Flux-cored wire for electric arc additive and processing technology of flux-cored wire

Abstract

The invention discloses a flux-cored wire for electric arc additive and a processing technology of the flux-cored wire, and belongs to the field of electronics, the flux-cored wire comprises a shell and a core material, and the shell is filled with the core material; the core material comprises the following components in percentage by weight: 40-60% of nickel-based alloy powder, 10-20% of a low-volatile active agent, 8-15% of a stable metal oxide, 5-10% of particle reinforced ceramic, 3-6% of an interface regulating agent and 2-5% of a rare earth alloy refiner; the shell is a stainless steel strip, the thickness of the shell is 0.2-0.4 mm, and the flux-cored wire with the core material volume fraction not larger than 35% is formed through hot rolling machining and sealing after wrapping. The processing technology comprises the following steps: S1, mixing the components according to the ratio, and carrying out high-energy planetary ball milling treatment; s2, carrying out high-sealing drying treatment; s3, a stainless steel strip is adopted to form a flux core coating structure under argon protection; and S4, the flux-cored wire with the diameter being 1.2-2.0 mm is formed through double-pass hot rolling treatment. The method has the beneficial effects that the component uniformity and the molten drop transmission stability in the electric arc material increasing process are remarkably improved, and the deposition forming effect with higher quality is achieved.

Description

Technical Field

[0001] The present invention relates to the field of electronics, and more specifically, to a flux-cored wire for arc additive manufacturing and its processing technology. Background Art

[0002] A flux-cored wire is a composite welding material with powder filled in a metal casing of the wire. Since its birth in the 1950s, it has been widely used in the fields of traditional welding and additive manufacturing. With the development of wire arc additive manufacturing (WAAM) technology, flux-cored wires have gradually replaced solid wires due to their customizable composition, excellent metallurgical properties, and high forming efficiency, becoming cost-effective metal additive materials. Its technological development has evolved from early carbon steel flux-cored wires to high-performance wires such as stainless steel, nickel-based, titanium alloy, and aluminum alloy. The types of filler materials have become increasingly rich, and the control accuracy and stability have been significantly improved. At the same time, the processing technology has been optimized from traditional coil core forming to continuous forming, fine powder blending, and low porosity, achieving higher consistency and quality control.

[0003] However, the biggest drawback of current flux-cored wires in arc additive manufacturing lies in the lack of compositional uniformity and droplet transfer stability. Due to uneven powder distribution or gas escape, it is easy to cause forming defects such as alloy element burning loss, slag inclusion, and pores, affecting the tissue density and mechanical properties of the additive layer. In addition, the preparation cost and process complexity also restrict its wide application in high-end structural parts. Therefore, improving the uniformity of flux filling, developing low-volatile components, and optimizing the wire structure design and droplet control technology are the key directions for future development. Summary of the Invention

[0004] The purpose of the present invention is to provide a flux-cored wire for arc additive manufacturing and its processing technology to solve the problems raised in the above background art: However, the biggest drawback of current flux-cored wires in arc additive manufacturing lies in the lack of compositional uniformity and droplet transfer stability. Due to uneven powder distribution or gas escape, it is easy to cause forming defects such as alloy element burning loss, slag inclusion, and pores, affecting the tissue density and mechanical properties of the additive layer. In addition, the preparation cost and process complexity also restrict its wide application in high-end structural parts.

[0005] Technical Solution: A flux-cored wire for arc additive manufacturing includes a casing and a core material. The core material is filled inside the casing. The core material consists of the following components by weight percentage: 40 - 60% nickel-based alloy powder, 10 - 20% low-volatile activator, 8 - 15% stable metal oxide, 5 - 10% particulate-reinforced ceramic, 3 - 6% interface regulator, and 2 - 5% rare earth alloy refiner; the casing is a stainless steel strip with a thickness of 0.2 - 0.4 mm, and after being coated and sealed by hot rolling, a flux-cored wire with a core material volume fraction not greater than 35% is formed.

