Coated hard-alloy blade member

Abstract: A coated hard alloy blade member is disclosed which includes a substrate formed of a hard alloy of a WC-based cemented carbide or a TiCN-based cermet, and a hard coating deposited on the substrate. The hard coating includes an inner layer of TiCN having unilaterally grown crystals of an elongated shape and an outer layer of Al 2 O 3 having a crystal form κ or κ + α wherein κ > α. The resulting blade member is highly resistant to wear and fracturing, and possesses cutting ability of a higher level.

Description: Technical Field of the Invention The present invention relates to coated hard alloy blade members or cutting tools having exceptional steel and cast iron cutting ability for both continuous and interrupted cutting. Background Art Until now, the use of a coated cemented carbide cutting tool made by using either chemical vapor deposition or physical vapor deposition to apply a coating layer of an average thickness of 0.5-20 µm comprised of either multiple layers or a single layer of one or more of titanium carbide, titanium nitride, titanium carbonitride, titanium oxycarbide titanium oxycarbonitride, and aluminum oxide (hereafter indicated by TiC, TiN, TiCN, TiCO, TiCNO, and Al 2 O 3 ) onto a WC-based cemented carbide substrate for cutting steel or cast iron has been widely recognized. The most important technological advance that led to the wide usage of the above-mentioned coated cemented carbide cutting tool was, as described in Japanese Patent Application No. 52-46347 (JP-A-53-131 909) and Japanese Patent Application No. 51-27171 (JP-A-52-110 209), the development of an exceptionally tough substrate wherein the surface layer of a WC-based cemented carbide substrate included a lot of Co, a binder metal, in comparison with the interior, whereby the fracture resistance of the coated cemented carbide cutting tool rapidly improved. In addition, as disclosed in Japanese Patent Application No. 52-156303 (JP-A-54-87 719) and Japanese Patent Application No. 54-83745 (JP-A-56-009 365), the confirmation that, by sintering the WC-based cemented carbide containing nitrogen in a denitrifying atmosphere such as a vacuum, the surface layer of the WC-based cemented carbide substrate can be made from WC-Co which does not include a hard dispersed phase having a B-1 type crystal structure, whereby it is possible to cheaply produce WC-based cemented carbide having more Co in its surface layer than in the interior, was also important. Concerning the advancement of the coating layer, coated cemented carbides having coating layers wherein the X-ray diffraction peaks of the Ti compounds such as TiC, TiN, and TiCN have a strong (200) orientation and the Al 2 O 3 has an α-type crystal structure such as described in Japanese Patent Application No. 61-231416 (JP-A-63-089 202) and coated cemented carbides having coating layers wherein the X-ray diffraction peaks of the Ti compounds such as TiC, TiN, and TiCN have a strong (220) orientation and the Al 2 O 3 has a κ-type crystal structure such as described in Japanese Patent Application No. 62-29268 (JP-A-63-195 268) have little variation in the tool life. Furthermore, Japanese Patent Application No. 2-156663 (JP-B-7-88 582) shows that a coated cemented carbide having a coating layer wherein the TiC has a strong (111) orientation and the Al 2 O 3 is of the κ-type has the features that there is less spalling of the coating layer and has a long life. However, since the Ti compounds such as TiC of Japanese Patent Application No. 61-231416, Japanese Patent Application No. 62-29268, and Japanese Patent Application No. 2-156663 are coated by the normal CVD method, the crystal structure is in a granular form identical to the coating layers of the past, and the cutting ability was not always satisfactory. Additionally, Japanese Patent Application No. 50-16171 (corresponding to GB-A-1 489 102) discloses that coating is possible with the use of organic gas for a portion of the reaction gas, at a relatively low temperature. In this patent, the crystal structure of the coating layer is not described, and furthermore, the crystal structure may have a granular form, or the crystals may grow in one direction (elongated crystals) depending on the coating conditions. Moreover, in the references given in this patent, the coating layer is made up