JPH0941126A - Cutting tool coated with hard film - Google Patents

Abstract

PROBLEM TO BE SOLVED: To attain superior crater wear resistance and excellent flank wear resistance by constituting the hard film, applied to a flank, of a combined nitride or a combined carbonitride of Ti and Hf. SOLUTION: This cutting tool coated with hard film is formed by applying a hard film at least to the flank and cutting face of a cutting edge of a base material for cutting tool. At this time, the hard film, applied to the flank, is constituted from a combined nitride or a combined carbonitride of Ti and Hf. Ti and Hf form a composition represented by (Ti1-x Hfx , where 0<x<=0.7). Further, the hard film is constituted from a combined nitride or a combined carbonitride of Ti and Al. The composition of Ti and Al is represented by (Ti1-y Aly , where 0<y<=0.7). By this method, the cutting tool capable of meeting the demand for heavy cutting, such as high speed cutting, heavy notching, and heavy feeding, can be obtained.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a hard film coated cutting tool, and more particularly to a hard film coated cutting tool in which a hard film is coated on at least a flank and a rake face of a cutting tool base, Belongs to the technical field of a hard film-coated cutting tool which has excellent wear resistance and is suitable for use in cutting such as milling and punching.

[0002]

2. Description of the Related Art When manufacturing wear resistant members such as cemented carbide (WC-Co based sintered alloy) or high speed tool steel, the purpose is to improve the performance such as wear resistance. A wear-resistant film made of metal nitride or carbide is formed on the surface of the base material of those members.

Examples of such wear resistant coatings include TiN coatings and
A TiC film is commonly used, and it is formed by the ion plating method. Comparing this TiN coating with the TiC coating, the TiN coating has superior heat resistance (high temperature oxidation resistance) to the TiC coating, and the crater wear of the tool rake surface that rises due to machining heat and friction heat during cutting Although it has a protective function, it has a lower hardness than the TiC coating, so it is rather vulnerable to flank wear that occurs on the flank that contacts the work material. Indicates high durability. Therefore, recently, a hard coating of TiCN that suppresses both crater wear and flank wear has been put into practical use.

By the way, in recent years, along with the labor saving, energy saving and productivity improvement of the cutting process, it has been desired to further increase the cutting speed, and heavy cutting such as high cutting or high feed is performed. . Since the cutting conditions tend to become more severe in this way, the TiN coating, TiC coating,
The TiCN coating is no longer able to meet this demand. That is, when high-speed cutting is performed with a cutting tool having a TiN coating, a TiC coating, or a TiCN coating, the coating in the coating deteriorates due to the oxidation of Ti in the coating at a high temperature, resulting in extremely severe wear.

Therefore, in order to further improve the characteristics (functions) of the hard coating, it has been attempted to add third and fourth elements other than Ti, N, and C to TiN, TiC, or TiCN, and heat resistance ( As a hard coating with excellent high temperature oxidation resistance), a composite nitride solid solution [(Al, Ti) N] of Ti and Al with Al added, a composite carbide solid solution [(Al, Ti) C] or a composite carbonitride solid solution 〔(Al, T
i) (N, C)] hard coatings (hereinafter, these are collectively referred to as conventional (Al, Ti) (N / C) -based coatings) have been proposed. A hard film-coated cutting tool having a surface coated has been proposed (Japanese Patent Publication No. 5-67705 and Japanese Patent Publication No. 4-53642).

[0006]

[Problems to be Solved by the Invention] The conventional (Al, Ti) (N /
The C) -based coating has superior heat resistance (high-temperature oxidation resistance) compared to TiN coating, TiC coating, and TiCN coating.
The hard coating-coated cutting tool coated with (having) (Al, Ti) (N / C) coating has a higher crater wear (tool rake face) than the latter hard coating-coated cutting tool with TiN, TiC, TiCN coating. Abrasion) is unlikely to occur. However, the hardness of the (Al, Ti) (N / C) -based coating is not so high as Hv2500, so it is insufficient for suppressing flank wear (wear on the tool flank), and its improvement is is necessary.

That is, since crater wear is wear caused by thermal embrittlement on the rake face of a tool, the characteristic required to suppress crater wear is heat resistance (high temperature oxidation resistance).
On the other hand, since the flank wear is the wear caused by the mechanical rubbing wear on the tool flank, the characteristic required for suppressing the flank wear is high hardness. Traditional
Since the (Al, Ti) (N / C) coating is relatively excellent in such heat resistance (high temperature oxidation resistance), crater wear is unlikely to occur, but with high hardness that can sufficiently suppress flank wear. Since it does not exist, flank wear cannot be sufficiently suppressed, and therefore, improvement in flank wear resistance is necessary.

