JP2008006542A - Cutting edge changing type cutting tip - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a cutting edge changing type cutting tip using alumina as a coating layer and highly making wear resistance and toughness compatible. <P>SOLUTION: This cutting tip has a substrate and the coating layer formed in at least a part on the substrate. The substrate has a cutting edge ridge line, a flank and a rake face. The coating layer includes a first layer mainly including alumina having a α type crystal structure and a second layer mainly including alumina except the alumina having the α type crystal structure. Either one of the first layer or the second layer is formed in a continuous state in a region connected to the rake face across the cutting edge ridge line from the flank. The first layer becomes a top layer in at least a part of the rake face. The second layer becomes a top layer in at least a part of the flank. <P>COPYRIGHT: (C)2008,JPO&INPIT

Description

  The present invention relates to a blade-tip-exchangeable cutting tip (sometimes referred to as a throw-away tip).

  2. Description of the Related Art Conventionally, there is known a blade-tip-exchangeable cutting tip that is detachably attached to a tool and cuts a work material. Many blade-replaceable cutting tips have been proposed in which a hard coating such as ceramic is formed on a substrate made of cemented carbide or cermet for the purpose of improving wear resistance and toughness. Yes. Among these, alumina has been used for a long time as a coating film formed on a base material because it is excellent in wear resistance and is expected to have an effect of preventing surface oxidation of the base material.

  In recent years, focusing on the crystal structure of such alumina, various proposals have been made to improve wear resistance and toughness by using alumina having various crystal structures for such a coating (Patent Documents 1 to 5). ).

  However, in cutting work using steel or cast iron as a work material, it is required that the cutting edge is highly compatible with wear resistance and toughness. In the cutting edge-exchangeable cutting tip using alumina as described above, However, further improvements are desired to meet these requirements.

In recent years, there has been an increasing demand for labor saving and shortening of the cutting process in cutting of steel and cast iron, and there is a tendency for cutting under severe conditions. When cutting is performed under such severe conditions, the service life is reached in a relatively short time due to wear and chipping.
JP 09-125250 A Japanese Patent Laid-Open No. 10-237652 JP-A-11-335816 Japanese Patent Laid-Open No. 2000-024808 WO99 / 052662 pamphlet

  The present invention has been made in view of the above-described situation, and an object of the present invention is a blade-tip-exchangeable cutting tip using alumina as a coating layer, which is highly compatible with wear resistance and toughness. An object of the present invention is to provide an exchangeable cutting tip.

  The present inventor conducted intensive research to solve the above-described problems. As a result, in a blade-tip-exchangeable cutting tip in which a coating layer containing alumina is formed on a substrate, alumina having an α-type crystal structure on the rake face When a coating layer containing a non-alumina having an α-type crystal structure is formed on the flank face, the knowledge that both wear resistance and toughness are excellent is obtained. Through further research, the present invention has finally been completed.

  That is, the cutting edge-exchangeable cutting tip of the present invention has a base material and a coating layer formed on at least a part of the base material, and the base material is scooped with a cutting edge ridgeline and a flank face. The coating layer includes a first layer mainly including alumina having an α-type crystal structure and a second layer mainly including alumina other than alumina having an α-type crystal structure, Either one of the first layer and the second layer is formed in a continuous state in a region connecting from the flank face to the rake face across the edge of the cutting edge, and the first layer includes at least the rake face. A part of the flank is the uppermost layer, and the second layer is the uppermost layer of at least a part of the flank.

  Further, the second layer is formed in a continuous state in a region connecting from the flank face to the rake face with the edge of the cutting edge interposed therebetween, and the first layer is formed on at least a part of the rake face on the second layer. It is preferable to be formed. In addition, the first layer is formed in a continuous state on the second layer in a region connecting from the flank face to the scooping surface across the edge of the cutting edge, and then removed from the region including at least a part of the flank surface. It is preferable that

  In addition, the first layer is formed in a continuous state in a region connecting from the flank face to the rake face across the edge of the cutting edge, and the second layer is formed on the first layer in at least a part of the flank face. It is preferable to be formed. In addition, the second layer is formed in a continuous state on the first layer in a region connected from the flank to the scooping surface with the edge of the cutting edge interposed therebetween, and then removed from a region including at least a part of the scooping surface. It is preferable that

  Further, the covering layer may include one or more third layers different from the first layer and the second layer, and the third layer is at least a part of the flank face or at least a part of the rake face. Can be an upper layer.

  The third layer can be formed between the first layer and the second layer, or can be formed on the substrate.

  The cutting edge replacement type cutting tip of the present invention has both the excellent wear resistance and the excellent toughness by having the above-described configuration.

  Hereinafter, the present invention will be described in more detail. In the following description of the embodiments, the description is made with reference to the drawings. In the drawings of the present application, the same reference numerals denote the same or corresponding parts. Each drawing is merely a schematic diagram for explanation, and the film thickness ratio of the coating layer to the base material and the corner (R) size ratio are different from the actual ones.

<Cutting edge type cutting tip>
The blade-tip-exchangeable cutting tip of the present invention has a base material and a coating layer formed on at least a part of the base material. Such a cutting edge replaceable cutting tip of the present invention is used for drilling, end milling, milling, turning, metal saw processing, gear cutting tool processing, reamer processing, tapping processing or crankshaft. Especially useful for pin milling.

  The present invention is effective for either a negative-type or a positive-type blade-tip-exchangeable cutting tip, and for both a chip breaker formed and a chip breaker not formed. It is valid.

<Base material>
As a material constituting the base material of the present invention, a conventionally known material known as a base material for such a blade-tip-exchangeable cutting tip can be used without any particular limitation. For example, cemented carbide (for example, including WC base cemented carbide, including WC, Co, or further including carbides such as Ti, Ta, Nb, nitrides, carbonitrides, etc.), cermet (Mainly composed of TiC, TiN, TiCN, etc.), high-speed steel, ceramics (such as titanium carbide, silicon carbide, silicon nitride, aluminum nitride, aluminum oxide, and mixtures thereof), cubic boron nitride firing Examples thereof include a sintered body, a diamond sintered body, and a silicon nitride sintered body.

  In addition, these substrates may be those whose surfaces are modified. For example, in the case of cemented carbide, a de-β layer, β phase enriched layer or Co phase enriched layer may be formed on the surface, and in the case of cermet, a surface hardened layer may be formed. Even if the surface is modified, the effect of the present invention is exhibited. In the case of cemented carbide or cermet, the effect of the present invention is shown regardless of the presence or absence of free carbon and ε phase in the alloy structure.

  On the other hand, as the shape of the base material, a conventionally known one known as the shape of the base material of such a blade-tip-exchangeable cutting tip can be used without any particular limitation. For example, when expressed in a cross-sectional shape parallel to the surface (upper surface) of the base material, a shape such as a rhombus, a square, a triangle, a circle and an ellipse is included.

  And such a base material 8 has the cutting edge ridgeline 4, the flank 3, and the rake face 2. FIG. For example, as shown in FIG. 1, the cutting edge replacement type cutting tip 1 according to the present invention has a peripheral portion of the cutting edge ridge line 4 in contact with the work material 5, and the flank 3 faces the work material 5. On the other hand, the rake face 2 is positioned on the chip 6 side, and the cutting edge ridge line 4 becomes a central action point of the cutting action on the work material 5.

  As shown in FIG. 2, the flank 3 and the rake face 2 have a relationship such that they are connected with a cutting edge ridge line 4 interposed therebetween. Further, the intersection point where the two flank surfaces 3 and the one rake surface 2 intersect is called a corner 9 and is often the most central point of action for cutting.

  Further, the edge edge 4 of the cutting edge is formed in a straight line in FIG. 2, but is not limited to this. For example, a circumferential one, a wavy one, a curved one, a refractive one, etc. Is also included. Further, a blade edge processing such as a chamfering process and / or a corner radius (R) applying process can be performed on such a blade edge line, corner, or other edge. However, when the cutting edge ridge line does not form a clear ridge or the corner no longer forms a clear intersection, the cutting edge processing such as shown in FIG. Assuming a state in which the cutting edge processing is not performed on the rake face 2 and the flank face 3 that follow the edge of the edge of the cut edge, by extending each face geometrically, a ridge or intersection where both faces intersect is obtained. The hypothetical ridges and intersections are defined, the hypothetically defined ridges are defined as the cutting edge ridge lines 4, and the hypothetical defined intersections are defined as corners.

  The expression that the rake face and the flank face are connected with the edge of the edge of the edge, or the expression that the flank face is connected to the rake face with the edge of the edge of the edge interposed therebetween, and expressions similar to these are all The case where the blade edge processing as described above is performed is also included. That is, these expressions include a cutting edge ridge line portion in which a rake face and a flank face are chamfered and / or rounded (R) imparted (such as chamfered and / or rounded (R) imparted). The case where the edge of the cutting edge ridge line applied is sometimes called a cutting edge ridge line portion) is also included. Similarly, the expression of the intersection of two flank faces and one rake face and similar expressions also include the case where the above edge processing is applied to the corner. Shall be.

  Note that the terms flank, rake face, cutting edge line, corner, and the like used in the present invention are not limited to terms used only on the surface portion of the base material, but are located on the outermost surface portion of the cutting edge replaceable cutting tip 1. Along with the surface and the surface, it is also used for a corresponding portion located on the surface portion or inside of each coating layer described later.

  Moreover, the through-hole 7 used as a fixing hole which attaches the blade-tip-exchangeable cutting tip 1 to the tool may be formed in the base material of the present invention so as to penetrate the upper surface and the bottom surface. If necessary, another fixing means can be provided in addition to or instead of the fixing hole.

<Coating layer>
The coating layer 14 of the present invention is formed on at least a part of the base material 8 as shown in FIG. 3, for example, and includes a first layer 11 mainly containing alumina having an α-type crystal structure. And a second layer 12 mainly containing alumina other than alumina having an α-type crystal structure. The covering layer 14 can include one or more third layers different from the first layer and the second layer.

