the fatigue fracture is not clear, it is speculated as follows.

[0047] The reaction of TiAl.sub.3 with cBN involves decomposition of TiAl.sub.3 and generates AlN and TiB.sub.2. The resulting AlN has low strength, and readily functions as a starting point of fracture caused by the impact applied in use of a drilling tool of the cBN sintered compact. Since one or more elements of the Si, Mg, and Zn elements are present as constituent raw materials of the binder phase, Al generated by the decomposition of TiAl.sub.3 reacts with a compound containing Si, Mg, and Zn elements to form Al.sub.2O.sub.3 and to reduce the formation of AlN. In addition, the TiAl alloy, which is produced by the decomposition of TiAl.sub.3 and contains one or more elements of Si, Mg, and Zn elements, probably improves the wear resistance.

[0048] The reason why the ratio S.sub.TiAlM/S.sub.TiAl preferably falls within the above range is as follows. At a ratio of less than 0.05, a large amount of AlN is generated in the cBN sintered compact to facilitate fatigue fracture, and a large AlN is present in the cBN sintered compact to facilitate propagation of cracking generated in the sintered compact. At a ratio exceeding 0.98, the formation of AlN is suppressed, but Al.sub.2O.sub.3 and TiCNO are abundant in the binder phase due to oxygen originating in the raw material. TiCNO works as a start point of fatigue fracture and thus decreases the toughness of the sintered compact.

[0049] The above description includes the features appended below.

(Appendix 1)

[0050] A cBN sintered compact comprising: [0051] cubic boron nitride crystal grains and a binder phase; wherein [0052] 1) the binder phase comprises a TiAl alloy containing at least one selected from the group consisting of Si, Mg, and Zn, and further comprises Ti.sub.2CN, TiB.sub.2, AlN, and Al.sub.2O.sub.3; [0053] 2) the ratio I.sub.Ti2CN/I.sub.TiAl is 2.0 or more and 30.0 or less, wherein I.sub.Ti2CN represents the intensity of the Ti.sub.2CN peak appearing at 2? from 41.9? to 42.2? and I.sub.TiAl represents the intensity of the TiAl alloy peak appearing at 2? from 39.0? to 39.3? in XRD; and [0054] 3) in the mapped image of each element of Ti, Al, Si, Mg, and Zn by Auger electron spectroscopy, the ratio S.sub.TiAlM/S.sub.TiAl, is 0.05 or more and 0.98 or less wherein S.sub.TiAlM represents the average area of the portions where Ti, Al and at least one selected from the group consisting of Si, Mg, and Zn overlap and S.sub.TiAl represents the average area of the portions where Ti and Al overlap.

(Appendix 2)

[0055] The cBN sintered compact described in Appendix 1, wherein the cubic boron nitride crystal grains have an average grain size of 0.5 ?m or more and 30.0 ?m or less.

(Appendix 3)

[0056] The cBN sintered compact described in Appendix 1 or 2, wherein the content of the cubic boron nitride crystal grains is 65% by volume or more and 93.0% by volume or less.

Examples

[0057] Examples will now be described. It should be noted that the present invention is not limited to examples applied to tools for cutting rock.

[0058] The samples of the examples were manufactured by the following steps (1) to (3). The raw material powders contained trace amounts of inevitable impurities.

(1) Preparation of Raw Material Powders

[0059] Hard material, i.e., cBN raw material that had a mean particle size of 0.5 to 35.0 ?m after sintering as shown in Table 2, and binder phase material, Ti.sub.2AlC and Ti.sub.3AlC.sub.2 were prepared. Both Ti.sub.2AlC and Ti.sub.3AlC.sub.2 raw powder had a mean particle size of 50 ?m.

[0060] TiN powder (0.6), TiCN powder (0.6), TiC powder (0.6), TiAl.sub.3 powder (0.4), and SiO.sub.2 powder (0.02), Si.sub.3N.sub.4 powder (0.02), MgSiO.sub.3 powder (0.8), ZnO powder (0.8), and MgO powder (0.8) as raw material were also prepared for forming binder phases, where the number in parentheses after the name of each powder represents the mean particle size (D50) in ?m. Table 1 shows the composition of these raw materials.

