Multi-channel high-conductivity porous carbon material, and preparation method therefor and use thereof

Abstract

A multi-channel high-conductivity porous carbon material, and a preparation method therefor and the use thereof. The preparation method comprises the following steps: S1, subjecting carbon nanotubes to an acidization treatment to obtain carboxylated carbon nanotubes, subjecting same to an emulsification treatment to obtain short carboxylated carbon nanotubes, uniformly mixing same with a nitriding agent, and washing the mixture to be neutral to obtain a functionalized carbon nanotube mixed solution A; S2, mixing a phenolic monomer, an aldehyde monomer and an alkaline solution, subjecting the mixture to condensation polymerization to obtain a phenolic resin oligomer, mixing the phenolic resin oligomer with the functionalized carbon nanotube mixed solution A, and uniformly stirring the mixture to obtain a functionalized carbon nanotube-phenolic resin precursor mixed solution B; S3, drying the functionalized carbon nanotube-phenolic resin precursor mixed solution B to obtain a porous carbon dry powder C; and S4, heating the porous carbon dry powder C to 800-1200ºC, introducing CO2 for activation, and cooling same to obtain the multi-channel high-conductivity porous carbon material. In the multi-channel high-conductivity porous carbon material obtained by the preparation method, the carbon nanotubes are more uniformly dispersed in the material, the specific surface area is larger, and the conductivity is better.

Description

Multi-channel high-conductivity porous carbon material, preparation method and application thereof TECHNICAL FIELD

[0001] The present application relates to the technical field of porous carbon-based composite material preparation, and particularly relates to a multi-channel high-conductivity porous carbon material, a preparation method and application thereof. BACKGROUND

[0002] Silicon-carbon negative electrode materials have a broad application prospect due to their high specific capacity and increasing penetration rate in the lithium-ion power battery market. The silane deposition method is one of the mainstream processes for preparing silicon-carbon negative electrode materials. In brief, a porous carbon is used as a substrate to adsorb silane and other silicon-containing gases, and amorphous silicon particles are formed by high-temperature cracking in the pores of the substrate, so as to slow down the expansion of silicon particles. Therefore, the properties of the porous carbon will directly affect the deposition effect of the silicon-containing gas and the performance of the silicon-carbon product. Resin-based porous carbon raw materials are controllable, adjustable in pore size, and stable in structure, and are currently the ideal porous carbon substrate. However, some properties still need to be improved, such as effective specific surface area and electrical conductivity.

[0003] Carbon nanotubes, as a new type of one-dimensional carbon material, have a unique hollow tubular structure, high electrical conductivity, large specific surface area and excellent mechanical properties. In addition, due to the quantum confinement effect, electrons can quickly migrate along the radial direction of the carbon nanotubes, so the carbon nanotubes are often combined with other materials to improve the electrochemical performance.

[0004] Chinese patent CN104828804B prepares a carbon nanotube-carbon spherical composite material by titration combined with layered oil bath curing. The obtained porous carbon is uniform in size and controllable, has rich pore structure, high specific surface area and other characteristics, so that the composite material has better adsorption performance. However, carbon nanotubes are prone to entanglement and aggregation, and the problem of uneven dispersion and poor combination exists when the carbon nanotubes are directly added in a high molecular solution by physical mixing.

[0005] Chinese patent application CN110148760A prepares a porous carbon-carbon nanotube composite material by one-step solid-phase pyrolysis. The carbon nanotubes are uniformly dispersed on the surface of the porous carbon, which greatly improves the electrical conductivity of the porous carbon material and exhibits excellent electrocatalytic activity. However, the growth of carbon nanotubes is not easy to control (length, diameter, etc.), and the attachment of carbon nanotubes on the surface of the carbon material is difficult to improve the ion solid-phase mass transfer process in the interior of the porous carbon.