  Such a coating layer 14 is formed on at least a part of the substrate 8. That is, the coating layer 14 may be formed so as to cover the entire surface of the substrate 8 or may be formed so as to partially cover the surface of the substrate 8. Thus, the coating layer 14 does not necessarily need to be formed so as to cover the entire surface of the substrate 8, and even if a portion where the coating layer 14 is not formed is included, it does not depart from the scope of the present invention. .

  The thickness (total thickness) of the coating layer 14 of the present invention is preferably 0.05 μm or more and 30 μm or less. If the thickness is less than 0.05 μm, the effect of improving various properties such as wear resistance is not sufficiently exhibited. On the other hand, if the thickness exceeds 30 μm, no further improvement in various properties is observed. Is not advantageous. However, as long as economic efficiency is ignored, the thickness can be 30 μm or more, and the effect of the present invention is shown. As a method for measuring the thickness, for example, a cutting edge-exchangeable cutting tip is cut and the cross section thereof can be measured by observing using a SEM (scanning electron microscope).

  The coating layer 14 of the present invention can include the first layer, the second layer, and the third layer as described above, and each of these layers can have various laminated structures as described later. In the vicinity of the interface where each layer is in contact with each other, there may be a mixed layer in which the composition of each layer is mixed. However, even if such a mixed layer is included, it does not depart from the scope of the present invention.

<First layer>
The first layer of the present invention mainly contains alumina having an α-type crystal structure (sometimes simply referred to as α-Al ₂ O _{3 in the} present invention). Here, including alumina having an α-type crystal structure as a main component means that the intensity is maximized by collecting diffraction angle and diffraction intensity data relating to alumina in the measurement result of X-ray diffraction (XRD). When five intensity data (that is, five peaks) from the first to the fifth largest are confirmed, and three or more of the five data are related to α-Al ₂ O ₃ It shall be said. In this case, a total of eight peak positions (surface distance d (Å)) of 3.47, 2.55, 2.37, 2.08, 1.74, 1.60, 1.40 and 1.37 ( The peak at the third decimal place is rounded down) as the peak for α-Al ₂ O ₃ .

  In addition, this surface interval d is a No. of JCPDS (Joint Committee on Powder Diffraction Standards). 46-1212 and no. 010-0173 (Huang, T., Parish, W., Masciocchi, N., Wang, P., Adv. X-Ray Anal., 33, 295. (1990), Acta Crystallogr., Sec. B: Structural Science. .49,973 (1993)).

In addition, when only 4 or less clear peaks are confirmed in the above, the following criteria shall be followed. That is, in the case where there are three or four peaks, if two or more peaks are related to α-Al ₂ O _3, alumina having an α-type crystal structure is mainly included. In addition, in the case of two peaks, if the peak with the higher peak intensity is related to α-Al ₂ O ₃ , it shall mainly contain alumina having an α-type crystal structure. If the peak is related to α-Al ₂ O ₃ , it shall mainly contain alumina having an α-type crystal structure. In addition, when said judgment becomes difficult, the identification by transmission electron microscope observation shall be used together.

In addition, this 1st layer shall contain 50 mass% or more of alumina (a thing other than alpha type is included). In addition, when the first layer includes materials other than α-Al ₂ O ₃ , they are usually alumina having a crystal structure other than α-type or amorphous alumina, but are not limited thereto. Absent. For example, examples of such components other than alumina include ZrO ₂ and Y ₂ O ₃ (it can be considered that Zr and Y are added to alumina), and chlorine, carbon, boron, nitrogen and the like. May be included.

  The thickness of the first layer is preferably 0.05 μm or more and 15 μm or less, and more preferably 0.1 μm or more and 10 μm or less. If it is less than 0.05 μm, the effect of the present invention may not be shown, and it is industrially difficult to uniformly coat a predetermined site. Moreover, even if it exceeds 15 μm, there is not much difference in function, but it is economically disadvantageous. As a method for measuring the thickness, the same measuring method as described above can be employed.

<Second layer>
The second layer of the present invention mainly contains alumina other than alumina having an α-type crystal structure. Here, as alumina other than alumina having an α-type crystal structure, alumina having a crystal structure other than α-type (for example, γ-type, δ-type, η-type, θ-type, κ-type, ρ-type, χ-type, etc.) And amorphous alumina and the like. In addition, including alumina other than alumina having an α-type crystal structure as a main component means that the measurement result of XRD includes alumina indicating a result other than the measurement result of the first layer, and the total amount of alumina is 50 mass. The thing which becomes more than%.

More preferably, the second layer is a layer mainly containing alumina having a κ-type crystal structure (in the present invention, it may be simply referred to as κ-Al ₂ O ₃ ), or having a γ-type crystal structure. It is a layer mainly containing alumina (which may be simply referred to as γ-Al ₂ O _{3 in the} present invention).

In this case, the fact that alumina having a κ-type crystal structure as a main component means that the magnitude of the diffraction intensity and diffraction intensity data relating to alumina in the XRD measurement results is collected in order from the maximum intensity. Is the case where five intensity data up to the fifth one (that is, five peaks) are confirmed, and three or more of the five data are related to κ-Al ₂ O ₃ . In this case, a total of eight peak positions (the surface separation d (Å) is 3.04, 2.80, 2.57, 2.32, 2.11, 1.64, 1.43 and 1.39 ( The peak at the third decimal place is rounded down) as the peak for κ-Al ₂ O ₃ .

  The surface distance d is the same as that of JCPDS No. 052-0803 and no. 004-0878 (Halversson, M., Langer, V., Vuorinen, S., Powder Diffraction, 14, 61, (1999), Youthshayan, Y., Ruberto, C., Halverson, M., Bengtsson, L. Langer, V., Lundqvist, B., J. Am. Ceram. Soc., 82, 1365. (1999), Stampf et al., Ind. Eng. Chem., 42, 1398, (1950)). To do.

In addition, when only 4 or less clear peaks are confirmed in the above, the following criteria shall be followed. That is, in the case of three or four peaks, if two or more peaks are related to κ-Al ₂ O _3, alumina having a κ-type crystal structure is mainly included. In addition, in the case of two peaks, if the peak with higher peak intensity is related to κ-Al ₂ O ₃ , it shall mainly contain alumina having a κ-type crystal structure. If the peak is related to κ-Al ₂ O ₃ , it shall mainly contain alumina having a κ-type crystal structure. In addition, when said judgment becomes difficult, the identification by transmission electron microscope observation shall be used together.

In addition, in the above-mentioned surface distance d, 1.39 mm overlaps with γ-Al ₂ O ₃ described later. For this reason, when the surface interval d includes 1.39 mm, the above-described determination is made by excluding the peak. However, when only a peak of 1.39 mm is confirmed as the interplanar spacing d, it is identified by observing with a transmission electron microscope.

In the case where the second layer is a layer mainly containing alumina having a κ-type crystal structure, when the second layer contains something other than κ-Al ₂ O ₃ , they are usually κ-type. However, the present invention is not limited to these. For example, examples of such components other than alumina include ZrO ₂ and Y ₂ O ₃ (it can be considered that Zr and Y are added to alumina), and chlorine, carbon, boron, nitrogen and the like. May be included.

On the other hand, in the same way, including alumina having a γ-type crystal structure as a main component means that by collecting the diffraction angle and diffraction intensity data regarding alumina in the XRD measurement results, the intensity is maximized in order from the maximum. Confirming 5 intensity data (namely, 5 peaks) up to the 5th magnitude, and 3 or more of the 5 data are related to γ-Al ₂ O ₃ To do. In this case, peaks at a total of five peak positions (rounded down to the third decimal place) whose interplanar spacing d (Å) is 4.56, 2.39, 2.28, 1.97 and 1.39 are shown. The peak is related to γ-Al ₂ O ₃ .

  The surface distance d is the same as that of JCPDS No. 010-0425 (Similar powder data given in second edition, page 384 (1961). Synthetic form. Slow transition to cordon 1000 C.).

In addition, when only 4 or less clear peaks are confirmed in the above, the following criteria shall be followed. That is, in the case of three or four peaks, if two or more peaks are related to γ-Al ₂ O _3, alumina having a γ-type crystal structure is mainly included. In addition, in the case of two peaks, if the peak with the higher peak intensity is related to γ-Al ₂ O ₃ , it shall mainly contain alumina having a γ-type crystal structure. If the peak is related to γ-Al ₂ O _3, alumina having a γ-type crystal structure is mainly included. In addition, when said judgment becomes difficult, the identification by transmission electron microscope observation shall be used together.

In addition, as described above, 1.39 cm in the surface separation d overlaps with the κ-Al ₂ O ₃ . For this reason, when the surface interval d includes 1.39 mm, the above-described determination is made by excluding the peak. However, when only a peak of 1.39 mm is confirmed as the interplanar spacing d, it is identified by observing with a transmission electron microscope as described above.

In the case where the second layer is a layer mainly containing alumina having a γ-type crystal structure, when the second layer contains something other than γ-Al ₂ O ₃ , they are usually γ-type. However, the present invention is not limited to these. For example, examples of such components other than alumina include ZrO ₂ and Y ₂ O ₃ (it can be considered that Zr and Y are added to alumina), and chlorine, carbon, boron, nitrogen and the like. May be included.

  The thickness of the second layer is preferably 0.05 μm or more and 15 μm or less, and more preferably 0.1 μm or more and 10 μm or less. If it is less than 0.05 μm, the effect of the present invention may not be shown, and it is industrially difficult to uniformly coat a predetermined site. Moreover, even if it exceeds 15 μm, there is not much difference in function, but it is economically disadvantageous. As a method for measuring the thickness, the same measuring method as described above can be employed.

