阅读说明：本技术 金属陶瓷、包括该金属陶瓷的切削工具及制造金属陶瓷的方法 (Cermet, cutting tool including the same, and method of manufacturing cermet ) 是由 道内真人 冈村克己 于 2018-05-15 设计创作，主要内容包括：一种金属陶瓷,包括：含有碳氮化物的硬质相,所述碳氮化物含有Ti和Nb；以及含有铁族元素的金属结合相。硬质相包括粒状的芯部和覆盖芯部的至少一部分的周边部。芯部含有表示为Ti<Sub>1-X-Y</Sub>Nb<Sub>X</Sub>W<Sub>Y</Sub>C<Sub>1-Z</Sub>N<Sub>Z</Sub>的复合碳氮化物,其中Y为0以上0.05以下且Z为0.3以上0.6以下。与芯部相比,周边部的组成中W的含量更高。(A cermet, comprising: a carbonitride containing carbonitride, said carbonitride containing Ti and Nb; and a metal binder phase containing an iron group element. The hard phase includes a granular core and a peripheral portion covering at least a portion of the core. The core contains Ti 1‑X‑Y Nb X W Y C 1‑Z N Z The compound carbonitride of (1), wherein Y is 0 to 0.05 and Z is 0.3 to 0.6. The content of W in the composition of the peripheral portion is higher than that of the core portion.)

1. A cermet, comprising:

a carbonitride containing carbonitride, said carbonitride containing Ti and Nb; and

a metal binder phase containing an iron group element,

the hard phase includes a granular core and a peripheral portion covering at least a portion of the core,

the core contains a compound represented by Ti_1-X-YNb_XW_YC_1-ZN_ZThe compound carbonitride of (1), wherein Y is 0 to 0.05 and Z is 0.3 to 0.6,

the content of W in the composition of the peripheral portion is higher than that of the core portion.

2. The cermet according to claim 1, wherein

X is 0.1 to 0.6.

3. Cermet according to claim 1 or 2, wherein

X is 0.1 to 0.2.

4. Cermet according to claim 1 or 2, wherein

X is 0.4 to 0.6.

5. The cermet according to any one of claims 1 to 4, comprising a WC phase consisting of WC, wherein

The content of the WC phase is 1 vol% or less.

6. The cermet according to any one of claims 1 to 4, which does not comprise a WC phase consisting of WC.

7. Cermet according to any one of claims 1 to 6, wherein

In the core, V, Cr and Mo together account for less than 2 atomic percent of the total of Ti, Nb, W, V, Cr, and Mo.

8. Cermet according to any one of claims 1 to 7, wherein

The average crystal grain diameter of the core part is 0.5-3 μm.

9. A cutting tool comprising the cermet according to any one of claims 1 to 8.

10. The cutting tool of claim 9, comprising:

a substrate composed of the cermet; and

and a coating film covering the base material.

11. A method of making a cermet comprising:

obtaining a first powder represented by Ti_1-X-YNb_XW_YC_1-ZN_ZThe compound carbonitride of (a);

obtaining a mixed powder by mixing the first powder, a second powder containing W, and a third powder containing an iron group element;

obtaining a molded body by pressure-molding the mixed powder; and

sintering the compact to obtain a sintered body,

y is 0 to 0.05 inclusive,

z is 0.3 to 0.6 inclusive,

said obtaining of the first powder comprises the following operations:

an oxide mixed powder is obtained by mixing an oxide powder containing two elements of Ti and Nb or three elements of Ti, Nb and W with a carbon source powder containing carbon,

granulating the oxide mixed powder to obtain granules,

obtaining a powder precursor composed of the composite carbonitride by heat-treating the granules at a temperature of 1800 ℃ or higher in an atmosphere containing nitrogen, and

obtaining the first powder by crushing the powder precursor.

Technical Field

The present invention relates to a cermet, a cutting tool including the same, and a method of manufacturing the cermet.

Background

Cemented carbides and cermets are known as hard materials containing Ti. Since such a hard material has excellent wear resistance, it is suitably used for cutting tools and wear-resistant tools. For example,

WO2010/008004 (patent document 1) discloses a sintered cemented carbide composed of a hard phase containing at least 90 vol% of (Ti) expressed as (Ti) with respect to the entire hard phase and a binder phase_1-xM_x)(C_1-yN_y) The composite carbonitride solid solution of (1). WO2011/136197 (patent document 2) discloses a cermet including a ceramic powder represented by (Ti)_1-x-yL_xMo_y)(C_1-zN_z) A first hard phase composed of a composite carbonitride solid solution of (a), a second hard phase composed of WC, and a binder phase composed mainly of both Co and Ni or one of Co and Ni.

