WO2019161644A1 - 一种复合材料及其制备方法 - Google Patents

一种复合材料及其制备方法 Download PDF

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WO2019161644A1
WO2019161644A1 PCT/CN2018/101824 CN2018101824W WO2019161644A1 WO 2019161644 A1 WO2019161644 A1 WO 2019161644A1 CN 2018101824 W CN2018101824 W CN 2018101824W WO 2019161644 A1 WO2019161644 A1 WO 2019161644A1
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silicon
based material
layers
carbon nanotubes
layered
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PCT/CN2018/101824
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English (en)
French (fr)
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苏航
李阳兴
于哲勋
王平华
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华为技术有限公司
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Priority to EP18907452.9A priority Critical patent/EP3748744A4/en
Publication of WO2019161644A1 publication Critical patent/WO2019161644A1/zh
Priority to US16/998,256 priority patent/US20200381715A1/en

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B82—NANOTECHNOLOGY
    • B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
    • B82Y30/00—Nanotechnology for materials or surface science, e.g. nanocomposites
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B82—NANOTECHNOLOGY
    • B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
    • B82Y40/00—Manufacture or treatment of nanostructures
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/26—Deposition of carbon only
    • 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
    • H01M4/04—Processes of manufacture in general
    • H01M4/0402—Methods of deposition of the material
    • H01M4/0421—Methods of deposition of the material involving vapour deposition
    • H01M4/0428—Chemical vapour deposition
    • 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
    • H01M4/04—Processes of manufacture in general
    • H01M4/0471—Processes of manufacture in general involving thermal treatment, e.g. firing, sintering, backing particulate active material, thermal decomposition, pyrolysis
    • 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
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/139—Processes of manufacture
    • H01M4/1395—Processes of manufacture of electrodes based on metals, Si or alloys
    • 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
    • H01M4/362—Composites
    • H01M4/364—Composites as mixtures
    • 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
    • H01M4/362—Composites
    • H01M4/366—Composites as layered products
    • 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
    • H01M4/38—Selection of substances as active materials, active masses, active liquids of elements or alloys
    • H01M4/386—Silicon or alloys based on silicon
    • 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
    • H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
    • H01M4/483—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides for non-aqueous cells
    • 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
    • H01M4/62—Selection of inactive substances as ingredients for active masses, e.g. binders, fillers
    • 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
    • H01M4/62—Selection of inactive substances as ingredients for active masses, e.g. binders, fillers
    • H01M4/624—Electric conductive fillers
    • H01M4/625—Carbon or graphite
    • 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
    • H01M4/62—Selection of inactive substances as ingredients for active masses, e.g. binders, fillers
    • H01M4/628—Inhibitors, e.g. gassing inhibitors, corrosion inhibitors
    • 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
    • H01M2004/021—Physical characteristics, e.g. porosity, surface area
    • 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
    • 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
    • H01M4/04—Processes of manufacture in general
    • H01M4/049—Manufacturing of an active layer by chemical means
    • 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

Definitions

  • the present application relates to the field of material technology, and in particular, to a composite material and a preparation method thereof.
  • Lithium-ion batteries usually use graphite as the anode material.
  • the theoretical gram capacity of graphite is 372 mAh/g, and the current gram capacity of graphite has exceeded 360 mAh/g, which is close to the theoretical limit value. It is difficult to have any room for further increase. A further increase in the energy density of the battery.
  • the theoretical gram capacity of silicon is much larger than that of graphite, reaching 4200 mAh/g, and it is promising to be used as a battery anode material.
  • the silicon-based anode material is continuously converted in the state of full lithium insertion and de-lithium, and the volume of the silicon-based anode material is increased in the state of full lithium insertion relative to the delithiation state. From about 300% to 400%, frequent and severe volume changes cause the silicon-based negative electrode material to be susceptible to cracking and chalking, reducing battery life.
  • the present application provides a composite material and a preparation method thereof for solving the problem that the silicon negative electrode material in the battery existing in the prior art is easily broken and pulverized.
  • the present application provides a composite material comprising: a layered silicon core and a plurality of carbon nanotubes.
  • the layered silicon core comprises a plurality of layers of silicon-based material
  • the layer of silicon-based material comprises an oxide of silicon or silicon, such as silicon monoxide or the like.
  • There are interlayer voids between two adjacent silicon-based material layers and the size of the interlayer voids may be different at different positions of two adjacent silicon-based material layers, and different adjacent two layers of interlayer voids The size can also be different.
  • Each of the silicon-based material layers has at least one through hole, and different through holes may have different shapes and sizes.
  • Each of the plurality of carbon nanotubes penetrates the silicon-based material layer through a through hole of the silicon-based material layer, and some of the carbon nanotubes may penetrate all of the silicon-based material layers of the layered silicon core, and some of the carbon nanotubes may only A portion of the silicon-based material layer is penetrated, and one of the through holes may have a carbon nanotube penetrating therethrough, and some of the through holes may have a plurality of carbon nanotubes penetrating therethrough.
  • the interlayer of the two adjacent silicon-based materials of the composite material has interlayer voids, which can suppress the expansion pressure of the composite material during lithium insertion, and reduce the probability of the composite material being broken or pulverized due to large volume change. .
  • the openings in the silicon-based material layer can alleviate the intra-layer stress of the layered silicon core during shrinkage-expansion, further reducing the probability of cracking and pulverization of the silicon-based material layer.
  • the array of carbon nanotubes running through the layered silicon core can provide strong longitudinal support to the layered silicon core, enhancing the strength of the composite.
  • the carbon nanotube array can also enhance the electrical conductivity of the composite, thereby improving the performance of the battery.
  • the carbon nanotube array refers to a plurality of carbon nanotubes that are oriented toward the same or similar.
  • At least a portion of two adjacent layers of silicon-based material are connected to enhance the structural strength of the layered silicon core and the interlayer conductivity of the layer of silicon-based material.
  • each carbon nanotube is connected to one or more layers of silicon-based material, for example, the carbon nanotubes may be connected to, or in contact with, the edge of one or more through-holes therethrough.
  • the layers of silicon-based material are connected to each other. The above structure can enhance the structural strength of the layered silicon core and the interlayer conductivity of the silicon-based material layer.
  • the composite material further includes: a cladding layer coated on an outer surface of the layered silicon core, the cladding layer coating the layered silicon core inside.
  • the coating layer may be a carbon coating layer, an inorganic compound coating layer or an organic coating layer.
  • the coating layer can reduce the direct contact between the layered silicon core and the electrolyte, and slow down the battery capacity attenuation.
  • the cladding layer is a carbon coating layer, it can also provide a highly efficient conductive interface and improve the power performance of the battery.
  • the interlaminar gap between two adjacent silicon-based material layers 111 of the layered silicon core 110 is between 10 nanometers (nm) and 10 micrometers ( ⁇ m) in the delithiated state.
  • the interlayer gap between two adjacent silicon-based material layers 111 may be 10 nm, 40 nm, 120 nm, 660 nm, 1 ⁇ m, 5 ⁇ m, 8 ⁇ m, 10 ⁇ m, or the like.
  • the inter-layer voids of the above size allow the layered silicon core 110 to have a small volume change when switching between the detached state and the lithium-intercalated state, reducing the probability of cracking and pulverization of the composite.
  • the present application provides a method of preparing a composite material, comprising: preparing a metal silicide having a hole according to a silicon-based material having a hole and a metal, the silicon-based material being an oxide of silicon or silicon, the hole having the hole
  • the silicon-based material may be a finished product or may be prepared by itself.
  • the hole may be located on the surface or inside of the silicon-based material, and the hole may also be a through hole.
  • the process for preparing the metal silicide from the silicon-based material and the metal may be sintering, evaporation, sputtering, electroplating, chemical vapor deposition (CVD), or the like.
  • the metal silicide having the holes is reacted with the metal removing agent to obtain a layered silicon core including a plurality of layers of the silicon-based material, and a layer between the two adjacent layers of the silicon-based material There are inter spaces, and each of the silicon-based material layers has at least one via, and the silicon-based material layer includes an oxide of silicon or silicon.
  • the metal removal agent may be ethanol, propanol, butanol, isopropanol, CuCl 2 , SnCl 2 , HCl or the like.
  • each of the plurality of carbon nanotubes penetrating the at least two silicon-based material layers via via holes of at least two silicon-based material layers
  • Some carbon nanotubes may penetrate all of the silicon-based material layers of the layered silicon core. Some of the carbon nanotubes may penetrate only a portion of the silicon-based material layer, and some of the through holes may have a carbon nanotube therethrough, and some through holes may penetrate therethrough. Multiple carbon nanotubes.