The present invention has been made by paying attention to such a situation, and its object is a problem in the conventional hard coating-coated cutting tool having (Al, Ti) (N / C) coating. Hard coating that eliminates the points (insufficient flank wear resistance) and has better flank wear resistance than the hard coating-coated cutting tool, resulting in excellent flank wear resistance as well as excellent crater wear resistance. It is intended to provide a coated cutting tool.

[0009]

In order to achieve the above-mentioned object, a hard coating-coated cutting tool according to the present invention is defined by claims 1 to 3.
The hard coating-coated cutting tool described above has the following configuration.

That is, the hard coating-coated cutting tool according to claim 1 is a hard coating-coated cutting tool in which at least a flank and a rake face of a cutting tool base material are coated with a hard coating. The hard coating is made of a composite nitride or composite carbonitride of Ti and Hf, and the composition of Ti and Hf is (Ti _1-x Hf _x ), where 0 <x ≦ 0.7 And the hard coating coated on the rake face is composed of a composite nitride or composite carbonitride of Ti and Al, and the composition of Ti and Al is (Ti _1-y Al _y ), where 0 <y ≦ A hard film-coated cutting tool having a composition represented by 0.7.

A hard film-coated cutting tool according to claim 2 is
The hard film-coated cutting tool according to claim 1, wherein the hard film coated on the flank and the hard film coated on the rake face have a film thickness of 0.1 to 20 µm.

The hard film-coated cutting tool according to claim 3 is
The cutting tool substrate is cemented carbide (WC-Co based sintered alloy)
Alternatively, the hard film-coated cutting tool according to claim 1 or 2, which is a high-speed tool steel.

[0013]

BEST MODE FOR CARRYING OUT THE INVENTION A hard film-coated cutting tool according to the present invention is, for example, by a sputtering method or the like, a composite nitride of Ti and Hf having a composition as described above on the flank of the cutting edge of a cutting tool substrate (or A carbonitride) hard coating.
It is obtained by coating the rake face with a hard film made of a composite nitride (or carbonitride) of Ti and Al having the above composition. Here, a hard coating made of a composite nitride of Ti and Hf (or carbonitride) has a high hardness, and therefore has an effect of suppressing flank wear (wear on the tool flank),
Excellent flank wear resistance. On the other hand, a hard coating consisting of a composite nitride of Ti and Al (or carbonitride) has excellent heat resistance (high temperature oxidation resistance), and is therefore effective in suppressing crater wear (wear on the tool rake face). It has excellent crater wear resistance. Therefore, the hard film-coated cutting tool has excellent crater wear resistance as well as excellent flank wear resistance.

As can be seen from the above, the hard film-coated cutting tool according to the present invention has excellent crater wear resistance as well as excellent flank wear resistance, and has excellent resistance to both the rake face and the flank face. Has wear resistance. Therefore,
It has excellent wear resistance and durability, and can be suitably used for cutting such as milling and drilling, can maintain a high level of tool function for a long time, greatly extend the tool life, and can perform high-speed cutting. It can smoothly handle heavy cutting such as high cutting or high feed.

The details will be described below.

In order to search for the optimum wear-resistant hard coating on each of the tool rake face and the flank face, various elements were added to TiN or TiCN, and the coating performance was evaluated. As a result, Al was added to TiN or TiCN. Composite nitride of Ti and Al [(Ti, Al) N]
Or a hard coating made of composite carbonitride [(Ti, Al) CN]
It has excellent heat resistance (high temperature oxidation resistance), which is effective in suppressing crater wear (wear on the tool rake face), and has excellent crater wear resistance.
The Al content is 70 at% as the proportion of Al in Ti and Al.
I found the following to be good.

The reason why the above coating is excellent in crater wear resistance is that when the coating is heated in the atmosphere, Al selectively oxidizes to form an Al oxide coating on the coating surface. Since the Al oxide film is excellent in high temperature oxidation resistance up to about ℃, it becomes a protective film to suppress thermal embrittlement, and as a result, crater wear (caused by thermal embrittlement) is less likely to occur. it is conceivable that. When the Al content: 70 at% or less, the above-mentioned film is not only excellent in high temperature oxidation resistance as described above, but also has high hardness, and the Al content: 70 at%
When it is over, the crystal structure of the film changes from Nacl type (Bl structure) to Zn
Changes to S type (Wurtzite type), which softens the film. From this point as well, it is necessary to make the Al content: 70 at% or less.

