WO2017135243A1 - Élément composite et outil de coupe - Google Patents

Élément composite et outil de coupe Download PDF

Info

Publication number
WO2017135243A1
WO2017135243A1 PCT/JP2017/003390 JP2017003390W WO2017135243A1 WO 2017135243 A1 WO2017135243 A1 WO 2017135243A1 JP 2017003390 W JP2017003390 W JP 2017003390W WO 2017135243 A1 WO2017135243 A1 WO 2017135243A1
Authority
WO
WIPO (PCT)
Prior art keywords
cemented carbide
based cemented
composite
joining
joint
Prior art date
Application number
PCT/JP2017/003390
Other languages
English (en)
Japanese (ja)
Inventor
五十嵐　誠
藤原　和崇
Original Assignee
三菱マテリアル株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from JP2017009853A external-priority patent/JP6757519B2/ja
Application filed by 三菱マテリアル株式会社 filed Critical 三菱マテリアル株式会社
Publication of WO2017135243A1 publication Critical patent/WO2017135243A1/fr

Links

Images

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
    • B22F7/06—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite workpieces or articles from parts, e.g. to form tipped tools
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23B—TURNING; BORING
    • B23B51/00—Tools for drilling machines
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23C—MILLING
    • B23C5/00—Milling-cutters
    • B23C5/16—Milling-cutters characterised by physical features other than shape
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/08—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on tungsten carbide

