Composite carbide reinforced single tooth roller surface high temperature wear-resistant flux-cored wire

Abstract

The present application relates to the technical field of welding material, in particular to a kind of composite carbide reinforced single-tooth roller surface high-temperature wear-resistant flux-cored wire.The specific technical scheme is as follows: a kind of flux-cored wire, by mass percentage, comprising the following components: graphite 5-10%, high-carbon chromium iron 20-50%, silicon carbide 2-5%, tungsten carbide 2-6%, electrolytic manganese 1-4%, niobium iron 10-20%, vanadium iron 3-7%, molybdenum iron 15-25%, and the rest is Fe powder.The flux-cored wire prepared by the flux-cored wire of the present application has good surfacing process, beautiful weld formation, and few surface pores, and also has high hardness and high-temperature wear resistance.

Description

Technical Field

[0001] This invention relates to the field of welding materials technology, specifically to a high-temperature wear-resistant flux-cored welding wire for a composite carbide-reinforced single-tooth roller surface. Background Technology

[0002] As a key piece of equipment in the sintering process of modern steel industry, the single-tooth roll crusher's main function is to crush high-temperature sintered materials (operating temperature typically maintained at 800-900℃). Under extreme operating conditions of continuous high temperature and high wear, the core components of this equipment often face severe high-temperature wear problems, leading to a significant shortening of its service life. To effectively solve this problem, advanced surface treatment technology is used to repair and strengthen vulnerable parts. This not only significantly extends the service life of the equipment but also prevents premature scrapping of the entire machine, thereby greatly reducing production and maintenance costs.

[0003] High-chromium iron-based cemented carbide (Cr: 12-30 wt.%, C: 2.0-4.0 wt.%) is widely used due to its excellent cost-effectiveness and wear resistance. In this alloy system, martensite and retained austenite together form a matrix structure that combines strength and toughness, while M7C3-type carbides (M = Cr, Fe) formed by the reaction of elements such as Cr and Fe with C provide crucial hardness and wear resistance. However, for the complex working conditions of single-tooth roller components, traditional Fe-Cr-C alloys have significant limitations: the coarse primary M7C3 carbides have weak interfacial bonding with the matrix, easily causing cracking and peeling of the weld overlay, seriously affecting the service life of the component.

[0004] To address this, this invention develops a multi-element alloyed carbide-reinforced iron-chromium alloy. High-melting-point elements such as Nb, W, and Mo are added to the flux-cored welding wire to form a multi-element carbide hard phase. This enhances the alloy's wear resistance and refines the M7C3 structure, improving weld overlay formability and interfacial bonding strength. The carbides formed by Nb and C refine the grain size, improving the alloy's high-temperature stability and wear resistance. W maintains good strength and hardness, resisting deformation and wear. Mo possesses excellent high-temperature strength and creep resistance, forming a dense oxide film at high temperatures. This oxide film prevents further oxidation and wear, enhancing the material's high-temperature wear resistance. V, a strong carbide-forming element, forms small-particle-size carbides that are dispersed throughout the alloy, providing both grain refinement and dispersion strengthening. This alloy system significantly improves the service life of single-tooth rollers under high-temperature wear conditions. Summary of the Invention

[0005] To address the shortcomings of existing technologies, this invention provides a high-temperature wear-resistant flux-cored welding wire for reinforcing the surface of a single-tooth roller with composite carbide. The flux-cored welding wire, when used for arc welding, produces a weld alloy that not only has good weldability and aesthetically pleasing weld formation with few surface pores, but also possesses high hardness and high-temperature wear resistance.

[0006] To achieve the above objectives, the present invention provides the following technical solution:

[0007] This invention discloses a core containing the following components by weight percentage:

[0008] Graphite 5-10%, high-carbon ferrochrome 20-50%, silicon carbide 2-5%, tungsten carbide 2-6%, electrolytic manganese 1-4%, ferroniobium 10-20%, ferrovanadium 3-7%, ferromolybdenum 15-25%, the remainder being Fe powder.