On the other hand, in order to suppress flank wear (wear on the flank of the tool), it is necessary to use a hard coating having a high hardness. However, the composite nitride of Ti and Al [(Ti, Al) N ] The hardness of the coating and composite carbonitride [(Ti, Al) CN] coating is Hv2500.
Since it is not so high, it has low durability for heavy-duty cutting such as high-speed cutting, high-cutting or high-feeding, and is insufficient for suppressing flank wear (wear on the tool flank). On the other hand, Ti and Hf obtained by adding Hf to TiN or TiCN
Compound nitride [(Ti, Hf) N] or compound carbonitride [(Ti, Hf) C]
N)] has a high hardness and a Vickers hardness of
Since it is Hv3500 or more, it is effective in suppressing flank wear (wear on the tool flank) and has excellent flank wear resistance. At this time, the content of Hf is Hf in Ti and Hf. It was found that the ratio should be 70 at% or less.

Although the reason why the above-mentioned coating has a high hardness is not clear, it is presumed that it is mainly due to a change in valence electron distribution and the like. That is, the relationship between valence electron distribution and hardness has already been reported for composite carbides of Ti and Nb [(Ti, Nb) C] (Surface and Coatings Technology, 3
3 (1987) 91-103), which is considered to be related to such changes in valence distribution.

From the above, a composite nitride of Ti and Al having excellent heat resistance (high temperature oxidation resistance) and excellent crater wear resistance as described above is provided on the tool rake face which requires crater wear resistance. A hard coating made of [(Ti, Al) N] or a composite carbonitride [(Ti, Al) CN] is coated on the tool flank that requires flank wear resistance, and the high hardness as described above If a hard film made of a composite nitride of Ti and Hf excellent in flank wear [(Ti, Hf) N] or a composite carbonitride [(Ti, Hf) CN] is coated,
It can be said that this is a hard coating-coated cutting tool having excellent crater wear resistance and excellent flank wear resistance. That is, taking advantage of the excellent advantages of each of these hard coatings,
It is effective to use them properly, which results in a hard film-coated cutting tool having excellent crater wear resistance and excellent flank wear resistance.

The present invention has been made based on the above findings, and the hard coating-coated cutting tool according to the present invention is
As described above, in the hard film-coated cutting tool at least the flank and rake face of the cutting tool base material coated with a hard film, the hard film coated on the flank is Ti and
It consists of Hf compound nitride or compound carbonitride, and its Ti and
The composition of Hf is (Ti _1-x Hf _x ) where 0 <x ≦ 0.7, and the hard film coated on the rake face is a composite nitride of Ti and Al or a composite carbon. It is made of a nitride, and the composition of Ti and Al is (Ti _1-y Al _y ), where 0 <y ≦ 0.7.

The hard film coated on the flank has a composition represented by (Ti _1-x Hf _x ) N or (Ti _1-x Hf _x ) CN, and 0 <x≤0.7. It is characterized by being. Here, when N or CN is Z, this hard film has a composition represented by (Ti _1-x Hf _x ) Z,
0 <x ≦ 0.7. In other words, it is composed of a composite nitride of Ti and Hf or a composite carbonitride [(Ti _1-x Hf _x ) Z], and the proportion of Hf in Ti and Hf is 70 at% or less (0
% Is not included). In addition, (Ti _1-x H
f _x ): Z does not always have to be 1: 1; 1: about 1 (1
It is also included in the case of 1 or less) which is close to 1) and may be, for example, 1: 0.90.

On the other hand, the hard film coated on the rake face is
In other words, is characterized in that the _{(Ti 1-y Al y)} N, or consists composition represented by _{(Ti 1-y Al y)} CN, it is 0 <y ≦ 0.7. Here, when N or CN is Z, this hard film has a composition represented by (Ti _1-y Al _y ) Z, and
<Y ≦ 0.7. In other words, it is composed of a composite nitride of Ti and Al or a composite carbonitride [(Ti _1-y Al _y ) Z],
This is a hard coating in which the proportion of Al in Ti and Al is 70 at% or less (not including 0%). In addition, (Ti _1-y Al _y ):
Z is not necessarily 1: 1, but 1: about 1 (1 close to 1
The following case is also included, and for example, it may be 1: 0.90.