of only TiCN, and Al 2 O 3 is not disclosed. Additionally, this TiCN had a low bonding strength with the substrate. SUMMARY OF THE INVENTION In recent years cutting technology has shown remarkable progress towards unmanned, high speed processes. Therefore, tools which are highly resistant to wear and fracturing are required. Consequently, the present inventors conducted research to develop a coated cemented carbide cutting tool having cutting ability of a higher level. It was discovered that by coating the surface of a WC-based cemented carbide substrate and a TiCN-based cermet substrate with TiCN having crystals growing in one direction (elongated crystals) as an inner layer, and coating with Al 2 O 3 having a crystal structure κ or κ + α wherein κ > α as an outer layer, remarkable steel and cast iron cutting ability was shown for both continuous cutting and interrupted cutting. Thus, the coated hard alloy blade member as described in claim 1, in accordance with the present invention comprises a substrate formed of a hard alloy selected from the group consisting of a WC-based cemented carbide and a TiCN-based cermet, and a hard coating deposited on said substrate, the hard coating including an inner layer of TiCN having unilaterally grown crystals of an elongated shape and an outer layer of Al 2 O 3 having a crystal form κ or κ + α wherein κ > α. BRIEF DESCRIPTION OF THE DRAWING FIG. 1 is a photograph of a coated cemented carbide blade member in accordance with the present invention as taken by a scanning electron microscope. DETAILED DESCRIPTION OF THE INVENTION The coated hard alloy blade member or cutting tool in accordance with the present invention will now be described in detail. As mentioned before, the coated hard alloy blade member in accordance with the present invention comprises a substrate formed of a hard alloy selected from the group consisting of a WC-based cemented carbide and a TiCN-based cermet, and a hard coating deposited on said substrate, the hard coating including an inner layer of TiCN having unilaterally grown crystals of an elongated shape and an outer layer of Al 2 O 3 having a crystal form κ or κ + α wherein κ > α. In order to practicalize the present invention, it is first necessary to coat the substrate with elongated crystal TiCN having high bonding strength. If the conditions are such that, for example, during the coating of the TiCN, the percentages of the respective volumes are: TiCl4: 1-10%, CH 3 CN: 0.1-5%, N 2 : 0-35%, H 2 : the rest, the reaction temperature is 800-950 °C, the pressure is 30-500 Torr, and furthermore, the CH 3 CN gas is decreased to 0.01-0.1% at the beginning of the coating as a first coating reaction for 1-120 minutes, then the CH 3 CN gas is increased to 0.1-1% as a second coating reaction, then elongated crystal TiCN having high bonding strength can be obtained. The thickness of the TiCN coating layer should preferably be 1-20 µm. This is because at less than 1 µm the wear resistance worsens, and at more than 20 µm the fracture resistance worsens. Furthermore, during the coating of the TiCN, if the reaction temperature or the amount of CH 3 CN is increased, the (200) plane component of the X-ray diffraction pattern of the TiCN becomes weaker than the (111) and (220) plane components, the bonding strength with the Al 2 O 3 in the upper layer which has κ as its main form increases, and the wear resistance goes up. Next, Al 2 O 3 of κ form or κ + α form wherein form κ > α is coated. For coating Al 2 O 3 which has κ as its principal form, the conditions should be such that, for example, the reaction gas is made up of the following volume percentages in the first 1-120 minutes: AlCl 3 : 1-20%, HCl: 1-20% and/or H 2 S: 0.05-5% as needed, and H 2 : the rest, and a first reaction be performed, then afterwards, a second reaction is performed in which AlCl 3 : 1-20%, CO 2 : 0.5-30%, HCl: 1-20% and/or H 2 S: 0.05-5% as needed, and H 2 : the rest, with the conditions of a reaction temperature of 850-1000 °C and pressure of 30-500 Torr. The thickness of this Al 2 O 3 coating layer should preferably be 0.1-10 µm. At less than 0.1 µm the wear resistance worsens, while at over 10 µm the fracturing resistance worsens. The combined thickness of the first TiCN layer and the second Al 2 O 3 layer should preferably be 2-30 µm. The K ratio of the κ + α Al 2 O 3 