WO2010110197A1 - Cermet - Google Patents

Cermet Download PDF

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Publication number
WO2010110197A1
WO2010110197A1 PCT/JP2010/054778 JP2010054778W WO2010110197A1 WO 2010110197 A1 WO2010110197 A1 WO 2010110197A1 JP 2010054778 W JP2010054778 W JP 2010054778W WO 2010110197 A1 WO2010110197 A1 WO 2010110197A1
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Prior art keywords
hard phase
phase
cermet
hard
particles
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PCT/JP2010/054778
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English (en)
Japanese (ja)
Inventor
和弘 広瀬
秀樹 森口
圭一 津田
Original Assignee
住友電気工業株式会社
住友電工ハードメタル株式会社
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Application filed by 住友電気工業株式会社, 住友電工ハードメタル株式会社 filed Critical 住友電気工業株式会社
Priority to KR1020107026206A priority Critical patent/KR101253853B1/ko
Priority to SE1051204A priority patent/SE536731C2/sv
Priority to CN201080001593.3A priority patent/CN102046823B/zh
Publication of WO2010110197A1 publication Critical patent/WO2010110197A1/fr

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    • 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
    • C22C29/04—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 carbonitrides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
    • 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
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy

Definitions

  • the present invention relates to a cermet suitable for a constituent material of a cutting tool and a coated cermet tool based on this cermet.
  • the present invention relates to a cermet that provides a cutting tool that is excellent in fracture resistance and capable of performing cutting with excellent quality of the work surface of a work material.
  • Patent Document 1 discloses a cermet having a hard phase composed of a single-phase particle and a core-structured particle whose core is covered by the periphery.
  • Patent Documents 2 and 3 disclose cermets in which cored particles having a core part and a peripheral part covering the core part are used as a hard phase.
  • Cermet tools based on cermets are generally superior in wear resistance and have a machined surface (finished surface) of the work material compared to tools made of cemented carbide with tungsten carbide (WC) as the main hard phase. Although it is beautiful, it has low toughness and inferior fracture resistance. Therefore, sudden breakage is likely to occur and the tool life is not stable. In recent years, it has been demanded to further improve the quality of the work surface of a work material in cutting and to improve the fracture resistance, which is a weak point of a cermet tool, so as to stabilize the tool life.
  • WC tungsten carbide
  • one of the objects of the present invention is to provide a cermet suitable for a constituent material of a cutting tool that is excellent in fracture resistance and capable of cutting with excellent quality of the processed surface.
  • Another object of the present invention is to provide a coated cermet tool comprising a substrate made of the cermet.
  • the present inventors have a high wear resistance when a hard phase exists in a specific range in the cermet and four kinds of particles having different compositions and forms exist as the particles constituting the hard phase.
  • the inventors have found that remarkable improvement in fracture resistance and welding resistance can be expected. Further, the surface quality of the work material can be improved by improving the welding resistance.
  • the present invention defines the content of the hard phase and the four hard phases.
  • the hard phase composed of one or more compounds selected from the group consisting of carbides, nitrides, carbonitrides, and their solid solutions of the Group 4, 5, 6 metals of the Periodic Table contains an iron group metal. It is a cermet bonded by a binder phase as a main component. This cermet contains 70% by mass or more and 97% by mass or less of the hard phase, with the balance being substantially composed of a binder phase.
  • the cermet contains the following first hard phase, second hard phase, third hard phase, and fourth hard phase as the hard phase.
  • First hard phase consists of a single phase of titanium carbonitride (Ti (C, N)), or part of the periphery of Ti (C, N) is titanium (Ti), periodic table 4, 5, 6 It is a hard phase covered with a composite carbonitride solid solution with one or more metals selected from group metals (excluding Ti).
  • Second hard phase a hard phase having a core structure including a core portion and a peripheral portion covering the entire periphery of the core portion. The core is composed of Ti (C, N), and the peripheral portion is composed of Ti and one or more metals selected from Group 4, 5, 6 metals (excluding Ti) of the periodic table. It is composed of a composite carbonitride solid solution.
  • Third hard phase a hard phase having a core structure including a core part and a peripheral part covering the entire periphery of the core part.
  • the said core part and the said peripheral part are comprised from the same element, and are comprised from the composite carbonitride solid solution containing Ti and W at least. Further, the W concentration in the core portion is larger than the W concentration in the peripheral portion.
  • Fourth hard phase A hard phase having a single-phase structure composed of a composite carbonitride solid solution of Ti and one or more metals selected from Group 4, 5, 6 metals (excluding Ti) of the periodic table. is there.