[0006] Chinese patent application CN105006375A avoids the self-winding and agglomeration of carbon nanotubes and enhances the binding capacity of the carbon nanotubes by combining carboxylated carbon nanotubes and phenolic resin, and further improves the electronic conduction capacity by doping nitrogen and phosphorus elements, thereby improving the specific capacitance and cycle stability of the supercapacitor. However, the morphology of the carbon nanotubes wrapped with phenolic resin is not easy to control after calcination, and the pore holes formed by the internal to external activation of melamine and phosphating agent are limited, and the obtained porous carbon composite material is a mesoporous structure, and the specific surface area is relatively small. SUMMARY

[0007] The present application aims to provide a multi-channel high-conductive porous carbon material with good carbon nanotube dispersity, higher conductivity and larger specific surface area, and a preparation method of the multi-channel high-conductive porous carbon material.

[0008] The present application discloses a multi-channel high-conductive porous carbon material, comprising the following steps:

[0009] S1: acidizing treatment of carbon nanotubes to obtain carboxylated carbon nanotubes, emulsification treatment to obtain short carboxylated carbon nanotubes, mixing with a nitrogenizing agent, washing to neutral, and obtaining a functionalized carbon nanotube mixture A;

[0010] S2: mixing of a phenolic monomer, an aldehyde monomer and an alkaline solution to polymerize into a phenolic resin oligomer, mixing with the functionalized carbon nanotube mixture A, and stirring to obtain a functionalized carbon nanotube-phenolic resin precursor mixture B;

[0011] S3: drying of the functionalized carbon nanotube-phenolic resin precursor mixture B to obtain a porous carbon dry powder C;

[0012] S4: heating of the porous carbon dry powder C to 800-1200℃, activation by carbon dioxide, and obtaining a multi-channel high-conductive porous carbon material after cooling.

[0013] Further, the acid solution for acidizing treatment is a mixture of concentrated sulfuric acid and concentrated nitric acid; the treatment method is: adding 100-300mL of acid solution to 1g of carbon nanotubes; the concentration of the acid solution is 80-99%; and the treatment time is 10-60min.

[0014] When the carbon nanotubes are acidized, the carbon chains at the ends of the carbon nanotubes are cut off and oxygen-containing functional groups such as carboxyl groups (-COOH) or hydroxyl groups (-OH) are introduced to the surface of the carbon nanotubes, thereby improving the dispersity and surface activity of the carbon nanotubes and being conducive to the combination of the nitrogenizing agent.

[0015] Further, in the step S1, the homogenization emulsification treatment process is at a speed of 5000-13000rpm for 10-60min.

[0016] The carboxylated carbon nanotubes are broken into short carboxylated carbon nanotubes after homogenization and emulsification treatment, and the dispersibility of the carboxylated carbon nanotubes is improved, so that the problem of entanglement and agglomeration of the carbon nanotubes is solved.

[0017] Further, in the step S1, the short carboxylated carbon nanotubes have a tube diameter of 1-10 nm and a length of 0.5-2 μm.

[0018] Further, in the step S1, the mass of the added nitrogenizing agent is 1-2 times the mass of the carbon nanotubes; and the nitrogenizing agent is selected from one or more of melamine, dicyandiamide, urea and thiourea.

[0019] The nitrogenizing agent dopes the carbon material and forms pores in the carbon material in the subsequent high-temperature heating process.

[0020] Further, in the step S2, the mass ratio of the added phenolic monomer to the added aldehyde monomer is 1:1-2; the phenolic monomer is selected from one or more of phenol, p-benzenediol, o-benzenediol and m-benzenediol; and the aldehyde monomer is selected from one of formaldehyde, trioxane, polyoxymethylene, acetaldehyde and propyl aldehyde.

[0021] Further, the alkaline solution is selected from one of an aqueous solution of NaOH, an aqueous solution of KOH, an aqueous solution of Na2CO3, an aqueous solution of NaHCO3 and ammonia water; the reaction temperature is 30-80℃; and the stirring time is 1-5 h.

[0022] Further, the alkaline solution is selected from one of an aqueous solution of NaOH, an aqueous solution of KOH, an aqueous solution of Na2CO3 and an aqueous solution of NaHCO3; and the concentration of the aqueous solution is 25-40 wt%.

[0023] Further, in the step S2, the volume of the added functionalized carbon nanotube mixture A accounts for 5-15% of the total volume of the mixture.

