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    • 专利摘要:
    28 ABSTRACTThere is provided a cerrnet suitable as a component for a cutting tool having excellent resistance to fracture and being capable of cutting a Workpiece so as to form a hi gh-quality machined surface of the workpiece, and a coated cermet tool. The cermetincludes hard phases composed of a compound, such as a carbonitride of a metal selectedfrom metals in groups 4, 5, and 6 of the periodic table, and a binder phase mainlycomposed of an iron group metal, the hard phases being bonded to each other With thebinder phase. The cerrnet includes the hard phases formed of four types of grains havingdifferent compositions and rnorphologies; hence, the cemiet has high wear resistance, isexcellent in terms of resistance to fracture and Welding resistance, and providessatisfactory quality of a machined surface. A first hard phase l is formed of grains havinga single phase composed of Ti(C,N). The second hard phase 2 is forrned of grains havinga core-rim structure including a core Za composed of Ti(C,N) and a rim 2b that entirelycovers the core 2a. The third hard phase 3 is formed of grains having a core-rim structureWhich includes a core and a rim and Which is cornposed of a complex carbonitride solidsolution containing Ti and W, the core 3a having a higher W concentration than that in therim Bb. The fourth hard phase 4 is formed of grains having a single phase composed of a complex carbonitride solid solution containing Ti.
    公开号:SE1051204A1
    申请号:SE1051204
    申请日:2010-03-19
    公开日:2011-02-08
    发明作者:Kazuhiro Hirose；Hideki Moriguchi；Keiichi Tsuda
    申请人:
    IPC主号:
    专利说明:

    [5] Known cermets including hard phases formed of grains having a single-phase structure that does not have a rim have low wettability with a binder phase and thus have inferior resistance to fracture.
    [6] [0006] For known cermets including hard phases formed of grains having a core-rim structure, cracks propagate easily along boundaries between cores and rirns, thus reducing the resistance to fracture. In particular, when cores are fi ne, it is difficult to inhibit the propagation of cracks and thus to improve the resistance to fracture.
    [7] Accordingly, it is an object of the present invention to provide a cermet which has excellent resistance to fracture and which is suitable as a material for a cutting tool capable of cutting a workpiece so as to form a high-quality machined surface of the workpiece. It is another object of the present invention to provide a coated cermet tool containing a substrate composed of the cermet.
    [8] [0008] The inventors have found that in the case Where a hard phase is present in a cermet in a specific range and Where four types of grains having different compositions and morphologies are present as grains constituting the hard phase, the cermet has high wear resistance and significantly improved resistance to fracture and welding resistance.
    [9] [0009] A cermet of the present invention includes hard phases composed of one or more compounds selected from the group consisting of earbides, nitrides, carbonitrides, and solid solutions of metals in groups 4, 5, and 6 of the periodic table, and a binder phase mainly composed of an iron group element, the hard phases being bonded to each other with the binder phase. The cermet contains 70% by mass to 97% by mass of the hard 'phases and the remainder being substantially formed of the binder phase. Furthermore, the hard phases of the cermet include a first hard phase, a second hard phase, a third hard phase, and a fourth hard phase described below.
    [10] [0010] In the cerrnet of the present invention, the incorporation of a specific amount of the hard phases and the coexistence of the first hard phase, the second hard phase, the third hard phase, and the fourth hard phase servings as the hard phases enables the cerniet to have the functions of the first hard phase to the fourth hard phase. Speci fi cally, for the cermet of the present invention, the presence of the high-hardness hard phase results in excellent wear resistance. Furthermore, the presence of the hard phase having excellent wettability with the binder phase allows the cermet to maintain satisfactory Wettability with the binder phase and to have microstructures in which the binder phase is uniformly present. The uniformization of the microstructures improves the wear resistance and the resistance to fracture. Moreover, for the cermet of the present invention, the presence of the hard phase having excellent thermal properties improves the thermal conductivity, thereby inhibiting thermal cracking and improving the welding resistance. As described above, the cermet of the present invention has excellent wear resistance and improves the resistance to fracture and the welding resistance. Thus, a cutting tool composed of the cermet of the present invention is not easily worn or fractured, stabilizing and extending the tool life. Furthermore, satisfactory welding resistance makes it possible to provide a fine machined surface, improving the quality of the machined surface of a workpiece.