Reference list

Patent document

Patent document 1: WO2010/008004

Patent document 2: WO2011/136197

Disclosure of Invention

A cermet according to one aspect of the present disclosure includes: a carbonitride containing carbonitride, said carbonitride containing Ti and Nb; and a metal binder phase containing an iron group element. The hard phase includes a granular core and a peripheral portion covering at least a portion of the core. The core contains Ti_1-X-YNb_XW_YC_1-ZN_ZThe compound carbonitride of (1), wherein Y is 0 to 0.05 and Z is 0.3 to 0.6. The content of W in the composition of the peripheral portion is higher than that of the core portion.

A cutting tool according to one aspect of the present disclosure includes a cermet.

A method of manufacturing a cermet according to one aspect of the present disclosure is a method of manufacturing a cermet including the steps of: obtaining a first powder represented by Ti_1-X-YNb_XW_YC_1-ZN_ZComposite carbonitride ofForming; obtaining a mixed powder by mixing the first powder, a second powder containing W, and a third powder containing an iron group element; obtaining a molded body by pressure-molding the mixed powder; and sintering the formed body to obtain a sintered body. Y is 0 to 0.05 and Z is 0.3 to 0.6. Said obtaining of the first powder comprises the following operations: mixing oxide powder containing two elements of Ti and Nb or three elements of Ti, Nb and W with carbon source powder containing carbon to obtain oxide mixed powder; granulating the oxide mixed powder to obtain granules; obtaining a powder precursor composed of the composite carbonitride by heat-treating the granules at a temperature of 1800 ℃ or higher in an atmosphere containing nitrogen gas; and obtaining the first powder by crushing the powder precursor.

Drawings

Fig. 1 is a schematic view schematically showing a cross section of a cermet according to the present embodiment.

Fig. 2 shows an example of an electron micrograph obtained by photographing a cross section of the cermet in sample 11.

Detailed Description

[ problem to be solved by the present disclosure ]

In the cemented carbide of patent document 1, the composite carbonitride solid solution contained in the hard phase is represented by (Ti)_1-xM_x)(C_1-yN_y). M in the composite carbonitride solid solution represents at least one element selected from the group consisting of W, Mo, Nb, Zr, and Ta, x is 0.05 to 0.5, and y is 0.01 to 0.75. Since such sintered cemented carbide has insufficient bonding force at the interface between the hard phase and the bonding phase, it is difficult to obtain both wear resistance and breakage resistance.

In the cermet of patent document 2, the composite carbonitride solid solution in the first hard phase is represented by (Ti)_{1-x- y}L_xMo_y)(C_1-zN_z). In the chemical formula, L represents a group selected from Zr, Hf, Nb and TaAt least one element of the group, x is 0.01 to 0.5, y is 0.03 to 0.05, and z is 0.05 to 0.75. The Mo content is preferably low, since Mo reduces the steel adhesion resistance of the carbonitride itself. The reason why the content of Mo in the composite carbonitride solid solution in the cermet of patent document 2 is not low is that the atomic ratio of Mo in all the metal elements (Ti, L, and Mo) is 0.03 or more. The steel adhesion resistance of the cermet is reduced by including the secondary hard phase composed of WC, which thus greatly affects the breakage resistance representing the cutting performance of the cermet.

Under such circumstances, an object of the present disclosure is to provide a cermet that achieves both wear resistance and breakage resistance in a well-balanced manner, a cutting tool including the cermet, and a method of manufacturing the cermet.

[ Effect of the present disclosure ]

According to the above, a cermet that achieves both wear resistance and breakage resistance in a well-balanced manner, a cutting tool including the cermet, and a method of manufacturing the cermet can be provided.

[ description of embodiments of the invention of the present application ]

The present inventors have developed a cermet to which Ti is applied_1-X-YNb_XW_YC_1-ZN_ZThe compound carbonitride of (2) is used as a new raw material. The inventors have found that the compound is represented by Ti_1-X-YNb_XW_YC_1-ZN_ZThe thermal properties of the composite carbonitride of (a) are superior to those of conventional Ti-based compounds. In particular, the present inventors have found that by appropriately controlling the compositions of Nb, W, and N, high mechanical strength can be obtained. Furthermore, the inventors have found that the carbonitride phase containing the composite carbonitride is structured to include a composition containing Ti as represented by_1-X-YNb_XW_YC_1-ZN_ZThe core portion of the composite carbonitride and the peripheral portion having a higher W content in the composition than the core portion can improve the bonding force at the interface between the hard phase and the metal bonding phase, and the present disclosure has been made.

Embodiments of the present invention are first listed and described.

[1]A cermet according to one aspect of the present disclosure includes: a carbonitride containing carbonitride, said carbonitride containing Ti and Nb; and a metal binder phase containing an iron group element. The hard phase includes a granular core and a peripheral portion covering at least a portion of the core. The core contains a compound represented by Ti_1-X-YNb_XW_YC_1-ZN_ZThe compound carbonitride of (1), wherein Y is 0 to 0.05 and Z is 0.3 to 0.6. The content of W in the composition of the peripheral portion is higher than that of the core portion. Thereby, it is possible to provide a cermet that can achieve both wear resistance and breakage resistance in a well-balanced manner.