[0024] Further, in the step S3, the drying operation is atomization drying; the inlet temperature of the atomization drying is 110-150℃; the feeding speed is 0.2-0.5 L / h; and the D50 of the spherical porous carbon dry powder C is 6-12 μm.

[0025] The spherical structure of the porous carbon is regulated by the method of atomization drying, so as to improve the tap density and the compacted density.

[0026] Further, the solid content of the functionalized carbon nanotube-phenolic resin precursor mixture before atomization drying is adjusted to 5-30% by adding pure water.

[0027] The solid content of the functionalized carbon nanotube-phenolic resin precursor mixed solution is controlled in the range, so that the mixed solution is not too thick, and the spraying effect is affected.

[0028] Further, in the step S4, the spherical porous carbon dry powder C is heated by using a CVD rotary furnace; the rotating speed of the CVD rotary furnace is 0.2-1.5 r / min.

[0029] Further, in the step S4, a two-stage heating mode is used; the first stage heating is from room temperature to 300-600 DEG C, and the temperature is kept for 1-2 h; the second stage heating is from 800-1200 DEG C, and the temperature is kept for 1-10 h; at the end of the second stage heating, CO2 gas is introduced, and the flow rate of the CO2 gas is 0.2-2 L / min.

[0030] During the temperature keeping process of the first stage heating, the volatile components in the multi-channel high-conductivity porous carbon material fully overflow, and the carbon dioxide is used for pore forming during the temperature keeping process of the second stage heating, so that the pore forming efficiency is higher.

[0031] Further, in the step S4, the multi-channel high-conductivity porous carbon material is sieved; the mesh number of the sieve is 200-350 meshes.

[0032] The application further provides a multi-channel high-conductivity porous carbon material, which is prepared by using the preparation method as described above; has a specific surface area of 1700 m 2 / g or above; and has a resistivity of less than 0.45 Ω·cm.

[0033] The application further provides an application of the multi-channel high-conductivity porous carbon material, and the multi-channel high-conductivity spherical porous carbon as described above is applied to preparation of a lithium ion battery.

[0034] The preparation method of the multi-channel high-conductivity porous carbon material provided by the application first performs functionalization treatment on the carbon nanotube, improves the dispersion performance of the carbon nanotube, then the carbon nanotube is added into a phenolic resin polymerization reaction solution, and is uniformly mixed with the phenolic resin oligomer; the nitrogenizing agent is cracked during high-temperature treatment, pores are formed from inside to outside, pore forming and doping are simultaneously performed, the doping of the heteroatomic nitrogen further accelerates electron transfer, and the conductivity of the material is improved; the CO2 activation is performed from outside to inside to expand the pores, two-way pore forming is performed, the porosity of the material is improved, and the pore forming time is shortened; the pore structure is mainly micropores, and the porosity is more compact; the introduction of the carbon nanotube strengthens the mechanical strength of the porous carbon, and forms longitudinal and transverse intersecting channels in the porous carbon, accelerates electron transfer, and improves the conductivity. BRIEF DESCRIPTION OF DRAWINGS

[0035] Fig. 1 is a structure schematic view of the multi-channel high-conductivity porous carbon material of the embodiment of the application;

[0036] Fig. 2 is an XRD diagram of the multi-channel high-conductivity porous carbon material of the embodiment 1 in the application;

[0037] Figure 3 is a N2adsorption-desorption curve of the multi-channel high-conductivity porous carbon material of Example 1 in the present application;

[0038] Figure 4 is a BJH desorption pore size distribution graph of the multi-channel high-conductivity porous carbon material of Example 1 in the present application;

[0039] Figure 5 is a HK method micropore size distribution graph of the multi-channel high-conductivity porous carbon material of Example 1 in the present application;

[0040] Figure 6 is a charge-discharge curve of the silicon-carbon material prepared by using the multi-channel high-conductivity porous carbon material of Example 1 in the present application as a carbon substrate. DETAILED DESCRIPTION

[0041] In order to make the technical solutions of the present application clearer, the present application is further described in detail below in combination with the drawings and specific examples. EXAMPLE

