Crushing, stirring, mixing, and kneading mechanism components

Abstract

This invention relates to a crushing, stirring, mixing, and kneading mechanism. It improves the impact resistance of the crushing, stirring, mixing, and kneading mechanism containing cermet disclosed in Japanese Patent No. 6922110, and imparts high corrosion resistance. The invention relates to a crushing, stirring, mixing, and kneading mechanism containing cermet, wherein raw materials are combined in the following mass ratio: Ti: 15-40%, Mo: 2-29%, Cr: 1-15%, C: 2-20%, Co: Co and Ni total 30%-55%, and the Co / Ni ratio is greater than 1. These raw materials are mixed to obtain a mixed powder, which is then pressed to obtain a pressed body. The pressed body is then sintered to obtain a cermet. This cermet has three phases: a core phase 2 mainly composed of TiCN, a ring phase 3 mainly composed of (Ti, Mo, Cr)(C, N) surrounding the core phase, and a metallic phase 4. SEM observation shows that no Mo2C phase or chromium carbide phase was observed.

Description

Technical Field

[0001] This invention relates to a crushing, stirring, mixing, and kneading mechanism for metal ceramics that possess excellent impact resistance, wear resistance, and corrosion resistance. Background Technology

[0002] In Patent Document 1, the inventors disclosed a crushing, stirring, mixing, and kneading mechanism comprising a metal ceramic with excellent impact resistance and wear resistance. That is, by employing the technology of Patent Document 1, a magnetic, lightweight metal ceramic with significantly improved wear resistance and impact resistance can be obtained, extending the lifespan of crushing, stirring, mixing, and kneading mechanisms prone to severe wear.

[0003] Existing technical documents

[0004] Patent documents

[0005] Patent Document 1: Japanese Patent No. 6922110 Summary of the Invention

[0006] The problem that the invention aims to solve

[0007] The inventors have prototyped and repeatedly tested a pulverizing, stirring, mixing, and compounding mechanism for metal ceramics as disclosed in Patent Document 1. The results indicate a desire to further improve impact resistance. Furthermore, it is understood that improved corrosion resistance is also desirable depending on the application. Specifically, high corrosion resistance is required when used in applications such as the compounding of materials containing corrosive metals, such as positive electrode materials for lithium-ion batteries and flame retardants for plastics.

[0008] Therefore, the objective of this invention is to improve the impact resistance of the crushing, stirring, mixing, and compounding mechanism components of the metal ceramic disclosed in Patent Document 1, and to impart high corrosion resistance.

[0009] Methods for solving problems

[0010] In order to solve the above-mentioned problems, the inventors incorporated Cr into the material and, taking into account the balance with other physical properties such as wear resistance and magnetism required by the crushing, stirring, mixing and kneading mechanism, reconstructed the composition of the cermet for the crushing, stirring, mixing and kneading mechanism.

[0011] That is, the present invention solves the above-mentioned problems by providing a pulverizing, stirring, mixing, and compounding mechanism for a cermet comprising the following steps: the cermet is obtained by means of powders arbitrarily selected from Ti or Ti compounds, Mo or Mo compounds, Cr or Cr compounds, Co or Co compounds, Ni or Ni compounds, and carbon, carbides, or carbonitrides, in a mass ratio of Ti: 15-40%, Mo: 2-29%, Cr: 1-15%, C: 2-20%, Co and Ni totaling 30%-55%, and a Co / Ni ratio exceeding 1. The process includes a wet or dry mixing process to obtain a mixed powder; a pressing process to form a pressed body by pressing the mixed powder under a pressure of 50–300 MPa; and a sintering process of the pressed body at 1300–1700 °C in any atmosphere of vacuum, reduction, inactive gas, hydrogen, or nitrogen. The cermet has three phases: a core phase mainly composed of Ti(C, N) (including the case where N = 0), an annular phase mainly composed of (Ti, Mo, Cr)(C, N) (including the case where N = 0) surrounding the core phase, and a metallic phase. No Mo2C phase or chromium carbide phase was observed by SEM.

[0012] The effects of the invention

[0013] According to the present invention, the impact resistance of the crushing, stirring, mixing and kneading mechanism components comprising the metal ceramic disclosed in Patent Document 1 can be improved, and high corrosion resistance can be imparted, thereby further extending the service life of the crushing, stirring, mixing and kneading mechanism components.