  • the composite material prepared by the above method has interlayer voids between adjacent two silicon-based material layers, and the interlayer voids can suppress the expansion pressure of the composite material during lithium insertion, and reduce the composite material to be broken due to large volume change or The chance of chalking.
  • the openings in the silicon-based material layer can alleviate the intra-layer stress of the layered silicon core during shrinkage-expansion, further reducing the probability of cracking and pulverization of the silicon-based material layer.
  • the array of carbon nanotubes running through the layered silicon core can provide strong longitudinal support to the layered silicon core, enhancing the strength of the composite.
  • the carbon nanotube array can also enhance the electrical conductivity of the composite, thereby improving the performance of the battery.
  • the method for preparing a composite material further includes: forming an outer surface of a layered silicon core having a plurality of carbon nanotubes, the cladding layer wrapping the layered silicon core Covered within the cladding layer.
  • the coating layer may be an amorphous carbon coating layer, or may be an inorganic compound coating layer such as a lithium titanate coating layer, or may be an organic coating layer such as a polyaniline coating layer.
  • the coating layer can reduce the direct contact between the layered silicon core and the electrolyte, and slow down the battery capacity attenuation.
  • the cladding layer is a carbon coating layer, it can also provide a highly efficient conductive interface and improve the power performance of the battery.
  • a plurality of carbon nanotubes are prepared on the layered silicon core by a chemical vapor deposition CVD process, each of the plurality of carbon nanotubes passing through at least two silicon groups A through hole of the material layer penetrates the at least two layers of the silicon-based material.
  • the method for preparing carbon nanotubes has lower cost and higher efficiency.
  • a plurality of carbon nanotubes are migrated into the layered silicon core, and each of the plurality of carbon nanotubes passes through at least two through holes of a silicon-based material layer Through the at least two layers of silicon-based material.
  • the method for preparing carbon nanotubes has lower cost and higher efficiency.
  • the silicon-based material having pores is prepared by self-assembling silicon-based particles and colloidal spheres to form a precursor, the silicon-based particles comprising particles of silicon particles or oxides of silicon, Colloidal spheres can be volatilized at elevated temperatures, for example, polystyrene (PS).
  • PS polystyrene
  • the precursor is calcined, and the colloidal sphere is removed to form the silicon-based material having pores.
  • the method of preparing a silicon-based material having pores is relatively low in cost and high in efficiency.
  • the metal from which the metal silicide is prepared includes an alkali metal or alkaline earth metal.
  • the present application provides a battery comprising: a positive electrode, an electrolyte, and a negative electrode; and the electrode material of the positive electrode may be a lithium-containing compound, such as lithium manganate, lithium iron phosphate, lithium nickel cobalt manganese oxide, etc.
  • the electrolyte may be: Ethylene carbonate, propylene carbonate, diethyl carbonate, dimethyl carbonate, ethyl methyl carbonate, phosphorus pentafluoride, hydrofluoric acid, and the like.
  • the present application provides a method for improving a negative electrode material of a lithium ion battery, the method comprising: using a layered silicon core as a main body of a silicon negative electrode material, wherein the layered silicon core comprises a plurality of silicon-based material layers, adjacent to two Each of the silicon-based material layers has an interlayer gap, and each of the silicon-based material layers has at least one via hole, and the silicon-based material layer includes an oxide of silicon or silicon.
  • the interlayer gap between two adjacent layers of the layered silicon core can alleviate the expansion pressure of the silicon anode material in the lithium intercalation state, because the silicon-based material layer can expand to the interlayer gap after intercalating lithium, thereby reducing the entire
  • the volume change of the layered silicon core reduces the probability of cracking and chalking of the composite.
  • the silicon-based material layer of the layered silicon core has an opening which can alleviate the intra-layer stress of the silicon-based material layer during the shrinkage-expansion process of the layered silicon core, further reducing the cracking and chalking of the silicon-based material layer. The chance.
  • the method further includes: disposing a plurality of carbon nanotubes inside the layered silicon core, each of the plurality of carbon nanotubes penetrating the at least two via holes of at least two of the silicon-based material layers The silicon-based material layer.
  • the plurality of carbon nanotubes can provide strong longitudinal support to the layered silicon core, enhance the strength of the silicon anode material, and can enhance interlayer electron conduction of the silicon-based material layer, enhance the conductivity of the silicon anode material, and thereby improve Battery performance.
  • 1a-1b are schematic structural views of a composite material provided by an embodiment of the present application.
  • FIG. 2 is a schematic view of a silicon-based material layer in a delithiated state and a lithium intercalation state
  • 3a-3b are schematic views of adjacent silicon-based material layers
  • Figure 4 is a schematic view of a coating of a composite material
  • Figure 5 is a schematic view showing the interlayer gap between adjacent silicon-based material layers
  • FIG. 6 is a schematic flow chart of a method for preparing a composite material according to an embodiment of the present application.
  • Figure 7a is a schematic view showing the formation process of a layered silicon core
  • Figure 7b is a schematic view showing a process of forming a via hole on a silicon-based material layer
  • FIG. 8 is a schematic structural diagram of a battery according to an embodiment of the present application.
  • the plurality referred to in the present application means two or more.
  • the term “and/or” in the present application is merely an association relationship describing an associated object, indicating that there may be three relationships, for example, A and/or B, which may indicate that A exists separately, and A and B exist simultaneously. There are three cases of B alone.
  • Carbon nanotubes also known as bucky tubes, seamless nano-scale tube structures formed by single or multi-layer graphene sheets curled around the same central axis. Carbon nanotubes have excellent mechanical properties. Strong strength, also has excellent electrical and thermal conductivity.
  • the carbon nanotube array includes a plurality of carbon nanotubes oriented toward the same or similar.
  • Chemical vapor deposition refers to introducing a vapor containing a gaseous reactant or a liquid reactant constituting an element of a target substance and other gases required for the reaction into a reaction chamber, and chemically reacting on the surface of the substrate to form a thin film.
  • Solid electrolyte interface (SEI) membrane During the first charge and discharge of a liquid lithium ion battery, the electrode material reacts with the electrolyte at the solid-liquid phase interface to form a passivation layer covering the surface of the electrode material.
  • the passivation film can effectively prevent the passage of solvent molecules, but lithium ions can be freely embedded and removed through the passivation layer, and have the characteristics of a solid electrolyte. Therefore, this passivation film is called a solid electrolyte interface film.
  • Self-assembly refers to a technique in which basic structural units (molecules, nanomaterials, micro- or larger-scale materials) spontaneously form ordered structures.
  • basic structural units molecules, nanomaterials, micro- or larger-scale materials
  • the basic structural units spontaneously organize or aggregate under a non-covalent bond-based interaction into a stable, regular geometric appearance.
  • FIG. 1a illustrates the structure of a composite 100 provided herein that includes a layered silicon core 110 and a carbon nanotube array 120.
  • the layered silicon core 110 includes a plurality of silicon-based material layers 111, which may be a silicon (Si) layer or an oxide layer of silicon, such as a silicon oxide (SiO) layer.
  • the silicon-based material layer 111 may further include silicon dioxide, but not all of silicon dioxide to improve lithium intercalation capability.
  • the thickness thereof may be the thickness of one or more atomic layers
  • the silicon-based material layer 111 is an oxide layer of silicon
  • the thickness may be the thickness of one or more molecular layers.
  • the thickness of the different silicon-based material layers 111 may be the same or different.
  • Each of the silicon-based material layers 111 has one or more through holes 112, and the shapes and sizes of the different through holes may be different.
  • the shapes of all the through holes are reduced to a circular shape in the drawings of the present specification.
  • the adjacent two silicon-based material layers 111 have interlayer gaps therebetween, and the interlayer gaps between different adjacent silicon-based material layers 111 may be different.
  • the carbon nanotube array 120 includes a plurality of carbon nanotubes 121.
  • the carbon nanotubes 121 penetrate the silicon-based material layer through the through holes of the silicon-based material layer. It should be understood that some of the carbon nanotubes 121 may penetrate all the silicon-based material layers 111, some The carbon nanotubes may penetrate only a portion of the silicon-based material layer 111, and one of the through holes may have a carbon nanotube 121 penetrating therein, and some of the through holes may have a plurality of carbon nanotubes 121 penetrating therethrough. For example, FIG.
  • 1b is a partially enlarged schematic view of a composite material
  • the silicon-based material layer 111-b is adjacent to both the silicon-based material layer 111-a and the silicon-based material layer 111-c
  • the silicon-based material layer 111-a has a through hole 112. -a and the via hole 112-b
  • the silicon-based material layer 111-b has a via hole 112-c and a via hole 112-d
  • the silicon-based material layer 111-c has a via hole 112-e and a via hole 112-f.
