JP2012179706A - Surface coated cutting tool having hard coated layer exhibiting excellent wear resistance - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a surface coated cutting tool having a hard coated layer exhibiting excellent chipping resistance and wear resistance in high speed continuous machining of steel, cast iron and the like.SOLUTION: The surface coated cutting tool includes: a lower layer (a) comprising a Ti compound layer having 3 to 20 μm total average layer thickness; an intermediate layer (b) comprising an aluminum oxide layer having 1 to 15 μm average layer thickness; and an upper layer (c) comprising a modified Ti carbonitride layer having a longitudinally grown crystal structure having 4 to 14 μm average layer thickness, the hard coated layers (a), (b) and (c) being formed by chemical deposition on a surface of a tool base body. In the surface coated cutting tool, (d) the modified Ti carbonitride layer configuring the upper layer has at least one oxygen concentrated region in which a plurality of peaks of oxygen contents appear on the internal side from the surface along the layer thickness direction at intervals in the range of 0.5 to 4.0 μm depth and the oxygen contents Oin the peak positions is O=3 to 8 atm%.

Description

  The present invention is a surface-coated cutting tool that exhibits excellent wear resistance and chipping resistance in a high-speed continuous cutting process such as steel and cast iron, and exhibits excellent cutting performance over a long period of use ( Hereinafter, this is referred to as a coated tool).

Conventionally, generally on the surface of a substrate (hereinafter collectively referred to as a tool substrate) composed of a tungsten carbide (hereinafter referred to as WC) -based cemented carbide or titanium carbonitride (hereinafter referred to as TiCN) -based cermet. ,
(A) Ti carbide (hereinafter referred to as TiC) layer, nitride (hereinafter also referred to as TiN) layer, carbonitride (hereinafter referred to as TiCN) layer formed by chemical vapor deposition of the lower layers. A Ti compound layer consisting of two or more of a carbon oxide (hereinafter referred to as TiCO) layer and a carbonitride oxide (hereinafter referred to as TiCNO) layer and having a total average layer thickness of 3 to 20 μm,
(B) an aluminum oxide (hereinafter referred to as Al ₂ O ₃ ) layer having an average layer thickness of 1 to 15 μm, in which the upper layer is formed by chemical vapor deposition;
Conventionally, a coated tool formed by forming a hard coating layer composed of (a) and (b) is known.

  Further, as shown in Patent Document 1, in the conventional coated tool, a TiCN layer constituting a Ti compound layer as a lower layer is mixed with a mixed gas containing an organic carbonitride as a reaction gas in a normal chemical vapor deposition apparatus. It is known that the strength of the hard coating layer itself is improved by forming a TiCN layer having a vertically grown crystal structure by chemical vapor deposition at a medium temperature range of 700 to 950 ° C.

  Furthermore, as shown in Patent Documents 2 and 3, in the conventional coated tool, the TiCN layer constituting the Ti compound layer as the lower layer has a crystal grain size (crystals) in the horizontal direction of the Ti compound layer located on the tool base side. Width) and the crystal grain size (crystal width) in the horizontal direction of the Ti compound layer located on the upper layer side, by maintaining a predetermined relationship, chipping resistance, chipping resistance, and abrasion resistance of the hard coating layer It is also known to improve this.

Japanese Patent Laid-Open No. 6-8010 JP-A-10-109206 Japanese Patent No. 4284144

  In recent years, the performance of cutting machines has been remarkable. On the other hand, there is a strong demand for labor saving and energy saving and further cost reduction for cutting, and with this, cutting tends to be further accelerated. For tools, there is no problem when used for continuous cutting and intermittent cutting under normal conditions such as steel and cast iron, but this is especially accompanied by high heat generation and intermittent cutting on the cutting edge. When used for high-speed continuous cutting where impact loads are applied, chipping (minute chipping), chipping, etc. are likely to occur in the hard coating layer, and it cannot be said that the wear resistance is sufficient. The current situation is that the service life is reached in a short time.

