Clay-in steel bond hard alloy bimetal composite toothed plate and preparation method thereof

Abstract

The invention relates to an embedded steel bond hard alloy bimetal composite toothed plate which comprises a tough base plate and a wear-resistant surface plate, a steel bond ZTA hard alloy tooth assembly is embedded in the wear-resistant surface plate, the steel bond ZTA hard alloy tooth assembly penetrates through an interface between the tough base plate and the wear-resistant surface plate, and the head end of the steel bond ZTA hard alloy tooth assembly reaches or penetrates out of the wear-resistant surface plate. The tail end is positioned in the tough base plate; and the wear-resistant surface layer plate and the tough base layer plate are molded by adopting a double-pouring method. The steel-bonded ZTA hard alloy tooth assembly comprises the following raw materials in percentage by volume: 50-60% of high manganese steel matrix powder, 10-15% of a hard phase, 10-30% of metallized ZTA ceramic particles, 3-5% of an interface wetting agent, 0.5-1% of a carbon compensating agent and 1-2% of a forming agent. And the hard phase is at least one of WC, TiC and TiB2. According to the invention, the steel bond ZTA hard alloy tooth assembly is utilized to enhance the binding force of the double metal layers, and the optimization of the components of the steel bond ZTA hard alloy tooth assembly is combined, so that the ore handling capacity of a single toothed plate is improved, and the comprehensive use cost is reduced.

Description

Technical Field

[0001] The present invention relates to the technical field of metal materials, and particularly relates to an inlaid cast steel-bonded carbide bimetallic composite tooth plate and a preparation method thereof. Background Art

[0002] Traditional mine crusher tooth plates face three major problems: insufficient wear resistance (the service life of high manganese steel is only 3 - 6 months), poor impact resistance (carbide is prone to cracking), and interface delamination (low bimetallic bonding strength). In the fields of mine crushing, ore dressing, and building materials processing, tooth plates, as the core wear-resistant components of equipment such as jaw crushers and roll crushers, are long-term exposed to harsh working conditions such as high-stress impact, abrasive wear, and corrosion. Traditional tooth plates are mainly made of high manganese steel (such as ZGMn13) or alloy steel. Although they have good toughness, their hardness and wear resistance are insufficient, resulting in short service life, frequent replacement, seriously affecting production efficiency and increasing maintenance costs. The ore processing capacity of a single set of tooth plates is also relatively low.

[0003] In recent years, steel-bonded carbides (such as WC / Fe-based composites) have been introduced into tooth plate manufacturing due to their high hardness and wear resistance. However, they are brittle and have poor impact resistance, and are prone to cracking or fracture failure during ore crushing. In addition, existing bimetallic composite tooth plates (such as high-chromium cast iron + low-alloy steel) can balance wear resistance and toughness, but the interface bonding strength is insufficient, and delamination is prone to occur under long-term impact loads, affecting the overall performance of the tooth plate.

[0004] Ceramic particle (such as Al2O3, SiC, TiC) reinforced metal matrix composites (MMCs) have become a research hotspot due to their ultra-high hardness and wear resistance. However, traditional processes (such as powder metallurgy, hot pressing sintering) are difficult to achieve high-strength metallurgical bonding between ceramic particles and steel matrix, and the cost is high, which limits their large-scale industrial application.

[0005] Therefore, there is an urgent need to develop a new type of composite tooth plate. By optimizing the material system and preparation process, while ensuring high toughness, significantly improving wear resistance, and ensuring interface bonding strength, the ore processing capacity of a single set of tooth plates can be greatly increased, and the comprehensive use cost can be reduced. Summary of the Invention

[0006] (I) Technical Problems to be Solved

[0007] In view of the above-mentioned disadvantages and deficiencies of the prior art, the present invention provides a cast-inlaid steel-bonded cemented carbide bimetallic composite tooth plate and a preparation method thereof. The composite tooth plate adopts a bimetallic and steel-bonded ZTA ceramic-cemented carbide composite process, uses a double-casting method to form a bimetallic layer, and utilizes a steel-bonded ZTA cemented carbide tooth assembly to enhance the bonding force of the bimetallic layer. Combining with the optimization of the composition of the steel-bonded ZTA cemented carbide tooth assembly, while ensuring high toughness, the wear resistance is significantly improved, and the interfacial bonding strength is ensured, thereby greatly increasing the ore processing capacity of a single set of tooth plates and reducing the comprehensive use cost.

[0008] (II) Technical Solution

[0009] In the first aspect, the present invention provides a cast-inlaid steel-bonded cemented carbide bimetallic composite tooth plate, which includes: a tough base plate and a wear-resistant surface plate. A number of steel-bonded ZTA cemented carbide tooth assemblies are cast inlaid in the wear-resistant surface plate, and the steel-bonded ZTA cemented carbide tooth assemblies penetrate the interface between the tough base plate and the wear-resistant surface plate. The head end of the steel-bonded ZTA cemented carbide tooth assembly reaches or penetrates the wear-resistant surface plate, and its tail end is located within the tough base plate; the wear-resistant surface plate and the tough base plate are formed by double-casting in a mold pre-embedded with cemented carbide tooth assemblies;

[0010] Among them, by volume percentage, the raw material formula of the steel-bonded ZTA cemented carbide tooth assembly is: 50-60% of high manganese steel matrix powder, 10-15% of hard phase, 10-30% of metallized ZTA ceramic particles, 3-5% of interfacial wetting agent, 0.5-1% of carbon compensator, and 1-2% of molding agent; the hard phase is at least one of WC, TiC, and TiB2.

[0011] According to a preferred embodiment of the present invention, the high manganese steel matrix powder is a pre-alloyed powder with a particle size of 5-20 μm; the pre-alloyed powder contains 1.0 wt% ± 0.1 of C, 12 wt% ± 1.0 of Mn, 1.5 wt% ± 0.2 of Cr, 0.5 wt% ± 0.05 of Mo, and the balance is Fe.