of the present invention uses a peak from Cu-κα X-ray diffraction, and is determined the following equation, wherein if κ > α then the κ ratio is over 50%. wherein I κ2.79 : The height of the X-ray diffraction peak for ASTM No. 4-0878 with a plane index spacing of d = 2.79 I κ1.43 : The height of the X-ray diffraction peak for ASTM No. 4-0878 with a plane index spacing of d = 1.43 I α2.085 : The height of the X-ray diffraction peak for ASTM No. 10-173 with a plane index spacing of d = 2.085 (the (113) plane) I α1.601 : The height of the X-ray diffraction peak for ASTM No. 10-173 with a plane index spacing of d = 1.601 (the (116) plane) As further modified embodiments of the present invention, the following are included. (1) As an outermost layer, either one or both of TiN or TiCN may be coated on the outer Al 2 O 3 layer. The reason for this coating layer is to discriminate between areas of use, and a thickness of 0.1-2 µm is preferable. (2) As an innermost layer, either one or more of TiN, TiC, or TiCN (granular form) may be coated underneath the inner TiCN layer. By coating with this innermost layer, the bonding strength of the elongated crystal TiCN improves and the wear resistance improves. The most preferable thickness for this coating is 0.1-5 µm. (3) Between the inner TiCN layer and the outer Al 2 O 3 layer, either one or more of TiN, TiC, or TiCN (granular form) may be coated as a first intermediate layer. This first intermediate layer improves the wear resistance during low speed cutting. However, during high speed cutting, it worsens the wear resistance. The most preferable thickness for this first intermediate layer is 1-7 µm. (4) Between the inner TiCN layer and the outer Al 2 O 3 layer, either one or both of TiCO, TiCNO is coated as a second intermediate layer. This second intermediate layer increases the bonding strength between the elongated crystal TiCN and the κ or κ + α form Al 2 O 3 . The most preferable thickness of this second intermediate layer is 0.1-2µm. (5) It is possible to combine the above-mentioned (1)-(4) as appropriate. (6) The inner layer coated with elongated crystal TiCN may be divided by one or more TiN layers to define a divided TiCN layer. This divided TiCN layer is less susceptible to chipping, and the fracture resistance improves. (7) With the divided elongated TiCN described above and the κ or κ + α form Al 2 O 3 , it is possible to coat with an outermost layer of one or both of TiN or TiCN as in (1) above, coat with an innermost layer of one or more of TiN, TiC, or TiCN as in (2) above, coat with a first intermediate layer of one or more of TiC, TiN, or TiCN as in (3) above, coat with a second intermediate layer of one or both of TiCO or TiCNO as in (4) above, or to take a combination of them. (8) The most preferable composition of the WC-based cemented carbide substrate is, by the percentage of weight, as follows: Co: 4-12% Ti: 0-7% Ta: 0-7% Nb: 0-4% Cr: 0-2% N: 0-1% W and C: the rest Unavoidable impurities such as O, Fe, Ni, and Mo are also included. (9) For the WC-based cemented carbide of the present invention, for lathe turning of steel, it is preferable that the cemented carbide be such that the amount of Co or Co + Cr in the surface portion (the highest value from the surface to within 100 µm) be 1.5 to 5 times the amount in the interior (1 mm from the surface), and for lathe turning of cast iron, it is preferable that there is no enrichment of the Co or Co + Cr, and that the amount of Co or Co + Cr be small. Furthermore, in the case of steel milling, cemented carbide in which there has been no enrichment of the Co or Co + Cr, and the amount of Co or Co + Cr is large, is preferable. (10) The most preferable composition of the TiCN-based cermet substrate is, by the percentage of weight, as follows: Co: 2-14% Ni: 2-12% Ta: 2-20% Nb: 0.1-10% W: 5-30% Mo: 5-20% N: 2-8% Ti and C: the rest Cr, V, Zr, Hf: 0-5% Unavoidable impurities such as O and Fe are included. (11) In the TiCN-based cermet of the present invention, the substrate surface layer (the largest value within 100 µm of the surface) should be 5% or more harder than the interior (1 mm from the surface) or there should be no difference between the hardnesses of the surface layer and the interior. The present invention will be explained in more detail by way of the following examples. EXAMPLE 1 As