Therefore, it can be seen that the hard film-coated cutting tool according to the present invention has excellent crater wear resistance and excellent flank wear resistance in comparison with the above findings. That is, the flank wear resistance is superior to that in the case of the conventional hard coating coated cutting tool having (Al, Ti) (N / C) coating, and as a result, the excellent crater wear resistance (wear resistance on the rake face) ) And excellent flank wear resistance (wear resistance on the flank), and excellent wear resistance on both the rake face and the flank face.

Here, of the hard film coated on the rake face
The ratio of Al in Ti and Al is 70 at% or less (not including 0%), that is, _{y in} (Ti _1-y Al _y ) Z is set to 0 <x ≦ 0.7. Then, as described above, the film softens due to the change in the crystal structure, and the hardness of Hv2000 is the same as that of TiN.
The heat resistance is also reduced to a certain extent, and as a result, the crater wear resistance is reduced and becomes insufficient. On the other hand, when y is 0, Al is not contained and the crater wear resistance is improved by adding Al. This is because the crater wear resistance becomes insufficient.

The proportion of Hf in Ti and Hf of the hard coating coated on the flank is 70 at% or less (not including 0%), that is, _x in (Ti _1-x Hf _x ) Z is 0 < x ≦ 0.7 is because when x exceeds 0.7, the hardness decreases, and
This is because flank wear resistance decreases and becomes insufficient. On the other hand, when x is set to 0, Hf is not contained and the flank wear resistance cannot be improved by adding Hf, resulting in insufficient flank wear resistance. . The cause of the decrease in hardness when x exceeds 0.7 is not clear, but it is considered to be related to the change in the valence distribution. That is, the hardness of the nitride [(Ti, Nb) N] in which Nb is added to TiN increases with the increase of the Nb amount, but if the Nb amount is increased too much, the hardness decreases conversely.
Since this is reported to be related to the change in the valence electron distribution, it is considered that the change in the valence electron distribution is also involved in the case of (Ti _1-x Hf _x ) Z.

Regarding x, it is desirable that 0 <x ≦ 0.3. This is because the hardness is more reliably increased and the flank wear resistance is improved. Further, it is desirable that y <0 ≦ y ≦ 0.3.
This is because the heat resistance is more surely improved and the crater wear resistance is improved more reliably.

The above-mentioned state in which "a hard coating is coated on at least the flank and rake face of the cutting edge of the cutting tool substrate" means
"For those with flanks and rake faces only on the cutting edge, such as cutting tools for lathe processing, the flanks and rake surfaces of the cutting edges are coated with a hard coating",
`` In the case of drills, end mills, etc., a state in which a hard film is coated only on the flank and rake face of the cutting edge that come into contact with the work material, or in addition to the flank and rake face of the cutting edge and the work material All the flanks and rakes that do not come into contact are covered with a hard film ”.

In the hard film-coated cutting tool according to the present invention, the film thickness of the hard film coated on the flank and the rake face is not particularly limited, but the wear resistance and heat resistance (oxidation resistance) are not limited. ), Both of which are required to be coated with the hard coating on a member such as a tool, the film thickness is 0.
It is desirable to make it 1 μm or more. In terms of oxidation resistance, it is the film thickness if the hard film is evenly coated.
Even if it is less than 0.1 μm, it is effective, but if the film thickness is less than 0.1 μm, the effect of imparting wear resistance is not sufficiently exhibited, and wear resistance (crater wear resistance on the rake face, flank wear resistance on the flank face) is insufficient. Because there is a possibility that On the other hand, if the film thickness exceeds 20 μm, the effect of improving wear resistance and oxidation resistance is small compared to the increase in film thickness, and the coating time increases and productivity decreases.
It is desirable that the thickness is m or less (hard coating according to claim 2).

As the cutting tool base material in the hard film-coated cutting tool according to the present invention, it is desirable to use cemented carbide or high speed tool steel (high speed steel) (hard film according to claim 3). This is because the coating of the present invention has very good adhesion, particularly to cemented carbide and high speed tool steel.

When manufacturing the hard film-coated cutting tool according to the present invention, the method of coating the hard film on the flank and the rake face is not particularly limited, and various coating methods can be used. A PVD method typified by an ion plating method, a sputtering method, or an ion implantation method in which a metal component is ionized by arc discharge using a cathode as an evaporation source may be used. Among these,
For example, by the arc ion plating method (Ti _1-x Al
_x ) When coating the N film, Ti and Al may be used individually as the target (cathode), but if Ti _1-x Al _x consisting of the target composition itself is used, the film composition can be controlled. It has the advantage of being easy.

