JP2003136302A - Surface coated cemented carbide cutting tool having hard coating layer exerting excellent wear resistance in high-speed cutting - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a surface coated cemented carbide cutting tool having a hard coating layer exerting excellent wear resistance in high-speed cutting. SOLUTION: This surface coated cemented carbide cutting tool is made by physically depositing the hard coating layer made of (b) a Ti-Al composite nitride layer which has average layer thickness of 2 to 15 μm, satisfies a composition formula: (Ti1- YAlY)N (Y shows 0.4 to 0.6 in an atomic ratio), shows a maximum peak on (200) plane by a measurement by an X-ray diffractometer using Cu-Kα rays and shows an X-ray diffraction pattern having the half-width of 2θand <=0.6 degrees of the maximum peak, on the surface of a tungsten carbide group cemented carbide base body or a titanium carbonitride group cermet base body, via a crystal orientation history layer made of (a) a Ti-Al composite carbide layer which has average layer thickness of 0.05 to 0.5 μm, satisfies a composition formula: (Ti1- XAlX)C (X shows 0.05 to 0.20 in the atomic ratio), shows a maximum peak on (200) plane by a measurement by the X-ray diffractometer using Cu-Kα rays and shows an X-ray diffraction pattern having the half-width of 2θ and <=0.6 degrees of the maximum peak.

Description

Description: BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-speed cutting process in which a hard coating layer has excellent high-temperature characteristics, and thus high heat generation of various steels and cast irons. The present invention relates to a surface-coated cemented carbide cutting tool exhibiting excellent wear resistance (hereinafter referred to as a coated cemented carbide tool). 2. Description of the Related Art Generally, a cutting tool includes a throw-away tip which is removably attached to a tip of a cutting tool for turning or planing of a work material such as steel or cast iron. There are drills and miniature drills used for drilling and cutting work materials, and solid type end mills used for face milling, grooving, shoulder processing, etc. of the work material. A throw-away end mill tool or the like which is freely mounted and performs cutting in the same manner as the solid type end mill is known. [0003] Further, as a cutting tool, a substrate made of tungsten carbide (hereinafter, referred to as WC) -based cemented carbide or a titanium cermet (hereinafter, referred to as TiCN) -based cermet (hereinafter, collectively referred to as a cemented carbide substrate). On the surface)
Ti—Al composite nitride satisfying the composition formula: (Ti _1-Y Al _Y ) N (where Y represents 0.4 to 0.6 in atomic ratio) [hereinafter, (Ti, Al) N Shown] A coated carbide tool is known which is obtained by physical vapor deposition of a hard coating layer having an average layer thickness of 2 to 15 μm, and is used for continuous cutting or intermittent cutting of various steels and cast irons. Is also well known. Further, the above-mentioned coated super hard tool is prepared by charging the above super hard substrate into an arc ion plating apparatus which is a kind of physical vapor deposition apparatus schematically shown in FIG. The atmosphere is, for example, 1.3 × 10 ^−3.
In a state of heating to a temperature of 500 ° C. as a vacuum of Pa,
An arc discharge is generated between the anode electrode and a cathode electrode (evaporation source) on which a Ti-Al alloy having a predetermined composition is set, for example, at a voltage of 35 V and a current of 90 A, and at the same time, as a reaction gas in the apparatus. Introduce nitrogen gas,
On the other hand, under the condition that a bias voltage of -200 V is applied, for example, the (T
It is also known to be manufactured by depositing a hard coating layer consisting of an i, Al) N layer. [0005] In recent years, the performance of cutting equipment has been remarkably improved, and on the other hand, there has been a strong demand for labor saving, energy saving, and further cost reduction in the cutting work. Although there is a tendency to increase the speed, in the above-mentioned conventional coated carbide tools, there is no problem if this is used under normal cutting conditions, but if this is used at high speed cutting conditions with high heat generation. At present, the progress of abrasion of the hard coating layer is promoted, and the service life is reached in a relatively short time. Means for Solving the Problems Accordingly, the present inventors have proposed:
In view of the above, in order to develop a coated carbide tool that demonstrates excellent wear resistance in high-speed cutting, we focused on the hard coating layer that constitutes the above-mentioned conventional coated carbide tool and conducted research. As a result, (a) constituting the above-mentioned conventional coated carbide tool (Ti, A
l) The hard coating layer composed of the N layer was measured by an X-ray diffractometer using Cu-Kα radiation, as shown in FIG.