  • the cermet of the present invention contains a specific amount of a hard phase, and the first hard phase, the second hard phase, the third hard phase, and the fourth hard phase coexist as the hard phase. It can have the functions of each of the hard phase to the fourth hard phase.
  • the cermet of the present invention has excellent wear resistance due to the presence of a hard phase having a high hardness, and good wetting with the binding phase due to the presence of a hard phase excellent in wettability with the binding phase.
  • the structure can be maintained, and the structure in which the binder phase exists uniformly can be obtained, and improvement of wear resistance and defect resistance can be expected by homogenizing the structure.
  • the cermet of the present invention can improve thermal conductivity due to the presence of a hard phase having excellent thermal characteristics, and can also be expected to suppress thermal cracking and improve welding resistance.
  • the cermet of the present invention has excellent wear resistance and can remarkably improve fracture resistance and welding resistance. For this reason, the cutting tool constituted by the cermet of the present invention is less likely to be worn or chipped, so that the tool life can be stabilized and the life can be extended. The quality of the machined surface of the work material can be improved.
  • the present invention will be described in more detail.
  • the cermet of the present invention is composed of a hard phase of 70% by mass or more and 97% by mass or less, and the balance is composed of a binder phase and inevitable impurities.
  • Inevitable impurities include oxygen and metal elements in the order of ppm, which are contained in the raw material or mixed in the manufacturing process.
  • the hard phase is a compound of at least one metal element selected from Group 4, 5, 6 metals of the periodic table and at least one element of carbon (C) and nitrogen (N), that is, a carbide of the above metal element. , Nitride, carbonitride, and at least one selected from these solid solutions.
  • the cermet of the present invention is a Ti (C, N) -based cermet containing at least a carbonitride solid solution containing titanium carbonitride (Ti (C, N)) and titanium (Ti).
  • a more preferable content of the hard phase is 80% by mass or more and 90% by mass or less.
  • the hard phase contains four kinds of different compositions and forms, such as the first hard phase, the second hard phase, the third hard phase, and the fourth hard phase described above. Specifically, it contains a Ti (C, N) -based hard phase and a hard phase having other composition including Ti, a single-phase hard phase, and a hard phase with a core structure.
  • the presence state of the four hard phases can be easily discriminated by the density of micrographs taken with a scanning electron microscope (SEM).
  • the particles constituting the first hard phase are particles having a single phase structure substantially consisting of only Ti (C, N), or a part of the periphery of Ti (C, N) is Ti and a periodic table other than Ti. Particles covered with a composite carbonitride solid solution of one or more metals selected from Group 4,5,6 metals, that is, the periphery of Ti (C, N) is completely covered with the composite carbonitride solid solution. The particles are not.
  • the first hard phase contains a large amount of Ti as compared with the third hard phase and the fourth hard phase, which will be described later, so that the hardness is high and the reactivity with steel that is widely used for work materials is low. Therefore, the presence of the first hard phase in the cermet makes it possible to achieve particularly improved wear resistance and welding resistance.
  • the particles constituting the second hard phase are substantially composed of Ti (C, N) in the core (Ti (C, N) occupies 95% or more of the entire core by atomic ratio).
  • the specific composition of the peripheral part is, for example, (Ti, W, Mo) (C, N), (Ti, W, Nb) (C, N), (Ti, W, Mo, Nb) (C, N ), (Ti, W, Mo, Nb, Zr) (C, N).
  • the second hard phase has a peripheral part that has good wettability with the binder phase over the entire periphery of the core part, reducing the occurrence of nests in the cermet Can be homogenized, and as a result, the hardness can be stabilized. Further, the homogenization of the structure can be expected to further improve toughness such as fracture resistance. Therefore, the presence of the second hard phase in the cermet can stabilize the effects of wear resistance and fracture resistance, in particular.
  • the particles constituting the third hard phase are core-structured particles in which the core portion and the peripheral portion are composed of the same element, and are composed of a composite carbonitride solid solution containing at least Ti and W.
  • the W concentration in the core portion of this particle is larger than the W concentration in the peripheral portion.
  • Specific compositions include, for example, (Ti, W) (C, N), (Ti, W, Mo) (C, N), (Ti, W, Nb) (C, N), (Ti, W, Mo, Nb) (C, N) and the like. Since the third hard phase contains a larger amount of W than the first hard phase and the second hard phase, it is possible to improve the thermal conductivity while maintaining high hardness. Therefore, thermal strength, heat crack resistance, chipping resistance, and plastic deformation resistance can be improved.