[0042] Preparation of the multi-channel high-conductivity porous carbon material:

[0043] S1 Preparation of functionalized carbon nanotube mixture A: 1 g of carbon nanotubes was placed in 150 mL of mixed acid solution of concentrated sulfuric acid and concentrated nitric acid (volume ratio of concentrated sulfuric acid to concentrated nitric acid was 2:1) and stirred for 30 min, and then subjected to high-speed homogenization emulsification treatment at 12000 rpm for 20 min to obtain short carboxylated carbon nanotubes (diameter 2 nm, length 1 μm), and then 1.5 g of dicyandiamide was slowly added, and after stirring, water was washed until neutral to obtain the functionalized carbon nanotube mixture A;

[0044] S2 Preparation of functionalized carbon nanotube-phenol formaldehyde resin precursor mixture B: m-diphenol and formaldehyde were added to 30 wt% NaOH aqueous solution (NaOH mass was 5% of the mass of phenol monomer) at a mass ratio of 1:1.5, and after stirring at 60°C for 5 h, the mixture A obtained in step S1 was slowly added (volume of mixture A accounted for 10% of the total solution volume), and continuous stirring was carried out to obtain functionalized carbon nanotube-phenol formaldehyde resin oligomers, and then pure water was added to adjust the emulsion solid content to 20% to obtain the precursor mixture B;

[0045] S3 The mixture B obtained in step S2 was atomized and dried, the inlet temperature was 120°C, and the feeding speed was 0.3 L / min, and the particle size D50 of the obtained porous carbon dry powder C was controlled at 7-8 μm;

[0046] S4: Put the porous carbon powder C obtained in step S3 into a CVD rotating furnace, rotate the furnace at a speed of 0.5 r / min, first heat to 400°C, keep for 1 h, then heat to 900°C, pass CO2 gas at a flow rate of 0.2 L / min, keep for 4 h, after cooling, pass the obtained powder through a 300-mesh sieve to obtain the multi-channel high-conductivity porous carbon material.

[0047] As shown in FIG. 1, the multi-channel high-conductivity porous carbon material is in a spherical structure as a whole, the outer layer is a phenolic resin carbon layer, and the inside is a diversified tubular channel formed by carbon nanotubes. Embodiment

[0048] Preparation of the multi-channel high-conductivity porous carbon material:

[0049] S1: Preparation of functionalized carbon nanotube mixed solution A: 1 g of carbon nanotubes was stirred in a mixed acid solution of concentrated sulfuric acid and concentrated nitric acid (volume ratio of concentrated sulfuric acid to concentrated nitric acid was 2:1) for 50 min, and then subjected to high-speed homogenization emulsification treatment at 12000 rpm for 20 min to obtain short carboxylated carbon nanotubes (diameter 4 nm, length 0.8 μm), then 1.2 g of melamine was slowly added, stirred and washed with water until neutral to obtain the functionalized carbon nanotube mixed solution A;

[0050] S2: Preparation of functionalized carbon nanotube-phenolic resin precursor mixed solution B: m-diphenol and formaldehyde were added to a 28%wt% NaOH solution (the mass of NaOH was 5% of the mass of the phenol monomer) at a mass ratio of 1:1.3, stirred at 70°C for 3.5 h, then the mixed solution A obtained in step S1 was slowly added (the volume of the mixed solution A accounted for 10% of the total solution volume), and continuous stirring was performed to obtain functionalized carbon nanotube-phenolic resin oligomers, then pure water was added to adjust the solid content of the emulsion to 15% to obtain the precursor mixed solution B;

[0051] S3: The mixed solution B obtained in step S2 was atomized and dried, the inlet temperature was 130°C, and the feeding speed was 0.5 L / min, and the particle size D50 of the obtained porous carbon powder C was controlled to be 7-8 μm;

[0052] S4: Put the porous carbon powder C obtained in step S3 into a CVD rotating furnace, rotate the furnace at a speed of 0.5 r / min, first heat to 400°C, keep for 1 h, then heat to 900°C, pass CO2 gas at a flow rate of 0.2 L / min, keep for 4 h, after cooling, pass the obtained powder through a 300-mesh sieve to obtain the multi-channel high-conductivity porous carbon material. Embodiment