The X-ray diffraction pattern in which the highest peak appears on the (00) plane and the half width of the highest peak is 0.9 ° or more in 2θ (horizontal axis) is shown. Prior to vapor deposition formation, the composition formula: (Ti _1-X A
l _x ) C However, in the atomic ratio, X shows 0.05 to 0.20).
i, Al) C] layer is extremely thin.
By vapor deposition with an average layer thickness of 5 μm, (Ti,
The Al) C layer is highly oriented on the (200) plane, and the (20)
0) X having a half width of a crystal plane peak of 0.6 degrees or less at 2θ.
Since the X-ray diffraction pattern is shown above, the half-width of the peak on the (200) plane of the X-ray diffraction pattern which is physically deposited on the X-ray diffraction pattern is 0.9 ° or more at 2θ. As shown in FIG. 1, the (Ti, Al) N layer also has a (200) plane with a half width of 0.
To show a highly oriented X-ray diffraction pattern of 6 degrees or less. (B) In a highly oriented (Ti, Al) N layer in which the half width of the peak on the (200) plane of the X-ray diffraction pattern is 0.6 ° or less at 2θ, the half width of the peak is 0.
Since the high-temperature characteristics (high-temperature oxidation resistance and high-temperature hardness) are superior to the (Ti, Al) N layer having a temperature of 9 degrees or more, the hard coating layer composed of the (Ti, Al) N layer having a high orientation is used. A coated cemented carbide tool formed by physical vapor deposition on the surface of a cemented carbide substrate will exhibit excellent wear resistance in high-speed cutting of steel or mild steel with high heat generation. The research results shown in (a) and (b) above were obtained. The present invention has been made on the basis of the above research results, and (a) 0.0
It has an average layer thickness of 5 to 0.5 μm and a composition formula: (T
i _1-X Al _X ) C where X is 0.05 to 0.
20), and the highest peak appeared on the (200) plane by a X-ray diffractometer using Cu-Kα ray, and the half width of the highest peak was 0.6 at 2θ. X-ray diffraction pattern which is less than
1) Through the crystal orientation history layer composed of the C layer, (b)
It has an average layer thickness of 15 μm and has a composition formula: (Ti _1-Y Al _Y )
N (however, in the atomic ratio, Y indicates 0.4 to 0.6), and the highest peak appears on the (200) plane by the same X-ray diffractometer using Cu-Kα ray. And a hard coating layer formed by physical vapor deposition of a hard coating layer composed of a (Ti, Al) N layer showing an X-ray diffraction pattern in which the half width of the highest peak is 0.6 ° or less at 2θ, and Is characterized by coated carbide tools exhibiting excellent wear resistance. Next, the reason why the composition and average layer thickness of the crystal orientation history layer and the hard coating layer constituting the coated carbide tool of the present invention are limited as described above will be described. (A) Crystal orientation history layer [(Ti, Al) C layer] Al in the (Ti, Al) C layer includes (200)
There is an effect of orienting the plane perpendicular to the rake face and flank face of the cutting edge. However, if the Al ratio is less than 0.05 in atomic ratio, the orientation to the (200) plane is insufficient and (200) )
The half-width of the highest peak appearing on the plane cannot be highly oriented to 0.6 ° or less at 2θ, while even if the ratio exceeds 0.20, the crystal orientation becomes disordered,
Since it becomes difficult to make the (200) plane highly oriented, the ratio is set to 0.05 to 0.20. If the average layer thickness is less than 0.05 μm, (Ti, Al) C
The crystal orientation history effect of converting the high orientation of the (200) plane inherent in the layer to the hard coating layer cannot be sufficiently exhibited, while the crystal orientation history effect is sufficient with an average layer thickness up to 0.5 μm. Therefore, the average layer thickness is 0.05
０．５0.5 μm. (B) Hard coating layer [(Ti, Al) N layer] Al in the (Ti, Al) N layer enhances the hardness and heat resistance of the TiN layer having high toughness, thereby improving the wear resistance. However, if the ratio is less than 0.4 in the ratio (atomic ratio) to the total amount with Ti, the desired effect of improving wear resistance cannot be obtained, while the ratio also exceeds 0.6. Since chipping (minute chipping) and the like easily occur on the cutting edge, the ratio is set to 0.4 to 0.6. If the average layer thickness is less than 2 μm, desired wear resistance cannot be ensured. On the other hand, if the average layer thickness exceeds 15 μm, chipping is likely to occur on the cutting edge. The thickness was determined to be 2 to 15 μm. Furthermore, X
The half width of the highest peak appearing on the (200) plane of the X-ray diffraction pattern: 0.6 ° or less (2θ) is empirically determined based on the test results. When the half-width increases to more than 0.6 degrees, that is, when the orientation of the (200) plane is reduced, it exhibits excellent wear resistance especially in high-speed cutting. This is because the desired wear resistance cannot be ensured. Next, the coated carbide tool of the present invention will be specifically described with reference to examples. (Example 1) As raw material powders, WC powder, TiC powder, ZrC powder, V
C powder, TaC powder, NbC powder, Cr ₃ C ₂ powder, T
An iN powder, a TaN powder, and a Co powder were prepared, and these raw material powders were blended in the blending composition shown in Table 1, wet-mixed in a ball mill for 72 hours, dried, and then dried.
