JP5315533B2 - Surface coated cutting tool - Google Patents

Description

  The present invention relates to a surface-coated cutting tool including a substrate and a coating film formed thereon.

  Recent cutting tool trends include the need for dry machining without cutting fluids from the viewpoint of global environmental conservation, the diversification of work materials, and higher cutting speeds to further improve machining efficiency. For example, the tool edge temperature tends to be higher, and the characteristics required for the tool material are becoming stricter. In particular, as a required characteristic of tool materials, the coating film formed on the base material has high temperature stability (oxidation resistance and coating film adhesion) as well as wear resistance related to the cutting tool life. Improvement of crack resistance and fracture resistance is becoming more important.

  In order to improve wear resistance and surface protection function, TiAl nitride is used as a hard coating on the surface of cutting tools and wear-resistant tools made of hard base materials such as WC-based cemented carbide, cermet, and high-speed steel. It is well known to form a single layer or multiple layers. However, in recent high-speed and dry processing, a sufficient tool life cannot be obtained with a coating film made of TiAl nitride.

  Under such circumstances, as a method for improving the heat resistance of the coating film and realizing a long tool life, Patent Document 1 discloses a coating film in which Si is further added to a composite nitride of Ti and Al. Proposed. Thus, the coating film containing Si has an advantage that the heat resistance is superior to the coating film made of a nitride of TiAl because a dense oxidation protective film containing Si is formed on the surface thereof. On the other hand, however, the coating film disclosed in Patent Document 1 has a problem that its performance of hardness and toughness is not sufficient.

  On the other hand, Patent Documents 2 to 4 attempt to improve the heat resistance of the coating film by forming an oxide using a physical vapor deposition method.

JP 07-310174 A JP 2004-124246 A Special table 2008-533310 gazette Special table 2010-506049 gazette

  However, since the hardness is lowered due to the high oxygen content in the coating film, there is a problem that the wear resistance is not sufficient.

  The present invention has been made in view of the above-described situation, and an object of the present invention is to provide a surface-coated cutting tool having a coating film on the surface that has wear resistance, fracture resistance, and adhesion. Is to provide.

  In order to solve the above-mentioned problems, the present inventors have made various studies on the composition of the coating film, and as a result, by incorporating oxygen on the surface side of the coating film, it is favorable in high-speed and dry processing. The knowledge that it shows tool performance was acquired. Based on this knowledge, the present invention was finally completed by further intensive studies on the atomic ratio of the layer made of AlTiN and the layer made of AlCrN.

That is, the surface-coated cutting tool of the present invention includes a base material and a coating film formed thereon, and the coating film is Al _a Ti _b M _c N _d O _e (where 0. 35 ≦ a ≦ 0.7, 0 <c ≦ 0.3, a + b + c = 1, 0 <d ≦ 1, 0 ≦ e <1, d + e = 1), and Al _f Cr _g Me _h N _d A layer B composed of O _e (wherein, 0.25 ≦ g ≦ 0.5, 0 ≦ h ≦ 0.3, f + g + h = 1, 0 <d ≦ 1, 0 ≦ e <1, d + e = 1) In which M and Me are each independently selected from the group consisting of V, Zr, Nb, Mo, Hf, Ta, W, and Si. An area containing 10% or more and 50% or less of the entire thickness of the coating film in the thickness direction of the coating film from the surface of the coating film is an oxygen-containing region containing oxygen. In oxygen-containing regions, A and B layers is characterized by a e> 0.

  In the oxygen-containing region, e is preferably 0.002 ≦ e ≦ 0.1, and the e varies in the thickness direction of the coating film, and is 1 or more maximum value and 1 or more minimum. It is preferable that the difference between any one local maximum value and any one local minimum value is 0.005 or more.

  The coating film preferably has a thickness of 1 μm or more and 10 μm or less. Each of the A layer and the B layer preferably has a thickness of 2 nm to 10 nm. The coating film is preferably formed by an arc ion plating method.

  Since the surface-coated cutting tool of the present invention has the above-described configuration, it exhibits an excellent effect of having wear resistance, fracture resistance, and adhesion.