[0009] Preferably, by mass percentage, it comprises the following components: 6-9% graphite, 25-46% high-carbon ferrochrome, 3-4% silicon carbide, 3-5% tungsten carbide, 2-4% electrolytic manganese, 10-19% ferroniobium, 4-6% ferrovanadium, 15-20% ferromolybdenum, and the remainder being Fe powder.

[0010] Preferably, the high-carbon ferrochrome has a chromium mass fraction of 68% and a carbon mass fraction of 8%; the silicon carbide has a silicon mass fraction of 70% and a carbon mass fraction of 30%; the tungsten carbide has a tungsten mass fraction of 94% and a carbon mass fraction of 6%; the niobium ferrochrome has a niobium mass fraction of 65%; the vanadium ferrovanadium has a vanadium mass fraction of 50%; the molybdenum ferromolybdenum has a molybdenum mass fraction of 60%; the electrolytic manganese has a manganese mass fraction greater than 90%; and the graphite has a carbon mass fraction greater than 99.5%.

[0011] Preferably, the high-carbon ferrochrome has a particle size of 30-50 mesh; the tungsten carbide, ferroniobium, ferromolybdenum, and ferrovanadium all have a particle size of 80-100 mesh; the electrolytic manganese has a particle size of 60-80 mesh; the silicon carbide has a particle size of 70-90 mesh; the graphite has a particle size of 40-60 mesh; and the Fe powder has a particle size of 100-150 mesh.

[0012] Accordingly, a composite carbide-reinforced high-temperature wear-resistant flux-cored welding wire for single-tooth roller surface is provided, wherein the raw material of the flux-cored welding wire includes the flux core.

[0013] Preferably, the flux-cored wire has a flux-cored filling rate of 40-60%.

[0014] Accordingly, a method for preparing a high-temperature wear-resistant flux-cored welding wire for a composite carbide-reinforced single-tooth roller surface involves encasing the flux core described in the above scheme in a metal shell.

[0015] Accordingly, a welding method for using a composite carbide-reinforced high-temperature wear-resistant flux-cored wire on the surface of a single-tooth roller is provided, wherein the composite carbide-reinforced high-temperature wear-resistant flux-cored wire prepared by the aforementioned preparation method is used for welding, and the welding process is an arc welding process.

[0016] Preferably, the arc welding process parameters are: voltage: 25-30V, current: 380-480A, wire feeding speed: 1000mm / min, and the length of the welding wire extending out of the contact tip: 15-25mm.

[0017] Preferably, after welding, the mass percentage of alloying elements in the obtained weld overlay alloy is within the following range: C: 3-6%; Cr: 15-30%; Si: 0.5-2%; W: 1-3%; Mn: 0.5-3%; Nb: 2-8%; V: 1.0-3.0%; Mo: 4-6%; Fe and unavoidable impurities: balance.

[0018] The present invention has the following beneficial effects:

[0019] The microstructure of the alloy obtained by arc welding using the high-temperature wear-resistant flux-cored welding wire of the present invention on the surface of a single-toothed roller consists of martensite, retained austenite, and carbides (M7C3, NbC, etc.). M7C3 carbide is the main wear-resistant phase in the alloy, effectively improving the wear resistance of the weld alloy. NbC acts as a heterogeneous nucleation site for M7C3 carbides, refining the M7C3 content, significantly improving the high-temperature wear resistance of the weld alloy, and extending the service life of the single-toothed roller. Attached Figure Description

[0020] Figure 1 The image shows the surface morphology of the weld overlay alloy prepared in Example 5.

[0021] Figure 2 This is a wear depth diagram of the weld overlay alloy prepared in Example 5. Detailed Implementation

[0022] The technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention.

[0023] Unless otherwise specified, the technical means used in the implementation examples are conventional means well known to those skilled in the art.

[0024] 1. This invention discloses a core containing the following components by weight percentage:

[0025] Graphite 5-10%, high-carbon ferrochrome 20-50%, silicon carbide 2-5%, tungsten carbide 2-6%, electrolytic manganese 1-4%, ferroniobium 10-20%, ferrovanadium 3-7%, ferromolybdenum 15-25%, the remainder being Fe powder.

