JP2002361502A - Surface covered cemented carbide made cutting tool excellent in surface lubricity against chip - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a surface covered cemented carbide made cutting tool excellent in surface lubricity against chips. SOLUTION: This surface covered cemented carbide made cutting tool is constituted of chemically evaporating and/or physically evaporating (a) a Ti compound layer made of a lamination layer made of one or more than two kinds of a Ti carbide layer, a nitride layer, a carbonitride layer, a carbooxide layer and a carbonitroxide layer having average layer thickness of 1-20 μm as a lower part layer, (b) an aluminum oxide and zirconium oxide mixed layer made by dispersing and distributing a zirconium oxide phase on a basis of an aluminum oxide layer and/or aluminum oxide having average layer thickness of 1-15 μm as an upper part layer, (c) a compound oxide layer of Zr and V having average layer thickness of 0.1-5 μm as a surface lubricating layer and to satisfy 0.1-0.6 at X: an aromatic ratio and 1.2-1.9 at Y: an atomic ratio against total quantity of Zr and V by measuring a central part in the thickness direction by an Auger spectrochemical analysis device in the case of expressing it by a composition formula: (Zr1- XVX)OY and a covered layer constituted of the above (a)-(c) on a surface of a tungsten carbide base cemented carbide base body.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to high-speed cutting of difficult-to-cut materials having excellent surface lubricating properties against chips and, in particular, extremely viscous materials such as stainless steel and mild steel, and the chips are easily welded to the cutting blade surface. Even when used for machining, cutting with a surface-coated cemented carbide that exhibits excellent cutting performance over a long period of time without chipping (small chipping) due to the high stickiness of the cutting chips on the cutting blade The present invention relates to a tool (hereinafter, referred to as a coated carbide tool).

[0002]

2. Description of the Related Art Generally, cutting tools include a throw-away tip which is removably attached to a tip of a cutting tool for turning or planing of various materials such as steel and cast iron. Drills and miniature drills used for drilling and drilling, etc., and furthermore, there are solid type end mills used for face milling and grooving of the work material, shoulder machining, and the like, and the detachable tip is detachably attached. In addition, a throw-away end mill tool or the like that performs cutting in the same manner as the solid type end mill is known. Further, conventionally, generally, as the above-mentioned cutting tool, a tungsten carbide-based cemented carbide substrate (hereinafter, referred to as
(Referred to as a super-hard substrate), and (a)
Ti carbide (hereinafter referred to as T) having an average layer thickness of 20 μm
iC) layer, nitride (hereinafter also indicated by TiN)
, A carbonitride (hereinafter, referred to as TiCN) layer, a carbon oxide (hereinafter, referred to as TiCO) layer, and a Ti or a carbonitride (hereinafter, referred to as TiCNO) layer. Compound layer, (b) 1 to 15 as upper layer
Aluminum oxide (hereinafter referred to as A) having an average layer thickness of μm
l ₂ O indicated by ₃₎ layer, and for example, JP 57-3916
Zirconium oxide matrix of Al ₂ O ₃ which is described in 8 and JP 61-201778 discloses (hereinafter, ZrO ₂
A coating layer composed of one or both of an Al ₂ O ₃ -ZrO ₂ mixed layer (hereinafter, referred to as an Al ₂ O ₃ -ZrO ₂ mixed layer) in which phases are dispersed and distributed. A coated carbide tool formed by physical vapor deposition is known.

In general, the Ti compound layer and the Al ₂ O ₃ layer constituting the coating layer of the coated cemented carbide tool have a granular crystal structure, and the Al ₂ O ₃ layer has an α-type crystal structure. And those having a κ-type crystal structure have been widely put to practical use. Further, as described in JP-A-6-8010 and JP-A-7-328808, for example, For the purpose of improving the toughness of the layer itself, a TiCN layer among the Ti compound layers constituting the layer is mixed with a normal chemical vapor deposition apparatus using a mixed gas containing an organic CN compound as a reaction gas at 700 to 950 ° C. It is also known to form a vertically elongated crystal structure by chemical vapor deposition in a medium temperature range.