(2) Mixing and Presintering Treatment

[0061] Raw powders other than powders containing Si, Mg, or Zn elements were placed together with cemented carbide alloy balls and acetone into a ball mill vessel lined with a cemented carbide. The mixing time was 1 hour so as not to pulverize the raw material powder mixture. Although not performed in these examples, it is more preferable that the raw material powders are mixed while agglomerates are disintegrated with an ultrasonic stirrer.

[0062] The mixed raw material powder was preliminarily presintered at a temperature described on the column Heat treatment temperature after mixing in Table 2 under a vacuum atmosphere of 1 Pa or less to evaporate the adsorbed water from the powder surfaces.

[0063] It is preferred that the presintering temperature be 250 to 900? C. under a vacuum atmosphere of 1 Pa or less for the following reasons: At a temperature of less than 250? C., the evaporation of the adsorbed water is insufficient and thus Ti.sub.2AlC and Ti.sub.3AlC.sub.2 react with the remaining moisture to form decomposed TiO.sub.2 and Al.sub.2O.sub.3 during ultra-high pressure and high temperature sintering. At a temperature exceeding 900? C., Ti.sub.2AlC and Ti.sub.3AlC.sub.2 react with oxygen to form decomposed TiO.sub.2 and Al.sub.2O.sub.3 during the presintering treatment. Both cases causes the contents of Ti.sub.2AlC and Ti.sub.3AlC.sub.2 in the binder phase to decrease and the toughness of the cBN sintered compact to decrease.

[0064] Presintered powders other than powders containing the Si, Mg, or Zn element and one or more of the SiO.sub.2, Si.sub.3N.sub.4, MgSiO.sub.3, ZnO, and MgO powders were placed together with cemented carbide balls and acetone into a ball mill vessel lined with a cemented carbide and mixed. The mixing time was 1 hour so as not to pulverize the raw material powder. Although not performed in these examples, it is more preferable that the raw material powders are mixed while agglomerates are disintegrated with an ultrasonic stirrer.

(3) Molding and Sintering

[0065] Green compacts were produced from the resulting sintered raw material powder, were placed into an ultrahigh pressure and high temperature sintering apparatus, and then were sintered at a pressure of 5 GPa and a temperature of 1600? C. to form cBN sintered compacts 1 to 23 of the present invention (referred to as sintered compacts of Examples). Each value in Table 2 was measured by the methods described above. The average particle size and content of the cBN particles were measured in an observation area containing at least 30 cBN observable particles, and the other observation areas were determined as already stated.

[0066] Comparative sintered compacts were also produced for comparison. As raw material for hard material, i.e., cBN raw material that had a mean particle size of 1.0 to 4.0 ?m after sintering as shown in Table 4, and binder phase material, Ti.sub.2AlC or Ti.sub.3AlC.sub.2 were prepared. Both Ti.sub.2AlC and Ti.sub.3AlC.sub.2 raw powder had a mean particle size (D50) of 50 ?m (the other powders had the same average particle size as that in Examples). These were blended so as to have compositions shown in Tables 1 and 3, and were mixed by a ball mill as in Examples. Each mixture was presintered at a predetermined temperature (described on the column Heat treatment temperature after mixing in Table 4) in the range of 100? C. to 1200? C. in a vacuum atmosphere of 1 Pa or less, and then was molded to prepare a green compact, which was then charged into an ultra-high pressure and high temperature sintering apparatus, and was sintered at a pressure of 5 GPa and a temperature of 1600? C. cBN sintered compacts of comparative examples 1 to 9 (referred to as comparative sintered compacts) shown in Table 4 were thereby prepared. Each value in Table 4 was determined as in examples.

