Coated tool and cutting tool having the same

Abstract

The coated tool (1) disclosed herein comprises: a first surface (5); a second surface (7); a cutting edge (11) located at least on a portion of the ridgeline of the first surface (5) and the second surface (7); a third surface (9) located on the opposite side of the first surface (5); and a through hole (15) extending from the first surface (5) to the third surface (9). The inner wall (17) constituting the through hole (15) comprises a binder phase-rich layer (19) having a higher binder phase content than the interior of the substrate (3) at least in the central portion. The thickness T1 of the binder phase-rich layer (19) at the central portion is thicker than the thickness T2 of the binder phase-rich layer (19) at the end portion of the inner wall. The coating layer (30) is located at least on the binder phase-rich layer (19). The coating layer (30) comprises a first layer (31) comprising cubic titanium carbonitride. The orientation coefficient Tc(220) of the titanium carbonitride of the first layer (31) is 3.0 or more based on X-ray diffraction analysis.

Description

Technical Field

[0001] The present disclosure relates to a coated tool used in cutting and a cutting tool including the coated tool. Background Art

[0002] Currently, cermets containing titanium (Ti) as a main component are widely used as substrates for components requiring wear resistance, sliding properties, and chipping resistance, such as cutting tools, wear-resistant components, and sliding components.

[0003] For example, Patent Document 1 describes a cutting insert having a titanium carbonitride-based cermet coated on the surface of a through-hole for mounting a tool body. Patent Document 1 describes providing an insert that is less susceptible to abnormal damage even during high-load cutting, by providing a metal seepage layer on the inner surface of the through-hole for mounting.

[0004] Prior art literature

[0005] Patent Literature

[0006] Patent Document 1: Japanese Patent Application Laid-Open No. 2012-245581 Summary of the Invention

[0007] The coated tool disclosed herein comprises: a base body of a metal ceramic containing hard particles and a binder phase, and a coating layer located on the base body. The coated tool comprises: a first surface; a second surface; a cutting edge located at least on a portion of the ridgeline of the first and second surfaces; a third surface located on the opposite side of the first surface; and a through hole extending from the first surface to the third surface. The inner wall constituting the through hole comprises a binder phase-rich layer having a higher binder phase content than the interior of the base body at least in the central portion. The thickness T1 of the binder phase-rich layer in the central portion is thicker than the thickness T2 of the binder phase-rich layer at the end portions of the inner wall. The coating layer is located at least on the binder phase-rich layer. The coating layer comprises a first layer comprising cubic titanium carbonitride. The orientation coefficient Tc(220) of the titanium carbonitride in the first layer, as determined by X-ray diffraction analysis, is 3.0 or greater. BRIEF DESCRIPTION OF THE DRAWINGS

[0008] Figure 1 This is a perspective view showing an example of the coated tool of the present disclosure.

[0009] Figure 2 This is a schematic diagram showing a cross section of an example of the coated tool disclosed herein.

[0010] Figure 3 This is an enlarged schematic view of a cross section of the coated tool of the present disclosure.

[0011] Figure 4 This is an enlarged schematic view of a cross section of another embodiment of the coated tool disclosed herein.

[0012] Figure 5This is an enlarged schematic view of a cross section of another embodiment of the coated tool disclosed herein.

[0013] Figure 6 This is a schematic enlarged view of a coating layer of the coated tool of the present disclosure.

[0014] Figure 7 This is a plan view showing an example of the cutting tool disclosed herein.

[0015] Figure 8 This is an enlarged schematic view of a cross section of a coated tool in the cutting tool of the present disclosure. DETAILED DESCRIPTION

[0016] <covered tool>

[0017] The coated tool disclosed herein is described in detail below using the accompanying drawings. However, for ease of explanation, the figures referenced below only simplify the illustrations of the essential components necessary to illustrate the embodiment. Therefore, the coated tool disclosed herein may include any components not shown in the referenced figures. Furthermore, the dimensions of the components in the figures do not faithfully represent the actual dimensions of the components or the dimensional ratios of the components. These points also apply to the cutting tools described below.