[0012] According to a preferred embodiment of the present invention, the particle size of the hard phase is submicron; the hard phase is preferably mainly WC (70 Vol.%), supplemented by TiC or TiB2 (30 Vol.%), or the hard phase is preferably a combination of WC, TiC, and TiB2, and the combined volume ratio of the three components in the hard phase is WC:TiC:TiB2 = 6:3:1, 7:2:1, or 5:3:2.

[0013] According to a preferred embodiment of the present invention, the particle size of the metallized ZTA ceramic particles is 8-20 mesh; the ZTA ceramic particles are Al2O3 particles reinforced with yttrium-stabilized zirconia (YSZ), and the YSZ content is 20 wt%.

[0014] According to a preferred embodiment of the present invention, the interfacial wetting agent is Ni powder, which promotes metal-ceramic bonding; the carbon compensator is graphite to make up for the carbon loss during the processing of the steel-bonded ZTA cemented carbide tooth assembly; the forming agent is a paraffin-based binder, a polymer composite system or a water-soluble temporary binder to ensure sufficient fluidity and green body strength during powder pressing. The paraffin-based is a paraffin + PE composite system. The polymer composite system consists of polyethylene (PE) + polypropylene (PP) + stearic acid (lubricant), and the water-soluble temporary binder is polyethylene glycol (PEG) + cellulose ether (such as hydroxypropyl methyl cellulose HPMC). The carbon compensator can prevent the formation of brittle η phase of TiB2.

[0015] According to a preferred embodiment of the present invention, the steel-bonded ZTA cemented carbide tooth assembly is in the shape of a rod or a block, and anti-slip grooves are integrally formed on its surface to increase the bonding force between the steel-bonded ZTA cemented carbide tooth assembly and the tough base plate and the wear-resistant surface plate.

[0016] According to a preferred embodiment of the present invention, the tough base plate is low-carbon steel ZG230-450 or low-carbon alloy steel with a carbon equivalent between 0.20-0.30 wt%; the wear-resistant surface plate is high manganese steel (such as ZGMn13), alloy steel or high chromium cast iron; during the preparation process, corresponding heat treatment processes are adopted according to the material composition of the wear-resistant surface plate.

[0017] In a second aspect, the present invention provides a method for preparing a cast-inlaid steel-bonded cemented carbide bimetallic composite tooth plate, which includes:

[0018] S1. Set a double gating system according to the shape of the composite tooth plate, weld a steel nail to one end of the pre-prepared steel-bonded ZTA cemented carbide tooth assembly, and then fix it at the position where the tooth plate needs to be strengthened in the mold; the raw material formula of the steel-bonded ZTA cemented carbide tooth assembly is: 50-60% of high manganese steel matrix powder, 10-15% of hard phase, 10-30% of metallized ZTA ceramic particles, 3-5% of interfacial wetting agent, 0.5-1% of carbon compensator and 1-2% of forming agent; the hard phase is at least one of WC, TiC and TiB2;

[0019] S2. Melt the molten steel of the tough base plate and the molten steel of the wear-resistant surface plate respectively. First, pour the molten steel of the wear-resistant surface plate into the mold from one gating port, and after a preset time interval, pour the molten steel of the tough base plate into the mold from the other gating port until the filling is complete;

[0020] S3. Heat treatment; adopt corresponding heat treatment processes according to the material composition of the wear-resistant surface plate.

[0021] Furthermore, the preparation method of the steel-bonded ZTA cemented carbide tooth assembly is as follows:

[0022] Step 1: Stir the high manganese steel matrix powder and the hard phase evenly and carry out ball milling to obtain a mixed powder;

[0023] Step 2: Mix the metallized ZTA ceramic particles evenly with the ball-milled mixed powder, add a forming agent, an interfacial wetting agent and a carbon compensating agent, and mix evenly again to obtain a forming material; the metallized ZTA ceramic particles are obtained by subjecting ZTA ceramic particles to surface metallization treatment by the Mo-Mn method or the electroless nickel plating method (to promote their wettability with cemented carbide);

[0024] Step 3: Load the forming material into the mold cavity, perform double-direction cold pressing at a pressure of 600-1000 Mpa, hold the pressure for 2-3 min, and demold to obtain a green blank;

[0025] Step 4: Carry out vacuum degreasing, vacuum sintering, and hot isostatic pressing treatments, and then cool under a protective atmosphere to obtain a steel-bonded ZTA cemented carbide tooth assembly.

[0026] In Step 4, the vacuum sintering conditions are: keep warm at 600 °C ± 10 °C for 55-65 min, and the heating rate is 4.5-5.5 °C / min; the vacuum sintering conditions: keep warm at 1280-1320 °C for 2 h, and the vacuum degree ≤ 10 -2 Pa; the hot isostatic pressing treatment conditions are: treat in argon at 1200 °C × 100 MPa for 1 h to eliminate residual pores; cooling under a protective atmosphere means cooling in a protective atmosphere of argon or nitrogen.

[0027] Preferably, the heat treatment method in Step S3 is: when the material composition of the wear-resistant surface layer plate is high manganese steel (such as ZGMn13), the heat treatment adopts the water toughening treatment process of high manganese steel; when the material composition of the wear-resistant surface layer plate is alloy steel, the heat treatment adopts the quenching + tempering process of alloy steel; when the material composition of the wear-resistant surface layer plate is high chromium cast iron, the heat treatment adopts the air quenching (or fog quenching) + tempering process of high chromium cast iron.

[0028] Preferably, by volume percentage, the raw material formula of the steel-bonded ZTA cemented carbide tooth assembly is: preferably 55-60% of high manganese steel matrix powder, 12-15% of hard phase, 20-25% of metallized ZTA ceramic particles, 4-5% of interfacial wetting agent, 0.8-1% of carbon compensating agent, and 1.2-1.6% of forming agent.