Definitions

  • the present invention relates to a composite member and a cutting tool having excellent joint strength at a joint portion, and more particularly, to a composite member obtained by joining a WC-based cemented carbide and a WC-based cemented carbide, and further to a cutting tool comprising the composite member. .
  • WC-based cemented carbide TiCN-based cermet, cBN sintered body, and the like are well known as tool materials.
  • tool materials are not formed from a single material but as a composite member. Has been proposed to form.
  • Patent Document 1 discloses a bonded body in which a cermet sintered body is a first material to be bonded 1 and a cBN sintered body or a diamond sintered body is a second material to be bonded 3.
  • the joining material and the second joining material are joined via a joining material 2 (for example, Ti, Co, Ni) that does not generate a liquid phase at a temperature lower than 1000 ° C., and the joining is performed at a pressure of 0.1 MPa to 200 MPa.
  • a joining material 2 for example, Ti, Co, Ni
  • Patent Document 2 discloses a bonded body in which a cemented carbide sintered body is a first material to be bonded 1 and a cBN sintered body is a second material to be bonded 2.
  • the two materials to be joined are joined to each other by at least two surfaces consisting of a back surface and a bottom surface of the second material to be joined, with a joining material 3 containing titanium (Ti),
  • TiN titanium nitride
  • TiN titanium nitride
  • Patent Document 3 discloses a cBN sintered body containing 20 to 100% by mass of cBN, carbides of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo and W, carbonitrides, and their mutual solid solutions.
  • Hard phase composed of at least one selected from the group consisting of: 50 to 97% by mass, and the balance as a main component of at least one selected from the group consisting of Co, Ni and Fe: 3 to
  • a bonding layer is provided between the cBN sintered body and the hard alloy, and the bonding layer is composed of a ceramic phase and a metal phase. It has been proposed to increase the bonding strength of the composite by setting the thickness to 2 to 30 ⁇ m.
  • the composite material proposed in Patent Documents 1 to 3 or a cutting tool made of the composite material exhibits a certain level of performance under normal conditions of cutting. For example, a high feed and a high incision in which a high load acts on the cutting edge. Under heavy cutting conditions, it could not be said that the joining strength was still sufficient, and there was a risk of breakage from the joint. Therefore, there is a demand for a composite member having a higher joint strength and a cutting tool made of the same that does not cause breakage from the joint even under heavy cutting conditions in which a high load acts on the cutting edge.
  • the present inventors have prepared a composite member comprising a WC-base cemented carbide and a WC-base cemented carbide and a cutting tool comprising the composite material, for example, A cutting edge portion made of a composite sintered body obtained by bonding a WC-based cemented carbide (backing material) and a WC-based cemented carbide tool base (base metal) simultaneously with sintering of a cBN sintered body during ultra-high pressure and high-temperature sintering.
  • One WC-based cemented carbide member and the other WC-based cemented carbide member are joined via a joining member mainly composed of Ti, and one WC-based cemented carbide member and the other WC-based cemented carbide member are In a composite member in which the WC base cemented carbide member is joined by a joint portion, a predetermined layer thickness is formed in the vicinity of the interface between the joint portion and the WC base cemented carbide member (hereinafter referred to as the WC base cemented carbide member interface vicinity).
  • the modified layer is formed and the composition of the components contained in the binder phase of the modified layer is maintained within the proper range, the adhesion strength and bonding strength between the WC-based cemented carbide member and the joint are improved. As a result, it has been found that a composite member having excellent bonding strength can be obtained.
  • the composite member When the composite member is used as a material for a cutting tool, breakage from the joint occurs even when subjected to heavy cutting of steel or cast iron in which a high load acts on the cutting edge. Thus, the inventors have found that excellent cutting performance can be exhibited over a long period of use.
  • the present invention has been made based on the above findings, “(1) A composite member in which WC-based cemented carbide members are joined together via a joint, (A) The WC-based cemented carbide member includes at least a binder phase mainly composed of a Co component that fills a gap between the WC particles and the WC particles, (B) The joining portion contains 50 atomic% or more of Ti, and the balance has a component composition containing at least W, C, and Co.
  • the binder phase composition in the vicinity of the interface between the joint and the WC-based cemented carbide member, the binder phase composition is W: 5 to 20 atomic%, C: 5 to 20 atomic%, and the balance is There is a modified layer composed of 60 to 90 atomic% Co and inevitable impurities and having an average width of 0.2 to 5.0 ⁇ m, and the binder phase composition on the inner side of the cemented carbide member from the modified layer W: less than 5 atomic%, C: less than 5 atomic%, balance Co and inevitable impurities.
  • the composite member according to (1), wherein the thickness of the joint is 2 to 100 ⁇ m.
  • a cutting tool comprising the composite member according to (1) or (2). " It is characterized by.
  • a joining member (pure Ti foil, Ti alloy foil, etc. containing 85 atomic% or more of Ti) is disposed between one WC-based cemented carbide member and the other WC-based cemented carbide member.
  • one WC-based cemented carbide member and the other WC-based cemented carbide member are abutted with each other via a joining member, and a predetermined temperature is applied, with a predetermined pressure applied,
  • the present invention in which WC-based cemented carbide members are joined to each other through a joint by solid-phase diffusion-bonding the WC-based cemented carbide member and the joining member over time (see FIG. 1B).
  • the composite member can be manufactured (see FIG. 1C). *
