JPH11323555A - Throw away cutting tip made of surface-coated cemented carbide excellent in wear resistance - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a cutting tip made of surface-coated cemented carbide excellent in wear resistance. SOLUTION: The surface of a cemented carbide substrate is cehcically vapor- deposited and/or physically vapor-deposited with a hard coating layer composed of (a) a TiN layer as a lowest layer, (b) a zone area mutually piled layer having a mutually piled structure of the multiple carbonitride zone area phases of Ti and Zr and the multiple carbo-nitride-oxide zone area phases of Ti and Zr, in which the highest and lowest phases are occupied by the Ti and Zr multiple carbonitride zone area phases, and moreover, a continuous longitudinally grown crystal structure is formed on the whole body of these zone area phases as a lowest layer, (c) one or >= two kinds among a TiC layer, a TiN layer, a TiCN layer, a TiCO layer, a TiNO layer and a TiCNO layer as an intermediate layer, (d) an α-Al2 O3 layer and/or a κ-Al2 O3 layer having the average layer thickness of 0.5 to 10 μm and (e) a TiN layer having the average layer thickness of 0.1 to 2 μm as the surface layer by the whole body average layer thickness of 5 to 20 μm.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a surface coated cemented carbide throw-away cutting tip (hereinafter referred to as coated cemented carbide tip) which exhibits excellent wear resistance especially in high-speed cutting of various steels. .

[0002]

2. Description of the Related Art Conventionally, for example, Japanese Patent Application Laid-Open No. 7-328809.
(A) nitriding of a granular crystal structure having an average layer thickness of 0.1 to 2 μm as a lowermost layer on the surface of a tungsten carbide-based cemented carbide substrate (hereinafter referred to as a cemented carbide substrate). Titanium (hereinafter, referred to as TiN) layer; (b) Titanium carbonitride (hereinafter, referred to as 1-TiCN) having a vertically elongated crystal structure having an average layer thickness of 3 to 15 μm as a lower layer
A layer, (c) an intermediate layer having an average layer thickness of 0.5 to 5 μm, each of which has a granular crystal structure, a Ti carbide layer, a nitride layer, a carbonitride layer, a carbonate layer, a nitroxide layer, And a carbonitride layer (hereinafter, TiC layer, TiN layer, T
iCN layer, TiCO layer, TiNO layer, and TiCNO
), And (d) as an upper layer, an α-type and / or κ-type aluminum oxide layer (hereinafter referred to as α-type) having a granular crystal structure having an average layer thickness of 0.5 to 10 μm. An Al ₂ O ₃ layer and a κ-Al ₂ O ₃ layer), (e) a titanium nitride (hereinafter referred to as TiN) layer having a granular crystal structure having an average layer thickness of 0.1 to 2 μm as a surface layer; There is known a coated superhard tip formed by subjecting the hard coating layer constituted by the above (a) to (e) to chemical vapor deposition and / or physical vapor deposition with a total average layer thickness of 5 to 20 μm. It is also well known that the coated cemented carbide tip is used for continuous cutting or intermittent cutting of various steels, for example. Further, the 1-TiCN layer constituting the hard coating layer of the coated superhard tip is disclosed in, for example, JP-A-3-87369.
And Japanese Patent Application Laid-Open No. 6-8008, 700 to 950 using a general chemical vapor deposition apparatus and a mixed gas containing an organic carbonitride as a reaction gas.
Formed by performing chemical vapor deposition in the medium temperature range of ℃,
It is also known to have excellent toughness.

[0003]

On the other hand, in recent years, there has been a strong demand for labor saving and energy saving in cutting work, and with this, cutting work tends to be performed at a higher speed. , 1-Ti constituting hard coating layer
CN layer has sufficient toughness, but on the other hand, because of insufficient hardness, especially when cutting various steel at high speed,
Since the wear of the cutting edge is remarkably promoted, the service life is currently reached in a relatively short time.