  • the through hole 112-a is completely opposite to the through hole 112-c.
  • the through hole 112-c is opposite to the through hole 112-e but partially offset.
  • the carbon nanotube 121-a penetrates the through hole 112-a and the through hole 112-c.
  • the carbon nanotubes 121-b penetrate through the through holes 112-a, the through holes 112-c, and the through holes 112-e; the through holes 112-b are opposite to but partially offset from the through holes 112-d, and the through holes 112-d and the through holes 112 -f is completely staggered, and the carbon nanotubes 121-c penetrate through the through holes 112-b and the through holes 112-d.
  • the carbon nanotubes 121 are simplified in a straight shape, and in actuality, the carbon nanotubes 121 can also be bent.
  • the layered silicon core 110 when the layered silicon core 110 is in the lithium intercalation state, lithium ions are intercalated into the silicon-based material layer 111, the volume of the silicon-based material layer 111 becomes large, and the interlayer gap between the silicon-based material layers 111 becomes small.
  • the reduced inter-layer voids of the layered silicon core 110 can reduce the overall outward extent of the layered silicon core 110. Therefore, the layered silicon core 110 structure can reduce the volume change of the composite material 100 during the delithiation state-lithium state transition, and reduce the probability of composite cracking and pulverization.
  • the silicon-based material layer 111 of the layered silicon core 110 has an opening which can alleviate the intra-layer stress of the silicon-based material layer 111 during the shrink-swell process of the layered silicon core, and further reduce the silicon-based material layer 111. The chance of rupture and chalking.
  • the carbon nanotube array 120 penetrating the plurality of silicon-based material layers 111 can provide strong longitudinal support to the layered silicon core 110, enhancing the strength of the composite material 100.
  • the carbon nanotube array 120 penetrating the plurality of silicon-based material layers 111 can also enhance the interlayer electron conduction of the silicon-based material layer 111, enhance the electrical conductivity of the composite material, and thereby improve the performance of the battery.
  • a portion of the adjacent two silicon-based material layers 111 are connected, as shown in FIG. 3a, the silicon-based material layers 111-e and the adjacent silicon-based material layers 111-d, respectively.
  • the silicon-based material layer 111-f is connected.
  • the adjacent two silicon-based material layers 111 may not be connected, as shown in FIG. 3b, the adjacent silicon-based material layer 111-h and the silicon-based material layer 111-i are not connected. They are connected, but are each connected to the silicon-based material layer 111-g.
  • the adjacent two silicon-based material layers 111 are connected to each other to enhance the structural strength of the layered silicon core 110 and the interlayer conductivity of the silicon-based material layer 111. It should be noted that in order to better embody the interlaminar voids of the layered silicon core 110, the silicon-based material layers 111 are simplified to phase separation between the drawings in the specification other than FIGS. 3a and 3b.
  • each of the carbon nanotubes 121 in the array of carbon nanotubes 120 is coupled to one or more layers of silicon-based material.
  • one or more of the carbon nanotubes 121-b may be The edges of the plurality of via holes are connected, and the carbon nanotubes 121-a may be connected to the silicon-based material layer 111-c which is not penetrated.
  • the above structure can enhance the structural strength of the layered silicon core 110 and the interlayer conductivity of the silicon-based material layer 111.
  • the composite material 100 further includes a cladding layer 130 overlying the outer surface of the layered silicon core 110, the cladding layer 130 encapsulating the layered silicon core 110 inside.
  • the coating layer may be an amorphous carbon coating layer, or may be an inorganic compound coating layer such as a lithium titanate coating layer, or may be an organic coating layer such as a polyaniline coating layer.
  • the cross-sectional shape of the coating layer in FIG. 4 is simplified to a circular shape. In specific implementation, the cross-sectional shape of the coating layer may be other shapes such as an elliptical shape, or may be an irregular shape.
  • the coating layer 130 is prepared on the outer surface of the layered silicon core 110, which can reduce the direct contact between the layered silicon core and the electrolyte, and slow down the battery capacity attenuation.
  • the cladding layer 130 is a carbon coating layer, the electrical conductivity of the composite material 100 can also be enhanced.
  • the interlaminar gap between adjacent two silicon-based material layers 111 of the layered silicon core 110 is in the range of 10 nanometers (nm) to 10 micrometers ( ⁇ m) in the delithiated state.
  • the interlayer gap between two adjacent silicon-based material layers 111 may be 10 nm, 40 nm, 120 nm, 660 nm, 1 ⁇ m, 5 ⁇ m, 8 ⁇ m, 10 ⁇ m, or the like.
  • the inter-layer voids of the above size allow the layered silicon core 110 to have a small volume change when switching between the detached state and the lithium-intercalated state, reducing the probability of cracking and pulverization of the composite.
  • the size of the interlayer gap between two adjacent layers may be different at different positions, as shown in FIG. 5, the interlayer gap between the adjacent silicon-based material layer 111-j and the silicon-based material layer 111-k.
  • the size is not a fixed value, with a minimum inter-layer gap (Cmin) at position A and a maximum inter-layer gap (Cmax) at position B.
  • the preparation method includes:
  • Step 21 Prepare a metal silicide having a hole according to a silicon-based material having a hole and a metal.
  • the silicon-based material includes an oxide of silicon or silicon, such as silicon monoxide or silicon dioxide.
  • the holes of the silicon-based material are located on the surface or inside of the silicon-based material, and the holes may also be through holes.
  • the silicon-based material having pores may be a finished product, or may be prepared by a process of: firstly, self-assembling silicon-based particles and colloidal spheres to form a precursor, and the silicon-based particles include oxidation of silicon particles or silicon. Particles of the substance, the colloidal spheres are volatilizable at high temperatures, for example, polystyrene (PS).
  • PS polystyrene
  • the precursor is calcined to remove the colloidal sphere, and the position originally occupied by the colloidal sphere becomes a hole, thereby obtaining a silicon-based material having pores.
  • the process for preparing a silicon-based material having pores is simple and low in cost.
  • the process for preparing the metal silicide from the silicon-based material and the metal may be sintering, evaporation, sputtering, electroplating, CVD, etc., and the metal used to prepare the metal silicide may be an alkali metal or an alkaline earth metal such as Li, Na, Ca, Mg, etc.
  • the metal silicide is prepared using only one metal, for example, a silica having pores is mixed with magnesium (Mg) to form Mg 2 Si having pores.
  • metal silicides may be prepared using two or more metals, for example, Li 3 NaSi 6 formed from lithium, sodium, and silicon dioxide.
  • Step 22 reacting a metal silicide having a hole with a metal remover to obtain a layered silicon core, the layered silicon core comprising a plurality of layers of a silicon-based material, and an interlayer between two adjacent layers of the silicon-based material
  • the voids, and each layer of silicon-based material has at least one via, and the layer of silicon-based material comprises an oxide of silicon or silicon.
  • the metal remover is used for demetallization reaction with the metal silicide, and the metal remover may be different depending on the type of the metal silicide.
  • the metal remover is a chemical delithiation reagent including, but not limited to, ethanol, propanol, butanol, isopropanol, and the like.
  • the metal silicide is calcium silicide (CaSi 2 )
  • the metal remover may be an oxidizing agent or an acid solution including, but not limited to, CuCl 2 , SnCl 2 , HCl, and the like.
  • the metal silicide and the metal remover react in different reaction media to obtain silicon-based materials of different oxidation states.
  • the reaction medium is an alcohol
  • the calcium silicide reacts with the metal remover to obtain a silica.
  • Other oxides of silicon are represented by SiOx; when the reaction medium is a molten salt, calcium silicide is reacted with a metal remover to obtain pure Si.
  • Fig. 7a shows the unit cell structure of MgSi in which Si particles form a face-centered cubic structure, Mg particles form a simple cubic structure, and the unit cell of the entire MgSi may have a layer of a to e.
  • the above mechanism theoretically explains the formation mechanism of the layered silicon core, and the metal silicide is removed due to various distortions (such as line defects, surface defects, and body defects) in the unit cell structure of the prepared metal silicide.
  • the thickness of the different silicon-based material layers of the layered silicon core formed after the metal may be different, and the size of the interlayer gaps between different adjacent silicon-based material layers may also be different.
  • FIG. 7a shows the formation process of the via holes on the silicon-based material layer.
  • the left side of Fig. 7b shows the b-d layer of the metal-pre-metal silicide, and a hole is formed in the three layers internally, and after the metal is removed, the hole of the c-layer is a through hole.
  • Step 23 preparing a plurality of carbon nanotubes on the layered silicon core, each of the plurality of carbon nanotubes penetrating the at least two silicon-based materials via via holes of at least two silicon-based material layers Floor.