It is typical sectional drawing of the surface coating cutting tool which formed the coating film which has the laminated body on which the A layer and the B layer were laminated | stacked alternately on the base material. It is the schematic of an arc ion plating apparatus.

  Hereinafter, the present invention will be described in detail. In the following description of the embodiments, the description is made with reference to the drawings. In the drawings of the present application, the same reference numerals denote the same or corresponding parts. In the present invention, the thickness of each layer is measured by a scanning electron microscope (SEM) or a transmission electron microscope (TEM), and the composition of the coating film is an energy dispersive X-ray analysis. It shall be measured by an apparatus (EDS: Energy Dispersive x-ray Spectroscopy).

<Surface coated cutting tool>
The surface-coated cutting tool of the present invention comprises a substrate and a coating film formed thereon. The surface-coated cutting tool of the present invention having such a basic configuration is, for example, a drill, an end mill, a milling or turning cutting edge replaceable cutting tip, a metal saw, a cutting tool, a reamer, a tap, or a crankshaft pin. It can be used very effectively as a chip for milling.

<Base material>
As the base material of the surface-coated cutting tool of the present invention, a conventionally known material known as such a cutting tool base material can be used without particular limitation. For example, cemented carbide (for example, WC base cemented carbide, including WC, including Co, or further including carbonitride such as Ti, Ta, Nb, etc.), cermet (TiC, TiN, TiCN, etc.) High-speed steel, ceramics (titanium carbide, silicon carbide, silicon nitride, aluminum nitride, aluminum oxide, and mixtures thereof), cubic boron nitride sintered body, diamond sintered body Etc. can be mentioned as examples of such a substrate. When a cemented carbide is used as such a base material, the effect of the present invention is exhibited even if such a cemented carbide contains an abnormal phase called free carbon or η phase in the structure.

  In addition, these base materials may have a modified surface. For example, in the case of cemented carbide, a de-β layer may be formed on the surface, and in the case of cermet, a surface hardened layer may be formed, and even if the surface is modified in this way, The effect is shown.

<Coating film>
FIG. 1 is a schematic cross-sectional view of a surface-coated cutting tool in which a coating film having a laminate in which A layers and B layers are alternately laminated on a base material is formed. As shown in FIG. 1, the coating film 101 of the present invention has Al _a Ti _b M _c N _d O _e (where 0.35 ≦ a ≦ 0.7, 0 <c ≦ 0.3, and a + b + c = 1,0 < d ≦ 1,0 ≦ e <1, d + e = 1) a layer 102 made _{of, Al f Cr g Me h N} d O e ( although Shikichu, 0.25 ≦ g ≦ 0. 5 and 0 ≦ h ≦ 0.3, f + g + h = 1, 0 <d ≦ 1, 0 ≦ e <1, d + e = 1) and a laminate in which two or more layers are alternately stacked. M and Me in the above formula each independently represent one or more elements selected from the group consisting of V, Zr, Nb, Mo, Hf, Ta, W and Si, and from the surface of the coating film 101 A region of 10% to 50% of the entire thickness of the coating film in the thickness direction of the coating film is an oxygen-containing region 104 containing oxygen, and the oxygen-containing region In 104, A and B layers is characterized in that an e> 0.

  Such a coating film of the present invention includes an aspect in which the entire surface of the substrate is coated, and also includes an aspect in which the coating film is not partially formed. The aspect which the lamination | stacking aspect of a part differs is also included. Moreover, it is preferable that the coating film of this invention is 1 micrometer or more and 10 micrometers or less in the whole thickness. If it is less than 1 μm, the abrasion resistance may be inferior, and if it exceeds 10 μm, the toughness decreases, which is not preferable. A particularly preferable thickness of such a coating film is 2 μm or more and 7 μm or less. In addition, said coating film may contain other arbitrary layers other than A layer and B layer.