  • FIG. 2 shows an enlarged schematic diagram of FIG. 1 (c).
  • W and WC particles constituting WC particles are shown in the binder phase near one WC-based cemented carbide member interface adjacent to the joint.
  • a modified layer in which C is diffused into Co as a binder phase is formed.
  • a modified layer in which W and C are diffused is also formed in the binder phase in the vicinity of the other WC-based cemented carbide member interface adjacent to the joint.
  • the joining member interposed between one WC-based cemented carbide member and the other WC-based cemented carbide member is composed of W, C, which are components thereof, from the WC-based cemented carbide member by solid phase diffusion bonding.
  • the compounding component composition of the WC-based cemented carbide suitable for forming the modified layer and the joint is a WC-based cemented carbide composed of Co: 5 to 15% by mass and the balance WC. , TaC, NbC, VC and Cr 3 C 2 , one or two or more components can be contained in a total content of 3% by mass or less.
  • the solid phase diffusion bonding employed in the present invention is the following bonding means. That is, the WC-based cemented carbide member and the WC-based cemented carbide member are abutted with each other through the joining member, and the joining member and the WC-based cemented carbide are maintained by holding a predetermined temperature and time with a predetermined pressure applied. Hard alloy components are reacted to form an alloy. Under the present circumstances, it can be set as the joining which has the outstanding intensity
  • WC-based cemented carbide at 1000 ° C. or lower. It is possible to control the reaction so that the brittle phase generated by the reaction does not reduce the strength of the bonding interface, and the diffusion rate becomes unbalanced in the interdiffusion between the WC-based cemented carbide and the bonding member. Conditions such as the difficulty of generating the generated Kirkendall void are required.
  • a pure Ti foil or a Ti alloy foil having a Ti content of 85 atomic% or more is used as a joining member meeting such requirements.
  • the composition of the composite member that is finally formed is different from that of the joining member.
  • W and C constituting the WC particles diffuse into Co as a binder phase, so that the WC base super A modified layer having a composition different from that of the binder phase of the hard alloy is formed.
  • it can be a starting point of delamination and a propagation path of cracks by forming a bonded portion having a component composition different from that of the bonded member and forming a modified layer having a composition different from the bonded phase of the WC-based cemented carbide before bonding.
  • the modified layer is strengthened, and as a result, a composite member having an excellent strength that hardly peels from the vicinity of the joint can be produced.
  • the surface of the WC-based cemented carbide member disposed opposite to the joining member is preliminarily blasted to introduce strain. It is desirable to keep it.
  • the strain of WC and Co is relaxed at the time of solid phase diffusion bonding, and as a result, the reaction between WC, Co and Ti is promoted, and even when the solid phase diffusion bonding temperature is low. Uniform reaction is realized.
  • FIG. 3 shows an SEM image near the interface between the WC-based cemented carbide member and the joint in the composite member of the present invention
  • FIG. 4 shows a schematic diagram near the interface.
  • W and C which are components constituting the WC particles
  • W and C are contained in the binder phase of the WC-based cemented carbide member.
  • a diffused modified layer is formed.
  • the region in which the contents of W and C diffused from the WC particles are 5 atom% or more and 20 atom% or less in the binder phase in the vicinity of the WC-based cemented carbide member interface is defined as the modified layer.
  • the average width of the modified layer is set to 0.2 to 5.0 ⁇ m.
  • the W and C contents in the binder phase in the modified layer are in the range of 5 atomic% to 20 atomic% as described above. This is because the W content in the modified layer is less than 5 atomic% or This is because if the C content is less than 5%, the effect of modifying the binder phase is insufficient, and interface peeling is likely to occur between the WC-based cemented carbide member and the joint portion. If the W content or C content exceeds 20% by mass, a large amount of fragile free C phase or ⁇ phase precipitates, and breakage easily occurs inside the modified layer.
  • the C content is 5 to 20 atomic%.
  • the modified phase Since the main component constituting the binder phase of the WC-based cemented carbide member is Co, the modified phase has a binder phase composition of W: 5 to 20 atomic%, C: 5 to 20 atomic%, and the balance of 60. ⁇ 90 atomic% of Co and inevitable impurities.
  • the binder phase composition On the inner side of the cemented carbide member from the modified layer, the binder phase composition was W: less than 5 atomic%, C: less than 5 atomic%, the balance Co and inevitable impurities. This is the average width of the modified layer If a binder phase containing 5 atomic% or more of W or C is present inside the cemented carbide exceeding the upper limit of 5.0 ⁇ m, a free C phase or ⁇ phase appears and the strength of the entire cemented carbide member decreases.
  • the binder phase composition inside the cemented carbide member from the modified layer was W: less than 5 atomic%, C: less than 5 atomic%, the remaining Co and inevitable impurities.
  • the average width of the modified layer in the present invention can be determined, for example, as follows. As shown in FIG. 3 and FIG. 4, first, using a scanning electron microscope and an Auger electron spectrometer, a longitudinal section of the vicinity of the boundary between the WC-based cemented carbide member and the joint is observed, and the WC-based cemented carbide member As viewed from the side, the critical position where the WC crystal grains are observed is defined as the interface between the WC-based cemented carbide member and the joint, and the interface is the starting point and is perpendicular to the interface from the interface toward the inside of the WC-based cemented carbide member. Then, a line measurement with a length of 20 ⁇ m is performed.
  • a total of 10 lines are measured with an interval of each line being 1 ⁇ m.