Therefore, from the above viewpoint, the present inventors have high high-temperature hardness and high-temperature strength in the upper layer of this hard coating layer in order to improve the chipping resistance and wear resistance of the coated tool, And as shown schematically in FIG. 1 (a), the crystal structure of NaCl type face-centered cubic crystal in which constituent atoms composed of Ti, carbon, and nitrogen are present at lattice points (note that FIG. 1 (b) is Focusing on the formation of a TiCN layer having a vertically grown crystal structure having a (011) plane cut state (hereinafter referred to as an l-TiCN layer), intensive research was conducted.
(A) First, the hard coating layer of the conventional coated tool is, for example, an ordinary chemical vapor deposition apparatus.
Reaction gas composition: by _{volume%, TiCl 4: 2~10%,} CH 3 CN: 0.5~3%, N 2: 10~30%, H 2: remainder,
Reaction atmosphere temperature: 800 to 900 ° C.
Reaction atmosphere pressure: 6-20 kPa,
After forming a lower layer made of an l-TiCN layer under the above conditions (referred to as normal conditions), an Al ₂ O ₃ layer is deposited thereon.
(B) The present inventors, after depositing the the Al ₂ O ₃ layer, thereon, was deposited top layer consisting of l-TiCN layer under normal conditions described above.
(C) At this time, in the middle of the film forming process for depositing the l-TiCN layer under normal conditions, the reaction atmosphere pressure is lowered, and at the same time, a small amount of CO ₂ component is added to the reaction gas for a short time. After the film formation, the vapor deposition was continued until the l-TiCN layer having a predetermined target layer thickness was formed according to the normal conditions. As a result, oxygen concentration was concentrated in the vicinity of the surface layer of the formed l-TiCN layer. A region is formed, and crystal grains in the oxygen-concentrated region of the deposited l-TiCN layer become a refined structure. Moreover, the l-TiCN layer on the Al ₂ O ₃ layer usually tends to have a coarse structure, but according to the present invention, it has been found that a fine structure can be formed.

Furthermore, it was confirmed that by repeating the step (c), a plurality of oxygen-enriched regions were formed at predetermined intervals inside the l-TiCN layer. Then, it has been found that by forming one or more oxygen-enriched regions, the crystal grain of the l-TiCN layer has a remarkable microstructure effect.
(D) In addition, the inventors of the l-TiCN layer in which the oxygen-enriched region is formed have an oxygen content in the layer thickness direction by Auger electron spectroscopy along the longitudinally polished surface. As a result of a line analysis, an oxygen-concentrated region is formed on the inner side of the l-TiCN layer from the interface between the Al ₂ O ₃ layer (intermediate layer) and the l-TiCN layer (upper layer). As shown in the figure, the crystal structure of the l-TiCN layer is refined, and further, an interval in the range of 0.5 to 4.0 μm is provided from the surface of the l-TiCN layer to the inner side along the thickness direction. In this case, a plurality of peaks of the oxygen content appear, and when the oxygen content O _MAX at the peak position was measured, it was found that 1− containing at least one oxygen-concentrated region with O _MAX = 3 to 8 atomic% TiCN layer (hereinafter referred to as “modified l-TiCN layer”) is shaped It was found to be the difference.
(E) Then, an Al ₂ O ₃ layer (intermediate layer) is formed by vapor deposition, and the modified l-TiCN layer (upper layer) having the at least one oxygen-concentrated region and having a refined structure is formed. The coating tool of the present invention having the hard coating layer formed by vapor deposition) improves the adhesion between the intermediate layer and the upper layer, and at the same time forms an l-TiCN layer (upper layer) on Al ₂ O _3. In spite of this, the coarsening of crystal grains in the upper layer is suppressed, so it is excellent even when used for high-speed continuous cutting that involves high heat generation and intermittent and impact loads on the cutting edge. It exhibits excellent chipping resistance and excellent wear resistance over a long period of use.