[0053] Preparation of the multi-channel high-conductivity porous carbon material:

[0054] Preparation of functionalized carbon nanotube mixture A: 1 g of carbon nanotubes was stirred in a mixed acid solution of concentrated sulfuric acid and concentrated nitric acid (volume ratio of concentrated sulfuric acid to concentrated nitric acid was 2:1) for 50 min, and then subjected to high-speed homogenization emulsification at 10000 rpm for 40 min to obtain short carboxylated carbon nanotubes (diameter 4 nm, length 1 μm), and then 1.5 g of melamine was slowly added, and after stirring, water was washed until neutral to obtain functionalized carbon nanotube mixture A;

[0055] Preparation of functionalized carbon nanotube-phenolic resin precursor mixture B: m-diphenol and trioxymethylene were added to a 35 wt% KOH solution (KOH mass was 8% of the mass of the phenol monomer) at a mass ratio of 1:1.6, stirred at 70°C for 3 h, and then the mixture A obtained in step S1 was slowly added (12% of the total solution volume), and continuous stirring was performed to obtain functionalized carbon nanotube-phenolic resin oligomers, and then pure water was added to adjust the emulsion solid content to 20% to obtain the precursor mixture B;

[0056] S3: The mixture B obtained in step S2 was atomized and dried, with an inlet temperature of 130°C and a feeding speed of 0.2 L / min, and the particle size D50 of the obtained porous carbon dry powder C was controlled at 8-9 μm;

[0057] S4: The porous carbon dry powder C obtained in step S3 was placed in a CVD rotary furnace, the rotary furnace was rotated at a speed of 0.3 r / min, first heated to 500°C, kept for 1 h, then heated to 950°C, and CO2 gas was passed at a flow rate of 0.2 L / min, kept for 3 h, and after cooling, the dry powder was passed through a 300 mesh sieve to obtain a multi-channel high-conductivity porous carbon material. Example

[0058] Preparation of a multi-channel high-conductivity porous carbon material:

[0059] Preparation of functionalized carbon nanotube mixture A: 1 g of carbon nanotubes was stirred in a mixed acid solution of concentrated sulfuric acid and concentrated nitric acid (volume ratio of concentrated sulfuric acid to concentrated nitric acid was 2:1) for 50 min, and then subjected to high-speed homogenization emulsification at 10000 rpm for 40 min to obtain short carboxylated carbon nanotubes (diameter 4 nm, length 1 μm), and then 1.5 g of melamine was slowly added, and after stirring, water was washed until neutral to obtain functionalized carbon nanotube mixture A;

[0060] Preparation of functionalized carbon nanotube-phenolic resin precursor mixture B: m-diphenol and trioxymethylene were added to a 35 wt% KOH solution (KOH mass was 8% of the mass of the phenol monomer) at a mass ratio of 1:1.6, stirred at 70°C for 3 h, and then the mixture A obtained in step S1 was slowly added (12% of the total solution volume), and continuous stirring was performed to obtain functionalized carbon nanotube-phenolic resin oligomers, and then pure water was added to adjust the emulsion solid content to 20% to obtain the precursor mixture B;

[0061] S3 centrifuging, washing and drying the mixed solution B obtained in step S2 to obtain a porous carbon dry powder C, and controlling the particle size D50 of the porous carbon dry powder C to be 7-8 μm;

[0062] S4 placing the porous carbon dry powder C obtained in step S3 in a CVD rotary furnace, rotating the furnace at a speed of 0.5 r / min, first heating to 400 ℃, holding for 1 h, then heating to 900 ℃, passing CO2 gas at a flow rate of 0.2 L / min, holding for 4 h, and after cooling, passing the dry powder through a 300-mesh screen to obtain a multi-channel high-conductivity porous carbon material.