[0004]

Means for Solving the Problems Accordingly, the present inventors have
From the above-mentioned viewpoints, attention was paid to the above-mentioned conventional coated carbide tips, and a study was conducted to improve the hardness of the l-TiCN layer constituting the hard coating layer.
A part of i is replaced with Zr, and a composite carbonitride of Ti and Zr having a vertically elongated crystal structure [hereinafter, l- (Ti, Zr)
In this case, the l- (Ti, Zr) CN has a high hardness due to the solid solution content of Zr, but on the other hand, a decrease in toughness is inevitable as compared with the l-TiCN.
On the other hand, a part of Ti in TiCNO is replaced with Zr, and Ti and Z
a composite carbonitride of r and having a vertically-grown crystal structure [hereinafter referred to as 1- (Ti, Zr) CNO]
And these l- (Ti, Zr) CN and l- (T
When the lower layer of the hard coating layer is constituted by a structure in which the band phase is composed of i, Zr) CNO alternately, the lower layer has a toughness equivalent to the excellent toughness of the l-TiCN layer. After that, it has higher hardness than this, and the l- (Ti, Zr) CN band phase has excellent adhesion to the lowermost layer and the intermediate layer constituting the hard coating layer. The l- (Ti, Zr) CNO band phase has excellent adhesion to the l- (Ti, Zr) CN band phase, but does not have sufficient adhesion to these constituent layers. To the above l- (T
(i, Zr) Conforms with the CN band phase to ensure excellent adhesion, and is used as a lower layer of a hard coating layer of a coated carbide chip in a state where a continuous vertically grown crystal structure is formed in the entire band phase. Then, the zone alternately stacked layers constitute the hard coating layer of the conventionally coated carbide tip.
Having the same excellent toughness as the TiCN layer, and having a higher hardness than this, the coated carbide tip of this result can perform continuous cutting and interrupted cutting of various steels at high speed. The research results show that excellent wear resistance is exhibited over a long period of time.

The present invention has been made on the basis of the above research results, and comprises: (a) a TiN layer having an average layer thickness of 0.1 to 2 μm as a lowermost layer,
(B) The lower layer has an average layer thickness of 3 to 15 μm, and has a 1- (Ti, Zr) CN band phase and 1- (Ti, Z).
r) The CNO band phase has an alternately stacked structure, but the uppermost phase and the lowermost phase are occupied by the 1- (Ti, Zr) CN band phase, and further, these band phases form a continuous vertically grown crystal structure. (C) As an intermediate layer, a TiC layer and a TiC layer having an average layer thickness of 0.5 to 5 μm.
N layer, TiCN layer, TiCO layer, TiNO layer, and T layer
one or more of the iCNO layers, (d) as an upper layer, α-Al ₂ having an average layer thickness of 0.5 to 10 μm.
An O ₃ layer and / or a κ-Al ₂ O ₃ layer, (e) a TiN layer having an average layer thickness of 0.1 to 2 μm as a surface layer,
The hard coating layer composed of (a) to (e) is
It is characterized by a coated carbide tip having excellent wear resistance, which is obtained by chemical vapor deposition and / or physical vapor deposition with a total average layer thickness of μm.

Next, the reason why the average layer thickness and the overall average layer thickness of the constituent layers of the hard coating layer of the coated superhard tip of the present invention are limited as described above will be described. (A) Lowermost layer (TiN layer) The TiN layer has excellent adhesion to the surface of the superhard substrate, and prevents diffusion and migration of the components of the superhard substrate into the hard coating layer. It has an effect of suppressing the deterioration of the property, but if the layer thickness is less than 0.1 μm, the above effect is not sufficiently exerted. On the other hand, the above effect is sufficient with a layer thickness of up to 2 μm. It was determined to be 1-2 μm.

(B) Lower layer (Alternate stacked layer of band phase) The alternating layer of band phase is formed entirely of l-Ti as described above.
Having the same excellent toughness as the CN layer, and having a higher hardness than this, this layer constitutes a hard coating layer. In addition, excellent wear resistance is exhibited without causing chipping or chipping in the cutting edge, but if the layer thickness is less than 3 μm, the desired wear resistance is exhibited over a long period of time. On the other hand, if the layer thickness exceeds 15 μm, thermoplastic deformation tends to occur in the cutting edge portion, which causes uneven wear. Therefore, the layer thickness is set to 3 to 15 μm.