[0026] Furthermore, the core disclosed in this invention comprises, by weight percentage, the following components: 6-9% graphite, 25-46% high-carbon ferrochrome, 3-4% silicon carbide, 3-5% tungsten carbide, 2-4% electrolytic manganese, 10-19% ferroniobium, 4-6% ferrovanadium, 15-20% ferromolybdenum, with the remainder being Fe powder.

[0027] Furthermore, the high-carbon ferrochrome has a chromium mass fraction of 68% and a carbon mass fraction of 8%; the silicon carbide has a silicon mass fraction of 70% and a carbon mass fraction of 30%; the tungsten carbide has a tungsten mass fraction of 94% and a carbon mass fraction of 6%; the niobium ferrochrome has a niobium mass fraction of 65%; the vanadium ferrovanadium has a vanadium mass fraction of 50%; the molybdenum ferromolybdenum has a molybdenum mass fraction of 60%; the electrolytic manganese has a manganese mass fraction greater than 90%; and the graphite has a carbon mass fraction greater than 99.5%.

[0028] Furthermore, the high-carbon ferrochrome has a particle size of 30-50 mesh; the tungsten carbide, ferroniobium, ferromolybdenum, and ferrovanadium all have a particle size of 80-100 mesh; the electrolytic manganese has a particle size of 60-80 mesh; the silicon carbide has a particle size of 70-90 mesh; the graphite has a particle size of 40-60 mesh; and the Fe powder has a particle size of 100-150 mesh.

[0029] 2. This invention provides a high-temperature wear-resistant flux-cored welding wire for a composite carbide-reinforced single-tooth roller surface, wherein the raw material of the flux-cored welding wire includes the aforementioned flux core. The flux core filling rate in the flux-cored welding wire is 40-60%, that is, the percentage of the area occupied by the flux core to the total cross-sectional area of ​​the welding wire, preferably 40-50%, more preferably 45-50%. The preparation process is as follows: the flux core described above is encased in a metal shell.

[0030] The specific preparation process is as follows:

[0031] (1) Powder selection and drying: Select alloy powders according to the above-mentioned core composition, and dry each powder in advance. The drying equipment is a vacuum drying oven, the drying temperature is 150℃, and the drying time is 2h.

[0032] (2) Sieving: In order to ensure the consistency of the particle size of the same powder, each powder needs to be sieved through a sieve according to the mesh size disclosed above.

[0033] (3) Powder preparation and mixing: Powder preparation is carried out according to the number of kilograms, filling rate and mass percentage of each type of flux-cored wire. After preparation, the different powders need to be mixed evenly to ensure that the components in the flux-cored wire are uniform.

[0034] (4) Selecting the strip: Select stainless steel strip as the metal shell. The thickness of the strip is 0.3mm and the width is 12mm.

[0035] (5) Drawing: The steel strip passes through the forming rollers and changes from a plane to a U-shape. At this time, the pre-prepared core powder is fed into the U-shaped steel strip through the conveyor belt. After the U-shaped steel strip carrying the powder passes through the closing rollers, the steel strip changes from a U-shape to an O-shape, and the steel strip closes, tightly wrapping the core powder.

[0036] (6) Diameter reduction and packaging: The drawn flux-cored wire is passed through a drawing die of a certain diameter to finally achieve the diameter required for the finished product. The reduced-diameter flux-cored wire is then loaded into an I-beam and sealed for storage until use.

[0037] 3. A welding method for using a composite carbide-reinforced high-temperature wear-resistant flux-cored wire on the surface of a single-toothed roller, wherein the composite carbide-reinforced high-temperature wear-resistant flux-cored wire prepared by the aforementioned method is used for welding, and the welding process is an arc welding process.

[0038] The arc welding process parameters are as follows: voltage: 25-30V, current: 380-480A, wire feeding speed: 1000mm / min, and the length of the welding wire extending out of the contact tip: 15-25mm.

[0039] Furthermore, after welding, the mass percentage of alloying elements in the obtained weld overlay alloy is within the following range: C: 3-6%; Cr: 15-30%; Si: 0.5-2%; W: 1-3%; Mn: 0.5-3%; Nb: 2-8%; V: 1.0-3.0%; Mo: 4-6%; Fe and unavoidable impurities: balance.

