CN112736242A - High-performance carbon negative electrode PTCDA hard carbon material and preparation method thereof - Google Patents
High-performance carbon negative electrode PTCDA hard carbon material and preparation method thereof Download PDFInfo
- Publication number
- CN112736242A CN112736242A CN202110045800.5A CN202110045800A CN112736242A CN 112736242 A CN112736242 A CN 112736242A CN 202110045800 A CN202110045800 A CN 202110045800A CN 112736242 A CN112736242 A CN 112736242A
- Authority
- CN
- China
- Prior art keywords
- ptcda
- carbon material
- negative electrode
- preparation
- tetracarboxylic dianhydride
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Images
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
- H01M4/36—Selection of substances as active materials, active masses, active liquids
- H01M4/58—Selection of substances as active materials, active masses, active liquids of inorganic compounds other than oxides or hydroxides, e.g. sulfides, selenides, tellurides, halogenides or LiCoFy; of polyanionic structures, e.g. phosphates, silicates or borates
- H01M4/583—Carbonaceous material, e.g. graphite-intercalation compounds or CFx
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B32/00—Carbon; Compounds thereof
- C01B32/05—Preparation or purification of carbon not covered by groups C01B32/15, C01B32/20, C01B32/25, C01B32/30
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/05—Accumulators with non-aqueous electrolyte
- H01M10/052—Li-accumulators
- H01M10/0525—Rocking-chair batteries, i.e. batteries with lithium insertion or intercalation in both electrodes; Lithium-ion batteries
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
- H01M2004/026—Electrodes composed of, or comprising, active material characterised by the polarity
- H01M2004/027—Negative electrodes
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
Abstract
The invention discloses a high-performance carbon cathode PTCDA hard carbon material and a preparation method thereof, wherein a product can be prepared by sintering perylene tetracarboxylic dianhydride in a solid phase, namely, the perylene tetracarboxylic dianhydride negative electrode material is sintered at high temperature under inert gas to obtain a blocky carbon material, and the perylene tetracarboxylic dianhydride is directly sintered into the carbon material, so that the used raw material is simple, graphite and other doped materials are not needed, the industrial production cost is low, the raw material is easy to obtain, and the preparation method has the advantages of simplicity, environmental protection, no toxicity and the like; the carbon material is obtained by directly sintering perylene tetracarboxylic dianhydride, the sintering temperature in the preparation process is low, the preparation process is easier to realize and control, industrial production is easier, and the obtained PTCDA organic carbon is used as a negative electrode material of a lithium ion battery, shows good cycle performance and capacity property, and has better cycle stability compared with the traditional graphite.
Description
Technical Field
The invention belongs to the functional material technology, and relates to a high-performance carbon negative electrode PTCDA hard carbon material and a preparation method thereof.
Background
The lithium ion battery has good energy storage characteristics and is widely applied to the fields of mobile communication, information technology, consumer electronics, mobile automobiles and the like. With the progress and development of human society, the requirements of higher capacity, better rate capability and longer service life are provided for the advanced lithium ion battery. In each component of a lithium ion battery, an electrode material is a key factor that restricts the performance of the lithium ion battery. The negative electrode material is used as an important component of the lithium ion battery, and has important influence on the electrochemical performance of the lithium ion battery. In the anode material of the lithium ion battery, the carbon material has the advantages of low electrode potential, high cycle efficiency, long cycle life, good safety performance and the like, and is the preferred anode material of the lithium ion battery. At present, graphite is a common carbon anode material, has a good layered structure, is suitable for lithium ion intercalation and deintercalation, has the advantages of high conductivity and large reversible specific capacity, and becomes a widely used traditional commercial anode material.
However, the conventional graphite anode material still has some disadvantages, which severely limit its application. Firstly, the theoretical capacity of the graphite negative electrode is only 372mAh g-1The requirements of high-performance lithium ion batteries can not be met; secondly, the stability of the laminated structure is poor, and collapse is easy to occur after a long-time charge-discharge period, so that the specific capacity is seriously reduced, and the energy storage life is shortened; third, during the first charge and discharge, the electrolyte decomposes to produce a large irreversible capacity. These defects largely limit the application of graphite negative electrode materials in high-performance lithium ion batteries. Therefore, a high performance, high capacity, stable layered structure, cyclic life is soughtThe long-lived new carbon anode materials have become the focus of many studies. However, for the layered graphite negative electrode material, in addition to the above disadvantages, the interlayer spacing is small, so that lithium ions can only be inserted from the end face of the material, which will increase the diffusion resistance of lithium ions, and finally, the rate capability of the layered graphite negative electrode is poor, which limits the application of the layered graphite negative electrode in a high-power battery. Therefore, improving the capacity and rate performance of carbon anode materials is an important issue to be solved at present.