Hereinafter, such a coating film will be described in more detail.
<A layer>
The A layer constituting the laminate is Al _a Ti _b M _c N _d O _e (where 0.35 ≦ a ≦ 0.7, 0 <c ≦ 0.3, a + b + c = 1, 0 <d ≦ 1, 0 ≦ e <1, d + e = 1). Such an A layer is excellent in heat resistance, hardness, and stress balance, and therefore effective for high-speed, chipping resistance of the cutting edge during dry processing. The a is preferably 0.5 ≦ a ≦ 0.65, and the c is more preferably 0 ≦ c ≦ 0.1. In this case, the balance of heat resistance, hardness, and compressive residual stress is further improved. In the above formula, if a is less than 0.35 or c exceeds 0.3, the effect of improving the oxidation resistance and hardness cannot be sufficiently obtained, and if a exceeds 0.7 , Since the hardness of the coating film is greatly reduced and the wear resistance is lowered. Note that suitable numerical ranges of the atomic ratio d of nitrogen and the atomic ratio e of oxygen in the A layer will be described later.

  Here, M constituting the A layer is one or more elements selected from the group consisting of V, Zr, Nb, Mo, Hf, Ta, W, and Si. By including such an element in the A layer at a ratio of 30 atomic% or less, solid solution strengthening occurs in the A layer, and the hardness of the A layer can be increased. Among the above elements, V, Nb, Mo, W, etc. have the merit that the tool life can be extended because an oxide is formed by the heat generated during cutting and the self-lubricating effect is exhibited. This is preferable.

Note that in the notation _{Al a Ti b M c N d} O e, as "Al _a Ti _b M _c", the composition ratio between "N _d O _e" is 1: not limited only to the case of 1, All possible ratios can be included as the composition ratio, and the ratio between the two is not particularly limited.

<B layer>
The layer B constituting the laminate together with the layer A is Al _f Cr _g Me _h N _d O _e (where 0.25 ≦ g ≦ 0.5, 0 ≦ h ≦ 0.3, f + g + h = 1) , 0 <d ≦ 1, 0 ≦ e <1, d + e = 1). Such a B layer is excellent in hardness and heat resistance. However, in order to cope with further high speed and dry processing, the single layer itself has difficulty in fracture resistance. Therefore, in the present invention, the above A layer having excellent fracture resistance. The layers are alternately stacked. Here, it is preferable that g is 0.3 ≦ g ≦ 0.4 and h is 0 ≦ h ≦ 0.1. In this case, the balance between wear resistance and toughness is further improved. In the above formula, if h exceeds 0.3, the compressive residual stress increases, and delamination tends to occur, which is not preferable.

  Here, Me constituting the B layer is one or more elements selected from the group consisting of V, Zr, Nb, Mo, Hf, Ta, W, and Si, similarly to M constituting the A layer. It is characterized by being. By including such an element in the B layer at a ratio of 30 atomic% or less, solid solution strengthening occurs in the B layer, and the hardness of the B layer can be increased. Among the above elements, V, Nb, Mo, W, etc. have the merit that the tool life can be extended because an oxide is formed by the heat generated during cutting and the self-lubricating effect is exhibited. This is preferable.

Note that in the notation _{Al f Cr g Me h N d} O e, the composition ratio between the "Al _f Cr _g Me _h", "N _d O _e" is 1: not limited only to the case of 1, the composition All possible ratios can be included, and the ratio between the two is not particularly limited.

<Oxygen-containing region>
In the present invention, a region of 10% to 50% of the thickness of the entire coating film in the thickness direction of the coating film from the surface of the coating film is an oxygen-containing region containing oxygen. In this way, by including oxygen in a certain thickness from the surface side of the coating film, it is possible to suppress the coarsening of the crystal grains on the surface side of the coating film, and the surface of the coating film is increased in hardness. At the same time, the wear resistance can be remarkably improved. In addition, by containing oxygen, the wear coefficient with the work material can be reduced, so that the welding wear resistance can be improved. If the oxygen-containing region is less than 10% of the total thickness of the coating film, the surface of the coating film cannot be sufficiently hardened, and if it exceeds 50%, the compressive stress increases. Is not preferable because the adhesion to the substrate is lowered. The oxygen-containing region is preferably 15% to 45% and more preferably 20% to 40% of the total thickness of the coating film.