a into a green compact at the pressure of a
sintering in a vacuum at a temperature of 1400 ° C. for 1 hour, and after sintering, the cutting edge portion is subjected to a honing process of R: 0.05 to form a WC having a chip shape of ISO standard CNMG120408. Substrates A1 to A10 made of base cemented carbide
Was formed. In addition, as raw material powders,
TiCN having an average particle size of 2 μm (by weight ratio TiC /
(TiN = 50/50) powder, Mo ₂ C powder, ZrC powder, NbC powder, TaC powder, WC powder, Co powder, and Ni powder were prepared, and these raw material powders were blended into the composition shown in Table 2. After wet-mixing with a ball mill for 24 hours and drying, the mixture is pressed into a green compact at a pressure of 100 MPa, and the green compact is heated in a nitrogen atmosphere of 2 kPa at a temperature of:
Sintered under the condition of holding at 1500 ° C. for 1 hour, and after sintering, the cutting edge portion is subjected to a honing process of R: 0.03 to obtain a TiC having a chip shape conforming to ISO standard, CNMG120408.
Carbide substrates B1 to B6 made of N-based cermet were formed. Next, these super-hard substrates A1 to A10 and B1 to B6 are ultrasonically cleaned in acetone and dried, and each is charged into a usual arc ion plating apparatus illustrated in FIG. On the other hand, a Ti-Al alloy for forming a crystal orientation history layer and a Ti-Al alloy for forming a hard coating layer having various component compositions are mounted as a cathode electrode (evaporation source), and the inside of the apparatus is evacuated to a vacuum of 0.5 Pa. After heating the inside of the device to 500 ° C with a heater,
Ar gas was introduced into the apparatus to form an Ar atmosphere of 10 Pa. In this state, a bias voltage of -800 V was applied to the super hard substrate to clean the surface of the super hard substrate by Ar gas bombardment, and then the introduction of Ar gas was stopped. In this state, the bias voltage applied to the cemented carbide substrate was reduced to -100 V, methane gas was introduced as a reaction gas into the apparatus to make a reaction atmosphere of 3.5 Pa, and the cathode electrode (for forming a crystal orientation history layer) was formed. An arc discharge is generated between the Ti—Al alloy) and the anode electrode, and the target compositions and target layer thicknesses shown in Tables 3 and 4 are respectively formed on the surfaces of the cemented carbide substrates A1 to A10 and B1 to B6. Crystal orientation history layer [(Ti,
Al) C layer], nitrogen gas is introduced as a reaction gas into the apparatus to make a reaction atmosphere of 3.5 Pa, and a bias voltage applied to the super hard substrate is -30.
V to the cathode electrode (Ti for forming the hard coating layer).