  • the plurality of carbon nanotubes form an array of carbon nanotubes, which can be prepared by:
  • a plurality of carbon nanotubes penetrating through holes of a silicon-based material layer of a layered silicon core are prepared in situ in a layered silicon core.
  • a carbon nanotube array can be prepared in a through hole of a layered silicon core by a CVD process.
  • the layered silicon core prepared in step 22 is heated, and the temperature is raised to a set temperature, and the gaseous carbon source is maintained. After a period of time, then the gaseous carbon source is turned off and cooled by argon Ar gas to form a carbon nanotube array of through holes through the silicon-based material layer of the layered silicon core.
  • the gaseous carbon source may be a gaseous hydrocarbon containing carbon, including but not limited to methane, ethane, propane, ethylene, propylene, acetylene, and the like.
  • the prepared carbon nanotubes are migrated to the through holes of the silicon-based material layer of the layered silicon core to form an array of carbon nanotubes.
  • the carbon nanotubes grown on other substrates are immersed in a solution, such as alcohol, isopropanolamine (IPA), etc., and then the substrate having the carbon nanotubes is etched away, and in the liquid phase
  • IPA isopropanolamine
  • the layered silicon core structure can reduce the volume change of the composite during the delithiation state-lithium state transition, and reduce the probability of composite cracking and pulverization.
  • the silicon-based material layer of the layered silicon core has an opening, which can alleviate the intra-layer stress of the silicon-based material layer during the shrinkage-expansion process of the layered silicon core, and further reduce the cracking and chalking of the silicon-based material layer. The chance.
  • the array of carbon nanotubes penetrating the plurality of layers of silicon-based material can provide strong longitudinal support to the layered silicon core and enhance the strength of the composite.
  • the carbon nanotube array penetrating through the plurality of silicon-based material layers can enhance the interlayer electron conduction of the silicon-based material layer, enhance the conductivity of the battery negative electrode, and further improve the performance of the battery.
  • step 23 the following steps are also performed:
  • Step 24 preparing a coating layer on the outer surface of the layered silicon core having a plurality of carbon nanotubes, the cladding layer coating the layered silicon core in the cladding layer.
  • the coating layer may be an amorphous carbon coating layer, or may be an inorganic compound coating layer such as a lithium titanate coating layer, or may be an organic coating layer such as a polyaniline coating layer.
  • the carbon coating layer can be prepared in various manners in the embodiments of the present application, including but not limited to: evaporation, sputtering, electroplating, CVD, and the like.
  • the layered silicon-carbon nanotube composite material formed in the step 23 is mixed with a carbon source, and cracked at a high temperature to form a carbon coating layer on the outer surface of the layered silicon-carbon nanotube composite material.
  • the carbon source is a gaseous carbon source, a liquid carbon source or a solid carbon source
  • the gaseous carbon source includes but is not limited to methane, ethane, ethylene, acetylene, propylene, carbon monoxide, etc.
  • the liquid carbon source includes but is not limited to Methanol, ethanol, n-hexane, cyclohexane, benzene, toluene, xylene, etc.
  • solid carbon sources include, but are not limited to, polyethylene, polypropylene, polyvinyl chloride, polyvinylidene fluoride, polyacrylonitrile, polystyrene, rings Oxygen resin, phenolic resin, glucose, fructose, sucrose, maltose, coal tar pitch, petroleum pitch, and the like.
  • a coating layer is prepared on the outer surface of the layered silicon core to solidify the layered silicon core, thereby avoiding direct contact between the layered silicon core and the electrolyte, reducing side reactions and preventing powdering of silicon during long-term circulation. Further improve cycle performance.
  • the cladding layer is a carbon coating layer, the conductivity of the composite material can be improved to improve battery performance.
  • This embodiment provides a specific preparation method of a porous layered silicon/carbon nanotube CNTs composite material, including:
  • the polystyrene PS/silica SiO 2 precursor was calcined at 450 ° C for 2 hours in an air atmosphere to remove polystyrene PS beads to obtain porous silica SiO 2 .
  • Porous silica SiO 2 and metal magnesium Mg were ball-milled at a stoichiometric ratio of 1:1.05, and thoroughly mixed. Then, the mixture was transferred to a tube furnace, heated up to 650 ° C at a heating rate of 5 ° C / min, and reacted in a hydrogen-argon mixed atmosphere (5:95) for 4 hours. After cooling to room temperature, the product was treated with 2 mol/L hydrochloric acid HCl for 6 h and 10% hydrofluoric acid HF for 1 h, and the impurity magnesium oxide MgO and silica SiO 2 were removed to obtain porous layered Si, and the porous layered Si was A possible form of a layered silicon core of a via.
  • the above process for preparing the composite material is simple and the cost is low, and the prepared porous layered silicon Si-carbon nanotube CNTs composite material not only has strong strength and electrical conductivity when used as a battery negative electrode, but also in the process of charging and discharging the battery.
  • the medium volume change is small, the structure is stable, and the service life is long.
  • FIG. 8 shows a battery provided by an embodiment of the present application, including a housing 301, a positive electrode 302, a negative electrode 303, and an electrolyte 304.
  • the positive electrode 302, the negative electrode 303, and the electrolyte 304 are housed in the casing 301.
  • the electrode material of the above positive electrode 302 may be a lithium-containing compound such as lithium manganate, lithium iron phosphate, lithium nickel cobalt manganese oxide or the like.
  • the anode 303 is prepared according to the composite material 100 described above, or the electrode material for preparing the anode 303 is prepared by the above steps 21 to 23 or steps 21 to 24.
  • the positive electrode 302 When the battery is charged, the positive electrode 302 releases a cation such as lithium ion, and the lithium ion released from the positive electrode moves to the negative electrode 303 through the electrolyte to be embedded in the negative electrode material. On the contrary, when the battery is discharged, the anode 303 releases the cation, and the cation moves to the cathode 302 through the electrolyte to be embedded in the cathode material.
  • the electrolyte 304 may be ethylene carbonate, propylene carbonate, diethyl carbonate, dimethyl carbonate, ethyl methyl carbonate, phosphorus pentafluoride, hydrofluoric acid or the like. It should be understood that the battery may also include a structure such as a diaphragm 305, an extraction electrode, and the like.
  • the composite material 100 for preparing the anode 303 When the composite material 100 for preparing the anode 303 is in a lithium-intercalation state, lithium ions are intercalated into the silicon-based material layer, the volume of the silicon-based material layer becomes large, the interlayer gap between the silicon-based material layers becomes small, and the layered silicon core is The smaller inter-layer voids can reduce the overall outward expansion of the layered silicon core. Therefore, the layered silicon core structure can reduce the volume change of the composite during the delithiation state-lithium state transition, and reduce the probability of composite cracking and pulverization.
  • the silicon-based material layer of the layered silicon core has an opening, which can alleviate the intra-layer stress of the silicon-based material layer during the shrinkage-expansion process of the layered silicon core, and further reduce the cracking and chalking of the silicon-based material layer. The chance.
  • the array of carbon nanotubes penetrating the plurality of layers of silicon-based material can provide strong longitudinal support to the layered silicon core and enhance the strength of the composite.
  • the carbon nanotube array penetrating through the plurality of silicon-based material layers can enhance the interlayer electron conduction of the silicon-based material layer, enhance the conductivity of the battery negative electrode, and thereby improve the performance of the battery.
  • the embodiment of the present application provides a method for improving a silicon negative electrode material of a lithium ion battery to solve the problem that the silicon negative electrode material is easily broken and pulverized.
  • the method is: using a layered silicon core as a main body of a silicon anode material, the so-called layered silicon core comprises a plurality of layers of silicon-based material, and between the two adjacent layers of the silicon-based material, there is an interlayer gap, and each of the layers
  • the silicon-based material layer has at least one via, and the silicon-based material layer includes an oxide of silicon or silicon.
  • the interlayer gap between two adjacent layers of the layered silicon core can alleviate the expansion pressure of the silicon anode material in the lithium intercalation state, because the silicon-based material layer can expand to the interlayer gap after intercalating lithium, thereby reducing the entire
  • the volume change of the layered silicon core reduces the probability of cracking and chalking of the composite.
  • the silicon-based material layer of the layered silicon core has an opening which can alleviate the intra-layer stress of the silicon-based material layer during the shrinkage-expansion process of the layered silicon core, further reducing the cracking and chalking of the silicon-based material layer. The chance.
  • a plurality of carbon nanotubes are further disposed inside the layered silicon core, and each of the plurality of carbon nanotubes penetrates the through holes of at least two of the silicon-based material layers.