  In the oxygen-containing region, the atomic ratio e of oxygen contained in the A layer and the B layer is essential to be e> 0, but is preferably 0.002 ≦ e ≦ 0.1, and more Preferably 0.005 ≦ e ≦ 0.05. When the atomic ratio e of oxygen is less than 0.002, coarsening of crystal grains constituting the coating film cannot be suppressed, and when it exceeds 0.1, an oxide is generated in the coating film. This is not preferable because the hardness decreases.

  In the oxygen-containing region, the oxygen atomic ratio e changes in the thickness direction of the coating film, and has one or more maximum values and one or more minimum values, and any one maximum value or any one The difference from the minimum value is preferably 0.005 or more. In this way, by changing the atomic ratio e of oxygen in the thickness direction of the coating film, the crystal growth of the crystal grains in the oxygen-containing region is effectively inhibited, so that the crystal structure on the surface of the coating film is further refined. To increase the hardness. The difference between the maximum value and the minimum value is more preferably 0.01 or more, and still more preferably 0.015 or more.

<Thickness of A layer and B layer>
Each of the A layer and the B layer as described above preferably has a thickness of 20 nm or less. By alternately laminating two or more layers of the A layer and the B layer having such a thickness, the adhesion between the A layer and the B layer becomes strong, and both layers of the A layer and the B layer are suppressed while preventing delamination between the layers. You can enjoy the characteristics of each. Since the A layer and the B layer can improve the adhesion by thinning them to such an extent that they do not peel between the layers, the thickness is preferably as thin as possible, but it is 2 nm or more and 10 nm or less for the convenience of manufacturing equipment. Is more preferable. When these thicknesses are less than 2 nm, the number of rotations of the rotary table on which the substrate of the film forming apparatus is set is too fast, making film formation difficult due to the specifications of the apparatus. The respective characteristics of both the B and B layers cannot be enjoyed.

<Manufacturing method>
The coating film of the present invention is preferably formed by physical vapor deposition (PVD method). In order to form the coating film of the present invention on the substrate surface, it is indispensable to be a film forming process capable of forming a compound having high crystallinity, and various film forming methods were examined. As a result, it has been found that it is optimal to use physical vapor deposition. Physical vapor deposition methods include, for example, sputtering method, ion plating method, etc. Especially, when using cathode arc ion plating method with high ion ratio of raw material elements, before forming the coating film, On the other hand, since metal or gas ion bombardment treatment is possible, the adhesion between the coating film and the substrate is significantly improved, which is preferable.

  Therefore, the coating film of the present invention is preferably formed by employing a cathode arc ion plating method which is a kind of physical vapor deposition method. FIG. 2 is a schematic diagram of an arc ion plating apparatus. In the opposing evaporation sources 201 and 202, an AlTiM target for the A layer is set in the evaporation source 201, and an AlCrMe target for the B layer is set in the evaporation source 202. Further, the base 210 (cutting tool) is set on the rotary table 204.

Here, by determining the _{Al a Ti b M c N d} O e of a, b, and c constituting the A layer by (the ratio of the M Al and Ti and) the composition of the target to be set in the evaporation source 201 Can do. Further, f, g, and h of Al _f Cr _g Me _h N _d O _e constituting the B layer may be determined by the composition of the target set in the evaporation source 202 (ratio of Al, Cr, and Me). it can. Further, d and e of Al _a Ti _b M _c N _d O _e and Al _f Cr _g Me _h N _d O _e can be determined by the volume ratio of N ₂ gas and O ₂ gas introduced into the apparatus. .

Then, after the apparatus is evacuated to a vacuum, sputter cleaning (bombarding) with Ar gas is performed while rotating the rotary table 204 at 5 rpm while the apparatus is heated to, for example, 500 ° C. Thereafter, a bias voltage of −50 V is applied to the substrate, and the evaporation sources 201 and 202 are always arc-discharged by a constant arc current while rotating the rotary table 204 at 3 rpm, thereby ionizing each target. At the same time, N ₂ gas, which is a reactive gas, is introduced from the gas inlet 205 so as to be 3 Pa, and A layers and B layers are alternately formed on the surface of the substrate 210.