[0004]

In recent years, the use of FA in cutting equipment has been remarkable. On the other hand, there is a strong demand for labor saving, energy saving, and lower cost for cutting work. Versatility that can cut as many types of work materials as possible is required,
Cutting also tends to be faster, but in the above-mentioned conventional coated carbide tools, there is no problem if this is used for cutting under ordinary conditions such as steel or cast iron, but this is extremely viscous. When used for high-speed cutting of work materials such as stainless steel and mild steel with high hardness, the chips of these work materials have a high affinity for the Al ₂ O ₃ layer and the Ti compound layer that constitute the coating layer. In addition, it is easy to weld to the cutting blade surface, and this welding phenomenon becomes more noticeable as the cutting speed increases,
At the present, chipping occurs in the cutting blade due to this welding phenomenon, and as a result, the service life is reached in a relatively short time.

[0005]

Means for Solving the Problems Accordingly, the present inventors have
From the viewpoints described above, especially when used for high-speed cutting of difficult-to-cut materials such as stainless steel and mild steel, in order to develop a coated cemented carbide tool that is difficult to weld chips to the cutting blade surface, focusing on the conventional coated cemented carbide tool, as a result of the study, at (a), for example, chemical vapor deposition apparatus, the reaction gas composition, by _{volume%, ZrCl 4: 0.2~10%,} VCl 4: 0.1 ~
_{5%, CO 2: 0.1~10%} , Ar: 5~60%,
When a layer is formed under the following conditions: H ₂ : remaining, reaction atmosphere temperature: 800 to 1100 ° C., reaction atmosphere pressure: 4 to 70 kPa, a composite oxide of Zr and V [hereinafter, (Zr, V ) O] layer is formed.

(B) When the (Zr, V) O layer is represented by the composition formula (Zr ₁ -XV _X ) O _Y , the above-mentioned layer forming conditions are adjusted to adjust the center in the thickness direction. Is measured by an Auger spectrometer, and X: 0.1-0.6, Y: 1.2-1.9 in atomic ratio to the total amount of Zr and V, , This (Zr, V)
The O layer is decomposed into Zr oxide and V oxide, which have extremely low affinity for work materials, particularly, highly viscous and difficult-to-cut materials such as stainless steel and mild steel, particularly due to high heat generated during cutting, and When both coexist, the Zr oxide and the V oxide exhibit more excellent surface lubricity than the surface lubricity exhibited individually by the synergistic effect.

(C) Therefore, the (Zr, V) O layer is used as a surface lubricating layer in the conventional coated carbide tool.
In a coated cemented carbide tool formed by chemical vapor deposition or physical vapor deposition with an average layer thickness of 1 to 5 μm, the excellent surface lubricity exhibited by the (Zr, V) O layer constituting the surface lubricating layer is particularly preferable for stainless steel. Chips of hard-to-cut materials, such as steel and mild steel, are not welded to the cutting edge, and this is the same even in high-speed cutting processing with even higher heat generation. To exhibit excellent cutting performance over

(D) The (Zr, V) O layer is coated on the surface of the Al ₂ O ₃ layer or the Al ₂ O ₃ -ZrO ₂ mixed layer constituting the coating layer of the above-mentioned conventional coated carbide tool with a surface lubricating layer. When the Y value is on the lower side in the range of 1.2 to 1.9, for example, in the range of 1.2 to 1.4, or the average layer thickness is 0.1 to 5 μm. When the film is formed on the thin side within the range of, for example, 0.1-1 μm, sufficient interlayer adhesion between the Al ₂ O ₃ layer and the Al ₂ O ₃ -ZrO ₂ mixed layer is obtained. [Of course, even in these cases, sufficient interlayer adhesion can be obtained by adjusting the conditions for forming the (Zr, V) O layer]. In this case, , The above (Zr, V) O
After forming the layer, the following atmosphere, that is, the atmosphere gas composition,
By volume%, ZrCl ₄ : 0.05 to 10%, VCl ₄ :
0.05 to 5%, inert gas: remaining, and ambient temperature: 800 to 1100 ° C., atmospheric pressure: 4 to 90 kPa, for a predetermined time, for example, about 5 minutes to 5 hours. , the interface portion between the (Zr, V) O layer and the the Al ₂ O ₃ layer or Al ₂ O ₃ -ZrO ₂ mixed layer, preferably forming a mutual diffusion layer with an average layer thickness of 0.05~2μm It is desirable to improve the interlayer adhesion by this, and furthermore, this interlayer adhesion improving treatment is a process in which the Y value and the average layer thickness of the (Zr, V) O layer are values other than the values on the low side and the thin side. Even if it is the case, it may be performed for the purpose of further improving the interlayer adhesion. (A) to (d) above
The research results shown in the above were obtained.