    [11] [0011] <> The cermet of the present invention contains 70% by mass to 97% by mass of the hard phases and the remainder being substantially formed of the binder phase and incidental impurities. Examples of the incidental impurities include oxygen and metal elements in a concentration on the order of parts per million contained in raw materials and mixed in the production process.
    [12] [0012] <> [Composition] Each of the hard phases contains a compound of at least one metal element selected from metals in groups 4, 5, and 6 of the periodic table and at least one element selected from carbon (C) and nitrogen (N). In other words, each of the hard phases contains at least one selected from carbides, nitrides, carbonitrides, and solid solutions of the metal elements described above. In particular, the cermet of the present invention is a Ti (C, N) - based cermet containing at least a carbonitride solid solution that contains a titanium carbonitride (Ti (C, N)) and titanium (Ti). lf the proportion of the hard phases exceeds 97% by mass, the resistance to fracture is significantly reduced due to an excessively low binder phase content. If the proportion of the hard phases is less than 70% by mass, the hardness is significantly reduced due to an excessively high binder phase content, thereby reducing the wear resistance. The proportion of the hard phases is more preferably in the range of 80% by mass to 90% by mass.
    [13] [0013] The hard phases include four types of hard phases: the first hard phase, the second hard phase, the third hard phase, and the fourth hard phase, which have different compositions and morphologies. Specifically, the hard phases include a Ti (C, N) -based hard phase, a Ti-containing hard phase having another composition, a hard phase having a single-phase structure, and a hard phase having a core-rim structure. The present states of the four types of hard phases described above can be easily discriminated by the light and shade of a photomicrograph taken with a scanning electron microscope (SBM).
    [14] [0014] (First Hard Phase) The first hard phase is formed of grains having a single-phase structure substantially composed of Ti (C, N) alone or is formed of grains in Which Ti (C, N) is partially covered With a complex carbonitride solid solution containing Ti and one or more metals selected from metals, other than Ti, in groups 4, 5, and 6 of the periodic table, ie, in which Ti (C, N) is not entirely covered with the complex carbonitride solid solution. The first hard phase has a high Ti content compared to the third hard phase and the fourth hard phase described below, so that the first hard phase has high hardness and low reactivity with steel generally used for a workpiece. Thus, the presence of the first hard phase in the cermet particularly results in improvement in wear resistance and welding resistance.
    [15] [0015] (Second Hard Phase) The second hard phase is formed of grains having a core-rim structure including a core and a rim that entirely covers the core, the core being substantially composed of Ti (C, N) (Ti (C) , N) accounts for 95% or more, in atomic percent, of the entire core), and the rim that entirely covers the core being composed of a complex carbonitride solid solution containing Ti and at least one metal selected from metals, other than Ti , in groups 4, 5, and 6 of the periodic table. Specific examples of the composition of the rim include (Ti, W, Mo) (C, N), (Ti, W, Nb) (C, N), (Ti, W, Mo, Nb) (C, N), and (Ti, W, Mo, Nb, Zr) (C, N).
    [16] [0016] (Third Hard Phase) The third hard phase is formed of grains having a core-rim structure that includes a core and a rim Which contain the same elements and which are composed of complex carbonitride solid solutions containing at least titanium and tungsten. Furthermore, the core of the grains has a higher tungsten concentration than that in the rim. Specific examples of the composition include (Ti, W) (C, N), (Ti, W, Mo) (C, N), (Ti, W, Nb) (C, N), and (Ti, W, Mo , Nb) (C, N). The third hard phase has a higher W content than those of the first hard phase and the second hard phase and thus has improved thermal conductivity With the high hardness maintained. This improves the thermostability, the heat crack resistance properties, the resistance to fracture, and the resistance to plastic deformation. [001 7] (Fourth Hard Phase) The fourth hard phase is formed of grains having a single-phase structure composed of a complex carbonitride solid solution containing Ti and at least one metal selected from metals, other than Ti, in groups 4, 5 , and 6 of the periodic table. Unlike the third hard phase, the grains do not have a distinct boundary between a core and a rim. All the grains have a uniform composition. A typical example of a metal other than Ti contained in the fourth hard phase is W. Specific examples of the composition of the fourth hard phase include (Ti, W) (C, N), (Ti, W, Mo) (C, N), (Ti, W, Nb) (C, N), and (Ti, W, Mo, Nb) (C, N). ln particular, in the case where the fourth hard phase contains W, unlike the third hard phase, the concentration of W is not significantly changed (W is not localized), i.e., W is uniformly distributed throughout the fourth hard phase. Thus, the presence of the fourth hard phase in the cermet results in only a slight reduction in hardness but results in uniform hardness, so that crack propagation does not easily occur in the hard phases. Furthermore, the coefficient of thermal conductivity is increased, thus leading to improvements in heat crack resistance properties and resistance to fracture.