  • the plurality of carbon nanotubes can provide strong longitudinal support to the layered silicon core, enhance the strength of the silicon anode material, and can enhance interlayer electron conduction of the silicon-based material layer, enhance the conductivity of the silicon anode material, and thereby improve Battery performance.

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Abstract

一种复合材料及其制备方法，用以解决现有技术中存在的电池中硅负极材料容易破裂和粉化的问题。该复合材料包括层状硅内核以及多个碳纳米管，所述层状硅内核包括多个硅基材料层，相邻两个所述硅基材料层之间具有层间空隙，且每个所述硅基材料层具有至少一个通孔，所述硅基材料层包括硅或硅的氧化物，所述多个碳纳米管中的每个碳纳米管贯穿至少两个所述硅基材料层的所述通孔。

Description

一种复合材料及其制备方法
本申请要求于2018年2月26日提交中国专利局、申请号为201810159491.2、申请名称为“一种复合材料及其制备方法”的中国专利申请的优先权，其全部内容通过引用结合在本申请中。
技术领域
本申请涉及材料技术领域，尤其涉及一种复合材料及其制备方法。
背景技术
锂离子电池通常采用石墨作为负极材料，石墨的理论克容量为372mAh/g，而当前实际使用的石墨的克容量已超过360mAh/g，已接近理论极限值，很难再有上升的空间，制约电池的能量密度的进一步提升。
硅的理论克容量远大于石墨，达到4200mAh/g，很有希望被用作电池负极材料。但是，在电池的充放电过程中，硅基负极材料不断在满嵌锂状态与脱锂状态下转换，而硅基负极材料在满嵌锂状态下体积相对于脱锂状态下体积增大可达约300％至400％，频繁且剧烈的体积变化导致硅基负极材料容易发生破裂和粉化，降低电池寿命。
发明内容
本申请提供一种复合材料及其制备方法，用以解决现有技术中存在的电池中硅负极材料容易破裂和粉化的问题。
第一方面，本申请提供一种复合材料，包括：层状硅内核以及多个碳纳米管。其中，所述层状硅内核包括多个硅基材料层，该硅基材料层包括硅或硅的氧化物，如一氧化硅等。相邻两个所述硅基材料层之间具有层间空隙，该层间空隙的大小在相邻两个硅基材料层不同位置处可以不同，且不同的相邻两层的层间空隙的大小也可以不同。每个所述硅基材料层具有至少一个通孔，不同的通孔的形状以及大小可以不同。该多个碳纳米管中的每个碳纳米管经由硅基材料层的通孔贯穿硅基材料层，一些碳纳米管可以贯穿层状硅内核的所有硅基材料层，一些碳纳米管可以只贯穿部分硅基材料层，且一些通孔中可以贯穿有一个碳纳米管，一些通孔可以贯穿有多个碳纳米管。
上述复合材料的相邻两个硅基材料层之间具有层间空隙，该层间空隙可以抑制复合材料在嵌锂时的膨胀压力，减少复合材料因体积变化较大而破裂或粉化的几率。不仅如此，硅基材料层上的开孔可以缓解层状硅内核在收缩-膨胀过程中的层内应力，进一步减小硅基材料层破裂和粉化的几率。再者，贯穿层状硅内核的碳纳米管阵列能够给层状硅内核提供较强的纵向支撑，增强复合材料的强度。不仅如此，碳纳米管阵列还能够增强复合材料的导电性能，进而提高电池的性能。碳纳米管阵列，是指包括多个朝向相同或相近的碳纳米管。
在一些可选的实现方式中，相邻两个所述硅基材料层的至少一部分相连，以增强层状硅内核的结构强度以及硅基材料层的层间导电性能。
在一些可选的实现方式中，每个碳纳米管与一个或多个硅基材料层相连，例如，碳纳米管可以与其贯穿的一个或多个通孔的边缘相连，也可以与其接触但未贯穿的硅 基材料层相连。上述结构可以增强层状硅内核的结构强度以及硅基材料层的层间导电性能。
在一些可选的实现方式中，复合材料还包括：包覆在所述层状硅内核的外表面的包覆层，该包覆层将层状硅内核包覆在内部。该包覆层可以为碳包覆层、无机化合物包覆层或有机物包覆层。该包覆层可以减少层状硅内核与电解液的直接接触，减缓电池容量衰减，而且，包覆层为碳包覆层时还可以提供高效的导电界面，提升电池的功率性能。
在一些可选的实现方式中，在脱锂状态下，层状硅内核110的相邻两个硅基材料层111之间的层间空隙的大小在10纳米(nm)至10微米(μm)范围内，例如，相邻两个硅基材料层111之间的层间空隙可以为10nm、40nm、120nm、660nm、1μm、5μm、8μm、10μm等。上述大小的层间空隙可以让层状硅内核110在脱离状态与嵌锂状态之间转换时，具有较小的体积变化，降低复合材料破裂和粉化的几率。
第二方面，本申请提供一种制备复合材料的方法，包括：根据具有孔洞的硅基材料与金属制备具有孔洞的金属硅化物，该硅基材料可以为硅或硅的氧化物，该具有孔洞的硅基材料可以为成品，也可以自行制备，该孔洞可以位于硅基材料的表面或内部，该孔洞也可以为通孔。由硅基材料与金属制备金属硅化物的工艺可以为烧结、蒸发、溅射、电镀、化学气相沉积(chemical vapor deposition，CVD)等。然后，将具有孔洞的金属硅化物与金属脱除剂进行反应，得到层状硅内核，该层状硅内核包括多个硅基材料层，相邻两个所述硅基材料层之间具有层间空隙，且每个所述硅基材料层具有至少一个通孔，所述硅基材料层包括硅或硅的氧化物。其中，金属脱除剂可以为乙醇、丙醇、丁醇、异丙醇、CuCl 2、SnCl 2、HCl等。然后，在层状硅内核上制备多个碳纳米管，所述多个碳纳米管中的每个碳纳米管经由至少两个硅基材料层的通孔贯穿所述至少两个硅基材料层，一些碳纳米管可以贯穿层状硅内核的所有硅基材料层，一些碳纳米管可以只贯穿部分硅基材料层，且一些通孔中可以贯穿有一个碳纳米管，一些通孔可以贯穿有多个碳纳米管。
采用上述方法制备的复合材料的相邻两个硅基材料层之间具有层间空隙，该层间空隙可以抑制复合材料在嵌锂时的膨胀压力，减少复合材料因体积变化较大而破裂或粉化的几率。不仅如此，硅基材料层上的开孔可以缓解层状硅内核在收缩-膨胀过程中的层内应力，进一步减小硅基材料层破裂和粉化的几率。再者，贯穿层状硅内核的碳纳米管阵列能够给层状硅内核提供较强的纵向支撑，增强复合材料的强度。不仅如此，碳纳米管阵列还能够增强复合材料的导电性能，进而提高电池的性能。
在一些可选的实现方式中，制备复合材料的方法还包括：形成有多个碳纳米管的层状硅内核的外表面制备包覆层，所述包覆层将所述层状硅内核包覆在所述包覆层内。该包覆层可以为无定形的碳包覆层，也可以为无机化合物包覆层，如钛酸锂包覆层，还可以为有机物包覆层，如聚苯胺包覆层。该包覆层可以减少层状硅内核与电解液的直接接触，减缓电池容量衰减，而且，包覆层为碳包覆层时还可以提供高效的导电界面，提升电池的功率性能。
在一些可选的实现方式中，采用化学气相沉积CVD工艺在所述层状硅内核上制备多个碳纳米管，所述多个碳纳米管中的每个碳纳米管经由至少两个硅基材料层的通孔 贯穿所述至少两个硅基材料层。该制备碳纳米管的方法成本较低，效率较高。
在一些可选的实现方式中，将多个碳纳米管迁移至所述层状硅内核内，所述多个碳纳米管中的每个碳纳米管经由至少两个硅基材料层的通孔贯穿所述至少两个硅基材料层。该制备碳纳米管的方法成本较低，效率较高。