That is, when the substrate 210 passes in front of the evaporation source 201, an A layer made of Al _a Ti _b M _c N is formed, and when the substrate 210 passes in front of the evaporation source 202, Al _f Cr _g The B layer made of Me _h N is formed, and the A layer and the B layer can be alternately stacked sequentially as the turntable 204 rotates in this way. Here, oxygen is not contained in the A layer and the B layer because oxygen is not introduced.

Then, at a stage where the film formation has progressed to some extent, oxygen is introduced into part of the composition of the A layer and the B layer by replacing part of the N ₂ gas as the reaction gas with O ₂ gas, A film can be formed. In this case A layer becomes a composition represented by _{Al a Ti b M c N d} O e, B layer becomes a composition expressed by _{Al f Cr g Me h N d} O e. O ₂ gas flow rate ratio is to flow the total of the N ₂ gas flow rate and O ₂ gas, it is preferably 5 vol% or less. If the flow rate ratio of O ₂ gas exceeds 5% by volume, the atomic ratio of oxygen introduced into the A layer and the B layer becomes too large, and the compressive stress of the coating film increases, which is not preferable.

It is preferable to form the oxygen-containing region while increasing or decreasing the flow rate ratio of the O ₂ gas over time. Thereby, the atomic ratio e of oxygen in the oxygen-containing region can be changed in the thickness direction of the coating film, and the crystal structure on the surface of the coating film can be refined. In addition, when the coating film is formed by changing the flow rate ratio of the O ₂ gas, the stress distribution of the coating film changes, but the cause is not clear, but the fracture resistance can be improved.

  By adjusting the arc current of the evaporation source 201 and the rotation speed of the table during film formation, the thicknesses of the A layer and the B layer can be adjusted. That is, the lower the arc current of the evaporation sources 201 and 202, the thinner the A layer and B layer are formed. However, the arc current needs to be 80 A or more in order to stabilize the discharge of the target. When the arc current is less than 80 A, the arc discharge becomes unstable and it becomes difficult to form the thicknesses of the A layer and the B layer uniformly.

  When the arc current is about 150 A, the A layer and the B layer having a thickness of 10 nm or less can be formed by setting the number of rotations of the table to 3 rpm or more, and preferably 5 rpm or more. If the number of rotations of the table is less than 3 rpm, the thicknesses of the A layer and the B layer may exceed 20 nm, and exceeding 15 rpm is not preferable because of restrictions on manufacturing equipment.

  Further, when forming the A layer and the B layer in the oxygen-containing region, in order to prevent an increase in the residual stress of the coating film due to the introduction of oxygen, the bias voltage applied to the substrate needs to be −100 V or less, preferably Is -70V or less. By introducing a small amount of oxygen in this way, the insulator formed on the surfaces of the furnace wall and the jig cart exhibits electrical conductivity, so that a complete insulator is not formed on those surfaces. For this reason, almost no maintenance work is required to remove the insulator on the surface of the furnace wall or the jig carriage before the next film formation, and the productivity is excellent.

  The thickness of each layer can be controlled by the number of rotations of the turntable 204 and the arc current value. If the thicknesses of the A layer and the B layer are less than 2 nm, the number of rotations of the turntable becomes very fast, and film formation becomes difficult due to the apparatus specifications. The arc ion plating apparatus 200 includes a plurality of heaters 206.

  EXAMPLES Hereinafter, although an Example is given and this invention is demonstrated in detail, this invention is not limited to these.

  In each example and each comparative example, an arc ion plating apparatus as shown in FIG. 2 was used, a target for forming each layer was set in the evaporation source, and a coating film was formed on the substrate.

  As a base material, a P20 equivalent cemented carbide milling throw tip (shape: SDKN42MT) was prepared, and the coating films of the examples and comparative examples shown in Table 1 were formed.

  The coating film was formed by laminating the A layer and the B layer having the composition described in the columns of “A layer” and “B layer” in Table 1. In the oxygen-containing region, a part of the composition described in the columns of “A layer” and “B layer” in Table 1 is replaced with oxygen. The ratio e changes in the thickness direction, and most of them do not take a constant value and are sufficiently smaller than the atomic ratio of nitrogen. Therefore, the atomic ratio of oxygen is not specified in Table 1. I have decided. The column of “A layer and B layer thickness” indicates the thickness of each of the A layer and B layer, and the column of “overall thickness” indicates the thickness of the coating film.