    [18] [0018] In the case Where the hard phases are substantially constituted by only the first hard phase and the second hard phase, it is difficult to improve the resistance to fracture. In the case Where the hard phases are substantially constituted by only the first hard phase and the third hard phase, pores are liable to be formed due to poor Wettability with the binder phase, thus leading to low resistance to fracture. In the case where the hard phases are substantially constituted by only the first hard phase and the fourth hard phase, pores are also liable to be formed due to poor wettability with the binder phase, thus leading to insufficient hardness and low resistance to fracture.
    [19] [0019] In the case where the hard phases are substantially constituted by only the second hard phase and the third hard phase, it is difficult to inhibit the propagation of cracks along boundaries between cores and rims, which is a problem in the related art, so that desired resistance to fracture is not provided. In the case where the hard phases are substantially constituted by only the second hard phase and the fourth hard phase, the resistance to fracture is not improved.
    [20] [0020] In the case where the hard phases are substantially constituted by the first hard phase, the second hard phase, and the third hard phase and do not contain the fourth hard phase, the proportion of the third hard phase containing W is relatively increased . A high W content is liable to cause the reaction of W With a workpiece (in particular, steel) during cutting. Thus, welding occurs easily, leading to the deterioration of a machined surface of the workpiece. That is, the presence of the fourth hard phase in addition to the first hard phase, the second hard phase, and the third hard phase results in excellent quality (glossiness) of a machined surface of a workpiece and makes it possible to stably maintain the excellent quality.
    [21] [0021] In the case where the hard phases are substantially constituted by the first hard phase, the second hard phase, and the fourth hard phase and do not contain the third hard phase, although the coefficient of therrnal conductivity is increased, the hardness is reduced. This is liable to cause the propagation of cracks, thus leading to a high incidence of fracture. That is, the presence of the third hard phase in addition to the first hard phase, the second hard phase, and the fourth hard phase results in a further increase in the coefficient of therrnal conductivity to inhibit therrnal cracking and the propagation of cracks, thus effectively improving the resistance to fracture.
    [22] [0022] In the case Where the hard phases are substantially constituted by the second hard phase, the third hard phase, and the fourth hard phase and do not contain the first hard phase, it is difficult to obtain the effect of improving the Wear resistance and the Welding resistance, which is the effect resulting from the presence of the first hard phase. In particular, a machined surface of a workpiece has low glossiness.
    [23] [0023] In the case where the hard phases are substantially constituted by the first hard phase, the third hard phase, and the fourth hard phase and do not contain the second hard phase, in other words, in the case Where a Ti (C , N) -based hard phase, which is a main component of the hard phases in the cermet, is the fi rst hard phase alone, the wettability With the binder phase is extremely degraded to easily form pores as described above, thus leading to the deterioration in mechanical properties.
    [24] [0024] ln the cermet of the present invention, the coexistence of, in particular, the third hard phase and the fourth hard phase in addition to the first hard phase and the second hard phase results in the inhibition of the reaction With steel With therrnostability maintained.
    [25] [0025] [Grain Size] The hard phases are preferably formed of a mixture of coarse grains and fine grains, in particular, formed of fine grains each having a size of l um or less and coarse grains each having a size of more than l um and 3 um or less. Furthermore, with respect to the total area of the hard phases, 60% to 90% of the hard phases are formed of the coarse grains, and the remainder of the hard phases are formed of the fi ne grains. Moreover, preferably, the coarse grains are formed of the first hard phase, the second hard phase, the third hard phase, and fourth hard phase, and the fine grains are substantially formed of the first hard phase and the second hard phase.
    [26] [0026] For such microstructures formed of the grains with different sizes, the fine grains are present so as to fill gaps between the coarse grains, irnproving the hardness and the fracture toughness. Since each of the coarse grains has a size exceeding 1 pm and each of the fine grains has a size of l pm or less, sufficiently large gaps are provided between the coarse grains, so that the fine grains can be present in the gaps. As a result, the effects of improving the hardness and the fracture toughness described above are provided.
