WO2005011902A1 - ダイヤモンド膜被覆工具およびその製造方法 - Google Patents
ダイヤモンド膜被覆工具およびその製造方法 Download PDFInfo
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- WO2005011902A1 WO2005011902A1 PCT/JP2003/014401 JP0314401W WO2005011902A1 WO 2005011902 A1 WO2005011902 A1 WO 2005011902A1 JP 0314401 W JP0314401 W JP 0314401W WO 2005011902 A1 WO2005011902 A1 WO 2005011902A1
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- Prior art keywords
- diamond
- diamond film
- film
- base material
- coated tool
- Prior art date
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Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23B—TURNING; BORING
- B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
- B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
- C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
- C23C16/26—Deposition of carbon only
- C23C16/27—Diamond only
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23B—TURNING; BORING
- B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
- B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
- B23B27/18—Cutting tools of which the bits or tips or cutting inserts are of special material with cutting bits or tips or cutting inserts rigidly mounted, e.g. by brazing
- B23B27/20—Cutting tools of which the bits or tips or cutting inserts are of special material with cutting bits or tips or cutting inserts rigidly mounted, e.g. by brazing with diamond bits or cutting inserts
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23G—THREAD CUTTING; WORKING OF SCREWS, BOLT HEADS, OR NUTS, IN CONJUNCTION THEREWITH
- B23G5/00—Thread-cutting tools; Die-heads
- B23G5/02—Thread-cutting tools; Die-heads without means for adjustment
- B23G5/06—Taps
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
- C23C16/02—Pretreatment of the material to be coated
- C23C16/0209—Pretreatment of the material to be coated by heating
- C23C16/0218—Pretreatment of the material to be coated by heating in a reactive atmosphere
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23G—THREAD CUTTING; WORKING OF SCREWS, BOLT HEADS, OR NUTS, IN CONJUNCTION THEREWITH
- B23G2200/00—Details of threading tools
- B23G2200/26—Coatings of tools
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23G—THREAD CUTTING; WORKING OF SCREWS, BOLT HEADS, OR NUTS, IN CONJUNCTION THEREWITH
- B23G2225/00—Materials of threading tools, workpieces or other structural elements
- B23G2225/08—Cermets
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23G—THREAD CUTTING; WORKING OF SCREWS, BOLT HEADS, OR NUTS, IN CONJUNCTION THEREWITH
- B23G2225/00—Materials of threading tools, workpieces or other structural elements
- B23G2225/16—Diamond
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23G—THREAD CUTTING; WORKING OF SCREWS, BOLT HEADS, OR NUTS, IN CONJUNCTION THEREWITH
- B23G2225/00—Materials of threading tools, workpieces or other structural elements
- B23G2225/28—Hard metal, i.e. cemented carbides
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/30—Self-sustaining carbon mass or layer with impregnant or other layer
Definitions
- the present invention relates to a diamond film-coated tool used for a cutting tool, a wear-resistant tool, a welding-resistant tool, and the like, and a method for producing the same. More specifically, the tool of the present invention can be used in fields such as aluminum alloys and magnesium alloys, which are difficult to machine and require a small surface roughness, and for sharpening of cutting edges such as drilling holes in glass epoxy resin. It is used in the field where pod welding resistance is required, in the field of semi-dry cutting, or in the field of bending or cutting the outer leads of semiconductor manufacturing equipment as a tool for IC / LSI package processing. Background art
- a cemented carbide base material such as silicon nitride or silicon carbide as a base material and that are coated with a diamond film to improve wear resistance and welding resistance.
- these diamond films are coated by a chemical vapor deposition method or the like, and the crystal grain diameter of the diamond constituting the diamond film is larger than about 4 / m.
- Fig. 3 shows the state of crystal growth during such a conventional diamond film coating process.
- this method for example, when the substrate 5 is set in a CVD apparatus and set to a predetermined condition, a diamond nucleus 1 is generated on the surface of the substrate 5 as shown in FIG. Then, when the nucleus 1 is grown with the setting conditions changed, the nucleus 1 grows mainly in the direction perpendicular to the surface of the base material 5 to become crystal grains 2 as shown in FIG. Each other Are bonded to form a diamond film 6.
- the crystal grain size of diamond is large as described above, sharp V-shaped irregularities on the order of microns are formed on the surface of the diamond film 6, and the surface is not glossy. Further, when used for a cutting tool or the like, the above-mentioned unevenness is the surface roughness of the tool, and a part of the unevenness is transferred to the workpiece, so that the processed surface roughness is also deteriorated. In addition, the unevenness firmly holds the chips and causes welding, resulting in a problem of reduced tool performance.
- Patent Document 1 Japanese Unexamined Patent Application Publication No. 2002-79406, pages 2, 4 to 7 proposes a diamond film-coated tool in which the crystal grain size on the surface of the diamond film is 2 ⁇ m or less.
- FIG. 4 shows the growth state of the diamond in this manufacturing method.
- a diamond nucleus 1 is generated on a substrate 5 as shown in FIG. 4 (a), and this nucleus 1 is grown as shown in FIG. Stop growth when reaches 1 m.
- the conditions for generating nuclei 1 are set again, and diamond nuclei 1 are generated on the grown diamond crystal particles 2.
- the nuclei 1 are grown, and diamond crystal particles 2 are further formed on the first diamond crystal particles 2. Also in this case, the grain size W became 1 m. Stop growth at the point.
- the present invention provides a diamond film-coated tool that has good bite to a workpiece, can efficiently supply a cutting fluid to a processing portion even in semi-dry cutting, and has excellent processing accuracy and tool life. And a method for producing the same.
- the present inventors When coating the substrate with a diamond film, the present inventors Diamond aggregates were formed under the conditions, and these were grown to form diamond films with excellent characteristics. In other words, a diamond film with a small diamond crystal grain size, a thin diamond film, a smooth coating film surface, good cutting edge biting during machining, and easy retention of cutting fluid in semi-dry cutting. The inventors have found that a film-coated tool can be obtained.
- a first feature of the diamond film-coated tool of the present invention is a diamond film-coated tool in which a diamond film is coated on the surface of a substrate, wherein the substrate is a cemented carbide or cermet,
- the average diameter of the diamond crystal grains constituting the growth surface is 1.5111 or less
- the thickness of the diamond film is ⁇ . ⁇ . Or more and 20m or less
- the average surface roughness R of the diamond film is The point is that a is not less than 0.01 im and not more than 0.2 ⁇ m.
- the growth surface is typically the surface as obtained when the diamond film was synthesized by vapor phase synthesis.
- it includes the surface of the film obtained by polishing the surface as obtained during the vapor phase synthesis.
- the polishing is performed to such an extent that the irregularities of the diamond crystal particles remain.
- the average particle size is a value obtained by observing the surface with a scanning electron microscope (SEM).
- the cemented carbide or cermet of the base material has high hardness and strength, and if a film is formed on the base material under appropriate conditions, it becomes a very excellent cutting tool.
- the cemented carbide is a sintered body in which the hard phase is mainly made of tungsten carbide and the binder phase is made of an iron group metal such as cobalt, and the term "cermet" means that the hard phase is made of titanium carbide in addition to titanium carbide. It is a sintered body composed of at least one of tungsten carbide and a binder phase composed of an iron group metal such as cobalt-nickel.