[0063] 1) Preparation of a phenolic resin precursor mixture: adding m-diphenol and formaldehyde at a mass ratio of 1:1.5 to a 30 wt% NaOH solution (the mass of NaOH is 5% of the mass of the phenol monomer), stirring at 60 ℃ for 5 h, then slowly adding 1.5 g of dicyandiamide, continuing to stir, obtaining a phenolic resin oligomer, and then adding pure water to adjust the solid content of the emulsion to 20%, obtaining a phenolic resin precursor mixture;

[0064] 2) atomizing and drying the phenolic resin precursor mixture obtained in step 1), with an inlet temperature of 120 ℃ and a feeding speed of 0.3 L / min, and controlling the particle size D50 of the obtained dry powder to be 7-8 μm;

[0065] 3) placing the dry powder obtained in step 2) in a CVD rotary furnace, rotating the furnace at a speed of 0.5 r / min, first heating to 400 ℃, holding for 1 h, then heating to 900 ℃, passing CO2 gas at a flow rate of 0.2 L / min, holding for 4 h, and after cooling, passing the dry powder through a 300-mesh screen to obtain a porous carbon material.

[0066] The porous carbon materials obtained in Examples 1-4 and Comparative Example 1 were subjected to tap density testing, powder compaction density, powder resistance, nitrogen adsorption / desorption isotherm testing, etc. The results obtained are shown in Table 1.

[0067] Table 1 Performance test results of the porous carbon obtained in Examples 1-4 and Comparative Example 1

[0068] Serial number Number Tap density g / cm 3 Compaction g / cm 3 Resistivity Ω·cm Specific surface m 2 / g1 Example 1 0.56 0.94 0.14 1967 2 Example 2 0.56 0.96 0.11 1896 3 Example 3 0.58 0.99 0.18 1835 4 Example 4 0.44 0.83 0.45 1792 5 Comparative Example 1 0.60 1.01 1.02 1478

[0069] The examples 1-4 have good electrical conductivity, larger specific surface area compared with the comparative example 1. The multi-channel high-conductive porous carbon material obtained by spray drying has higher tap density and compacted density, and more excellent electrical conductivity compared with the example 4.

[0070] The multi-channel high-conductive porous carbon material obtained from the example 1 was subjected to XRD test, nitrogen adsorption / desorption isotherm test. The obtained results are shown in Figures 2-5.

[0071] As shown in Figure 2, the XRD pattern of the example 1 indicates that the obtained multi-channel high-conductive porous carbon material mainly presents amorphous carbon structure.

[0072] As shown in Figure 3, the nitrogen adsorption / desorption curve of the example 1 indicates that the obtained multi-channel high-conductive porous carbon material is type I adsorption isotherm, and the pore structure is mainly microporous structure, and the pore is more compact.

[0073] As shown in Figure 4, the BJH desorption curve of the example 1, the average pore size is 1.7 nm.

[0074] As shown in Figure 5, the HK method micropore size distribution of the example 1 is 0.7-1 nm, and the pore size size distribution is more uniform.

[0075] The multi-channel high-conductive porous carbon material obtained from the example 1 was subjected to gas phase deposition of silicon carbon, and the mass of the deposited silicon was 50-52% of the mass of the porous carbon. The obtained silicon-carbon material was prepared into a model 2032 button cell for evaluation. The specific scheme is that the prepared silicon-carbon material, conductive agent VGCF, and binder LA136 were mixed in a ratio of 75:5:10:10, water was used as the solvent, the slurry was coated on a copper foil, the counter electrode was a lithium sheet, the separator was a Celgard 2400 microporous polypropylene film, the charge / discharge cutoff voltage was 0.005-1.5 V, the discharge rate was first discharged to 0.005 V at 0.1 C, and then discharged to 0.005 V at 0.02 C, so as to fully discharge, and the charge rate was 0.1 C charged to 1.5 V.

[0076] The results are shown in Figure 6. The multi-channel high-conductive porous carbon obtained from the example 1 was used as the substrate for silicon deposition, and the obtained silicon-carbon material had a reversible capacity of 2215 mAh / g, a first charge / discharge efficiency of 90.5%, and good electrical performance.