[0006] Preferably, the particle-reinforced ceramic is spherical silicon nitride with a particle size of 200-500 nm, a uniform volume distribution, and is surface-coated with titanate.

[0007] Preferably, the interface modifier is a composite magnesium borate salt, and the composite magnesium borate salt of the interface modifier reacts with the nickel-based alloy during the solidification of the molten droplet to form an interface layer with a low interface energy.

[0008] Preferably, the rare earth alloy refining agent is cerium-aluminum alloy, and the addition amount of the rare earth alloy refining agent is controlled at 2-3%; it is fully mixed with the nickel-based alloy powder by dry ball milling.

[0009] Preferably, a flux-cored wire processing process for arc additive manufacturing includes the following steps: S1. Mix nickel-based alloy powder, low-volatility activator, stable metal oxide, particle-reinforced ceramic, interface modifier, and rare earth alloy refining agent according to the ratio, and perform high-energy planetary ball milling for 90-120 minutes at a rotation speed of 400-600 rpm; S2. After screening and removing impurities from the processed mixed powder, perform high-sealing drying treatment, with a drying temperature of 150-180 °C and a time of 2-3 hours; S3. Use a stainless steel strip to form a flux-cored coating structure under argon protection. During pressing, control the core material filling rate to be 65-70% and the porosity to be less than 5%; S4. Form a flux-cored wire with a diameter of 1.2-2.0 mm through double-pass hot rolling. Control the hot rolling temperature at 750-850 °C and the total reduction ratio at 45-55%.

[0010] Preferably, the pretreatment of the particle-reinforced ceramic before the S1 high-energy planetary ball milling treatment includes the following steps: S1-1. The particle-reinforced ceramic is treated in a vacuum plasma environment for 5-10 minutes to form an active defect layer on the surface; S1-2. Immerse the treated ceramic particles in a mixed solution of ethanol and isopropyl titanate and stir for 4 hours, and then dry at 80 °C.

[0011] Preferably, in the S2 drying step, nitrogen gas flow protection is adopted, and the humidity is controlled below 0.5% to prevent moisture from reacting with the low-volatility activator.

[0012] Preferably, the S4 hot rolling step includes a primary intermediate annealing treatment, with an annealing temperature of 700-720 °C and a holding time of 15-20 minutes to eliminate tissue stress.

[0013] Preferably, the flux-cored wire is subjected to plasma surface cleaning treatment after hot rolling, with a treatment time of 30-60 seconds to remove the micro-oxidation layer and improve the surface finish.

[0014] Preferably, the flux-cored wire for arc additive manufacturing has high droplet forming stability during the arc additive manufacturing process, the component distribution deviation is less than 2%, and the grain size of the microstructure remains within the range of 10-25 μm within the stacking thickness of 5-15 layers.

[0015] Compared with the prior art, the advantages of the present invention are as follows: (1) By introducing the synergistic design of particulate-reinforced ceramics and composite interface modifiers, the present invention effectively improves the compositional uniformity of the core material in the flux-cored wire and the interfacial wettability of the metal matrix. During the arc additive process, the droplet transfer process is stable, the bonding between stacking layers is dense, and the tissue segregation degree is reduced to less than 1.5%, significantly improving the problem of large compositional fluctuations in the existing wire at the initial stage of stacking.

[0016] (2) The present invention adopts high-energy planetary ball milling powder mixing and plasma surface activation pretreatment technologies to make the ceramic reinforcements in the core powder evenly distributed at the microscale, significantly suppressing agglomeration and segregation during the sintering process. The grain size of the finished wire remains within 10-25 μm in the 5-15 layer stacking area, and the degree of tissue refinement is more than 30% higher than that of the conventional process, improving the comprehensive mechanical properties of the additive components.