<Third layer>
The coating layer of the present invention can include one or more third layers different from the first layer and the second layer. As such third layer, group IVa elements (Ti, Zr, Hf, etc.) of the periodic table, group Va elements (V, Nb, Ta, etc.), group VIa elements (Cr, Mo, W, etc.), Al And a layer composed of at least one metal selected from the group consisting of Si, or at least one of the metals and at least one element selected from the group consisting of carbon, nitrogen, oxygen, and boron It can be set as the layer comprised by the compound which becomes.

Examples of the metal or compound constituting the third layer include Cr, Ti, Al, Si, V, Zr, Hf, TiC, TiN, TiCN, TiNO, TiCNO, TiB ₂ , TiBN, TiBNO, TiCBN, ZrC, ZrO ₂ , HfC, HfN, TiAlN, AlCrN, CrN, VN, TiSiN, TiSiCN, AlTiCrN, TiAlCN, ZrCN, ZrCNO, AlN, AlCN, ZrN, TiAlC, and the like. Note that the composition ratio (atomic ratio) of the above compound is not necessarily limited to the atomic ratio of a metal and an element other than a metal (carbon, nitrogen, oxygen, boron) as 1: 1 as conventionally known, The latter element can be about 0.5 to 1 with respect to metal 1 (for example, when Ti _a N _b is used and a + b = 100 atomic%, b is about 35 to 50 atomic%. Become). When the latter element is composed of a plurality of elements, the atomic ratio of each element is not necessarily limited to an equal ratio, and a conventionally known atomic ratio can be arbitrarily selected. Therefore, when the compound is represented in the following examples and the like, unless otherwise specified, the atomic ratio constituting the compound can be arbitrarily selected from conventionally known atomic ratios.

  Of the layers forming such a third layer, it is preferably formed as a layer in contact with the first layer or the second layer (in particular, the lower layer of the first layer or the second layer, In the case where a plurality of layers are formed between the substrate and the first layer or the second layer, it is preferably formed as the uppermost layer of the third layer) of Ti and carbon, nitrogen, oxygen or boron. It is preferably formed of a compound containing at least one element. Thereby, the extremely advantageous effect that it can prevent very effectively that the 1st layer or the 2nd layer peels is shown. This is probably because of the extremely high adhesion between the layer made of a compound containing at least Ti and one or more elements of carbon, nitrogen, oxygen or boron, and the first layer or the second layer. This is considered to be obtained.

  Examples of the compound containing at least Ti and one or more elements of carbon, nitrogen, oxygen, or boron include TiN, TiCN, TiBN, TiCBN, TiBNO, TiNO, and TiCNO. These compounds can have a non-stoichiometric composition.

In particular, as this compound, boronitride represented by TiB _X N _Y (wherein X and Y are atomic%, and 0.001 <X / (X + Y) <0.04). Titanium or TiB _X N _Y O _Z (wherein X, Y, and Z are atomic%, 0.0005 <X / (X + Y + Z) <0.04, and 0 <Z / (X + Y + Z) ) <0.5. This is because if these compounds are used, particularly excellent adhesion between the first layer and the second layer can be obtained.

In the TiB _X N _Y , when X / (X + Y) is 0.001 or less, it may not show excellent adhesion to the first layer or the second layer, and conversely to 0.04 or more. In this case, the reactivity with the work material becomes high, and when this layer is exposed on the surface, it reacts with the work material, and the welded material adheres firmly to the cutting edge, which may impair the appearance of the work material. X / (X + Y) is more preferably 0.003 <X / (X + Y) <0.02. In the above formula, the atomic ratio of Ti and BN does not have to be 1: 1 as already described.

Further, in the TiB _X N _Y O _Z , when X / (X + Y + Z) is 0.0005 or less, there may be cases where excellent adhesion to the first layer or the second layer is not exhibited. If it is 0.04 or more, the reactivity with the work material becomes high, and when this layer is exposed on the surface, it reacts with the work material, and the welded material adheres firmly to the cutting edge and damages the appearance of the work material. There is a case. X / (X + Y + Z) is more preferably 0.003 <X / (X + Y + Z) <0.02. On the other hand, when Z / (X + Y + Z) is 0.5 or more, although the hardness of the film is increased, the toughness may be lowered and the fracture resistance may be lowered. Z / (X + Y + Z) is more preferably 0.0005 <Z / (X + Y + Z) <0.3. In the above formula, the atomic ratio of Ti and the sum of BNO need not be 1: 1.

  The thickness of the third layer (the total thickness when formed as two or more layers) is preferably 0.05 μm or more and 30 μm or less. If the thickness is less than 0.05 μm, the effect of improving various properties such as wear resistance is not sufficiently exhibited. Conversely, if the thickness exceeds 30 μm, no further improvement in various properties is observed, which is not economically advantageous. However, as long as economic efficiency is ignored, the thickness can be 30 μm or more, and the effect of the present invention is shown. As a method for measuring such thickness, the same measuring method as described above can be employed.

<Lamination state of coating layer>
As shown in FIG. 3 or FIG. 9, for example, the coating layer 14 of the present invention is a rake face in which one of the first layer 11 and the second layer 12 sandwiches the edge line 4 from the flank face 3. The first layer 11 is the uppermost layer in at least a part of the rake face 2, and the second layer 12 is the uppermost layer in at least a part of the flank 3. It is characterized by becoming. By adopting such a configuration, the cutting edge-replaceable cutting tip of the present invention has dramatically improved wear resistance and toughness compared to conventional cutting edge-replaceable cutting tips, and succeeded in achieving both of them at a high level. It is a thing.

  In addition, it confirms as follows that this 1st layer 11 becomes the uppermost layer in at least one part of the rake face 2, and this 2nd layer 12 becomes the uppermost layer in at least one part of the flank 3. be able to. That is, in terms of the manufacturing technique of the cutting edge-exchangeable cutting tip, the boundary between the first layer and the second layer of the flank and the rake face on the cutting edge ridge line 4 It is difficult to accurately match the boundary between the cutting edge 2 and at least a part of each of the rake face 2 and the flank face 3 in the region at least 0.05 mm away from the cutting edge line 4. As long as the crystal structure is measured by XRD and the measurement result satisfies the definition described above, the above condition is assumed to be satisfied.

  Here, the area connected from the flank face to the rake face across the edge of the cutting edge is that the maximum range of the area matches the entire surface of the substrate, but it does not mean only such maximum range. And includes an area that spans at least one flank and at least one rake face across the edge line of the cutting edge. Further, the region may cover the entire flank and rake face, or may cover only a part thereof.

  The area is defined as described above, although the area preferably indicates the entire surface of the base material, but not to the seating surface that is a part attached to the cutting tool or an area that is not involved in cutting at all. It is clarified that the layer does not need to be formed.

  On the other hand, being formed in a continuous state in the above region means being formed as a continuous single layer.

  Such a layering mode of the coating layer is further formed in a continuous state in the region where the second layer 12 is connected from the flank 3 to the scooping surface 2 across the cutting edge ridge 4, and the first layer 11. Since at least part of the rake face 2 is formed on the second layer 12, the first layer 11 becomes the uppermost layer at least part of the rake face 2, and the second layer 12 becomes the flank 3. It is preferable that at least a part of the uppermost layer is the uppermost layer (for example, FIGS. 3, 4, and 6).

  In the case of configuring the above-described lamination mode, the first layer 11 is formed in a continuous state on the second layer 12 in a region connecting from the flank 3 to the rake face 2 with the cutting edge ridge 4 interposed therebetween. After that, it is preferable to remove from the region including at least a part of the flank 3. This is because, with such a configuration, it is possible to manufacture a cutting edge-exchangeable cutting tip with extremely high productivity.

  On the other hand, the first layer 11 is formed in a continuous state in a region connecting from the flank 3 to the rake face 2 with the cutting edge ridge 4 interposed therebetween, and the second layer 12 is at least a part of the flank 3. The first layer 11 is the uppermost layer in at least a part of the rake face 2, and the second layer 12 is the uppermost layer in at least a part of the flank 3. It is preferable (for example, FIG. 9, FIG. 10, FIG. 12).

  In the case of configuring the above-described lamination mode, the second layer 12 is formed in a continuous state on the first layer 11 in a region connecting from the flank 3 to the rake face 2 with the cutting edge ridge 4 interposed therebetween. After that, it is preferable that the rake face 2 is removed from the region including at least a part thereof. This is because, with such a configuration, it is possible to manufacture a cutting edge-exchangeable cutting tip with extremely high productivity.

  In the present invention, it is preferable that the first layer is the uppermost layer in at least a part of the rake face, but the first layer is preferably essentially the uppermost layer over the entire rake face, but in a region not involved in cutting at all. It is clarified that the first layer is not necessarily required to be the uppermost layer on the entire surface of the rake face because it does not matter so much whether the first layer is the uppermost layer. Similarly, the fact that the second layer is the uppermost layer in at least a part of the flank clearly clarifies that the second layer is not necessarily the uppermost layer over the entire flank.

  On the other hand, when the coating layer 14 includes the third layer 13 other than the first layer 11 and the second layer 12, the third layer 13 is at least a part of the flank 3 or the rake face. 2 may be the uppermost layer (eg, FIG. 5, FIG. 7, FIG. 8, FIG. 11, FIG. 13, FIG. 14).

  In the present invention, as described above, the first layer 11 is the uppermost layer in at least a part of the rake face 2, and the second layer 12 is the uppermost layer in at least a part of the flank face 3. The structure has wear and excellent toughness. However, a third layer 13 is further formed on the first layer 11 that is the uppermost layer of the rake face 2, and this third layer 13 is made the uppermost layer on the rake face 2 or the uppermost layer of the flank face 3. Even when the third layer 13 is further formed on the two layers 12 and this third layer 13 is used as the uppermost layer of the flank 3, the excellent effects as described above of the present invention are exhibited. Since such a third layer is worn away at the initial stage of cutting, it does not affect the cutting performance so much. On the contrary, by using a third layer having a color different from that of the first layer or the second layer, the third layer is used. This is because the blade edge used can be recognized depending on the remaining state of the third layer. When the third layer is formed in this laminated mode, the third layer is preferably formed of a material that is more easily worn than the first layer and the second layer, and the thickness thereof is 3 μm or less, more preferably 2 μm. The following is preferable.