[2] X is preferably 0.1 to 0.6. So that significant wear and breakage resistance can be obtained.

[3] X is more preferably 0.1 to 0.2. So that a significant wear resistance can be obtained.

[4] X is still more preferably 0.4 to 0.6. So that a significant breakage resistance can be obtained.

[5] Preferably, the cermet includes a WC phase composed of WC, and the content of the WC phase is 1 vol% or less. Since the decrease in the adhesion of steel can be prevented even if the WC phase is included, both wear resistance and breakage resistance can be obtained in a more balanced manner.

[6] The cermet preferably does not include a WC phase consisting of WC. Since the decrease in the adhesion of the steel can be prevented, the wear resistance and the breakage resistance can be obtained in a more balanced manner.

[7] In the core, V, Cr and Mo preferably account for less than 2 atomic% of the total of Ti, Nb, W, V, Cr and Mo. Since V, Cr and Mo (representing an element that lowers the steel adhesion resistance of the cermet) can be sufficiently suppressed, wear resistance and breakage resistance can be obtained in a more balanced manner.

[8] The average crystal grain size of the core is preferably 0.5 μm or more and 3 μm or less. So that higher wear resistance and breakage resistance can be obtained.

[9] A cutting tool according to one aspect of the present disclosure includes a cermet. Thereby, a cutting tool having excellent wear resistance and breakage resistance attributed to the cermet can be provided.

[10] The cutting tool preferably includes a base material made of cermet and a coating film covering the base material. Such a cutting tool may also have excellent wear resistance and breakage resistance due to the cermet.

[11]A method of manufacturing a cermet according to one aspect of the present disclosure is a method of manufacturing a cermet including the steps of: obtaining a first powder represented by Ti_1-X-YNb_XW_YC_1-ZN_ZThe compound carbonitride of (a); obtaining a mixed powder by mixing the first powder, a second powder containing W, and a third powder containing an iron group element; obtaining a molded body by pressure-molding the mixed powder; and sintering the formed body to obtain a sintered body. Y is 0 to 0.05 and Z is 0.3 to 0.6. Said obtaining of the first powder comprises the following operations: mixing oxide powder containing two elements of Ti and Nb or three elements of Ti, Nb and W with carbon source powder containing carbon to obtain oxide mixed powder; granulating the oxide mixed powder to obtain granules; obtaining a powder precursor composed of the composite carbonitride by heat-treating the granules at a temperature of 1800 ℃ or higher in an atmosphere containing nitrogen gas; and obtaining the first powder by crushing the powder precursor. Thereby enabling the manufacture of cermets that achieve both wear resistance and breakage resistance in a balanced manner.

[ details of the embodiments of the invention of the present application ]

Although an embodiment of the present invention (hereinafter also referred to as "the present embodiment") will be described in further detail hereinafter, the present embodiment is not limited thereto. The following description will be made with reference to the accompanying drawings.

The expression "a to B" herein refers to the upper and lower limits of the range (i.e., a above and B below). When a unit is not given but only B, the units of a and B are the same. When referred to hereinThe compound is represented by a chemical formula and when there is no particular limitation on the atomic ratio, all conventionally known atomic ratios may be included, and the atomic ratio is not necessarily limited to only the atomic ratio within the stoichiometric range. For example, when the expression "TiAlN" is given, the ratio of the number of atoms forming TiAlN is not limited to Ti: Al: N ═ 0.5:0.5:1 but includes all conventionally known atomic ratios. This also applies to expressions for compounds other than "TiAlN". In the present embodiment, a compound shown as containing a metal element such as titanium (Ti), aluminum (Al), silicon (Si), tantalum (Ta), chromium (Cr), niobium (Nb), or tungsten (W) and a nonmetal element such as nitrogen (N), oxygen (O), or carbon (C) does not necessarily have a stoichiometric composition. When carbonitrides and composite carbonitrides are referred to herein as alpha_Xβ_Yγ_ZC_SN_T(metal α β γ and nonmetal CN), carbonitrides and complex carbonitrides may vary, for example, within a range of 0.6 ≦ S + T ≦ 1.0 when the condition of X + Y + Z ≦ 1 is satisfied. The term "mechanical strength" as used herein means mechanical strength including various characteristics such as abrasion resistance, breakage resistance and bending strength.

< cermet >)

As shown in fig. 1, the cermet according to the present embodiment includes: a carbonitride-containing carbonitride 1 containing Ti and Nb; and a metal binder phase 2 containing an iron group element. The hard phase 1 includes a granular core portion 11 and a peripheral portion 12 covering at least a part of the core portion 11. The core 11 contains Ti_1-X-YNb_XW_YC_1-ZN_ZThe compound carbonitride of (1), wherein Y is 0 to 0.05 and Z is 0.3 to 0.6. The content of W in the composition of the peripheral portion 12 is higher than that of the core portion 11. Cermets having such characteristics can attain both wear resistance and breakage resistance in a well-balanced manner.