- the surface of the substrate on which diamond is coated preferably has an appropriately rough surface. The surface state of the substrate appears on the surface of the diamond coating film, This is because the bite to the work material is improved. Such moderately rough surfaces are obtained by grinding rather than polishing the substrate.
- the average diameter of the diamond crystal particles is as follows. By forming a diamond film with such fine crystal grains, a smooth diamond film surface can be obtained.
- the thickness of the diamond film is between 0.1 m and 20 m.
- the thickness of 0.1 m or more is the thickness required for the diamond film to maintain the strength as a cutting tool and a wear-resistant tool.
- the reason for setting the thickness to 20 m or less is that if the film thickness is larger than this, the residual stress in the film increases, and the diamond film is easily peeled from the cemented carbide or cermet as the base material. It is more desirable that the length is 3 mm or more and 12 m or less.
- the average surface roughness Ra of the diamond film is set to 0.01 m or more and 0.2111 or less. Below this lower limit, the diamond film will be too smooth and the cutting fluid will not be sufficiently retained in the working area of the tool. Conversely, exceeding the upper limit results in an increase in cutting resistance and a decrease in welding resistance.
- the more preferable average surface roughness Ra is not less than 0.05 ⁇ and not more than 0.15 m.
- a second feature of the diamond film-coated tool of the present invention is that, in the cross section of the diamond film, fine diamonds are arranged long and narrow in the growth direction of the diamond film, and the minor axis is not less than 0.1 l ⁇ m. is there.
- the diamond crystal particles are formed by assembling fine diamonds.
- the reason why the fine diamond is elongated in the present invention is that the growth is stopped when the length of the fine diamond is less than about 1 m, and the process of growing a new elongated fine diamond is repeated thereafter.
- the minor axis size is also Is limited to Such a state can be observed by polishing and etching the cross section as described later.
- fine diamonds are used as primary particles, and they are collected to form diamond particles as secondary particles. Furthermore, these diamond crystal particles gather to form an aggregate that is a tertiary particle.
- a third feature of the present invention is that the aspect ratio of the elongated fine diamond is 2 or more and 20 or less.
- a more desirable range of the aspect ratio which is the value obtained by dividing the major axis of the fine diamond by the minor axis, is approximately 2 or more and 10 or less. If the aspect ratio is too large, the hardness of the fine diamond decreases, and the diamond is easily worn.
- a fourth feature of the present invention is that at least a part of the elongated fine diamond is formed in a cedar leaf shape. The reason for this has not been elucidated yet, but is presumed to be due to the formation of twins by fine diamond.
- a fifth characteristic of the present invention is that the relationship between the diamond peak height D obtained by Raman spectroscopic analysis of the diamond film and the graphite or amorphous carbon peak height G has a specific relationship. It is. Specifically, the value of D / G is 5 or less and 0.5 or more. In this region, the diameter of the diamond crystal does not increase, and the film can be formed while keeping the size small.
- the peak D appearing in the vicinity of 1 333Cm- 1 in Raman spectroscopy is a peak due to the SP 3 hybridized orbital of diamond, a peak G appearing in the range of 1 550 soil 1 50 cm- 1 is a graph eye Toya This is a peak due to SP 2 hybrid orbitals in amorphous carbon. Therefore, the higher the value of D / G, the more complete the diamond film.
- a sixth aspect of the present invention the peak intensity of da Iyamondo crystal surface when the diamond film was measured X-ray diffraction (220) I 2 2. And diamond crystal face The ratio of the peak intensities of (111), (220), (311), (400) and (331) to the total I t I 22 . ZI Z was set to 0.6 or more. The fact that the growth surface of the diamond film has the above-mentioned orientation is a preferable feature in the crystal orientation of the diamond film obtained by the present invention.
- a seventh feature of the present invention is that the diamond film has a hydrogen content of 1% or more and 5% or less in atomic ratio.
- the content is 1 at% or more, the modulus of elasticity of the diamond film is reduced and cracks are less likely to occur, so that peeling of the diamond film is prevented.
- the reason for setting the content to 5 at% or less is that if the content is more than 5 at%, the hardness of the diamond film becomes low, so that the performance as a diamond film-coated tool is not obtained.
- the diamond film of the present invention contains a large amount of hydrogen and also has a diamond crystal structure, so that a diamond peak exists in XRD (X-ray diffraction) analysis.
- the hydrogen content in the diamond film can be measured by infrared absorption spectroscopy when it is coated on a single element substrate such as a Si substrate, but when it is coated on a multi-element substrate such as a cemented carbide.
- the hydrogen content in a diamond film coated on a carbide substrate is accurately measured by combining hydrogen forward scattering analysis (HFS) and rutherford backscattering analysis (RBS). It is carried out.
- HFS hydrogen forward scattering analysis
- RBS rutherford backscattering analysis
- An eighth feature of the present invention resides in that in the cross-sectional structure of the diamond film, a single-layer coating film covers up to 70% of the film thickness from the substrate.
- the present invention Since the film growth rate of a diamond film is usually different due to slight differences in conditions, when the film thickness exceeds about 70% of the expected value, the film thickness is temporarily stopped and the film thickness is measured. In addition, the thickness of the additional film is determined, and the additional film is often formed under the same conditions as the previous film formation. In that case, the boundary surface is formed in the film at the position where the film formation is stopped, so that the boundary surface is formed as many times as stopped halfway. Therefore, a single layer is formed from the substrate to at least 70% of the film thickness. The range exceeding 70% may be a single layer or multiple layers.
- a ninth feature of the present invention is that a cemented carbide containing 0.1% by mass or more and 6% by mass or less of Co is used as a base material. Since Co has an adverse effect on diamond film formation, a smaller amount is desirably set to 6% by mass or less, and the lower limit is set to 0.1% by mass, which is the lower limit at which cemented carbide can be industrially manufactured. When part of Co is replaced with Cr or V and sintered, the crystal growth of the hard phase, tantalum carbide, is suppressed, and a high-strength cemented carbide having a fine hard phase can be obtained.
- a tenth feature of the present invention is that the value of the saturation magnetization of the base material is not less than U 900 X (the ratio of the binder phase in the alloy (% by mass)) / 100 ⁇ (G-cm 3 / g) and ⁇ 20 ⁇ ( The ratio of the binder phase in the alloy (% by mass)) / 100 ⁇ (G ⁇ cm 3 / g) or less.
- the saturation magnetization of Co in cemented carbide is between 1600 and 2023 (G ⁇ cm 3 / g). However, in the present invention, it is desirable to be between 1900 and 2023 (G-cm 3 / g).
- Saturation magnetization is the intensity of magnetization at magnetic saturation, and is equal to the intensity of spontaneous magnetization in ferromagnetic materials such as Co.