[0029] (III) Beneficial effects

[0030] 1. The composite tooth plate of the present invention uses a steel-bonded ZTA cemented carbide tooth component to penetrate the interface between the ductile base layer and the wear-resistant surface layer, forming a mechanical-metallurgical dual bond, greatly improving the interface shear strength to ≥450 MPa (only 250-300 MPa for the traditional inlay casting process). The steel-bonded ZTA cemented carbide tooth component uses ZTA ceramic particles in cooperation with WC / TiC / TiB2 hard phases to achieve high hardness (HV 2600-2700), high wear resistance, thermal conductivity, thermal shock resistance, high impact resistance, high modulus, and excellent fracture toughness and anti-cracking properties on the surface layer. Among them, the high manganese steel matrix in the steel-bonded ZTA cemented carbide tooth component is pre-alloyed, containing C (1.0 wt%), Mn (12 wt%), and Cr (1.5 wt%). After sintering, the austenite stability is improved, and the work hardening rate is increased. Among them, the hard phase is preferably a ternary hard phase composed of WC:TiC:TiB2. Through solid solution strengthening and grain boundary pinning, compared with pure WC (fracture toughness 9-10 MPa·m 1 / [[ID=! 2 )), the fracture toughness can be significantly improved.

[0031] 2. When preparing the steel-bonded ZTA cemented carbide tooth component of the present invention, according to various working conditions, by adjusting the proportion of the hard phase (such as 5:3:2 for high impact and 7:2:1 for high wear), it can cover crushing scenarios such as iron ore, limestone, granite, and copper ore.

[0032] 3. When preparing the composite tooth plate of the present invention, double-pouring time sequence control is adopted. First, the wear-resistant surface layer plate (high manganese steel) is poured, and then the ductile base layer plate (low carbon steel) is poured to avoid interface segregation, and the porosity is <1.5%. The present invention adopts the double-pouring method to form in one step, reducing subsequent welding / bolting processes and greatly improving production efficiency. When preparing the steel-bonded ZTA cemented carbide tooth component, vacuum sintering + hot isostatic pressing (HIP) is adopted to reduce the residual porosity to below 0.05% and reduce the cracks at the ZTA ceramic-metal interface. BRIEF DESCRIPTION OF THE DRAWINGS

[0033] Figure 1 FIG. is a front structural schematic diagram of the wear-resistant surface layer plate of the inlaid steel-bonded cemented carbide bimetallic composite tooth plate.

[0034] Figure 2 FIG. is a side schematic diagram of the inlaid steel-bonded cemented carbide bimetallic composite tooth plate.

[0035] Figure 3 FIG. is a three-dimensional structural schematic diagram of the inlaid steel-bonded cemented carbide bimetallic composite tooth plate. [[ID=2!

[0036] Figure 4 FIG. is a schematic diagram of the double-pouring system for preparing the inlaid steel-bonded cemented carbide bimetallic composite tooth plate.

[0037] Figure 5Schematic diagram of pre-burying the steel-bonded ZTA cemented carbide tooth assembly at a predetermined position in the mold of a double-pouring system before pouring.

[0038] Figure 6 Schematic diagram of the structure of the steel-bonded ZTA cemented carbide tooth assembly. Specific implementation mode

[0039] For better explaining the present invention for easy understanding, the present invention will be described in detail below in conjunction with the drawings through specific implementation modes.

[0040] Combined Figures 1-3 As shown, the inlaid-cast steel-bonded cemented carbide bimetallic composite tooth plate of a preferred embodiment of the present invention includes a tough base plate 2, a wear-resistant surface plate 1, and a steel-bonded ZTA cemented carbide tooth assembly 3. There is a bonding interface 11 between the tough base plate 2 and the wear-resistant surface plate 1. The steel-bonded ZTA cemented carbide tooth assembly 3 is a strip-shaped assembly, such as a rod-shaped or block-shaped one. The tough base plate 2 is located below the wear-resistant surface plate 1, and it is usually connected to the crusher jaw body through a liner plate. The wear-resistant surface plate 1 directly contacts the ore and is the working surface for ore crushing. A number of steel-bonded ZTA cemented carbide tooth assemblies 3 are inlaid in the wear-resistant surface plate 1, and the steel-bonded ZTA cemented carbide tooth assemblies 3 penetrate through the bonding interface 11 between the tough base plate 2 and the wear-resistant surface plate 1. The head end of the steel-bonded ZTA cemented carbide tooth assembly 3 reaches the wear-resistant surface plate 1, and preferably is close to or penetrates through the surface of the wear-resistant surface plate 1, and its tail end is located in the tough base plate 2. The steel-bonded ZTA cemented carbide tooth assembly 3 strengthens the connection relationship between the tough base plate 2 and the wear-resistant surface plate 1. Among them, the wear-resistant surface plate 1 and the tough base plate 2 are integrally cast in a mold pre-buried with the cemented carbide tooth assembly 3 by a double-pouring method.

[0041] As Figure 6 shown, the schematic diagram of the structure of the steel-bonded ZTA cemented carbide tooth assembly 3. The steel-bonded ZTA cemented carbide tooth assembly 3 is designed as a long-shaped rod or block, and anti-slip grooves 31 are integrally formed on its surface. These anti-slip grooves 31 are provided at both ends of the steel-bonded ZTA cemented carbide tooth assembly 3 or cover the entire outer surface of the steel-bonded ZTA cemented carbide tooth assembly 3, and are used to increase the bonding firmness between it and the tough base plate 2 and the wear-resistant surface plate 1. The steel-bonded ZTA cemented carbide tooth assembly 3 includes a high-manganese steel matrix and a number of ZTA ceramic particles 32 dispersed in the high-manganese steel matrix ( Figure 6 ).