The present invention has been made based on the above knowledge,
"On the surface of the tool base made of tungsten carbide base cemented carbide or titanium carbonitride base cermet,
(A) Ti compound having a total average layer thickness of 3 to 20 μm and one or more of Ti carbide layer, nitride layer, carbonitride layer, carbonate layer and carbonitride oxide layer A lower layer consisting of layers,
(B) an intermediate layer comprising an aluminum oxide layer having an average layer thickness of 1 to 15 μm,
(C) an upper layer comprising a modified Ti carbonitride layer having a vertically grown crystal structure with an average layer thickness of 4 to 14 μm,
In the surface-coated cutting tool in which the hard coating layers (a), (b), and (c) are formed by chemical vapor deposition,
(D) The modified Ti carbonitride layer having the vertically grown crystal structure constituting the upper layer is subjected to line analysis of the oxygen content along the layer thickness direction by Auger electron spectroscopy on the polished surface of the longitudinal section. In this case, a plurality of peaks of oxygen content appear on the inner side along the layer thickness direction from the surface at intervals of a depth in the range of 0.5 to 4.0 μm, and the oxygen content at the peak position O _MAX has at least one oxygen-concentrated region where O _MAX = 3 to 8 atomic%. "
It has the characteristics.

Next, the constituent layers of the hard coating layer of the coated tool of the present invention will be described in detail.
(A) Lower layer (Ti compound layer)
Ti compound layer consisting of one or more of TiC layer, TiN layer, TiCN layer (including 1-TiCN layer), TiCO layer, TiCNO layer itself has high temperature strength and is hard due to its presence In addition to the coating layer having high-temperature strength, the tool base and the Al ₂ O ₃ layer, which is an intermediate layer, are firmly adhered to each other, thereby contributing to the improvement of the adhesion of the hard coating layer to the tool base. When the total average layer thickness is less than 3 μm, the above-mentioned effect cannot be sufficiently exerted. On the other hand, when the total average layer thickness exceeds 20 μm, chipping is likely to occur particularly in high-speed continuous cutting with high heat generation. Therefore, the total average layer thickness was determined to be 3 to 20 μm.
(B) Intermediate layer (Al ₂ O ₃ layer)
The intermediate layer composed of the Al ₂ O ₃ layer has excellent high-temperature hardness and heat resistance, and contributes to improving the wear resistance of the hard coating layer.

When the average layer thickness of the intermediate layer made of Al ₂ O ₃ is less than 1 μm, the hard coating layer cannot exhibit sufficient wear resistance, while the average layer thickness exceeds 15 μm. If it is too much, chipping tends to occur, so the average layer thickness was determined to be 1 to 15 μm.
(C) Upper modified l-TiCN layer The intermediate layer is composed of the Al ₂ O ₃ layer as described above, but the upper layer formed on the intermediate layer has an average layer thickness of at least 4 μm. It is necessary to comprise a quality l-TiCN layer.

As described above, the modified l-TiCN layer is formed in the middle of the film forming process for depositing the l-TiCN layer under normal conditions, for example, the film formation of the l-TiCN layer having a predetermined target layer thickness is completed. The reaction atmosphere pressure was reduced to 2.5 to 3 kPa at a time before 5 minutes, and at the same time, CO ₂ was kept in the reaction gas for 50 to 70 seconds so that the proportion of the reaction gas was 0.5 to 1.8% by volume. In addition, a 1-TiCN layer is formed until a predetermined target layer thickness is obtained according to normal conditions. It can be formed by repeating this step a predetermined number of times (at least once).

  As shown in FIG. 2, at least one oxygen-concentrated region is formed at a predetermined interval inside the formed modified l-TiCN layer, and the modified l-TiCN layer in the oxygen-concentrated region is formed. The crystal grains have a refined structure.

When the oxygen content in the longitudinal cross-section polished surface of the modified l-TiCN layer was analyzed by Auger electron spectroscopy along the layer thickness direction, the internal surface was measured from the surface of the modified l-TiCN layer along the layer thickness direction. There is at least one oxygen-concentrated region in which a plurality of peaks of oxygen content appear with an interval in the range of 0.5 to 4.0 μm on the side, and the oxygen content O _{MAX at the} peak position is , O _MAX = 3 to 8 atomic%.

  When the peak of oxygen content is at a depth of less than 0.5 μm, the strength of the modified l-TiCN layer grown by nucleation of a new TiCN crystal is insufficient, and in-layer breakdown during processing When the oxygen content peak position is on the inner side exceeding 4.0 μm, the grain size of the modified l-TiCN layer grown by nucleation of new TiCN crystals Becomes too big. Therefore, the interval between the oxygen-enriched regions was set to 0.5 to 4.0 μm.