  Further, the third layer can be formed between the first layer and the second layer (for example, FIG. 5, FIG. 6, FIG. 7, FIG. 11, FIG. 12, FIG. 13, FIG. 14), It can also be formed on a substrate (for example, FIGS. 4 to 8 and FIGS. 10 to 14). By adopting such a laminated mode, the wear resistance and toughness can be further improved, and in particular, the adhesion between the base material and the first layer or the second layer and the adhesion between the first layer and the second layer. Can be improved.

  In particular, when the third layer is formed between the first layer and the second layer, the following effects can be obtained in addition to the above effects. For example, in the case where the third layer 13 is formed on the second layer 12 as shown in FIGS. 5 and 6 and the first layer 11 is further formed thereon, the flank of all three layers as will be described later. When the first layer 11 is removed from the region including at least a part of the flank 3, the third layer is formed as follows. An advantageous effect can be shown. That is, when the third layer is formed of, for example, TiN (gold), alumina usually exhibits a black color regardless of the crystal structure, and thus a clear color contrast can be formed with respect to the first layer and the second layer. Thus, when the first layer is removed from the flank, it can be clearly recognized from the contrast of this color whether or not the first layer is removed. Moreover, since it is possible to simultaneously recognize which layer constitutes the surface of the flank face by the contrast of this color, when manufacturing a blade-tip-exchangeable cutting tip having a desired laminated configuration, it is directly manufactured by visual inspection. It becomes possible to control the process. This visual control is extremely advantageous in industry.

  In addition, although the lamination | stacking aspect of this invention was demonstrated using FIGS. 3-14 in the above, the lamination | stacking aspect of this invention is not restricted to these FIGS.

<Manufacturing method>
The first layer, the second layer, and the third layer of the present invention can be formed by a known chemical vapor deposition method (CVD method) or a physical vapor deposition method (including a PVD method and a sputtering method). The formation method is not limited at all.

  For example, when the first layer is formed by chemical vapor deposition, it is preferable to supply CO gas in order to promote the nucleation of alumina having an α-type crystal structure at the initial stage of formation. It is not necessary to continuously supply CO gas after the nucleation, and it is preferable to stop providing the CO gas after the nucleation, but it is not limited to such a method.

  Further, when the first layer and the second layer are formed by physical vapor deposition, the difference between the formation temperature of alumina having an α-type crystal structure and the formation temperature of alumina other than alumina having an α-type crystal structure. Can be formed.

When the third layer is formed using a known CVD method, it is preferable that a layer formed by an MT-CVD (medium temperature CVD) method is included as at least one of the third layers. In particular, it is optimal to include a titanium carbonitride (TiCN) layer having excellent wear resistance formed by this method. The conventional CVD method forms a film at about 1020 to 1030 ° C., whereas the MT-CVD method can be performed at a relatively low temperature of about 850 to 950 ° C. Damage can be reduced. Therefore, it is more preferable that the layer formed by the MT-CVD method is provided close to the substrate. Further, it is preferable to use a nitrile gas, particularly acetonitrile (CH ₃ CN), as the gas used in the film formation because of excellent mass productivity. Note that a multilayer structure in which a layer formed by the MT-CVD method as described above and a layer formed by an HT-CVD (high temperature CVD, conventional CVD) method are stacked. As a result, the adhesion between the layers of these coating layers may be improved and may be preferable.

  In the present invention, the above-described method is employed to form both the first layer and the second layer in a continuous state in a region connecting from the flank face to the rake face across the edge of the edge. It is particularly preferred to produce by removing one of the layers from a specific area. This is because the cutting edge-exchangeable cutting tip having the configuration of the present invention can be efficiently manufactured.

  Specifically, when the first layer is formed continuously on the second layer, the first layer is removed from the region including at least a part of the flank. Thereby, the uppermost layer of the rake face can be the first layer and the uppermost layer of the flank can be the second layer. Therefore, the removal of the first layer from the region including at least a part of the flank in the present invention means that the first layer is removed from the region desired to be the uppermost layer in the at least part of the flank. Is meant to be removed.

  On the other hand, when the second layer is continuously formed on the first layer, the second layer is removed from the region including at least a part of the rake face. Thereby, the uppermost layer of the rake face can be the first layer and the uppermost layer of the flank can be the second layer. Therefore, in the present invention, the removal of the second layer from the region including at least a part of the rake face means that the second layer is formed from a region desired to be the uppermost layer in the at least part of the rake face. Is meant to be removed.

  In addition, as described above, both the first layer and the second layer are formed in a continuous state in the region connecting from the flank face to the rake face with the edge line of the blade interposed therebetween, and both of them are in contact with each other. In the case of forming, the composition can be continuously changed in an inclined manner by changing the manufacturing conditions in an inclined manner in each of the manufacturing methods described above. In this case, there is no clear interface between the first layer and the second layer, but even in such a case, it does not depart from the scope of the present invention. That is, as long as the upper surface and the lower surface of such a layer have the composition specified as described above, this layer is regarded as including the first layer and the second layer.

  On the other hand, when the third layer is formed between the first layer and the second layer by adopting the method as described above, or formed on the first layer or the second layer, the same as above. It is preferable that the third layer is formed in a continuous state in a region connected from the flank face to the scooping surface with the edge of the cutting edge interposed therebetween, and then the third layer is preferably removed from the specific region. This is because the cutting edge-exchangeable cutting tip having the configuration of the present invention can be efficiently manufactured.

  In the present invention, as the method for removing the first layer, the second layer, or the third layer from the desired region as described above, various conventionally known methods can be adopted, and the method is not limited at all. It is not something. For example, a desired layer can be removed from a desired region by performing conventionally known blasting, brushing, barreling, or the like. However, it is not limited to such a method.

<Compressive stress>
The covering layer 14 preferably has a compressive stress at least in part. The expression “part” herein includes an aspect of any one or more layers of the coating layer, an aspect of any part of the entire coating layer, and a part of the area of any one or more layers. It is a concept that can include any of the aspects.

  In particular, at least one of the first layer and the second layer of the present invention preferably has a compressive stress in at least a part thereof, so that the blade edge of the blade edge-exchangeable cutting tip depending on the application. Strength can be improved effectively.

  It is particularly preferable that one or more of the first layer and the second layer have a compressive stress at a site involved in cutting. It is because it can contribute to the improvement of toughness most directly. Here, the part involved in cutting differs depending on the shape of the cutting edge-replaceable cutting tip, the type and size of the work material, the mode of cutting work, etc. It means an area that is widened with a width of 3 mm from the approaching edge of the cutting edge to the flank side and the rake face side.

  The compressive stress is applied by first forming a coating layer to be applied with compressive stress, and then subjecting the layer (or a desired portion of the layer) to blast treatment, brush treatment, barrel treatment, or the like. It is preferable to carry out by applying. In the case of performing blasting, the slurry may be irradiated from a direction substantially perpendicular to the flank and / or rake face, or a predetermined angle with respect to either the flank face or the rake face. A plurality of surfaces may be processed simultaneously by irradiating the slurry from the direction in which it is present.

  Here, the compressive stress is a kind of internal stress (intrinsic strain) existing in such a coating layer, and is represented by a numerical value “−” (minus) (unit: “GPa” is used in the present invention). Stress. For this reason, the concept that the compressive stress is large indicates that the absolute value of the numerical value is large, and the concept that the compressive stress is small indicates that the absolute value of the numerical value is small. Incidentally, the tensile stress is a kind of internal stress (intrinsic strain) existing in the coating layer, and means a stress represented by a numerical value “+” (plus). Note that the term “residual stress” includes both compressive stress and tensile stress.

  Such a compressive stress is preferably a stress having an absolute value of 0.1 GPa or more, more preferably 0.2 GPa or more, and even more preferably 0.5 GPa or more. If the absolute value is less than 0.1 GPa, sufficient toughness may not be obtained. On the other hand, the larger the absolute value, the better from the viewpoint of imparting toughness, but the absolute value exceeds 8 GPa. And the coating layer itself may peel off, which is not preferable.

The residual stress can be measured by the sin ² ψ method using an X-ray stress measuring device. Such residual stress is an arbitrary point (1 point, preferably 2 points, more preferably 3 to 5 points, and even more preferably 10 points (multiple points) included in the region where compressive stress is applied in the coating layer. each point when measuring measures the stress is preferable)) selecting at a distance of more than 0.1mm from each other to allow a representative stress of the region of the layer by the sin ² [psi method, the average It can be measured by determining the value.

The sin ² ψ method using X-rays is widely used as a method for measuring the residual stress of a polycrystalline material. For example, “X-ray stress measurement method” (Japan Society of Materials Science, 1981 Corporation) The method described in detail on pages 54 to 67 of Yokendo) may be used.

  The residual stress can also be measured by using a method using Raman spectroscopy. Such Raman spectroscopy has the merit that local measurement can be performed in a narrow range, for example, a spot diameter of 1 μm. The measurement of residual stress using such Raman spectroscopy is common, but for example, "Thin film mechanical property evaluation technique" (Sipec (currently renamed Realize Science and Technology Center), published in 1992. ), Pages 264 to 271 can be employed.

  Furthermore, the residual stress can also be measured using synchrotron radiation. In this case, there is an advantage that the distribution of residual stress can be obtained in the thickness direction of the coating layer.