[0042] Among them, the ductile base plate 2 and the wear-resistant surface plate 1 are respectively cast and formed from different metal melts. The ductile base plate 2 is made of low-carbon steel ZG230-450 or low-carbon alloy steel with a carbon equivalent between 0.20-0.30 wt%. The wear-resistant surface plate 1 is made of high manganese steel, alloy steel or high chromium cast iron. The functions of the ductile base plate 2 include: ① providing impact resistance support, absorbing the dynamic load during ore crushing, and preventing brittle fracture; ② structural fixation: connecting to the crusher body through welding or bolts to provide mechanical stability; ③ interface stress buffering: coordinating the thermal expansion difference between the wear-resistant layer and the machine body (thermal expansion coefficient matching design). The core functions of the wear-resistant surface plate 1 include: ① direct wear resistance: resisting the cutting and chiseling of ore abrasive grains; ② work hardening: the surface hardness of high manganese steel can be increased from HB200 to above HB500 under impact; ③ high-temperature stability: high chromium cast iron maintains red hardness under high-temperature working conditions (such as iron ore crushing).

[0043] The metal material of the ductile base plate 2 is low-carbon steel ZG230-450 (GB / T 11352-2023) or low-carbon alloy steel. Low-carbon steel ZG230-450 has low cost, good weldability (carbon equivalent CE≤0.25%), and is easy to machine, and is more suitable for medium and low impact limestone crushing scenarios. The low-carbon alloy steel is preferably 27MnCr5 (EN 10084) or 30CrMnTi (GB / T 3077-2025). 27MnCr5 improves hardenability by adding Cr (0.8-1.2%) and Mn (1.0-1.3%), and has high tensile strength; it is more suitable for high-frequency impact granite crushing. 30CrMnTi refines grains by adding Ti, has high low-temperature impact toughness at -40°C, is suitable for cold-region mines, and is more suitable for polar or high-altitude mining areas.

[0044] The metal material of the wear-resistant surface plate 1 is high manganese steel (such as ZGMn13), alloy steel (such as 40CrMnMo) or high chromium cast iron (such as Cr26). ZGMn13 (GB / T 5680-2024) has extremely high work hardening ability (surface hardness can reach HB550) and excellent impact resistance (ak≥150J / cm 2) It is applicable to high-impact working conditions such as iron ore and basalt. The hardness of 40CrMnMo (DIN 1.2311) is HRC 48 - 52, with a balanced combination of strength and toughness, and strong reparability, being applicable to the medium and fine crushing in copper mines and gold mines. For high-chromium cast iron such as Cr26 (ASTM A532 ClassIII), the Cr content is 26 - 28%, the hardness is HRC 58 - 62, and it has excellent corrosion resistance (salt spray test > 500h), being very suitable for the crushing working conditions of wet beneficiation or acidic ores. During the preparation process, corresponding heat treatment processes are adopted according to the material composition of the wear-resistant surface plate 1. For example, when the material composition of the wear-resistant surface plate 1 is high manganese steel (such as ZGMn13), the heat treatment adopts the water toughening treatment process for high manganese steel; when the material composition of the wear-resistant surface plate 1 is alloy steel, the heat treatment adopts the quenching + tempering process for alloy steel; when the material composition of the wear-resistant surface plate 1 is high-chromium cast iron, the heat treatment adopts the air quenching (or fog quenching) + tempering process for high-chromium cast iron.

[0045] Among them, the raw material formula of the steel-bonded ZTA cemented carbide tooth assembly 3, by volume percentage, is: 50 - 60Vol.% of high manganese steel matrix powder, 10 - 15Vol.% of hard phase, 10 - 30Vol.% of metallized ZTA ceramic particles, 3 - 5Vol.% of interfacial wetting agent, 0.5 - 1Vol.% of carbon compensator, and 1 - 2Vol.% of forming agent; the hard phase is at least one of WC, TiC, and TiB2. And preferably, the raw material formula is: 55 - 60Vol.% of high manganese steel matrix powder, 12 - 15Vol.% of hard phase, 20 - 25Vol.% of metallized ZTA ceramic particles, 3 - 4Vol.% of interfacial wetting agent, 0.8 - 1Vol.% of carbon compensator, and 1.2 - 1.6Vol.% of forming agent.

[0046] Among them, the high manganese steel matrix powder is a pre-alloyed powder with a particle size of 5 - 20μm. The pre-alloyed powder contains C at 1.0wt% ± 0.1, Mn at 12wt% ± 1.0, Cr at 1.5wt% ± 0.2, Mo at 0.5wt% ± 0.05, and the balance is Fe.

[0047] The particle size of the hard phase is sub-micron level; the hard phase is preferably mainly WC (70Vol.%), with TiC or TiB2 as the auxiliary (30Vol.%), or the hard phase is preferably a combination of WC, TiC, and TiB2.

[0048] The WC particles have an Hv of 2200, leading in wear resistance and with a relatively low cost; the TiC particles have an Hv of 3200, showing excellent high-temperature stability. TiB2 has a high hardness (HV 3400) and high thermal conductivity, and has strong thermal shock resistance. TiB2 has good interfacial wettability with ZTA ceramic particles, can form chemical bonds (generate TiAl3) with the Al2O3 phase in the ZTA ceramic particles, and can reduce interfacial pores; TiB2 also reacts with ZrO2 in ZTA to generate ZrB2 (HV 2800), which can also fill the micro-pores at the ceramic-metal interface. However, the costs of TiC and TiB2 are quite high, and their prices are 2.5 - 3 times and 4 - 6 times that of WC particles respectively.