  • the particles constituting the fourth hard phase have a single-phase structure composed of a composite carbonitride solid solution of Ti and at least one metal selected from Group 4, 5, 6 metals of the periodic table other than Ti. Particles. Unlike the third hard phase, this particle does not have a clear boundary between the core part and the peripheral part, and the entire particle has a uniform composition.
  • a typical example of the metal other than Ti constituting the fourth hard phase is W.
  • the specific composition of the fourth hard phase is, for example, (Ti, W) (C, N), (Ti, W, Mo) (C, N), (Ti, W, Nb) (C, N), (Ti, W, Mo, Nb) (C, N).
  • the fourth hard phase contains W
  • the W distribution is not seen
  • the entire fourth hard phase is uniform. W exists.
  • the presence of the fourth hard phase in the cermet causes a slight decrease in hardness, but the hardness becomes uniform and crack propagation in the hard phase hardly occurs.
  • thermal conductivity can be improved, the thermal crack resistance and fracture resistance can be improved.
  • the hard phase is substantially composed of only the first hard phase and the second hard phase, it is difficult to improve the fracture resistance.
  • the hard phase is substantially composed only of the first hard phase and the third hard phase, the wettability with the binder phase is deteriorated, so that nests are likely to be generated and the fracture resistance is poor.
  • the hard phase is substantially composed only of the first hard phase and the fourth hard phase, the wettability with the binder phase is poor, so nests are likely to occur, and sufficient hardness cannot be obtained and fracture resistance is obtained. Is bad.
  • the hard phase is substantially composed only of the second hard phase and the third hard phase, it is difficult to suppress the progress of cracks that pass through the boundary between the core and the peripheral part, which is a conventional problem, The expected fracture resistance cannot be obtained.
  • the hard phase is substantially composed only of the second hard phase and the fourth hard phase, improvement in fracture resistance cannot be expected.
  • the hard phase is substantially composed of the first hard phase, the second hard phase, and the third hard phase, and does not contain the fourth hard phase
  • the proportion of the third hard phase containing W is relatively increased.
  • W tends to react with the work material (particularly steel) during cutting, and welding tends to occur. Therefore, the work surface of the work material is deteriorated.
  • the presence of the fourth hard phase improves the quality (glossiness) of the work surface of the work material, and this excellent Can maintain stable quality.
  • the hard phase is substantially composed of the first hard phase, the second hard phase, and the fourth hard phase and does not contain the third hard phase, although it can be expected to improve the thermal conductivity, it causes a decrease in hardness and cracks occur. Since it progresses easily, the defect occurrence rate increases. In other words, in addition to the first hard phase, the second hard phase, and the fourth hard phase, the presence of the third hard phase further improves the thermal conductivity, thereby causing thermal cracks and the progress of these cracks. It is possible to reduce and effectively improve the fracture resistance.
  • the hard phase is substantially composed of the second hard phase, the third hard phase, and the fourth hard phase and does not contain the first hard phase, the wear resistance and welding resistance that can be expected by the presence of the first hard phase. It is difficult to obtain the effect of improvement, and particularly the gloss of the processed surface of the work material is inferior.
  • the hard phase is substantially composed of the first hard phase, the third hard phase, and the fourth hard phase and does not contain the second hard phase, that is, Ti (C, N, which is the main component of the hard phase in the cermet
  • the hard phase of the) system is only the first hard phase, the wettability with the binder phase becomes extremely poor as described above, and nests are likely to be generated, resulting in deterioration of mechanical properties.
  • the cermet of the present invention in addition to the first hard phase and the second hard phase, in particular, due to the simultaneous presence of the third hard phase and the fourth hard phase, the reaction with the steel while maintaining the thermal strength. It can be suppressed. Therefore, the cutting tool based on the cermet of the present invention can be expected to improve the resistance to thermal plastic deformation, improve the thermal crack resistance, and improve the welding resistance. It is expected that the properties can be improved.
  • the hard phase is preferably a mixture of coarse particles and fine particles, particularly fine particles having a particle size of 1 ⁇ m or less and coarse particles having a particle size of more than 1 ⁇ m and 3 ⁇ m or less. Furthermore, it is preferable that a hard phase of 60% or more and 90% or less with respect to the total area of the hard phase is made of the coarse particles, and the remainder of the hard phase is made of the fine particles.