-Al alloy) and the anode electrode to generate an arc discharge, and thereby deposit a hard coating layer [(Ti, Al) N layer] having the target composition and target layer thickness also shown in Tables 3 and 4. FIG. 4A is a schematic perspective view, and FIG. 4B is a schematic longitudinal sectional view of the present invention. Inventive coated carbide tips) 1 to 20 were manufactured respectively. For comparison purposes, as shown in Tables 5 and 6, the crystal orientation history layer [(Ti, Al) C layer]
Under the same conditions, except that the formation of No. was not performed, conventional surface-coated cemented carbide throwaway tips (hereinafter referred to as conventionally-coated cemented carbide tips) 1 to 20 as conventionally-coated cemented carbide tools were produced, respectively. Next, the coated carbide tips 1-2 of the present invention
0 and the conventional coated carbide tips 1 to 20 were screwed to the tip of a tool steel tool with a fixing jig. Work material: JIS / SNCM439 round bar, Cutting speed: 360 m / min . Infeed: 1.5 mm Feed: 0.2 mm / rev. , Cutting time: 10 minutes, Dry high-speed continuous turning test of alloy steel under the following conditions: Work material: JIS S50C, longitudinally-elongated round bar with four longitudinal grooves, Cutting speed: 280 m / min. Notch: 1.8 mm Feed: 0.3 mm / rev. , Cutting time: 5 minutes, Dry high-speed intermittent turning test of carbon steel under the following conditions: Work material: JIS FC250, 4 longitudinally spaced round bars at regular intervals in the longitudinal direction, Cutting speed: 200 m / min . Infeed: 1.5 mm Feed: 0.3 mm / rev. A dry high-speed intermittent turning test of cast iron was performed under the following conditions: cutting time: 5 minutes, and the flank wear width of the cutting edge was measured in each turning test. The measurement results are shown in Tables 7 and 8. [Table 1] [Table 2] [Table 3] [Table 4] [Table 5] [Table 6] [Table 7] [Table 8] Example 2 As raw material powder, average particle size:
Medium coarse WC powder having 5.5 μm, fine WC powder of 0.8 μm, TaC powder of 1.3 μm, 1.2 μm
NbC powder, 1.2 μm ZrC powder, 2.3 μm
m Cr ₃ C ₂ powder, 1.5 μm VC powder, 1.0
μm of (Ti, W) C powder and 1.8 μm of Co
Powders were prepared, and each of these raw material powders was blended into the blending composition shown in Table 9, further added with wax, and ball-mixed in acetone for 24 hours, and dried under reduced pressure.
Press molding at a pressure of 0 MPa into various green compacts of a predetermined shape, and pressing these green compacts in a vacuum atmosphere of 6 Pa at 7 ° C. /
The temperature was raised to a predetermined temperature in the range of 1370 to 1470 ° C. at a heating rate of 1 minute, kept at this temperature for 1 hour, and then sintered under the condition of furnace cooling to obtain a sample having a diameter of 8 mm, 13 mm and 26 mm. Kinds of round bar sintered bodies for forming a cemented carbide substrate are formed, and the above three kinds of round bar sintered bodies are subjected to grinding processing in a combination shown in Table 9 to obtain a diameter shown in FIG. Is 6mm × 1 each
3mm, 10mm x 22mm, and 20mm x 45m
Carbide substrates (end mills) a to h having a size of m were manufactured, respectively. Next, these super-hard substrates (end mills)
Honing was performed on the surfaces a to h, ultrasonically cleaned in acetone, and dried, and then charged into a usual arc ion plating apparatus also illustrated in FIG. Under the conditions, the crystal orientation history layer [(Ti, Al) C having the target composition and the target layer thickness shown in Table 10
5A and a hard coating layer [(Ti, Al) N layer], the shape shown in the schematic front view in FIG. 5A and the schematic cross-sectional view of the cutting edge in FIG. End mills (hereinafter referred to as “coated carbide end mills of the present invention”) 1 to 8 of the surface coated cemented carbide of the present invention as the coated carbide tools of the present invention were manufactured. For the purpose of comparison, as shown in Table 11, under the same conditions except that the above-mentioned crystal orientation history layer [(Ti, Al) C layer] was not formed, the conventional surface-coated carbide as a conventional coated carbide tool was used. Alloy end mills (hereinafter referred to as conventional coated carbide end mills) 1 to 8 were manufactured, respectively. Next, the coated carbide end mill 1 of the present invention will be described.