[0018] It is desirable that a coated tool used in cutting has less abnormal damage. The present disclosure provides a coated tool having less abnormal damage and a cutting tool having the same.

[0019] The coated tool disclosed herein comprises a cermet matrix containing hard particles and a binder phase. Examples of the hard particles include TiCN, TiC, TiN, and (TiM)CN (where M is one or more selected from W, Nb, Ta, Mo, and V). The binder phase is primarily composed of an iron-group metal such as Ni or Co. The term "main component" refers to a component that accounts for 50% or more of the total mass of the components.

[0020] like Figure 1 、 2 As shown, the shape of the coated tool 1 of the present disclosure may be, for example, a square plate shape. Figure 1 The upper surface in the tool 1, that is, the first surface 5 is a so-called rake face.

[0021] The coated tool 1 has a third surface 9 which is located on the lower surface opposite to the first surface 5. The second surface 7 is connected to the first surface 5 and the third surface 9, respectively.

[0022] The coated tool 1 of the present disclosure has a cutting edge 11 located at least a portion of the ridgeline where the first surface 5 and the second surface 7 intersect. In other words, the coated tool 1 of the present disclosure has a cutting edge 11 located at least a portion of the ridgeline where the front cutting surface and the back cutting surface intersect. The cutting edge 11 has a fourth surface that is continuous with the first surface 5 and the second surface 7. The fourth surface can be a C surface (bevel surface) in which the corners of the first surface 5 and the second surface 7 are obliquely and linearly removed. In addition, the fourth surface can be an R surface (round surface) in which the corners of the first surface 5 and the second surface 7 are rounded.

[0023] In the coated tool 1, the entire outer periphery of the first surface 5 can serve as the cutting edge 11, but the coated tool 1 is not limited to such a structure. For example, only one side of the square rake face, in other words, one of the four fourth surfaces may have the cutting edge 11.

[0024] The coated tool 1 of the present disclosure has a through hole 15 that penetrates the base 3 from the first surface 5 to the third surface 9. Figure 3 As shown, a binder phase-rich layer 19 exists at least in the central portion 17a of the inner wall 17 forming the through-hole 15. Binder phase-rich layer 19 contains hard particles and a binder phase, and its binder phase content is higher than that of the interior of the substrate 3. The interior of the substrate 3 refers to the portion that is at least 500 μm away from the surface of the substrate 3. Binder phase-rich layer 19 does not need to exist on the entire inner wall 17 of the through-hole 15; it only needs to be located in the central portion 17a.

[0025] The center portion 17a is the middle when the through hole 15 is divided into nine equal parts in the depth direction. In addition, the end portions 17b are the end portions when the through hole 15 is divided into nine equal parts in the depth direction.

[0026] like Figure 3 As shown, in the coated tool 1 of the present disclosure, the thickness T1 of the binder phase-rich layer 19 at the center portion 17a of the inner wall 17 constituting the through-hole 15 is greater than the thickness T2 of the binder phase-rich layer 19 at the end portion 17b of the inner wall 17 constituting the through-hole 15. The thickness T1 of the binder phase-rich layer 19 at the center portion 17a and the thickness T2 of the binder phase-rich layer 19 at the end portion 17b are average values. The thicknesses T1 and T2 can be measured by observing a cross section of the coated tool 1 using a metal microscope or an electron microscope. Furthermore, the binder phase-rich layer 19 may not be present at the end portion 17b.

[0027] The coated tool 1 of the present disclosure has such a structure, and thus suppresses abnormal damage starting from the inner wall 17 to which a large force is applied when the coated tool 1 is fixed to a stent (not shown).

[0028] Figure 6 Schematic enlarged view of the coating layer of the coated tool 1 of the present disclosure. Figure 6As shown, the coated tool 1 has a coating layer 30 .

[0029] The coating layer 30 is located at least on the binder phase-rich layer 19. The coating layer 30 may be located on the first surface 5 or on a surface other than the first surface 5 of the substrate 3. The coating layer 30 improves the wear resistance and chipping resistance of the coated tool 1 during cutting.