[0017] (3) By constructing a multi-scale composite powder system, introducing rare earth alloy refiners, and cooperating with intermediate annealing treatment, the present invention reduces the stress concentration and crack initiation tendency during the rolling process of the flux-cored wire. The obtained wire shows excellent processability and thermal stability after hot rolling, no obvious defects are seen in the tensile section, and the qualified rate of the finished product is increased by more than 25% compared with the traditional process.

[0018] (4) The present invention adopts a closed argon protection environment and a low-humidity drying process to effectively control the water vapor and oxide impurity content in the core powder. The finally prepared flux-cored wire shows a low spatter rate, low soot emission and high metal deposition efficiency during arc additive manufacturing. Compared with the traditional open process, the deposition efficiency is increased by 12%, improving the operation safety and environmental friendliness. Description of the Drawings

[0019] Figure 1 It is a schematic flow chart of the processing technology of the flux-cored wire for arc additive manufacturing of the present invention; Detailed Embodiments

[0020] Examples Examples 1-3 Example 1: A flux-cored wire for arc additive manufacturing includes a shell and a core material. The core material is filled inside the shell. The core material consists of the following components by weight percentage: 40-60% nickel-based alloy powder, 10-20% low-volatility activator, 8-15% stable metal oxide, 5-10% particle-reinforced ceramic, 3-6% interface modifier, and 2-5% rare-earth alloy refiner; the shell is a stainless-steel strip with a thickness of 0.2-0.4 mm. After coating, it is sealed by hot rolling to form a flux-cored wire with a core material volume fraction not greater than 35%.

[0021] The particle-reinforced ceramic is spherical silicon nitride with a particle size of 200-500 nm, a uniform volume distribution, and is treated by surface titanate coating.

[0022] The interface modifier is a composite magnesium borate salt. The composite magnesium borate salt of the interface modifier reacts with the nickel-based alloy during the solidification of the molten droplet to form a low-interface-energy interface layer.

[0023] The rare-earth alloy refiner is cerium-aluminum alloy, and the addition amount of the rare-earth alloy refiner is controlled at 2-3%; it is fully mixed with the nickel-based alloy powder by dry ball milling.

[0024] A processing process for a flux-cored wire for arc additive manufacturing includes the following steps: S1. Mix the nickel-based alloy powder, low-volatility activator, stable metal oxide, particle-reinforced ceramic, interface modifier, and rare-earth alloy refiner according to the ratio, and perform high-energy planetary ball milling for 90-120 minutes at a rotation speed of 400-600 rpm; S2. After screening and impurity removal of the treated mixed powder, perform high-sealing drying treatment at a drying temperature of 150-180 °C for 2-3 hours; S3. Use a stainless-steel strip to form a flux-cored coating structure under argon protection. During pressing, control the core material filling rate to be 65-70% and the porosity to be less than 5%; S4. Form a flux-cored wire with a diameter of 1.2-2.0 mm through double-pass hot rolling. Control the hot rolling temperature at 750-850 °C and the total reduction ratio at 45-55%.

[0025] Before the high-energy planetary ball milling treatment in S1, the pretreatment of the particle-reinforced ceramic includes the following steps: S1-1. Treat the particle-reinforced ceramic in a vacuum plasma environment for 5-10 minutes to form an active defect layer on the surface; S1-2. Immerse the treated ceramic particles in a mixed solution of ethanol and isopropyl titanate and stir for 4 hours, and then dry at 80 °C.

[0026] In the drying step of S2, use nitrogen gas flow protection and control the humidity below 0.5% to prevent moisture from reacting with the low-volatility activator.

[0027] The S4 hot rolling step includes an intermediate annealing treatment. The annealing temperature is 700 - 720 °C, and the holding time is 15 - 20 minutes to eliminate the tissue stress.

[0028] After the hot rolling of the flux-cored wire, a plasma surface cleaning treatment is carried out for 30 - 60 seconds to remove the micro-oxidation layer and improve the surface finish.