在一些可选的实现方式中，具有孔洞的硅基材料的制备方法为：将硅基粒子与胶体球自组装形成前驱体，所述硅基粒子包括硅粒子或硅的氧化物的粒子，该胶体球在高温下可挥发，例如，聚苯乙烯(polystyrene，PS)。煅烧所述前驱体，去除所述胶体球，形成所述具有孔洞的硅基材料。该制备具有孔洞的硅基材料的方法成本较低，效率较高。
在一些可选的实现方式中，制备金属硅化物的金属包括碱金属或碱土金属。
第三方面，本申请提供一种电池，包括：正极、电解液以及负极，正极的电极材料可以为含锂的化合物，如锰酸锂、磷酸铁锂、镍钴锰酸锂等，负极的电极材料为第一方面或第一方面的任意可选方式所述的复合材料，或者，负极的电极材料根据第二方面或第二方面的任意可选方式所述的方法制备，电解液可以为.碳酸乙烯酯、碳酸丙烯酯、碳酸二乙酯、碳酸二甲酯、碳酸甲乙酯、五氟化磷以及氢氟酸等。
第四方面，本申请提供一种改良锂离子电池负极材料的方法，该方法包括：将层状硅内核作为硅负极材料的主体，所谓层状硅内核包括多个硅基材料层，相邻两个所述硅基材料层之间具有层间空隙，且每个所述硅基材料层具有至少一个通孔，所述硅基材料层包括硅或硅的氧化物。该层状硅内核的相邻两层之间的层间空隙可以缓解硅负极材料在嵌锂状态下的膨胀压力，因为硅基材料层在嵌锂后可以向层间空隙扩张，进而减小整个层状硅内核的体积变化，降低复合材料破裂和粉化的几率。而且，层状硅内核的硅基材料层具有开孔，该开孔可以缓解层状硅内核在收缩-膨胀过程中硅基材料层的层内应力，进一步减小硅基材料层破裂和粉化的几率。该方法还包括：在层状硅内核内部设置多个碳纳米管，所述多个碳纳米管中的每个碳纳米管经由至少两个所述硅基材料层的通孔贯穿所述至少两个所述硅基材料层。该多个碳纳米管能够给层状硅内核提供较强的纵向支撑，增强硅负极材料的强度，而且还能够增强硅基材料层的层间电子传导，增强硅负极材料的导电性能，进而提高电池的性能。
附图说明
图1a-图1b为本申请实施例提供的复合材料的结构示意图；
图2为硅基材料层在脱锂状态以及嵌锂状态下的示意图；
图3a-图3b为相邻硅基材料层的示意图；
图4为复合材料的包覆层的示意图；
图5为相邻硅基材料层之间层间空隙的示意图；
图6为本申请实施例提供的制备复合材料的方法的流程示意图；
图7a为层状硅内核的形成过程的示意图；
图7b为硅基材料层上通孔的形成过程的示意图；
图8为本申请实施例提供的电池的结构示意图。
具体实施方式
为了使本申请的目的、技术方案和优点更加清楚，下面将结合附图对本申请作进一步地详细描述。
本申请中所涉及的多个，是指两个或两个以上。另外，本申请中术语“和/或”，仅仅是一种描述关联对象的关联关系，表示可以存在三种关系，例如，A和/或B，可以表示：单独存在A，同时存在A和B，单独存在B这三种情况。
下面先介绍本申请实施例涉及的一些概念。
碳纳米管(carbon nanotubes，CNTs)：又称巴基管，由单层或多层石墨烯片围绕同一中心轴卷曲而成的无缝纳米级管结构，碳纳米管具有优良的力学性能，具有较强的强度，还具有优异的导电、导热性能。
碳纳米管阵列，包括多个朝向相同或相近的碳纳米管。
化学气相淀积(chemical vapor deposition，CVD)：指把含有构成目标物质的元素的气态反应剂或液态反应剂的蒸气及反应所需其它气体引入反应室，在衬底表面发生化学反应生成薄膜、颗粒或量子点的过程。
固体电解质界面(solid electrolyte interface，SEI)膜：在液态锂离子电池首次充放电过程中，电极材料与电解液在固液相界面上发生反应，形成一层覆盖于电极材料表面的钝化层，该钝化膜能有效地阻止溶剂分子的通过，但锂离子却可以经过该钝化层自由地嵌入和脱出，具有固体电解质的特征，因此这层钝化膜被称为固体电解质界面膜。
自组装(self-assembly)，是指基本结构单元(分子，纳米材料，微米或更大尺度的物质)自发形成有序结构的一种技术。在自组装的过程中，基本结构单元在基于非共价键的相互作用下自发的组织或聚集为一个稳定、具有一定规则几何外观的结构。
图1a示出本申请提供的复合材料100的结构，复合材料100包括层状硅内核110和碳纳米管阵列120。
层状硅内核110包括多个硅基材料层111，该硅基材料层111可以为硅(Si)层或硅的氧化物层，例如一氧化硅(SiO)层。可选的，硅基材料层111还可以包括二氧化硅，但不全部为二氧化硅，以提高嵌锂能力。在硅基材料层111为Si层时，其厚度可以为一个或多个原子层的厚度，在硅基材料层111为硅的氧化物层时，其厚度可以为一个或多个分子层的厚度，且不同硅基材料层111的厚度可以相同，也可以不同。每个硅基材料层111具有一个或多个通孔112，不同通孔的形状以及大小可以不同，本申请的说明书附图中将所有通孔的形状简化为圆形。相邻的两个硅基材料层111之间具有层间空隙，不同的相邻硅基材料层111之间的层间空隙可以不同。
碳纳米管阵列120，包括多个碳纳米管121，碳纳米管121经由硅基材料层的通孔贯穿硅基材料层，应理解，一些碳纳米管121可以贯穿所有硅基材料层111，一些碳纳米管可以只贯穿部分硅基材料层111，且一些通孔中可以贯穿有一个碳纳米管121，一些通孔可以贯穿有多个碳纳米管121。例如，图1b为复合材料的局部放大示意图，硅基材料层111-b与硅基材料层111-a、硅基材料层111-c均相邻，硅基材料层111-a具有通孔112-a以及通孔112-b，硅基材料层111-b具有通孔112-c以及通孔112-d，硅基材料层111-c具有通孔112-e以及通孔112-f。通孔112-a与通孔112-c完全正对，通 孔112-c与通孔112-e相对但部分错开，碳纳米管121-a贯穿通孔112-a与通孔112-c，碳纳米管121-b贯穿通孔112-a、通孔112-c以及通孔112-e；通孔112-b与通孔112-d相对但部分错开，通孔112-d与通孔112-f完全错开，碳纳米管121-c贯穿通孔112-b与通孔112-d。图1b中，碳纳米管121简化为笔直形状，实际情况中，碳纳米管121也可以弯曲。
参见图2，在层状硅内核110处于嵌锂状态下时，锂离子嵌入硅基材料层111，硅基材料层111的体积变大，硅基材料层111之间的层间空隙变小，层状硅内核110的层间空隙变小可以减少层状硅内核110整体向外的扩张程度。因此，层状硅内核110结构可以减少复合材料100在脱锂状态-嵌锂状态转换过程中的体积变化，降低复合材料破裂和粉化的几率。另外，层状硅内核110的硅基材料层111具有开孔，该开孔可以缓解层状硅内核在收缩-膨胀过程中硅基材料层111的层内应力，进一步减小硅基材料层111破裂和粉化的几率。再者，贯穿多个硅基材料层111的碳纳米管阵列120能够给层状硅内核110提供较强的纵向支撑，增强复合材料100的强度。不仅如此，贯穿多个硅基材料层111的碳纳米管阵列120还能够增强硅基材料层111的层间电子传导，增强复合材料的导电性能，进而提高电池的性能。
在一种可选的设计中，相邻两个硅基材料层111之间有一部分相连，如图3a所示，硅基材料层111-e分别与相邻的硅基材料层111-d、硅基材料层111-f相连。在另一种可选的设计中，相邻两个硅基材料层111之间可以不相连，如图3b所示，相邻的硅基材料层111-h与硅基材料层111-i不相连，而是均与硅基材料层111-g相连。前一种设计中，相邻两个硅基材料层111之间相连，能够增强层状硅内核110的结构强度以及硅基材料层111的层间导电性能。需要说明的是，为了更好地体现层状硅内核110的层间空隙，在图3a、图3b之外的说明书附图中，硅基材料层111之间被简化为相分离。
在一些可选的设计中，碳纳米管阵列120中的每个碳纳米管121与一个或多个硅基材料层相连，例如，参见图1b，碳纳米管121-b可以与其贯穿的一个或多个通孔的边缘相连，碳纳米管121-a可以与其未贯穿的硅基材料层111-c相连。上述结构可以增强层状硅内核110的结构强度以及硅基材料层111的层间导电性能。