< hard phase >

As described above, the carbonitride phase 1 contains carbonitride containing Ti and Nb. Specifically, the hard phase 1 includes a granular core portion 11 and a peripheral portion 12 covering at least a part of the core portion 11. The core 11 contains Ti_1-X-YNb_XW_YC_1-ZN_ZThe compound carbonitride of (1), wherein Y is 0 to 0.05 and Z is 0.3 to 0.6. The content of W in the composition of the peripheral portion 12 is higher than that of the core portion 11. When the composition of the granular core 11 (Ti) in the hard phase 1_1-X-YNb_XW_YC_1-ZN_Z) With the atomic ratio within the above range, the cermet may have high mechanical strength. Since the hard phase 1 includes the core portion 11 and the peripheral portion 12 covering at least a part of the core portion 11, the adhesion strength between the hard phase 1 and the metal bonding phase 2 can be improved. As shown in fig. 1, the core portion 11 and the peripheral portion 12 in the hard phase 1 preferably have a double structural relationship (so-called core-shell structure) in which the core portion 11 is partially or completely covered with the peripheral portion 12.

(core part)

The core 11 contains Ti_1-X-YNb_XW_YC_1-ZN_ZThe compound carbonitride of (1). X is more than 0 and less than 1, Y is 0 to 0.05, and Z is 0.3 to 0.6. The core 11 is mainly composed of Ti and contains Nb as a subcomponent. The core may further comprise W as a third component. When the values of X and Y are within the above ranges, the cermet can attain both wear resistance and breakage resistance in a well-balanced manner. The atomic ratio X of Nb is preferably 0.1 or more and 0.6 or less, more preferably 0.1 or more and 0.2 or less, and most preferably 0.13 or more and 0.17 or less. X is more preferably 0.4 to 0.6. The atomic ratio Y of W is preferably 0 to 0.03. The atomic ratio (1-X-Y) of Ti is preferably 0.75 to 0.9 from the viewpoint of setting the addition amounts of the subcomponent and the third component to at most the solid solubility limit and sufficiently exhibiting the effect of the added metal element. Z indicating the atomic ratio of carbon to nitrogen in the composite carbonitride is preferably 0.4 or more and 0.6 or less. Although there should be no particular limitation on the composition of the core portion 11 as long as the effects of the present disclosure are exhibited and the content of W in the composition of the core portion is lower than the content of W in the peripheral portion 12, an exemplary composition includes Ti_0.9Nb_0.1C_0.5N_0.5、Ti_0.8Nb_0.15W_0.05C_0.4N_0.6And Ti_0.75Nb_0.2W_0.05C_0.6N_0.4。

In the core 11, it is preferable that V, Cr and Mo account for less than 2 atomic% of the total of Ti, Nb, W, V, Cr, and Mo. In the core 11, it is more preferable that V, Cr and Mo account for 1 atom% or less of the total of Ti, Nb, W, V, Cr, and Mo. The content is most preferably 0.

The core 11 may contain the above-mentioned V, Cr and Mo elements as impurities or trace elements in addition to the main component Ti, the subcomponent Nb, and the third component W. In the present embodiment, the total content of V, Cr and Mo in the above elements is preferably less than 2 atomic% with respect to all of these metal elements. Since V, Cr and Mo (which represent elements that decrease the steel adhesion resistance of the cermet) can be sufficiently suppressed, both wear resistance and breakage resistance can be obtained in a more balanced manner. When the content is 2 at% or more, these impurities may reduce the steel-adhesion resistance of the cermet.

By analyzing the cut surface obtained by cutting the cermet along any surface using an energy dispersive X-ray spectrometer (EDX) attached to a Scanning Electron Microscope (SEM), the composition and atomic ratio of the composite carbonitride contained in the core portion 11 can be determined. For example, a cermet cutting surface is prepared and the core 11 contained in the carbonitride phase 1 appearing in the cutting surface is measured by a tool to obtain composite carbonitride (Ti) in the core 11_1-X-YNb_XW_YC_1-ZN_Z) Composition and atomic ratio of (a). Similarly, by measuring the WC phase appearing in the cut surface, the peripheral portion 12, or the metallic bonding phase 2 by the same measuring method, it is also possible to determine the WC content (content) in the cermet, which will be described later, the composition and atomic ratio of the composite carbonitride in the peripheral portion 12, and the content of the iron group element in the metallic bonding phase 2. Before observation using SEM, the surface of the cut surface is preferably polished using a Focused Ion Beam (FIB).

The average crystal particle diameter (i.e., 50% number cumulative distribution particle diameter (hereinafter also referred to as "D50 of the core")) of the core 11 is preferably 0.5 μm or more and 3 μm or less. That is, D50 of the plurality of granular core portions 11 appearing on the cut surface is preferably 0.5 μm or more and 3 μm or less. Since the bending strength and toughness among mechanical strengths can be improved in particular, higher wear resistance and breakage resistance can be obtained. D50 in core 11 is more preferably 1 μm to 2 μm.