Disclosure of Invention
Aiming at the defects in the prior art, the invention aims to provide a high-performance carbon negative electrode PTCDA hard carbon material and a preparation method thereof.
In order to achieve the purpose, the invention adopts the technical scheme that:
a preparation method of a high-performance carbon negative electrode PTCDA hard carbon material specifically comprises the following steps:
step 1, dissolving perylene tetracarboxylic dianhydride powder in a porcelain boat by using sufficient NMP, covering a porcelain boat cover, and drying in an oven at 100 ℃ for 24-48 h;
step 2, heating to 530 ℃ at room temperature at the rate of 3 ℃/min, and preserving heat for 2 hours;
and 3, heating to 1000-1150 ℃ at the speed of 2 ℃/min, finally preserving heat for 2h, and cooling to room temperature to obtain the carbon cathode PTCDA hard carbon material.
Further, the relative molecular mass of the perylene tetracarboxylic dianhydride powder in the step 1 is 838.679W.
Further, in the step 3, heating to 1000 ℃, 1050 ℃, 1100 ℃ or 1150 ℃ at the speed of 2 ℃/min, preserving heat for 2h, and cooling to room temperature to obtain the carbon cathode PTCDA hard carbon material.
Further, the perylene tetracarboxylic dianhydride hard carbon material obtained in the step 3 is pre-ground and sieved by a 300-mesh sieve to obtain the carbon cathode PTCDA hard carbon material.
The invention has the following beneficial effects:
according to the invention, the product can be prepared by sintering the perylene tetracarboxylic dianhydride in a solid phase, namely, the perylene tetracarboxylic dianhydride negative electrode material is sintered at high temperature to obtain the massive carbon material, and the perylene tetracarboxylic dianhydride is directly sintered to form the carbon material, so that the raw material is simple, other doping materials such as graphite and the like are not needed, the industrial production cost is low, the raw material is easy to obtain, and the preparation method has the advantages of simplicity, environmental protection, no toxicity and the like; the carbon material is obtained by sintering perylene tetracarboxylic dianhydride, and the preparation process has low sintering temperature, is easier to realize, is simple to control and is easier for industrial production.
The obtained perylene tetracarboxylic dianhydride is used as a negative electrode material of a lithium ion battery, and the first charging specific capacity of the perylene tetracarboxylic dianhydride is 334.9mAh g respectively through tests-1，335.5mAh g-1，325.3mAh g-1The first coulombic efficiencies were 98.95%, 95.85% and 96.46%, respectively. Compared with graphite, the PTCDA organic carbon material has the advantages of larger specific surface area, total pore volume and average pore diameter and wide pore size distribution range, which is more beneficial to intercalation of lithium ions; the discharge specific capacity of the PTCDA carbon material sintered at 1100 ℃ is not greatly different from that of graphite, but the initial specific capacity of voltage reduction is higher, namely the high-voltage discharge capacity range is narrower, which indicates that the PTCDA carbon material has poorer high-voltage discharge performance and faster capacity reduction under high voltage; li consumed for SEI film formation+More or the surface of the material is adsorbed with impurities to react part of Li+The irreversible capacity of PTCDA carbon material is higher.
The PTCDA is decomposed in a high-temperature nitrogen atmosphere to obtain the PTCDA organic carbon which is used as a negative electrode material of a lithium ion battery, shows good cycle performance and capacity property and has better cycle stability compared with the traditional graphite.
Drawings
FIG. 1 is a graph showing the impedance properties of graphite and materials prepared in examples 1 to 4 of the present invention
FIG. 2 is a graph of 1C cycle performance of graphite and materials prepared in examples 1-4 of the present invention
FIG. 3 is a graph showing the rate discharge curves of graphite and materials prepared in examples 1 to 4 of the present invention
FIG. 4 is a scanning electron micrograph of materials of examples 1 to 4 of the present invention
FIG. 5 is a transmission electron microscope photograph of the materials of examples 1-4 of the present invention
Detailed Description
The present invention will be described in further detail with reference to the following examples, which are not intended to limit the invention thereto.