[0029] A flux-cored wire for arc additive manufacturing has high droplet forming stability during the arc additive manufacturing process. The deviation of the composition distribution is less than 2%, and the grain size of the tissue remains within the range of 10 - 25 μm within the stacking thickness of 5 - 15 layers.

[0030] Example 2: The difference from Example 1 is that the ceramic particles in the core powder are TiB2, and the addition amount is 12 parts by weight; The rare earth refiner is Y2O3, and the addition amount is 3 parts by weight; The ball milling speed is 250 rpm, and the time is extended to 4 hours; After cold rolling, two intermediate annealing treatments are carried out at a temperature of 720 °C for 20 minutes; The grain size of the stacked component is 14 - 20 μm, the tensile strength is 760 MPa, and the elongation is 17%.

[0031] Example 3: The difference from Example 1 is that 10 parts by weight of Al2O3 nanoparticles are added to the core powder, and the particle size of the reinforcing phase is 50 - 100 nm; An argon / hydrogen mixed atmosphere (argon: hydrogen = 95:5) is used for protection, and the humidity is controlled below 5%; The final wire specification is φ1.6 mm; When used in the vertical arc additive path, the interlayer bonding strength of the stacked parts is increased by 15%, and the metal deposition efficiency is 92%.

[0032] Example 4: The difference from Example 1 is that the core powder uses high-energy ultra-fine plasma atomized alloy powder (particle size D50 is 8 μm), and 6 parts by weight of ZrO2 nanoparticles are added; A closed automatic loading device is used, and the powder filling density is controlled to be 4.2 g / cm³; The intermediate annealing temperature is 700 °C, and the time is 20 minutes; The surface roughness Ra of the wire deposition component drops to 3.5 μm, and the tissue density is increased by 12%.

[0033] Comparative Example Comparative Example 1: Compared with Example 1, the plasma surface activation treatment is not used, and other parameters remain the same.

[0034] The obtained welding wire shows obvious irregular droplet transfer phenomenon during arc additive manufacturing; In the deposited layer structure, segregation of inclusions is obvious, the grain size distribution is uneven, and the range is 10 - 38 μm; The tensile strength drops to 690 MPa, the interlayer bonding is poor, and there are microcracks.

[0035] Comparative Example 2: Compared with Example 2, no rare earth refiner is added.

[0036] During the deposition process of the welding wire, the solidification speed of the molten pool is inconsistent, and the grains are coarse; The average grain size is 26 - 42 μm, and the mechanical properties of the deposited parts decrease significantly; The tensile strength drops to 670 MPa, and the elongation is lower than 13%.

[0037] Comparative Example 3: Compared with Example 3, no dry protective atmosphere is used, and compressed air is directly used.

[0038] The core powder absorbs moisture and oxidizes severely during the encapsulation process, resulting in a high oxygen content in the final welding wire; During the additive manufacturing process, the spatter is large and the smoke and dust are obvious; There are porosity defects during the welding process, and the deposition efficiency is only 75%.

[0039] Comparative Example 4: Compared with Example 1, traditional powder mixing (without ball milling) is adopted and the operation is carried out in an open environment.

[0040] The uniformity of the core powder mixing is poor, and the ceramic particles agglomerate severely; The composition of the final deposited parts fluctuates significantly, and the mechanical properties are unstable; The tensile strength fluctuates between 680 - 720 MPa, and a layered and segregated structure appears.

[0041] To determine the composition uniformity and droplet transfer stability of the flux-cored welding wires in Examples and Comparative Examples during arc additive manufacturing, the following comparative experiments are designed, and the experimental steps are as follows: Preparation of experimental items: The flux-cored welding wire samples are φ1.2 mm and φ1.6 mm flux-cored welding wires prepared in Examples 1, 2, 3, 4 and Comparative Examples 1, 2, 3, 4.

[0042] Additive manufacturing equipment: A high-precision numerically controlled arc additive manufacturing system with a constant current control and a high-speed droplet imaging system.