the raw materials, medium grain WC powder having an average particle size of 3 µm, 5 µm coarse grain WC powder, 1.5 µm (Ti, W)C (by weight ratio, TiC/WC = 30/70) powder 1.2 µm (Ti, W)(C, N) (TiC/TiN/WC = 24/20/56) powder, 1.5 µm Ti(C, N) (TiC/TiN = 50/50) powder, 1.6 µm (Ta, Nb)C (TaC/NbC=90/10) powder, 1.8 µm TaC powder, 1.1 µm Mo 2 C powder, 1.7 µm ZrC powder, 1.8 µm Cr 3 C 2 powder, 2.0 µm Ni powder, 2.2 µm NiAl (Al: 31% by weight) powder, and 1.2 µm Co powder were prepared, then these raw material powders were blended in the compositions shown in Table 1 and wet-mixed in a ball mill for 72 hours. After drying, they were press-shaped into green compacts of the form of ISO CNMG 120408 (cemented carbide substrates A-D, cermet substrates F-G) and SEEN 42 AFTN 1 (cemented carbide substrates E and E'), then these green compacts were sintered under the conditions described in Table 1, thus resulting in the production of cemented carbide substrates A-E, E' and cermet substrates F-G. Experimental values taken at over 1 mm from the surface of the sintered compacts of the cemented carbide substrates A-E, E' and the cermet substrates F-G are as shown in Table 2. Furthermore, in the case of the above cemented carbide substrate B, after maintenance in an atmosphere of CH 4 gas at 100 torr and a temperature of 1400 °C for 1 hour, a gradually cooling carburizing procedure was run, then, by removing the carbon and Co attached to the substrate surface using acid and barrel polishing, a Co-rich region 40 µm deep was formed in the substrate surface layer wherein, at a position 10 µm from the surface the maximum Co content was 15% by weight. Additionally, in the case of cemented carbide substrates A and D above, while sintered, a Co-rich region 20 µm deep was formed wherein, at a position 15 µm from the surface, the maximum Co content was 11% and 9% by weight, respectively, and in the remaining cemented carbide substrates C, E and E', no Co-rich region was formed, and they had similar compositions over their entirety. In the above cermet substrates F and G, in the sintered state, a surface layer harder than the interior existed. The hardnesses at the surface and 1 mm below the surface for the cermet substrates F and G are shown in Table 2. Next, after honing the surfaces of the cemented carbide substrates A-E, E' and cermet substrates F and G, by forming coating layers under the special coating conditions shown in Tables 3(a) and 3(b) and having the compositions, crystal structures, orientation of TiCN (shown, starting from the left, in the order of the intensity of the corresponding X-ray diffraction peak) and average thicknesses shown in Table 4 by using a chemical vapor deposition apparatus, the coated cemented carbide cutting tools of the present invention 1-12 and 15-26, the coated cermet cutting tools of the present invention 13, 14, 27, and 28, the coated cemented carbide cutting tools of the prior art 1-12 and 15-26, and the coated cermet cutting tools 13, 14, 27, and 28 of the prior art were produced. Then, for the coated cemented carbide cutting tools of the present invention 1-10 and 15-24, and the coated cemented carbide cutting tools of the prior art 1-10 and 15-24, a mild steel continuous cutting test was performed under the following conditions, Workpiece: mild steel round bar Cutting Speed: 270 m/min Feed: 0.25 mm/rev Depth of Cut: 2 mm Cutting Time: 30 min in which a determination was made whether or not the cutting failed due to tears made in the workpiece because of chipping of the cutting blade or spalling of the coating layer. Then, for those which were able to cut for the set period of time, the amount of flank wear was measured. Furthermore, an interrupted cutting test was performed under the following conditions, Workpiece: mild steel round bar with groove Cutting Speed: 250 m/min Feed: 0.25 mm/rev Depth of Cut: 1.5 mm Cutting Time: 40 min in which a determination was made whether or not the cutting failed due to trouble such as fracturing or chipping of the cutting blade. Then, for those which were able to cut for the set period of time, the amount of flank wear was measured. For the coated cemented carbide cutting tools of the present invention 11, 12, 25 and 26, and the coated cemented carbide cutting tools of the prior art 11, 12, 25 and 26, a mild steel milling test was performed under