The present invention has been made on the basis of the above research results, and comprises: (a) a TiC layer having an average layer thickness of 1 to 20 μm as a lower layer,
TiN layer, TiCN layer, TiCO layer, and TiCNO
A Ti compound layer comprising one or more of the layers,
(B) as the upper layer has an average layer thickness of 1 to 15 m, Al ₂ O ₃ layer and / or Al ₂ O ₃ -ZrO ₂ mixed layer, as (c) a surface lubricating layer, the average of 0.1~5μm When it has a layer thickness and is represented by the composition formula: (Zr ₁ -XV _X ) O _Y , the central part in the thickness direction is measured by an Auger spectroscopic analyzer, and X: 0.1 to 0.1. 6, Y: a (Zr, V) O layer satisfying the atomic ratio to the total amount of Zr and V of 1.2 to 1.9, and a coating layer composed of the above (a) to (c) by chemical vapor deposition. And / or physical vapor deposition, which is characterized by a coated carbide tool having excellent surface lubricity to chips.

In the coated carbide tool of the present invention, the V component of the (Zr, V) O layer constituting the surface lubricating layer has a high viscosity such as stainless steel or mild steel due to heat generated during cutting as described above. It has the effect of decomposing into a V oxide having an extremely low affinity for difficult-to-cut materials and, at the same time, exhibiting excellent surface lubricity to the difficult-to-cut materials in a state where it coexists with the Zr oxide generated by decomposition. If the ratio (atomic ratio) to the total amount of Zr and Zr, that is, the X value is less than 0.1, the ratio of the Zr oxide generated during the cutting becomes relatively too large, and the surface lubrication by substantially only the Zr oxide On the other hand, when the X value exceeds 0.6, the production of the Zr oxide becomes too small, and the excellent surface lubricity brought about by the coexistence of the Zr oxide and the V oxide tends to decrease. Become , Defining the X value and 0.1 to 0.6. The oxygen (O) in the (Zr, V) O layer
The atomic ratio (Y value) to the total amount of r and V is 1.2 to 1.9.
The reason is that if the value is less than 1.2, the desired excellent surface lubricity cannot be secured, while the value is 1.9.
If the ratio exceeds the above range, pores are easily formed in the layer, and it is difficult to stably form a sound surface layer. Further, the average layer thickness of the (Zr, V) O layer is set to 0.
If the average layer thickness is less than 0.1 μm, the desired surface lubricity cannot be ensured. On the other hand, the surface lubricity imparting action is sufficiently performed with the average layer thickness of 5 μm. It is based on the reason that you can do it.

[0011] In the coated carbide tool of the present invention,
The lower layer (Ti compound layer) that constitutes the coating layer imparts excellent toughness to the coating layer so that the tool exhibits excellent fracture resistance, and the adhesion between the constituent layers of the coating layer. But the average layer thickness is 1μ
If the average thickness is less than 20 μm, on the other hand, if the average layer thickness exceeds 20 μm, it becomes easy to cause thermoplastic deformation which causes uneven wear during cutting, so that the average layer thickness is 1 to It was determined to be 20 μm. Further, the upper layer (Al ₂ O ₃ layer and / or Al ₂ O ₃ -ZrO ₂ mixed layer) has excellent high-temperature hardness, heat resistance, and thermal stability, and due to these characteristics, the resistance of the tool is improved. It has the effect of improving abrasion. However, if the average layer thickness is less than 1 μm, the desired effect cannot be obtained, while the average layer thickness is less than 15 μm.
If the thickness exceeds μm, chipping is likely to occur on the cutting edge. Therefore, the average layer thickness is set to 1 to 15 μm.

[0012]

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Next, the coated carbide tool of the present invention will be specifically described with reference to examples. (Example 1) As raw material powders, each was 0.5 to 4 μm.
WC powder having a predetermined average particle size in the range of (Ti,
W) CN [mass ratio, hereinafter the same, TiC / TiN / WC
= 24/20/56] powder, (Ta, Nb) C (TaC
/ NbC = 90/10) powder, ZrC powder, Cr ₃ C ₂ powder, and Co powder were prepared, and these raw material powders were blended in the composition shown in Table 1, wet-mixed in a ball mill for 72 hours, and dried. Thereafter, a green compact of a predetermined shape is press-molded at a pressure of 100 MPa, and the green compact is vacuum-sintered under the same conditions as shown in Table 1, and subjected to grinding and honing at 0.05R to obtain ISO / CNMG120408. Carbide bases (tips) A to E having a throw-away tip shape as specified in (1) were manufactured. In addition, in the resulting super-hard substrates (chips) A to E, the maximum Co content of the super-hard substrate C at the position of 20 μm from the surface: 7. 9% by mass, depth: 26 μm, Co-enriched zone, the surface of the cemented carbide substrate D has a maximum Co content at the position of 18 μm from the surface: 11.
5% by mass, Co-enriched zone with a depth of 24 μm, Co-enriched zone with a maximum Co content of 14.2% by mass and a depth of 28 μm on the surface of the cemented carbide substrate E at a position 22 μm from the surface. Are formed, and the remaining cemented carbide substrates A and B
Did not have the Co-enriched zone and had a uniform structure as a whole. Further, Table 1 shows the internal hardness (Rockwell hardness A scale) of each of the carbide substrates A to E.