在一些可选的设计中，参见图4，复合材料100还包括：包覆在层状硅内核110的外表面的包覆层130，该包覆层130将层状硅内核110包覆在内部。该包覆层可以为无定形的碳包覆层，也可以为无机化合物包覆层，如钛酸锂包覆层，还可以为有机物包覆层，如聚苯胺包覆层。需要说明的是，图4中包覆层的截面形状简化为圆形，在具体实施时，包覆层的截面形状可以为椭圆形等其他形状，也可以为不规则形状。
层状硅内核与电解液直接接触将导致硅与电解液不断产生新的SEI膜，导致电解液消耗殆尽，电池容量迅速衰减。上述技术方案中，在层状硅内核110的外表面制备包覆层130，可以减少层状硅内核与电解液的直接接触，减缓电池容量衰减。而且，在包覆层130为碳包覆层时，还可以增强复合材料100的导电性。
在一些可选的设计中，在脱锂状态下，层状硅内核110的相邻两个硅基材料层111之间的层间空隙的大小在10纳米(nm)至10微米(μm)范围内，例如，相邻两个硅基材料层111之间的层间空隙可以为10nm、40nm、120nm、660nm、1μm、5μm、 8μm、10μm等。上述大小的层间空隙可以让层状硅内核110在脱离状态与嵌锂状态之间转换时，具有较小的体积变化，降低复合材料破裂和粉化的几率。
应理解，相邻两层之间的层间空隙的大小在不同位置处可以不同，如图5所示，相邻的硅基材料层111-j与硅基材料层111-k的层间空隙的大小不是固定值，在位置A处具有最小的层间空隙(Cmin)，在位置B处具有最大的层间空隙(Cmax)。
下面介绍复合材料100的一些可能的制备方法，参见图6，该制备方法包括：
步骤21、根据具有孔洞的硅基材料与金属制备具有孔洞的金属硅化物。
硅基材料包括硅或硅的氧化物，如一氧化硅、二氧化硅，硅基材料的孔洞位于硅基材料的表面或内部，该孔洞也可以为通孔。该具有孔洞的硅基材料可以为成品，也可以采用如下工艺制备，该制备工艺为：首先，将硅基粒子与胶体球自组装形成前驱体，所述硅基粒子包括硅粒子或硅的氧化物的粒子，该胶体球在高温下可挥发，例如，聚苯乙烯(polystyrene，PS)。然后，煅烧前驱体，去除胶体球，原来被胶体球占据的位置变成孔洞，得到具有孔洞的硅基材料。该制备具有孔洞的硅基材料的工艺简单，成本较低。
由硅基材料与金属制备金属硅化物的工艺可以为烧结、蒸发、溅射、电镀、CVD等，而用于制备金属硅化物的金属可以为碱金属或碱土金属，如Li、Na、Ca、Mg等。在一些实施例中，只使用一种金属制备金属硅化物，例如，将具有孔洞的二氧化硅与镁(Mg)混合加热，形成具有孔洞的Mg 2Si。在另一些实施例中，可以使用两种或以上的金属制备金属硅化物，例如，根据锂、钠与二氧化硅形成的Li 3NaSi 6。
步骤22、将具有孔洞的金属硅化物与金属脱除剂进行反应，得到层状硅内核，该层状硅内核包括多个硅基材料层，相邻两个硅基材料层之间具有层间空隙，且每个硅基材料层具有至少一个通孔，硅基材料层包括硅或硅的氧化物。
金属脱除剂用于与金属硅化物发生脱金属反应，金属脱除剂根据金属硅化物的种类不同而可以不同。例如，当金属硅化物为锂的硅化物(LiSix)时，金属脱除剂为化学脱锂试剂，包括但不限于乙醇、丙醇、丁醇、异丙醇等。当金属硅化物为硅化钙(CaSi 2)时，金属脱除剂可以为氧化性试剂或酸溶液，包括但不限于CuCl 2、SnCl 2、HCl等。金属硅化物与金属脱除剂在不同的反应介质中反应，可以得到不同氧化态的硅基材料，当反应介质为醇类时，硅化钙与金属脱除剂反应可以得到二氧化硅之外的硅的其他氧化物，表示为SiOx；当反应介质为熔盐时，硅化钙与金属脱除剂进行反应得到纯Si。
下面以MgSi为例，介绍MgSi脱除金属后，形成层状硅内核的机制。图7a示出MgSi的晶胞结构，其中，Si粒子形成面心立方结构，Mg粒子形成简立方结构，整个MgSi的晶胞分可以为a～e五层。MgSi在与金属脱除剂反应后，b层与d层的Mg粒子被脱除，a层与c层之间以及c层与e层之间的间隙较大，即形成层间空隙。应理解，上述机制为理论上阐述层状硅内核的形成机制，由于制备的金属硅化物的晶胞结构存在各种畸变(如线缺陷、面缺陷以及体缺陷等)，金属硅化物在脱除金属后所形成的层状硅内核的不同硅基材料层的厚度可以不同，不同的相邻硅基材料层之间的层间空隙的大小也可以不同。
以图7a所示c层为例，介绍硅基材料层上的通孔的形成过程。图7b中左侧示出脱除金属前金属硅化物的b～d层，三层内部共同形成有一个孔洞，而在脱除金属后，c 层的孔洞即为一通孔。
步骤23、在层状硅内核上制备多个碳纳米管，所述多个碳纳米管中的每个碳纳米管经由至少两个硅基材料层的通孔贯穿所述至少两个硅基材料层。
该多个碳纳米管形成碳纳米管阵列，其制备方式可以为：
其一，在层状硅内核中原位制备贯穿层状硅内核的硅基材料层的通孔的多个碳纳米管。例如，可以采用CVD工艺在层状硅内核的通孔中制备碳纳米管阵列，具体的，将步骤22制备得到的层状硅内核进行加热，升温至设定温度后，气态碳源，并保持一段时间，然后关闭气态碳源，并通入氩Ar气冷却，便可形成贯穿层状硅内核的硅基材料层的通孔的碳纳米管阵列。其中，气态碳源可以为含碳的气态烃类物质，包括但不限于甲烷、乙烷、丙烷、乙烯、丙烯、乙炔等。
其二，将已经制备好的碳纳米管迁移至层状硅内核的硅基材料层的通孔，形成碳纳米管阵列。例如，将生长在其他衬底上的碳纳米管浸入溶液内，例如酒精，异丙醇胺(Isopropanolamine，IPA)等溶剂，然后将长有碳纳米管的衬底腐蚀掉，在液相中将碳纳米管迁移至层状硅内核的硅基材料层的通孔中。
采用上述工艺制备的复合材料在处于嵌锂状态下时，锂离子嵌入硅基材料层，硅基材料层的体积变大，硅基材料层之间的层间空隙变小，层状硅内核的层间空隙变小可以减少层状硅内核整体向外的扩张程度。因此，层状硅内核结构可以减少复合材料在脱锂状态-嵌锂状态转换过程中的体积变化，降低复合材料破裂和粉化的几率。另外，层状硅内核的硅基材料层具有开孔，该开孔可以缓解层状硅内核在收缩-膨胀过程中硅基材料层的层内应力，进一步减小硅基材料层破裂和粉化的几率。再者，贯穿多个硅基材料层的碳纳米管阵列能够给层状硅内核提供较强的纵向支撑，增强复合材料的强度。不仅如此，贯穿多个硅基材料层的碳纳米管阵列还能够增强硅基材料层的层间电子传导，增强电池负极的导电性能，进而提高电池的性能。
在一些可选的设计中，在步骤23之后，还执行如下步骤：
步骤24、在形成有多个碳纳米管的层状硅内核的外表面制备包覆层，该包覆层将层状硅内核包覆在包覆层内。该包覆层可以为无定形的碳包覆层，也可以为无机化合物包覆层，如钛酸锂包覆层，还可以为有机物包覆层，如聚苯胺包覆层。
以碳包覆层为例，本申请实施例中可以采用多种方式制备碳包覆层，包括但不限于：蒸发、溅射、电镀、CVD等。例如，将步骤23形成的层状硅基-碳纳米管复合材料与碳源混合，在高温下裂解，在层状硅基-碳纳米管复合材料的外表面形成碳包覆层。其中，所述的碳源为气态碳源、液态碳源或固态碳源，其中，气态碳源包括但不限于甲烷、乙烷、乙烯、乙炔、丙烯、一氧化碳等；液态碳源包括但不限于甲醇、乙醇、正己烷、环己烷、苯、甲苯、二甲苯等；固态碳源包括但不限于聚乙烯、聚丙烯、聚氯乙烯、聚偏氟乙烯、聚丙烯腈、聚苯乙烯、环氧树脂、酚醛树脂、葡萄糖、果糖、蔗糖、麦芽糖、煤焦油沥青、石油沥青等。
上述技术方案中，在层状硅内核的外表面制备包覆层，可以固化层状硅内核，避免层状硅内核与电解液直接接触，减少副反应，防止长期循环过程中硅的粉化，进一步提高循环性能。另外，在包覆层为碳包覆层时，还可以提高复合材料的导电性，提升电池性能。