[0040] In this invention, the various elements function as follows:

[0041] C: Carbon is an important component element in wear-resistant iron-based alloys. A small amount of carbon can dissolve in the iron matrix, causing lattice distortion, thereby increasing the strength and hardness of the alloy. When the carbon content is high enough, carbon can form a large number of carbides with elements such as chromium and iron. These hard phase carbides can significantly improve the wear resistance and strength of the alloy; under high temperature conditions, carbides can also pin dislocations, improving the high-temperature strength of the alloy.

[0042] Cr: Cr combines with C to form high-hardness carbides, among which Cr7C3 has extremely high hardness, which can significantly improve the alloy's resistance to abrasive wear. At high Cr contents, the carbides are distributed in isolated blocks or chrysanthemum-like patterns, reducing the cutting effect on the matrix and improving the alloy's toughness. In addition, Cr dissolves in the ferrite or martensitic matrix, increasing the matrix's hardness and strength. When the Cr content is ≥12%, a dense Cr2O3 passivation film can form on the alloy surface, resisting corrosion from media (such as acids and salt water). The Cr2O3 film remains stable at high temperatures (<900℃), slowing down the alloy's oxidation and thermal fatigue.

[0043] Niobium (Nb) is a strong carbide-forming element. It significantly improves the wear resistance of alloys primarily by refining the microstructure, forming high-hardness carbides, and enhancing high-temperature stability, especially under high-temperature and high-stress wear conditions. Nb forms high-hardness, high-stability NbC carbides with carbon (C), whose hardness is far higher than Fe3C and Cr7C3, significantly improving the alloy's resistance to abrasive wear. NbC precipitates in the matrix at the nanoscale, hindering dislocation movement, enhancing matrix strength, and also promoting the growth of Cr7C3 phase and austenite grains, resulting in a finer and more uniform microstructure and improved impact toughness. NbC remains stable above 1000℃ and is more resistant to high-temperature wear than the Cr7C3 phase. Furthermore, Nb can fix carbon (C), reducing Cr carbide precipitation, preventing intergranular corrosion, and improving the alloy's corrosion resistance.

[0044] Tungsten (W) is a high-melting-point, strong carbide-forming element. In wear-resistant iron-based alloys, it significantly enhances alloy performance primarily by forming ultra-hard carbides, improving red hardness, and enhancing high-temperature wear resistance. WC's hardness is also much higher than Fe3C and Cr7C3, significantly improving the alloy's resistance to abrasive wear. Furthermore, W forms (W,Cr)7C3 and (W,V)C with Cr, V, and Mo, enhancing carbide stability. W carbides can pin grain boundaries, refine the alloy microstructure, and improve the material's impact toughness.

[0045] Mo: Molybdenum reacts with carbon to form Mo₂C, with a hardness between Cr₇C₃ and Fe₃C, enhancing resistance to abrasive wear. It also forms (Mo,Cr)₇C₃ and (Mo,V)C with Cr and V, improving the thermal stability of the carbides. Mo dissolves in the matrix, slowing down high-temperature softening and allowing the alloy to maintain high strength at 600–800°C. Furthermore, molybdenum promotes the formation of a dense oxide film at high temperatures, reducing surface degradation caused by high-temperature oxidation. The synergistic effect of NbC and Mo₂C further improves the high-temperature wear resistance of the alloy.

[0046] V (V) is also a strong carbide-forming element, capable of forming carbides and improving the wear resistance of alloys. These carbides mainly precipitate at the nanoscale, pinning dislocations and grain boundaries to strengthen the matrix. V's solid solution in austenite increases the tendency of supercooled austenite to transform into martensite, promoting martensite formation. V's carbides (VC) can pin dislocations and grain boundaries at high temperatures, improving the high-temperature strength and impact toughness of the alloy.

[0047] Mn and Si: The elemental transition coefficient is improved by using manganese-silicon combined deoxidation.

[0048] Fe: Filling the gap.

[0049] To better understand the present invention, specific embodiments are described below, but the scope of the invention is not limited to these embodiments. The common parts in each embodiment are described below:

[0050] In the following embodiments, all raw materials used are commercially available.