TABLE-US-00001 TABLE 1 Composition (% by volume) Type Ti.sub.2AlC Ti.sub.3AlC.sub.2 TiN TiCN TiC TiAl.sub.3 SiO.sub.2 Si.sub.3N.sub.4 MgSiO.sub.3 ZnO MgO Raw a 98 2 material b 98 2 of binder c 95 5 phae for d 90 10 Example* e 80 20 f 99 1 g 85 15 h 85 15 i 75 25 j 85 10 5 k 75 19 4 2 l 80 3 15 2 m 80 15 5 n 80 15 5 o 80 18 2

[0067] In Table 1, the symbol - indicates not containing, * represents that part of the material was used as a binder phase material for comparison.

TABLE-US-00002 TABLE 2 Heat Ratio Identi- CBN treatment of peak faction Average Material temperature intensities of Si, Zn, Content grain for after by XRD and Mg (% by size binder mixing I.sub.Ti2CN/ S.sub.TiAlM/ elements Type volume) (?m) phase (? C) I.sub.TiAl S.sub.TiAl by AES Composition of sintered compact (identified by XRD) Sintered 1 74.8 2.5 g 600 10.2 0.29 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*) compact 2 75.1 2.7 k 650 11.4 0.06 Identified cBN, Ti.sub.2CN, TiC, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN of 3 75.1 2.8 b 650 10.5 0.24 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*) example 4 86.5 2.8 a 650 10.1 0.16 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 5 69.7 1.4 o 350 2.5 0.12 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 6 74.6 3.1 d 650 10.1 0.30 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*) 7 92.7 2.2 a 650 10.1 0.14 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 8 75.2 2.4 m 900 22.9 0.20 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 9 76.1 2.3 f 600 10.7 0.05 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*) 10 76.3 2.1 m 450 30.0 0.23 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 11 75.1 2.7 o 250 2.0 0.11 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 12 76.5 2.6 c 600 11.5 0.26 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 13 75.9 2.1 a 650 12.1 0.15 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 14 70.9 19.8 b 800 9.4 0.21 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*) 15 75.6 2.2 j 650 12.7 0.45 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 16 68.1 30.0 a 650 8.7 0.17 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 17 75.3 2.7 h 600 10.3 0.89 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*) 18 75.8 0.5 l 800 12.8 0.16 Identified cBN, Ti.sub.2CN, TiC, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 19 74.9 7.9 n 650 15.8 0.14 Identified cBN, Ti.sub.2CN, TiC, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 20 76.2 2.6 e 600 9.7 0.65 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*) 21 74.9 2.3 i 600 9.6 0.98 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*) 22 76.2 14.9 a 900 12.3 0.14 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 23 74.9 2.5 o 650 4.9 0.13 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN

[0068] In Table 2, the symbol * indicates that Al.sub.2O.sub.3 was identified with an electron probe micro analyzer (EPMA).

TABLE-US-00003 TABLE 3 Composition (% by volume) Type Ti.sub.2AlC Ti.sub.3AlC.sub.2 TiCN TiAl.sub.3 SiO.sub.2 MgSiO.sub.3 Raw material p 35 15 50 of binder q 35 50 15 phae for r 35 60 5 Comparative s 40 45 5 10 example t 25 30 5 40 u 35 55 10 v 40 59.5 0.5

[0069] In Table 3, the symbol - indicates not containing,

TABLE-US-00004 TABLE 4 Heat Ratio Identi- cBN treatment of peak faction Average Material temperature intensities of Si, Zn, Content grain for after by XRD and Mg (% by size binder mixing I.sub.Ti2CN/ S.sub.TiAlM/ elements Type volume) (?m) phase (? C) I.sub.TiAl S.sub.TiAl by AES Composition of sintered compact (Identified by XRD) Sintered 1 74.9 2.1 s 650 57.9 0.49 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*.sup.2) compact 2 74.1 2.4 p 650 0.5 1.00 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN of 3 75.7 2.5 s 100 42.7 0.53 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*.sup.2) compar- 4 76.0 2.2 q 650 0.5 0.41 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN ative 5 75.9 2.6 v 650 0.5 0.01 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN example 6 75.5 2.5 t 650 40.2 1.00 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, AlN (Al.sub.2O.sub.3 peak not found*.sup.2) 7 74.8 2.2 u 650 0.4 0.48 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN 8 76.3 2.3 r 650 59.7 0.00 Not cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN identified 9 75.7 2.6 c 1200 *.sup.1 0.23 Identified cBN, Ti.sub.2CN, TiB.sub.2, TiAl.sub.3, Al.sub.2O.sub.3, AlN