The particle size of each core portion 11 can be obtained by image analysis of SEM images of the cross section (cut surface) of the cermet. For example, ImageJ (https:// ImageJ. nih. gov/ij /) can be used as software for image analysis. The "particle size" of the core 11 means the maximum Feret diameter. The overall parameter of D50 for obtaining the core 11 (i.e., the number of "particle sizes" of the core 11) is set to at least 50 and preferably at least 100. From the viewpoint of accuracy of analysis, SEM images for image analysis are taken at a magnification of 3000 to 5000 times, and it is preferable to prepare the number of particle diameters of the core 11 satisfying the overall parameters by setting a plurality of fields.

The volume ratio of the core 11 in the cermet is preferably 5 vol% or more and 60 vol% or less. So that higher wear resistance and breakage resistance can be obtained. The volume ratio of the core 11 in the cermet is more preferably 10 vol% or more and 50 vol% or less.

The volume ratio of the core 11 in the cermet can be obtained according to the analysis of D50 of the core 11. More specifically, the cut surface is prepared, observed at a magnification of 3000 to 5000 times by SEM, and the image is analyzed by the software, whereby the area ratio of the core portion 11 in the observation field can be obtained. Then, the area ratio is defined as the volume ratio of the core 11 in the cermet by considering the area ratio to be also continuous in the depth direction of the cutting face. The volume ratio of the core 11 in the cermet can thereby be obtained. Preferably, the average value of the area ratio is calculated based on the analysis of the above-mentioned image prepared by selecting the SEM image of one cut surface in at least three fields of view, and the average value is defined as the volume ratio of the core 11 in the cermet.

(peripheral part)

As described above, the hard phase 1 includes the peripheral portion 12 covering at least a part of the core portion 11. In particular, the core portion 11 and the peripheral portion 12 in the hard phase 1 preferably have a double structural relationship (so-called core-shell structure) in which the core portion 11 is partially or completely covered by the peripheral portion 12.

The peripheral portion 12 is formed in a step of sintering cermet (fourth step) which will be described later. Due to composite carbonitride (Ti) used as raw material in liquid phase sintering_1-X-YNb_XW_YC_1-ZN_Z) The formation and re-precipitation of a solid solution of the particles and the W-containing particles (e.g., WC particles) therearound form the peripheral portion 12 around the core portion 11. In this case, the peripheral portion 12 precipitates as composite carbonitride having a higher W content than that of the composite carbonitride (i.e., Ti) contained in the core portion 11_{1-X- Y}Nb_XW_YC_1-ZN_Z) W content of (2). The values of X and Z of the composite carbonitride in the core portion 11 and the composite carbonitride in the peripheral portion 12 vary depending on the value of Y and the atmosphere during sintering (particularly, the partial pressure of nitrogen in the atmosphere), and the value of Y in the composite carbonitride in the peripheral portion 12 increases due to the formation and re-precipitation of solid solutions of W-containing particles (e.g., WC particles).

The peripheral portion 12 serves as an adhesion layer which enhances the adhesion strength between the hard phase 1 and the metal binder phase 2. Thereby improving the mechanical properties of the cermet. The peripheral portion 12 may partially or completely cover the core portion 11 as long as the effects of the present disclosure can be exhibited, and the thickness of the peripheral portion 12 should not be limited. The composition of the peripheral portion 12 should not be particularly limited as long as the effects of the present disclosure can be exhibited and the content of W in the composition of the peripheral portion is higher than that of the core portion 11. An exemplary composition of the peripheral portion 12 may include Ti_0.8Nb_0.1W_0.1C_0.5N_0.5、Ti_0.75Nb_0.15W_0.1C_0.4N_0.6And Ti_0.7Nb_0.15W_0.15C_0.6N_0.4。

< Metal binding phase >

The metallic bonding phase 2 contains an iron group element. The metallic bonding phase 2 is mainly composed of an iron group element. The metallic bonding phase 2 may contain, in addition to the iron group element, inevitable elements introduced from the hard phase 1 and trace amounts of impurity elements. The content of the iron group element in the metallic bonding phase 2 is preferably 90 at% or more, and more preferably 95 at% or more, from the viewpoint of maintaining the state as a metal and avoiding the formation of a brittle intermediate compound. The upper limit of the content of the iron group element in the metallic bonding phase 2 is 100 atomic%. The iron group elements refer to elements of groups 8, 9 and 10 in the fourth period of the periodic table, i.e., iron (Fe), cobalt (Co) and nickel (Ni). Examples of the element other than the iron group element contained in the metallic binder phase 2 also include titanium and niobium.

The metal binder phase 2 in the cermet preferably consists essentially of Co. The content of the iron group element other than Co in the metallic bonding phase 2 is preferably less than 75 vol%, and more preferably less than 50 vol%.