[0051] In the following embodiments, the outer sheath of the flux-cored wire is made of stainless steel strip with a thickness of 0.3 mm and a width of 12 mm. The flux composition of the flux-cored wire is specifically described in the embodiments. After passing through the rollers, the steel strip is rolled into a U-shape. The various powders in the formula are weighed in advance according to the designed proportions, dried, and mixed evenly before being mechanically added to the steel strip. The U-shaped steel strip is closed after passing through subsequent rollers. The closed steel strip is repeatedly drawn and reduced in diameter using a drawing die to produce a flux-cored wire with a diameter of 2.8 mm. A high-temperature wear-resistant flux-cored wire with a single-toothed roller surface is obtained.

[0052] In the core, the high-carbon ferrochrome has a particle size of 30-50 mesh; the tungsten carbide, ferroniobium, ferromolybdenum, and ferrovanadium all have a particle size of 80-100 mesh; the manganese has a particle size of 60-80 mesh; the silicon carbide has a particle size of 70-90 mesh; the graphite has a particle size of 40-60 mesh; and the Fe powder has a particle size of 100-150 mesh.

[0053] The high-carbon ferrochrome has a chromium mass fraction of 68% and a carbon mass fraction of 8%; the silicon carbide has a silicon mass fraction of 70% and a carbon mass fraction of 30%; the tungsten carbide powder has a tungsten mass fraction of 94% and a carbon mass fraction of 6%; the niobium ferrochrome has a niobium mass fraction of 65%; the vanadium ferrochrome powder has a vanadium mass fraction of 50%; the molybdenum ferrochrome has a molybdenum mass fraction of 60%; the electrolytic manganese has a manganese mass fraction greater than 90%; and the graphite has a carbon mass fraction greater than 99.5%.

[0054] During the welding process, an electric arc welding process is used to prepare the welding alloy. The welding process parameters are: voltage: 25-30V, current: 380-480A, wire feed speed: 1000mm / min, and the length of the welding wire extending out of the contact tip: 15-25mm.

[0055] The weld overlay alloys prepared in the following embodiments were subjected to hardness tests, abrasive wear tests, and tribological wear tests. To simulate the actual high-temperature conditions of a single-toothed roller, the weld overlay alloys were subjected to heat treatment at 900°C for 2 hours, followed by furnace cooling. The heat-treated weld overlay alloys were then subjected to hardness tests, abrasive wear tests, and tribological wear tests. The specific test steps are as follows:

[0056] (1) The Rockwell hardness of the weld overlay alloy was tested using an HR-150A electric Brinell hardness tester. The hardness tester indenter was a diamond cone indenter, with a load of 150 kg, a loading time of 5 s, and a recovery time of 3 s. The distance between two adjacent test points was 5 mm, and the number of test points was 10. The final hardness of the weld overlay alloy was taken as the average value of the data from the 10 test points.

[0057] (2) Abrasive wear tests were conducted using an MLS-225 wet sand rubber wheel abrasive wear testing machine. The wear specimen dimensions were 57mm × 25mm × 10mm. The main test parameters included: rubber wheel diameter of 176mm, rubber wheel speed of 240rpm, rubber wheel hardness of 60 Shore hardness, 40-70 mesh quartz sand as the abrasive, a loading load of 100N, and the addition of 1000g of water and 1500g of quartz sand during the test. Before each test, a pre-grinding process was performed at 2000rpm to avoid the surface roughness of the specimen affecting the wear results. The specimen was weighed after pre-grinding as its pre-wear weight. After 8000rpm, the specimen was immersed in an ethanol solution, ultrasonically cleaned, and dried with a hair dryer. The specimen was then weighed using a Beijing Sartorius precision balance, with the weight accurate to 0.0001g. Each specimen underwent three tests, and the average weight loss of the specimen was taken as the reference standard for wear resistance.

[0058] (3) High-temperature friction and wear tests were conducted using an MS-HT1000 high-temperature friction and wear testing machine. The wear specimen size was 20mm×20mm×7mm. The test parameters were: φ4 silicon carbide, load 2000g, friction radius 6mm, rotation speed 300r / min, test temperature at room temperature and 600℃, and test time 60min. To reduce experimental error, each specimen was tested three times. After the test, the three-dimensional morphology of the wear track was obtained using an OLMPUS-4100 laser confocal scanning microscope, and the wear volume of the specimen was calculated. The wear track morphology was observed using a field emission scanning electron microscope.