Next, these super-hard substrates (chips) A to
Tables 2 and 3 (l-TiCN in Table 2 shows the conditions for forming a TiCN layer having a vertically-grown crystal structure described in JP-A-6-8010, using a conventional chemical vapor deposition apparatus on the surface of E. The other conditions are the conditions for forming a normal granular crystal structure.) By forming a coating layer having the composition and target layer thickness shown in Table 4 under the conditions shown in FIG. (A) is a schematic perspective view, and (b) is a coated carbide tool according to the present invention as a coated carbide tool having a shape shown in a schematic longitudinal sectional view. 1 to 10).

The coated carbide tips 1 to 1 of the present invention described above.
In the case of the present invention-coated carbide tip 1 and the present invention-coated cemented carbide tip 3 among 0, in the former, the atmosphere gas composition is Z
rCl ₄ : 1% by volume, VCl ₄ : 0.5% by volume, Ar: remaining, ambient temperature 1020 ° C, ambient pressure 7 kP
a for 1 hour in the atmosphere defined as a, and in the latter, the atmosphere gas composition was ZrCl ₄ : 0.2% by volume, VC
l ₄ : 0.1% by volume, Ar: remaining, ambient temperature is 1
In an atmosphere of 000 ° C. and an atmospheric pressure of 20 kPa.
The upper layer (Al ₂ O ₃ layer or Al ₂ O ₃
-ZrO ₂ mixed layer) and surface lubrication layer [(Zr, V) O layer]
Was subjected to an interlayer adhesion improving treatment for forming an interdiffusion layer at the interface. After the above-mentioned interlayer adhesion improving treatment, the thickness of the interdiffusion layer was measured using a scanning electron microscope and an Auger spectrometer. The average value of the five measurements was 0.9 μm for the former and 0. The average layer thickness of 6 μm is shown.

For the purpose of comparison, as shown in Table 5, the conventional surface coating as a conventional coated carbide tool was performed under the same conditions except that the (Zr, V) O layer as the surface lubricating layer was not formed. Cemented carbide throw-away tips (hereinafter referred to as conventionally coated cemented carbide tips) 1 to 10 were produced, respectively.

Next, the coated carbide tips 1 to 1 according to the present invention will be described.
0 and the conventional coated carbide tips 1 to 10 were screwed to the tip of a tool steel tool with a fixing jig. Work material: JIS SUS316 round bar, Cutting speed: 320 m / min . Infeed: 0.25 mm / rev. , Cutting time: 10 minutes, Dry high-speed continuous cutting test of stainless steel under the following conditions: Work material: JIS S15C, 4 longitudinally spaced round bars at regular intervals in the longitudinal direction, Cutting speed: 330 m / min. Infeed: 1.5 mm Feed: 0.25 mm / rev. A dry high-speed intermittent cutting test of mild steel was performed under the following conditions: cutting time: 10 minutes, and the flank wear width of the cutting edge was measured in each cutting test. This measurement result is shown in Table 6 as an average value of five test pieces.

[0017]

[Table 1]

[0018]

[Table 2]

[0019]

[Table 3]

[0020]

[Table 4]

[0021]

[Table 5]

[0022]

[Table 6]

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
μm of (Ti, W) C powder and 1.8 μm of Co
Powders are prepared, and each of these raw material powders is blended in the composition shown in Table 7, further wet-mixed in a ball mill for 72 hours, dried, and then pressed into various compacts of a predetermined shape at a pressure of 100 MPa. , These compacts are 6P
1370-1 at a heating rate of 7 ° C./min in the vacuum atmosphere of a.
The temperature is raised to a predetermined temperature in the range of 470 ° C.
After holding for a time, sintering was carried out under the condition of furnace cooling.
Three types of round bar sintered bodies for forming a cemented carbide substrate of 3 mm and 26 mm are formed, and the above three types of round bar sintered bodies are further ground by a cutting process in a combination shown in Table 7 by grinding. Diameter of part ×
Each length is 6mm x 13mm, 10mm x 22m
m, and four-flute square-shaped carbide substrates (end mills) a to e having dimensions of 20 mm × 45 mm were produced, respectively.