-8 and the conventional coated carbide end mills 1-8, the coated carbide end mills 1-3 of the present invention and the conventional coated carbide end mills 1-3 are: work material: plane dimension: 100 mm × 250 mm, thickness: 5
0 mm JIS SCM440 plate, Cutting speed: 160 m / min. , Groove depth (cut): 2.5 mm, Table feed: 700 mm / min, Dry high-speed grooving test of alloy steel, coated carbide end mills 4 to 6 according to the present invention and conventional coated carbide end mills 4 to About 6, work material: plane dimensions: 100 mm x 250 mm, thickness: 5
0 mm JIS S45C plate, Cutting speed: 180 m / min. , Groove depth (cut): 5 mm, table feed: 550 mm / min, dry high-speed groove cutting test of carbon steel under the following conditions, coated carbide end mills 7 and 8 of the present invention and conventional coated carbide end mills 7 and 8 , Work material: Plane dimensions: 100 mm x 250 mm, thickness: 5
JIS FC300 plate material of 0 mm, Cutting speed: 180 m / min. , Groove depth (cut): 10 mm, Table feed: 300 mm / min., Dry high-speed grooving test for cast iron under the following conditions: In all grooving tests, the flank wear of the outer peripheral edge is used. The cutting groove length up to 0.1 mm, which is a standard for the life, was measured. The measurement results are shown in Tables 10 and 11, respectively. [Table 9] [Table 10] [Table 11] (Example 3) The diameters of 8 mm (for forming the super-hard substrates a to c), 13 mm (for forming the super-hard substrates d to f), and 26 mm (for the super-hard substrate g) produced in Example 2 described above. h
(For forming), the diameter x length of the groove forming portion was 4 mm x 13 mm (the cemented carbide substrate a ') by grinding from the three types of round rod sintered bodies. ~ C '), 8mm
× 22 mm (carbide substrate d ′ to f ′) and 16 mm ×
Carbide substrates (drills) a 'to h' each having a size of 45 mm (carbide substrates g 'and h') were manufactured. Next, these super hard substrates (drills) a '
~ H 'was subjected to honing, ultrasonically cleaned in acetone, dried, and charged in a usual arc ion plating apparatus also illustrated in FIG. Under the conditions, the crystal orientation history layer [(Ti, Al) C having the target composition and the target layer thickness shown in Table 12
6A and 6B, the hard coating layer [(Ti, Al) N layer] is vapor-deposited so that the shape shown in the schematic front view in FIG. Drills made of the surface-coated cemented carbide of the present invention (hereinafter referred to as the coated carbide drills of the present invention) 1 to 8 as the coated carbide tools of the present invention were manufactured. For the purpose of comparison, as shown in Table 13, under the same conditions except that the above-mentioned crystal orientation history layer [(Ti, Al) C layer] was not formed, the conventional surface-coated carbide as a conventional coated carbide tool was used. Alloy drills (hereinafter referred to as conventional coated carbide drills) 1 to 8 were manufactured, respectively. Next, the above-described coated carbide drills 1 to 8 of the present invention will be described.
Of the coated carbide drills 1 to 8 of the present invention, the coated carbide drills 1 to 3 of the present invention and the coated carbide drills 1 to 3 of the present invention are: work material: plane dimension: 100 mm × 250, thickness: 50 m
m JIS SNCM439 plate material, Cutting speed: 120 m / min. , Feed: 0.12 mm / rev, Wet high-speed drilling test of alloy steel under the following conditions: coated carbide drills of the present invention 4-6 and conventional coated carbide drills 4-
About 6, work material: plane dimensions: 100 mm x 250 mm, thickness: 5
0 mm JIS S55C plate, Cutting speed: 100 m / min. , Feed: 0.25 mm / rev, Wet high-speed drilling test of carbon steel under the following conditions: coated carbide drills 7 and 8 of the present invention and conventional coated carbide drills 7 and 8
About 8, work material: plane dimension: 100 mm x 250 mm, thickness: 5
0mm JIS FC250 plate, Cutting speed: 100m / min. , Feed: 0.25mm / rev, Wet high-speed drilling cutting test of cast iron under the following conditions: In any wet high-speed drilling cutting test (using water-soluble cutting oil), flank wear of the cutting edge at the tip 0.3 width
The number of drilling processes up to mm was measured. The measurement results are shown in Tables 12 and 13, respectively. [Table 12] [Table 13] The coated carbide tips 1-20, coated end mills 1-8, and coated drill 1 of the present invention as the coated carbide tools of the present invention obtained as a result.