  • the amount of W, C, and Co contained in the binder phase is determined from the results of the line measurement, and among the points containing 5 atomic% or more of W and C in the binder phase, the WC-based cemented carbide member from the interface.
  • the distance to the innermost point is defined as the modified region in each line, and the average width of the modified layer is obtained by averaging the three modified region widths of the wide modified region out of the 10 line measurements. be able to.
  • the contents of W, C, and Co in the modified layer of the present invention can be determined, for example, as follows. First, using a scanning electron microscope, the longitudinal vicinity of the boundary between the WC-based cemented carbide member and the joint is observed, and three straight lines parallel to the interface are obtained in the width direction of the modified layer obtained above. Draw into 4 equal parts. The bonded phases existing on the three straight lines are selected in three places on each straight line, a total of nine places, point measurement is performed at the nine places using an Auger electron spectrometer, and the measured values at the nine points are averaged. Thus, the contents of W, C, and Co can be obtained.
  • a joining part is formed by solid phase diffusion joining using a joining member made of pure Ti foil or a Ti alloy foil of 85 atomic% or more, and the composition of the joining part is 50 atoms of Ti. %, And the balance is at least W, C, and Co. Since W, C, and Co, which are components of the WC-based cemented carbide member, diffuse in the joint, the composition of the joint varies from the composition of the joint, but the Ti content of the joint is 50. If it is less than atomic%, the joint itself shows a tendency to become brittle, so the Ti content in the joint must be 50 atomic% or more.
  • the Ti content in the bonded portion can be 50 atomic% or more.
  • the thickness of the joint is 2 ⁇ m or less, voids are likely to be generated in the joint, so that it is difficult to obtain a sufficient joint strength. If the thickness is 100 ⁇ m or more, the metal Ti remains thick, Is peeled off, and it is difficult to obtain sufficient bonding strength. Therefore, the thickness of the bonded portion is desirably in the range of 2 to 100 ⁇ m.
  • the composite member of the present invention can be produced, for example, by the following method.
  • a pretreatment for introducing strain is performed by blasting the surfaces of one WC-based cemented carbide member and the other WC-based cemented carbide member facing the joining member.
  • a pure Ti foil as a joining member or a Ti alloy foil containing 85 atomic% or more Ti is sandwiched between one WC-based cemented carbide member and the other WC-based cemented carbide member.
  • a vacuum at a predetermined temperature of 600 to 900 ° C.
  • the composite member of the present invention can constitute a cutting tool by using one WC-based cemented carbide member as the cutting edge portion side and the other WC-based cemented carbide member as the tool base. More specifically, for example, one WC-based cemented carbide member of the composite member is used as a backing material for a cBN sintered body on the cutting edge side, and the other WC-based cemented carbide member is used as a tool base. By using (base metal), a cBN cutting tool can be formed.
  • the present invention relates to a Ti alloy containing WC-based cemented carbide members (one WC-based cemented carbide member and the other WC-based cemented carbide member) as a joining member using pure Ti foil or 85 atomic% or more Ti.
  • This is a composite member joined through a joint formed by solid phase diffusion bonding using foil, in which W and C are diffused in the binder phase near the interface of the WC-based cemented carbide member adjacent to the joint.
  • the WC-based cemented carbide member and the joint portion are formed by controlling the composition of the components contained in the modified layer within an appropriate range while the average width of the modified layer is within a predetermined range. As a result, a composite member having excellent bonding strength can be obtained.
  • the cutting tool comprised from the said composite member does not produce the fracture
  • WC powder, VC powder, TaC powder, NbC powder, Cr 3 C 2 powder and Co powder each having an average particle diameter of 0.5 to 1 ⁇ m were prepared. These raw material powders are shown in Table 1. It is blended into the blended composition, wet mixed in a ball mill for 24 hours, dried, and then pressed into a green compact at a pressure of 100 MPa, and this green compact is vacuumed at 6 Pa, temperature 1400 ° C., holding time 1 hour. Sintering was performed under the conditions to form four types of WC-based cemented carbide sintered bodies (hereinafter simply referred to as “superhard alloys”) A-1 to A-4 shown in Table 1.
  • superhard alloys WC-based cemented carbide sintered bodies
  • cBN powder, TiN powder, TiCN powder, TiB 2 powder, TiC powder, AlN powder, and Al 2 O each having an average particle size in the range of 0.5 to 4 ⁇ m are used as raw material powders for the cBN sintered body.
  • 3 powders were prepared, these raw material powders were blended in a prescribed composition, wet mixed with acetone for 24 hours in a ball mill, dried, and then pressure having a size of 15 mm diameter ⁇ 1 mm thickness at 100 MPa pressure. Press-molded into powder.
  • the cemented carbides A-1 to A-4 are formed into a sintered body having a diameter of 15 mm ⁇ thickness of 2 mm, and this is used as a backing material during the sintering of the cBN sintered body.
  • the joining members shown in Table 3 are inserted between the cemented carbides A-1 to A-4 and the composite sintered bodies B-1 to B-4, and the conditions shown in Table 4 (that is, 1 to 1).
  • a pure Ti foil having a thickness of 100 ⁇ m or a Ti alloy foil containing 85 atomic% or more of Ti is used as a joining member, and a predetermined temperature within a range of 600 to 900 ° C. in a vacuum of 1 ⁇ 10 ⁇ 3 Pa or less is set to 5 to
  • the composite sintered body and the cemented carbide were pressure bonded under the conditions of holding for 600 minutes and applying a pressing force of 0.5 to 5 MPa to produce the composite members 1 to 10 of the present invention shown in Table 6.
  • the composite sintered body is such that the cBN sintered body is the outer surface and the backing material is the inner surface, that is, the WC-based cemented carbide that is the backing material and the WC-based cemented carbide that is the tool base (base metal) are the bonding members. It arrange
