In-situ crosslinking fused deposition electrode wire

Abstract

The invention discloses an in-situ cross-linked fused deposition electrode wire, which belongs to the technical field of lithium batteries and is prepared from a lithium battery active material, a conductive agent, a nano material, a cross-linking agent and a polymer carrier material, the lithium battery active material and the nano material are subjected to a cross-linking reaction with the cross-linking agent and then loaded into the polymer carrier material, and the polymer carrier material is loaded into the conductive agent. And electrode wires are extruded and printed in a fused deposition mode. The polymer and the active conductive material are polymerized under the action of the cross-linking polymerization agent, stable molecules of a network structure are formed through mutual bonding and cross-linking, and more active materials and conductive materials can be embedded into the polymerized and molten electrode material in a certain space; and the strength and the thermal stability of the electrode material are further improved while the capacity is improved.

Description

Technical Field

[0001] The present invention relates to the technical field of lithium batteries, and in particular to a method for preparing lithium battery electrode wires by combining in-situ cross-linking polymerization with melt deposition extrusion. Background Art

[0002] With the development of the new energy industry, the total capacity of lithium-ion batteries will increase from 700 GWh to 4,700 GWh between 2022 and 2030, and the market size will grow from US$85 billion to US$400 billion. Lithium-ion batteries are currently widely used in consumer electronics, new energy vehicles, industrial energy storage, and other fields. Currently, the commonly used lithium battery material systems mainly include lithium iron phosphate and lithium cobalt oxide for the positive electrode, and graphite for the negative electrode. Silicon-carbon materials with higher capacity and lithium titanate, known for its safety, are also beginning to be commercialized. These materials are currently the most widely used in commercial applications. The battery structure involves many materials, and these materials require a suitable structural system to effectively combine them. Therefore, the electrode structure design must be more scientific and reasonable, and the battery will achieve better performance.

[0003] The current mainstream battery structure is to coat the positive electrode material on aluminum foil and the negative electrode material on copper foil, which are then combined with a separator to form a battery. The copper and aluminum foils collect the current generated by the active materials, acting as current collectors. The coating thickness of the electrode material produced by the traditional coating process is less than 100μm. The coating thickness produced by the traditional coating process is an important factor affecting the charge and discharge speed. Due to the limitations of the traditional coating process, the production of a large-capacity battery requires multiple coatings and then combining the coating units. The production process of this battery requires the use of a large amount of copper and aluminum foil, which affects the energy density of the battery.

[0004] In order to improve the energy density of the battery, the more mature technical route is to use a thinner current collector to reduce the volume and mass occupied by the current collector. The current thickness of the current collector can reach 6μm, and the thickness of the diaphragm can also reach 10μm. The thinner current collector and diaphragm process can reduce the space occupancy of the battery components to a certain extent. Due to the constraints of the manufacturing process, relying on reducing the space occupancy of the current collector and diaphragm to increase the battery energy density is limited to improve the range of battery energy density.

[0005] By modifying epoxy resin, Harvard University has achieved the first 3D printing of thermosetting resin and used slurry direct writing 3D printing technology to produce a battery prototype. 3D printing can basically meet the needs of electrode structure innovation. Combining 3D printing technology with battery electrode materials can produce thick electrodes on the current collector, increasing the effective load ratio of electricity and thus improving the energy density of the battery. Since then, many scientific research institutions and companies around the world have begun to study 3D printed lithium-ion batteries; however, while 3D printing increases the thickness of the electrode material layer, it also slows the diffusion of lithium ions in the active material interface, which affects the battery's charge and discharge efficiency. Summary of the Invention

[0006] In order to further improve the transfer speed of lithium ions in the active material interface layer, the lithium ion diffusion channel is modified by in-situ cross-linking to improve the diffusion rate of lithium ions in the active material interface layer, and the loading amount of active substances on the current collector is increased by relying on 3D printing technology. The present invention provides an in-situ cross-linked melt-deposited electrode wire with high active substance loading amount and rapid lithium ion diffusion channel.