[0059] Example 1

[0060] Weigh the core according to the following percentages: 7% graphite, 25% high-carbon ferrochrome, 4% silicon carbide, 3.0% tungsten carbide, 3.0% electrolytic manganese, 10% ferroniobium, 4% ferrovanadium, 15.0% ferromolybdenum, and the remainder is Fe powder.

[0061] The welding alloy prepared according to the welding process disclosed above in this invention has the following mass percentage content of alloying elements: C: 4%; Cr: 17%; Si: 1.2%; W: 1%; Mn: 0.8%; Nb: 2.8%; V: 1.3%; Mo: 4.0%; Fe balance.

[0062] The Rockwell hardness of the weld overlay alloy is 52 HRC, and the wear weight loss in the abrasive wear test is 1.7710 g; the Rockwell hardness after heat treatment is 45 HRC, and the wear weight loss is 2.8266 g; the friction depth at room temperature and at 600℃ is 9 μm and 16.4 μm, respectively.

[0063] Example 2

[0064] Weigh the core according to the following percentages: 8% graphite, 25% high-carbon ferrochrome, 3% silicon carbide, 4.5% tungsten carbide, 3.0% electrolytic manganese, 10% ferroniobium, 5% ferrovanadium, 18% ferromolybdenum, and the remainder is Fe powder.

[0065] The welding alloy prepared according to the welding process disclosed above in this invention has the following mass percentage content of alloying elements: C: 4.9%; Cr: 18%; Si: 1.2%; W: 2%; Mn: 1.0%; Nb: 3.0%; V: 1.3%; Mo: 5.0%; Fe balance.

[0066] The Rockwell hardness of the weld overlay alloy is 55.5 HRC, and the wear weight loss in the abrasive wear test is 1.0181 g; the Rockwell hardness after heat treatment is 50 HRC, and the wear weight loss is 1.7411 g; in the tribological wear test, the wear depth at room temperature and 600℃ is 7.1 μm and 13.2 μm, respectively.

[0067] Example 3

[0068] Weigh the core according to the following percentages: 8% graphite, 28% high-carbon ferrochrome, 3% silicon carbide, 4.5% tungsten carbide, 3.0% electrolytic manganese, 11.5% ferroniobium, 5% ferrovanadium, 18% ferromolybdenum, and the remainder is Fe powder.

[0069] The welding alloy is prepared according to the welding process disclosed above in this invention. The mass percentage of alloying elements in the obtained welding alloy is C: 5%; Cr: 20%; Si: 1.2%; W: 2.2%; Mn: 1.1%; Nb: 3.5%; V: 1.3%; Mo: 5.0%; Fe balance.

[0070] The Rockwell hardness of the weld overlay alloy is 62 HRC, and the wear weight loss in the abrasive wear test is 0.7431 g; the Rockwell hardness after heat treatment is 58 HRC, and the wear weight loss is 1.0291 g; in the tribological wear test, the wear depth at room temperature and 600℃ is 5.7 μm and 11.2 μm, respectively.

[0071] Example 4

[0072] Weigh the core according to the following percentages: 8% graphite, 37% high-carbon ferrochrome, 3% silicon carbide, 4.5% tungsten carbide, 3.0% electrolytic manganese, 18% ferroniobium, 5% ferrovanadium, 18% ferromolybdenum, and the remainder is Fe powder.

[0073] The welding alloy prepared according to the welding process disclosed above in this invention has the following mass percentage content of alloying elements: C: 5.3%; Cr: 21%; Si: 1.2%; W: 2.2%; Mn: 1.1%; Nb: 5.4%; V: 1.3%; Mo: 5.0%; Fe balance.

[0074] The welding process produces less spatter, and the weld alloy surface is bright, highly smooth, and free of micro-cracks. The Rockwell hardness of the weld alloy is 65 HRC, and the wear weight loss in the abrasive wear test is 0.5917 g. After heat treatment, the Rockwell hardness is 61 HRC, and the wear weight loss is 0.6273 g. In the tribological wear test, the wear depth at room temperature and 600℃ is 4.5 μm and 9 μm, respectively.