[0043] Observation equipment: High-speed camera (frame rate ≥ 5000 fps), scanning electron microscope (SEM) and energy dispersive spectroscopy (EDS), laser confocal imaging system, metallurgical microscope Experimental environment control: A thermostatic and humidistatic laboratory is adopted, with the temperature controlled at 25 ± 2 °C and the relative humidity at 40 ± 5%; the protective gas is argon or argon-hydrogen mixture with a purity of ≥99.99%.

[0044] The experimental steps are as follows: Wire feeding stability test of welding wire: Each group of welding wires is respectively installed in the automatic wire feeding mechanism, and the wire feeding speed is adjusted to 10 mm / s.

[0045] Set the arc additive manufacturing parameters: current 180 A, voltage 24 V, interlayer cooling time 15 s.

[0046] Use a high-speed imaging system to record the droplet formation, necking, and transition processes of the welding wire at the front end of the molten pool, and the test duration is 60 seconds.

[0047] Analyze the droplet transfer modes, including the occurrence frequencies of short-circuit transfer, globular transfer, liquid bridge transfer, etc., and record the number of droplets and the average diameter per unit time.

[0048] Evaluation of composition uniformity: Prepare standard additive manufacturing specimens (50×10×10 mm³) for each group of welding wires, and take longitudinal section samples after processing.

[0049] Use SEM for microstructure observation, combined with EDS for line scanning and point scanning to analyze the distribution states of ceramic particles and alloy elements in different regions.

[0050] Digitally analyze the particle distribution map with ImageJ and calculate the uniformity index (mean / standard deviation) of the reinforcing particles.

[0051] Conduct cross-sectional metallographic analysis on the welding wire body, observe the distribution trend of the core powder at the cross-sectional position, and identify whether there is eccentricity, agglomeration, or cavity.

[0052] Analysis of the consistency of deposited tissues: Prepare multiple deposited layer samples under the same process conditions (repeated three times for each group).

[0053] Use an optical microscope to observe the grain distribution and morphology of the deposited layers and evaluate the grain size range.

[0054] Conduct X-ray diffraction analysis (XRD) to determine the main metal phases and distribution differences in each region.

[0055] Compare the changes in element contents at different height layers to judge the consistency of composition transfer during the deposition process.

[0056] Welding defect and spatter evaluation: Record the frequency and quantity of spatter generated during the additive manufacturing process in real time; Conduct X-ray flaw detection on the cross-section of the deposited layer to identify typical defects such as holes and inclusions; Conduct a comparative analysis of the welding defects and metal loss caused by unstable droplet transfer.

[0057] The experimental table is as Figure 1 shown: Table 1 Experimental analysis: The flux-cored wires prepared in Examples 1–4 showed better performance during arc additive manufacturing: Wire feeding and droplet behavior: The wire feeding of the example wires was stable, the droplets were mainly transferred by liquid bridge, the transfer frequency was stable, and the average particle size was consistent; while the wires of the comparative examples were prone to short-circuit transfer and unstable droplets, affecting the control of the molten pool.

[0058] Composition uniformity: The elements and particles in the deposited layers in the examples were evenly distributed, and the core powder was well arranged in the cross-section of the wire; while the wires of the comparative examples had segregation, agglomeration and local powder deficiency.

[0059] Consistency of the deposited microstructure: The grains of the deposited samples in the examples were uniform, the interlayer bonding was good, and the microstructure was dense; while the grains of the comparative example samples were coarse and uneven, and there were large fluctuations between layers.

[0060] Welding defect and spatter control: The examples had less spatter, fewer defects, and high welding stability; while the comparative examples had more spatter, were prone to form pores and inclusions, and had low material utilization rate.

[0061] To determine the microstructure density and crack sensitivity of the metal deposited layers of the flux-cored wires in the examples and comparative examples, the following comparative experiments were designed, and the experimental steps are as follows: In this experiment, the flux-cored wire prepared in Example 1 (hereinafter referred to as sample A) and the flux-cored wire prepared in Comparative Example 2 (hereinafter referred to as sample B) were selected for comparison, and the differences in the effects on the microstructure density and crack sensitivity of the deposited layer during arc additive manufacturing were mainly evaluated.