Further, when the oxygen content O _{MAX at} the peak position is less than 3 atomic%, the nucleation of new TiCN crystals is not sufficient, so that the crystal grains in the modified l-TiCN layer on the upper layer side from the oxygen concentration region On the other hand, when the oxygen content O _{MAX at the} peak position exceeds 8 atomic%, Ti ₂ O ₃ having a different crystal structure is formed and causes peeling, so that the oxygen at the peak position is small. The content O _MAX needs to be O _MAX = 3 to 8 atomic%.

As for reforming l-TiCN layer of the present invention, from the surface layer, for example, the average oxygen content _{O AV} at 2.5μm or more depth inside of was _measured, the _{O MAX} values and _{O AV} value It was confirmed that the relationship of 2O _AV ≦ O _MAX ≦ 5O _AV was established.

Conventionally, a TiCNO layer is well known as a kind of Ti compound layer that forms the lower layer. However, depending on the adjustment of the deposition conditions of TiCNO, O _MAX = 3 to 8 atomic% and 2O _AV ≦ O _{MAX as described above.} Since it is not possible to form a TiCNO layer satisfying the relation of ≦ 5O _AV , in this sense, the modified l-TiCN layer having an oxygen-enriched region as referred to in the present invention is a conventionally known TiCNO layer. It can be clearly distinguished.

Furthermore, in the present invention, in the modified l-TiCN layer formed on the intermediate layer (Al ₂ O ₃ layer), an oxygen concentration region in which a peak of oxygen content exists at the predetermined depth position is formed. by being, and crystal grains finer reforming l-TiCN layer in the oxygen concentrated region, with adhesion between the Al ₂ O ₃ layer of the intermediate layer is improved, usually on the the Al ₂ O ₃ layer When the Ti compound layer is formed on the crystal, the crystal grains become coarse. However, in the present invention, the crystal grains of the modified l-TiCN layer are refined, and the chipping resistance and wear resistance are reduced due to the coarse crystal grains. Can be suppressed.

The coated tool of the present invention comprises a modified l-TiCN layer (upper layer) having at least one oxygen-concentrated region and having a refined structure on an Al ₂ O ₃ layer (intermediate layer). The formation of the vapor deposition improves the adhesion between the intermediate layer and the upper layer, and at the same time suppresses the coarsening of the crystal grain of the modified l-TiCN layer of the upper layer. Even when used for high-speed continuous cutting in which the blade is subjected to intermittent and impact loads, it exhibits excellent chipping resistance and excellent wear resistance over a long period of use.

It is a schematic diagram which shows the crystal structure of the NaCl type face centered cubic crystal which the modified l-TiCN layer which comprises the upper layer of a hard coating layer has. It is a schematic longitudinal cross-sectional schematic diagram which shows an example of the longitudinal cross-section structure | tissue structure of a hard coating layer.

  Next, the coated tool of the present invention will be specifically described with reference to examples.

WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr ₃ C ₂ powder, TiN powder, TaN powder, and Co powder all having an average particle diameter of 1 to 3 μm are prepared as raw material powders. These raw material powders were blended into the composition shown in Table 1, added with wax, ball milled in acetone for 24 hours, dried under reduced pressure, and pressed into a green compact with a predetermined shape at a pressure of 98 MPa. The green compact was vacuum sintered at a predetermined temperature in the range of 1370 to 1470 ° C. for 1 hour in a vacuum of 5 Pa. After sintering, the cutting edge portion was R: 0.07 mm honing By performing the processing, tool bases A to F made of WC-based cemented carbide having an insert shape specified in ISO · CNMG120408 were manufactured.

In addition, as raw material powders, TiCN (mass ratio TiC / TiN = 50/50) powder, Mo ₂ C powder, ZrC powder, NbC powder, TaC powder, WC powder, all having an average particle diameter of 0.5 to 2 μm. Co powder and Ni powder are prepared, and these raw material powders are blended in the blending composition shown in Table 2, wet mixed by a ball mill for 24 hours, dried, and pressed into a compact at a pressure of 98 MPa. The green compact was sintered in a nitrogen atmosphere of 1.3 kPa at a temperature of 1540 ° C. for 1 hour, and after the sintering, the cutting edge portion was subjected to a honing process of R: 0.07 mm. Tool bases a to f made of TiCN-based cermet having an insert shape of standard / CNMG12041 were formed.