  The “thickness” in the “oxygen-containing region” column indicates the ratio (%) of the thickness of the oxygen-containing region to the total thickness of the coating film, and the “average e” column indicates the oxygen-containing region. The average value of the atomic ratio of oxygen contained is shown. Further, the “extreme value” column indicates the number of values when the value of e takes the maximum value and the minimum value, and the “density difference” column indicates the maximum value of the e value and the minimum value of the e value. The difference from is described. When the maximum value and the minimum value of the atomic ratio e of oxygen were 2 or more, the maximum maximum value and the minimum minimum value were selected, and the difference between them was calculated as the concentration difference.

For example, in Example 1, the arc ion plating apparatus of FIG. 2 is used, Al _0.5 Ti _0.5 is set as the target material of the evaporation source 201, and Al _0.55 Cr _0.35 Nb _0.1 is set as the target material of the evaporation source 202. Then, a surface-coated cutting tool was produced by forming a coating film. In order to make the coating film have a desired composition, N ₂ gas was introduced as a reaction gas, and Ar gas and O ₂ gas were introduced as appropriate to adjust the pressure in the chamber.

  First, after evacuating so that the pressure in the chamber of the arc ion plating apparatus of FIG. 2 became a vacuum, the temperature in the chamber was raised to 600 ° C. Then, Ar gas was introduced, the pressure in the chamber was maintained at 1.0 Pa, the DC bias voltage was gradually increased to −1000 V, and the substrate surface was cleaned (bombarded) for 15 minutes. Thereafter, the argon gas was exhausted. As a result, Ar ions sputter-cleaned the substrate surface, and strong dirt and oxide films were removed.

Next, an A layer and a B layer were formed. N ₂ gas is introduced so that the pressure in the chamber becomes 3 Pa, and the Al _0.5 Ti _0.5 target and the Al _0.55 Cr _0.35 Nb _0.1 target are ionized as an arc current 150 A while rotating the rotary table 204 at 3 rpm. , By reacting with N ₂ gas, respectively, an A layer made of Al _0.5 Ti _0.5 N having a thickness of 5 nm and a B layer made of Al _0.55 Cr _0.35 Nb _0.1 N having a thickness of 5 nm are alternately formed on the substrate. did. After 2.5 hours from the start of film formation, instead a part of the remained N ₂ gas pressure was maintained at 3Pa in the chamber O ₂ gas, additional hour deposited alternately A layer and B layer did.

The amount of O ₂ gas introduced was changed every 20 minutes, and A layers and B layers were alternately formed. That is, the first 20 minutes, oxygen was introduced so that the flow rate of O ₂ gas to the sum of the N ₂ gas and O ₂ gas is 4 vol%, the next 20 minutes, N ₂ gas and O ₂ the flow rate of O ₂ gas to the total gas reduces the amount of introduction of O ₂ gas to be 1 vol%, the last 20 minutes, the O ₂ gas to the sum of the N ₂ gas and O ₂ gas O ₂ gas was increased and introduced so that the flow rate was 2%. The surface-coated cutting tool of Example 1 was produced as described above. In Examples 2 to 21 and Comparative Examples 1 to 6 and 9 to 10, oxygen-containing regions were produced while adjusting the flow rate and introduction time of O ₂ gas, as in Example 1. On the other hand, in Comparative Examples 7 and 8, a coating film was formed without introducing O ₂ gas.

  In the coating film in Example 1, 20% of the thickness of the entire coating film in the thickness direction of the coating film from the surface of the coating film was an oxygen-containing region containing oxygen. The atomic ratio e of oxygen in the oxygen-containing region changed in the thickness direction of the coating film, and had one maximum value and one minimum value, and the difference between them was 0.03. The average oxygen atomic ratio e in the oxygen-containing region was 0.032. The coating film thus formed had a thickness of 4.8 μm, and 480 layers of A layers and B layers were alternately laminated. The average value, maximum value, and minimum value of the atomic ratio e of oxygen in the oxygen-containing region were measured by EDS.