    [27] The area proportion of the coarse grains is 60% or more. That is, an appropriate amount of the coarse grains is present, thus sufficiently providing the effect of inhibiting the propagation of cracks and enhaneing the toughness. Furthermore, the area proportion of the coarse grains is 90% or less. Thus, the fine grains are suf fi ciently present in gaps between the coarse grains, improvirig the hardness and inhibiting the propagation of cracks.
    [28] [0028] The size and area proportions of the grains constituting the hard phases are adjusted by, for example, adjusting the size and amounts of raw material powders added and production conditions (eg, grinding time and sintering conditions). A longer grinding time tends to lead to finer grains constituting the hard phases in the cennet. A higher sintering temperature tends to lead to coarser grains constituting the hard phases in the 10 cermet. Even if the grinding time is prolonged to form a powder ner powder, a higher sintering temperature may result in grain growth to form coarse grains constituting the hard phases.
    [29] [0029] With respect to the total area of the hard phases, in the case that the area proportion of the first hard phase having a grain size of more than 1 um and 3 pm or less (coarse grains) is denoted by S1 and the area proportion of the second hard phase having a grain size of more than l um and 3 um or less (coarse grains) is denoted by S2, (S1 + S2) is preferably in the range of 0.1 to 0.5. In the case Where (S1 + S2) is 0.1 or more, welding of the cermet to a Workpiece does not occur easily. This inhibits the occurrence of a minute tear on a surface of a workpiece, improving the quality of an inachined surface of the workpiece. Furthermore, improvement in welding resistance results in a reduction in Wear, improving the Wear resistance of tools. In the case where (S1 + S2) is 0.5 or less, a reduction in toughness due to an increase in hardness is inhibited, so that fracture and chipping are less prone to occur. More preferably, (S1 + S2) is in the range of 0.3 to 0.5. [003 0] In the case that the area proportion of the third hard phase having a grain size of more than 1 pm and 3 um or less (coarse grains) is denoted by S3 and the area proportion of the fourth hard phase having a grain size of more than 1 pm and 3 um or less (coarse grains) is denoted by S4, When Sl / (Sl + S2) is in the range of 0.1 to 0.4 and S3 / (S3 + S4) is in the range of 0.4 to 0.9, a better balance between Wear resistance and resistance to fracture is provided. Furthermore, the surface gloss of a workpiece is further improved.
    [32] [0032] The proportion of the total area of the third hard phase and the fourth hard phase is preferably more than 40% With respect to the total area (hard phases + binder phase) of the cermet. In this case, stable thermal properties are obtained, improving the resistance to thermal cracking and resistance to fracture. In particular, most of the third and fourth hard phases are preferably formed of coarse grains. [003 3] <> The binder phase is composed of at least one metal, serving as a main component, selected from iron group elements of cobalt (Co), iron (Fe), and nickel (Ni). In the case where the binder phase consists substantially of one or more metals selected from the iron group metals described above, the one or more metals are defined as the "main component".
    [34] [0034] In the case Where the binder phase contains both Ni and Co, in particular, in the case Where the mass ratio of Ni to Co present in the binder phase (the ratio of the mass of Ni to the mass of Co) is denoted by Ni / Co, Ni / Co is preferably .in the range of 0.7 to 1.5.
    [39] [0039] Cermets are typically produced through the steps of the preparation of raw materials, the grinding and mixing of the raw materials, molding, and sintering. The cermet of the present invention can be produced by using raw material powders described below and adjusting the grinding and mixing time and sintering conditions.
    [40] [0040] <> A powder of a compound of at least one metal selected from metals in groups 4, 5, and 6 of the periodic table with at least one element selected from carbon (C) and nitrogen (N), and a powder , typically an iron group metal powder, to be formed into the binder phase are used as raw materials. The use of a fine powder and a relatively coarse powder as these powders has a tendency to lead to the cermet having the hard phases formed of mixed grains of the coarse and fine grains, as described above. The particle size of the powders may be appropriately selected in view of the size of grains constituting the hard phases. [004l] To form the first hard phase and the second hard phase, for example, a Ti (C, N) powder is used. Regarding the Ti (C, N) powder, hitherto, Ti (C, N) powders have been produced from sponge Ti serving as a starting material. ln particular, the use of a Ti (C, N) l4 powder produced from TiOZ serving as a starting material has a tendency to form the fine first hard phase. Furthermore, as described above, the additional use of a Mo-containing compound powder has a tendency to form the second hard phase. To form the third hard phase, a W-containing powder, such as a WC powder, is used. To form the fourth hard phase, a powder of a compound containing Ti and a metal selected from metals, other than Ti, in groups 4, 5, and 6 of the periodic table, for example, a (Ti, W) (C, N) powder, is used.