[0030] The coating layer 30 includes a first layer 31 and a second layer 32. The first layer 31 is located on the first surface 5 and contains cubic titanium carbonitride. The second layer 32 is provided in contact with the first layer 31. The second layer 32 may contain, for example, aluminum oxide (Al2O3).

[0031] A titanium nitride layer 33 may be provided between the first layer 31 and the base 3. With such a structure, the bonding between the base 3 and the first layer 31 is high.

[0032] The first layer 31 includes a titanium carbonitride layer 34. In addition to titanium carbonitride, the first layer 31 may also contain titanium carbide, nitride, oxide, oxycarbide, and oxycarbonitride. Furthermore, as long as the first layer 31 contains cubic titanium carbonitride, it may have a single-layer structure or a stacked structure of multiple layers.

[0033] The main components of titanium nitride layer 33 and titanium carbonitride layer 34 are titanium nitride and titanium carbonitride, respectively. The term "main component" refers to the component with the largest mass % value compared to other components. Titanium nitride layer 33 and titanium carbonitride layer 34 may contain components other than titanium nitride and titanium carbonitride, respectively.

[0034] The coating layer 30 may include only the first layer 31 and the second layer 32 , or may include layers other than these layers. For example, another layer may be present between the substrate 3 and the first layer 31 , or another layer may be present on the second layer 32 .

[0035] The first layer 31 is located at least on the binder phase-rich layer 19. The first layer 31 has a portion having a higher hardness than the binder phase-rich layer 19. This structure improves the wear resistance of the fixture portion. The first layer 31 can be formed by CVD or PVD.

[0036] X-ray diffraction (XRD) analysis of the first layer 31 shows a maximum peak on the (220) plane among the crystal planes of the cubic titanium carbonitride. The orientation coefficient Tc(220) of the titanium carbonitride based on X-ray diffraction analysis is 3.0 or greater. With such a structure, the adhesion between the binder-rich layer 19 and the first layer 31 becomes stronger, making it difficult to cause delamination at the interface between the binder-rich layer 19 and the first layer 31, thereby suppressing abnormal damage to the coated tool 1 caused by delamination. In addition, when other layers are provided between the first layer 31 and the binder-rich layer 19, the adhesion between the other layers and the first layer 31 becomes stronger, making it difficult to cause delamination at the interface between the other layers and the first layer 31, thereby suppressing abnormal damage to the coated tool 1 caused by delamination.

[0037] The orientation coefficient Tc(hkl) is calculated by the following formula.

[0038] Tc(hkl)={I(hkl) / I0(hkl)} / 〔(1 / 7)×Σ{I(HKL) / I0(HKL)}〕

[0039] Here, (HKL) refers to all the crystal planes (111), (200), (220), (311), (331), (420), and (422). In addition, (hkl) refers to each crystal plane.

[0040] I(HKL) and I(hkl) are peak intensities of peaks attributed to respective crystal planes detected in X-ray diffraction analysis of cubic titanium carbonitride in the first layer 31 .

[0041] I0(HKL) and I0(hkl) are standard diffraction intensities of each crystal plane described in JCPDS card No. 00-042-1489.

[0042] The above-mentioned orientation coefficient Tc(hkl) may be measured from the flat upper surface of the first layer 31 , and may be measured on the second surface 7 , for example.

[0043] Examples of the second layer 32 containing aluminum oxide include α-alumina (α-Al2O3), γ-alumina (γ-Al2O3), and κ-alumina (κ-Al2O3). Among these, when the second layer 32 contains α-alumina, the heat resistance of the coated tool 1 can be improved. The second layer 32 may contain only one of the above compounds, or may contain multiple compounds.

[0044] Whether the aluminum oxide contained in the second layer 32 is one of the above-mentioned compounds can be evaluated by, for example, performing X-ray diffraction (XRD) analysis and observing the distribution of peaks.

[0045] The first layer 31 may contain components other than titanium carbonitride. Furthermore, the second layer 32 may contain components other than aluminum oxide. For example, the first layer 31 may contain aluminum oxide. Furthermore, the second layer 32 may contain a titanium compound such as titanium carbonitride. In this case, the bonding between the first layer 31 and the second layer 32 is improved.