(C) Intermediate layer (TiC layer, TiN layer, Ti
CN layer, TiCO layer, TiNO layer, and TiCNO
Layer) The above-mentioned 1- (Ti,
Zr) The adhesion between the CN band phase and the α- and κ-Al ₂ O ₃ layers is relatively low, and when both are directly laminated,
Although each of these layers causes the peeling of the hard coating layer, each of these layers is composed of the above-mentioned 1- (Ti, Zr) CN band phase and α-A
The layer firmly adheres to both the l ₂ O ₃ layer and the κ-Al ₂ O ₃ layer, thereby contributing to the improvement of the adhesion between the constituent layers of the hard coating layer. However, when the layer thickness is less than 0.5 μm, it is desirable. Does not have the effect of improving the adhesion, while the layer thickness is 5 μm
If the thickness exceeds 0.5 mm, chipping or chipping is likely to occur in the cutting edge portion, so the layer thickness is set to 0.5 to 5 μm.

(D) Upper layer (α-Al ₂ O ₃ layer and κ-
Al ₂ O ₃ layer) Since the α-Al ₂ O ₃ layer and the κ-Al ₂ O ₃ layer are both excellent in oxidation resistance and thermal stability and have high hardness, the rake face in the cutting edge portion However, when the layer thickness is less than 0.5 μm, the desired effect of improving the wear resistance cannot be obtained. On the other hand, when the layer thickness exceeds 10 μm, the cutting edge lacks. Since layering and chipping easily occur, the layer thickness is set to 0.5 to 10 μm.

(E) Surface layer (TiN layer) Since the TiN layer itself has a golden color tone, it is formed to make it easy to identify the cutting tip before and after use. Therefore, when the layer thickness is less than 0.1 μm, the application of the color tone is insufficient, and on the other hand, the layer thickness up to 2 μm is sufficient, so the layer thickness is set to 0.1 to 2 μm. .

(F) Overall Average Layer Thickness of Hard Coating Layer When the layer thickness is 5 μm, the desired excellent wear resistance cannot be ensured. On the other hand, when the layer thickness exceeds 20 μm,
Since chipping and chipping easily occur in the cutting edge,
The overall average layer thickness was determined to be 5 to 20 μm.

[0012]

Next, the coated cemented carbide tip of the present invention will be specifically described with reference to examples. As raw material powder,
Average particle size: fine WC powder having 1.5 μm, same as 3 μm
Medium WC powder, 1.2 μm (Ti, W) CN (weight ratio, same hereafter, TiC / TiN / WC = 24/20)
/ 56) powder, 1.2 μm ZrC powder, 1.3 μm
m (Ta, Nb) C (TaC / NbC = 90/10)
Powder, 1 μm Cr powder, and 1.2 μm Co powder
Powders are prepared, and these raw material powders are blended in the composition shown in Table 1, wet-mixed in a ball mill for 72 hours, dried, and then pressed into a green compact of a predetermined shape. Carbide substrates A to E having shapes conforming to ISO • CNMG120408 were manufactured by vacuum sintering under the conditions shown in Table 1. Further, the cemented carbide substrate E was heated to 80 Torr in a CH ₄ gas atmosphere at a temperature of 1: 1.
After holding at 420 ° C. for 1 hour, a slow cooling carburizing treatment is performed, and after the treatment, carbon and Co adhering to the surface of the super hard substrate are removed by acid and barrel polishing, so that the maximum Co content at a position of 11 μm from the surface is contained. Amount: 17.5% by weight, depth: 36μ
A Co-enriched zone of m was formed on the surface of the substrate. In addition, while the sintered body was still sintered, the superhard substrate C had a Co-rich zone having a maximum Co content of 10.9 wt% and a depth of 25 µm on the surface at a position of 18 µm from the surface. In the base D,
Maximum Co content at a position 18 μm from the surface on the surface: 1
A Co-enriched zone of 2.7% by weight and a depth of 23 μm is formed respectively, and the remaining carbide substrates A and B have no homogeneous Co-enriched zone and have an overall homogeneous structure. I had it. Table 1 shows that the super hard substrates A to E
Of each sample (Rockwell hardness A scale).