[0062] Preparation of experimental items: 5 kg each of flux-cored wire samples A (Example 1) and B (Comparative Example 2) Medium carbon steel substrate plates, with dimensions of 150 mm × 150 mm × 10 mm, and the surfaces were polished with a grinding wheel and wiped with alcohol GMAW (Gas Metal Arc Welding) additive manufacturing equipment, with a constant current power supply Argon protection, purity ≥99.99%, and the flow rate was adjusted to 25 L / min Thermocouple, infrared thermal imager, XRD analyzer, optical metallographic microscope, scanning electron microscope (SEM), crack analysis system The experimental steps are as follows: A1. Select the above medium carbon steel substrate plates and clean them with alcohol to remove oxides and oil stains to ensure the same initial surface cleanliness.

[0063] A2. The surfacing forming is carried out using sample A and sample B respectively, and the control parameters are as follows: welding current 140 A, voltage 24 V, welding speed 8 mm / s, wire feeding speed 12 m / min, interlayer temperature not exceeding 150 °C, single-pass surfacing thickness 2.5 mm, and a three-layer and six-pass surfacing component is manufactured.

[0064] A3. Samples perpendicular to the weld bead direction are intercepted from the middle of the additive component for metallographic sample preparation, and an optical microscope and SEM are used to analyze the tissue uniformity, grain size, and pore distribution. The number of pores per square millimeter, average grain size, and inclusion distribution index are counted.

[0065] A4. Stress cold cracking sensitivity tests are carried out on the surfacing areas of the two samples respectively. The constrained plate test method with a V-shaped notch is used to observe whether thermal cracks and cold cracks appear during the cooling process to room temperature after additive manufacturing, and their distribution and crack lengths are recorded.

[0066] A5. Residual stress scanning is carried out on the surface and cross-section of the deposition layer by XRD method to compare the principal stress values, stress gradients, and stress concentration regions in the samples made of the two wires.

[0067] The experimental data are shown in Table 2: Table 2 Experimental analysis: The grain size of sample A is significantly smaller than that of sample B, and the number of pores is much lower than that of sample B. The effect of grain refinement makes sample A have a more uniform tissue structure, reduces the stress concentration region caused by micro-defects, and helps to enhance the mechanical properties of the welded joint. In contrast, sample B has larger grains and more pores during the surfacing process, indicating that its compositional uniformity is poor and it is easy to form defect regions, affecting the overall quality of the material.

[0068] Crack sensitivity: No thermal cracks or cold cracks appeared in sample A after surfacing, while multiple cracks appeared in sample B, with the maximum crack length reaching 3.5 mm. The existence of cracks indicates that sample B has a stronger crack sensitivity, which may be due to compositional non-uniformity, welding stress accumulation, and local deformation caused by thermal cycling. In contrast, sample A has improved wire composition and process, making it more resistant to the generation of thermal cracks and cold cracks.

[0069] Residual stress: The XRD test results show that the residual stress of sample A is lower and controlled within a reasonable range, indicating that the thermal stress during the surfacing process is more evenly distributed and it is not easy to generate stress concentration; while the residual stress of sample B is higher, which may cause deformation or cracks during use.

[0070] The foregoing has shown and described the basic principles, main features and advantages of the present invention; those skilled in the art should understand that the present invention is not limited by the above embodiments, and the above embodiments and the descriptions in the specification are only preferred examples of the present invention, and are not used to limit the present invention. Without departing from the spirit and scope of the present invention, the present invention will have various changes and improvements, and these changes and improvements all fall within the scope of the present invention claimed; the scope of the present invention claimed is defined by the appended claims and their equivalents.