    [42] [0042] <> A longer grinding time results in a fi ner powder and has a tendency to form the fine hard-phase grains in the cermet. However, an excessively long grinding time can cause reaggregation or dif fi culty in forrning a compound serving as a nucleus because of excessively small size. The grinding and mixing time is preferably in the range of 12 hours to 36 hours.
    [43] [0043] <> An excessively high sintering temperature can cause the growth of grains constituting the hard phases, which is liable to lead to a large number of coarse grains in the cermet. In particular, an excessively high sintering temperature can cause difficulty in forming grains constituting the fourth hard phase. Thus, the sintering temperature is preferably in the range of 140 ° C to 1600 ° C. Furthermore, in the sintering step, a molded article that has been heated for a predetermined time is preferably cooled in vacuum or an inert gas atmosphere, such as argon (Ar). In the case of the inert gas atmosphere, in particular, a relatively low pressure of 665 Pa to 6650 Pa is preferably used. In addition, a higher cooling rate of, for example, 10 ° C / min or more has a tendency to form the fourth hard phase.
    [44] [0044] A coated cermet tool of the present invention has excellent wear resistance and resistance to fracture and is capable of cutting a workpiece so as to form a high-quality machined surface of the workpiece. A cermet of the present invention is suitably usable as a component of the tool.
    [45] [Fig. 1] Fig. 1 is a schematic explanatory drawing of four types of hard phases present in a cermet of the present invention.
    [46] A cutting tool composed of a cermet was produced. The composition and microstructures of the cermet and the cutting performance of the cutting tool were investigated.
    [47] [0047] The cutting tool was produced as follows. Raw material powders described below Were prepared. (1) Ti (C, N) powder with average particle size of 0.7 um A Ti (C, N) powder is a powder produced from TiOg as a starting material. The C / N ratio is 1 / 1. (2) Ti (C, N) powder with average particle size of 0.8 um and Ti (C, N) powder with average particle size of 3.0 um Each of the Ti (C, N ) powders is a powder produced from sponge Ti serving as a starting material. The C / N ratio is l / l. In Table I, these Ti (C, N) powders are expressed as "s-TiCN". (3) (Ti, W) (C, N) powder with average particle size of 2.8 um A (Ti, W) (C, N) powder is a powder in which a Ti (C, N) powder forrns a solid solution with W. The C / N ratio is l / l. (4) WC powder, NbC powder, TaC powder, MozC powder, Ni powder, and Co powder with average particle size of 0.5 to 3.0 um These powders are cornmercially available.
    [48] [Table I] Compositions of raw material powder (% by mass) i 1 10 10 20 25 10 10 0 1 7 7 2 20 20 10 15 10 10 0 1 6 8 3 10 5 20 20 20 10 0 1 7 7 4 20 15 10 10 20 10 0 1 6 8 5 10 5, 15 20 25 10 0 1 7 7 6 20 15 5 10 25 10 0 1 8 0 7 0 30 10 15 20 10 0 1 7 7 ~ 8 10 10 20 25 10 5 5 1 7 7 9 20 10 0 25 20 10 0 1 7 7 10 20 20 25 0 10 10 0 1 7 7 11 20 10 15 30 0 10 0 1 7 7 12 0 10 25 40 0 10 0 1 7 7
    [49] [0049] The prepared powders were charged into a Stainless-steel pot together With an acetone solvent and cemented carbide balls. The rnixture was ground and mixed (wet process). Table II shows raw material powders used to produce samples and grinding and mixing time (hour). After grinding and mixing, the mixture was dried to provide a mixed powder. A small amount of paraffin was added to the resulting mixed powder. Press forming was performed with a mold at 98 MPa to produce a molded compact with the geometry CNMG 120408.