[0007] In order to solve the above technical problems, the technical solution of the present invention is: An in-situ cross-linked melt-deposited electrode wire is prepared from lithium battery active materials, conductive agents, nanomaterials, cross-linking agents and polymer carrier materials. The lithium battery active materials and nanomaterials are loaded into the polymer carrier material after undergoing a cross-linking reaction with the cross-linking agent, and the electrode wire is extruded and printed by melt deposition.

[0008] Wherein, the lithium battery active materials are lithium battery positive electrode and negative electrode active material substances.

[0009] The lithium battery active material is any one or more of lithium iron phosphate (LFP) material, lithium titanate, graphite, nano-silicon-based material, and silicon-carbon material.

[0010] Wherein, the conductive agent is any one or more of a zero-dimensional conductive agent, a one-dimensional conductive agent, and a two-dimensional conductive agent.

[0011] The conductive agent is any one or more of conductive carbon black, conductive graphite, conductive carbon fiber (SP), single-walled carbon nanotube (SWCNT), multi-walled carbon nanotube (MWCNT), and mixed conductive paste.

[0012] Wherein, the nano material is a nano powder material, and the nano powder material is nano alumina and / or nano titanium dioxide.

[0013] The cross-linking agent is any one or more of polyvinylidene fluoride (PVDF), carboxymethyl cellulose (CMC) powder, styrene-butadiene rubber (SBR) emulsion, polyvinyl alcohol (PVA), lithiated polyacrylic acid binder (PAA-Li), polytetrafluoroethylene (PTFE), polyolefins, phenolic resin, coal tar, coal tar, triglycidyl isocyanurate, and ethylene glycol dimethacrylate.

[0014] Wherein, the polymer carrier material is a carbon chain polymer, a non-carbon chain polymer, a thermoplastic polymer or a thermosetting polymer.

[0015] The polymer carrier material is any one or more of polypropylene (PP), ethylene-octene copolymer (POE), polylactic acid (PLA), polycaprolactone (PCL), polyacrylonitrile (PAN), and thermoplastic starch.

[0016] The mass ratio of the lithium battery active material to the conductive material is 1.5:1-4.5:1, the mass ratio of the lithium battery active material to the crosslinking agent is 1.5:1-35:1, and the mass ratio of the lithium battery active material to the polymer carrier material is 1:6-5:1.

[0017] Compared with the prior art, the present invention has the following positive effects: The present invention utilizes polymers and active conductive materials to polymerize under the action of a cross-linking polymerization agent, and forms stable molecules with a network structure through mutual bonding and cross-linking. The electrode material after polymerization and melting can embed more active materials and conductive materials in a certain space, which can improve the battery capacity to a certain extent. BRIEF DESCRIPTION OF THE DRAWINGS

[0018] Figure 1 For measuring the resistance of extruded active material electrode wire; Figure 2 Make an electrode sheet model diagram using modeling software; Figure 3 Print the active material electrode wire according to the established electrode sheet model using a printer; Figure 4 The discharge capacity diagram at different rates; Figure 5 The charge and discharge voltage platform curves at different sintering temperatures; Figure 6 Print the active material electrode wire according to the established electrode sheet model using a printer; Figure 7 The resistance measurement of the positive electrode sheet; Figure 8This is a comparison chart of the rate capacity of the 3D printed lithium iron phosphate spray dry material electrode buckle test and the normal slurry coating buckle test; Figure 9 This is a test chart of 170 cycles at 1C rate; Figure 10 This is the charge and discharge voltage platform curve of lithium iron phosphate spray dry material at 1C rate; Figure 11 The process of 3D printing pole pieces; Figure 12 The discharge capacity curve is obtained by performing 5 cycles of charge and discharge test at 1C and 0.1C rates. Figure 13 Data sheet for charge and discharge tests performed at 1C and 0.1C rates for 5 cycles. DETAILED DESCRIPTION