Example 1
Step 1, dissolving about 20g of perylene tetracarboxylic dianhydride (added in multiple times) in a porcelain boat by using enough NMP, covering the porcelain boat with a cover, and drying the porcelain boat in an oven at 100 ℃ for 24-48 h.
And 2, heating to 530 ℃ at the room temperature of 30 ℃ at the speed of 3 ℃/min for 167min, and preserving heat for 2 h.
Step 3, carbonizing: and then reaching 1000 ℃ at the speed of 2 ℃/min, finally preserving the heat for 2h, and cooling to room temperature.
And 4, grinding the obtained perylene tetracarboxylic dianhydride negative electrode material, and sieving the ground perylene tetracarboxylic dianhydride negative electrode material with a 300-mesh sieve to obtain the extremely fine perylene tetracarboxylic dianhydride negative electrode material.
Example 2
Step 1, dissolving about 20g of perylene tetracarboxylic dianhydride (added in multiple times) in a porcelain boat by using enough NMP, covering the porcelain boat with a cover, and drying the porcelain boat in an oven at 100 ℃ for 24-48 h.
And 2, heating to 530 ℃ at the room temperature of 30 ℃ at the speed of 3 ℃/min for 167min, and preserving heat for 2 h.
Step 3, carbonizing: and then 1050 ℃ is reached at the speed of 2 ℃/min, and finally the temperature is kept for 2h, and the perylene tetracarboxylic dianhydride negative electrode material is cooled to room temperature.
And 4, grinding the obtained perylene tetracarboxylic dianhydride negative electrode material, and sieving the ground perylene tetracarboxylic dianhydride negative electrode material with a 300-mesh sieve to obtain the superfine perylene tetracarboxylic dianhydride negative electrode material.
Example 3
Step 1, dissolving about 20g of perylene tetracarboxylic dianhydride (added in multiple times) in a porcelain boat by using enough NMP, covering the porcelain boat with a cover, and drying the porcelain boat in an oven at 100 ℃ for 24-48 h.
And 2, heating to 530 ℃ at the room temperature of 30 ℃ at the speed of 3 ℃/min for 167min, and preserving heat for 2 h.
Step 3, carbonizing: and then reaching 1100 ℃ at the speed of 2 ℃/min, finally preserving the heat for 2h, and cooling to room temperature.
And 4, grinding the obtained perylene tetracarboxylic dianhydride negative electrode material, and sieving the ground perylene tetracarboxylic dianhydride negative electrode material with a 300-mesh sieve to obtain the extremely fine perylene tetracarboxylic dianhydride negative electrode material.
Example 4
Step 1, dissolving about 20g of perylene tetracarboxylic dianhydride (added in multiple times) in a porcelain boat by using enough NMP, covering the porcelain boat with a cover, and drying the porcelain boat in an oven at 100 ℃ for 24-48 h.
And 2, heating to 530 ℃ at the room temperature of 30 ℃ at the speed of 3 ℃/min for 167min, and preserving heat for 2 h.
Step 3, carbonizing: then the temperature reaches 1150 ℃ at the speed of 2 ℃/min, finally the temperature is kept for 2h, and the perylene tetracarboxylic dianhydride negative electrode material is cooled to room temperature.
And 4, grinding the obtained perylene tetracarboxylic dianhydride negative electrode material, and sieving the ground perylene tetracarboxylic dianhydride negative electrode material with a 300-mesh sieve to obtain the extremely fine perylene tetracarboxylic dianhydride negative electrode material.
As shown in FIG. 1, the impedance diagram of the lithium ion negative electrode material prepared by the invention shows EIS spectra of a half cell composed of PTCDA-1000, PTCDA-1050, PTCDA-1100 and PTCDA-1150 four kinds of hard carbon, graphite and lithium metal. Wherein, the small semi-circle diameter of the medium-high frequency region of PTCDA-1100 is larger than and close to graphite; the small semi-circle diameter of the middle-high frequency region of PTCDA-1150 is smaller than that of PTCDA-1050 and larger than that of PTCDA-1100. The diameter of the small semicircle in the middle-high frequency region of the PTCDA-1000 is the largest, but the diameters of the small semicircles in the middle-high frequency region of the carbonized PTCDA sample at four temperatures are all larger than those of graphite, and the approximate straight line in the low frequency region of the carbonized PTCDA sample basically keeps the same slope, but the slopes are all smaller than the approximate straight line in the low frequency region of the graphite sample.