the following conditions, Workpiece: mild steel square block Cutting Speed: 250 m/min Feed: 0.35 mm/tooth Depth of Cut: 2.5 mm Cutting Time: 40 min in which a determination was made whether or not the milling failed due to trouble such as chipping of the cutting blade. Then, for those which were able to cut for the set period of time, the amount of flank wear was measured. For the coated cermet cutting tools of the present invention 13, 14, 27 and 28, and the coated cermet cutting tools of the prior art 13, 14, 27 and 28, a mild steel continuous cutting test was performed under the following conditions, Workpiece: mild steel round bar Cutting Speed: 320 m/min Feed: 0.25 mm/rev Depth of Cut: 1 mm Cutting Time: 20 min in which a determination was made whether or not the cutting failed due to chipping or fracturing of the cutting blade. Then, for those which were able to cut for the set period of time, the amount of flank wear was measured. Furthermore, an interrupted cutting test was performed under the following conditions, Workpiece: mild steel round bar with groove Cutting Speed: 300 m/min Feed: 0.20 mm/rev Depth of Cut: 1 mm Cutting Time: 20 min in which a determination was made whether or not the cutting failed due to trouble such as chipping of the cutting blade. Then, for those which were able to cut for the set period of time, the amount of flank wear was measured. The results of the above tests are shown in Tables 4-7. As is able to be seen from Tables 4-7, all of the coated cemented carbide cutting tools and coated cermet cutting tools of the present invention demonstrate the properties that it is difficult to fracture or chip the cutting blades and spalling of the coating layers is rare, in addition to exhibiting superior wear and fracture resistance. EXAMPLE 2 Using the same cemented carbide substrates A-E, E' and cermet substrates F and G as Example 1, under the same coating conditions as shown in Tables 3(a) and 3(b) in Example 1, by forming coating layers of the composition, crystal structures, and average thicknesses shown in Tables 8 and 9, the coated cemented carbide cutting tools of the present invention 29-40, the coated cermet cutting tools of the present invention 41 and 42, the coated cemented carbide cutting tools of the prior art 29-40. and the coated cermet cutting tools 41 and 42 of the prior art were produced. Then, for the coated cemented carbide cutting tools of the present invention 29-38, and the coated cemented carbide cutting tools of the prior art 29-38, a mild steel continuous cutting test was performed under the following conditions, Workpiece: mild steel round bar Cutting Speed: 250 m/min Feed: 0.27 mm/rev Depth of Cut: 2 mm Cutting Time: 30 min and an appraisal identical to that of Example 1 was made. Furthermore, an interrupted cutting test was performed under the following conditions, Workpiece: mild steel round bar with groove Cutting Speed: 230 m/min Feed: 0.27 mm/rev Depth of Cut: 1.5 mm Cutting Time: 40 min and an appraisal identical to that of Example 1 was made. For the coated cemented carbide cutting tools of the present invention 39 and 40, and the coated cemented carbide cutting tools of the prior art 39 and 40, a mild steel milling test was performed under the following conditions, Workpiece: mild steel square block Cutting Speed: 230 m/min Feed: 0.37 mm/tooth Depth of Cut: 2.5 mm Cutting Time: 40 min and an appraisal identical to that of Example 1 was made. For the coated cermet cutting tools of the present invention 41 and 42, and the coated cermet cutting tools of the prior art 41 and 42, a mild steel continuous cutting test was performed under the following conditions, Workpiece: mild steel round bar Cutting Speed: 300 m/min Feed: 0.27 mm/rev Depth of Cut: 1 mm Cutting Time: 20 min and an appraisal identical to that of Example 1 was made. Furthermore, an interrupted cutting test was performed under the following conditions, Workpiece: mild steel round bar with groove Cutting Speed: 280 m/min Feed: 0.22 mm/rev Depth of Cut: 1 mm Cutting Time: 20 min and an appraisal identical to that of Example 1 was made. The results of the above tests are shown in Tables 8, 9(a) and 9(b). As is able to be seen from Tables 8, 9(a) and 9(b), all of the coated cemented carbide cutting tools and coated cermet cutting tools of the present invention demonstrate the