- the value of the saturation magnetization depends on the amount of Co in the cemented carbide, the solid solution material in Co, and the amount of carbon in the alloy. As the amount of carbon in the alloy increases, the amount of W dissolved in Co decreases as it precipitates as WC, and the saturation magnetization of Co increases. Therefore, the value of the saturation magnetization of the cemented carbide is If it is smaller than the limit, the amount of carbon in the cemented carbide will be insufficient, and the density of diamond nuclei on the substrate during film formation will decrease. If the upper limit is exceeded, free carbon will precipitate in the cemented carbide and the strength will decrease. In the present invention, it is considered that diamond is applied to a base material, which becomes a seed, and a nucleus is generated on the seed. Since the diamond to be applied is very small, it is preferable to secure an appropriate amount of carburization so that the diamond becomes carbon and does not diffuse into the cemented carbide.
- the eleventh feature of the present invention is that the saturation magnetization value of a substrate in which a part of Co is replaced by Cr is U 900 X (ratio of binder phase in alloy (mass%)) / 100 ⁇ X 0.93 (G'cm 3 / g) or more and ⁇ 2023 X (ratio of binder phase in alloy (mass%)) no 100 ⁇ (G ⁇ cm 3 / g). This is because when the binder phase of the cemented carbide contains Cr, the value of the saturation magnetization decreases by about 7%.
- a twenty-second feature of the present invention is that the diamond film is partially coated on the surface of the base material, and the value of the saturation magnetism in the base material at a portion separated from the outer edge of the diamond film by 5 mm or more along the base material surface is as follows. Meet requirement A.
- the film Carburization may be performed by heating the lament, or carburizing may be performed by using a heating device other than the filament and heating to a point at least 5 mm away from the surface to be coated.
- a thirteenth feature of the present invention is that a part of Co of the base material is replaced by Cr, the diamond film is partially coated on the base material surface, and 5 mm from the outer edge of the diamond film along the base material surface.
- the value of the saturation magnetization of the base material at the above-mentioned separated portion satisfies the following requirement B.
- This configuration stipulates the value of the saturation magnetization when a part of Co of the substrate is replaced by Cr. Also in this case, peeling of the diamond film can be suppressed by limiting the value of the saturation magnetization by carburizing at least a portion at least 5 mm away from the diamond-coated portion.
- a fifteenth feature of the present invention is that the surface of the diamond film has an RMS (root mean square) of 15 nm or more and 200 nm or less as measured by an atomic force microscope.
- RM S root-mean-square average
- RMS the RMS of the irregularities obtained by measuring the diamond surface with an atomic force microscope.
- a fifteenth feature of the present invention is that a composition having a composition in which the amount of the binder phase near the surface of the base material is smaller than the amount of the binder phase inside the substrate,
- the depth of the minute should be between 1 im and 20 zm.
- the bonding phase here refers to iron group metals such as Co and Ni.
- the diamond has a small crystal grain size and has a large cutting fluid holding force even in semi-dry cutting, so that the cutting resistance is extremely low. Therefore, if a phase having a small amount of binder phase is formed up to a depth of 20 i iii from the surface, tool breakage does not occur, and the amount of binder phase metal that causes a decrease in film adhesion on the substrate surface is greatly reduced. As a result, the adhesion of the diamond film is greatly improved.
- the ratio of the binder phase metal on the surface of the substrate is preferably less than 6% by mass.
- the binder phase on the substrate surface may be zero.
- the layer having a low ratio of the binder phase metal can be observed by polishing a cross section of the coated substrate and performing a line analysis on the binder phase metal with EDX-SEM.
- a sixteenth feature of the present invention resides in that the diamond film is a diamond film that has been synthesized in a vapor phase.
- the diamond film of the present invention can be used as it is. With a conventional cutting tool coated with a coarse-grained diamond film, the roughness of the diamond film is large and the cutting surface deteriorates. It could not be used in applications where welding was severe such as semi-dry cutting. However, in the present invention, since the growth surface is smooth, it can be used as a cutting tool as it is. If the surface is too smooth, the tool will not bite into the work material, so if the diamond film is coated on the surface with the grinding marks by grinding instead of polishing the base material, The surface roughness affects the surface shape of the coating film, and the bite is improved.
- a first feature of the method for producing a diamond film-coated tool of the present invention is a method for producing a diamond film-coated tool in which a diamond film is coated on the surface of a substrate, wherein the cemented carbide has a tool shape as the substrate.
- prepare a cermet carburize the base material, and coat the base material with a diamond film in a mixed gas of hydrogen and hydrocarbons at a pressure of 0.13 to 6.5 kPa. It is in.
- a cemented carbide or cermet is used as the base material.
- the binder phase metal is, for example, cobalt-nickel as described above.
- a polycrystalline diamond aggregate can be formed at a high density by subjecting the above-described base material to heat treatment and carburizing, growing diamond crystals under specific conditions and coating the diamond film.
- Carburizing is performed in a mixed gas atmosphere of 1 to 99% by volume of methane and hydrogen, at a pressure of 0.65 to 13.3 kPa, at a temperature of 800 to 11 O Ot, and for 3 to 9 hours. Desirable.
- the diamond film is formed in a mixed gas atmosphere of 1 to 5% by volume of methane and hydrogen at a pressure of 0.13 to 6.5 kPa and a filament temperature of 1800 to 2200 ° C. It is desirable to coat the diamond film at a substrate temperature of ⁇ 900 ° C.
- the formation of the diamond film is most preferably a thermal filament CVD method or a microwave plasma CVD method from the viewpoint of production.
- the Kokodei cormorants hard phase particles refers WC, Ta bC, a hard quality carbides such as V Cr 3 C 2, Ti Mo 2 C.
- a second feature of the production method of the present invention is that diamond having an average particle diameter of 500 A (500 nm) or less is applied to the surface of the substrate after carburizing. By doing so, the nucleation density can be further improved, and a diamond film having a small diamond crystal grain size can be easily obtained.
- the reason why the average particle size is less than 500 A (50 nm) is that if the average particle size is larger than this, the aggregate may become too large when grown.
- a third feature of the production method of the present invention is that the diamond to be applied is a polycrystalline diamond.
- the diamond to be applied becomes the nucleus for diamond growth, but if the nucleus is polycrystalline, the diamond to be formed is also likely to be polycrystalline.To obtain fine diamond crystals, apply polycrystalline diamond rather than single crystal It is desirable. It is easier to obtain polycrystalline diamond aggregates if the nuclei before growth are polycrystalline diamond. This is because
- diamond is applied by ultrasonic waves. This is because diamond can be applied to the substrate firmly and with high density.
- a fourth feature of the production method of the present invention is that between the carburizing treatment and the diamond coating, the base material surface is subjected to an acid treatment to remove a part of the binder phase metal.
- the acid treatment By performing the acid treatment, the binder phase metal on the surface of the substrate is reduced, and the adhesion between the diamond film and the substrate is improved.
- a particularly desirable method of manufacturing the diamond-coated tool of the present invention is to combine the above-described partial removal of the binder phase metal with the application of diamond.
- the surface of the substrate is carburized, the surface of the substrate is acid-treated to remove part of the binder phase metal, diamond powder is applied to the surface of the substrate, and the substrate is set in a thermal filament CVD apparatus. Then, a diamond aggregate is formed to form a diamond film by forming a diamond film, and the diamond film is used without polishing.