Next, on the surfaces of these tool bases A to F and tool bases a to f, the combination shown in Table 5 is used as a lower layer of the hard coating layer using a normal chemical vapor deposition apparatus under the conditions shown in Table 3. A Ti compound layer (however, excluding the modified l-TiCN layer) is formed by vapor deposition.
Subsequently, an Al ₂ O ₃ layer as an intermediate layer is formed by vapor deposition under the conditions shown in Table 3 and with the target layer thickness shown in Table 5 again, and then the upper layer is formed under the conditions shown in Table 4. The coated tools 1 to 13 of the present invention were produced by vapor-depositing the modified l-TiCN layers as layers in the combinations shown in Table 5 and with the target layer thickness.

Further, for the purpose of comparison, as a lower layer of the hard coating layer, a Ti compound layer is formed by vapor deposition with the combination shown in Table 6 and the target layer thickness also shown in Table 6 under the conditions shown in Table 3. Thereafter, an Al ₂ O ₃ layer as an intermediate layer is formed by vapor deposition at the target layer thickness shown in Table 6 under the conditions shown in Table 3, and then as an upper layer under the conditions shown in Table 3. Conventional coated tools 1 to 13 were manufactured by vapor-depositing normal l-TiCN layers with the target layer thicknesses shown in Table 6 as well.

Next, with respect to the modified l-TiCN layer of the coated tool of the present invention, the oxygen content is linearly analyzed along the layer thickness direction by Auger electron spectroscopy on the vertical cross-section polished surface, and the peak of the oxygen content appears. together determine the respective peak positions were determined values of the oxygen content O _MAX at respective peak positions.

In addition, for reference, the oxygen content at the depth position on the inner side of each oxygen concentration region of the modified l-TiCN layer was also measured, and the average oxygen content O _AV (however, the average value of five-point measurement) )

Table 5 shows values of the oxygen content O _MAX and the average oxygen content O _AV .

Similarly, the oxygen content of the l-TiCN layer of the conventional coated tool was also measured, and the average oxygen content O _AV (however, the average value of five-point measurement) was obtained.

Table 6 shows the values of the average oxygen content _{O AV.}

Further, for the modified l-TiCN layer of the coated tool of the present invention, per unit area of the modified l-TiCN crystal grains in each oxygen concentration region using a field emission scanning electron microscope and an electron backscatter diffraction image apparatus. The grain boundary length is obtained, and the grain boundary length per unit area of the crystal grains on the inner side from each oxygen-concentrated region is obtained, and the crystal refinement ratio R _TiCN (where R = (Grain boundary length per unit area of modified l-TiCN crystal grains in oxygen-enriched region) / (grain boundary length per unit area of modified l-TiCN crystal grains on the inner side of the oxygen-enriched region) ) Was calculated.

  Here, the grain boundary length per unit area of the modified l-TiCN crystal grains can be measured and calculated as follows.

That is, the modified l-TiCN layer is set in a lens barrel of a field emission scanning electron microscope in a state where the vertical cross section of the modified l-TiCN layer is a polished surface, and electrons having an acceleration voltage of 15 kV are incident on the polished surface at an incident angle of 70 degrees. A line is irradiated at an irradiation current of 1 nA to individual crystal grains existing within the measurement range of the vertical cross-section polished surface, and an electron backscatter diffraction image apparatus is used, and a predetermined measurement region is spaced at an interval of 0.1 μm / step. The inclination angle formed by the normal lines of the (001) plane and the (011) plane, which are crystal planes of the crystal grains, is measured with respect to the normal line of the vertical cross-section polished surface, and based on the measured inclination angle obtained as a result. Then, the angles at which the (001) plane normal lines and the (011) plane normal lines cross each other at the interface between adjacent crystal grains are obtained, and the (001) plane normal lines and ( 011) The angle at which the surface normals intersect is 2 degrees After setting the above case as a grain boundary, the field emission scanning electron microscope is used to scan the longitudinal cross-sectional measurement region in the oxygen-enriched region of the modified l-TiCN layer, and as a grain boundary in the measurement region The length GB _LO (μm) of the part to be identified was obtained, and the value GB _LO / G _AO of the ratio to the measured area G _AO (μm ² ) of the polished surface of the longitudinal section was obtained.