  • a joining member shown in Table 3 was used, and this was interposed between cemented carbides A-1 to A-4 and composite sintered bodies B-1 to B-4.
  • the composite sintered body and the cemented carbide were pressure-bonded under the conditions shown in Table 8 to produce comparative example composite members 1 to 10 shown in Table 8.
  • the joint arrangement of the composite sintered body was the same as that of the composite member of the present invention.
  • High temperature shear strength measurement test For the composite members 1 to 10 of the present invention and the comparative composite members 1 to 10 produced above, a shear strength measurement test was performed in order to measure the strength of the joint.
  • the test pieces used for the test were composite sintered bodies of 1.5 mm (W) ⁇ 1.5 mm (L) ⁇ 0.00 mm from the composite members 1 to 10 of the present invention and the comparative composite members 1 to 10 prepared above.
  • test piece The upper and lower surfaces of the test piece are clamped and fixed, and a prismatic pressing piece made of cemented carbide with a side of 1.5 mm is used.
  • the ambient temperature is set to 600 ° C. and a load is applied near the center of the upper surface of the test piece The load at which the test piece breaks was measured.
  • Tables 6 and 8 show the measured shear strength values.
  • the modified layer in which W and C as components constituting the WC particles are diffused in the binder phase in the vicinity of the interface of the WC-based cemented carbide member was measured and calculated as follows using a scanning electron microscope and an Auger electron spectrometer. First, the longitudinal section of the boundary between the WC-based cemented carbide member and the joint is observed, and the critical position where the WC crystal grains are observed is viewed from the WC-based cemented carbide member side. And the interface.
  • 10 lines were measured at intervals of 1 ⁇ m from the interface to the inside of the WC-based cemented carbide member and in a direction perpendicular to the interface from 20 ⁇ m, and the W content, C content, and Co content contained in the binder phase were measured. Asked.
  • the distance from the interface to the innermost point of the WC-based cemented carbide member is defined as the modified region in each line, and 10 lines are measured.
  • the average width of the modified layer was determined by averaging the widths of the three modified regions having a wide modified region.
  • W amount, C amount, and Co amount in the modified layer a vertical cross-sectional observation of the vicinity of the boundary between the WC-based cemented carbide member and the joint is performed using a scanning electron microscope.
  • the straight line of the book is drawn so that the width direction of the modified layer obtained above is divided into four equal parts, and point measurement is performed on the bonded phase in the modified layer existing on each straight line using an Auger electron spectrometer.
  • the content of W, C, and Co was calculated
  • Tables 7 and 9 show the measurement results of the modified layer on the composite sintered body side.
  • the measurement results on the tool base (base metal) side and the composite sintered body side were substantially the same. It was shown to.
  • a cutting tool made of a composite member was produced as follows.
  • the composite sintered bodies B-1 to B-4 produced above were cut into a planar shape: an isosceles triangle having an opening angle of 80 ° with a side of 4 mm ⁇ thickness: 2 mm.
  • the cemented carbides A-1 to A-4 are formed into a sintered body having a planar shape: 12.7 mm inscribed circle and an open angle of 80 ° rhombus ⁇ thickness: 4.76 mm.
  • a notch having a size corresponding to the shape of the composite sintered body was formed in one corner of any one of the upper and lower parallel surfaces of the bonded body using a grinding machine.
  • the area of the bottom surface of this notch is 2.96 mm 2 and the area of the side surface is 4.89 mm 2 .
  • the joining members shown in Table 3 are inserted between the cemented carbides A-1 to A-4 and the composite sintered bodies B-1 to B-4, and the composite sintered body is subjected to the conditions shown in Table 4.
  • the WC base cemented carbide are pressure bonded, and after cutting the outer periphery of this composite member, the cutting edge portion is subjected to a honing process of R: 0.07 mm to have an ISO standard / CNGA120408 insert shape.
  • Tools 1 to 10 were produced.
  • the composite sintered body was arranged so that the cBN sintered body was the outer surface and the backing material was the inner surface, that is, the backing material and the tool base (base metal) were joined via the joining member. Further, it was confirmed that the joints of these cutting tools 1 to 10 of the present invention were substantially the same as the composite members 1 to 10 of the present invention shown in Table 6.
  • the composite members 1 to 10 of the present invention have superior bonding strength compared to the composite members 1 to 10 of the comparative example. Further, from the results shown in Table 10, the cutting tools 1 to 10 of the present invention composed of the composite members 1 to 10 of the present invention exhibit excellent cutting performance over a long period of use without the removal of the cutting edge. On the other hand, it can be seen that, in the comparative cutting tools 1 to 10 composed of the comparative composite members 1 to 10, the cutting edge falls off from the joint during cutting, and the tool life is reached early.
  • the insert has been specifically described as an example.
  • the present invention is not limited to the insert, and all cutting tools having a joint between the cutting edge portion and the tool body, such as a drill and an end mill. Needless to say, the present invention is applicable to drilling tools such as bits.
  • the composite member of the present invention has a high bonding strength, and a cutting tool made from this composite member can be used for high-load cutting such as high-speed heavy cutting such as various steels and cast irons. Since it exhibits stable cutting performance over a long period of time, it can sufficiently satisfactorily cope with higher performance of the cutting apparatus, labor saving and energy saving of cutting, and cost reduction.