< WC phase >

The cermet according to the present embodiment preferably does not contain a WC phase consisting of WC. When the work material is composed of a material based on iron and steel, a WC phase occurs due to excessive precipitation of WC in the cermet, and thus wear resistance and breakage resistance of the cermet tend to be lowered due to adhesion of WC to the work material. However, when WC is to be included in order to design a cermet having high toughness, the content of the WC phase in the cermet is preferably 1 vol% or less. That is, the cermet contains a WC phase composed of WC, and the content of the WC phase is preferably 1 vol% or less. When the content of the WC phase in the cermet exceeds 1 vol%, the steel adhesion resistance is lowered, and it tends to be difficult to obtain both wear resistance and breakage resistance in a well-balanced manner.

The content (% by volume) of the WC phase in the cermet can be obtained by the same method as the above-described method of calculating the volume ratio of the core portion 11 in the cermet. In a visual field (back scattered electron image) observed by SEM, WC particles were observed as high-brightness (white) particles. In X-ray diffraction (XRD) analysis of the cermet, it can be confirmed that there is no WC phase composed of WC in the cermet based on the diffraction peak of WC at the background level.

[ method for producing cermet ]

Although there should be no particular limitation on the method for producing the cermet according to the present embodiment, the following method is preferred. The method of manufacturing the cermet includes: obtaining a first powder represented by Ti_1-X-YNb_XW_YC_1-ZN_ZThe composite carbonitride composition (first step); obtaining a mixed powder by mixing the first powder, the second powder containing W, and the third powder containing an iron group element (second step); obtaining a compact by press-molding the mixed powder (third step); and sintering the formed body to obtain a sintered body (fourth step). At Ti_1-X-YNb_XW_YC_1-ZN_ZWherein Y is 0 to 0.05 and Z is 0.3 to 0.6. At Ti_1-X-YNb_XW_YC_1-ZN_ZIn (3), X is more than 0 and less than 1.

< first step >

The first step is a step of obtaining a first powder represented by Ti_1-X-YNb_XW_YC_1-ZN_ZThe compound carbonitride of (2).

The step of obtaining the first powder comprises the following operations: obtaining an oxide mixed powder by mixing an oxide powder containing two elements of Ti and Nb or three elements of Ti, Nb, and W with a carbon source powder containing carbon (first operation); granulating the oxide mixed powder to obtain granules (second operation); obtaining a powder precursor composed of a composite carbonitride by heat-treating the granulated body at a temperature of 1800 ℃ or higher in an atmosphere containing nitrogen gas (third operation); and by crushing the powder precursor, thereby obtaining a first powder (fourth operation).

(first operation)

In the first operation, an oxide mixed powder is obtained by mixing an oxide powder containing two elements of Ti and Nb or three elements of Ti, Nb, and W with a carbon source powder containing carbon.

As described above, the oxide powder is composed of two elements of Ti and Nb or three elements of Ti, Nb and WIs used as a catalyst. In this case, the first powder having a small primary particle diameter can be easily obtained, thereby enabling the D50 of the core to be made smaller, for example, the D50 thereof is at most 3 μm. The oxide powder may contain at least one element selected from the group consisting of V, Cr and Mo as a component introduced by the apparatus for manufacturing. In this case, in the oxide powder, the total content of V, Cr and Mo is preferably less than 2 atomic% with respect to the total amount of Ti, Nb, W, V, Cr, and Mo. Specific examples of the oxide powder include powders containing TiO₂、Nb₂O₅And WO₃And mixed powders of oxides. The oxide powder may be formed of Ti_0.9Nb_0.1O₂Or Ti_0.9Nb_0.05W_0.05O₂And the like. Unless the purpose is contrary, the oxidation number of each element or the content of impurities may be changed.

The carbon source powder contains at least carbon. The carbon source powder preferably contains graphite, and more preferably consists of graphite. In the first operation, an oxide mixed powder is obtained by mixing a carbon source powder and an oxide powder. Therefore, in a third operation to be described later, in an atmosphere containing nitrogen, the reduction reaction of the oxide, the solid solution forming reaction caused by interdiffusion of Ti and Nb in the reduced oxide, and the carbonitriding reaction of Ti and Nb in the solid solution state can be simultaneously and continuously performed. When the oxide powder contains W, in the third operation, in the atmosphere containing nitrogen, the reduction reaction of the oxide, the solid solution forming reaction caused by interdiffusion of Ti, Nb, and W, and the carbonitriding reaction of Ti, Nb, and W in the solid solution state can be simultaneously and continuously performed. So that the first powder can be obtained efficiently.