[0019] The present invention is further illustrated by way of examples below, but the present invention is not limited to the scope of the examples. Experimental methods in the following examples where specific conditions are not specified were performed according to conventional methods and conditions, or selected according to the product specifications. Example 1

[0020] This embodiment provides an in-situ cross-linked melt-deposited electrode wire, which is made by the following preparation method: (1) The main lithium salt lithium iron phosphate material, conductive carbon fiber, and multi-walled carbon nanotubes are added to a solvent in 1,4-dioxane, and the mixed solution is placed on a magnetic stirrer for stirring and dispersion. The stirring is performed at a speed of 1000 rm so that the substances between the phases can be fully dispersed into the solvent phase; the mass ratio of the lithium salt lithium iron phosphate material to the conductive carbon fiber is 6:1, and the mass ratio of the lithium iron phosphate material to the multi-walled carbon nanotubes is 6:1; (2) Adding the polymer material polylactic acid and the cross-linking agent polyvinylidene fluoride to the uniformly mixed dispersion and continuing stirring for 12 hours; the mass ratio of the polymer material polylactic acid to the lithium iron phosphate material is 1:20, and the mass ratio of polyvinylidene fluoride to the lithium iron phosphate material is 1:2; (3) Pour the stirred mixture into a crystallization dish and dry it in a forced air drying oven at a drying temperature of 50-70°C for 12 hours to remove excess organic solvent; (4) After drying, the excess organic solvent is removed to obtain a uniformly dispersed solid active material, and then the solid material is pretreated; that is, the solid active material is cut and crushed to obtain solid material particles of uniform size and a particle size of 0.5 cm; (5) The processed small particles of solid material are pushed through a screw in a screw extruder. The extrusion temperature of the extruder is 165°C and the extrusion speed of the extruder is 900 rpm to obtain an active material electrode wire with a diameter of 1.75 mm, a continuous structure and a smooth surface.

[0021] Performance testing: ①Measure the resistance of the extruded active material electrode wire, such as Figure 1 shown.

[0022] ② Combine the extruded active material electrode wire with the FDM3D printer to print the electrode sheet a. Make an electrode sheet model using modeling software, print out a gradient triangle electrode sheet with a diameter of 12mm and a height of 0.4mm, and convert the model into a G-code file using slicing software and send it to the printer web page, such as Figure 2 As shown; b. Print the active material electrode wire according to the established electrode sheet model through the printer, such as Figure 3 As shown, the printing temperature is 235℃ and the printing platform temperature is 60℃ ③Measure the resistance and physical properties of the 3D printed electrode sheets; ④Put the electrode sheet printed by the 3D printer into a tube furnace and sinter it under inert gas conditions. The selected inert gas is nitrogen. The sintering temperature is 50℃ and the sintering time is 4h. The active material electrode sheet with intact structure after 3D printing and sintering is used as the positive electrode, and the metal lithium sheet is used as the negative electrode to make a button battery. The assembled battery is subjected to charge and discharge cycle test on a neware test cabinet.

[0023] Figure 4 The discharge capacity at different rates is shown. At low rates, such as 0.1C, the specific capacity decreases relatively slowly. This is likely because at smaller discharge currents, the electrochemical reaction inside the battery is relatively mild, causing less damage to the internal structure of the battery and a relatively slow loss of active materials. However, at high rates, such as 2C, the specific capacity decreases more rapidly. High-rate discharge generates more heat inside the battery, exacerbating the damage to the polymer structure in the electrode material. At the same time, high currents accelerate the decomposition of the electrolyte and the shedding of active materials, causing a rapid decrease in specific capacity.

[0024] ⑤ The printed electrode is sintered at different temperatures, and then the charge and discharge test is performed. The charge and discharge voltage platform curves at different sintering temperatures are as follows: Figure 5 shown.

[0025] 375° (black curve): At the highest sintering temperature, the polymer material decomposes and volatilizes more thoroughly, leaving less residue in the electrode. High temperatures also facilitate a tighter bond between the active material and conductive agent particles, forming a more stable electrode structure. This results in a higher specific capacity and a more stable voltage plateau, thanks to improved electrode conductivity and lithium-ion diffusion rates.