Next, these super-hard substrates (end mills)
The surfaces of a to e were ultrasonically cleaned in acetone, dried, and then dried, using the same general chemical vapor deposition apparatus, under the same conditions as shown in Tables 2 and 3, and the compositions and target layers shown in Table 8. By forming a thick coating layer, the present invention as a coated carbide tool of the present invention having a shape shown in a schematic front view in FIG. 2A and a schematic cross-sectional view of a cutting edge portion in FIG. End mills 1 to 8 made of surface-coated cemented carbide (hereinafter referred to as “coated cemented carbide end mills of the present invention”) were manufactured.

For the purpose of comparison, as shown in Table 9, under the same conditions except that the (Zr, V) O layer as the surface lubricating layer was not formed, the conventional surface-coated super-hard tool as the conventional coated carbide tool was used. End mills made of hard alloy (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 as follows: Work material: plane dimension: 100 mm × 250 mm, thickness: 5
0 mm JIS S15C plate material, Cutting speed: 130 m / min. , Groove depth (cut): 2 mm, table feed: 600 mm / min, form: dry type (air blow), high speed grooving test of mild steel under the following conditions, coated carbide end mills 4 to 6 of the present invention and conventional coated carbide For the end mills 4 to 6, work material: plane size: 100 mm x 250 mm, thickness: 5
0 mm JIS SUS420J2 plate, Cutting speed: 110 m / min. , Groove depth (cut): 4 mm, Table feed: 300 mm / min, Form: High-speed grooving test of stainless steel under wet (water-soluble cutting oil) conditions, coated carbide end mills 7 and 8 of the present invention and conventional coated For the carbide end mills 7 and 8, work material: plane dimension: 100 mm x 250 mm, thickness: 5
0 mm JIS SUS630 plate material, Cutting speed: 90 m / min. , Groove depth (cut): 8 mm, Table feed: 150 mm / min, Form: Wet (water-soluble cutting oil), High speed grooving test of stainless steel under the following conditions. The cutting groove length was measured until the flank wear width of the blade was reduced by 0.1 mm, which is a measure of the service life. The measurement results are shown in Tables 8 and 9, respectively.

[0027]

[Table 7]

[0028]

[Table 8]

[0029]

[Table 9]

(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 22 mm (the carbide substrate a ') by grinding from the three types of round rod sintered bodies. , B '), 8 mm
× 37 mm (carbide substrate c ′, d ′) and 16 mm ×
Carbide substrates (drills) a 'to e' each having a size of 58 mm (carbide substrate e ') were produced.

Next, the super hard substrate (drill) a '
-E 'were ultrasonically cleaned in acetone, dried and dried in the same manner using a conventional chemical vapor deposition apparatus under the conditions shown in Tables 2 and 3 and the composition and target layer shown in Table 10. By forming a thick coating layer, FIG.
In the schematic front view, a drill made of the surface-coated cemented carbide of the present invention as the coated cemented carbide tool of the present invention having the shape shown in the schematic cross-sectional view of the groove forming portion (b) (hereinafter, the coated carbide of the present invention) Drills) 1 to 8 were manufactured respectively.

For the purpose of comparison, as shown in Table 11, under the same conditions except that the (Zr, V) O layer as the surface lubricating layer was not formed, the conventional surface-coated super-hard tool as a conventional coated super-hard tool was obtained. Drills made of hard alloys (hereinafter referred to as conventional coated carbide drills) 1 to 8 were manufactured, respectively.

Next, the above-mentioned coated carbide drills 1 to 8 according to the present invention.
Among 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 mm
JIS S20C plate material, Cutting speed: 110 m / min. , Hole depth: 8 mm, feed: 0.2 mm / rev, wet high speed drilling test of mild steel, coated carbide drills 4-6 according to the present invention and conventional coated carbide drills 4-6
About: Work material: Plane dimensions: 100 mm x 250 mm, thickness: 5
JIS SUS630 plate material of 0 mm, Cutting speed: 110 m / min. , Hole depth: 15 mm, Feed: 0.2 mm / rev, Wet high-speed drilling test of stainless steel under the following conditions: coated carbide drills 7 and 8 of the present invention and coated carbide drills 7 and 8 of the prior art Work material: Plane dimensions: 100 mm x 250 mm, thickness: 5
0 mm JIS S15C plate, Cutting speed: 150 m / min. , Hole depth: 30mm, Feed: 0.25mm / rev, Wet cutting test for mild high-speed drilling of mild steel under the following conditions: In any wet type (using water-soluble cutting oil) high-speed drilling cutting test The flank wear width of the blade surface is 0.3
The number of drilling processes up to mm was measured. The measurement results are shown in Tables 10 and 11, respectively.