The flank face is coated with a hard coating in a state where the portion other than the flank face (including the rake face) is masked, and the rake face is coated with the hard coating portion except the rake face (the flank face is covered). (Including) is preferably masked. The order of coating may be from the flank or the rake face.

[0033]

【Example】

(Example 1) Using a platinum plate as a substrate, a hard film having various compositions shown in Table 1 was formed on the platinum plate by the following method, and the oxidation resistance (heat resistance) and hardness of these films were examined. . That is, using a cathodic arc type ion plating apparatus, Ti _1-x Hf _x or Ti
_1-y Al _y solid solution (where, x, y: various changes) fitted with a target made of, on the other hand, fitted with a platinum plate as a substrate on a substrate (base material) holder of the device. Further, the apparatus was provided with a substrate rotating mechanism and a heater for ensuring the uniformity of the film formation state.

Then, while the substrate (platinum plate) was heated and held at 400 ° C. by the above heater, high purity N ₂ was placed in the apparatus.
Alternatively, after introducing a N ₂ / CH ₄ mixed gas, an atmosphere of 3 × 10 ^-2 Torr is applied, a bias voltage of -70 V is applied to the base material to start arc discharge, and a film thickness of 15 μm is formed on the base material surface. The membrane was made.
The composition of the film thus obtained is shown in Table 1 (No. 1-16).
Shown in Of these, Nos. 3 to 8 and 11 to 16 are hard coatings according to the examples of the present invention, and Nos. 1 to 2 and 9 to 11 are coatings according to comparative examples.

For comparison, a TiN film was formed by using Ti for the cathode (target) and using the same apparatus and method as above except for this point (Table 1-No. 17).

In order to examine the oxidation resistance of the film thus formed on the sample thus formed, using a thermobalance device, the temperature raising range: room temperature to 1000 ° C., the temperature raising rate: 10 ° C./min, the atmosphere gas : Oxidation test was carried out under the conditions of dry air and atmospheric gas flow rate: 150 cc / min. Then, the temperature at the point of abrupt weight increase that occurs during the temperature rising process was defined as the oxidation start temperature and was determined. Table 1 shows the results. Also, the Vickers hardness of the coating (load 50 g) was measured. The results are also shown in Table 1.

As is clear from Table 1, TiN coating (No. 1
In (7), oxidation starts at about 600 ° C, and in the (Ti _1-x Hf _x ) Z film (where Z is N or CN), x> 0.7.
Oxidation starts at 0 to 560 ° C (No.1 to 2), and when 0 <x≤0.7, oxidation starts at 620 to 700 ° C (No.3 to 8). On the other hand, in the (Ti _1-y Al _y ) Z film, 0 <y ≦ 0.7 (No. 11 to 16) has a high oxidation initiation temperature and is excellent in high temperature oxidation resistance (heat resistance). Suitable as a hard coating for coating the rake face of a cutting tool. In addition, (Ti _1-y Al
_y ) Z coatings with y> 0.7 (No. 9 to 11) have a high oxidation initiation temperature, but have low hardness, and therefore have low crater wear resistance and are insufficient, and hard coatings for cutting tools. Is not suitable as

[0038] (Ti _1-x Hf _x) in Z film 0 <those x ≦ 0.7 (No.3~8) is compared with the _{(Ti 1-y Al y)} Z coating oxidation start temperature as described above is Although low, it has high hardness and is therefore suitable as a hard coating for covering the flank of a cutting tool. Among them, (Ti _1-y Al _y ) (C, N) coating where Z is CN (No. 7-8) has the highest hardness and is most suitable.

[0039]

[Table 1]

[0040]

[Table 2]

[0041]

[Table 3]

(Example 2) A cathode arc type ion plating apparatus was used, and Ti was used as the cathode electrode.
_A target made of _1-x Hf _x solid solution (however, x: various changes) is attached, while a substrate (base material) holder of the device is made of cemented carbide (WC-10% Co sintered alloy) as a base material. I attached the tool tip of. Further, the apparatus was provided with a substrate rotating mechanism and a heater for ensuring the uniformity of the film formation state. Then, the heater is used to remove the base material (chip)
High-purity N ₂ or N ₂ / C is stored in the device while being heated and maintained at 0 ° C.
After introducing H ₄ mixed gas, make an atmosphere of 7 × 10 ⁻³ Torr,
A bias voltage of -70 V was applied to the base material to start arc discharge, and a film having a thickness of 20 μm was formed on the flank of the tool tip (base material). At this time, the film was formed with the rake face masked.