[0026] 340° (red curve): At moderate sintering temperatures, the polymer material may not decompose as thoroughly as at high temperatures, leaving a small amount of polymer material in the electrode. The electrode structure stability and conductivity lie between those at high and low sintering temperatures. This results in slightly lower stability of the specific capacity and voltage plateaus than at high sintering temperatures, but higher than at low sintering temperatures.

[0027] 300° (blue curve): At the lowest sintering temperature, the polymer material may not be completely decomposed, resulting in a large amount of residual polymer material in the electrode. The electrode structure is less stable, and the conductivity and lithium ion diffusion rate may be low. This results in a lower specific capacity and an unstable voltage plateau due to the limited electrochemical activity of the electrode. Example 2

[0028] This embodiment provides an in-situ cross-linked melt-deposited electrode wire, which is made by the following preparation method: (1) Weigh 5 g of lithium iron phosphate spray dried material (LFP) positive electrode active material, place it in a tube furnace and sinter it at high temperature to obtain lithium iron phosphate (LFP) active material; the sintering atmosphere is nitrogen, and the sintering temperature is 750 ° C; the lithium iron phosphate (LFP) positive electrode active material after high temperature sintering accounts for 35% of the lithium iron phosphate (LFP) spray dried material; (2) Weighing conductive carbon fiber (SP) and lithium iron phosphate (LFP) positive electrode active material and mixing them to obtain a conductive positive electrode active material; the mass ratio of lithium iron phosphate (LFP) spray-dried material to conductive agent (SP) is 2.15:1; (3) Phenolic resin, coal tar and coal tar were weighed. Phenolic resin, coal tar and coal tar were used as high-temperature binders (cross-linking agents). The mass ratio of lithium iron phosphate (LFP) spray-dried material to phenolic resin was 14:1, the mass ratio of lithium iron phosphate (LFP) spray-dried material to phenolic resin was 1.43:1, the mass ratio of lithium iron phosphate (LFP) spray-dried material to coal tar was 1.43:1, and the mass ratio of lithium iron phosphate (LFP) spray-dried material to coal tar was 1.43:1. (4) Single-walled carbon nanotubes (SWCNTs) were weighed as conductive materials. The addition of single-walled carbon nanotubes can improve the mechanical properties of the material. The mass ratio of lithium iron phosphate (LFP) spray-dried material to single-walled carbon nanotubes (SWCNTs) was 2.15:1. (5) Weigh polylactic acid (PLA) as the 3D printing extrusion skeleton support material, and the mass ratio of lithium iron phosphate (LFP) spray-dried material to polylactic acid (PLA) is 14:1; (6) Weigh 1,4-dioxane as a mixed solvent to fully dissolve and evenly mix the substances; the mass ratio of lithium iron phosphate (LFP) spray-dried material to 1,4-dioxane is 1:24; (7) Use a beaker to measure 120 mL of 1,4-dioxane, put a magnet in the beaker and place it on a magnetic stirrer for stirring at a speed of 400-500 rpm. After the speed of the 1,4-dioxane solvent in the beaker stabilizes, gradually add the weighed conductive carbon fiber into the beaker for dissolution and mixing. After the conductive carbon fiber is dissolved in the 1,4-dioxane solvent and mixed evenly, add the sintered lithium iron phosphate (LFP) spray-dried material and continue stirring in the beaker. During the stirring process, add the conductive agent (SWCNT), cross-linking agent, and polylactic acid (PLA) in sequence at intervals of 5 minutes and continue stirring and mixing for 12 hours. (8) After the stirring is completed, a uniformly mixed solution of lithium iron phosphate (LFP) active material is obtained, and the mixed solution is introduced into a glass dish and placed in an oven for drying to obtain a mixed active material; (9) The dried material is cut into small pieces of uniform size and complete structure. The cut mixed active material is poured into a screw extruder for extrusion at an extrusion temperature of 133~145℃ and an extrusion speed of 600~900rpm. After extrusion by the extruder, an active material electrode wire with a diameter of 1.75mm, a continuous structure and a smooth surface can be obtained.