[0049] Based on the consideration of high cost performance, the combined volume ratio of the three components in the hard phase is selected according to the applicable working conditions of the composite tooth plate. For general working conditions, the preferred ratio is WC:TiC:TiB2 = 6:3:1, and the applicable scenarios include medium and high impact crushing such as iron ore and limestone. For extremely wear-resistant working conditions, the preferred ratio is WC:TiC:TiB2 = 7:2:1, which is suitable for extremely wear-resistant applications such as granite crushing; in extremely wear-resistant working conditions, the proportion of WC is increased to maximize wear resistance, TiC is used to assist in suppressing the growth of WC grains, and a small amount of TiB2 is retained to utilize its thermal conductivity (20 - 25 W / m·K) to relieve thermal stress. For high-strength impact working conditions, the preferred ratio is WC:TiC:TiB2 = 5:3:2, which is suitable for dynamic load scenarios such as copper ore impact crushing. At this ratio, the proportion of TiB2 is relatively high. By utilizing its high modulus and fracture toughness, and the formation of (Ti,W)C solid solution between TiC and WC to strengthen the matrix bonding force, the anti-cracking property of the steel-bonded ZTA cemented carbide tooth assembly is significantly improved; when the working condition of the tooth plate is air-cooled, the proportion of TiB2 can also be appropriately increased for heat conduction.

[0050] Among them, the particle size of the metallized ZTA ceramic particles (represented by the symbol "32" as shown) is 8 - 20 mesh; the ZTA ceramic particles are Al2O3 particles reinforced with yttria-stabilized zirconia (YSZ), and the YSZ content is 20 wt%. The metallized ZTA ceramic particles refer to a layer of metal material coated on the surface of the ZTA ceramic particles to promote their wettability and bonding tightness with the cemented carbide (i.e., high manganese steel matrix powder). The metallized ZTA ceramic particles are products obtained by surface metallization modification of ZTA ceramic particles by the Mo-Mn method or electroless nickel plating method. Figure 6

[0051] ​Among them, the interfacial wetting agent is preferably Ni powder, which is used to promote metal-ceramic bonding. The carbon compensator is graphite to make up for the carbon loss during the processing of the steel-bonded ZTA cemented carbide tooth assembly; the molding agent is a paraffin-based binder, a polymer composite system or a water-soluble temporary binder to ensure sufficient fluidity and green body strength during powder pressing. The paraffin-based binder is a paraffin + PE composite system. The polymer composite system consists of polyethylene (PE) + polypropylene (PP) + stearic acid (lubricant), and the water-soluble temporary binder is polyethylene glycol (PEG) + cellulose ether (such as hydroxypropyl methylcellulose HPMC). The carbon compensator can prevent the formation of brittle η phase in TiB2.

[0052] As Figures 4-5 shown, it is the double-pouring system for preparing the cast-inlaid steel-bonded cemented carbide bimetal composite tooth plate of the present invention and the embedding method of the steel-bonded ZTA cemented carbide tooth assembly 3 in the pouring mold. The double-pouring system includes a mold 100, and the mold 100 includes a cavity 11 (not filled with diagonal lines in the figure) for forming the wear-resistant surface plate 1 and a cavity 22 (filled with diagonal lines in the figure) for forming the tough base plate 2. The cavity 11 and the cavity 22 are in a completely connected state, and a connection interface 21 is formed between the two cavities. The sprue cup 111 is connected to the cavity 11, and the cavity 222 is connected to the cavity 22. After the molten steel is poured from the sprue cup 111, the cavity 11 is filled with molten steel. After the molten steel is poured from the sprue cup 222, the cavity 22 is filled with molten steel. During the double-pouring process, first, the molten steel for forming the wear-resistant surface plate 1 is poured into the cavity 11 from the sprue cup 111, and then the molten steel for forming the tough base plate 2 is poured into the cavity 22 from the sprue cup 222. Among them, several holes are provided at the bottom of the cavity 11 for fixing the steel-bonded ZTA cemented carbide tooth assembly 3. One end of the steel-bonded ZTA cemented carbide tooth assembly 3 needs to be pre-welded with a steel nail 4 (as Figure 6 shown), and the steel-bonded ZTA cemented carbide tooth assembly 3 with the welded steel nail is inserted into the holes at the bottom of the cavity 11 of the double-pouring system, so as to fix the pre-made steel-bonded ZTA cemented carbide tooth assembly 3 at the predetermined position of the wear-resistant surface plate 1 on the composite tooth plate finished product, and the tail end of the steel-bonded ZTA cemented carbide tooth assembly 3 passes through the connection interface 21 and reaches the cavity 22. By using the fixing effect of the steel nail 4 at the end of the steel-bonded ZTA cemented carbide tooth assembly 3 inserted into the holes at the bottom of the cavity 11, the steel-bonded ZTA cemented carbide tooth assembly 3 is prevented from tilting, falling or shifting during the high-temperature pouring process. The preparation method of the cast-inlaid steel-bonded cemented carbide bimetal composite tooth plate is as follows:

[0053] (1) Set the double-pouring system according to the shape of the composite tooth plate, weld a steel nail at one end of the pre-prepared steel-bonded ZTA cemented carbide tooth assembly 3, and then insert the end with the steel nail into each hole at the bottom of the cavity 11 of the double-pouring system.

[0054] (2) Smelt the molten steel for the tough base plate and the molten steel for the wear-resistant surface plate separately. First, pour the molten steel for the wear-resistant surface plate 1 from the pouring cup 111 into the mold 100, so that the molten steel fills the cavity 11, around the steel-bonded ZTA cemented carbide tooth assembly 3 and the anti-slip groove 31. Wait for an appropriate time, and then pour the molten steel for forming the tough base plate 2 from the pouring cup 222 into the mold 100, so that the molten steel fills the cavity 22 and the anti-slip groove 31 of the steel-bonded ZTA cemented carbide tooth assembly 3 until the filling is complete.

[0055] (3) Heat treatment; adopt the corresponding heat treatment process according to the material composition of the wear-resistant surface plate.