Conventionally known methods can be used as a method of mixing the oxide powder and the carbon source powder. From the viewpoint of reducing the 50% number cumulative distribution particle diameter of the oxide mixed powder (hereinafter also referred to as "D50 of the oxide mixed powder"), a mixing method using a dry ball mill having a high crushing function and a mixing method using a wet ball mill can be suitably employed. A mixing method using a rotary impeller fluid mixer (rotary impeller fluid mixer) having a low crushing function may also be applied. The D50 of the oxide mixed powder can be obtained based on at least 100 particles appearing in a micrograph observed at a magnification of 10000 times with an SEM. For all particles appearing in the micrograph, the diameter of a circle equal to the area of the particles (equivalent circle diameter) was calculated using image analysis software (e.g., ImageJ), and the 50% number cumulative distribution equivalent circle diameter of the particles was defined as D50 of the oxide mixed powder.

(second operation)

In the second operation, the oxide mixed powder is granulated to obtain granules. Conventionally known granulation methods can be used as the granulation method in the second operation. Examples of the granulation method include a method using known equipment such as a spray dryer and an extrusion granulator. For granulation, for example, a binder component such as a wax material may be suitably used as the binder. There should be no particular limitation on the shape and size of the granules. The pellet may be, for example, a cylindrical shape having a diameter of 0.5mm to 5mm and a length of 5mm to 20 mm.

(third operation)

In the third operation, the granulated body is heat-treated at a temperature of 1800 ℃ or higher in an atmosphere containing nitrogen gas, thereby obtaining a powder precursor composed of a composite carbonitride. In the third operation, in the atmosphere containing nitrogen gas, oxygen in the oxide powder contained in the granulated body reacts with carbon in the carbon source powder, so that Ti and Nb in the oxide powder are reduced. The solid solution forming reaction of the reduced Ti and Nb proceeds due to interdiffusion. The carbonitriding reaction of the reduced Ti and Nb with nitrogen in the atmosphere and carbon in the carbon source powder also occurs simultaneously. Thereby forming the above-mentioned film represented by Ti_1-X-YNb_XW_YC_1-ZN_ZThe powder precursor of (3) is composed of a composite carbonitride. The nitrogen contained in the atmosphere serves as a source of N for the composite carbonitride.

In the third operation, when a mixed powder obtained by mixing a metal powder containing Ti and Nb, a metal powder containing Ti, Nb, and W, a carbonitride powder containing Ti and Nb, or a carbonitride powder containing Ti, Nb, and W, instead of an oxide powder, with a carbon source powder is subjected to heat treatment, a powder precursor composed of composite carbonitride cannot be obtained. This is because the carbonitriding reaction of the metal powder containing Ti, Nb, and the like proceeds early in the heat treatment, and therefore the solid solution forming reaction by interdiffusion of Ti, Nb, and the like cannot proceed. Since carbonitride powders containing Ti, Nb, and the like are chemically stable even in a high temperature region exceeding 2000 ℃, solid solution forming reactions due to interdiffusion of Ti, Nb, and the like cannot proceed.

The heat treatment atmosphere in the third operation should not be particularly limited as long as it is an atmosphere containing nitrogen. Can convert pure N₂By reacting hydrogen (H)₂Gas), argon (Ar gas), helium (He gas), or carbon monoxide gas (CO gas) to N₂The resulting gas mixture in the gas was used as the atmosphere.

The temperature during the heat treatment in the third operation is preferably 1800 ℃ or more, and more preferably 2000 ℃ or more, from the viewpoint of the progress and acceleration of the reduction reaction, solid solution formation reaction, and carbonitriding reaction of the oxide powder. From the viewpoint of preventing excessive aggregation of the powder precursor obtained by the heat treatment, the temperature is preferably 2400 ℃ or lower.

The time of the heat treatment in the third operation is preferably adjusted according to the D50 of the oxide powder. For example, when the D50 of the oxide mixed powder is 0.3 μm to 0.5 μm, the time of the above heat treatment is suitably 15 minutes to 60 minutes. When the value of D50 is small, the time of the heat treatment in the third operation is preferably short. When the value of D50 is large, the time of the heat treatment in the third operation is preferably long.

In the third operation, it is preferable to use a rotary continuous heat treatment apparatus such as a rotary kiln. The heat treatment apparatus includes an inclined rotary reaction tube. The heat treatment apparatus further includes a heating mechanism for heating the rotary reaction tube, a gas inlet for introducing a nitrogen-containing gas into the rotary reaction tube, a gas outlet for discharging the nitrogen-containing gas from the rotary reaction tube, an inlet for introducing the granulated gas into the rotary reaction tube, and an outlet for taking out the powder precursor from the rotary reaction tube. Such a heat treatment apparatus is preferable because it can heat-treat the granulated body under constant conditions, and therefore it can continuously and efficiently produce a powder precursor of composite carbonitride of stable quality.

In the third operation, when the heat treatment apparatus is used, the rotary reaction tube is first heated to a temperature of 1800 ℃. The granulated material is continuously supplied through an inlet at the upper part of the rotary reaction tube, and the granulated material is moved through the inside of the rotary reaction tube while rotating the rotary reaction tube, thereby heat-treating the granulated material. Thereby, a powder precursor composed of composite carbonitride can be formed. The powder precursor can be taken out through an outlet at the lower part of the rotary reaction tube.