[0014] As components for crushing, stirring, mixing, and compounding mechanisms, specifically, they are suitable for use in screw elements of twin-screw extruders, barrels, crushing pins of pin mill devices, impellers of mixing mixers, powder processing device components such as bead mills, etc. Attached Figure Description

[0015] Figure 1 This is a schematic diagram of the cross-sectional structure of the metal ceramics used in the crushing, stirring, mixing, and kneading mechanism of the present invention.

[0016] Figure 2 This is a schematic diagram of the cross-sectional structure of the cermet used in the crushing, stirring, mixing, and kneading mechanism of the present invention, wherein the cermet has a phase containing a relatively high amount of Mo in the annular phase.

[0017] Figure 3 This is a SEM image of the cermet used in the crushing, stirring, mixing, and kneading mechanism of Example 1.

[0018] Explanation of reference numerals in the attached figures

[0019] 1. Cross-sectional microstructure of cermets

[0020] 2 core phases

[0021] 3. Ring phase

[0022] 4. Metallic phase

[0023] 5 Mo has relatively more phases Detailed Implementation

[0024] The crushing, stirring, mixing, and kneading mechanism of the present invention can be implemented through the following methods.

[0025] First, powders arbitrarily selected from Ti or Ti compounds, Mo or Mo compounds, Cr or Cr compounds, Co or Co compounds, Ni or Ni compounds, and carbon, carbides or carbonitrides are used as raw materials, with each element having a mass ratio of Ti: 15-40%, Mo: 2-29%, Cr: 1-15%, C: 2-20%, Co: 10-50%, Co and Ni totaling 30%-55%, and a Co / Ni ratio exceeding 1.

[0026] For example, the compounds used for Ti can be any form of carbides, nitrides, carbonitrides, or complex carbonitrides, such as TiC, TiN, TiCN, (Ti,Mo)(C,N), or (Ti,W)(C,N). The same applies to Mo, Cr, Co, and Ni. Furthermore, carbon, carbides, or carbonitrides can be used as the carbon (C) source.

[0027] Then, they are wet- or dry-mixed to obtain a mixed powder, which is then pressed into a molded body under a pressure of 50–300 MPa. This molded body is then sintered at 1300–1700 °C in any atmosphere of vacuum, reduction, inert gas, hydrogen, or nitrogen, thereby obtaining a pulverizing, stirring, mixing, and compounding mechanism containing cermet. This cermet has three phases: a core phase, a ring phase, and a metallic phase. The specific design of each phase is described below. It should be noted that in the following description, the mass ratio of each element refers to the mass ratio at the raw material stage.

[0028] (Design of core phase and toroidal phase)

[0029] By setting the carbon content to 2-20%, a hard phase composed of fine core and ring phases with improved sinterability is formed. When the carbon content is less than 2%, a core and ring phase with sufficient volume is not formed, resulting in reduced wear resistance. On the other hand, when more than 20% carbon is added, a free carbon phase is generated, which significantly reduces mechanical properties (strength, hardness, impact resistance) and corrosion resistance.

[0030] Nitrogen (N) can be omitted, or, if added, can be added arbitrarily within a range exceeding 0% but not exceeding 5%. Adding N tends to reduce the thickness of the annular phase, improving wear resistance and impact resistance. Furthermore, by keeping the N content below 5%, residual porosity in the alloy caused by nitrogen gas generated during sintering can be suppressed, thereby improving mechanical properties.

[0031] Furthermore, the preferred ratio is C:N = 7:3 to 10:0. By setting the C:N ratio within this range, good wettability is maintained between the metallic phase and the hard phase composed of the core phase and the annular phase, thereby improving density.

[0032] Mo is mixed in the range of 2% to 29%. TiCN, which forms the core phase, has poor wettability with Co and Ni, which form the metallic phase. However, by adding a cyclic phase such as Mo₂C, the wettability of the hard phase composed of the core and cyclic phases can be improved. This improves the sinterability of the material and enhances its mechanical properties. Furthermore, the addition of Mo is also effective from the viewpoint of improving corrosion resistance. On the other hand, when more than 29% of Mo is added, the impact resistance decreases.

[0033] The Cr content is mixed in the range of 1% to 15%. When the Cr content is less than 1%, sufficient corrosion resistance cannot be obtained. On the other hand, when more than 15% of Cr is added, wear resistance and magnetism decrease.

[0034] The total content of Cr and Mo (Cr+Mo) is preferably 3% to 30%. The higher the content of (Cr+Mo), the better the corrosion resistance. However, if it exceeds 30%, abnormal phases may appear, which will reduce the impact resistance.