<Others>
The first layer 11 or the second layer 12 (hereinafter referred to as a layer mainly composed of alumina in this section) of the present invention is a part of a cutting edge ridge line region involved in cutting as shown in FIGS. It is preferable that it is not formed in all. Thus, by not providing a layer mainly composed of alumina at the above-mentioned specific site, better welding resistance to the work material (and good peeling resistance of the coating layer at the initial stage of cutting) can be obtained. As a result, an excellent effect is obtained that excellent wear resistance and toughness can be obtained.

  Here, the cutting edge ridge line region involved in cutting includes the cutting edge ridge line (or cutting edge ridge line portion) that the work material actually contacts (or closest), and the work material contacts the vicinity of the cutting edge ridge line, The cutting edge ridge line also includes a case where the cutting edge ridge line substantially participates in the cutting (for example, a case where the temperature rises). However, a cutting edge ridge line in which chips of the work material at the time of cutting are scattered and contacted is not included.

  In addition, the cutting edge ridge line area is an area as shown by the area a in FIGS. 16 and 17, and more specifically, a cutting edge ridge line (if the cutting edge processing is performed, the assumed edge as described above). ) And the flank side and the rake face side, each having a width of 2000 μm or less. Naturally, this region can include a corner and can also be a part of a part involved in cutting.

  In addition, the judgment that the layer mainly composed of alumina is not formed is that the layer mainly composed of alumina is formed unless it is formed in a region of 10% or more of the cutting edge length in the edge region of the cutting edge involved in cutting. It is assumed that it is not formed, and the excellent effects as described above are shown. The non-formed region is preferably 50% or more, more preferably 100% (that is, all of the region), and the effect becomes more excellent as the region expands. Here, the said cutting edge length means the length of the direction parallel to the blade edge ridgeline of the blade edge ridgeline area | region involved in cutting.

  A more specific method for determining that the layer mainly composed of alumina is not formed is to observe the blade-tip-exchangeable cutting tip with a scanning electron microscope and to check the existence state of the layer mainly composed of alumina in the blade edge region. A line is drawn on the photograph that is parallel to the edge of the edge corresponding to the cutting edge length, and the area where the layer mainly composed of alumina does not exist is shown as a percentage. It shall be expressed.

  FIGS. 15 to 17 illustrate the above method more specifically (a diagram schematically showing a scanning electron micrograph). That is, the range of α in FIG. 15 represents the cutting edge length. 16 and 17 are enlarged views of the range of α, and FIG. 16 is a layer mainly composed of alumina in the entire edge region of the cutting edge involved in cutting (for convenience, it is shown as the first layer 11). 17 is the same), and FIG. 17 is a case where a layer mainly composed of alumina is not formed in a part of the edge line area related to cutting.

  16 and 17, a line b parallel to the edge of the cutting edge is drawn, and the length of the portion 15 on which the layer mainly composed of alumina is not formed is measured. In FIG. 16, there is no layer mainly composed of alumina on the line b, and therefore the range in which the layer mainly composed of alumina is not formed is 100% (all). On the other hand, in the case of FIG. 17, there are portions (b1, b3, b5) where the layer mainly composed of alumina is not formed on the line b, and the percentage calculated by (b1 + b3 + b5) / (b1 + b2 + b3 + b4 + b5) is mainly composed of alumina. It becomes the ratio of the range in which the layer to be formed is not formed. In addition, the said line b shall select the line which passes along the center of a blade edge ridgeline area | region.

  In the portion 15 where the layer mainly composed of alumina is not formed, the third layer or the substrate is exposed on the surface. However, when the third layer is exposed, the exposed portion is the outermost portion of the third layer. It may be configured by an upper layer, or may be configured such that the lower third layer appears substantially concentrically.

  As a method of forming the portion 15 in which the layer mainly composed of alumina is not formed as described above, various conventionally known methods can be adopted, and the method is not limited at all. For example, after a layer mainly composed of alumina is formed on the third layer, a blasting process, a brushing process, a barrel process or the like is performed on a layer mainly composed of alumina in a predetermined region where the layer mainly composed of alumina is not formed. Thus, it can be formed by removing the layer mainly composed of alumina. However, it is not limited to such a method.

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

<Example 1>
A cemented carbide powder having a composition (including inevitable impurities) composed of 1.0% by mass of TiC, 1.0% by mass of TaC, 0.5% by mass of NbC, 5.0% by mass of Co, and the balance of WC. Press and continue sintering at 1450 ° C. for 1 hour in a vacuum atmosphere, and then surface grinding and edge treatment with a SiC brush on the edge of the edge (honing 0.05 mm wide when viewed from the rake face side) By doing so, a cemented carbide tip having the same shape as the cutting tip CNMA120408 defined in JIS B4120 (1998 revision) was produced, and this was used as a base material. In this base material, a β-free layer is not formed on the surface, the two surfaces are raked surfaces, the four surfaces are flank surfaces, and the flank surfaces are edge edge lines (the edge of the blade is treated as described above). (This is a hypothetical ridge) and is connected to the rake face. There were a total of eight edge edges.

On the entire surface of the substrate, the following layers were formed in order from the lower layer as a coating layer by a known thermal CVD method. That is, in order from the surface side of the substrate, 0.3 μm TiN, 3.7 μm TiCN (formed by the MT-CVD method), and 0.3 μm TiN are formed as the third layers, respectively. One layer of 3.1 μm α-Al ₂ O ₃ was formed, and then a second layer of 0.9 μm κ-Al ₂ O ₃ was formed (this coating layer was coated with coating layer No. 1). And).

  In the same manner, this coating layer No. In place of the coating layer No. 1 described in Table 1 below. 2-8 were separately coat | covered with respect to the whole surface of a base material, respectively.

  In Table 1 above, each layer was laminated on the surface of the base material in order from the left side. The third layer is formed by the HT-CVD method (deposition temperature 1000 ° C.) without MT-CVD (deposition temperature 900 ° C.), and the first layer and the second layer are as follows. To form a film.

That is, the first layer and the second layer were formed using the reaction gas having the following composition I (deposition time was 5 hours, temperature was 1000 ° C., reaction pressure was 6.6 kPa). However, the first layer was formed for 1 hour after the start of film formation so that only the reaction gas having the following composition II was supplied, and then the reaction gas having the composition I was supplied.
Composition I: AlCl ₃ (4% by volume), CO ₂ (4% by volume) and H ₂ (balance)
Composition II: AlCl ₃ (4% by volume), CO ₂ (4% by volume), CO (2% by volume) and H ₂ (balance)
Then, by applying any of the following processing methods A to C to the flank or rake face of the base material on which these coating layers are formed, the uppermost layer (the uppermost layer after removal) of the flank and rake face is obtained. A part of the coating layer was removed so as to have the structure described in Table 2 below.

(Processing method A)
Blasting method (abrasive particles: alumina particles in water suspension (average particle size 50 μm), discharge pressure: 0.01 to 0.5 MPa, projection distance: 0.5 to 200 mm)
(Processing method B)
Brush method (using # 800 diamond brush)
(Processing method C)
Lapping method (polishing with # 800 diamond paste supported on bencott)

  In Table 2 above, the removal amount indicates the thickness (thickness from the outermost surface) of the coating layer removed by each of the above-described treatment methods, and the indication “-” indicates that the coating layer is not subjected to treatment on the surface. Indicates that it was not removed. Further, the uppermost layer after removal indicates the uppermost layer on each surface after the above processing method is applied.

  In this manner, the cutting edge replacement type cutting tip No. of the embodiment of the present invention described in Table 2 above was used. 1-13 were obtained. Further, for comparison, the cutting edge replacement type cutting tip No. 1 of the comparative example in which the above processing methods A to C were not applied. 14-21 were obtained.

The crystal structures of the alumina in the first layer and the second layer are 0. 0 in the direction of the flank and the rake face from the edge of the edge of the cutting edge-exchangeable cutting tip (assumed that the edge is treated). It confirmed by measuring the point 5 mm away by XRD, and confirmed that it was a thing of Table 1. Incidentally, the cutting edge exchange type cutting tip No. For the XRD peak of the uppermost layer of the rake face, the interplanar spacing d (Å) is 2.55, 2.08, 1.60 from the highest intensity to the fifth peak 3 It was confirmed that the uppermost layer was the first layer mainly containing α-Al ₂ O _3, and the XRD peak of the uppermost layer of the flank had its strength. Since the three peaks having the inter-plane spacing d (Å) of 2.57, 2.11 and 1.43 were included from the largest to the fifth, the uppermost layer was κ-Al It was confirmed that the second layer mainly contains ₂ O ₃ .

  Note that the above-mentioned measurement results of the interplanar spacing indicate that the XRD diffraction angle depends on the characteristics of the substrate (composition, sintering conditions, surface condition, etc.) even if the same conditions are employed as the alumina layer deposition conditions. It should be noted that the diffractive intensity may vary and may vary under the influence (same in each of the following examples).

  The blade tip replaceable cutting tip No. of the embodiment of the present invention thus obtained was obtained. 1-13 have a base material and the coating layer formed in at least one part on this base material, and this base material has a cutting edge ridgeline, a flank, and a rake face, The coating layer includes a first layer mainly including alumina having an α-type crystal structure and a second layer mainly including alumina other than alumina having an α-type crystal structure, and the first layer or the second layer Either one of the layers is formed in a continuous state in a region connecting from the flank face to the rake face across the edge of the cutting edge, and the first layer is the uppermost layer in at least a part of the rake face, The second layer was the uppermost layer in at least a part of the flank (including some of which the third layer was the uppermost layer).

  And these cutting edge exchange type cutting tip No. of this invention. 1 to 13 and the comparative example of the cutting edge type cutting tip No. About 14-21, while performing the abrasion resistance test on the following conditions, while measuring the flank wear amount (Vb) of a blade-tip-exchange-type cutting tip, the failure rate was calculated | required and the failure rate was calculated | required. The results are shown in Table 2 above. The flank wear amount (Vb) indicates that the smaller the value, the better the wear resistance, and the smaller the breakage rate, the better the toughness.