[0029] Performance testing: ①Measure the resistance of the extruded active material electrode wire; ② The extruded active material electrode wire is combined with the FDM3D printer to print the electrode sheet. The electrode sheet model is made by modeling software, and a gradient triangular electrode sheet with a diameter of 12mm and a height of 0.4mm is printed. The model is converted into a G-code file by slicing software and sent to the printer web page. The active material electrode wire is printed according to the established electrode sheet model by the printer, such as Figure 6 As shown, the printing temperature is 235°C and the printing platform temperature is 60°C.

[0030] ③Measure the resistance and physical properties of the 3D printed electrode sheets.

[0031] The electrode sheets and anhydrous glucose printed by the 3D printer were placed in a tubular furnace and sintered under inert gas conditions. The selected inert gas was nitrogen, the heating rate was 5°C / min, and the sintering was carried out at 750°C for 9 hours.

[0032] The sintered lithium iron phosphate (LFP) spray-dried active material electrode sheet was transferred and fixed onto an aluminum foil current collector to serve as a battery positive electrode sheet. The resistance of the positive electrode sheet was measured, such as Figure 7 shown.

[0033] ④Use the metal lithium sheet as the negative electrode of the battery to assemble the button battery. The assembled battery is tested for charge and discharge cycle on the neware test cabinet. The 3D printed lithium iron phosphate spray dry material electrode is tested for charge and discharge at 0.1C, 0.2C, 0.5C, 1C, 2C, and 5C respectively. Figure 8 and 3 3D printed lithium iron phosphate spray dry material electrode buckle test normal slurry coating buckle test rate capacity comparison chart.

[0034] The average discharge capacity of the 3D printed lithium iron phosphate spray-dried electrode at 0.1C, 0.2C, 0.5C, 1C, 2C, and 5C rates was 168 mAh / g, 165 mAh / g, 147 mAh / g, 126 mAh / g, 100 mAh / g, and 69 mAh / g, respectively. The average discharge capacity of the lithium iron phosphate material slurry coated at the same rate was 155 mAh / g, 155 mAh / g, 152 mAh / g, 146 mAh / g, 134 mAh / g, and 2.7 mAh / g, respectively. As can be seen from the curve in the figure, the discharge capacity of the 3D printed lithium iron phosphate spray-dried material is higher than that of the lithium iron phosphate material at low rates of 0.1C and 0.2C, and is lower than that of the lithium iron phosphate material at rates of 0.5C-2C. Between 0.1C and 2C, the rate discharge capacity of the two is not much different. The charge and discharge at a rate of 5C showed that the 3D printed lithium iron phosphate spray-dried material can still maintain a discharge specific capacity of 69 mAh / g, which is much higher than the discharge specific capacity of 2.7 mAh / g of lithium iron phosphate coating at the same rate.

[0035] Figure 9This is a test chart for 170 cycles at a 1C rate. The initial capacity of the lithium iron phosphate spray-dried material printed electrode is 135 mAh / g. After 100 cycles, the capacity is 124 mAh / g, with a capacity retention rate of 91.8%. After 170 cycles, the capacity is 85 mAh / g, with a capacity retention rate of 62.9%. The initial capacity of the lithium iron phosphate material is 146 mAh / g. After 100 cycles, the capacity is 133 mAh / g, with a capacity retention rate of 91.1%. After 170 cycles, the capacity is 127 mAh / g, with a capacity retention rate of 86.9%. In the first 100 cycles, the capacity retention rate of the lithium iron phosphate spray-dried material is close to that of the lithium iron phosphate material. In the cycles of 100-170 cycles, the capacity retention rate of the lithium iron phosphate spray-dried material is slightly lower than that of the lithium iron phosphate material.