As shown in FIG. 2, it can be clearly seen that the initial capacity of the PTCDA hard carbon electrode is much higher than that of the graphite electrode at the current rate of 3C, and the PTCDA hard carbon electrode also shows more stable cycling performance than the graphite electrode, and the 3C charging capacity is 225 mAh g and 235mAh g-1The method is suitable for PTCDA hard carbon electrodes and graphite electrodes. The capacity retention rates of the PTCDA hard carbon electrode and the graphite electrode are respectively 90% and 79% after 300 cycles, and the 3C cycle is basically maintained at 200mAh g-1Above, far higher than stone100mAh g of ink-1Show the superior rate capability of the PTCDA hard carbon material.
As shown in FIG. 3, the anode material prepared by the invention shows the specific charge capacities of the PTCDA-1000, PTCDA1050, PTCDA-1100 and PTCDA-1150 hard carbon graphite/lithium half-batteries at different rates. As can be seen from FIG. 3, the specific charge capacities of the four hard carbons PTCDA-1000, PTCDA1050, PTCDA-1100 and PTCDA-1150 under different multiplying rates are all larger than that of the graphite/lithium half-cell, and the specific charge capacities of the PTCDA-1100 with the highest multiplying rate performance are 324.14mAh g respectively, namely the specific charge capacities of 0.2C, 0.5C.1C.3C, 5C and 0.2C-1、285.41mAh g-1、250.16mAh g-1、199.16mAh g-1、170.75mAh g-1、329.14mAh g-1And the specific charging capacity of the graphite/lithium half-electricity is 333.42mAh g respectively-1、241.47mAh g-1、171.16mAh g-1、96.07mAh g-1、64.29mAh g-1、306.34mAh g-1And under the charge and discharge of each multiplying power, the specific charge capacity of the PTCDA-1100 is larger than that of graphite.
As shown in FIG. 4, the scanning electron microscope pictures of the lithium ion negative electrode material prepared by the invention show SEM images of four hard carbons of the raw materials (a, b), PTCDA-1000(c, d), PTCDA-1050(e, f), PTCDA-1100(g, h) and PTCDA-1150(i, j) and graphite (k, l). As can be seen from fig. 4 at different magnifications, the PTCDA hard carbon material is composed of a large number of irregularly shaped particles, and as the carbonization temperature of PTCDA increases, the diameter of the particles gradually increases and the degree of pore breakage increases, wherein the particle size of PTCDA-1100 hard carbon particles is significantly more uniform than other temperatures; overall, the material gradually "crumbles" and this change is caused by high temperature carbonization and mechanical grinding. The blocky microstructure has a plurality of microscopic pores and a plurality of active sites, and is more beneficial to the intercalation and deintercalation of lithium ions compared with graphite.
As shown in fig. 5, transmission electron microscope pictures of the lithium ion negative electrode material prepared by the invention show images of four hard carbons, namely graphite (a, f), PTCDA-1000(b, g), PTCDA-1050(c, h), PTCDA-1100(d, i) and PTCDA-1150(e, j), wherein the lattice spacing of graphite is 0.1747nm, the lattice is very orderly and orderly, PTCDA is amorphous, the lattice spacing is totally characterized by short-range order and long-range disorder, and the lattice spacing is 0.3202nm, which is obviously larger than that of graphite, so that the lithium ion deintercalation and intercalation in the charging and discharging processes of the battery are facilitated.
The method for testing the half cell comprises the following steps: and (2) uniformly mixing 85% of a negative electrode sample, N-methyl pyrrolidone containing 5% of polyvinylidene fluoride and 10% of conductive carbon black, coating the mixture on a copper foil, weighing the coated pole piece stamped sheet, and putting the stamped sheet into a vacuum drying oven at the temperature of 100 ℃ for vacuum drying for 12 hours for later use. Half cells were assembled in a German Braun glove box filled with argon, the electrolyte was 1M, LiPF6+ EC: DEC: DMC was 1: 1 (volume ratio), a metallic lithium sheet was used as a counter electrode, electrochemical performance tests were performed on an American ArbinBT2000 type cell tester, the charge-discharge voltage range was 0.005 to 1.0V, the charge-discharge rate was 0.2C, and high-rate cycle tests were performed at the same time, and the cycle performance of the perylene tetracarboxylic dianhydride hard carbon material prepared in examples 1 to 4 was shown in Table 1.