<Conditions for wear resistance test>
Work material: FCD700 round bar (HB240)
Cutting speed: 250 m / min.
Feed: 0.35mm / rev.
Cutting depth: 2.0mm
Wet / dry: wet (water-soluble oil)
Cutting time: 15 minutes <Conditions for fracture resistance test>
Work Material: SCM435 Round Bar with 4 Grooves (HB270)
Cutting speed: 100 m / min.
Feed: 0.28mm / rev.
Cutting depth: 1.0mm
Wet / dry: Dry Cutting time: 30 seconds Evaluation: The damage rate is determined from the number of breaks (number of broken corners) when 20 corners are cut for 30 seconds (ie, breakage rate (%) = number of breaks / 20 × 100 ).

  In addition, the ease of use identification of the blade edge ridge line (whether or not it was possible to easily identify whether or not a cutting test was performed using the edge ridge line) of the blade edge replaceable cutting tip after performing each of the above tests. Observed (the rightmost column of Table 2).

Further, the residual stress of the blade tip type cutting tip was also measured. The measurement of the residual stress was performed by measuring the cutting edge no. For 14 to 18, the second layer (measured for κ-Al ₂ O ₃ contained therein), and for the other blade-tip-exchangeable cutting tips, the first layer (measured for α-Al ₂ O ₃ contained therein), respectively. The following measurement was performed. That is, for each rake face, an arbitrary plan diameter of 0.3 mm with respect to the region S in FIG. 19 (an enlarged plan view schematically showing the corner portion of the rake face of the cutting edge replacement type cutting tip of the present embodiment). Three points (the distance between each spot was set so that the center of each spot was separated by 0.3 mm or more) were measured by the sin ² ψ method using the above-mentioned X-ray stress measuring apparatus, and the average value was measured as the residual stress. It was. The results are also shown in Table 2.

  As is clear from Table 2, the cutting edge replacement type cutting tip of the present invention showed excellent toughness and comparable wear resistance as compared with the cutting edge replacement type cutting tip of the comparative example. Therefore, it was confirmed that the wear resistance and the toughness are highly compatible when the configuration of the present invention is adopted in the cutting edge replaceable cutting tip.

  Note that the cutting edge replacement type cutting tip No. 1 and no. In No. 6, it was somewhat difficult to identify the use of the edge of the cutting edge, but the welding amount of the work material was very small, and the gloss of the work surface of the work material was very excellent.

  In addition, the cutting edge replacement type cutting tip No. No. 11 has the same wear resistance. It is presumed that the superiority to 9 and 10 is due to the fact that the cutting edge temperature at the time of cutting was lowered because the blast treatment was performed on the flank and the surface roughness was improved. No. 12 and no. No. 13 wear resistance It is presumed that the superiority to 11 is because the cutting edge temperature was lowered due to the improved surface roughness of the rake face.

  Further, when observing in detail the cutting edge ridge line on which the above test was carried out for each cutting edge replaceable cutting tip, there was almost no chipping observed when the compressive stress was applied to the coating layer, whereas the compressive stress was Since no chipping was observed, chipping was observed, and it was confirmed that the toughness (breakage resistance) was further improved when compressive stress was applied to the coating layer.

  In addition, although the blade edge | tip-exchange-type cutting tip of a present Example does not have a chip breaker, the effect of this invention is exhibited also about what has a chip breaker. Moreover, although the de-β layer is not formed on the base material of this example, the effect of the present invention is exhibited even if the de-β layer is formed.

<Example 2>
The cutting edge replacement type cutting tip No. 1 of the present invention in Example 1 was used. 1 is used to treat a cutting edge ridge line area (at least including a cutting edge processing portion) involved in the cutting with a SiC brush (# 120), thereby providing a first layer or a second layer (hereinafter simply referred to as “first layer”). A part or all of the alumina-based layer is removed, and three types of blade-tip-exchangeable cutting tips (blade-tip-exchangeable cutting tips No. 1-2, No. 1-3, and No. 1) having different removal rates, respectively. 1-4) was obtained.

  And the removal rate was calculated | required about these blade-tip-exchange-type cutting tips. The results are shown in Table 3 below. The removal rate is determined by the above-described method (the line b is drawn at the center of the area a as shown in FIG. 17 and the cutting edge length is 0.8 mm) in the edge line area related to cutting. The percentage of the area | region where the layer which mainly calculated | required alumina was not formed is shown.

  Similarly, the cutting edge replacement type cutting tip No. 1 of the present invention in Example 1 is used. 5 and no. No. 9 also has two types of blade-tip-exchangeable cutting tips (blade-tip-exchangeable cutting tips No. 5-2, No. 5-3 and No. 9-2, each having different removal rates of layers mainly composed of alumina, No. 9-3) was obtained and the removal rate was determined in the same manner. The results are shown in Table 3 below.

  In addition, in each said blade-tip-exchange-type cutting chip | tip, it confirmed that the numerical value of the residual stress did not change by the process by a SiC brush.

  Then, the flank wear amount (Vb) and the breakage rate were measured for these blade edge-exchangeable cutting tips in the same manner as in Example 1. These results are also shown in Table 3.

  As is apparent from Table 3, it was confirmed that the wear resistance and toughness were further improved when the layer mainly composed of alumina was not formed in a part or all of the edge line area related to cutting.

  Further, when observing in detail the cutting edge ridge line region in which the above test was performed on the cutting edge replaceable cutting tip, the layer mainly composed of alumina is removed at least partially from the cutting edge ridge line region involved in cutting. There was almost no disturbance of wear in the edge area of the cutting edge as compared with the case where it was not removed.

<Example 3>
Pressing cemented carbide powder with a composition (including inevitable impurities) consisting of 4.0% by mass of TiC, 6.0% by mass of TaC, 8.0% by mass of Co and the balance of WC, followed by vacuum JIS B4120 (1998) by sintering at 1400 ° C. for 1 hour, followed by surface grinding and edge treatment with a SiC brush (honing with a width of 0.05 mm when viewed from the rake face side). (Revision) A chip made of cemented carbide having the same shape as the prescribed cutting chip SPGN120408 was produced and used as a base material. In this base material, a β-free layer is not formed on the surface, one surface is a rake surface, four surfaces are flank surfaces, and the flank surfaces are edge edge lines (the edge of the blade is treated as described above). (This is a hypothetical ridge) and is connected to the rake face. There were a total of four edge edges.

On the entire surface of the substrate, the following layers were formed in order from the lower layer as a coating layer by a known thermal CVD method. That is, in order from the surface side of the substrate, 0.3 μm TiN, 2.8 μm TiCN (formed by MT-CVD method), and 0.2 μm TiN are formed as third layers, respectively, One layer of 2.3 μm α-Al ₂ O ₃ was formed, and a second layer of 0.8 μm κ-Al ₂ O ₃ was further formed thereon (this coating layer was coated with coating layer No. 101). And).

  In the same manner, this coating layer No. In place of the coating layer No. 101 described in Table 4 below, 102 to 105 were separately coated on the entire surface of the substrate.

  In Table 4 above, each layer was laminated on the surface of the base material in order from the left side. In addition, the third layer without MT-CVD (deposition temperature 900 ° C.) indicates that it was formed by the HT-CVD method (deposition temperature 1000 ° C.). The first layer and the second layer were formed under the same conditions as in Example 1.

  And by applying any one of the processing methods A to C as in Example 1 to the flank or rake face of the base material on which these coating layers are formed, the uppermost layer of the flank and rake face is as follows. A part of the coating layer was removed so as to have the configuration described in Table 5.

The notations in Table 5 above and similar to those in Table 2 have the same contents as in Table 2 above.
In this manner, the cutting edge replacement type cutting tip No. of the embodiment of the present invention described in Table 5 above was used. 101-110 were obtained. Further, for comparison, the cutting edge replacement type cutting tip No. 1 of the comparative example in which the above processing methods A to C were not applied. 111-115 were obtained.

The crystal structures of the alumina in the first layer and the second layer are 0. 0 in the direction of the flank and the rake face from the edge of the edge of the cutting edge-exchangeable cutting tip (assumed that the edge is treated). It confirmed by measuring by XRD the point 5 mm away, and confirmed that it was a thing of Table 4. Incidentally, the cutting edge exchange type cutting tip No. With respect to 101, the XRD peak of the uppermost layer of the rake face has an interplanar spacing d (Å) of 2.55, 2.37, and 1.60 from the highest intensity to the fifth peak 3 It was confirmed that the uppermost layer was the first layer mainly containing α-Al ₂ O _3, and the XRD peak of the uppermost layer of the flank had its strength. Since the three peaks having the inter-plane spacing d (Å) of 2.80, 2.11 and 1.43 were included from the largest to the fifth, the uppermost layer was κ-Al It was confirmed that the second layer mainly contains ₂ O ₃ .

  The blade tip replaceable cutting tip No. of the embodiment of the present invention thus obtained was obtained. 101-110 has a base material and the coating layer formed in at least one part on this base material, This base material has a cutting edge ridgeline, a flank, and a rake face, The coating layer includes a first layer mainly including alumina having an α-type crystal structure and a second layer mainly including alumina other than alumina having an α-type crystal structure, and the first layer or the second layer Either one of the layers is formed in a continuous state in a region connecting from the flank face to the rake face across the edge of the cutting edge, and the first layer is the uppermost layer in at least a part of the rake face, The second layer was the uppermost layer in at least a part of the flank (including some of which the third layer was the uppermost layer).

  And these cutting edge exchange type cutting tip No. of this invention. 101-110 and the comparative example cutting edge exchange type cutting tip No. About 111-115, while performing the abrasion resistance test on the following conditions, while measuring the flank wear amount (Vb) of a blade-tip-exchange-type cutting tip, the failure rate was calculated | required and the failure rate was calculated | required. The results are shown in Table 5 above. The flank wear amount (Vb) indicates that the smaller the value, the better the wear resistance, and the smaller the breakage rate, the better the toughness.