[0046] The hardness of the binder phase-rich layer 19 is lower than that of the substrate 3 but higher than that of the metal seepage layer described in Reference 1. Therefore, the binder phase-rich layer 19 suppresses deformation more than the metal seepage layer.

[0047] Due to the above-mentioned structure, when the coated tool 1 is fixed to the bracket with a fixture, the local force applied to the base 3 due to the suppressed deformation of the adhesive phase enriched layer 19 at the central portion 17a during the contact between the central portion 17a of the inner wall 17 and the fixture is small, so the coated tool 1 is difficult to break and difficult to be abnormally damaged.

[0048] The size of the coated tool 1 is not particularly limited. For example, the length of one side of the rake face is set to about 3 to 20 mm. In addition, the thickness of the coated tool 1 is set to about 1 to 20 mm. Figure 1 In the figure, a square-shaped coated tool 1 is shown as an example, but a triangular shape or a disk shape may also be used.

[0049] In addition, if Figure 4 As shown in FIG. 1 , the coated tool 1 of the present disclosure may have an enlarged diameter portion 21 connected to the inner wall 17. There is a height difference at the boundary between the through hole 15 and the enlarged diameter portion 21. Figure 4 In the illustrated example, the binder phase-rich layer 19 is not present on the inner wall of the expanded diameter portion 21, but a binder phase-rich layer 19 may also be present there. In the coated tool 1 of the present disclosure, the expanded diameter portion 21 is not included in the through-hole 15. The expanded diameter portion 21 is a so-called spot facing surface. The diameter of the expanded diameter portion 21 is at least 300 μm larger than the diameter of the through-hole 15.

[0050] The thickness T1 of the binder phase-rich layer 19 in the central portion 17a can be 1 μm or greater. Alternatively, the thickness T1 can be 20 μm or less. This structure suppresses abnormal damage to the coated tool 1. The thickness T1 can be 3 μm or greater. Alternatively, the thickness T1 can be 10 μm or less.

[0051] The thickness T2 of the binder phase-rich layer 19 at the end portion 17b may be 0.2 μm or more. Alternatively, the thickness T2 may be 6 μm or less. With such a structure, abnormal damage to the coated tool 1 is suppressed.

[0052] like Figure 5As shown, the diameter R1 of the center portion 17a can be larger than the diameter R2 of the end portion 17b. With such a structure, the contact area between the fixture and the inner wall 17 is increased, thereby increasing the clamping force.

[0053] The diameter R1 at the center portion 17a may be larger than the diameter R2 at the end portion 17b by 5 μm or more and 30 μm or less. With such a structure, abnormal damage to the coated tool 1 is suppressed.

[0054] The hardness of the binder-phase-rich layer 19 in the central portion 17a can be between 10 GPa and 20 GPa. With this structure, the binder-phase-rich layer 19 deforms appropriately when the clamp pins make contact, increasing the clamping force. The hardness of the binder-phase-rich layer 19 in the central portion 17a can be measured using nanoindentation on the exposed binder-phase-rich layer 19 in a cross section of the coated tool 1.

[0055] The binder-phase-rich layer 19 in the central portion 17a may include a metal layer (not shown) on the through-axis side of the through-hole 15, containing a higher binder phase than the binder-phase-rich layer 19. This metal layer contains only metal, without a hard layer. With this structure, the metal layer functions as a buffer material between the fixture (described later) and the binder-phase-rich layer 19, thereby preventing abnormal damage to the coated tool 1. The thickness of the metal layer can be between 0.3 μm and 2 μm.

[0056] <Method for Manufacturing Coated Tool>

[0057] The following describes a method for manufacturing the coated tool of the present disclosure.

[0058] The raw material powder used for producing the coated tool of the present disclosure is generally used for producing cermets.

[0059] The matrix contains, for example, 40% to 80% by mass of TiCN as hard particles and 6% to 30% by mass of Co as a binder phase. Furthermore, the matrix may contain WC, TaC, NbC, Mo2C, VC, ZrC, etc. for improved properties.