- the adhesion of the diamond film to the substrate can be increased.
- by applying diamond powder to the substrate surface as a pretreatment for film formation it is possible to improve the nucleation density of diamond during film formation.
- the diamond film-coated tool of the present invention it is difficult to adhere to the diamond film surface, and it is possible to obtain a good surface roughness.
- the diamond film does not easily peel off from the base material, so that a long-life tool can be obtained.
- the method for producing a diamond film-coated tool of the present invention it is possible to suppress the growth of diamond nuclei to obtain a diamond film having a small crystal grain size, and to perform a diamond film-coated tool with high precision. Can be easily manufactured. Of tap When such a tool is applied with the diamond film of the present invention, a tool with less welding can be obtained.
- FIG. 1 is a conceptual cross-sectional view of the vicinity of the surface in the diamond film-coated tool of the present invention.
- FIG. 2 is a schematic explanatory view showing the growth state of diamond in the manufacturing method of the present invention, and (a) to (d) show the process.
- FIG. 3 is a schematic explanatory view showing a growth state of diamond in a conventional manufacturing method, and (a) to (b) show the process.
- FIG. 4 is a schematic explanatory view showing a diamond growth state in another conventional manufacturing method, and (a) to (d) show the process.
- FIG. 5 (a) is an AFM micrograph showing the surface state of the diamond film of the present invention
- FIG. 5 (b) is an AFM micrograph showing the surface state of another diamond film of the present invention.
- FIG. 6 (c) is an AFM micrograph showing the surface state of the diamond film of the comparative example
- FIG. 6 (d) is a SEM micrograph showing the surface state of the diamond film of the present invention
- FIGS. 7 (a) and 7 (b) are micrographs each showing a cross section of the diamond film obtained by the present invention.
- FIG. 8 is a micrograph showing a cross section of the diamond film of the comparative example.
- FIG. 9 is a graph showing the results of Raman spectroscopic analysis of the diamond film obtained in the present invention.
- FIG. 10 is a graph showing the results of Raman spectroscopic analysis of the diamond film obtained by the present invention.
- FIGS. 12 (a), (b) and (c) are cross-sectional views showing operations in a machining process using an IC or LSI package machining tool.
- FIG. 3 is a conceptual cross-sectional view of the vicinity of the surface in the diamond film-coated tool of the present invention.
- FIG. 2 schematically shows a state of forming a diamond film in the present invention
- FIGS. 3 and 4 show conventional examples of a state of forming a film.
- Figures 5 and 6 are surface micrographs of the diamond film.
- Figures 5 (a) and (b) show the results of the present invention
- Figure 6 (c) shows the conventional diamond film as AFM (atomic force microscope).
- Fig. 6 (d) shows the diamond film of the present invention observed by SEM (scanning electron microscope).
- FIGS. 7 (a) and 7 (b) are micrographs obtained by etching a polished cross section of the diamond film obtained by the present invention with hydrogen plasma and observing it with SEM.
- FIG. 8 is a micrograph of a cross section of a conventional fine-grained diamond film similarly etched and observed by SEM.
- FIG. 9 and FIG. 10 are drawings of Raman spectroscopic analysis of the diamond film obtained by the present invention.
- FIG. 11 (a) is a front view of the tap
- FIGS. 11 (b) and (c) are cross-sectional views of the tap obtained by the present invention.
- FIGS. 12 (a), (b) and (c) are cross-sectional views showing processing steps using tools for processing IC and LSI packages.
- FIG. 1 shows a conceptual diagram of the vicinity of the surface of the diamond film-coated tool of the present invention.
- this tool uses a cemented carbide cermet or the like as a base material 5, and a diamond film 6 is formed on the surface of the base material 5.
- the diamond film 6 is formed by a large number of diamond crystal particles 2 gathering to form an aggregate 3, and the aggregates are connected to each other.
- FIG. 1 shows only the crystal particles 2 present on the surface of the diamond film 6, and omits the inside of the diamond film 6.
- the crystal grain 2 itself is also composed of a large number of fine diamonds (not shown in FIGS. 1 and 2). Grooves 4 are formed at the points where the aggregates 3 are connected. The distance from the bottom is configured as the undulation h of the diamond film surface.
- a substrate 5 that has been subjected to a pretreatment such as carburizing is set in a thermal filament CVD device or the like, and the temperature, pressure, and atmosphere under predetermined conditions are set.
- a nucleus 1 of diamond is generated on the surface of the substrate 5.
- the nucleus 1 is made of single-crystal diamond or a single-crystal diamond aggregate, and is grown under the same conditions as it is to form a spherical aggregate 3 as shown in FIG. 2 (b).
- the spherical aggregate 3 is a collection of diamond crystal particles 2.
- the diamond crystal particles 2 forming the aggregate 3 grow mainly in a direction perpendicular to the surface of the substrate 5 and, simultaneously, in a direction parallel to the surface of the substrate 5 To grow. That is, the crystal grains grow radially. This growth is continued until the aggregates 3 are combined to form a diamond film 6 having a predetermined thickness, as shown in FIG. 2 (d). Finally, the average diameter of the diamond crystal particles 2 constituting the growth surface of the diamond film becomes 1.5 m or less, and a diamond film having high wear resistance can be obtained when used as a tool.
- the diamond crystal particles 2 are composed of a collection of fine diamonds (primary particles) on the order of 100 nm. It can be seen from the photograph in Fig. 7 that these crystal grains are composed of a collection of fine diamonds.
- FIGS. 7A and 7B are micrographs showing a cross section of a diamond film obtained according to the present invention. Further, the diamond crystal particles 2 are gathered to form an aggregate 3 having a diameter of several m to about 10 m, which is a tertiary particle, and the aggregates 3 are connected to each other to form a diamond film having a predetermined thickness.
- the number of aggregates 3 is considered to be proportional to the number of nucleation density, available.
- the nucleation density is low, the aggregate becomes large because the aggregate 3 grows until the growth is inhibited by the adjacent aggregate.
- the aggregates 3 become smaller, and the number of diamond crystal particles 2 constituting one aggregate 3 also decreases as described later. Further, the groove 4 generated between the aggregates 3 becomes shallow, making it difficult to identify the aggregates.
- the average diameter of the diamond crystal particles 2 constituting the growth surface of the diamond film is as fine as 1.5 m or less.
- FIGS. 5 (a), 5 (b) and 6 (c) are micrographs showing the irregularities on the surface of the diamond taken by an AFM (atomic force microscope).
- An AFM Atomic Force Microscope
- An AFM is an image of the surface of a sample by operating the probe while keeping the atomic force acting between the probe and the sample surface constant when the probe is brought close to the sample surface. It is a microscope that changes The AFM can measure very fine irregularities of a very fine structure that cannot be measured with a SEM, a stylus-type surface roughness meter, or an optical interference type three-dimensional surface roughness meter.
- FIGS. 5 (a) and 5 (b) show two types of diamond films obtained by the present invention.
- the white part is high, and it decreases as gray approaches black.
- Fig. 5 (a) fine particles are aggregated to form a spherical diamond aggregate. This is very similar to the state schematically shown in FIGS.
- FIG. 5 (b) shows the surface state of another diamond film obtained by the present invention.