  • the coarse particles are composed of the first hard phase, the second hard phase, the third hard phase, and the fourth hard phase, and the fine particles are substantially composed of the first hard phase and the second hard phase. It is preferable that
  • the presence of fine particles so as to fill gaps formed between coarse particles can improve hardness and fracture toughness. Since the particle size of the coarse particles is more than 1 ⁇ m and the particle size of the fine particles is 1 ⁇ m or less, a sufficient gap is provided between the coarse particles, and the fine particles can intervene in the gap. The effect of improving hardness and fracture toughness can be obtained. Further, when the particle size of coarse particles is 3 ⁇ m or less, the binder phase existing between the particles does not become excessive, and the decrease in hardness and the deterioration of fracture toughness due to the presence of a large binder phase pool can be reduced.
  • the particle size of the fine particles is particularly preferably 0.1 ⁇ m or more and 0.8 ⁇ m or less.
  • the area ratio of the coarse particles is 60% or more, since the coarse particles are present appropriately, the effect of suppressing the progress of cracks is large, and the toughness can be increased. Further, when the area ratio of the coarse particles is 90% or less, fine particles are sufficiently present in the gaps formed between the coarse particles, and the improvement in hardness and the progress of cracks can be suppressed. Furthermore, since fine particles are present appropriately, the surface roughness of the outermost surface of the cermet can be reduced, and excellent cutting performance can be obtained. A more preferable range of the area ratio of the coarse particles is 70% or more and 85% or less.
  • the total area of the fine particles is 80% or more, preferably 90% or more, and more preferably almost all of them are composed of the first hard phase and the second hard phase.
  • C, N is sufficiently present to improve wear resistance. The method for obtaining the particle size, area, and area ratio defined in the present invention will be described later.
  • the particle size and area ratio of the hard phase particles can be adjusted, for example, by adjusting the size and amount of the raw material powder and the production conditions (such as grinding time and sintering conditions).
  • the production conditions such as grinding time and sintering conditions.
  • the pulverization time is lengthened, the hard phase particles in the cermet tend to be fine, and when the sintering temperature is high, the hard phase particles in the cermet tend to be coarse. Even if the pulverization time is lengthened and the powder is made fine, if the sintering temperature is increased, the particles may grow and coarse hard phase particles may be present.
  • the area ratio of the first hard phase with a particle size of more than 1 ⁇ m and 3 ⁇ m or less (coarse) is S1
  • the area ratio of the second hard phase with a particle size of more than 1 ⁇ m and 3 ⁇ m or less (coarse) with respect to the total area of the hard phase is S2
  • (S1 + S2) preferably satisfies 0.1 or more and 0.5 or less.
  • (S1 + S2) is 0.1 or more, it is difficult to weld to the work material, and it is possible to reduce the occurrence of minute rashes on the work material surface, and to improve the properties of the work surface of the work material.
  • the wear resistance of the tool can be improved by reducing the wear due to welding by improving the welding resistance.
  • (S1 + S2) when (S1 + S2) is 0.5 or less, a decrease in toughness due to the increase in hardness can be suppressed, and chipping and chipping can hardly occur.
  • a more preferable range of (S1 + S2) is 0.3 or more and 0.5 or less.
  • SS1 / (SS1 + SS2) is 0.5 or more and 0.9
  • SS1 / (SS1 + SS2) is 0.5 or more, the minute first hard phase is present more than the second hard phase, so that it is possible to significantly improve the wear resistance.
  • SS1 / (SS1 + SS2) is 0.9 or less, the proportion of the first hard phase in the fine hard phase does not become excessive, and wetting due to the presence of the fine first hard phase in excess The possibility of causing the deterioration of hardness can be suppressed by the generation of minute nests accompanying the decrease in the wettability and the decrease in the wettability.
  • a more preferable range of SS1 / (SS1 + SS2) is 0.55 or more and 0.7 or less.
  • the total area ratio of the area of the third hard phase and the area of the fourth hard phase is larger than 40% with respect to the total area of the cermet (hard phase + binding phase). In this case, since the thermal characteristics are stabilized, the thermal cracking resistance is improved, and thus the fracture resistance can be improved.
  • the third hard phase and the fourth hard phase are preferably roughly coarse as described above.
  • the binder phase is mainly composed of at least one metal selected from iron group metals such as cobalt (Co), iron (Fe), and nickel (Ni).
  • “Main component” means that the binder phase is substantially composed of only one or more metals selected from the above iron group metals, or one or more selected from the above iron group metals.
  • An alloy in which the constituent elements of the hard phase described above are dissolved in 0.1% by mass to 20% by mass with respect to the total mass of the binder phase, that is, 80% by mass or more of the binder phase is composed of an iron group metal.