[0056] Among them, the preparation of the steel-bonded ZTA cemented carbide tooth assembly 3 is as follows:

[0057] Step 1: Provide ZTA ceramic particles, and carry out surface metallization treatment on the ceramic particles by the Mo-Mn method or electroless nickel plating method to obtain metallized ZTA ceramic particles with a particle size of 8-20 mesh. The metallization treatment can promote the wetting of the ceramic particles and the cemented carbide (high manganese steel matrix).

[0058] Step 2: Stir the high manganese steel matrix powder and the hard phase evenly and carry out ball milling to obtain a mixed powder. Mix the metallized ZTA ceramic particles evenly with the ball-milled mixed powder, add 1-2 Vol.% of a forming agent, and mix evenly again to obtain a forming material.

[0059] Step 3: Load the forming material into the mold cavity, and carry out double-sided cold pressing at a pressure of 600-1000 Mpa, hold the pressure for 2-3 min, and demold to obtain a green blank; there are convex parts with anti-slip grooves 31 inside the mold cavity.

[0060] Step 4: Carry out vacuum degreasing, vacuum sintering, and hot isostatic pressing treatments, and then cool under a protective atmosphere to obtain the steel-bonded ZTA cemented carbide tooth assembly; the vacuum sintering conditions are: keep warm at 600 °C ± 10 °C for 55-65 min, and the heating rate is 4.5-5.5 °C / min; the vacuum sintering conditions: keep warm at 1280-1320 °C for 2 h, and the vacuum degree ≤ 10 -2 Pa; the hot isostatic pressing treatment conditions are: treat for 1 h in argon at 1200 °C × 100 MPa to eliminate residual pores; cooling under a protective atmosphere means cooling in a protective atmosphere of argon or nitrogen.

[0061] The following is described in conjunction with the preferred embodiments of the present invention.

[0062] Example 1

[0063] This embodiment provides a cast-inlaid steel-bonded cemented carbide bimetallic composite tooth plate, which includes the preparation of a steel-bonded ZTA cemented carbide tooth component and the preparation of a cast-inlaid steel-bonded cemented carbide bimetallic composite tooth plate. The raw material formula and specifications of the steel-bonded ZTA cemented carbide tooth component 3 are shown in Table 1.

[0064] Table 1

[0065]

[0066] Among them, ZTA (20% YSZ - Al2O3) represents Al2O3 particles reinforced by yttria-stabilized zirconia YSZ, where the YSZ content is 20 wt%. The preparation method of the steel-bonded ZTA cemented carbide tooth component 3 is as follows: Stir the high-manganese steel matrix powder and the hard phase evenly and perform ball milling to obtain a mixed powder. Mix the metallized ZTA ceramic particles evenly with the ball-milled mixed powder, add a forming agent, an interfacial wetting agent, and a carbon compensation agent, and mix evenly again to obtain a molding material. Load the molding material into the mold cavity, and use two-way cold pressing to form at a pressure of 800 Mpa, hold the pressure for 3 min, and demold to obtain a green blank. Sinter the green blank, and the sintering mechanism is: First, heat up to 600 °C at a rate of 5 °C / min, hold for 1 h for vacuum degreasing, and then keep it at a vacuum degree ≤ 10 -2 Pa and 1300 °C for 2 h; finally, treat it in an argon atmosphere at 1200 °C × 100 MPa for 1 h to eliminate residual pores. Finally, cool it to room temperature under the protection of nitrogen to obtain the steel-bonded ZTA cemented carbide tooth component 3. The steel-bonded ZTA cemented carbide tooth component 3 prepared in this embodiment is a rod, with a length of 50 mm, a diameter of 22 mm, and three annular anti-slip grooves 31 with a depth of 3 mm are respectively provided at both ends.

[0067] According to Figures 4-5 the double-gating system and the pre-embedding method of the steel-bonded ZTA cemented carbide tooth component 3 in the casting mold are arranged, and the double-gating method is used to prepare the bimetallic composite tooth plate. Among them, the metal material of the tough base plate 2 is low-carbon steel ZG230-450 (GB / T 11352-2023); the metal material of the wear-resistant surface plate 1 is high-manganese steel ZGMn13 (GB / T 5680-2024).

[0068] Among them, the wear-resistant surface plate 1 is as Figures 2-3As shown, its surface has several horizontally arranged strip-shaped bosses 101. These strip-shaped bosses 101 are the teeth of the composite tooth plate and are the main parts that play a role in ore crushing during the ore crushing process. There are horizontal grooves between the strip-shaped bosses 101, which provide space for ore blocks to fall, so as to interact with the teeth of another composite tooth plate and effectively crush the ore. Steel-bonded ZTA cemented carbide tooth assemblies 3 are evenly cast on the strip-shaped bosses 101, which greatly improve the hardness, wear resistance and ore crushing efficiency of the strip-shaped bosses 101. The head end of the steel-bonded ZTA cemented carbide tooth assemblies 3 reaches the top surface of the wear-resistant surface plate 1 but does not penetrate the wear-resistant surface plate 1. The specification model of the cast steel-bonded cemented carbide bimetallic composite tooth plate prepared in this embodiment is AL11449, which is suitable for iron ore and basalt crushing. The thickness of its tough base plate 2 is 75 mm; the thickness of the wear-resistant surface plate 1 is 80 mm. The casting density of the steel-bonded ZTA cemented carbide tooth assemblies 3 on the tooth surface is 0.045 / cm 2 .

[0069] During the preparation process, after the double casting is completed, a water toughening treatment process is carried out. The treatment conditions are as follows: first, keep it at 1050 °C for 1.5 h, then use forced-circulating room temperature water to cool at a cooling rate of ≥ 30 °C / s, and then carry out stress relief annealing at 240 °C for 2 h.

[0070] Example 2

[0071] This embodiment provides a cast steel-bonded cemented carbide bimetallic composite tooth plate, and the difference from Example 1 is only that the metal material of the tough base plate 2 is different. In this embodiment, the metal material of the tough base plate 2 is 27MnCr5 (EN 10084).