properties that it is difficult to fracture or chip the cutting blades and spalling of the coating layers is rare, in addition to exhibiting superior wear and fracture resistance. EXAMPLE 3 Using the same cemented carbide substrates A-E, E' and cermet substrates F and G as Example 1, under the same coating conditions as shown in Tables 3(a) and 3(b) in Example 1, by forming coating layers of the composition, crystal structures, and average thickness shown in Tables 10-13, the coated cemented carbide cutting tools of the present invention 43-54 and 57-68, the coated cermet cutting tools of the present invention 55,56, 69 and 70, the coated cemented carbide cutting tools of the prior art 43-54 and 57-68, and the coated cermet cutting tools 55, 56, 69 and 70 of the prior art were produced. Figure 1 shows a photograph of the surface layer of the coated cemented carbide cutting tool of the present invention as taken by a scanning electron microscope. Then, for the coated cemented carbide cutting tools of the present invention 43-52 and 57-66, and the coated cemented carbide cutting tools of the prior art 43-52 and 57-66, a mild steel continuous cutting test was performed under the following conditions. Workpiece: mild steel round bar Cutting Speed: 280 m/min Feed: 0.23 mm/rev Depth of Cut: 2 mm Cutting Time: 30 min and an appraisal identical to that of Example 1 was made. Furthermore, an interrupted cutting test was performed under the following conditions, Workpiece: mild steel round bar with groove Cutting Speed: 260 m/min Feed: 0.23 mm/rev Depth of Cut: 1.5 mm Cutting Time: 40 min and an appraisal identical to that of Example 1 was made. For the coated cemented carbide cutting tools of the present invention 53, 54, 67 and 68, and the coated cemented carbide cutting tools of the prior art 53, 54, 67 and 68, a mild steel milling test was performed under the following conditions, Workpiece: mild steel square block Cutting Speed: 260 m/min Feed: 0.33 mm/tooth Depth of Cut: 2.5 mm Cutting Time: 40 min and an appraisal identical to that of Example 1 was made. For the coated cermet cutting tools of the present invention 55, 56, 69 and 70, and the coated cermet cutting tools of the prior art 55, 56, 69 and 70, a mild steel continuous cutting test was performed under the following conditions, Workpiece: mild steel round bar Cutting Speed: 330 m/min Feed: 0.23 mm/rev Depth of Cut: 1 mm Cutting Time: 20 min and an appraisal identical to that of Example 1 was made. Furthermore, an interrupted cutting test was performed under the following conditions, Workpiece: mild steel round bar with groove Cutting Speed: 310 m/min Feed: 0.18 mm/rev Depth of Cut: 1 mm Cutting Time: 20 min and an appraisal identical to that of Example 1 was made. The results of the above tests are shown in Tables 10-13. As is able to be seen from Tables 10-13, all of the coated cemented carbide cutting tools and coated cermet cutting tools of the present invention demonstrate the properties that it is difficult to fracture or chip the cutting blades and spalling of the coating layers is rare, in addition to exhibiting superior wear and fracture resistance. EXAMPLE 4 Using the same cemented carbide substrates A-E, E' and cermet substrates F and G as Example 1, under the same coating conditions as shown in Tables 3(a) and 3(b) in Example 1, by forming coating layers of the composition, crystal structures, and average thicknesses shown in Tables 14-17, the coated cemented carbide cutting tools of the present invention 71-82 and 85-96, the coated cermet cutting tools of the present invention 83, 84, 97 and 98, the coated cemented carbide cutting tools of the prior art 71-82 and 85-96, and the coated cermet cutting tools 83, 84, 97 and 98 of the prior art were produced. Then, for the coated cemented carbide cutting tools of the present invention 71-80 and 85-94, and the coated cemented carbide cutting tools of the prior art 71-80 and 85-94, a mild steel continuous cutting test was performed under the following conditions, Workpiece: mild steel round bar Cutting Speed: 260 m/min Feed: 0.26 mm/rev Depth of Cut: 2 mm Cutting Time: 30 min and an appraisal identical to that of Example 1 was made. Furthermore, an interrupted cutting test was performed under the following conditions, Workpiece: mild steel round bar with groove Cutting Speed: 240 m/min Feed: 