[0070] In Table 4, the symbol *1 indicates that no XRD peak assigned to TiAl.sub.3 was found, and the symbol *2 indicates that Al.sub.2O.sub.3 was identified with an electron probe micro analyzer (EPMA).

[0071] Example tools 1 to 23 (referred to as Examples 1 to 23) and Comparative example tools 1 to 9 (referred to as Comparative examples 1 to 9) each having an ISO standard RNGN090300 geometry were made from Example sintered compacts 1 to 23 and Comparative example sintered compacts 1 to 9, respectively, and each tool was mounted on an NC lathe and the following wet cutting test was conducted. [0072] Cutting speed: 150 m/min [0073] Depth of cut: 0.3 mm [0074] Feed rate: 0.1 mm/rev [0075] Workpiece material to be cut: granite (from Takine), shape (D150 mm by 200 mm L [0076] Cutting fluid material: water-soluble cutting oil (Neocool by MORESCO Co., Ltd.)

[0077] The amount of wear of the cutting edge and the state of the cutting edge were checked after the cutting length (cutting distance) reached 800 m. Regardless of this, the cutting edge was observed every 100 m of cutting length to observe any defect and the amount of wear. If the amount of wear exceeded 2000 ?m, the cutting test was stopped at that point. The results are shown in Table 5.

TABLE-US-00005 TABLE 5 Type Amount of wear (State of edge) Example 1 1960 ?m(Chipping observed) 2 1290 ?m(Chipping not observed) 3 1510 ?m(Chipping not observed) 4 1380 ?m(Chipping not observed) 5 2090 ?m(Chipping observed) 6 1920 ?m(Chipping observed) 7 1310 ?m(Chipping not observed) 8 1810 ?m(Chipping observed) 9 1820 ?m(Chipping observed) 10 1920 ?m(Chipping observed) 11 1890 ?m(Chipping not observed) 12 1750 ?m(Chipping not observed) 13 1610 ?m(Chipping not observed) 14 1880 ?m(Chipping observed) 15 1900 ?m(Chipping not observed) 16 1710 ?m(Chipping not observed) 17 2090 ?m(Chipping observed) 18 1420 ?m(Chipping not observed) 19 1630 ?m(Chipping not observed) 20 2000 ?m(Chipping observed) 21 2150 ?m(Chipping observed) 22 1560 ?m(Chipping not observed) 23 1800 ?m(Chipping not observed) Comparative 1 Not measured (Fracture)* example 2 Not measured (Fracture)* 3 2400 ?m(Chipping observed)* 4 2600 ?m(Chipping observed)* 5 2200 ?m(Chipping observed)* 6 Not measured (Fracture)* 7 2200 ?m(Chipping observed)* 8 Not measured (Fracture)* 9 Not measured (Fracture)*

[0078] In Table 5, the symbol * indicates the state at a cutting length of 100 m.

[0079] Table 5 evidentially demonstrates that all Examples show reduced amount of wear and no chipping indicating high abrasive wear resistance, and also are resistant to damage factors, such as fracture due to impacts and vibrations to destroy the rock, even use as drilling tools. In contrast, all Comparative examples experience fracture or a high amount of wear after only a short cutting length, and thus have low abrasion resistance, which results indicate that they are difficult to use as drilling tools.

[0080] The disclosed embodiments are illustrative only and not restrictive in all respects. The scope of the invention is indicated by the claims rather than the aforementioned embodiments and is intended to include all modifications within the gist and scope of the claims and equivalents.