[0072] Example 3

[0073] This embodiment provides a cast steel-bonded cemented carbide bimetallic composite tooth plate, and the main difference from Example 1 is that the raw material formula composition of the steel-bonded ZTA cemented carbide tooth assemblies 3 is different. The raw material formula and specifications of the steel-bonded ZTA cemented carbide tooth assemblies 3 are shown in Table 2.

[0074] Table 2

[0075]

[0076]

[0077] Example 4

[0078] This embodiment provides a cast-inlaid steel-bonded cemented carbide bimetallic composite tooth plate, and the main difference from Embodiment 1 lies in the different raw material formula of the steel-bonded ZTA cemented carbide tooth component 3. The raw material formula and specifications of the steel-bonded ZTA cemented carbide tooth component 3 are shown in Table 3.

[0079] Table 3

[0080]

[0081] Embodiment 5

[0082] This embodiment provides a cast-inlaid steel-bonded cemented carbide bimetallic composite tooth plate, and the main difference from Embodiment 1 lies in the different hard phases in the raw material formula of the steel-bonded ZTA cemented carbide tooth component 3. The raw material formula and specifications of the steel-bonded ZTA cemented carbide tooth component 3 are shown in Table 4.

[0083] Table 4

[0084]

[0085]

[0086] Embodiment 6

[0087] This embodiment provides a cast-inlaid steel-bonded cemented carbide bimetallic composite tooth plate, and the main difference from Embodiment 1 lies in the different hard phases in the raw material formula of the steel-bonded ZTA cemented carbide tooth component 3. The raw material formula and specifications of the steel-bonded ZTA cemented carbide tooth component 3 are shown in Table 5.

[0088] Table 5

[0089]

[0090] Embodiment 7

[0091] This embodiment provides a cast-inlaid steel-bonded cemented carbide bimetallic composite tooth plate, and the differences from Embodiment 1 include: the different hard phases in the raw material formula of the steel-bonded ZTA cemented carbide tooth component 3; the different metal materials of the wear-resistant surface plate 1. The metal material of the wear-resistant surface plate 1 is 40CrMnMo (DIN 1.2311). The raw material formula and specifications of the steel-bonded ZTA cemented carbide tooth component 3 are shown in Table 6.

[0092] Table 6

[0093]

[0094]

[0095] During the preparation process, after the double casting is completed, the following "quenching + tempering" heat treatment process is carried out: heat preservation at 850 - 870 °C for the thickness (mm) × 1.2 min, water quenching, then air cooling at 500 °C for 2 h; finally, heat preservation at 300 °C for 4 h to further eliminate machining stress. The heat preservation thickness refers to the thickness of the wear-resistant surface layer plate 1.

[0096] The specification model of the cast-in steel-bonded cemented carbide bimetallic composite tooth plate prepared in this embodiment is AL11405, which is applicable to copper ore crushing (used for iron ore crushing during the following tests). The thickness of its tough base plate 2 is 100 mm; the thickness of the wear-resistant surface layer plate 1 is 120 mm. The casting density of the steel-bonded ZTA cemented carbide tooth assembly 3 on the tooth surface is 0.045 / cm 2 .

[0097] Comparative Example

[0098] The main difference between this comparative example and Example 1 is that: the length of the steel-bonded ZTA cemented carbide tooth assembly 3 prepared in this comparative example is only 1 / 2 of that in Example 1, the diameter is the same as that in Example 1, and only three annular anti-slip grooves 31 with a depth of 4 mm are provided at the head end. In this comparative example, since the tail end of the steel-bonded ZTA cemented carbide tooth assembly 3 cannot be cast into the tough base plate 2, that is, it can only be cast into the wear-resistant surface layer plate 1, it cannot play a role in enhancing the connection of the bimetal layers of the tough base plate 2 and the wear-resistant surface layer plate 1.

[0099] The bimetallic composite tooth plates of Examples 1 - 7 and the comparative example are tested for wear resistance, bimetal interface bonding strength, drop hammer impact, thermal shock resistance, etc. under the working conditions of iron ore crushing. The test results are shown in the summary table of Table 7. The drop hammer impact hammer head is selected as hemispherical (diameter 12.7 mm, ASTM standard), and the impact speed is 4 m / s. The test results are the distribution ranges of multiple test results at different parts of the composite tooth plate.

[0100]

[0101] It can be seen from the above examples and comparative examples that the bimetal layer interface bonding strength of the composite tooth plates in each example is high, and the anti-drop hammer impact and anti-thermal shock performance are excellent. In the comparative example, due to the insufficient bonding force between the two layers of metal of the composite tooth plate, the interface cannot effectively transfer stress, resulting in local stress concentration and accelerating the crack initiation of the composite tooth plate; in the drop hammer impact experiment, the comparative example is prone to edge fragmentation due to interface delamination. Therefore, the anti-drop hammer impact and anti-thermal shock performance of the composite tooth plate prepared in the comparative example are significantly reduced.

[0102] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention, rather than to limit them; although the present invention has been described in detail with reference to the foregoing embodiments, those of ordinary skill in the art should understand that they can still modify the technical solutions described in the foregoing embodiments, or perform equivalent replacements for some or all of the technical features; and these modifications or replacements, or when the technical features in the above embodiments do not conflict with each other, can be combined in the manner described in the embodiments, and these modifications, replacements or combinations do not cause the essence of the corresponding technical solutions to deviate from the scope of the technical solutions of the embodiments of the present invention.