[0035] W can be omitted, or, if added, can be added arbitrarily within a range of more than 0 and less than 10%. Adding W further improves wear resistance. This is because the hard phase, composed of the core and ring phases, is strengthened by W atoms through solid solution, making it less prone to destruction during abrasive wear.

[0036] It should be noted that when the total Mo and W content is below 35%, alloys of W and Co, Mo and Co, or W and Mo and Co are not formed, and the impact resistance is further improved.

[0037] (Design of the metallic phase)

[0038] The combined Co and Ni content is 30–55%. When the metal content is less than this range, the impact resistance becomes insufficient. When the metal content is more than this range, the wear resistance decreases, and the wear on components of crushing, stirring, mixing, and compounding mechanisms becomes more severe.

[0039] Furthermore, the Co / Ni ratio is greater than 1. By adding a large amount of Co, which has superior mechanical properties (hardness, wear resistance) compared to Ni, the mechanical properties of crushing, stirring, mixing, and kneading components can be improved. Moreover, the interaction with the improved corrosion resistance caused by the addition of Cr and Mo can extend the service life of crushing, stirring, mixing, and kneading components.

[0040] Furthermore, cermets containing a combined Co and Ni content of 30% or more possess sufficient magnetism for magnetic separation. Magnetic separation is used in crushing, stirring, mixing, and kneading equipment for detecting foreign matter in materials caused by component chips, etc.

[0041] As an example, the crushing, stirring, mixing, and kneading mechanism of the present invention can be manufactured using the following manufacturing method.

[0042] (Manufacturing method)

[0043] In manufacturing the crushing, stirring, mixing, and kneading mechanism of the present invention, the following steps (processes) are included.

[0044] That is, the steps are as follows: using powders of any choice from Ti or Ti compounds, Mo or Mo compounds, Cr or Cr compounds, Co or Co compounds, Ni or Ni compounds, and carbon, carbides or carbonitrides as raw materials, in a manner where the mass ratio of each element is Ti: 15-40%, Mo: 2-29%, Cr: 1-15%, C: 2-20%, Co and Ni combined to 30%-55%, and the Co / Ni ratio is greater than 1, mixing them wet or dry to obtain a mixed powder; pressing the mixed powder under a pressure of 50-300 MPa to obtain a pressed body; and sintering the pressed body at 1300-1700°C in any atmosphere of vacuum, reduction, inactive gas, hydrogen or nitrogen.

[0045] In wet mixing, a volatile solvent such as ethanol is used as the solvent, and the slurry is dried by vacuum settling or spray drying. At this time, the particle size of the core and ring-shaped phases formed after the raw material mixing (hereinafter referred to as "particle size before sintering") is appropriately adjusted according to the target value of the average particle size of the hard phase after sintering. For example, when the target value of the average particle size of the hard phase after sintering is less than 3 μm, the particle size before sintering can be 2.0 μm or less, preferably 1.5 μm or less, more preferably 1.0 μm or less, and even more preferably 0.6 μm or less. Generally, particle growth is achieved through sintering. If the particle size before sintering is 2.0 μm or less, the generation of coarse hard particles can be suppressed. If it is 1.5 μm or less, the average particle size of the hard phase after sintering can easily be made less than 3 μm. If it is 1.0 μm or less, the average particle size of the hard phase after sintering becomes smaller, and the wear resistance is improved. Furthermore, if the micrometer size is below 0.6 μm, sintering can be performed at lower temperatures, thereby improving wear resistance.

[0046] On the other hand, if the average particle size of the hard phase after sintering is 3 μm or more, large raw material powder can be used as the raw material powder constituting the core phase, or the raw material powder can be pulverized without pulverizing, or pulverized for a short time. For example, the particle size before sintering can be set to 2 μm or more.

[0047] The resin component, which forms the molding binder, is mixed into the obtained raw material powder and then granulated. Spray drying can also be used in the granulation process.

[0048] The granulated powder is then pressed into shape using a molding press or isostatic press at a pressure of 50–300 MPa. After molding, it can be introduced into intermediate processing as needed.

[0049] Regarding sintering conditions, formal sintering is carried out in a vacuum or gas atmosphere at 1300–1700°C. Degreasing and pre-sintering processes can be introduced before formal sintering, and intermediate processing can be introduced as needed at various stages after degreasing and pre-sintering. Degreasing and pre-sintering processes can be performed continuously, or they can be performed continuously with formal sintering. In the case of degreasing and pre-sintering, it is carried out in a vacuum or gas atmosphere at 600–1000°C. Furthermore, hot water pressing can be performed as needed.