    [50] [0050] 17 [Tabie 111 Sam le Powder Gfindi fi šä fi d '' '. content Now Now (goiüirglg time šdzïdïietrilonšs Nl / CO by mass) 1 6 36 B 0. 73 0. 94 2 I 6 24 B 0. 72 0. 94 3 i 2 12 Å l. 31 0. 93 4 2 i 12 C 1. 29 0. 93 6 1 24 Å 0. 96 0. 94 6 3 24 Å 0. 96 0. 95 7 4 36 Å 1. 34 0. 93 8 8 24 C 0. 96 0. 92 9 3 36 C 0. 96 0. 94 10 05 36 Å 0. 97 0. 93 11 4 36 C 1. 29 0. 93 12 4 36 B 1. 29 0. 93 13 5 24 Å 0. 96 0. 94 14 2 36 Å 1. 29 0. 94 15 6 36 C 0. 96 0. 93 16 2 24 B 0. 97 0. 93 17 6 12 C 0. 74 0. 93 18 6 36 Å 0. 72 0. 96 19 9 36 B 0. 97 0. 93 100 7 12 C 0. 96 0. 93 101 9 36 Å 0. 96 0. 92 102 ll 36 B 0. 97 - 0. 93 103 10 12 Ål 0. 96 0. 93 104 12 36 Å 0. 96 0. 94 105 10 36 Å 0. 97 0. 94
    [51] After each of the molded compacts was heated to 450 ° C to remove paraffin, the resulting cornpacts were heated from room temperature to 1250 ° C in vacuum. The subsequent sintering (including a Cooling step) was performed under conditions shown in Table III to form a sintered compact.
    [52] [Table III] 18 Sintering conditions _ Sintering Holding.
    [53] Any section of each of the resulting sintered compacts was formed. The section was observed With a scanning electron microscope (SEM) at a magnification of> <5000.
    [54] TEM-EDX analysis of compositions of the grains described above showed that the single black grain was composed of Ti (C, N); in the black-core double grain, the core was composed of Ti (C, N) and the rim covering the core was composed of a complex 19 carbonitride solid solution containing Ti and one or more metals selected from W, Nb, Ta, and Mo; in the white ~ core double grain was a complex carbonitride solid solution containing Ti and one or more metals selected from W, Nb, Ta, and Mo, and the core had a higher W concentration than that in the rim covering the core; and the gray grain was composed of a complex carbonitride solid solution Ti and one or more metals selected from W, Nb, Ta, and Mo. Furthermore, the gray grain did not have a distinct boundary between a core and a rim. The components of the hard phases can be analyzed by, for example, EPMA, X-ray fluorescence analysis, ICP-AES as well as TEM-EDX analysis.
    [55] The binder phase was present between the grains. TEM-EDX analysis showed that the binder phase was substantially composed of Co and Ni. Among samples, some binder phases contained approximately several percent by mass of the constituent elements of the hard phases in the form of a solid solution. Analysis of the binder phase showed that the sintered compact had a Co content substantially equal to the amount of the raw material Co powder fed and that the Ni content of the sintered compact tended to be reduced by about 0.2% to about 03%, as compared with the amount of the raw material Ni powder fed. Thus, the hard phase content of each sample (sintered compact) is substantially equal to an amount (about 86% by mass) obtained by subtraction of the amounts of the Co powder and the Ni powder used as raw materials. Furthermore, the mass ratio of Ni to Co, i.e., Ni / Co, present in the binder phase was determined. Table II shows the results. Moreover, the Mo content (% by mass) of each sample (sintered compact) was investigated by ICP analysis. Table II also shows the results.
    [56] [0056] The size of all grains of each sample (sintered compact) present in the observation field of view was determined on the basis of the SEM observation images (> <5000) of the sections. The Martin's diameter (the length of a chord bisecting the projected area of a grain when the grain is projected onto a plane from a certain direction) was used as the grain size. Specifically, a photomicrograph of the section of each sintered compact was used, and the length of a chord bisecting the area of a grain present in the photomicrograph was defined as the grain size. Regarding a grain having a core-rim structure, the diameter of a region including the rim was defined as the grain size. The results demonstrated that in any sample, grains each having a size of more than 3 um were little observed and that 20 the hard phases Were substantially formed of the grains each having a size of 3 pm or less.
    [57] [0057] The area of each of the grains Was determined using the grain size (the Martins diameter described above) determined from the observation images (> <5000) of the sections.