Claims

1. A cast-inlaid cemented carbide bimetal composite tooth plate, characterized in that, Comprising: A ductile base plate and a wear-resistant surface layer plate. A number of steel-bonded ZTA cemented carbide tooth assemblies are inlaid and cast in the wear-resistant surface layer plate, and the steel-bonded ZTA cemented carbide tooth assemblies penetrate the interface between the ductile base plate and the wear-resistant surface layer plate. The head end of the steel-bonded ZTA cemented carbide tooth assemblies reaches or penetrates the wear-resistant surface layer plate, and its tail end is located within the ductile base plate; the wear-resistant surface layer plate and the ductile base plate are cast and formed in a mold pre-embedded with cemented carbide tooth assemblies by a double casting method; Among them, by volume percentage, the raw material formula of the steel-bonded ZTA cemented carbide tooth assemblies is: 50-60% of high manganese steel matrix powder, 10-15% of hard phase, 10-30% of metallized ZTA ceramic particles, 3-5% of interface wetting agent, 0.5-1% of carbon compensator, and 1-2% of molding agent; the hard phase is at least one of WC, TiC, and TiB2.

2. The cast-inlaid cemented carbide bimetal composite tooth plate according to claim 1, characterized in that, The high manganese steel matrix powder is a pre-alloyed powder with a particle size of 5-20 μm; the pre-alloyed powder contains C at 1.0 wt% ± 0.1, Mn at 12 wt% ± 1.0, Cr at 1.5 wt% ± 0.2, Mo at 0.5 wt% ± 0.05, and the balance is Fe.

3. The cast-inlaid cemented carbide bimetal composite tooth plate according to claim 1, characterized in that, The particle size of the hard phase is sub-micron level; the hard phase is a composition of WC and TiC, or a composition of WC, TiC, and TiB2, or the hard phase is preferably a composition of WC, TiC, and TiB2.

4. The cast-inlaid cemented carbide bimetal composite tooth plate according to claim 3, characterized in that, The hard phase is a composition of WC:TiC:TiB2 in a volume ratio of 6:3:1, 7:2:1, or 5:3:

2.

5. The cast-inlaid cemented carbide bimetal composite tooth plate according to claim 1, wherein The particle size of the metallized ZTA ceramic particles is 8-20 mesh; the ZTA ceramic particles are Al2O3 particles reinforced with yttria-stabilized zirconia YSZ, where the YSZ content is 20 wt%.

6. The cast-inlaid cemented carbide bimetal composite tooth plate according to claim 1, characterized in that, The interface wetting agent is Ni powder; the carbon compensator is graphite; the molding agent is a paraffin-based binder, a polymer composite system, or a water-soluble temporary binder.

7. The cast-inlaid cemented carbide bimetal composite tooth plate according to claim 1, characterized in that The steel-bonded ZTA cemented carbide tooth assemblies are in the shape of rods or blocks, and anti-slip grooves are integrally formed on their surfaces to increase the bonding force between the steel-bonded ZTA cemented carbide tooth assemblies and the ductile base plate and the wear-resistant surface layer plate.

8. The cast-inlaid cemented carbide bimetal composite tooth plate according to claim 1, characterized in that, The ductile base plate is low-carbon steel ZG230-450 or low-carbon alloy steel with a carbon equivalent between 0.20-0.30 wt%; the wear-resistant surface layer plate is high manganese steel, alloy steel, or high chromium cast iron; during the preparation process, corresponding heat treatment processes are used for treatment according to the material composition of the wear-resistant surface layer plate.

9. A preparation method of a cast-inlaid steel-bonded cemented carbide bimetallic composite tooth plate, characterized in that, Comprising: S1. Set a double casting system according to the shape of the composite tooth plate. Weld a steel nail to one end of the pre-prepared steel-bonded ZTA cemented carbide tooth assemblies, and then fix them in the corresponding parts of the mold that need to be strengthened for the tooth plate; the raw material formula of the steel-bonded ZTA cemented carbide tooth assemblies is: 50-60% of high manganese steel matrix powder, 10-15% of hard phase, 10-30% of metallized ZTA ceramic particles, 3-5% of interface wetting agent, 0.5-1% of carbon compensator, and 1-2% of molding agent; the hard phase is at least one of WC, TiC, and TiB2; S2. Melt the molten steel for the tough base plate and the molten steel for the wear-resistant surface plate separately. First, pour the molten steel for the wear-resistant surface plate into the mold from one pouring gate. After a preset time interval, pour the molten steel for the tough base plate into the mold from the other pouring gate until the mold is completely filled. S3. Heat treatment: Adopt the corresponding heat treatment process according to the material composition of the wear-resistant surface plate.

10. The preparation method according to claim 9, characterized in that, The preparation method of the steel-bonded ZTA cemented carbide tooth component is as follows: Step 1: Stir the high manganese steel matrix powder and the hard phase evenly and perform ball milling to obtain a mixed powder. Step 2: Mix the metallized ZTA ceramic particles evenly with the ball-milled mixed powder, add a forming agent, an interfacial wetting agent, and a carbon compensation agent, and mix evenly again to obtain a forming material. The metallized ZTA ceramic particles are obtained by surface metallization treatment of ZTA ceramic particles by the Mo-Mn method or the electroless nickel plating method. Step 3: Load the forming material into the mold cavity, perform double-sided cold pressing at a pressure of 600-1000 Mpa, hold the pressure for 2-3 minutes, and demold to obtain a green blank. Step 4: Perform vacuum degreasing, vacuum sintering, and hot isostatic pressing treatments, and then cool under a protective atmosphere to obtain the steel-bonded ZTA cemented carbide tooth component. In Step 4, the vacuum sintering conditions are as follows: keep warm at 600°C ± 10°C for 55 - 65 min, with a heating rate of 4.5 - 5.5°C / min; the vacuum sintering conditions are: keep warm at 1280 - 1320°C for 2 h, with a vacuum degree ≤ 10 -2 Pa; the hot isostatic pressing treatment conditions are: treat in argon at 1200°C × 100 MPa for 1 h to eliminate residual pores; cooling under a protective atmosphere means cooling in a protective atmosphere of argon or nitrogen.

Images