- This photograph looks blurred as a whole, indicating that it is a smooth diamond film with almost no irregularities.
- the groove running obliquely in the center is a grinding mark formed when the substrate is ground before film formation.
- the base material is polished, the diamond film also has a mirror surface and is not bite well.
- FIG. 6 (c) is a photograph of a coarse diamond film as a comparative example.
- this comparative example as shown in Fig. 3, nuclei were generated, and the nuclei were grown as columnar crystals in the longitudinal direction and the lateral direction, and adjacent columnar crystals were connected to each other to form a diamond film. It is. Thus, well-grown angular diamond grain particles can be observed.
- the scale on the right side of the photograph expresses the difference in height by color density. By comparing the shade of the color of a specific part with that of another part, it is possible to grasp the difference in height of the relief.
- FIGS. 5 (a) and 6 (c) are obtained by observing specimens 35 and 36 produced in Example 7 described later.
- FIG. 5 (b) shows a diamond synthesized at a pressure of 1.3 kPa on a carburized ordinary cemented carbide base material of Example 1 described later.
- FIG. 6D is a SEM photograph showing the surface state of the diamond film obtained by the method of the present invention.
- diamond crystal particles having an average particle size of 1.5 m or less can be observed.
- the lower limit of the average particle size is the size of the particle size of the fine diamond that is the primary particle.
- This photograph shows a diamond film of a specimen 35 produced in Example 7 described later.
- FIGS. 7A and 7B show cross sections of a diamond film obtained according to the present invention. It is a microscope picture. In this photograph, the diamond film was cut together with the base material, the surface was polished, etched in hydrogen plasma, and observed by SEM. The general conditions of the etching are as follows: a microwave CVD apparatus is used for processing in a hydrogen atmosphere of 600 to 1000 ° C. and 0.13 to 13 kPa. 7 is etched at 870 ° (: 13 kPa for 30 minutes. FIG. 7 (a) is 1 xm from the substrate, and (b) is the substrate. Fig. 8 shows a cross section of the diamond film at a position of 6 m from Fig. 8.
- FIG. 8 shows the specimen 34 of the seventh embodiment, which will be described later.
- the diamond film of the present invention has a feature in the growth of the diamond crystal.
- a nucleus composed of a single crystal diamond or an aggregate of a plurality of single crystal diamonds is generated, and this nucleus is grown in an initial stage of film formation to form a polycrystalline diamond spherical aggregate. I have. When this is further grown, the crystal grains of polycrystalline diamond grow, so that the aggregates also grow, and the adjacent aggregates combine to form a film.
- each fine diamond grows elongated in the growth direction of the diamond film, and its major axis or length is 0.01!
- the growth stops and a new diamond begins to grow. If this state is replaced with the short diameter of the fine diamond, the growth of the fine diamond will occur if the short diameter grows from 0.01 im to 0.1 m or less. Stops and the next new fine diamond begins to grow. This indicates that fine diamonds with an aspect ratio (major axis / minor axis) of 2 to 20 have been formed.
- Such a special diamond film greatly depends on the atmospheric pressure particularly when the diamond film is formed.
- the diamond film of the present invention can be obtained in a pressure range of 0.13 to 6.5 kPa.
- the surface of the diamond film is formed by an aggregate composed of a large number of diamond crystal grains, and a thin black line that serves as a boundary between the aggregates.
- the aggregate 3 existing on the surface of the base material 5 in FIG. 1 form undulations h so as to draw gentle irregularities.
- the undulation h is in a relationship approximately proportional to the average surface roughness Ra.
- the undulation h should be 50 nm or more and 700 nm or less. Is more preferred.
- diamond having an average particle diameter of 500 A or less is applied on the substrate 5 after carburizing and before coating the diamond film 6. It is good to keep.
- the amount of application For example, it is desirable to set the number of diamonds to 2 ⁇ 10 4 Zmm 2 or more. Since the number of diamonds and the number of aggregates substantially correspond, increasing the number of aggregates makes it possible to form a diamond film by bonding with each other even if the amount of aggregate growth is small. . Thus, a thin diamond film having small diamond crystal grains can be obtained.
- the bite can be improved by using a grinding mark of the base material. This undulation h can be accurately measured by AFM.
- FIGS. 9 and 10 show typical examples of the Raman spectrum of the diamond film obtained by the present invention.
- the horizontal axis represents Raman Shift (cnr), and the vertical axis represents intensity.
- the peak height D and 1550 of the diamond at 1330 cm- 1 relative to the base line are shown.
- the height of the highest part of the graphite and amorphous carbon peaks in soil 150 cm- 1 is G, and the ratio D / G is preferably in the range of 0.5 to 5. If it is less than 0.5, the diamond bond is too small and the wear resistance is reduced, and if it is more than 5, the diamond bond is too large and the toughness of the film is reduced. , 0.78, and Fig. 10 shows that it is 1.43.Note that Fig. 9 and Fig. 10 show the test of Example 7 described later. Articles 37 and 35.
- a 5% by mass Co cemented carbide strip (10X10X1t (mm)) was manufactured as a base material.
- a film-forming experiment was performed on this.
- the substrate 5 was subjected to a carburizing treatment and an untreated substrate was prepared.
- the base material was set in a thermal filament C VD device, and 1% by volume methane-hydrogen Carburizing was performed in a mixed gas atmosphere at a pressure of 13.0 kPa and an atmosphere temperature of 900 for 6 hours.
- the saturation magnetization of the carburized substrate was 97.5 to 98.5 G ⁇ cg, whereas that of the uncarburized substrate was 80 to 83 G.cm 3 / g.
- the deposition pressure (synthesis pressure) was applied to these substrates at 1.3 kPa, 3.9 kPa, 6.5 kPa, 9.8 kPa and 13 kPa.
- a diamond film with a film thickness of 10 ⁇ m was formed for each type, and the formation of polycrystalline diamond aggregates was confirmed.
- the substrate temperature during film formation was 850 ° C. Table 1 shows the results. No diamond aggregates were formed in the case without carburizing regardless of the synthesis pressure. In the high pressure range where the diamond forming pressure was 9.8 kPa or higher, no diamond aggregates were formed even with a carburized substrate.
- the average diameter of the diamond crystal particles thus formed into the diamond aggregate was in the range of 1 to 1.5 m, and the average surface roughness was Ra 0.07 to 0.15 m. .
- a cemented carbide having a composition in which 0.5% by mass of Cr was replaced with Cr of 5% by mass was carburized under the above conditions to form a diamond film at 1.3 kPa.
- a polycrystalline diamond aggregate was formed.
- the average diameter of the diamond crystal grains was 1.3 m, and the average surface roughness was 0.1 m.
- the value of the saturation magnetization was 94 G'cm 3 / g, and a good coating film could be obtained.
- the diamond film was coated with a hot filament C VD device at a hydrogen flow rate of 170 sccm, a methane flow rate of 45 sccm, a pressure of 3.9 kPa, a filament temperature of 2120 ° C, and a substrate temperature of 7600. ° C.
- the hydrogen content was adjusted to 1.5 at% (atomic%), and the nucleation density was changed by changing the amount of diamond applied to the substrate.