  • the binder phase is a solid solution of the constituent elements of the hard phase, the toughness can be improved and the fracture resistance tends to be increased by solid solution strengthening.
  • the binder phase since at least one of Co and Ni is a main component (80 mass% or more of the total mass of the binder phase), the binder phase has high wettability with the hard phase and excellent corrosion resistance. It becomes a preferable cermet by a constituent material.
  • Ni / Co is It is preferably 0.7 or more and 1.5 or less.
  • Ni / Co satisfies 0.7 or more and 1.5 or less, a decrease in wettability can be reduced and high toughness can be maintained, and a decrease in hardness can be reduced and high strength can be maintained.
  • Ni / Co is 0.8 or more and 1.2 or less.
  • Ni / Co can be adjusted, for example, by adjusting the amount of Co powder or Ni powder added to the raw material.
  • the cermet of the present invention may contain molybdenum (Mo).
  • Mo molybdenum
  • the second hard phase tends to be formed particularly easily. Therefore, since the wettability between the hard phase and the binder phase can be improved, the binder phase can sufficiently exist around the particles constituting the hard phase, and the toughness can be improved.
  • the Mo content is preferably 0.01% by mass or more and 2.0% by mass or less. When the Mo content is 0.01% by mass or more, as described above, the cermet as a whole can improve the wettability and improve the hardness and toughness. By setting the content to 2.0% by mass or less, the first hard phase is formed. It can be suppressed that the second hard phase and the third hard phase are relatively increased.
  • a more preferable content of Mo is 0.5% by mass or more and 1.5% by mass or less. It does not have to contain Mo.
  • cermet tool "Base material"
  • the cermet of the present invention having the above-described configuration is excellent not only in wear resistance but also in chipping resistance and welding resistance by providing the four hard phases as described above, and a good finished surface is desired. It can be suitably used as a base material for a cutting tool (cermet tool).
  • the base material may include a hard film coated on at least a part of its surface.
  • the hard film is preferably provided at least at the blade edge and in the vicinity thereof, and may be provided over the entire surface of the substrate.
  • the hard film may be a single layer or multiple layers, and the total thickness is preferably 1 to 20 ⁇ m.
  • a chemical vapor deposition method such as a thermal CVD method (CVD method) or a physical vapor deposition method such as an arc ion plating method (PVD method) can be used.
  • the composition of the hard film is one or more elements selected from the group consisting of metals of Groups 4, 5, 6 of the periodic table, aluminum (Al), and silicon (Si), carbon (C), nitrogen (N ), Oxygen (O) and boron (B) selected from the group consisting of one or more elements, that is, carbides, nitrides, oxides, borides, and solid solutions of elements such as the above metals 1 or more selected from the group consisting of a compound consisting of: cubic boron nitride (cBN), diamond, and diamond-like carbon (DLC).
  • Specific film quality includes Ti (C, N), Al 2 O 3 , (Ti, Al) N, TiN, TiC, (Al, Cr) N and the like.
  • the cermet is generally produced by a process of raw material preparation-raw material crushing and mixing-molding-sintering.
  • the cermet of the present invention can be produced by using the raw material powder described later and adjusting the grinding and mixing time and sintering conditions.
  • the raw material includes a compound powder comprising a compound of at least one metal selected from Group 4, 5, 6 metals of the periodic table and at least one element of carbon (C) and nitrogen (N), and a binder phase.
  • a binder phase typically an iron group metal powder.
  • Ti (C, N) powder is used.
  • Some Ti (C, N) powders are conventionally produced using sponge Ti as a starting material.
  • fine particles 1 It tends to form a hard phase.
  • the compound powder containing Mo is used together as described above, the second hard phase tends to be easily formed.
  • a powder containing W for example, a WC powder is used.
  • a compound powder containing Ti and Group 4, 5, 6 metals excluding Ti for example, (Ti, W) (C, N) powder is used.
  • particles of the fourth hard phase that is, particles having a single phase structure in which Ti and Group 4, 5, and 6 metals excluding Ti are uniformly dissolved are obtained. easy.
  • a preferable grinding and mixing time is 12 hours or more and 36 hours or less.
  • the sintering temperature is preferably 1400 ° C. or higher and 1600 ° C. or lower.