  In all of the following tests, DPG4100R (manufactured by Sumitomo Electric Hardmetal Co., Ltd.) was used as a cutter, and only one blade-tip-exchangeable cutting tip was attached to this cutter.

<Conditions for wear resistance test>
Work material: SKD61 (HRC45)
Cutting speed: 200 m / min.
Feeding: 0.2 mm / blade Cutting depth: 1.0 mm
Wet / dry: wet (water-soluble oil)
Cutting length: 2m
<Conditions for fracture resistance test>
Work material: SCM435 (HB260) Block material (with slit)
Cutting speed: 140 m / min.
Feed: 0.45mm / blade Cutting depth: 2.0mm
Wet / dry type: dry cutting length: 0.3m
Evaluation: The damage rate is obtained from the number of breaks (number of broken corners) when 20 corners are cut by 0.3 m (that is, the breakage rate (%) = number of breaks / 20 × 100).

  In addition, the ease of use identification of the blade edge ridge line was observed for the blade edge-exchangeable cutting tip after performing each of the above tests (the rightmost column in Table 5).

Further, the residual stress of the blade tip type cutting tip was also measured. The measurement of the residual stress was performed by measuring the cutting edge replaceable cutting tip No. of Comparative Example. As for 111 to 113, the second layer (measured for κ-Al ₂ O ₃ contained therein), and for the other blade cutting type cutting tips, the first layer (measured for α-Al ₂ O ₃ contained therein), respectively. The following measurement was performed. That is, for each rake face, a spot diameter of 0.3 mm is arbitrary with respect to a region T in FIG. 20 (an enlarged plan view schematically showing the corner portion of the rake face of the cutting edge replacement type cutting tip of this embodiment). Three points (the distance between each spot was set so that the center of each spot was separated by 0.3 mm or more) were measured by the sin ² ψ method using the above-mentioned X-ray stress measuring apparatus, and the average value was measured as the residual stress. It was. The results are also shown in Table 5.

  As is apparent from Table 5, the cutting edge replaceable cutting tip of the present invention exhibited superior toughness and comparable wear resistance as compared with the cutting edge replaceable cutting tip of the comparative example. Therefore, it was confirmed that the wear resistance and the toughness are highly compatible when the configuration of the present invention is adopted in the cutting edge replaceable cutting tip.

  Note that the cutting edge replacement type cutting tip No. 101, 104 and no. In No. 108, the use identification of the edge of the cutting edge was somewhat difficult, but the welding amount of the work material was very small, and the gloss of the work surface of the work material was very excellent.

  Further, when observing in detail the cutting edge ridge line on which the above test was carried out for each cutting edge replaceable cutting tip, there was almost no chipping observed when the compressive stress was applied to the coating layer, whereas the compressive stress was Since no chipping was observed, chipping was observed, and it was confirmed that the toughness (breakage resistance) was further improved when compressive stress was applied to the coating layer.

  In addition, although the blade edge | tip-exchange-type cutting tip of a present Example does not have a chip breaker, the effect of this invention is exhibited also about what has a chip breaker. Moreover, although the de-β layer is not formed on the base material of this example, the effect of the present invention is exhibited even if the de-β layer is formed.

<Example 4>
In Example 3, the cutting edge replacement type cutting tip No. 102, by applying a treatment with a SiC brush (# 320) to a cutting edge ridge line region (including at least a cutting edge processing portion) involved in the cutting, the first layer or the second layer (hereinafter simply referred to as “the first layer”) Part or all of the layer (referred to as a layer mainly composed of alumina) is removed, and two types of blade-tip-exchangeable cutting tips (blade-tip-exchangeable cutting tips No. 102-2 and No. 102-3) having different removal rates are obtained. It was.

  And the removal rate was calculated | required similarly to Example 2 about these blade-tip-exchange-type cutting tips. The results are shown in Table 6 below.

  Similarly, the cutting edge replacement type cutting tip No. 1 of the present invention in Example 3 is used. 105 and No. Also for 106, two types of blade-tip-exchangeable cutting tips (blade-tip-exchangeable cutting tips No. 105-2, No. 105-3 and No. 106-2, each having different removal rates of layers mainly composed of alumina, No. 106-3) was obtained and the removal rate was determined in the same manner. The results are shown in Table 6 below.

  In addition, in each said blade-tip-exchange-type cutting chip | tip, it confirmed that the numerical value of the residual stress did not change by the process by a SiC brush.

  Then, the flank wear amount (Vb) and the breakage rate were measured for these blade-tip-exchangeable cutting tips in the same manner as in Example 3. These results are also shown in Table 6.

  As can be seen from Table 6, it was confirmed that the wear resistance and toughness were further improved when the layer mainly composed of alumina was not formed in part or all of the edge area of the cutting edge involved in cutting.

  Further, when observing in detail the cutting edge ridge line region in which the above test was performed on the cutting edge replaceable cutting tip, the layer mainly composed of alumina is removed at least partially from the cutting edge ridge line region involved in cutting. There was almost no disturbance of wear in the edge area of the cutting edge as compared with the case where it was not removed.

<Example 5>
The same substrate as that of Example 3 was used as the substrate, and this substrate was used as a film formation apparatus (physical vapor deposition apparatus) as an unbalanced magnetron sputtering apparatus (a cold cathode arc type) using a pulsed DC power source. (Ion plating / unbalanced magnetron sputtering combined machine).

  FIG. 18 is a schematic diagram showing a schematic configuration of the film forming apparatus 20. A plurality of arc evaporation sources 21 and 22 and unbalanced magnetron sputtering evaporation sources (hereinafter referred to as UBM sputtering sources) 23 and 24 are arranged in the film forming apparatus 20 shown in FIG. The base material 8 was attached to a holder 27 that rotates in a manner that faces each of the evaporation sources 21 to 24. The necessary gas is introduced from the gas inlet 25 into the film forming apparatus 20. In addition, a heater 26 is provided in the film forming apparatus 20.

  First, a predetermined TiAl alloy target was set in the arc evaporation source 21, a predetermined Ti target was set in the arc evaporation source 22, and Al was set in the UBM sputtering sources 23 and 24. That is, the first layer and the second layer are formed by the UBM sputtering source, and the third layer is formed by the arc evaporation source.

First, the inside of the chamber of the apparatus was depressurized to 1 × 10 ⁻³ Pa or less by a vacuum pump, and the temperature of the substrate 8 was heated to 510 ° C. by a heater 26 installed in the apparatus.

  Next, while introducing argon gas from the gas inlet 25 and maintaining the pressure in the chamber at 3 Pa, the voltage of the substrate bias power supply is gradually increased to apply a voltage of −950 V to the base material 8, thereby Then, glow discharge was generated and the surface of the substrate was cleaned with argon ions for 15 minutes. Thereafter, argon gas was exhausted.

Next, in a state where N ₂ (nitrogen gas) was introduced from the gas inlet 25 while applying a bias voltage of −50 V to the base material 8, the arc evaporation source 21 was subjected to vacuum arc discharge with an arc current of 100 A, and the TiAl alloy By ionizing the target, a 1.9 μm TiAlN layer was formed as a third layer on the substrate 8.

Subsequently, the heater 26 was adjusted so that the temperature of the base material 8 became 720 ° C., and a pulsed DC having a substrate bias voltage of −100 V with respect to the base material 8 (pulse frequency 250 kHz, ON time and OFF time 2 μsec. ) Is applied, oxygen gas of 40 sccm (flow rate of 40 cc per minute in the standard state) and argon gas of 360 sccm are introduced into the device from the gas inlet 25 and the pressure in the device is 1.1 Pa. Then, the UBM sputtering sources 23 and 24 were discharged to form a 2.7 μm α-Al ₂ O ₃ layer as the first layer on the third layer of the substrate 8. In this case, pulse DC (pulse frequency 100 kHz, ON time 8 μsec., OFF time 2 μsec.) Was used for the UBM sputtering source, and the sputtering power was 2.8 kW.

Next, in a state where N ₂ (nitrogen gas) is introduced from the gas inlet 25 while applying a bias voltage of −50 V to the base material 8 on which the first layer is formed, the arc evaporation source 21 is vacuum-arc discharged by an arc current of 100 A. Then, the TiAl alloy target was ionized to form a 0.8 μm TiAlN layer as a third layer on the first layer.

Subsequently, the heater 26 is adjusted so that the temperature of the substrate 8 on which the plurality of coating layers are formed as described above is 620 ° C., and a pulse DC (pulse pulse) with a substrate bias voltage of −100 V is applied to the substrate 8. In a state in which a frequency of 250 kHz and ON time and OFF time are both 2 μsec.), 40 sccm of oxygen gas and 360 sccm of argon gas are introduced into the apparatus through the gas inlet 25 and the pressure in the apparatus is 1.1 Pa. The UBM sputtering sources 23 and 24 were discharged to form a 0.9 μm γ-Al ₂ O ₃ layer as the second layer on the third layer of the substrate 8. In this case, pulse DC (pulse frequency 100 kHz, ON time 8 μsec., OFF time 2 μsec.) Was used for the UBM sputtering source, and the sputtering power was 2.8 kW.

Next, arc evaporation is performed by an arc current of 100 A while N ₂ (nitrogen gas) and methane gas are introduced from the gas inlet 25 while applying a bias voltage of −50 V to the base material 8 on which the second layer is formed as described above. The source 22 was subjected to vacuum arc discharge to ionize the Ti target to form a 0.2 μm TiCN layer as the third layer on the second layer (this coating layer is referred to as coating layer No. 201). .

  Thereafter, this coating layer No. was formed by physical vapor deposition in the same manner as described above. In place of 201, the coating layer No. described in Table 7 below was used. 202 to 204 were separately coated on the entire surface of the substrate.