0.26 mm/rev Depth of Cut: 1.5 mm Cutting Time: 40 min and an appraisal identical to that of Example 1 was made. For the coated cemented carbide cutting tools of the present invention 81, 82, 95 and 96, and the coated cemented carbide cutting tools of the prior art 81, 82, 95 and 96, a mild steel milling test was performed under the following conditions, Workpiece: mild steel square block Cutting Speed: 240 m/min Feed: 0.36 mm/tooth Depth of Cut: 2.5 mm Cutting Time: 40 min and an appraisal identical to that of Example 1 was made. For the coated cermet cutting tools of the present invention 83, 84, 97 and 98, and the coated cermet cutting tools of the prior art 83, 84, 97 and 98, a mild steel continuous cutting test was performed under the following conditions, Workpiece: mild steel round bar Cutting Speed: 310 m/min Feed: 0.26 mm/rev Depth of Cut: 1 mm Cutting Time: 20 min and an appraisal identical to that of Example 1 was made. Furthermore, an interrupted cutting test was performed under the following conditions, Workpiece: mild steel round bar with groove Cutting Speed: 290 m/min Feed: 0.21 mm/rev Depth of Cut: 1 mm Cutting Time: 20 min and an appraisal identical to that of Example 1 was made. The results of the above tests are shown in Tables 14-17. As is able to be seen from Tables 14-17, all of the coated cemented carbide cutting tools and coated cermet cutting tools of the present invention demonstrate the properties that it is difficult to fracture or chip the cutting blades and spalling of the coating layers is rare, in addition to exhibiting superior wear and fracture resistance. EXAMPLE 5 Using the same cemented carbide substrates A-E, E' and cermet substrates F and G as Example 1, under the same coating conditions as shown in Tables 3(a) and 3(b) in Example 1, by forming coating layers of the composition, crystal structures, and average thicknesses shown in Tables 18-21, the coated cemented carbide cutting tools of the present invention 99-112 and 122-126, the coated cermet cutting tools of the present invention 113-121, the coated cemented carbide cutting tools of the prior art 99-112 and 122-126, and the coated cermet cutting tools 113-121 of the prior art were produced. Then, for the coated cemented carbide cutting tools of the present invention 99-112, and the coated cemented carbide cutting tools of the prior art 99-112, a mild steel high-feed continuous cutting test was performed under the following conditions, Workpiece: mild steel round bar Cutting Speed: 210 m/min Feed: 0.38 mm/rev Depth of Cut: 2 mm Cutting Time: 30 min and an appraisal identical to that of Example 1 was made. Furthermore, a deep cut interrupted cutting test was performed under the following conditions, Workpiece: mild steel round bar Cutting Speed: 210 m/min Feed: 0.23 mm/rev Depth of Cut: 4 mm Cutting Time: 40 min and an appraisal identical to that of Example 1 was made. For the coated cemented carbide cutting tools of the present invention 122-126, and the coated cemented carbide cutting tools of the prior art 122-126, a mild steel milling test was performed under the following conditions, Workpiece: mild steel square block Cutting Speed: 260 m/min Feed: 0.33 mm/tooth Depth of Cut: 3 mm Cutting Time: 40 min and an appraisal identical to that of Example 1 was made. For the coated cermet cutting tools of the present invention 113-121, and the coated cermet cutting tools of the prior art 113-121, a mild steel continuous cutting test was performed under the following conditions, Workpiece: mild steel round bar Cutting Speed: 340 m/min Feed: 0.22 mm/rev Depth of Cut: 1 mm Cutting Time: 20 min and an appraisal identical to that of Example 1 was made. Furthermore, an interrupted cutting test was performed under the following conditions, Workpiece: mild steel round bar with groove Cutting Speed: 320 m/min Feed: 0.17 mm/rev Depth of Cut: 1 mm Cutting Time: 20 min and an appraisal identical to that of Example 1 was made. The results of the above tests are shown in Tables 18-21. As is able to be seen from Tables 18-21, all of the coated cemented carbide cutting tools and coated cermet cutting tools of the present invention demonstrate the properties that it is difficult to fracture or chip the cutting blades and spalling of the coating layers is rare, in addition to exhibiting superior wear and fracture resistance.