TABLE 1
The present invention is described in detail with reference to the above embodiments, and those skilled in the art will understand that: modifications and equivalents may be made to the embodiments of the invention without departing from the spirit and scope of the invention, which is to be covered by the claims.
Claims (5)
1. A preparation method of a high-performance carbon negative electrode PTCDA hard carbon material is characterized by comprising the following steps: the method specifically comprises the following steps:
step 1, dissolving perylene tetracarboxylic dianhydride powder in a porcelain boat by using sufficient NMP, covering a porcelain boat cover, and drying in an oven at 100 ℃ for 24-48 h;
step 2, heating to 530 ℃ at room temperature at the rate of 3 ℃/min, and preserving heat for 2 hours;
and 3, heating to 1000-1150 ℃ at the speed of 2 ℃/min, finally preserving heat for 2h, and cooling to room temperature to obtain the carbon cathode PTCDA hard carbon material.
2. The preparation method of the high-performance carbon negative electrode PTCDA hard carbon material as claimed in claim 1, wherein the preparation method comprises the following steps: the relative molecular mass of the perylene tetracarboxylic dianhydride powder in the step 1 is 838.679W.
3. The preparation method of the high-performance carbon negative electrode PTCDA hard carbon material as claimed in claim 1, wherein the preparation method comprises the following steps: and in the step 3, heating to 1000 ℃, 1050 ℃, 1100 ℃ or 1150 ℃ at the speed of 2 ℃/min, preserving the heat for 2h, and cooling to room temperature to obtain the carbon cathode PTCDA hard carbon material.
4. The preparation method of the high-performance carbon negative electrode PTCDA hard carbon material as claimed in claim 1, wherein the preparation method comprises the following steps: and (3) pre-grinding the perylene tetracarboxylic dianhydride hard carbon material obtained in the step (3), and sieving the perylenetetracarboxylic dianhydride hard carbon material with a 300-mesh sieve to obtain the carbon cathode PTCDA hard carbon material.
5. A high performance carbon negative electrode PTCDA hard carbon material prepared according to the method of claims 1-4.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110045800.5A CN112736242A (en) | 2021-01-14 | 2021-01-14 | High-performance carbon negative electrode PTCDA hard carbon material and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110045800.5A CN112736242A (en) | 2021-01-14 | 2021-01-14 | High-performance carbon negative electrode PTCDA hard carbon material and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN112736242A true CN112736242A (en) | 2021-04-30 |
Family
ID=75592865
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202110045800.5A Pending CN112736242A (en) | 2021-01-14 | 2021-01-14 | High-performance carbon negative electrode PTCDA hard carbon material and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112736242A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113415799A (en) * | 2021-06-30 | 2021-09-21 | 北京化工大学 | PTCDA modified resin-based carbon material and preparation method and application thereof |
| CN114639809A (en) * | 2022-03-18 | 2022-06-17 | 上海电力大学 | Composite hard carbon negative electrode material, preparation method and application |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108242543A (en) * | 2016-12-26 | 2018-07-03 | 福建新峰二维材料科技有限公司 | A kind of soft carbon makees the preparation method of the sodium Dual-ion cell of negative material |
| CN109449440A (en) * | 2018-10-31 | 2019-03-08 | 武汉理工大学 | Ultra-thin soft carbon nanometer sheet of micropore and its preparation method and application |
| US20190127225A1 (en) * | 2017-10-26 | 2019-05-02 | Soochow University | Carbon nitride modified with perylenetetracarboxylic dianhydride / graphene oxide aerogel composite material, preparation method and application thereof |
-
2021
- 2021-01-14 CN CN202110045800.5A patent/CN112736242A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108242543A (en) * | 2016-12-26 | 2018-07-03 | 福建新峰二维材料科技有限公司 | A kind of soft carbon makees the preparation method of the sodium Dual-ion cell of negative material |
| US20190127225A1 (en) * | 2017-10-26 | 2019-05-02 | Soochow University | Carbon nitride modified with perylenetetracarboxylic dianhydride / graphene oxide aerogel composite material, preparation method and application thereof |