(fourth operation)

In the fourth operation, the first powder is obtained by crushing the powder precursor. A conventionally known crushing method may be used as the method of crushing the powder precursor in the fourth operation.

< second step >

The second step is a step of obtaining a mixed powder by mixing the first powder, the second powder containing W, and the third powder containing an iron group element. Conventionally known mixing methods can be used as a method of mixing these powders. Examples of the method include a mixing method using a dry ball mill and a mixing method using a wet ball mill, which have a high crushing function, and a mixing method using a rotary impeller fluid mixer, which have a low crushing function when the powder is slightly aggregated. A commercially available WC powder may be used as the second powder containing W, and a commercially available Co powder may be used as the third powder containing an iron group element.

< third step >

The third step is to obtain a product by pressure molding the mixed powderAnd (5) forming the body. Conventionally known press molding methods can be used as a method of press molding the mixed powder. Examples of the method include press forming by filling a die with the mixed powder and applying pressure with a punch, cold isostatic pressing, injection forming, and extrusion forming. The pressure at the time of press molding is preferably 0.5t/cm²(about 50MPa) or more and 2.0t/cm²(about 200MPa) or less.

< fourth step >

The fourth step is a step of obtaining a sintered body by sintering the molded body. In the method of sintering the molded body, the molded body is preferably kept for a predetermined period of time in a temperature region in which a liquid phase is generated. The sintering temperature is preferably 1300 ℃ to 1600 ℃. The sintering temperature is more preferably 1300 ℃ to 1500 ℃. The time for holding the formed body is preferably 0.5 hours or more and 2 hours or less, and more preferably 1 hour or more and 1.5 hours or less. The atmosphere during sintering is preferably an inert gas atmosphere such as nitrogen or argon or a vacuum (about 0.5Pa or less).

After the sintered body is thus obtained, a cermet as a final product can be obtained by machining the sintered body as necessary. The cermet obtained by such a manufacturing method can attain both wear resistance and breakage resistance in a well-balanced manner. The sintered body obtained by this manufacturing method does not necessarily require machining such as surface polishing, and the sintered skin of the sintered body can be maintained to make a final product (cermet).

The composition and atomic ratio of the first powder can be obtained by conventionally known component analysis techniques. For example, the composition (metals, carbon and nitrogen) and content in the powder can be determined by induced plasma emission spectroscopy, high frequency combustion or thermal conduction techniques.

The 50% number cumulative distribution particle diameter of the first powder (hereinafter also referred to as D50 of the first powder) is preferably 0.3 μm or more and 1.5 μm or less from the viewpoint of workability in application as a cutting tool and achievement of both high hardness and high toughness. The method of measuring D50 of the first powder may be the same as or different from the method of measuring D50 of the core. Phase D50 with coreSimilarly, D50 of the first powder can be determined using SEM. For example, a laser diffraction particle size distribution measuring instrument (trade name;) "

MT3000II ", manufactured by microtrac bel corp.), D50 was determined by setting the refractive index of the particles to 2.4. The D50 of the first powder refers to D50 of the primary particles of composite carbonitride.

[ cutting tools ]

The cutting tool according to the present embodiment includes a cermet. It is thus possible to provide a cutting tool that obtains both wear resistance and breakage resistance in a balanced manner. The cutting tool may be suitably used as a drill, an end mill, a replaceable insert for a drill, a replaceable insert for an end mill, a replaceable insert for milling, a replaceable insert for rotary cutting, a metal saw, a gear cutting tool, a reamer, a tap, a cutting drill, a wear resistant tool, or a tool for friction stir welding.

When the cutting tool is applied as a replaceable insert, the substrate may or may not have a chip breaker. The cutting edge line portion serving as the cutting center portion at the time of cutting a work material may have a sharp edge (an edge at which the rake face and the flank face intersect), may be honed (with a sharp edge of R), may have a negative margin (chamfer), and may be honed and have a negative margin.

The cutting tool according to the present embodiment includes a base material composed of cermet and a coating film covering the base material. Since such a cutting tool further includes a coating film, higher adhesion resistance can be obtained in addition to wear resistance. The coating may cover the entire surface of the substrate or a portion (e.g., a cutting edge line portion, which is a region that contributes greatly to cutting performance) thereof. The composition of the coating film should not be particularly limited, and any conventionally known coating film may be employed.

As a method for covering a substrate composed of cermet with a coating film, a conventionally known method can be employed. For example, Physical Vapor Deposition (PVD) or Chemical Vapor Deposition (CVD) may be employed. In particular, examples of PVD include resistive thermal evaporation, Electron Beam (EB) evaporation, Molecular Beam Epitaxy (MBE), ion plating, ion beam deposition, and sputtering.