  • the sintering step when cooling the heated compact while maintaining the sintering temperature for a predetermined time, it is preferable to cool in a vacuum or an inert gas atmosphere such as argon (Ar). In the case of an inert gas atmosphere, a relatively low pressure of 665 Pa or more and 6650 Pa or less is particularly preferable. Further, when the cooling rate is increased, specifically, 10 ° C./min or more, the fourth hard phase tends to be easily generated.
  • the coated cermet tool of the present invention is excellent in wear resistance and chipping resistance, and can be cut with excellent work surface quality.
  • the cermet of the present invention can be suitably used as a constituent material for such a tool.
  • FIG. 1 is an explanatory view schematically showing four types of hard phases present in the cermet of the present invention.
  • ⁇ Test example> A cutting tool made of cermet was prepared, and the composition, structure, and cutting performance of the cutting tool were examined.
  • the cutting tool was produced as follows. First, the following were prepared as raw material powder.
  • This Ti (C, N) powder is a powder produced using TiO 2 as a starting material and has a C / N ratio of 1/1.
  • These Ti (C, N) powders all use sponge Ti as a starting material.
  • the produced powder has a C / N ratio of 1/1.
  • these Ti (C, N) powders are described as “s-TiCN”.
  • Each molded body obtained was heated to 450 ° C. to remove paraffin, then heated from room temperature to 1250 ° C. in a vacuum, and then sintered (including the cooling step) under the conditions shown in Table 3. A sintered body was obtained.
  • the arbitrary cross section was taken about each of each obtained sintered compact, and the cross section was magnified 5000 times and observed with the scanning electron microscope (SEM).
  • SEM scanning electron microscope
  • first hard phase 1 black single particles
  • second hard phase 2 black core double particles
  • third Four types of particles, hard phase 3 white core double particles
  • gray particles fourth hard phase 4
  • the first hard phase 1 is composed of only black particles, and the one part of the black particles is covered with a gray region (peripheral part 1b)
  • the second hard phase 2 is the core part 2a Is black
  • the peripheral part 2b is gray
  • the third hard phase 3 appears that the core part 3a is white and the peripheral part 3b is gray.
  • the sintered bodies of Sample Nos. 100 to 105 at least one of black single particles, black core double particles, white core double particles, and gray particles was not observed.
  • the black single particle was Ti (C, N)
  • the core part of the black core double particle was Ti (C, N)
  • the peripheral part covering the core part was Composite carbonitride solid solution containing Ti and one or more metals of W, Nb, Ta and Mo
  • white core double particle is a composite containing Ti and W and one or more metals of Nb, Ta and Mo
  • gray particles are composite carbon containing Ti, W and one or more metals of Nb, Ta, and Mo It was composed of a nitride solid solution.
  • the gray particles did not show a clear boundary between the core and the peripheral part.
  • the component analysis of the hard phase can be performed using EPMA, fluorescent X-ray, ICP-AES, etc. in addition to TEM-EDX analysis.
  • the particle size was determined for all particles present in the observation field of each sample (sintered body).
  • the particle diameter was defined as the Martin diameter (the length of a line segment that bisects the projected area of the particle when the particle is projected onto a plane from a certain direction).
  • a micrograph obtained by observing a cross section of the sintered body was used, and the length of a line segment that bisects the area of the particles present in the micrograph was defined as the particle size.
  • the particle diameter of the cored structure particles was determined in a state including the peripheral portion. As a result, in all samples, particles having a particle size of more than 3 ⁇ m were hardly observed, and the hard phase was composed of particles having a particle size of substantially 3 ⁇ m or less.
  • the area of each particle was determined using the particle diameter (the above-mentioned Martin diameter) obtained from the cross-sectional observation image (5000 times).
  • the total area of the particles having a particle size of more than 1 ⁇ m and 3 ⁇ m or less (hereinafter, these total areas are respectively rough.
  • grain area (1) coarse grain area (2), coarse grain area (3), coarse grain area (4)
  • fine particle area (2) the total area of grains having a grain size of 1 ⁇ m or less for the first hard phase
  • the total of the coarse phase area (1), coarse grain area (2), coarse grain area (3), coarse grain area (4), fine grain area (1), and fine grain area (2) is the total area of the hard phase
  • Table 4 shows the total ratio of the coarse grain areas (1) to (4) with respect to the total area of the hard phase, that is, the coarse grain area ratio “coarse grains / total hard phase” (%).
  • the coarse area (1), coarse area (2), coarse area (3), coarse area (4), fine area (1), and fine area (2) with respect to the total area of the hard phase Table 4 shows the area ratio (%).