    [58] [0058] [Table IV] 22 oo oo .o oo .o oo .o oo .oo .o oo o oo oo oo oo oo oo oo oo .o oo .o 8 .o oo .o oo oo o oo oo oo oo ooo oo oo. o oo .o oo .o oo .o oo o oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo .o oo oo o oo o oo oo. ooo oo oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo. o oo .o oo o oo o oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo .o oo o oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo o oo oo oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo o oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo o oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo .o oo .o oo .o oo .o oo oo oo oo oo oo oo oo oo oo oo oo. o oo .o oo .o oo .o oo oo oo o oo o oo o oo oo .o oo .o oo .o oo .o oo oo oo o oo o oo o oo o ooooon Éooo 23% oooošowowoooou ooooooo. ^ Loï_3om + wo_; ov oooooom oouoooo US oo uoooofoøo oo u oooošo mwmna wow; Ucoomw mwmcm nom; wwo fi mÉEmw oootâooo ä: š: oíoooooo ooå 23 [005 9] Surfaces of the resulting sintered compacts Were subj ected to surface grinding treatment and edging treatment, producing a cutting insert (cutting tool), provided With a breaker, with the geometry CNMG 120408 Cutting tests (turning tests in all cases) were performed with the resulting cutting inserts under conditions shown in Table V described below to evaluate the wear resistance, resistance to fracture, and the surface roughness of the machined surfaces. Table VI shows the results. measured according to JlS B 0601 (200l).
    [60] [0060] [Table v] The surface roughness Ra was Wear resistance test Fracture resistance test Workpiece I SCM435 Surface roughness test of machined surface Workpiece I SCM415 with four slot grooves Workpi ece 2 SCM415 Cutt i ne Speed: 300m / min Cuttingl sueecl I 250mIn / min Cutting speed I IOOmm / min Cut: 1.0mm Cut: 1. 5111111 cut: 1. Omni Feed I Û. l-Smm / Tev.
    [62] Table VI shows that samples 1 to 19 each including all of the first hard phase, the second hard phase, the third hard phase. and the fourth hard phase had excellent wear resistance and excellent resistance to fracture compared With samples 100 to 105 in which any one of the four types described above was absent. Furthermore, each of samples l to 19 provided a small surface roughness Ra and a high-quality machined surface of the xvorkpiece.
    [63] [0063] 25 Among samples 1 to 19, in particular, for samples having an area proportion of the coarse grains of 60% to 90%, the hardness and fracture toughness tend to be improved, further enhancing the Wear resistance and resistance to fracture. Furthermore, among samples 1 to 19, in particular, for samples in Which (S1 + S2) is in the range of 0.] to 0.5 and samples in Which Sl / (Sl + S2) is in the range of 0.1 to 0.4 and S3 / (S3 + S4) is in the range of 0.4 to 0.9, the surface roughness Ra tends to be further reduced, resulting in excellent surface quality. Among samples 1 to 19, in particular, samples in Which SSl / (SSl + SS2) is in the range of 0.5 to 0.9 tend to have further enhanced wear resistance.
    [64] (Ti, Al) N coatings (thickness: 4 pm) Were formed by an arc ion plating method on the surfaces of the cutting inserts of samples 1 to 19, forming coated inserts. The wear resistance test Was performed under test conditions shown in Table V. The results demonstrated that all samples had excellent Wear resistance compared with the samples Without the hard coatings.
    [65] The foregoing embodiments may be appropriately modified without departing from the scope of the present invention. The present invention is not limited to the configurations described above. For exarnple, the compositions and average particle size of the raw material powders, the present states of the grains of the hard phases, and the composition and thickness of the hard coating may be appropriately changed.
    [66] The cermet of the present invention is suitably usable as a material for a cutting tool.