Claims

1. A flux-cored wire for arc additive manufacturing, characterized in that, It includes a shell and a core material. The core material is filled inside the shell. The core material is composed of the following components by weight percentage: 40-60% nickel-based alloy powder, 10-20% low-volatility activator, 8-15% stable metal oxide, 5-10% particle-reinforced ceramic, 3-6% interface modifier, and 2-5% rare-earth alloy refiner; the shell is a stainless-steel strip with a thickness of 0.2-0.4 mm, and after coating, it is sealed by hot rolling to form a flux-cored wire with a core material volume fraction not greater than 35%.

2. The flux-cored wire for arc additive manufacturing according to claim 1, wherein, The particle-reinforced ceramic is spherical silicon nitride with a particle size of 200-500 nm, a uniform volume distribution, and is treated by surface titanate coating.

3. The flux-cored wire for arc additive manufacturing according to claim 1, wherein, The interface modifier is a composite magnesium borate salt. The composite magnesium borate salt of the interface modifier reacts with the nickel-based alloy during the solidification of the molten droplet to form a low-interface-energy interface layer.

4. The flux-cored wire for arc additive manufacturing according to claim 1, wherein The rare-earth alloy refiner is cerium-aluminum alloy, and the addition amount of the rare-earth alloy refiner is controlled at 2-3%; it is fully mixed with the nickel-based alloy powder by dry ball milling.

5. A processing process for flux-cored wire used in arc additive manufacturing, characterized in that, The processing technology of the flux-cored wire for arc additive manufacturing includes the following steps: S1. Mix the nickel-based alloy powder, low-volatility activator, stable metal oxide, particle-reinforced ceramic, interface modifier, and rare-earth alloy refiner according to the ratio, and perform high-energy planetary ball milling treatment for 90-120 minutes at a rotation speed of 400-600 rpm; S2. After screening and impurity removal of the treated mixed powder, perform high-sealing drying treatment, with a drying temperature of 150-180 °C and a time of 2-3 hours; S3. Use a stainless-steel strip to form a flux-cored coating structure under argon protection. During pressing, control the core material filling rate at 65-70% and the porosity below 5%; S4. Form a flux-cored wire with a diameter of 1.2-2.0 mm through double-pass hot rolling treatment. The hot rolling temperature is controlled at 750-850 °C, and the total reduction is 45-55%.

6. The processing technology of the flux-cored wire for arc additive manufacturing according to claim 5, characterized in that, Before the S1 high-energy planetary ball milling treatment, the pretreatment of the particle-reinforced ceramic includes the following steps: S1-1. The particle-reinforced ceramic is treated in a vacuum plasma environment for 5-10 minutes to form an active defect layer on the surface; S1-2. Immerse the treated ceramic particles in a mixed solution of ethanol and isopropyl titanate and stir for 4 hours, and then dry at 80 °C.

7. The processing technology of the flux-cored wire for arc additive manufacturing according to claim 5, characterized in that In the S2 drying step, nitrogen gas flow protection is adopted, and the humidity is controlled below 0.5% to prevent moisture from reacting with the low-volatility activator.

8. A processing technology for flux-cored wire used in arc additive manufacturing according to claim 5, characterized in that, The S4 hot rolling step includes a primary intermediate annealing treatment, with an annealing temperature of 700-720 °C and a holding time of 15-20 minutes to eliminate tissue stress.

9. The processing technology of the flux-cored wire for arc additive manufacturing according to claim 5, wherein, After the hot rolling of the flux-cored wire, plasma surface cleaning treatment is carried out for 30-60 seconds to remove the micro-oxidation layer and improve the surface finish.

10. A flux-cored wire processing process for arc additive manufacturing according to any one of claims 1-9, characterized in that, The flux-cored wire for arc additive manufacturing has high molten droplet forming stability during the arc additive manufacturing process, with a composition distribution deviation of less than 2%, and the grain size of the tissue remains within the range of 10-25 μm within the stacking thickness of 5-15 layers.

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