[0036] Figure 10 This is the charge and discharge voltage platform curve of lithium iron phosphate spray dry material at 1C rate. The charge and discharge voltage range is between 1.8-4.2V, which is consistent with the lithium iron phosphate material. Example 3

[0037] Ball milling method for the preparation of PVDF premixed for 3D printing electrode sheets Reagents: Silicon carbon (CNS-SG1500), multi-walled carbon nanotubes (MWCNT), conductive carbon black (SP), polyvinylidene fluoride, polylactic acid (PLA), N-methylpyrrolidone (NMP) This embodiment provides an in-situ cross-linked melt-deposited electrode wire, which is made by the following preparation method: (1) Take 21.6 g of polylactic acid and dissolve it in 1,4-dioxane solution at a mass concentration of 8 wt %; (2) According to the mass ratio of silicon carbon: multi-walled carbon nanotubes: conductive carbon black: polyvinylidene fluoride = 6:1.0:0.3:0.17, 3.6g of silicon carbon material, 0.6g of multi-walled carbon nanotubes, 0.2g of conductive carbon black, and 0.1g of polyvinylidene fluoride were weighed respectively, and several agate grinding beads were placed in an agate grinding tube jar together with the materials for ball milling; the ball milling method adopted was dry milling, and the ball milling time was 5min; (3) Add N-methylpyrrolidone to the dry-milled material at a polyvinylidene fluoride concentration of 5 wt%, stir and mix evenly with a glass rod, then place the evenly mixed and fully contacted phase materials in a ball mill for ball milling for 1 hour, gather the stirred phases at the bottom of the ball ink tank, then add N-methylpyrrolidone solvent again at a polyvinylidene fluoride concentration of 4 wt%, and continue ball milling the material in the ball mill for 1 hour. The ball-milled material maintains a uniform viscosity and has a certain fluidity; (4) Add the slurry (containing 3.6 g of silicon-carbon material, 0.6 g of multi-walled carbon nanotubes, 0.2 g of conductive carbon black, and 0.1 g of polyvinylidene fluoride) to the PLA solution and stir at 600 rpm for 12 h. Pour the stirred slurry into a crystallizing dish and dry it in an oven at 55 °C for 48 h. (5) After drying, a black flake material is obtained, which is cut into small pieces and extruded into wires with a diameter of ≤1.75 mm using a single-screw extruder; (6) The extruded active material electrode wire is combined with an FDM 3D printer to print electrode sheets.

[0038] Performance testing: ① Use modeling software to make a regular hexagonal electrode sheet model with a side length of 5mm and grooves of different thicknesses. Use slicing software to convert the model into a G-code file and send it to the printer web page. Use the printer to print the active material electrode wire according to the established electrode sheet model. In some preferred embodiments, the printing temperature is 235°C and the printing platform temperature is 60°C. The process of 3D printing the electrode sheet is as follows: Figure 11 shown.

[0039] ② Place the electrode sheet printed by the 3D printer into a tubular furnace and sinter it under inert gas conditions. The selected inert gas is argon, the heating rate is 5℃ / min, the sintering temperature is 600℃, and the sintering time is 3h.