| CN109449440A (en) * | 2018-10-31 | 2019-03-08 | 武汉理工大学 | Ultra-thin soft carbon nanometer sheet of micropore and its preparation method and application |
Non-Patent Citations (2)
| Title |
|---|
| FEI-BIAO CHEN等: ""Modified disordered carbon prepared from 3,4,9,10-perylenetetracarboxylic dianhydride as an anode material for Li-ion batteries"", 《INTERNATIONAL JOURNAL OF MINERALS, METALLURGY AND MATERIALS》 * |
| 肖泽恩: ""锂离子电池铜箔集流体超声喷化与有机碳表面改性技术研究"", 《中国优秀博硕士学位论文全文数据库(硕士) 工程科技Ⅱ辑》 * |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113415799A (en) * | 2021-06-30 | 2021-09-21 | 北京化工大学 | PTCDA modified resin-based carbon material and preparation method and application thereof |
| CN114639809A (en) * | 2022-03-18 | 2022-06-17 | 上海电力大学 | Composite hard carbon negative electrode material, preparation method and application |
| CN114639809B (en) * | 2022-03-18 | 2023-10-10 | 上海电力大学 | Composite hard carbon negative electrode material, preparation method and application |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN107946576B (en) | High-rate graphite negative electrode material, preparation method thereof and lithium ion battery | |
| JP7209089B2 (en) | Negative electrode active material for lithium secondary battery, manufacturing method thereof, and lithium secondary battery including the same | |
| KR20220092556A (en) | Anode active material for battery and manufacturing method thereof, battery negative electrode, battery | |
| CN111146416B (en) | Nitrogen-doped silicon-based material, preparation method thereof and application thereof in battery | |
| CN110104677B (en) | Composite lithium titanate material and preparation method and application thereof | |
| KR100758383B1 (en) | Sulfur electrode coated with carbon for using in the li/s secondary battery | |
| CN107180958B (en) | Anthracite/silicon monoxide/amorphous carbon negative electrode material and preparation method thereof | |
| CN111244414A (en) | Method for preparing silicon-carbon negative electrode material by magnesiothermic reduction | |
| CN113651304A (en) | Organic carbon-coated lithium iron phosphate cathode material and preparation method thereof | |
| CN111017903A (en) | High-performance carbon anode PAN hard carbon material and preparation method thereof | |
| KR20230137807A (en) | Method for preparing carbon-coated lithium iron phosphate material from ferrous phosphate | |
| CN112736242A (en) | High-performance carbon negative electrode PTCDA hard carbon material and preparation method thereof | |
| CN113224292A (en) | High-performance lithium ion battery polyacrylonitrile carbon fiber negative electrode material and preparation method thereof | |
| CN110577204A (en) | preparation of N/O co-doped hard carbon material and application of N/O co-doped hard carbon material in potassium ion battery | |
| CN106684367B (en) | Low-temperature petroleum coke negative electrode material coated with nitrogen-containing polymer pyrolytic carbon and preparation method thereof | |
| CN112768657A (en) | High-performance carbon negative electrode PTCDA hard carbon coated graphite material and preparation method thereof | |
| CN111072012B (en) | Microcrystalline graphite graphene-doped negative electrode material of lithium ion battery and preparation method thereof | |
| CN111755665B (en) | Lithium ion battery negative electrode material, battery negative electrode and application thereof | |
| CN115566170B (en) | Preparation method of high-energy-density quick-charging lithium ion battery anode material | |
| CN114122392B (en) | High-capacity quick-charging graphite composite material and preparation method thereof | |
| CN115275166A (en) | Long-life graphite composite material and preparation method thereof | |
| CN114520328B (en) | Lithium ion battery negative electrode material, preparation method thereof, negative electrode and battery | |
| CN114695851B (en) | Composite anode material, anode, battery and preparation method thereof | |
| CN113659117A (en) | Preparation method of carbon-doped sandwich-structure lithium ion battery cathode material | |
| Cech et al. | Synthesis of LiFePO4/C composite cathode for lithium-ion batteries |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20210430 |
|
| RJ01 | Rejection of invention patent application after publication |