Similarly, the longitudinal cross section measurement region on the inner side of the oxygen concentration region of the modified l-TiCN layer is scanned to obtain the length GB _LI (μm) of the portion identified as the grain boundary in the measurement region. and it was determined values _GB LI _{/ G AI} ratio between the area _{G AI} of the measured longitudinal sectional polished surface (μm ^2).

Next, the GB _LO / G _AO (corresponding to the grain boundary length per unit area in the oxygen concentrated region) and the GB _LI / G _AI (grain boundary length per unit area on the inner side from the oxygen concentrated region). And defined as the crystal refinement rate R _TiCN of the modified l-TiCN layer.

That is, the crystal refinement ratio R _TiCN
= (Grain boundary length per unit area of modified l-TiCN crystal grains in oxygen-enriched region) / (grain boundary length per unit area of modified l-TiCN crystal grains located on the inner side of the oxygen-enriched region) Sa)
= (GB _LO / G _AO ) / (GB _LI / G _AI )
It is.

Table 5 shows the value of the crystal refinement ratio R _TiCN of each oxygen-concentrated region for the modified l-TiCN layer of the coated tool of the present invention.

As shown in Tables 5 and 6, respectively, the modified l-TiCN layer of the coated tool of the present invention has a crystal refinement ratio R _TiCN larger than 7.2, and crystal grains are refined in the oxygen concentration region. I understand that.

In addition, when the thickness of the lower layer, the intermediate layer, and the upper layer of the coated tool of the present invention and the conventional coated tool was measured using the scanning electron microscope (same longitudinal section measurement), all were substantially equal to the target layer thickness. The same average layer thickness (average value of 5-point measurement) was shown.

つぎに、前記の各種の被覆工具をいずれも工具鋼製バイトの先端部に固定治具にてネジ止めした状態で、本発明被覆工具１〜１３および従来被覆工具１〜１３について、
被削材：ＪＩＳ・Ｓ４５Ｃの長さ方向等間隔４本縦溝入り丸棒、
切削速度：４００ｍ／ｍｉｎ．、
切り込み：１．５ｍｍ、
送り：０．３０ｍｍ／ｒｅｖ．、
切削時間：１８分、
の条件（切削条件Ａ）での炭素鋼の乾式高速連続切削試験
（通常の切削速度は、２５０ｍ／ｍｉｎ）、
被削材：ＪＩＳ・ＳＮＣＭ４３９の長さ方向等間隔４本縦溝入り丸棒、
切削速度：３５０ｍ／ｍｉｎ．、
切り込み：１．８ｍｍ、
送り：０．３２ｍｍ／ｒｅｖ．、
切削時間：１３分、
の条件（切削条件Ｂ）での合金鋼の乾式高速連続切削試験
（通常の切削速度は、２５０ｍ／ｍｉｎ．）、
被削材：ＪＩＳ・ＦＣ３００の長さ方向等間隔４本縦溝入り丸棒、
切削速度：４５０ｍ／ｍｉｎ．、
切り込み：１．５ｍｍ、
送り：０．３０ｍｍ／ｒｅｖ．、
切削時間：２０分、
の条件（切削条件Ｃ）での鋳鉄の乾式高速連続切削試験
（通常の切削速度は、３００ｍ／ｍｉｎ）、
を行い、いずれの切削試験でも切刃の逃げ面摩耗幅を測定した。
この測定結果を表７に示した。