- six types of end mills having diamond films with different diameters of diamond crystal grains and different undulations h were manufactured, and a high-silicon aluminum alloy (A 1-12 mass% S i) A cutting test was performed.
- the cutting conditions were as follows. Cutting speed (V): 400 m / min
- Cutting fluid water-soluble emulsion
- Table 2 shows the results of the cutting test performed under the above conditions.
- the average surface roughness is in the range of 0.01 to 0.2 / ⁇
- the undulation h is in the range of 50 to 900 nm
- the processed surface roughness is excellent.
- the average surface roughness was as small as 0.05 m, and if the undulation h was too small, chatter occurred during processing and the processed surface roughness was reduced.
- the machined surface roughness was reduced due to the large unevenness on the tool surface.
- the sample 4 was taken out from the film forming apparatus before being formed into a film, and the number of diamond aggregates was counted. As a result, the number was 5 ⁇ 10 4 Zmm 2 . This number coincided with the number of diamond aggregates after film formation within an error range. (Example 3)
- an end mill with a diameter of 8 mm was manufactured and its performance was evaluated.
- a cemented carbide of 5 mass% Co was used as a base material.
- the cemented carbide was set in a thermal filament C VD device, and a pressure of 13.0 kPa was applied in a 1 vol% methane-hydrogen mixed gas atmosphere.
- Carburizing was performed at a treatment temperature of 900 ° C. for 6 hours. Thereafter, a diamond film was formed to have a film thickness of 20 im.
- the diamond aggregate formed a diamond film, and the average diameter of the diamond crystal grains was all 0.7 to 1.
- the coating of the diamond film 6 was performed using a thermal filament C VD device, with a hydrogen flow of 170 sccm, a methane flow of 45 sccm, a pressure of 3.9 kPa, a filament temperature of 212 ° C, and a substrate. The test was performed at a temperature of 760 ° C. By setting the hydrogen content to 1.5 at% and changing the diamond application density, six types of end mills with diamond films with different RMS were formed, and the high silicon aluminum alloy ( A 1-12 mass% S i) cutting test was performed. The cutting conditions were the same as in Example 2, and the results are shown in Table 3.
- the RMS is 1 O nm.
- the size becomes smaller and the undulations become larger such as 300 nm, the roughness of the machined surface tends to become coarser, and the result is more preferably set to 15 to 20 O nm.
- the RMS of the diamond film is 15 to 2
- the one at 0 O nm was better.
- an end mill with a diameter of 8 mm was manufactured and its performance was evaluated.
- a cemented carbide of 5 mass% Co was used as a base material.
- the cemented carbide was set in a thermal filament C VD device, and a pressure of 13.0 kPa and a processing temperature of 1% by volume methane-hydrogen mixed gas atmosphere.
- Carburizing was performed at 900 ° C for 6 hours. The carburization was performed at least 5 mm from the outer edge of the surface to be coated along the surface. Thereafter, a film was formed so that the thickness of the diamond film became 0.
- the diamond film was coated with a hot filament C VD apparatus at a hydrogen flow rate of 170 sccm, a pressure of 3.9 kPa, a filament temperature of 212 ° C, and a substrate temperature of 760 ° C. .
- the methane flow rate was set to 90 sccm (hydrogen content: 6.0 at%), 70 sccm (hydrogen content: 5.0 at%), 40 sccm (hydrogen content: 1) 0 at%) and 20 sccm (hydrogen content: 0.2 at%).
- the diamond aggregate formed a diamond film, and the diameters of the diamond crystal grains on the growth surface were all 0.2 to 0.2.
- the average surface roughness Ra of each test sample was 0.16 to 0.18 zm, but it was difficult to unify all samples on the order of nanometers for undulation h and RMS values. Therefore, an approximation was made and used.
- the high-silicon aluminum alloy (A 1-12 quality) was formed by the end mill on which the diamond films 6 having different hydrogen contents were formed.
- a cutting test of the amount% S i) was performed. The cutting conditions were as follows. Cutting speed (V): 400 m / min
- Cutting fluid water-soluble emulsion
- Table 4 shows the results of the cutting test performed under the above conditions.
- the diamond film with a hydrogen content of 1 to 5 at% (atomic ratio%) showed excellent performance in chipping and film abrasion, while the hydrogen content was low.
- the amount is too large, chipping is likely to occur, and when the amount is too large, the wear resistance of the diamond film 6 is reduced, so that the wear is liable to progress.
- a drill with a diameter of 0.8 mm was manufactured in order to confirm the state of peeling of the diamond film and destruction of the base material due to the difference in the thickness of the layer.
- a performance evaluation was performed. Using a 5% by mass Co cemented carbide as the base material It was set in the apparatus and carburized in a 1% by volume methane-hydrogen mixed gas atmosphere at a pressure of 13.0 kPa and a treatment temperature of 900 ° C for 6 hours. This treatment carburized the diamond-coated surface up to 5 mm or more along the surface from the outer edge of the surface. Thereafter, the surface of the substrate 5 was treated with nitric acid to form a layer having a reduced amount of the binder phase.
- the diamond film was coated with a hot filament C VD device at a hydrogen flow rate of 170 sccm, a methane flow rate of 45 sccm, a pressure of 3.9 kPa, a filament temperature of 2120 ° C, and a substrate temperature of 7600. ° C.
- the diamond aggregate formed a diamond film, and the diameters of the diamond crystal grains were all 0.5 to 0.8 ain.
- the average surface roughness Ra is in the range of 0.14 to 0.15 im, and the values of undulation h and RMS are approximated because it is difficult to unify all samples on the order of nanometers.
- the hydrogen content was set to 1.5 at%. Using the five types of drills thus obtained, a hole drilling test was performed on the SiC pre-sintered body.
- Table 5 shows the results of the cutting test.
- the composition with a small amount of the binder phase is small. It was confirmed that the layer having a thickness of 20 zm or less exhibited particularly excellent performance. However, chipping due to a decrease in substrate strength was observed for the layers having a composition having a small amount of the binder phase and the thicknesses of 30 and 40 zm.
- FIG. 11 (a) is a schematic front view of the tap 11
- FIGS. 11 (b) and 11 (c) are partial cross-sectional views of one cutting edge of the tap which rotates about O.
- the tap 11 has a cutting edge 12 on a base material 14 made of a cemented carbide.
- the cutting edge portion 12 has a biting portion 12a formed at the distal end and having an incompletely shaped screw thread, and a complete threaded portion 12b formed continuously from the biting portion 12a.
- the cutting edge portion 12 is divided by a spiral or linear tool groove 13 in the circumferential direction.
- the ground cutting edge 12 is coated with the above-mentioned diamond film.
- a tap with a cutting edge composed of a rake face and a flank of a flank as shown in Fig. 11 (b)
- the ridgeline of the cutting edge was cut off, and both taps having chamfered surface ⁇ were prepared.
- the cross section of the biting portion 12a and the complete mountain portion 12b has a shape without the chamfer surface 17 (see FIG. 11 (c)) as shown in FIG. 11 (b).