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Composite Materials (AREA)
  • Manufacturing & Machinery (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
  • Powder Metallurgy (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)

Abstract

L'invention concerne l'amélioration de la résistance de liaison d'un élément composite obtenu par liaison de carbures cimentés à base de WC par le biais d'éléments de liaison, formés chacun d'une feuille de Ti pur ou d'une feuille d'alliage de Ti. L'invention concerne un élément composite et un outil fabriqué à partir de l'élément composite. Dans l'élément composite, les éléments de carbure cimenté à base de WC sont liés ensemble avec une section de liaison et des couches modifiées sont intercalées entre eux et des éléments de liaison formés chacun de feuille de Ti pur ou de feuille d'alliage de TI sont reliés ensemble par diffusion à l'état solide : la section de liaison a une composition de composants dans laquelle pas moins de 50 % atomiques de Ti sont contenus et la partie restante contient au moins W, C et Co ; dans des phases de liant qui sont adjacentes à la section de jonction et qui sont à proximité des interfaces des éléments de carbure cimentés à base de WC respectifs, les couches modifiées ayant chacune une largeur de moyenne de 0,2 à 5,0 µm sont formées ; et chacune des phases de liant des couches modifiées présente une composition formée de 5 à 20 % atomiques de W, 5 à 20 % atomiques de C et la partie restante de 60 à 90 % atomiques de Co et les impuretés inévitables.
PCT/JP2017/003390 2016-02-01 2017-01-31 Élément composite et outil de coupe WO2017135243A1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2016016961 2016-02-01
JP2016-016961 2016-02-01
JP2017-009853 2017-01-23
JP2017009853A JP6757519B2 (ja) 2016-02-01 2017-01-23 複合部材及び切削工具