  • the area ratio of the coarse grain area (1) to the total area of the hard phase is S1
  • the area ratio of the coarse grain area (2) is S2
  • the area ratio of the coarse grain area (3) is S3, and the coarse grain area (4) area.
  • the rate was S4, and (S1 + S2), S1 / (S1 + S2), and S3 / (S3 + S4) at this time were determined. The results are shown in Table 4.
  • the fine particle area (1) is SS1 and the fine particle area (2) is SS2, it corresponds to the area of SS1 / (SS1 + SS2) and the entire cermet (hard phase + binder phase) (here, the field of view of the observed image)
  • the area ratio of the total area of the area of the third hard phase and the area of the fourth hard phase: (third + fourth) / (whole cermet) was obtained.
  • Table 4 Note that in any of the samples in which the third hard phase and the fourth hard phase existed, the particle diameters of the particles of the third hard phase and the particles of the fourth hard phase are generally more than 1 ⁇ m and the particle diameter is 1 ⁇ m or less. 3 hard phase particles and 4th hard phase particles were hardly observed.
  • each obtained sintered body was subjected to planar polishing treatment and blade edge treatment, respectively, to produce a cutting tip (cutting tool) with a breaker having a shape of CNMG120408.
  • Each of the obtained cutting tips was subjected to a cutting test (all turned) under the conditions shown in Table 5 below, and the wear resistance, fracture resistance, and surface roughness of the processed surface were examined. The results are shown in Table 6.
  • the surface roughness Ra was measured according to JIS B 0601 (2001).
  • sample Nos. 1 to 19 in which all of the first hard phase, the second hard phase, the third hard phase, and the fourth hard phase are present are any of the above four types. It can be seen that it is superior in wear resistance and chipping resistance as compared with Sample Nos. 100 to 105. In addition, it can be seen that Sample Nos. 1 to 19 have a small surface roughness Ra of the processed surface of the work material and a high surface quality of the processed surface.
  • sample Nos. 1 to 19 especially when the area ratio of coarse particles satisfies 60% or more and 90% or less, it tends to be more excellent in wear resistance and fracture resistance due to improved hardness and fracture toughness. I understand that there is. Samples Nos. 1 to 19 that satisfy (S1 + S2) in the range of 0.1 to 0.5, or samples that satisfy S1 / (S1 + S2) in the range of 0.1 to 0.4 and S3 / (S3 + S4) in the range of 0.4 to 0.9. It can be seen that the surface roughness Ra tends to be further reduced and the surface quality is excellent. It can be seen that among samples Nos.
  • composition and average particle diameter of the raw material powder, the presence state of each particle of the hard phase, and the composition and thickness of the hard film can be appropriately changed.
  • the cermet of the present invention can be suitably used as a material for a cutting tool.
  • the coated cermet tool of the present invention can be suitably used for turning, milling, particularly steel cutting.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Powder Metallurgy (AREA)

Abstract

La présente invention concerne un cermet apte à être utilisé comme matériau pour outils de coupe présentant une excellente résistance à l'ébréchure et avec lequel des pièces peuvent être coupées pour l'obtention de surfaces de coupe présentant une excellente qualité ; ainsi qu'un outil en cermet revêtu. Le cermet comporte des phases dures constituées de composés tels que des carbonitrures de métaux des groupes 4, 5, et 6 du tableau périodique et une phase liante comprenant un métal de la famille du fer en tant que constituant principal, les phases dures ayant été liées les unes aux autres par la phase liante. Les phases dures comportent quatre types de particules de structure et composition différentes. Ce cermet présente donc non seulement une résistance élevée à l'usure mais également une excellente résistance à l'ébréchure et une excellente résistance au soudage et permet d'obtenir des surfaces de coupe de bonne qualité. La première phase dure (1) est constituée de particules à phase unique de Ti(C,N) ; la seconde phase dure (2) est constituée de particules à noyau comprenant chacune une partie noyau (2a) constituée de Ti(C,N) et d'une partie périphérique (2b) recouvrant l'ensemble de la partie noyau (2a) ; la troisième phase dure (3) est constituée de particules à noyau qui comportent une solution solide d'un carbonitrure composite contenant Ti et W et dans laquelle une partie noyau (3a) présente une concentration en W supérieure à la partie périphérique (3b) ; et la quatrième phase dure (4) est constituée de particules à phase unique comportant une solution solide d'un carbonitrure composite contenant Ti.