[0060] The raw material having the above composition is formed into a shape having a space that will become a through hole after firing. Thereafter, firing is performed at a temperature of, for example, 1400° C. to 1600° C. The firing environment can be set to an N 2 partial pressure environment.

[0061] When the N2 partial pressure is set to 1 kPa or higher, the thickness of the binder phase-rich layer after firing increases. Furthermore, when the average particle size d50 of the hard particles used as a raw material is set to 0.7 μm or lower, a binder phase-rich layer can be obtained, in which a metal layer having a higher binder phase content than the binder phase-rich layer is provided on the through-axis (not shown) side of the through-hole.

[0062] Furthermore, during the aforementioned molding process, if the molding pressure is high, deformation during firing can be suppressed. On the other hand, if the molding pressure is low during molding, the diameter R1 at the center of the inner wall tends to become larger than the diameter R2 at the end. The relationship between molding pressure and deformation varies depending on the composition and firing temperature, and can therefore be adjusted in various combinations.

[0063] For example, after firing, a rotating brush is inserted into the through-hole from both ends to grind the inner wall of the through-hole so that the thickness T1 of the binder phase-rich layer in the center becomes thicker than the thickness T2 of the binder phase-rich layer at the ends. Alternatively, the brush can be inserted from both sides of the through-hole or from one side in two passes.

[0064] Next, a coating layer is formed on the surface of the substrate by chemical vapor deposition (CVD). First, a titanium carbonitride layer in the first layer is formed on the surface of the substrate. A first mixed gas is prepared by mixing 0.5% by volume or more and 10% by volume of titanium tetrachloride gas, 1% by volume or more and 60% by volume or less of nitrogen gas, and 0.1% by volume or more and 3.0% by volume or less of acetonitrile gas into hydrogen gas. While introducing the first mixed gas into the chamber, the acetonitrile gas is increased by 0.4% by volume per hour from the start of film formation. At this time, the first mixed gas is introduced into the chamber at a gas partial pressure of 6 kPa or more and 12 kPa or less, and a titanium carbonitride layer containing MT-titanium carbonitride is formed in a temperature range of 830°C or more and 870°C or less.

[0065] Next, the second layer 32 is formed. The film formation temperature is set to 950°C to 1100°C, the gas pressure is set to 5 kPa to 20 kPa, and the reaction gas composition is hydrogen gas mixed with 5% to 15% by volume of aluminum trichloride (AlCl₃) gas, 0.5% to 2.5% by volume of hydrogen chloride (HCl) gas, 0.5% to 5.0% by volume of carbon dioxide gas, and 0% to 1% by volume of hydrogen sulfide (H₂S) gas to create a second mixed gas. The second mixed gas is introduced into the chamber to form the second layer 32. This produces the coated tool 1 of the present disclosure.

[0066] Furthermore, after firing, a binder phase-rich layer may exist in regions other than the through-holes, such as the first surface, the second surface, and the third surface. However, the binder phase-rich layer may be removed as needed.

[0067] <Cutting Tools>

[0068] Next, the cutting tool of the present disclosure will be described using the drawings.

[0069] like Figure 7 As shown, the cutting tool 101 of the present disclosure is, for example, Figure 7 The upper end of the middle) to the second end ( Figure 7 The rod-shaped body extends from the lower end of the Figure 7 As shown, the cutting tool 101 includes: a holder 105 having a pocket 103 on a first end side (front end side); and the above-mentioned coated tool 1 positioned in the pocket 103 .