Publications (1)

Publication Number Publication Date
WO2017135243A1 true WO2017135243A1 (fr) 2017-08-10

Family

ID=59500220

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2017/003390 WO2017135243A1 (fr) 2016-02-01 2017-01-31 Élément composite et outil de coupe

Country Status (1)

Country Link
WO (1) WO2017135243A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2019181592A (ja) * 2018-04-04 2019-10-24 住友電気工業株式会社 切削工具

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH08168905A (ja) * 1994-12-15 1996-07-02 G N Tool Kk 切削工具
JP2015182161A (ja) * 2014-03-24 2015-10-22 三菱マテリアル株式会社 複合部材及び切削工具

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH08168905A (ja) * 1994-12-15 1996-07-02 G N Tool Kk 切削工具
JP2015182161A (ja) * 2014-03-24 2015-10-22 三菱マテリアル株式会社 複合部材及び切削工具

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2019181592A (ja) * 2018-04-04 2019-10-24 住友電気工業株式会社 切削工具
JP7087596B2 (ja) 2018-04-04 2022-06-21 住友電気工業株式会社 切削工具

Similar Documents

Publication Publication Date Title
CN104044308B (zh) 表面包覆切削工具
US8074865B2 (en) Gradient polycrystalline cubic boron nitride materials and tools incorporating such materials
JP6245520B2 (ja) 複合部材及び切削工具
JP5603954B2 (ja) 超硬要素、その使用方法及びその製造方法
JP6459042B2 (ja) 接合用ろう材およびそれを用いた複合部材、切削工具
WO2017038855A1 (fr) Élément composite et outil de coupe
WO2017135243A1 (fr) Élément composite et outil de coupe
JP2008254159A (ja) 表面被覆立方晶窒化ほう素基超高圧焼結材料製切削工具
US20190271062A1 (en) Composite sintered material
JP2018140416A (ja) 複合部材とこれを作製するために用いる接合部材およびこの複合部材からなる切削工具
JP6757519B2 (ja) 複合部材及び切削工具
JP5656076B2 (ja) ｃＢＮインサート
JP6694597B2 (ja) 複合部材及び切削工具
JP2018051619A (ja) 複合部材及び切削工具
JP2019063901A (ja) 複合部材及び切削工具
JP2018122313A (ja) 複合部材とこれを作製するために用いる接合部材およびこの複合部材からなる切削工具
JP2008302439A (ja) 表面被覆立方晶窒化ほう素基超高圧焼結材料製切削工具
JP2018111108A (ja) 複合部材およびこの複合部材からなる切削工具
JP2018048038A (ja) 積層構造焼結超砥粒複合材及びその製造方法
JP2008018505A (ja) 硬質難削材の高速切削加工ですぐれた耐欠損性を発揮する表面被覆立方晶窒化ほう素基超高圧焼結材料製切削工具
JP4883479B2 (ja) 高硬度鋼の高速断続切削加工ですぐれた耐欠損性を発揮する表面被覆立方晶窒化ほう素基超高圧焼結材料製切削工具
JP5004690B2 (ja) 切削工具の製造方法
JP2016101603A (ja) 複合部材及び切削工具
JP2016140920A (ja) 複合部材及び切削工具
JP5804380B2 (ja) 超高圧焼結体製切削工具

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 17747399

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 17747399

Country of ref document: EP

Kind code of ref document: A1