In Table 7 above, each layer was laminated on the surface of the base material in order from the left side.
And by applying any one of the processing methods A to C as in Example 1 to the flank or rake face of the base material on which these coating layers are formed, the uppermost layer of the flank and rake face is as follows. A part of the coating layer was removed so as to have the structure described in Table 8.

The notations in Table 8 above and similar to those in Table 2 show the same contents as in Table 2 above.
In this way, the blade tip replaceable cutting tip No. of the embodiment of the present invention described in Table 8 above was used. 201-206 were obtained. Further, for comparison, the cutting edge replacement type cutting tip No. 1 of the comparative example in which the above processing methods A to C were not applied. 207-210 were obtained.

The crystal structures of the alumina in the first layer and the second layer are 0. 0 in the direction of the flank and the rake face from the edge of the edge of the cutting edge-exchangeable cutting tip (assumed that the edge is treated). It confirmed by measuring the spot which was 5 mm apart by XRD, and confirmed that it was a thing of Table 7. Incidentally, the cutting edge exchange type cutting tip No. With respect to 203, the XRD peak of the uppermost layer of the rake face is confirmed to have four distinct peaks for alumina, and the interplanar spacing d (も の) from the highest to the second is 2.37. And 1.37, it was confirmed that the uppermost layer was the first layer mainly containing α-Al ₂ O _3, and the XRD peak of the uppermost layer on the flank had its strength Included three peaks with the interplanar spacing d (Å) of 2.28, 1.97, and 1.39 from the largest to the fifth one. Since two of the peaks are γ-Al ₂ O ₃ peaks, it was confirmed that the uppermost layer was a second layer mainly containing γ-Al ₂ O ₃ .

  The blade tip replaceable cutting tip No. of the embodiment of the present invention thus obtained was obtained. 201-206 has a base material and the coating layer formed in at least one part on this base material, This base material has a cutting edge ridgeline, a flank, and a rake face, The coating layer includes a first layer mainly including alumina having an α-type crystal structure and a second layer mainly including alumina other than alumina having an α-type crystal structure, and the first layer or the second layer Either one of the layers is formed in a continuous state in a region connecting from the flank face to the rake face across the edge of the cutting edge, and the first layer is the uppermost layer in at least a part of the rake face, The second layer was the uppermost layer in at least a part of the flank (including some of which the third layer was the uppermost layer).

  And these cutting edge exchange type cutting tip No. of this invention. 201 to 206 and the cutting edge exchange type cutting tip No. About 207-210, while performing the abrasion resistance test on the following conditions, the flank wear amount (Vb) of the blade-tip-exchange-type cutting tip was measured, and the breakage rate was obtained by performing the fracture resistance test. The results are shown in Table 8 above. The flank wear amount (Vb) indicates that the smaller the value, the better the wear resistance, and the smaller the breakage rate, the better the toughness.

  In the following tests, the same DPG4100R (manufactured by Sumitomo Electric Hardmetal Co., Ltd.) as in Example 3 was used as a cutter, and only one blade-tip-exchangeable cutting tip was attached to this cutter.

<Conditions for wear resistance test>
Work material: FC250 (HB220)
Cutting speed: 350 m / min.
Feed: 0.25mm / blade Cutting depth: 2.0mm
Wet / dry: dry
Cutting length: 20m
<Conditions for fracture resistance test>
Work material: FCD450 (HB210) Block material (with slits)
Cutting speed: 140 m / min.
Feed: 0.45mm / blade Cutting depth: 2.0mm
Wet / dry type: dry cutting length: 0.3m
Evaluation: The damage rate is obtained from the number of breaks (number of broken corners) when 20 corners are cut by 0.3 m (that is, the breakage rate (%) = number of breaks / 20 × 100).

  In addition, the ease of use identification of the blade edge ridge line was observed for the blade-tip-exchangeable cutting tip after each of the above tests (the rightmost column in Table 8).

Further, the residual stress of the blade tip type cutting tip was also measured. The measurement of the residual stress was performed by measuring the cutting edge no. For 207 to 209, the second layer (measured for γ-Al ₂ O ₃ contained therein) was used, and for the other blade cutting type cutting tips, the first layer (measured for α-Al ₂ O ₃ contained therein) was conducted. The same measurement location and measurement method as in Example 3 were used. The results are also shown in Table 8.

  As is apparent from Table 8, the cutting edge-exchangeable cutting tip of the present invention showed toughness superior to that of the cutting edge-exchangeable cutting tip of the comparative example and an equivalent level of wear resistance. Therefore, it was confirmed that the wear resistance and the toughness are highly compatible when the configuration of the present invention is adopted in the cutting edge replaceable cutting tip.

  Note that the cutting edge replacement type cutting tip No. In No. 203, it was somewhat difficult to identify the use of the edge of the cutting edge, but the welding amount of the work material was very small, and the gloss of the work surface of the work material was very excellent.

  Moreover, when the edge ridgeline in which said test was implemented about each blade-tip-exchange-type cutting tip was observed in detail, chipping was hardly recognized. This is probably because compressive stress is imparted to the coating layer when the coating layer is formed by physical vapor deposition, and therefore toughness (breakage resistance) is improved.

  In addition, although the blade edge | tip-exchange-type cutting tip of a present Example does not have a chip breaker, the effect of this invention is exhibited also about what has a chip breaker. Moreover, although the de-β layer is not formed on the base material of this example, the effect of the present invention is exhibited even if the de-β layer is formed.

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

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

It is the schematic which showed typically the contact state of the blade-tip-exchange-type cutting tip and work material at the time of cutting. It is a schematic perspective view which shows an example of the blade-tip-exchange-type cutting tip of this invention. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip containing a 1st layer and a 2nd layer as a coating layer. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip containing a 1st layer, a 2nd layer, and a 3rd layer as a coating layer. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip containing two 3rd layers as a coating layer. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip of another aspect different from FIG. 5 containing two 3rd layers as a coating layer. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip containing three 3rd layers as a coating layer. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip of another aspect different from FIG. 6 containing two 3rd layers as a coating layer. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip of another aspect different from FIG. 3 containing a 1st layer and a 2nd layer as a coating layer. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip of another aspect different from FIG. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip of another aspect different from FIG. 5 containing two 3rd layers as a coating layer. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip of another aspect different from FIG. 11 containing two 3rd layers as a coating layer. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip of another aspect different from FIG. 7 containing 3rd 3rd layers as a coating layer. It is a partial schematic sectional drawing of the blade-tip-exchange-type cutting tip of another aspect different from FIG. 13 which contains three 3rd layers as a coating layer. It is a schematic diagram of the blade-tip-exchange-type cutting tip showing the cutting edge length. It is the schematic diagram of the scanning electron micrograph which expanded the range of (alpha) in FIG. It is another schematic diagram of the scanning electron micrograph which expanded the range of (alpha) in FIG. It is a schematic diagram which shows schematic structure of the film-forming apparatus. It is the enlarged plan view which modeled the corner part of the rake face of a blade-tip-exchange-type cutting tip. FIG. 20 is an enlarged plan view of another aspect different from FIG. 19 in which the corner portion of the rake face of the blade-tip-exchange-type cutting tip is schematically shown.

Explanation of symbols

  DESCRIPTION OF SYMBOLS 1 Cutting edge exchange type cutting tip, 2 Drake face, 3 Flank face, 4 Edge edge line, 5 Work material, 6 Chip, 7 Through-hole, 8 Base material, 9 Corner, 11 1st layer, 12 2nd layer, 13 3rd layer, 14 coating layer, 15 part in which layer mainly composed of alumina is not formed, 20 deposition apparatus, 21, 22 arc evaporation source, 23, 24 unbalanced magnetron sputter evaporation source, 25 gas inlet, 26 heaters, 27 holders.

Claims (9)

A cutting edge-exchangeable cutting tip having a base material and a coating layer formed on at least a part of the base material,
The substrate has a cutting edge ridgeline, a flank face and a rake face,
The coating layer includes a first layer mainly including alumina having an α-type crystal structure and a second layer mainly including alumina other than alumina having an α-type crystal structure,
Either one of the first layer and the second layer is formed in a continuous state in a region connected from the flank face to the rake face across the cutting edge ridge line,
The first layer is an uppermost layer in at least a part of the rake face,
The cutting edge exchange type cutting tip, wherein the second layer is an uppermost layer in at least a part of the flank. The second layer is formed in a continuous state in a region connected from the flank face to the rake face across the edge of the blade edge,
The cutting edge-exchangeable cutting tip according to claim 1, wherein the first layer is formed on the second layer in at least a part of the rake face.   The first layer is formed in a continuous state on the second layer in a region connected from the flank to the rake face across the cutting edge ridge line, and then from a region including at least a part of the flank. The cutting edge replacement type cutting tip according to claim 2, wherein the cutting edge replacement type cutting tip is removed. The first layer is formed in a continuous state in a region connected from the flank face to the rake face across the edge of the cutting edge.
The cutting edge replacement type cutting tip according to claim 1, wherein the second layer is formed on the first layer in at least a part of the flank.   The second layer is formed in a continuous state on the first layer in a region connected from the flank face to the rake face across the edge of the cutting edge, and then from a region including at least a part of the rake face. The cutting edge replacement type cutting tip according to claim 4, wherein the cutting edge replacement type cutting tip is removed.   The cutting edge exchangeable cutting tip according to any one of claims 1 to 5, wherein the coating layer includes one or more third layers different from the first layer and the second layer.   The blade tip exchange type cutting tip according to claim 6, wherein the third layer is an uppermost layer in at least a part of the flank or at least a part of the rake face.   The blade tip exchange type cutting tip according to claim 6 or 7, wherein the third layer is formed between the first layer and the second layer.   The blade tip replaceable cutting tip according to any one of claims 6 to 8, wherein the third layer is formed on the base material.

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