Next, the surface of each of the superhard substrates A to E is subjected to honing processing, and a conventional chemical vapor deposition apparatus is used. No. 4,078,098, which has a vertically-grown crystal structure described in Japanese Patent Application Laid-Open Publication No. H11-207, and a l- (Ti, Zr) CN band phase is based on the conditions for forming the l-TiCN layer, and ZrCl ₄ is added thereto as a reaction gas. are those formed under the conditions, further l- (Ti, Zr) CNO band phase also well as the basic forming conditions of the l-TiCN layer, which in one form under the conditions plus ZrCl ₄ and CO as reaction gas Under the conditions shown in Tables 3 and 4 to form hard coating layers having the layer configurations and average layer thicknesses shown in Tables 3 and 4, thereby obtaining coated superhard chips 1 to 10 of the present invention and comparative superhard chips 1 to Each Manufactured.

Next, the coated carbide tips 1 to 1 according to the present invention will be described.
Workpiece: SCM440 round bar, Cutting speed: 320 m / min. Infeed: 2.0 mm Feed: 0.25 mm / rev. Cutting time: 10 minutes, Dry high-speed continuous cutting test of alloy steel under the following conditions: Work material: Round bar with four longitudinal grooves at equal intervals in the longitudinal direction of S45C, Cutting speed: 350 m / min. Infeed: 1.5 mm Feed: 0.3 mm / rev. A dry high-speed intermittent cutting test of carbon steel was performed under the following conditions: cutting time: 10 minutes. In each cutting test, the flank wear width of the cutting edge was measured, and the wear resistance was evaluated. Table 5 shows the results of these measurements.

[0015]

[Table 1]

[0016]

[Table 2]

[0017]

[Table 3]

[0018]

[Table 4]

[0019]

[Table 5]

[0020]

According to the results shown in Table 5, the lower layer of the hard coating layer is composed of the l- (Ti, Zr) CN band phase and the l- (Ti, Z).
r) The coated carbide tips 1 to 10 according to the present invention each having an alternately stacked structure with a CNO zone phase, and constituted by zone phase alternating stacked layers formed by forming a vertically elongated crystal structure that is continuous with the entire zone phase, In any case, the lower layer of the hard coating layer is made of l-TiC without any chipping or chipping.
It is evident that the abrasion resistance is much higher than that of the comparative coated carbide tips 1 to 10 composed of N layers. As described above, the coated cemented carbide tip of the present invention has excellent wear resistance, not only in continuous cutting and intermittent cutting of various steels under ordinary conditions, but also in particular when these cuttings are performed at high speed. It exhibits excellent cutting performance over a long period of time, and can sufficiently cope with labor saving and energy saving in cutting.

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[Procedure amendment]

[Submission date] October 20, 1998

[Procedure amendment 1]

[Document name to be amended] Statement

[Correction target item name] 0015

[Correction method] Change

[Correction contents]

[0015]

[Table 1]

 ──────────────────────────────────────────────────続 き Continued on the front page (72) Inventor Yuki Hamaguchi 1511 Furimagi, Ishishita-cho, Yuki-gun, Ibaraki Prefecture Inside the Tsukuba Works, Mitsubishi Materials Corporation (72) Inventor Masayuki Miichi 1511 Furimagi, Ishishita-cho, Yuki-gun, Ibaraki Prefecture Address Mitsubishi Materials Corporation Tsukuba Works

Claims (1)

[Claims] 1. A surface of a tungsten carbide-based cemented carbide substrate, comprising: (a) a titanium nitride layer having a granular crystal structure having an average layer thickness of 0.1 to 2 μm as a lowermost layer; It has an average layer thickness of 15 μm and has an alternately stacked structure of a composite carbonitride zone phase of Ti and Zr and a composite carbonitride zone phase of Ti and Zr. A band-phase alternating stacked layer in which a composite carbonitride band phase of Ti and Zr occupies and further forms a continuous vertically-grown crystal structure in the entire band phase; (c) an average of 0.5 to 5 μm as an intermediate layer One or more of a Ti carbide layer, a nitride layer, a carbonitride layer, a carbonate layer, a carbonitride layer, and a carbonitride layer, each having a layer thickness and a granular crystal structure, (D) As upper layer, granular crystals having an average layer thickness of 0.5 to 10 μm An α-type and / or κ-type aluminum oxide layer of the structure; (e) a titanium nitride layer having a granular crystal structure having an average layer thickness of 0.1 to 2 μm as a surface layer; A wear-resistant surface coated cemented carbide throw-away cutting tip comprising a hard coating layer formed by chemical vapor deposition and / or physical vapor deposition with a total average layer thickness of 5 to 20 μm.