[0050] Finally, it is precision machined into its final shape through machining or electrical discharge machining to obtain the target crushing, stirring, mixing, and compounding mechanism component.

[0051] (The microstructure of metal-ceramic components used in crushing, stirring, mixing, and compounding mechanisms)

[0052] The microstructure of the cermet used in this invention was confirmed by cross-sectional observation using SEM.

[0053] The above-mentioned metal ceramics, such as in Figure 1 The diagram schematically illustrates a cross-sectional microstructure 1, comprising a core phase 2 with Ti(C,N) as the main component (including the case where N=0, i.e., TiC in the absence of N), a ring phase 3 surrounding the core phase 2 and composed primarily of (Ti,Mo,Cr)(C,N) (including the case where N=0, i.e., (Ti,Mo,Cr)C in the absence of N), and a metallic phase 4. In principle, cermets do not contain Mo2C or chromium carbide phases. In the presence of Mo2C and chromium carbide phases, SEM (scanning electron microscopy) observation reveals that the metallic phase, besides the core and ring phases, exists as particles of varying brightness. In cases where the presence or absence of Mo2C and chromium carbide phases cannot be determined, analysis using EPMA (electron probe microanalysis), EDX (energy dispersive X-ray diffraction), and XRD (X-ray diffraction) is employed to comprehensively determine the presence or absence of the Mo2C and chromium carbide phases. Under irregular observation conditions, at a magnification of 10,000x, there are fewer than one particle larger than 1 μm and fewer than five particles larger than 0.3 μm. It should be noted that in this invention, "no Mo2C phase and chromium carbide phase were observed by SEM" also includes the aforementioned situation where there are fewer than one particle larger than 1 μm and fewer than five particles larger than 0.3 μm in the 10,000x magnification field of view.

[0054] By configuring it as described above, a material with high impact resistance and wear resistance can be obtained.

[0055] In addition, the aforementioned cermets have the following characteristics.

[0056] (Core Phase)

[0057] The core phase is a hard phase with Ti(C, N) as the main component (including the case where N=0), and has high hardness.

[0058] (ring phase)

[0059] The toroidal phase exists around the core phase, with (Ti, Mo, Cr) or (C, N) (including the case where N=0) as the main components. For example... Figure 2 As shown, the annular phase can also contain two phases: one with a relatively high Mo content and the other with a relatively high Ti content. When the annular phase contains two phases, its hardness increases, and its wear resistance is further improved.

[0060] (particle size)

[0061] There is no particular limitation on the average grain size of the hard phase, which consists of the core phase and the annular phase. The average grain size of the hard phase can be observed by SEM of the cross-sectional microstructure of the cermet and is calculated by the following Felman formula (Mathematical Formula 1).

[0062] [Mathematical Expression 1]

[0063] d m = (4 / π) × (N) L / N S (Equation 1)

[0064] N L =n L / L (Equation 2)

[0065] N S =n S / S (Equation 3)

[0066] In equation (1), d m N represents the average particle size, π represents pi, and N represents the average particle size. L N represents the number of particles per unit length hit by any straight line on the cross-section of the tissue. S Let n represent the number of particles contained in any unit area, in equation (2). L Let n represent the number of particles hit by any straight line on the cross-section, and L represent the length of any straight line on the cross-section. In Equation 3, n S The number of particles contained within any measurement area is represented by , and S represents the area of ​​any measurement region.

[0067] The average particle size of the hard phase, composed of a core phase and a ring-shaped phase, can be less than 3 μm. By reducing the average particle size of the hard phase to less than 3 μm, the hardness and wear resistance are improved. In particular, by reducing the average particle size of the hard phase to below 1.5 μm, the hardness and wear resistance are further improved.

[0068] On the other hand, the average particle size of the hard phase can also be set to 3 μm or more. By making the average particle size of the hard phase 3 μm or more, the fracture toughness is improved.

[0069] Thus, the average particle size of the hard phase can be appropriately determined according to the specific application (necessary characteristics). It should be noted that when the average particle size of the hard phase is 3 μm or more, there is no particular upper limit to its average particle size; it can be determined within the scope of common technical knowledge, for example, it can be set to 10 μm or less. It should also be noted that when the average particle size of the sintered hard phase is set to 3 μm or more and 10 μm or less, for example, the particle size before sintering can be set to 2 μm or more and 7 μm or less.