    [67] [0067] l first hard phase, lb rim, 2 second hard phase, 2a, 3a core, 2b, 3b rim, 3 third hard phase, 4 fourth hard phase, 10 binder phase i
    权利要求:
    Claims (9)
    [1]
    1. l. A cermet comprising hard phases composed of one or more compounds selected from the group consisting of carbides, nitrides, carbonitrides, and solid solutions of metals in groups 4, S, and 6 of the periodic table; and a binder phase mainly composed of an iron group element, the hard phases being bonded to each other with the binder phase, the cermet containing 70% by mass to 97% by mass of the hard phases and the remainder being substantially formed of the binder phase, the hard phases including a first hard phase, a second hard phase, a third hard phase, and a fourth hard phase, Wherein the first hard phase is a hard phase Which has a single phase composed of only titanium carbonitride or Which has a single-phase structure in Which titanium carbonitride is partially covered With a complex carbonitride solid solution containing titanium and one or more metals selected from metals (provided that titanium is excluded) in groups 4, 5, and 6 of the periodic table, the second hard phase is a hard phase having a core-rim structure including a core and a rim that entirely covers the core, the core being composed of titanium carbonitride, and the rim being composed of a complex carbonitride solid soluti on containing titanium and one or more metals selected from metals (provided that titanium is excluded) in groups 4, 5, and 6 of the periodic table, the third hard phase is a hard phase having a core-rim structure that includes a core and a rim entirely covering the core, the core and the rim containing the same elements and being composed of complex carbonitride solid solutions containing at least titanium and tungsten, and the core having a higher tungsten concentration than the tungsten concentration in the rim, and the fourth hard phase is a hard phase having a single-phase structure composed of a complex carbonitride solid solution containing titanium and one or more metals selected from metals (provided that titanium is excluded) in groups 4, S, and 6 of the periodic table.
    [2]
    2. The cermet according to Claim 1, wherein With respect to the total area of the hard phases, 60% to 90% of the hard phases are formed of coarse grains each having a size of more than l um and 3 um or less, and the remainder of the hard phases are formed of fine grains each having a size of 1.0 um or less, Wherein the coarse grains are formed of the fi rst hard phase, the second hard phase, 27 the third hard phase, and fourth hard phase, and the fine grains are substantially formed of the first hard phase and the second hard phase.
    [3]
    3. The cermet according to Claim 2, Wherein With respect to the total area of the hard phases, in the case that the area proportion of the first hard phase formed of the coarse grains is denoted by S1 and the area proportion of the second hard phase formed of the coarse grains is denoted by S2, (S1 + S2) is in the range of 0.1 to 0.5.
    [4]
    4. The cermet according to Claim 2 or 3, Wherein with respect to the total area of the hard phases, in the case that the area proportion of the first hard phase formed of the coarse grains is denoted by S1, the area proportion of the second hard phase formed of the coarse grains is denoted by S2, the area proportion of the third hard phase formed of the coarse grains is denoted by S3, and the area proportion of the fourth hard phase formed of the coarse grains is denoted by S4, S1 / (S1 + S2) is in the range of 0.1 to 0.4, and S3 / (S3 + S4) is in the range of 0.4 to 0.9.
    [5]
    5. The cermet according to any one of Claims 2 to 4, Wherein, in the case that the area of the first hard phase having a grain size of 1.0 pm or less is denoted by SS1 and the area of the second hard phase having a grain size of 1.0 pm or less is denoted by SS2, SS1 / (SS1 + SS2) is in the range of 0.5 to 0.9.
    [6]
    6. The cermet according to any one of Claims 1 to 5, Wherein the proportion of the total area of the third hard phase and the fourth hard phase is more than 40% With respect to the total area of the cermet.
    [7]
    7. The cermet according to any one of Claims 1 to 6, Wherein the cermet contains nickel (Ni) and cobalt (Co) in the binder phase, and Wherein, in the case that the mass ratio of Ni to Co present in the binder phase is denoted by Ni / Co, Ni / Co is in the range of 0.7 to 1.5.
    [8]
    8. The cerrnet according to any one of Claims 1 to 7, Wherein the cermet contains 0.01% by mass to 2.0% by mass molybdenum.
    [9]
    9. A coated cennet tool cornprising a substrate composed of the cermet according to any one of Claims 1 to 8 and a hard coating that covers at least part of a surface of the substrate.
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    同族专利:
    公开号 | 公开日
    JP2010222650A|2010-10-07|
    TW201042054A|2010-12-01|
    SE536731C2|2014-07-01|
    CN102046823B|2013-02-13|
    KR20100135941A|2010-12-27|
    TWI457445B|2014-10-21|
    KR101253853B1|2013-04-12|
    JP4690475B2|2011-06-01|
    WO2010110197A1|2010-09-30|
    CN102046823A|2011-05-04|
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    法律状态:
    优先权:
    申请号 | 申请日 | 专利标题
    JP2009072102A|JP4690475B2|2009-03-24|2009-03-24|Cermet and coated cermet tools|
    PCT/JP2010/054778|WO2010110197A1|2009-03-24|2010-03-19|Cermet|
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