[0075] Example 5

[0076] Weigh the core according to the following percentages: graphite 8%, high-carbon ferrochrome 46%, silicon carbide 3%, tungsten carbide 5%, electrolytic manganese 3.0%, ferroniobium 18%, ferrovanadium 5%, ferromolybdenum 18%, and the remainder is Fe powder.

[0077] The welding alloy prepared according to the welding process disclosed above in this invention has the following mass percentage content of alloying elements: C: 5.5%; Cr: 24%; Si: 1.2%; W: 2.5%; Mn: 1%; Nb: 5.4%; V: 1.3%; Mo: 5.0%; Fe balance.

[0078] The welding process produces less spatter, resulting in a beautiful weld formation. The weld alloy surface is bright, free of obvious porosity, and exhibits high flatness and no cracks (e.g.). Figure 1 (As shown); the Rockwell hardness of the weld overlay alloy is 67.5 HRC, and the wear loss weight in the abrasive wear test is 0.3242 g; the Rockwell hardness after heat treatment is 62.2 HRC, and the wear loss weight is 0.3613 g; in the tribological wear test, the wear depth at room temperature and 600℃ is 4.1 μm and 8.2 μm, respectively (as shown). Figure 2 (As shown).

[0079] The embodiments described above are merely preferred embodiments of the present invention and are not intended to limit the scope of the present invention. Various modifications and improvements made by those skilled in the art to the technical solutions of the present invention without departing from the spirit of the present invention should fall within the protection scope defined by the claims of the present invention.

Claims

1. A core, characterized in that: It includes the following components by mass percentage: Graphite 6-9%, high carbon ferrochrome 25-46%, silicon carbide 3-4%, tungsten carbide 3-5%, electrolytic manganese 2-4%, ferroniobium 10-19%, ferrovanadium 4-6%, ferromolybdenum 15-20%, the remainder being Fe powder; The high-carbon ferrochrome has a chromium mass fraction of 68% and a carbon mass fraction of 8%; the silicon carbide has a silicon mass fraction of 70% and a carbon mass fraction of 30%; the tungsten carbide has a tungsten mass fraction of 94% and a carbon mass fraction of 6%; the niobium ferrochrome has a niobium mass fraction of 65%; the vanadium ferrochrome has a vanadium mass fraction of 50%; the molybdenum ferrochrome has a molybdenum mass fraction of 60%; the electrolytic manganese has a manganese mass fraction greater than 90%; and the graphite has a carbon mass fraction greater than 99.5%.

2. The drug core according to claim 1, characterized in that: The high-carbon ferrochrome has a particle size of 30-50 mesh; the tungsten carbide, ferroniobium, ferromolybdenum, and ferrovanadium all have a particle size of 80-100 mesh; the electrolytic manganese has a particle size of 60-80 mesh; the silicon carbide has a particle size of 70-90 mesh; the graphite has a particle size of 40-60 mesh; and the Fe powder has a particle size of 100-150 mesh.

3. A high-temperature wear-resistant flux-cored welding wire for a composite carbide-reinforced single-tooth roller surface, characterized in that: The raw material of the flux-cored welding wire includes the flux core as described in any one of claims 1-2, and the flux core filling rate in the flux-cored welding wire is 40-60%.

4. A welding method using a composite carbide-reinforced high-temperature wear-resistant flux-cored welding wire on the surface of a single-tooth roller, characterized in that: The composite carbide-reinforced single tooth roller surface is welded using the high-temperature wear-resistant flux-cored welding wire as described in claim 3, and the welding method employs an electric arc welding process. The arc welding process parameters are as follows: voltage: 25-30V, current: 380-480A, wire feed speed: 1000mm / min, and wire extension length from the contact tip: 15-25mm. After welding, the mass percentage of alloying elements in the obtained weld overlay alloy is within the following range: C: 3-6%; Cr: 15-30%; Si: 0.5-2%. W: 1-3%; Mn: 0.5-3%; Nb: 2-8%; V: 1.0-3.0%; Mo: 4-6%; Fe and unavoidable impurities: balance.

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