Next, remove the masking of the rake face of the tool tip, was subjected to masking flank, Ti _1-y Al _y solid solution as a target (where, y: various changes) with, this point Except for the above, the film thickness of 20 μm was formed on the rake face of the tool tip under the same conditions as above.

The composition of the film thus obtained is shown in Table 2.
~ 3 (No. 18 to 25). Of these, Nos. 20 to 25 are hard coatings according to the examples of the present invention, and Nos. 18 to 19 are coatings according to comparative examples.

Further, for comparison, the target is Ti, Ti
_0.4 Al _0.6 or Ti _0.8 Hf _0.2 is used, and the film thickness is set on the flank of the tool tip by the same device and method as above except for this point.
After forming a film with a thickness of 20 μm, a film with a thickness of 20 μm was formed on the rake face, and the flank and rake face of the tool tip were coated with TiN (No. 26, 37), (Ti _0.4 Al _0.6 ) N Coated with
(No.27, 38), (Ti _0.8 Hf _0.2 ) N coated (No. 28,
39) was produced.

Using the tool tip having the film formed as described above, a cutting test was conducted under the following two conditions. The test results are shown in Tables 2-3. Work Material: S45C, Cutting Speed: 170m / min, Feeding Speed: 0.
25mm / rev, depth of cut: 1mm, cutting time: 25 minutes (Table 2) Work material: SKD11, cutting speed: 150m / min, feed rate: 0.
2mm / rev, depth of cut: 2mm, cutting time: 25 minutes (Table 3)

As is clear from Tables 2 and 3, the tool tips according to the examples of the present invention have a flank wear width (flank wear amount) and a rake face wear depth (compared with the tool tips according to the comparative examples). The amount of crater wear) is extremely small and the wear resistance is extremely excellent.

That is, on the flank and rake face of the tool tip
TiN coated (No. 26, 37), (Ti _0.4 Al _0.6 ) N coated (No. 27, 38), (Ti _0.8 Hf _0.2 ) N coated (No. 28, 39) , On the flank with (Ti _1-x Hf _x ) Z film x
> 0.7, and the rake face is coated with (Ti _1-y Al _y ) Z film with y> 0.7 (No. 18-19, 29-3)
In 0), flank wear resistance and / or crater wear resistance is low and insufficient. On the other hand, on the flank (Ti _1-x
Hf _x) covering those 0 <x ≦ 0.7 in Z film, and, rake surface _{(Ti 1-y Al y)} Z coating at 0 <tool tip (No.20 coated ones y ≦ 0.7 ~ 25, 31 to 36: Tool tips according to the examples of the present invention) are excellent in flank wear resistance and crater wear resistance.

[0049]

The hard film-coated cutting tool according to the present invention is
Flanging wear resistance compared to conventional hard-coating cutting tools coated with (Al, Ti) (N / C) -based coating (relatively excellent crater wear resistance, but low flank wear resistance) It has excellent wear resistance and therefore has excellent flank wear resistance as well as excellent crater wear resistance, and therefore has excellent wear resistance and durability, making it suitable for cutting such as milling and drilling. Can be used, can maintain a high level of tool function for a long time, greatly extend the tool life,
Moreover, it is possible to smoothly cope with heavy cutting such as high-speed cutting, high-cutting, and high-feed.

 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Masanori Cai 1-5-5 Takatsukadai, Nishi-ku, Kobe-shi, Hyogo Prefecture Kobe Steel Co., Ltd. Kobe Research Institute (72) Inventor Kazuhisa Kawada Takatsuka, Nishi-ku, Kobe-shi, Hyogo Prefecture 1-5-5 stand, Kobe Steel, Ltd. Kobe Research Institute

Claims (3)

[Claims] 1. A hard film-coated cutting tool in which at least a flank and a rake face of a cutting tool base material are coated with a hard film, and the hard film coated on the flank is Ti.
And Hf compound nitride or compound carbonitride, whose Ti
And the composition of Hf is (Ti _1-x Hf _x ), where 0 <x ≦ 0.7, and the hard film coated on the rake face is a composite nitride or composite of Ti and Al. A hard coating-coated cutting tool comprising a carbonitride and having a composition of Ti and Al (Ti _1-y Al _y ) where 0 <y ≦ 0.7. 2. The hard film-coated cutting tool according to claim 1, wherein the hard film coated on the flank and the hard film coated on the rake face have a film thickness of 0.1 to 20 μm. 3. The hard coating coated cutting tool according to claim 1, wherein the cutting tool base material is cemented carbide or high speed tool steel.