To 8 (Ti, Al) C layer and hard coating layer [(Ti, Al) N layer], and conventional coated carbide tips 1 to 20 as conventional coated carbide tools, Hard end mills 1-8 and conventional coated carbide drills 1-8
The composition of the hard coating layer [(Ti, Al) N layer]
When the central part in the thickness direction was measured using an Auger spectroscopic analyzer, it showed substantially the same composition as the target composition. Further, when the thickness of the above-described constituent layers of the coated carbide tool of the present invention and the conventional coated carbide tool was measured in cross section using a scanning electron microscope, the average layer thickness was substantially the same as the target layer thickness. The thickness (average value of five-point measurements) is shown. Furthermore, the above-mentioned constituent layers of the coated carbide tool of the present invention and the conventional coated carbide tool are observed on the rake face and / or flank of the cutting edge using an X-ray diffractometer using Cu-Kα radiation. From the X-ray diffraction pattern obtained as a result, (200)
Measure the half-value width of the peak appearing on the surface (in this case, if accurate measurement is difficult, use the X-ray diffraction pattern of the measurement piece simultaneously loaded in the arc ion plating apparatus in the above embodiment). Table 3 shows the measurement results.
To 6 and Tables 10 to 13, respectively. From the results shown in Tables 3 to 13, it can be seen that the (200) plane of the hard coating layer is highly oriented by the interposition of the crystal orientation history layer, whereby the high temperature properties (high temperature oxidation resistance and The coated carbide tool of the present invention, which has high-temperature hardness), while exhibiting excellent wear resistance even when cutting steel or cast iron at high speed with high heat generation, In the conventional coated carbide tool having a low orientation of the (200) plane of the hard coating layer, it is clear that the wear of the cutting edge progresses rapidly in high-speed cutting at high temperatures, and the service life is reached in a relatively short time. . As described above, the coated cemented carbide tool of the present invention exhibits excellent wear resistance especially in high-speed cutting of various steels and cast irons, and exhibits excellent cutting performance over a long period of time. The present invention can sufficiently satisfy the high performance of the cutting device, the labor saving and energy saving of the cutting process, and the cost reduction.

BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is an X-ray diffraction pattern of a hard coating layer of a coated superhard tip 15 of the present invention. FIG. 2 shows the X of the hard coating layer of the conventional coated carbide tip 15.
It is a line diffraction pattern. FIG. 3 is a schematic explanatory view of an arc ion plating apparatus. FIG. 4A is a schematic perspective view of a coated carbide tip, and FIG.
1 is a schematic vertical sectional view of a coated carbide tip. FIG. 5 (a) is a schematic front view of a coated carbide end mill,
(B) is a schematic transverse sectional view of the cutting blade portion. FIG. 6A is a schematic front view of a coated carbide drill, and FIG.
FIG. 3 is a schematic cross-sectional view of the groove forming portion.

──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. ⁷ Identification symbol FI theme coat ゛ (Reference) C23C 14/06 C23C 14/06 P (72) Inventor Akihiro Kondo 179 Kanegasaki Nishi-Oike, Uozumi-cho, Akashi-shi, Hyogo Prefecture Address 1 MMC Kobelcourt Co., Ltd. (72) Inventor Yusuke Tanaka 179 Kanegasaki Nishiike, Uozumi-cho, Akashi-shi, Hyogo 1 FMC Term Co., Ltd. 3C037 CC02 CC04 CC09 CC11 3C046 FF03 FF05 FF10 FF13 FF16 FF19 FF25 4K029 AA02 AA04 BA55 BA58 BB02 BB07 BD05 CA04 DD06

Claims (1)

Claims 1. A surface of a tungsten carbide-based cemented carbide substrate or a titanium carbonitride-based cermet substrate, (a) having an average layer thickness of 0.05 to 0.5 µm; (Ti _1-X Al _X ) C, where X is 0.05 to 0.20 in atomic ratio). Further, the measurement by an X-ray diffractometer using Cu-Kα ray shows that (200 (B) via a crystal orientation history layer composed of a Ti—Al composite carbide layer showing an X-ray diffraction pattern in which the highest peak appears on the plane and the half width of the highest peak is not more than 0.6 degree at 2θ, ) Having an average layer thickness of 2 to 15 μm, and satisfying the composition formula: (Ti _{1 -Y} Al _Y ) N (where Y represents 0.4 to 0.6 in atomic ratio). In the measurement with an X-ray diffractometer using Kα ray, the highest peak appeared on the (200) plane, Hard coating layer consisting of Ti-Al complex nitride layer showing an X-ray diffraction pattern with half peak width of 2 ° or less at 2θ of 0.6 ° or less by physical vapor deposition. Surface-coated cemented carbide cutting tool that exhibits excellent wear resistance.