[0034]

[Table 10]

[0035]

[Table 11]

The coated carbide tips 1-10, the coated end mills 1-8, and the coated drill 1 of the present invention as the coated carbide tools of the present invention obtained as a result.
The V content and the oxygen (O) content (X value and Y value) at the center in the thickness direction of the surface lubricating layers Nos. To 8 were measured using an Auger spectrometer, and the target shown in Table 3 was obtained. The value was substantially the same as the value. Further, the coated layers of the coated carbide tools of the present invention and the conventionally coated carbide tips 1 to 10, the conventionally coated carbide end mills 1 to 8 and the conventionally coated carbide drills 1 to 8 as the conventionally coated carbide tools are described. When the thicknesses of the constituent layers were measured in cross section using a scanning electron microscope, all of them showed substantially the same average layer thickness as the target layer thickness (average value of five-point measurements).

[0037]

According to the results shown in Tables 4 to 11, all of the coated carbide tools of the present invention in which the (Zr, V) O layer is formed as the surface lubricating layer can generate high heat while cutting stainless steel and mild steel. Even at the accompanying high speed, the (Zr, V) O layer has extremely low affinity with the high-temperature heated chips, the chips do not adhere to the (Zr, V) O layer, and the cutting edge is Since excellent surface lubricity is always maintained, chipping due to chip welding to the cutting edge does not occur on the cutting edge, and excellent wear resistance is exhibited.
V) In the conventional coated cemented carbide tool without formation of the O layer, chips are easily welded to the coating layer, and the coating layer is locally peeled off due to this. It is clear that the service life can be reached in an extremely short time. As described above, the coated cemented carbide tool of the present invention is not limited to cutting under ordinary conditions such as various types of steel and cast iron,
In particular, it exhibits excellent surface lubricity against chips even in high-speed cutting such as stainless steel and mild steel, which are highly viscous and chips easily adhere to the cutting blade surface, and show versatile cutting performance. Therefore, it is possible to satisfactorily cope with the use of the FA in the cutting device, the labor saving and energy saving of the cutting process, and the cost reduction.

[Brief description of the drawings]

FIG. 1A is a schematic perspective view of a coated carbide tip, and FIG.
1 is a schematic longitudinal sectional view of a coated carbide tip.

FIG. 2 (a) is a schematic front view of a coated carbide end mill,
(B) is a schematic cross-sectional view of the cutting blade portion.

FIG. 3A 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.

Continued on the front page F term (reference) 3C046 FF03 FF10 FF11 FF13 FF16 FF19 FF22 FF25 4K029 BA41 BA44 BA50 BA54 BA55 BA60 BC00 BD05 EA01 4K030 BA35 BA36 BA38 BA41 BA42 BA43 CA05 JA01 LA01 LA22

Claims (1)

[Claims] 1. A surface of a tungsten carbide-based cemented carbide substrate, comprising: (a) as a lower layer, a carbide layer, a nitride layer, a carbonitride layer, and a carbonate layer of Ti having an average layer thickness of 1 to 20 μm. And a Ti compound layer composed of one or more of carbon oxynitride layers. (B) As an upper layer, an aluminum oxide layer and / or an aluminum oxide substrate having an average layer thickness of 1 to 15 μm. An aluminum oxide-zirconium oxide mixed layer in which a zirconium oxide phase is dispersed and distributed; (c) a surface lubricating layer having an average layer thickness of 0.1 to 5 μm, and a composition formula: (Zr _1−X V _X) ) When represented by O _Y , the central part in the thickness direction is measured by an Auger spectrometer, and X: 0.1 to 0.6, Y: 1.2 to atomic ratio to the total amount of Zr and V 1.9, a composite oxide of Zr and V satisfying , More than (a) ~
A surface-coated cemented carbide cutting tool having excellent surface lubricity against chips, obtained by subjecting the coating layer constituted by (c) to chemical vapor deposition and / or physical vapor deposition.