[0040] The printed pole pieces of different thicknesses (400μm, 600μm, 800μm) and normal slurry coating (200μm) were subjected to a charge-discharge test. The charge-discharge test was performed at 0.1C, 0.2C, 0.5C, 1C, and 0.1C rates for 5 cycles. The test results are as follows: Figure 12 and Figure 13 shown As can be seen from the figure, among the three thicknesses of 3D printed electrodes, the one with a thickness of 400μm has the best comprehensive performance. At a rate of 0.1C, compared with the average discharge capacity of 1399.6 mAh / g of traditional slurry coating, the average discharge capacity of 400μm, 600μm, and 800μm thickness electrodes printed by 3D are 1617.1 mAh / g, 1442.7 mAh / g, and 1328.3 mAh / g, respectively. The discharge capacity of the 3D printing process at a low rate is significantly higher than that of the traditional slurry coating process. Under a 0.1C rate cycle, the average discharge capacity of the 400μm thick 3D printed electrode is 1617.1 mAh / g, which is 15.5% higher than the 1399.6 mAh / g discharge capacity of the traditional slurry coating process. Under a 0.2C rate cycle, the average discharge capacity of the 400μm thick 3D printed electrode is 1394.7 mAh / g, which is 18.9% higher than the 1172.6 mAh / g discharge capacity of the traditional slurry coating process. Under a 0.5C rate cycle, the average discharge capacity of the 400μm thick 3D printed electrode is 1022.9 mAh / g, which is 33.2% higher than the 768.2 mAh / g discharge capacity of the traditional slurry coating process. Under a higher rate cycle of 1C, the average discharge capacity of the 3D printed electrode with a thickness of 400μm is 527.6mAh / g, which is 8.4% higher than the discharge capacity of 486.9mAh / g obtained by the traditional slurry coating process. After cycling at a high rate of 1C, the battery continued to cycle at a low rate of 0.1C. It was found that the discharge capacity of the traditional slurry coating process was only 694.5 mAh / g, and the capacity retention rate at the low rate at the beginning was only 49.6%. The discharge capacities of the 3D-printed 400μm, 600μm, and 800μm thick electrodes were 1592.9 mAh / g, 1231.5 mAh / g, and 1167.5mAh / g, respectively, and the capacity retention rates were 98.5%, 85.4%, and 87.8%, respectively. The rate cycling capacity retention was much higher than that of the traditional slurry coating process.

Claims

1. An in-situ cross-linked melt-deposited electrode wire, characterized in that It is prepared from lithium battery active materials, conductive materials, cross-linking agents and polymer carrier materials. The lithium battery active materials and conductive materials are loaded into the polymer carrier material after cross-linking reaction with the cross-linking agent, and the electrode wire is extruded and printed by melt deposition.

2. The in-situ cross-linked melt-deposited electrode wire according to claim 1, characterized in that: The lithium battery active materials are lithium battery positive electrode and negative electrode active material substances.

3. The in-situ cross-linked melt-deposited electrode wire according to claim 2, characterized in that: The lithium battery active material is any one or more of lithium iron phosphate, lithium titanate, graphite, nano-silicon-based materials, and silicon-carbon materials.

4. The in-situ cross-linked melt-deposited electrode wire according to claim 1, characterized in that: The conductive material is any one or more of a zero-dimensional conductive material, a one-dimensional conductive material, and a two-dimensional conductive material.

5. The in-situ cross-linked melt-deposited electrode wire according to claim 4, characterized in that: The conductive material is any one or more of conductive carbon black, conductive graphite, conductive carbon fiber, single-walled carbon nanotubes, multi-walled carbon nanotubes, and mixed conductive slurry.

6. The in-situ cross-linked melt-deposited electrode wire according to claim 1, characterized in that: The crosslinking agent is any one or more of polyvinylidene fluoride, carboxymethyl cellulose powder, styrene-butadiene rubber emulsion, polyvinyl alcohol, lithiated polyacrylic acid binder, polytetrafluoroethylene, polyolefins, phenolic resin, coal pitch, coal tar, triglycidyl isocyanurate, and ethylene glycol dimethacrylate.

7. The in-situ cross-linked melt-deposited electrode wire according to claim 1, characterized in that: The polymer carrier material is a carbon chain polymer, a non-carbon chain polymer, a thermoplastic polymer or a thermosetting polymer.

8. The in-situ cross-linked melt-deposited electrode wire according to claim 7, characterized in that: The polymer carrier material is any one or more of polypropylene, ethylene-octene copolymer, polylactic acid, polycaprolactone, polyacrylonitrile, and thermoplastic starch.

9. The in-situ cross-linked melt-deposited electrode wire according to claim 1, characterized in that: The mass ratio of the lithium battery active material to the conductive material is 1.5:1-4.5:1, the mass ratio of the lithium battery active material to the crosslinking agent is 1.5:1-35:1, and the mass ratio of the lithium battery active material to the polymer carrier material is 1:6-5:1.

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