下面介绍制备上述复合材料的一种应用实例。本实施例提供一种多孔层状硅/碳纳米管CNTs复合材料的具体制备方法，包括：
(1)根据特定化学计量比，将500纳米(nm)聚苯乙烯(PS)胶体球与7nm的二氧化硅粒子分散在装有去离子水中的玻璃生长瓶中，超声分散，并将生长瓶放置在60℃恒温水浴中。控制瓶内压力，并在红外灯的照射下辅助自组装过程，维持15-30分钟，形成聚苯乙烯PS/二氧化硅SiO 2前驱体。
(2)将聚苯乙烯PS/二氧化硅SiO 2前驱体在450℃，空气氛围下，煅烧2小时，去除聚苯乙烯PS小球，得到多孔二氧化硅SiO 2。
(3)按计量比为1：1.05将多孔二氧化硅SiO 2与金属镁Mg球磨，充分混合。然后转入管式炉，以5℃/min的加热速率升温至650℃，在氢氩混合气氛中(5:95)反应4h。冷却至室温，将产物经过2mol/L盐酸HCl处理6h、10％氢氟酸HF处理1h，出去杂质氧化镁MgO和二氧化硅SiO 2，得到多孔层状Si，该多孔层状Si即为具有通孔的层状硅内核的一种可能形式。
(4)将多孔层状硅Si分散在石英片基底上，并转移至反应炉中，通入保护气体(如氢氩混合气)，以20℃/min的速率升至700℃，维持20min，然后停止通入保护气体，并通入体积比为1:1的碳源气体乙炔和氮气，流量为200～300mL/min，反应30～60min。然后在保护气氛下冷却至室温，得到碳纳米管CNTs贯穿在多孔层状硅Si中的复合材料。
上述制备复合材料的工艺简单、成本较低，且制备的多孔层状硅Si-碳纳米管CNTs复合材料在用作电池负极时，不仅具有较强的强度以及导电性能，而且在电池充放电过程中体积变化较小，结构稳定、使用寿命较长。
图8示出本申请实施例提供的一种电池，包括：壳体301、正极302、负极303以及电解液304。其中，正极302、负极303以及电解液304容置与壳体301内。上述正极302的电极材料可以为含锂的化合物，如锰酸锂、磷酸铁锂、镍钴锰酸锂等。上述负极303根据前述复合材料100制备，或者，制备负极303的电极材料采用前述步骤21～步骤23或步骤21～步骤24的工艺制备。在电池充电时，正极302释放阳离子，如锂离子，正极释放的锂离子通过电解液移动至负极303，嵌入负极材料。反之，在电池放电时，负极303释放阳离子，阳离子通过电解液移动至正极302，嵌入正极材料。上述电解液304可以为.碳酸乙烯酯、碳酸丙烯酯、碳酸二乙酯、碳酸二甲酯、碳酸甲乙酯、五氟化磷以及氢氟酸等。应理解，电池还可以包括隔膜305、引出电极等结构。
制备负极303的复合材料100在处于嵌锂状态下时，锂离子嵌入硅基材料层，硅基材料层的体积变大，硅基材料层之间的层间空隙变小，层状硅内核的层间空隙变小可以减少层状硅内核整体向外的扩张程度。因此，层状硅内核结构可以减少复合材料在脱锂状态-嵌锂状态转换过程中的体积变化，降低复合材料破裂和粉化的几率。另外，层状硅内核的硅基材料层具有开孔，该开孔可以缓解层状硅内核在收缩-膨胀过程中硅基材料层的层内应力，进一步减小硅基材料层破裂和粉化的几率。再者，贯穿多个硅基材料层的碳纳米管阵列能够给层状硅内核提供较强的纵向支撑，增强复合材料的强度。不仅如此，贯穿多个硅基材料层的碳纳米管阵列还能够增强硅基材料层的层间电 子传导，增强电池负极的导电性能，进而提高电池的性能。
本申请实施例提供一种改良锂离子电池的硅负极材料的方法，以解决硅负极材料容易破裂和粉化的问题。该方法为：将层状硅内核作为硅负极材料的主体，所谓层状硅内核包括多个硅基材料层，相邻两个所述硅基材料层之间具有层间空隙，且每个所述硅基材料层具有至少一个通孔，所述硅基材料层包括硅或硅的氧化物。该层状硅内核的相邻两层之间的层间空隙可以缓解硅负极材料在嵌锂状态下的膨胀压力，因为硅基材料层在嵌锂后可以向层间空隙扩张，进而减小整个层状硅内核的体积变化，降低复合材料破裂和粉化的几率。而且，层状硅内核的硅基材料层具有开孔，该开孔可以缓解层状硅内核在收缩-膨胀过程中硅基材料层的层内应力，进一步减小硅基材料层破裂和粉化的几率。进一步，该方法中，还在层状硅内核内部设置多个碳纳米管，所述多个碳纳米管中的每个碳纳米管贯穿至少两个所述硅基材料层的所述通孔。该多个碳纳米管能够给层状硅内核提供较强的纵向支撑，增强硅负极材料的强度，而且还能够增强硅基材料层的层间电子传导，增强硅负极材料的导电性能，进而提高电池的性能。
以上，仅为本申请的具体实施方式，但本申请的保护范围并不局限于此，任何熟悉本技术领域的技术人员在本申请揭露的技术范围内，可轻易想到变化或替换，都应涵盖在本申请的保护范围之内。因此，本申请的保护范围应以权利要求的保护范围为准。

Claims (11)

  1. 一种复合材料，其特征在于，包括：
    层状硅内核，所述层状硅内核包括多个硅基材料层，相邻两个所述硅基材料层之间具有层间空隙，且每个所述硅基材料层具有至少一个通孔，所述硅基材料层包括硅或硅的氧化物；
    多个碳纳米管，所述多个碳纳米管中的每个碳纳米管经由至少两个硅基材料层的通孔贯穿所述至少两个硅基材料层。
  2. 根据权利要求1所述的复合材料，其特征在于，相邻两个所述硅基材料层的至少一部分相连。
  3. 根据权利要求1所述的复合材料，其特征在于，每个所述碳纳米管与至少一个所述硅基材料层相连。
  4. 根据权利要求1至3任一项所述的复合材料，其特征在于，还包括：
    包覆层，用于将所述层状硅内核包覆在所述包覆层内。
  5. 根据权利要求1至4任一项所述的复合材料，其特征在于，相邻两个所述硅基材料层之间的层间空隙的大小在10nm～10μm范围内。
  6. 一种制备复合材料的方法，其特征在于，包括：
    根据具有孔洞的硅基材料与金属制备具有孔洞的金属硅化物，所述硅基材料包括硅或硅的氧化物；
    将所述具有孔洞的金属硅化物与金属脱除剂进行反应，得到层状硅内核，所述层状硅内核包括多个硅基材料层，相邻两个所述硅基材料层之间具有层间空隙，且每个所述硅基材料层具有至少一个通孔，所述硅基材料层包括硅或硅的氧化物；
    在所述层状硅内核上制备多个碳纳米管，所述多个碳纳米管中的每个碳纳米管经由至少两个硅基材料层的通孔贯穿所述至少两个硅基材料层。
  7. 根据权利要求6所述的方法，其特征在于，还包括：
    在形成有所述多个碳纳米管的层状硅内核的外表面制备包覆层，所述包覆层将所述层状硅内核包覆在所述包覆层内。
  8. 根据权利要求6或7所述的方法，其特征在于，在所述层状硅内核上制备多个碳纳米管，包括：
    采用化学气相沉积CVD工艺在所述层状硅内核上制备多个碳纳米管，所述多个碳纳米管中的每个碳纳米管经由至少两个硅基材料层的通孔贯穿所述至少两个硅基材料层；或者
    将多个碳纳米管迁移至所述层状硅内核内，所述多个碳纳米管中的每个碳纳米管经由至少两个硅基材料层的通孔贯穿所述至少两个硅基材料层。
  9. 根据权利要求6至8任一项所述的方法，其特征在于，在根据具有孔洞的硅基材料与金属制备金属硅化物之前，还包括：
    将硅基粒子与胶体球自组装形成前驱体，所述硅基粒子包括硅粒子或硅的氧化物的粒子；
    煅烧所述前驱体，去除所述胶体球，形成所述具有孔洞的硅基材料。
  10. 根据权利要求6至9任一项所述的方法，其特征在于，所述金属包括碱金属 或碱土金属。
  11. 一种电池，包括：正极、电解液以及负极，其特征在于，所述负极的电极材料为如权利要求1至5中任一项所述的复合材料，或者，所述负极的电极材料根据权利要求6至10中任一项所述的方法制备。
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