- a tap coated with the diamond film of the present invention and a conventional tap coated with the conventional diamond film were manufactured, and performance evaluation was compared. Each is coated with a 10-m-thick diamond and has M3 screw holes.
- the test specimens 21 to 23 of the present invention and the test specimens 24 and 25 of the comparative examples have the four-flute front view of the tap shown in FIG. 11 (a), and a partial cross section thereof.
- the chamfered substrate 14 shown in FIG. 11 (C) was used.
- As a test sample 26 as a comparative example a substrate 14 without a chamfer having a front view and a partial cross section shown in FIG. 11B was used.
- the material of the base material 14 is a 5 mass% Co cemented carbide.
- the angle j3 of the rake face 15 was 3 ° as shown in Fig. 11 (b), and the chamfer angle ⁇ ; was-20 ° as shown in Fig. 11 (a).
- a chamfered surface 17 was formed from the tip 18 of the cutting blade to the relief 16 so as to be as short as possible.
- the chamfer surface 17 was finished to have a surface roughness Ra of 0.2 m, and the width of the chamfer surface 17 shown in FIG. 11C was set to 0.4 mm.
- the test sample 26 differs from the test samples 21 to 25 in that the angle 13 of the rake face 15 in the M3 sunset is set to ⁇ 20 ° and the chamfer face is not provided.
- Carburizing treatment was performed on these substrates 14 as pretreatment.
- the conditions were as follows.
- the base material 1 was set in a thermal filament CVD apparatus, and carburized at a pressure of 13 kPa and a processing temperature of 900 in a 10% by volume methane-hydrogen gas atmosphere for 6 hours. This carburizing was heated so that the surface to be coated with diamond could be carburized to a distance of 5 mm or more along the surface from the outer edge of the substrate surface.
- Specimen 23 is the bonding layer of cemented carbide of the base material after carburizing Co was removed by nitric acid over a depth of 20 m from the surface.
- the base materials of the test samples 21 to 26 were immersed in a solution in which ultrafine polycrystalline diamond was dispersed in an organic solvent, and ultrasonic waves were applied to apply the ultrafine diamond to the base material.
- the diamond film was formed using the hot filament CVD apparatus under the conditions shown in Table 6.
- the diamond film formed a diamond aggregate, and the particle size of the diamond crystal particles was as shown in Table 7.
- the synthesis of the test pieces 21 to 23 of the present invention and Comparative Examples 25 and 26 was interrupted when the film thickness was expected to be 9 m.
- the actual film thickness was measured. As a result, each had a thickness of 8.51 or more, and the thickness range of 70% or more with respect to 1 of the film thickness after the completed product was formed as a single layer. On the cross section of the diamond film, traces of the suspension of the growth remained.
- Test product 24 is a reproduction of Patent Document 2.
- the surface was treated by sandblasting without carburizing.
- Test sample 24 was coated with diamond using a microphone mouth wave device instead of a hot filament CVD device.
- the conditions were different between the step of attaching the diamond nucleus and the step of growing the nucleus, and the film was formed by repeating these conditions.
- the upper stage of the test product 24 in Table 6 is the condition of the process of attaching the nucleus
- the lower stage is the condition of the process of growing the nucleus. In the process of growing nuclei, the processing time was determined so that the crystal grain size was 1 m or less.
- FIG. 8 shows a photograph obtained by polishing the cross section of this sample and performing hydrogen plasma etching.
- Table 7 shows the state of the diamond film after film formation.
- the average surface roughness Ra is in the range of 0.16 to 0.18 ⁇ .
- holes formed in MMC were processed without polishing the surface, and the number of holes was set to 700.
- the evaluation items were three points: welding thickness, cutting resistance, and the number of peeled diamond films.
- the thickness of the weld was measured at one point on the rake face of the bite of the cutting blade.
- the cutting force is calculated using the Y axis (rotation) when machining from the 1st to 5th holes. Direction) The cutting force in the direction was measured and the average value was taken.
- the number of peels refers to the number of peels that appeared on one tap after the above drilling test.
- Table 7 shows the results.
- the tap coated with the diamond film of the present invention showed very little welding and little peeling of the diamond film.
- no delamination was observed in the test specimen 22 with a high hydrogen content of 1.5 at% and in the test specimen 23 with the base material surface graded by acid treatment with nitric acid after carburizing. .
- the cutting resistance is small and the bite is good due to the minute undulations on the surface.
- the specimen 24, which is a comparative example had the smoothest diamond film surface, but showed a tendency to increase cutting resistance because it was slippery and hard to bite.
- the specimens 25 and 26 in which the diamond particles composing the diamond film had a large particle diameter were welded and peeled off.
- the surface roughness of the diamond film was rough and the cutting resistance was large.
- the chamfer angle is desirably in the range from 160 ° to 15 °.
- Example 7 A cemented carbide chip having a composition of mass% Co-WC (model number SEGN 12 0 3 0 8) was manufactured. Next, the above chip was set in a thermal filament CVD system, and carburized at 6.5 kPa at a pressure of 6.5 kPa and a processing temperature of 850 ° C for 6 hours in an atmosphere of a mixed gas of 10% by volume methane and hydrogen. Processed. Then, the obtained chip was immersed in an 8% nitric acid solution so that a portion having a composition with a small amount of the binder phase was formed on the chip surface layer, and the binder phase in the cemented carbide was removed at the chip surface layer. After washing and drying well.
- ultrafine diamond was applied to the chip.
- 0.02 g of polycrystalline diamond powder having a particle size of 4 to 6 nm was dispersed in 100 cc of isopropyl alcohol.
- the chip was immersed in this solution, and ultrasonic waves were applied for 10 minutes to apply polycrystalline diamond.
- the methane concentration was set at 2% by volume
- the filament temperature was set at 250 ° C
- the substrate temperature was set at 850 ° C
- the pressure was set as shown in Table 8.
- the thickness of the diamond was 30 m for specimens 30 to 36, and 2 m for specimen 37.
- the chip was manufactured through the steps marked with circles in Table 8, and the steps without circles were omitted.
- test samples 31 to 36 were 9] 11, and the test sample 37 stopped when the film thickness was expected to reach 1.5 m and measured the actual film thickness. Was added to form a film. Traces remained on the cross section of the part where the film formation was temporarily stopped as a boundary surface. The average surface roughness Ra of the test sample was also measured. Table 8 also shows the results.
- X-ray diffraction, hardness, and average surface roughness were measured using specimen 34. X-ray diffraction intensity ratio 122 . / (1 22., The peak intensity of the diamond crystal face (220), I t is die Yamon de crystal plane (1 1 1), the (220), (311), (400) and (33 1) The sum of the peak intensities) was 0.8. The hardness was 750 kgf / mm 2 .
- the cross section of the test article 34 Figures 7 (a) and 7 (b) show this state.
- the specimen 30 had no peel strength enough to withstand practical use because it was not carburized.
- the test articles 32 and 36 had high pressure at the time of coating and had an average particle diameter of more than 1 on the surface of the diamond film, which is outside the scope of the present invention. Others have a fine average particle size of less than 1.5 m.
- a cutting test was performed using the chip manufactured as described above.
- the cutting length was set at 300 m.