[0070] In addition, if Figure 8 As shown in FIG. 1 , the through hole 15 (refer to FIG. Figure 1 ) is inserted into the holder 107. Figure 8 In the example shown, the fixing member 107 is connected to the adhesive phase-rich layer 19 (refer to FIG. Figure 2 ) in direct or indirect contact. In addition, the so-called indirect contact between the fixture 107 and the bonding phase rich layer 19 refers to the state in which a metal layer and a coating layer exist between the bonding phase rich layer 19 and the fixture 107. The bonding phase rich layer 19 that the fixture 107 contacts is easier to deform than the base body 3, so it is difficult to apply a strong force locally to the coated tool 1. In addition, if there is a bonding phase rich layer 19, the contact area between the fixture 107 and the bonding phase rich layer 19 is large, so it is difficult for the coated tool 1 to move in the pocket during cutting. Such effects interact with each other, and the coated tool 1 disclosed in the present invention is not easily damaged abnormally. The cutting tool 101 is equipped with the coated tool 1, so that stable cutting processing can be performed for a long time.

[0071] The pocket 103 is a portion where the coated tool 1 is mounted, and has a seating surface parallel to the lower surface of the holder 105 and a restraining side surface inclined relative to the seating surface.

[0072] The coated tool 1 is placed in the pocket 103. In this case, the lower surface of the coated tool 1 may be in direct contact with the pocket 103, or a sheet (not shown) may be interposed between the coated tool 1 and the pocket 103.

[0073] The coated tool 1 is mounted on the holder 105 so that at least a portion of the portion serving as the cutting edge 11 at the ridgeline where the rake face and the flank face intersect protrudes outward from the holder 105. In this embodiment, the coated tool 1 is mounted on the holder 105 via a holder 107. Specifically, the holder 107 is inserted into the through-hole 15 of the coated tool 1, and the tip of the holder 107 is inserted into a threaded hole (not shown) formed in the pocket 103, whereupon the threaded portions are screwed together, thereby mounting the coated tool 1 on the holder 105.

[0074] As a material of the bracket 105, steel, cast iron, etc. can be used, for example. Among these members, steel with high toughness can be used.

[0075] In this embodiment, a cutting tool 101 used in so-called turning is illustrated. Examples of turning include inner diameter machining, outer diameter machining, grooving, and end surface machining. Furthermore, the cutting tool 101 is not limited to those used in turning. For example, the coated tool 1 of the above-described embodiment can also be used in a cutting tool 101 used in turning.

[0076] Example

[0077] The coated tool of the present disclosure will be described below.

[0078] The substrate is prepared as follows. After adding a binder to a raw material powder containing 40% by mass of TiCN, 12% by mass of TiN, 20% by mass of WC, 8% by mass of NbC, 20% by mass of Co, and other unavoidable carbides, the powder is pressed into the desired shape to produce a molded body in the shape of a tool with a through hole. These raw material powders are generally used in the manufacture of metal ceramics. The composition of the substrate disclosed in the present invention is not a special composition. After that, after removing the binder component, the substrate is fired under the conditions of a nitrogen environment of 3kPa and a temperature of 1530°C for 1 hour to obtain a substrate having a bonding phase-rich layer with a metal layer on the inner wall of the through hole. Thereafter, a coating layer is formed on the substrate based on the aforementioned coating layer forming process.

[0079] Thereafter, the inner wall of the through hole was polished with a brush to produce a coated tool having the structure shown in Table 1. The brush polishing time was extended for portions where there was no binder phase-rich layer or where the binder phase-rich layer was thin.

[0080] [Table 1]

[0081] (Table 1)

[0082]

[0083] In addition, the first, second, and third surfaces of any coated tool were sandblasted to remove the binder phase-rich layer.

[0084] A polishing liquid containing a mixture of 0.1 to 3 μm diamond powder and lubricating oil is applied to a bristle brush, and the brush is inserted into the through-hole while being rotated to perform brush polishing.

[0085] The thickness at the center and end portions of the binder phase-rich layer, and the diameter R1 at the center and R2 at the end portions were measured on a cross section of the substrate cut along a plane including the through-axis in the thickness direction.

[0086] Furthermore, the hardness of the interior of the substrate and the hardness of the binder phase-rich layer were measured using a cross section of the coated tool. As a result, the hardness of the binder phase-rich layer was lower than the hardness of the interior of the substrate.

[0087] The obtained coated tool was placed in the pocket of the holder, and a fixture was inserted into the through hole of the coated tool to secure the coated tool with the fixture. A cutting test was then conducted under the following conditions.