PCT/JP2010/054778 2009-03-24 2010-03-19 Cermet WO2010110197A1 (fr)

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JP2013014792A (ja) * 2011-06-30 2013-01-24 Sumitomo Electric Ind Ltd 硬質材料とその製造方法、並びに切削工具
US20130264373A1 (en) * 2010-12-22 2013-10-10 Sumitomo Electric Industries, Ltd. Rotary tool
US20130284793A1 (en) * 2010-12-22 2013-10-31 Sumitomo Electric Industries, Ltd. Rotary tool
CN106216662A (zh) * 2016-09-18 2016-12-14 广东工业大学 一种金属陶瓷颗粒及其制备方法与应用
CN106216663A (zh) * 2016-09-18 2016-12-14 广东工业大学 一种金属陶瓷颗粒及其制备方法应用

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CN102839311B (zh) * 2012-08-29 2014-07-16 成都美奢锐新材料有限公司 金属陶瓷及金属陶瓷的制备方法
CN102796932B (zh) * 2012-08-29 2014-04-09 成都美奢锐新材料有限公司 用于制备金属陶瓷的粉末颗粒及金属陶瓷的制备方法
CN102943195A (zh) * 2012-11-12 2013-02-27 成都美奢锐新材料有限公司 含纳米立方氮化硼的金属陶瓷及其制备方法
JP5885791B2 (ja) * 2013-08-20 2016-03-15 Ｊｘ金属株式会社 表面処理銅箔及びそれを用いた積層板、キャリア付銅箔、銅箔、プリント配線板、電子機器、電子機器の製造方法、並びに、プリント配線板の製造方法
US10208365B2 (en) 2014-03-19 2019-02-19 Tungaloy Corporation Cermet tool
CN104018017B (zh) * 2014-05-27 2016-02-24 南京航空航天大学 废旧Ti(C,N)基金属陶瓷材料的回收与再生方法
DE112015005350T5 (de) * 2014-11-27 2017-08-10 Kyocera Corporation Cermet und Schneidwerkzeug
CN104498938A (zh) * 2014-12-02 2015-04-08 佛山铭乾科技有限公司 一种金属陶瓷膜
JP6439975B2 (ja) * 2015-01-16 2018-12-19 住友電気工業株式会社 サーメットの製造方法
EP3372701A4 (fr) * 2015-11-02 2019-04-24 Sumitomo Electric Industries, Ltd. Alliage dur, et outil de coupe
CN106001550B (zh) * 2016-06-03 2018-10-19 广东工业大学 一种以TiC-Ni-Mo2C合金为耐磨相的耐磨金属陶瓷及其制备方法与应用
CN105970061A (zh) * 2016-06-23 2016-09-28 王莹 一种高强度碳化物基金属陶瓷衬板及其制备方法
KR101963655B1 (ko) 2017-06-12 2019-04-01 주식회사 웨어솔루션 써멧 분말조성물 및 이를 이용한 써멧 및 써멧 라이닝 플레이트
CN113025861A (zh) * 2021-03-08 2021-06-25 昆山长鹰硬质材料科技股份有限公司 一种混晶Ti（C,N）基金属陶瓷材料及其制备方法
CN116162838B (zh) * 2023-04-26 2023-06-30 崇义章源钨业股份有限公司 一种金属陶瓷及其制备方法

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US20130264373A1 (en) * 2010-12-22 2013-10-10 Sumitomo Electric Industries, Ltd. Rotary tool
US20130284793A1 (en) * 2010-12-22 2013-10-31 Sumitomo Electric Industries, Ltd. Rotary tool
US8936186B2 (en) * 2010-12-22 2015-01-20 Sumitomo Electric Industries, Ltd. Rotary tool
US8998062B2 (en) * 2010-12-22 2015-04-07 Sumitomo Electric Industries, Ltd. Rotary tool
JP2013014792A (ja) * 2011-06-30 2013-01-24 Sumitomo Electric Ind Ltd 硬質材料とその製造方法、並びに切削工具
CN106216662A (zh) * 2016-09-18 2016-12-14 广东工业大学 一种金属陶瓷颗粒及其制备方法与应用
CN106216663A (zh) * 2016-09-18 2016-12-14 广东工业大学 一种金属陶瓷颗粒及其制备方法应用

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KR20100135941A (ko) 2010-12-27
JP4690475B2 (ja) 2011-06-01
SE1051204A1 (sv) 2011-02-08
CN102046823B (zh) 2013-02-13
JP2010222650A (ja) 2010-10-07
TW201042054A (en) 2010-12-01
CN102046823A (zh) 2011-05-04
TWI457445B (zh) 2014-10-21
SE536731C2 (sv) 2014-07-01

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