Claims: A coated hard alloy blade member comprising a substrate formed of a hard alloy selected from the group consisting of a WC-based cemented carbide and a TiCN-based cermet, and a hard coating deposited on said substrate, said hard coating including an inner layer of TiCN having unilaterally grown crystals of an elongated shape obtainable by a two-step deposition process wherein a first coating of TiCN is formed using a CVD gas for TiCN deposition comprising acetonitrile having a concentration of acetonitrile gas from 0.01 to 0.1 vol % and a second coating of TiCN is formed using a CVD gas for TiCN deposition comprising acetonitrile wherein the concentration of acetonitrile is increased to be from 0.1 to 1.0 vol % and an outer layer of Al203 having a crystal form of κ or κ + α, wherein, κ > a. A coated hard alloy blade member according to claim 1, wherein the substrate is formed of a WC-based cemented carbide substrate. A coated hard alloy blade member according to claim 1 and/or 2, wherein the TiCN in said elongated crystals of said inner layer has X-ray diffraction peaks such that strength (200) plane is weak compared to strengths at (111) and (220) planes. A coated hard alloy blade member according to any one of the preceding claims wherein said hard coating further includes an innermost layer of one or more of granular TiN, TiC, or TiCN formed underneath said inner layer. A coated hard alloy blade member according to any one of the preceding claims, wherein said hard coating further includes an outermost layer of one or both of granular TiN or TiCN formed on said outer layer of Al 2 O 3 . A coated hard alloy blade member according to any one of the preceding claims, wherein said hard coating further includes a first intermediate layer of one or more of granular TiC, TiN, or TiCN formed between said inner layer of TiCN and said outer layer of Al 2 O 3 . A coated hard alloy blade member according to any one of the preceding claims, wherein said hard coating further includes a second intermediate layer of one or both of TiCO or TiCNO formed between said inner layer of TiCN and said outer layer of Al 2 O 3 . A coated hard alloy blade member according to any one of the preceding claims, wherein said inner layer of TiCN further includes one or more layers of TiN such that the inner layer is divided by the layers of TiN. A coated hard alloy blade member according to any one of the preceding claims, wherein said WC-based cemented carbide consists essentially of 4 - 12 % by weight of Co, 0 - 7 % by weight of Ti, 0 - 7 % by weight of Ta, 0 - 4 % by weight of Nb, 0 - 2 % by weight of Cr, 0 - 1 % by weight of N, and balance W and C. A coated hard alloy blade member according to claim 8, wherein the maximum amount of Co in a surface layer of the substrate ranging up to 100 µm depth from a surface thereof is 1.5 to 5 times as much as the amount of Co in an interior 1 mm deep from the surface. A coated hard alloy blade member according to any one of the preceding claims, wherein said TiCN-based cermet consists essentially of 2 - 14 % by weight of Co, 2 - 12 % by weight of Ni, 2 - 20 % by weight of Ta, 0.1 - 10 % by weight of Nb, 5 - 30 % by weight of W, 5 - 20 % by weight of Mo, 2 - 8 % by weight of N, optionally no greater than 5 % by weight of at least one of Cr, V, Zr or Hf, and balance Ti and C. A coated hard alloy blade member according to claim 11, wherein hardness in a surface layer of the substrate ranging up to 100 µm depth from a surface thereof is more than 5% harder than hardness of an interior 1 mm deep from the surface. The use of a hard coated blade member according to any one of the preceding claims in cutting tools.

Inventors: HAMAGUCHI YUUKI, OSADA AKIRA, OSHIKA TAKATOSHI, SUGAWARA JUN, UNOU KENICHI, YOSHIMURA HIRONORI, HAMAGUCHI, YUUKI, OSADA, AKIRA, OSHIKA, TAKATOSHI, SUGAWARA, JUN, UNOU, KENICHI, YOSHIMURA, HIRONORI, Hamaguchi, Yuuki, c/o, Osada, Akira, c/o, Oshika, Takatoshi, c/o, Sugawara, Jun, c/o, Unou, Kenichi, c/o, Yoshimura, Hironori, c/o
Applicants: MITSUBISHI MATERIALS CORP, MITSUBISHI MATERIALS CORPORATION
Application year: 1995
Main classification: C23C30
IPC codes: C23C16, C23C30