[0088] <Defect Resistance Test>

[0089] Workpiece: SCM435 with 4 grooves (5mm width)

[0090] Cutting speed: 300m / min

[0091] Feed: 0.3mm / rev

[0092] Cutting: 0.5mm

[0093] Cutting state: wet

[0094] Evaluation method: The presence or absence of cracks or chips after 10,000 impacts were applied was determined.

[0095] In addition, the orientation coefficient Tc(220) of titanium carbonitride in the first layer of all samples in Table 1, as determined by X-ray diffraction analysis, was 3.5. Samples No. 1, 2, and 9, which did not have the coated tool structure disclosed herein, exhibited abnormal damage. The coated tool disclosed herein suppressed abnormal damage. Furthermore, the coated tool was well retained in the holder, and the surface roughness of the processed workpiece was also good.

[0096] The coated tool and the cutting tool including the coated tool of the present disclosure described above are merely examples, and may have different structures without departing from the gist of the present application.

[0097] Explanation of symbols

[0098] 1…covered tool

[0099] 3…Matrix

[0100] 5…Page 1

[0101] 7…Page 2

[0102] 9…Page 3

[0103] 11…Cutting edge

[0104] 15…Through hole

[0105] 17…Inner wall

[0106] 17a··Central

[0107] 17b··End

[0108] 19…Binder phase-rich layer

[0109] 21…Expanded diameter

[0110] T1…Thickness of the binder phase-rich layer at the center

[0111] T2…thickness of the binder phase-rich layer at the end

[0112] R1…diameter at the center

[0113] R2…diameter at the end

[0114] 101…Cutting Tools

[0115] 103…pocket hole

[0116] 105…Stand

[0117] 107…fixator.

Claims

1. A coated tool comprising: a base body of a cermet containing hard particles and a binder phase; and a coating layer located on the base body, The coated tool has: Page 1; Page 2; a cutting edge located on at least a portion of the ridgeline of the first surface and the second surface; a third surface located on the opposite side of the first surface; and A through hole extending from the first surface to the third surface, The inner wall constituting the through hole has a binder phase-rich layer containing hard particles and a binder phase at least in the central portion, wherein the binder phase content is higher than that in the interior of the matrix. The thickness T1 of the binding phase-rich layer at the central portion is thicker than the thickness T2 of the binding phase-rich layer at the end portion of the inner wall. The interior of the substrate is a portion that is 500 μm or more away from the surface of the substrate. The central portion is the middle when the through hole is divided into nine equal parts in the depth direction. The end portion is an end portion when the through hole is divided into nine equal parts in the depth direction. The coating layer is at least located on the binder phase-rich layer, The coating layer includes a first layer containing cubic titanium carbonitride. The orientation coefficient Tc(220) of the titanium carbonitride of the first layer based on X-ray diffraction analysis is 3.0 or more.

2. The coated tool according to claim 1, wherein The thickness T1 is not less than 1 μm and not more than 20 μm.

3. The coated tool according to claim 1 or 2, wherein: The thickness T2 is not less than 0.2 μm and not more than 6 μm.

4. The coated tool according to claim 1 or 2, wherein: The diameter R1 at the center portion is larger than the diameter R2 at the end portions.

5. The coated tool according to claim 4, wherein The diameter R1 is greater than the diameter R2 by 5 μm or more and 30 μm or less.

6. The coated tool according to claim 1 or 2, wherein: The hardness of the binder phase-rich layer in the central portion is greater than or equal to 10 GPa and less than or equal to 20 GPa.

7. The coated tool according to claim 1 or 2, wherein: The binder phase-rich layer in the central portion includes a metal layer having a higher binder phase content than that of the binder phase-rich layer on the through-axis side of the through-hole.

8. The coated tool according to claim 1 or 2, wherein: The coating layer has a portion having a higher hardness than the binder phase-rich layer.

9. A cutting tool comprising: The bracket has a length extending from the first end to the second end and has a pocket located on the side of the first end; The covered tool according to any one of claims 1 to 8 located in the pocket; and The holder is inserted into the through hole of the coated tool.

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