(Cutting performance evaluation)
The throwaway tip for surface-coated milling in each example and each comparative example was evaluated under the following cutting conditions. The results of the cutting evaluation are shown in Table 2.

(1) Milling continuous evaluation A milling continuous test was performed using the throw-away tip for surface-coated milling produced above. The conditions for continuous milling are as follows: a P20 equivalent cemented carbide throw-away tip (shape: SDKN42MT) is used as the base material, and SCM435 (block material of length 300 mm × width 200 mm) is used as the work material. The speed was 200 m / min, the feed amount was 0.2 mm / t, the cutting amount was 1.5 mm, and no cutting oil was used. The wear width of the flank at a cutting time of 15 minutes was measured. The smaller the wear width, the better the wear resistance.

(2) Milling Intermittent Evaluation A milling intermittent test was performed using the surface-coated milling throwaway tip produced above. Milling interrupted cutting conditions were S50C (length: 300 mm × width: 200 mm) as a work material, cutting speed = 140 m / min, feed rate = for an interrupted surface in which 300 holes were drilled with a φ8 drill. 0.3 mm / t, depth of cut = 1.5 mm, performed without cutting oil, and measured the distance cut until the chip surface was damaged. The longer the cutting distance, the better the chipping resistance.

  From Table 2, it was found that the surface-coated cutting tool of the example has a significantly improved tool life as compared with the surface-coated cutting tool of the comparative example, and can sufficiently cope with high-speed machining and dry machining. Thereby, it was confirmed that the surface-coated cutting tool of the present invention has the characteristics of AlTiMN and AlCrMeN, and also has wear resistance, fracture resistance, and adhesion.

  Although the embodiments and examples of the present invention have been described as described above, it is also planned from the beginning to appropriately combine the configurations of the above-described embodiments and examples.

  It should be understood that the embodiments and examples disclosed herein are illustrative and non-restrictive in every respect. The scope of the present invention is defined by the terms of the claims, rather than the description above, and is intended to include any modifications within the scope and meaning equivalent to the terms of the claims.

  DESCRIPTION OF SYMBOLS 100 Surface coating cutting tool, 101 Coating film, 102 A layer, 103 B layer, 104 Oxygen containing area | region, 110,210 Base material, 200 Arc ion plating apparatus, 201,202 Evaporation source, 204 Rotary table, 205 Gas introduction Mouth, 206 Heater.

Claims (5)

A substrate and a coating film formed thereon,
The coating film is made of Al _a Ti _b M _c N _d O _e (where 0.35 ≦ a ≦ 0.7, 0 <c ≦ 0.3, a + b + c = 1, 0 <d ≦ 1, 0 a ≦ e <1, d + e = 1) consisting of A _{layer, Al f Cr g Me h N} d O e ( although Shikichu, 0.25 ≦ g ≦ 0.5,0 ≦ h ≦ 0.3, f + g + h = 1 and 0 <d ≦ 1, 0 ≦ e <1, d + e = 1) and a laminate in which two or more layers are alternately laminated,
In the formula, M and Me each independently represent one or more elements selected from the group consisting of V, Zr, Nb, Mo, Hf, Ta, W, and Si;
A region of 10% to 50% of the total thickness of the coating film in the thickness direction of the coating film from the surface of the coating film is an oxygen-containing region containing oxygen,
In the oxygen-containing region, the A layer and the B layer are a surface-coated cutting tool in which 0.002 ≦ e ≦ 0.1 . In the oxygen-containing region, the e changes in the thickness direction of the coating film, and has a maximum value of 1 or more and a minimum value of 1 or more,
The surface-coated cutting tool according to claim 1, wherein a difference between any one of the maximum values and any one of the minimum values is 0.005 or more. The coating film is 10μm or less in thickness than 1 [mu] m, surface-coated cutting tool according to claim 1 or 2. The surface-coated cutting tool according to any one of claims 1 to 3 , wherein each of the A layer and the B layer has a thickness of 2 nm to 10 nm. The coating film is formed by arc ion plating method, the surface-coated cutting tool according to any one of claims 1-4.

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