[0077] The above examples only express several embodiments of the present application, and the description is more specific and detailed, but it cannot be understood as a limitation on the scope of the patent of the present application. It should be noted that for ordinary skilled persons in the art, without departing from the concept of the present application, a number of modifications and improvements can be made, which all belong to the protection scope of the present application. Therefore, the protection scope of the patent of the present application should be subject to the appended claims.

Claims

1. A method for preparing a multi-channel highly conductive porous carbon material, characterized by, The method comprises the following steps: S1: acidizing carbon nanotubes to obtain carboxylated carbon nanotubes, emulsifying the carboxylated carbon nanotubes to obtain short carboxylated carbon nanotubes, mixing the short carboxylated carbon nanotubes with a nitrogenizing agent, and washing until neutral to obtain a functionalized carbon nanotube mixture A; S2: mixing a phenolic monomer and an aldehyde monomer with an alkaline solution to polymerize into a phenolic aldehyde resin oligomer, and mixing the phenolic aldehyde resin oligomer with the functionalized carbon nanotube mixture A to obtain a functionalized carbon nanotube-phenolic aldehyde resin precursor mixture B; S3: drying the functionalized carbon nanotube-phenolic aldehyde resin precursor mixture B to obtain a porous carbon dry powder C; S4: heating the porous carbon dry powder C to 800-1200 DEG C, and activating the porous carbon dry powder C by introducing carbon dioxide to obtain a multi-channel high-conductivity porous carbon material.

2. The method of claim 1, wherein the porous carbon material is prepared by the steps of: mixing a carbon precursor and a polymer to form a mixture; and heating the mixture to form the porous carbon material. In the step S1, the homogenizing emulsification process is carried out at a speed of 5000-13000 rpm for 10-60 min.

3. The method of claim 1, wherein the porous carbon material is prepared by the steps of: mixing a carbon precursor and a polymer to form a mixture; heating the mixture to form a carbonized mixture; and heating the carbonized mixture to form the porous carbon material. In the step S1, the short carboxylated carbon nanotubes have a tube diameter of 1-10 nm and a length of 0.5-2 μm.

4. The method of claim 1, wherein the porous carbon material is a multi-channel, high-conductivity porous carbon material. In the step S1, the mass of the nitrogenizing agent added is 1-2 times the mass of the carbon nanotubes; the nitrogenizing agent is selected from one or more of melamine, dicyandiamide, urea, and thiourea.

5. The method of claim 1, wherein the porous carbon material is a multi-channel, high-conductivity porous carbon material. In the step S2, the mass ratio of the phenolic monomer to the aldehyde monomer is 1:1-2; the phenolic monomer is selected from one or more of phenol, p-benzenediol, o-benzenediol, and m-benzenediol; and the aldehyde monomer is selected from one of formaldehyde, trioxane, polyoxymethylene, acetaldehyde, and propyl aldehyde.

6. The method of claim 1, wherein the multi-channel highly conductive porous carbon material is prepared by the steps of: In the step S2, the volume of the functionalized carbon nanotube mixture A added accounts for 5-15% of the total volume of the mixture.

7. The method of claim 4, wherein the porous carbon material is a multi-channel, high-conductivity porous carbon material. In the step S3, the drying operation is atomization drying; the inlet temperature of the atomization drying is 110-150 DEG C, and the feeding speed is 0.2-0.5 L / h; and the D50 of the spherical porous carbon dry powder C is 6-12 μm.

8. The method of claim 1, wherein the multi-channel highly conductive porous carbon material is prepared by the steps of: In the step S4, a two-stage heating method is adopted; the first stage is heating from room temperature to 300-600 DEG C and holding for 1-2 h; the second stage is heating to 800-1200 DEG C and holding for 1-10 h; and carbon dioxide gas is introduced at the end of the second stage, and the flow rate of the carbon dioxide gas is 0.2-2 L / min.

9. A multi-channel highly conductive porous carbon material, characterized by, obtained by the production method as claimed in any one of claims 1 to 8; having a specific surface area of 1700 m 2 / g or more; and an electrical resistivity of less than 0.45 Ω-cm.

10. Use of a multi-channel highly conductive porous carbon material, characterized in that, The multi-channel high-conductivity porous carbon material of claim 9 is applied to prepare a lithium ion battery.

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