[0070] (proportion)

[0071] The specific gravity of the crushing, stirring, mixing, and kneading mechanism components involved in this embodiment is 9 or less. Crushing, stirring, mixing, and kneading machines have traditionally been designed with steel components as the basis for assembly. Therefore, when the specific gravity of the components exceeds 9, it leads to the deflection of the rotating shaft and an increase in the load on the drive unit. When the specific gravity is 8 or less, it is possible to perform the same processing as steel materials, and further, when the specific gravity is 7.5 or less, it is lighter than steel materials, allowing for greater flexibility in device design.

[0072] For cermets possessing the aforementioned characteristics, while their wear resistance is comparable to or greater than that of superhard alloys, their specific gravity is similar to that of steel, thus exhibiting magnetic properties and high impact resistance and corrosion resistance. By using this material as a component in crushing, stirring, mixing, and compounding mechanisms, it is possible to suppress breakage caused by contact between components, wear during use, and corrosion, thereby extending the service life of the components.

[0073] Example

[0074] First, the raw material powders shown in Example 1 of Table 1 are pulverized and mixed using ethanol as a solvent via a grinder or ball mill. The resulting slurry is dried in a vacuum, and the resulting alkanes, which will become the binder, are then mixed and pressed into a compressed body.

[0075] The pressed body is pre-sintered at 800°C under atmospheric hydrogen atmosphere, and then formally sintered at 1400°C under vacuum atmosphere, thereby obtaining the metal ceramic used in the crushing, stirring, mixing and kneading mechanism of the present invention.

[0076] The average particle size of the cermet obtained in Example 1, calculated according to the above-described Firmman formula, is 1.13 μm.

[0077] Examples 2 and thereafter, as well as comparative examples, were sintered at the lowest temperature at which the highest density was obtained within the range of 1300–1500°C. Other conditions were the same as in Example 1.

[0078] Furthermore, in Examples 1-13 and all comparative examples, the average particle size of the hard phase composed of the core phase and the annular phase was less than 1.5 μm. On the other hand, in Examples 14 and 15, the average particle size of the hard phase composed of the core phase and the annular phase was about 5 μm. It should be noted that Comparative Example 1 corresponds to "Example 1" shown in Table 1 of the aforementioned Patent Document 1.

[0079] Furthermore, SEM observation was used to examine the composition of the cermet cross-section microstructure. The results showed that no Mo2C, chromium carbide, or WC phases were detected in any of the embodiments. Additionally, a relatively high Mo content was observed in the annular phase in all embodiments.

[0080] The overall elemental composition ratio of cermet materials deviates significantly from that of the raw materials. Furthermore, the coefficient of determination between the raw material composition and the composition ratio of the sintered cermet is low, making accurate quantification impossible. As explained in Patent Document 1 above, this is attributed to the influence of changes in the lattice state caused by the formation of solid solutions between the constituent elements. Specifically, as described in Non-Patent Document 1 cited in Patent Document 1 (Kawabata, Fujimura, and Chitoku, "Powders and Powder Metallurgy," Vol. 29, No. 1 (1980), pp. 30-34), it is known that past research has struggled to quantify the alloy composition of cermet materials, making accurate quantification difficult.

[0081] Thus, in this invention, it is impossible or impractical to directly determine the object based on its structure or characteristics; in this invention, there exists what is called an "impossible / impractical situation".

[0082] [Table 1]

[0083]

[0084] [Table 2]

[0085]

[0086] Next, the properties of the manufactured cermet were evaluated using the measurement methods shown below.

[0087] *Specific gravity...Archimedes method (Standard: JIS Z 8807)

[0088] *Hardness... Vickers Hardness Test (Standard: JIS Z 2244)

[0089] *Abrasion resistance... Rubber wheel test (Standard: ASTM G65)

[0090] *Impact resistance...Charpy impact test using test pieces with a 10R notch (Standard: JIS Z 2242)

[0091] * Fracture toughness value... JIS R 1607 (IF method)

[0092] *Magnetic Saturation Magnetization Measurement

[0093] *Corrosion resistance... An immersion test was conducted in an acidic solution at room temperature for 24 hours. The depth of corrosion progression was calculated based on the weight loss before and after the test, as well as the shape and specific gravity of the test piece.