Next, in the state where all the above-mentioned various coated tools are screwed to the tip of the tool steel tool with a fixing jig, the present coated tools 1 to 13 and the conventional coated tools 1 to 13,
Work material: JIS · S45C lengthwise equal 4 round grooved round bars,
Cutting speed: 400 m / min. ,
Incision: 1.5mm,
Feed: 0.30 mm / rev. ,
Cutting time: 18 minutes
Dry high-speed continuous cutting test of carbon steel under the conditions (cutting condition A) (normal cutting speed is 250 m / min),
Work material: JIS / SNCM439 round direction bar with 4 equal intervals in the length direction,
Cutting speed: 350 m / min. ,
Cutting depth: 1.8mm,
Feed: 0.32 mm / rev. ,
Cutting time: 13 minutes
Dry high-speed continuous cutting test of alloy steel under the following conditions (cutting condition B) (normal cutting speed is 250 m / min.),
Work material: JIS / FC300 lengthwise equidistant 4 bars with vertical grooves,
Cutting speed: 450 m / min. ,
Incision: 1.5mm,
Feed: 0.30 mm / rev. ,
Cutting time: 20 minutes,
A dry high-speed continuous cutting test of cast iron under the above conditions (cutting condition C) (normal cutting speed is 300 m / min),
In each cutting test, the flank wear width of the cutting edge was measured.
The measurement results are shown in Table 7.

表５〜７に示される結果から、本発明被覆工具１〜１３は、酸素濃化領域を備えかつ微細化された組織を有する改質ｌ−ＴｉＣＮ層（上部層）が形成されていることにより、中間層と上部層の密着性が向上すると同時に、上部層の改質ｌ−ＴｉＣＮ層の結晶粒粗大化が抑制されることから、高熱発生を伴い、かつ、切刃部に断続的・衝撃的負荷がかかる高速連続切削に用いた場合でも、すぐれた耐チッピング性を発揮し、長期の使用に亘ってすぐれた耐摩耗性を示す。

From the results shown in Tables 5 to 7, the coated tools 1 to 13 of the present invention have the modified l-TiCN layer (upper layer) having an oxygen-concentrated region and a refined structure. In addition, the adhesion between the intermediate layer and the upper layer is improved, and at the same time, the coarsening of crystal grains in the modified l-TiCN layer of the upper layer is suppressed. Even when used for high-speed continuous cutting where a heavy load is applied, it exhibits excellent chipping resistance and excellent wear resistance over a long period of use.

  On the other hand, as the upper layer of the hard coating layer, in the conventional coated tools 1 to 13 that are provided with an oxygen-concentrated region and are not formed with a modified l-TiCN layer having a refined structure, Grain coarsening is likely to occur in the layer, and therefore, the adhesion and wear resistance between the intermediate layer and the upper layer are not sufficient, resulting in high heat generation and high speed that causes intermittent and impact loads on the cutting edge. In continuous cutting, it is clear that chipping, chipping, peeling, etc. occur and the service life is reached in a relatively short time.

  As described above, the coated tool of the present invention exhibits excellent chipping resistance and wear resistance in high-speed continuous cutting of various steels and cast irons, and exhibits excellent cutting performance over a long period of time. It can cope with high performance of cutting equipment, labor saving and energy saving of cutting, and cost reduction.

Claims (1)

On the surface of the tool base composed of tungsten carbide based cemented carbide or titanium carbonitride based cermet,
(A) Ti compound having a total average layer thickness of 3 to 20 μm and one or more of Ti carbide layer, nitride layer, carbonitride layer, carbonate layer and carbonitride oxide layer A lower layer consisting of layers,
(B) an intermediate layer comprising an aluminum oxide layer having an average layer thickness of 1 to 15 μm,
(C) an upper layer comprising a modified Ti carbonitride layer having a vertically grown crystal structure with an average layer thickness of 4 to 14 μm,
In the surface-coated cutting tool in which the hard coating layers (a), (b), and (c) are formed by chemical vapor deposition,
(D) The modified Ti carbonitride layer having the vertically grown crystal structure constituting the upper layer is subjected to line analysis of the oxygen content along the layer thickness direction by Auger electron spectroscopy on the polished surface of the longitudinal section. In this case, a plurality of peaks of oxygen content appear on the inner side along the layer thickness direction from the surface at intervals of a depth in the range of 0.5 to 4.0 μm, and the oxygen content at the peak position O _MAX has at least one oxygen-concentrated region where O _MAX = 3 to 8 atomic%.

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