- the test articles 33, 34, 35, and 37 of the present invention had a long life and the surface finish of the work material was excellent.
- the test sample 31 of the present invention although a small peeling was observed at one place on the flank surface as compared with the above-mentioned test sample, it was at a level that can be used sufficiently. (Example 8)
- a diamond was formed on a polished base material of a cemented carbide having a composition of 5.5 mass% Co-WC under the same conditions as for test samples Nos. 30 to 37 manufactured in Example 7.
- the test pieces were numbered 40 to 47.
- test sample No. 30 and test sample No. 40, and test sample No. 31 and test sample No. 41 are test samples manufactured under the same conditions, and so on.
- the tool shape is the tool for processing IC and LSI packages shown in Fig. 12.
- FIG. 12 is a cross-sectional view illustrating operations and functions in a processing step using a tool for processing an IC or an LSI package, and arrows indicate operation directions.
- outer leads Since a large number of outer leads are usually arranged at narrow intervals in a package, if the outer leads are bent at the time of cutting, the outer leads come into contact with each other or cannot be mounted, resulting in a defective product. Therefore, the bending of the outer lead must be minimized.
- FIG. 12A shows a state in which the package 30 is placed on the bending die 21.
- the outer lead 31 passes over the bending die 21 and reaches the force die 23.
- FIG. 12 (b) shows a state in which the bending cut punch 22 is lowered in the direction of the arrow and presses the artery lead against the bending die 21 to bend. At this time, the solder 32 covering the outer lead comes into strong contact with the bending die 21 and the bending 'cut punch 22', which causes solder to adhere to the tool.
- FIG. 12 (c) shows a state where an extra portion of the outer lead is cut. That is, the cutting die ⁇ rises in the direction of the arrow while the bending / punching punch 22 keeps holding the outer lead 31. As a result, an extra portion of the outer lead 31 is cut by the shear generated between the bend and the cut punch 22. Also in this process, the solder adheres to the tool.
- the present invention is applicable to a field in which a hard-cutting surface such as an aluminum alloy or a magnesium alloy is required and a small surface roughness is required, and a field in which a sharp cutting edge is required as a cutting edge such as a hole in a glass epoxy resin. Applicable. Furthermore, it can be applied to applications such as cutting of ceramics such as alumina, silicon carbide, and silicon nitride. It can also be used as a tool for adding IC and LSI packages.
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Abstract
Description
Claims
Priority Applications (6)
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AU2003280758A AU2003280758A1 (en) | 2003-07-31 | 2003-11-12 | Diamond film coated tool and process for producing the same |
US10/566,633 US7883775B2 (en) | 2003-07-31 | 2003-11-12 | Diamond film coated tool and process for producing the same |
EP03772725.2A EP1649955B1 (en) | 2003-07-31 | 2003-11-12 | Diamond film coated tool and process for producing the same |
JP2005507414A JP4420901B2 (ja) | 2003-07-31 | 2003-11-12 | ダイヤモンド膜被覆工具およびその製造方法 |
MYPI20040218A MY138872A (en) | 2003-07-31 | 2004-01-27 | Diamond coated tool and method of manufacturing the same |
HK06113139A HK1091435A1 (en) | 2003-07-31 | 2006-11-30 | Diamond film coated tool |
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Cited By (17)
Publication number | Priority date | Publication date | Assignee | Title |
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JP2006138011A (ja) * | 2004-10-14 | 2006-06-01 | Sumitomo Electric Ind Ltd | ダイヤモンド膜被覆部材およびその製造方法 |
JP2010524710A (ja) * | 2007-04-27 | 2010-07-22 | デグテック エルティーディー | コーティングされた超硬合金切削工具とその製造のための前処理及びコーティング方法 |
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JP2006138011A (ja) * | 2004-10-14 | 2006-06-01 | Sumitomo Electric Ind Ltd | ダイヤモンド膜被覆部材およびその製造方法 |
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JP2010524710A (ja) * | 2007-04-27 | 2010-07-22 | デグテック エルティーディー | コーティングされた超硬合金切削工具とその製造のための前処理及びコーティング方法 |
JP2011020179A (ja) * | 2009-07-13 | 2011-02-03 | Mitsubishi Materials Corp | 耐欠損性と耐摩耗性にすぐれたダイヤモンド被覆工具 |
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JP2012110998A (ja) * | 2010-11-25 | 2012-06-14 | Mitsubishi Materials Corp | 硬質難削材の高速高送り切削加工で硬質被覆層がすぐれた耐剥離性とすぐれた耐チッピング性を発揮する表面被覆切削工具 |
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JP2013220554A (ja) * | 2012-04-13 | 2013-10-28 | Mitsuboshi Diamond Industrial Co Ltd | スクライビングホイール及びその製造方法 |
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JP2013233793A (ja) * | 2012-04-13 | 2013-11-21 | Mitsuboshi Diamond Industrial Co Ltd | スクライビングホイール及びその製造方法 |
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US9981317B2 (en) | 2013-11-22 | 2018-05-29 | Element Six Technologies Limited | Polycrystalline chemical vapour deposited diamond tool parts and methods of fabricating, mounting, and using the same |
JP2017504548A (ja) * | 2013-11-22 | 2017-02-09 | エレメント シックス テクノロジーズ リミテッド | 多結晶化学蒸着ダイヤモンド工具部品ならびにそれを製作、取付、および使用する方法 |
JPWO2015163470A1 (ja) * | 2014-04-24 | 2017-04-20 | 京セラ株式会社 | 被覆工具 |
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US10118229B2 (en) | 2014-04-24 | 2018-11-06 | Kyocera Corporation | Coated tool |
US10428416B2 (en) | 2014-09-17 | 2019-10-01 | Nippon Itf, Inc. | Coating film, manufacturing method for same, and PVD device |
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US11554421B2 (en) | 2017-08-22 | 2023-01-17 | Sumitomo Electric Hardmetal Corp. | Cutting tool and method of manufacturing the same |
JPWO2019039005A1 (ja) * | 2017-08-22 | 2020-09-17 | 住友電工ハードメタル株式会社 | 切削工具およびその製造方法 |
JP7006881B2 (ja) | 2017-08-22 | 2022-01-24 | 住友電工ハードメタル株式会社 | 切削工具およびその製造方法 |
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Also Published As
Publication number | Publication date |
---|---|
TWI268192B (en) | 2006-12-11 |
KR101065572B1 (ko) | 2011-09-19 |
KR20060109868A (ko) | 2006-10-23 |
CN1819885A (zh) | 2006-08-16 |
MY138872A (en) | 2009-08-28 |
EP1649955A1 (en) | 2006-04-26 |
CN100387385C (zh) | 2008-05-14 |
US20060216515A1 (en) | 2006-09-28 |
EP1649955B1 (en) | 2013-08-14 |
JPWO2005011902A1 (ja) | 2006-09-14 |
TW200503873A (en) | 2005-02-01 |
AU2003280758A1 (en) | 2005-02-15 |
HK1091435A1 (en) | 2007-01-19 |
US7883775B2 (en) | 2011-02-08 |
EP1649955A4 (en) | 2009-10-21 |
JP4420901B2 (ja) | 2010-02-24 |
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