[0094] The characteristics of the cermets in the embodiments and comparative examples of the present invention are shown in Table 3.

[0095] Here, regarding the evaluation criteria for impact resistance (Charpy impact value) and corrosion resistance, exceeding the level of "Comparative Example 1" as the cermet disclosed in the aforementioned Patent Document 1 is set as a qualified level. Furthermore, regarding the evaluation criteria for wear resistance and magnetism, being equal to or better than superhard alloys (JIS classification: V40 equivalent material) is set as a qualified level.

[0096] [Table 3]

[0097]

[0098] ※Super Hard Wear Volume (mm) 3 / Sample wear volume (mm) 3 )

[0099] In all embodiments, the impact resistance and corrosion resistance exceeded those of "Comparative Example 1," the cermet disclosed in Patent Document 1, demonstrating excellent impact resistance and corrosion resistance. Furthermore, the specific gravity was suppressed to below the target value of 9, all lower than the specific gravity of SKD (7.7). Additionally, regarding wear resistance, it was equivalent to or better than that of superhard alloys (JIS classification: V40 equivalent material).

[0100] It should be noted that in Example 5, where the amount of W added is 10% or more, the improvement effect on impact resistance is reduced compared to other examples. Furthermore, in Examples 3 and 4, where the amount of W added is 6% or more, the improvement effect on impact resistance is slightly reduced compared to other examples. Therefore, it can be seen that when W is added, the amount added is preferably less than 10%, more preferably less than 6%. It should be noted that, as demonstrated in Examples 12 and 13, W may not be added to the cermet of the present invention. Furthermore, as demonstrated in Examples 14 and 15, it can be seen that by making the average particle size of the hard phase 3 μm or more, the fracture toughness is improved.

[0101] Comparative Example 1 is the cermet disclosed in the aforementioned Patent Document 1, which has insufficient impact resistance and corrosion resistance.

[0102] In Comparative Example 2, the corrosion resistance was reduced due to the low amount of Cr added.

[0103] In Comparative Example 3, the wear resistance and saturation magnetization were reduced due to the large amount of Cr added.

[0104] In Comparative Example 4, the wear resistance and saturation magnetization were reduced due to the low amount of Mo added.

[0105] In Comparative Example 5, the impact resistance was reduced due to the high amount of Mo added.

[0106] In Comparative Example 6, since the Co / Ni ratio is less than 1, the wear resistance and saturation magnetization are reduced.

[0107] In Comparative Example 7, the wear resistance was reduced due to the high amount of metallic phase (Co+Ni).

[0108] In Comparative Example 8, the impact resistance was reduced due to the low amount of metallic phase (Co+Ni).

[0109] exist Figure 3 The image shows a SEM image of the cermet of Example 1. The darkest part is the core phase, the darker parts are the annular phase, and the lightest part is the metallic phase.

Claims

1. Mechanisms for crushing, stirring, mixing, and compounding metals and ceramics, wherein, The metal-ceramic is obtained through the following steps: The method involves mixing powders selected from Ti or Ti compounds, Mo or Mo compounds, Cr or Cr compounds, Co or Co compounds, Ni or Ni compounds, and carbon, carbides or carbonitrides as raw materials in a wet or dry manner, with each element having a mass ratio of Ti: 15-40%, Mo: 2-29%, Cr: 1-15%, C: 2-20%, Co and Ni totaling 30%-55% and a Co / Ni ratio exceeding 1, and the total mass ratio of Cr and Mo in the raw materials being 3-30%. The step of pressing the mixed powder under a pressure of 50-300 MPa to obtain a pressed body; and The step of sintering the pressed body at 1300–1700°C under any atmosphere of vacuum, reduction, inert gas, hydrogen, or nitrogen. The cermet comprises three phases: a core phase mainly composed of Ti (C, N), a ring-shaped phase mainly composed of (Ti, Mo, Cr)(C, N) surrounding the core phase, and a metallic phase. The core phase contains Ti (C, N) with N=0 as the main component, and the ring-shaped phase contains (Ti, Mo, Cr)(C, N) with N=0 as the main component. No Mo2C or chromium carbide phases were observed by SEM.

2. The crushing, stirring, mixing, and compounding mechanism comprising metal ceramics according to claim 1, wherein, The ratio of the total mass ratio of Cr to Mo in the raw material (Cr+Mo) to the total mass ratio of Co to Ni in the raw material (Co+Ni) ((Cr+Mo) / (Co+Ni)) is 0.24 to 1.

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