KR102108922B1 - Method of preparing nano composite for anode of lithium battery and nano complex prepared by same - Google Patents

Abstract

The present application relates to a method for manufacturing a nanocomposite for an anode of a lithium battery and a nanocomposite prepared thereby, and more specifically, includes a transition metal oxide, a carbon-based matrix, and a conductive polymer. By controlling the type, it relates to a method of manufacturing a customized plug-and-play nanocomposite and a nanocomposite produced thereby.

Description

Method for manufacturing nanocomposite for anode of lithium battery and nanocomposite produced thereby {METHOD OF PREPARING NANO COMPOSITE FOR ANODE OF LITHIUM BATTERY AND NANO COMPLEX PREPARED BY SAME}

The present application relates to a method for manufacturing a nanocomposite for an anode of a lithium battery and a nanocomposite prepared thereby, and more specifically, includes a transition metal oxide, a carbon-based matrix, and a conductive polymer. By controlling the type, it relates to a method of manufacturing a customized plug-and-play nanocomposite and a nanocomposite produced thereby.

In recent years, research on lithium-based batteries has been performed in various fields. In particular, the development of active materials for lithium anodes to secure high energy density and cycle stability as well as light weight and economic efficiency were important factors.

Although studies on various energy storage devices have been continued, the proposed composite for anodes is not environmentally friendly, causing chemical problems. Recently, due to the global warming problem, research to minimize the exhaust gas emitted while manufacturing a lithium battery has been recommended.

So, the material for the developed anode selects an appropriate composition and provides advantages in continuous production and custom production. However, the spray pyrolysis method employed for continuous production has a problem that requires a template, uses toxic chemicals, and requires a high temperature process to produce a porous material.

Therefore, there is a need to study how to solve this problem and manufacture a digitized anode assembly.

According to an aspect of the present application, it is intended to provide an apparatus for manufacturing a nanocomposite including a spark ablation connected in series, a mechanical injection device, and a UA irradiation device.

According to an aspect of the present application, it is intended to provide a method of manufacturing a material for a lithium battery anode in a continuous process.

According to an aspect of the present application, it is intended to provide a material for a custom lithium battery anode.

One aspect of the present application comprises the steps of preparing a gas containing transition metal oxide nanoparticles; Preparing a hybrid droplet comprising the transition metal oxide nanoparticle, a carbon-based compound and a conductive polymer from a composite slurry comprising a gas containing the transition metal oxide nanoparticle, a carbon-based compound and a conductive polymer; It provides a method of manufacturing a nanocomposite comprising the step of irradiating ultraviolet (ultraviolet, UV) to the hybrid droplets.

Another aspect of the present application is a spark ablation unit for producing a gas including transition metal oxide nanoparticles by irradiating plasma between a plurality of transition metal electrodes under a gas atmosphere; Slurry supply unit for supplying a composite slurry of a carbon-based compound and a conductive polymer; A mechanical injection unit that is fluidly connected to the spark ablation unit and the slurry supply unit, receives a gas including the transition metal oxide nanoparticles, and receives a composite slurry of the carbon-based compound and a conductive polymer, thereby producing a hybrid droplet ( mechanical spray); A UV irradiation unit fluidly connected to the mechanical injection unit and irradiating ultraviolet rays to the manufactured hybrid droplets; A reaction gas removal unit for removing reaction gas from the hybrid droplets irradiated with the ultraviolet rays; And a collection unit for collecting the nanocomposite from which the reaction gas is removed.

Another aspect of the present application provides a nanocomposite comprising a composite of transition metal oxide nanoparticles and a carbon-based matrix and a conductive polymer formed on the composite as a nanocomposite for the anode of a lithium battery.

Another aspect of the present application is an anode comprising a nanocomposite (anode); A cathode disposed opposite the anode; It provides a lithium battery comprising a; a separator disposed between the anode and the cathode, and an electrolyte interposed between the anode and the cathode.

According to one aspect of the present application, it is possible to provide a variable-structure plug and play nanocomposite.

According to an aspect of the present application, a nanocomposite for a lithium battery anode of various combinations may be provided.

According to one aspect of the present application, a nanocomposite for a lithium battery anode may be manufactured in a continuous process.

According to an aspect of the present application, an anode of a lithium battery may be provided using various combinations of transition metals according to a desired capacity of the lithium battery.

According to one aspect of the present application, it is possible to provide a lithium battery having excellent stability during charging and discharging cycling.

1 is a flow chart for a method of manufacturing a nanocomposite, which is an aspect of the present application.
2 is a schematic diagram of an apparatus for manufacturing a nanocomposite, which is an aspect of the present application.
3 is a schematic diagram of an apparatus for manufacturing a nanocomposite, which is an aspect of the present application.
4 is a schematic diagram of an apparatus for manufacturing a nanocomposite, which is an aspect of the present application.
5 is a graph of results for particle size distribution measurement.
6 is a graph of results for X-ray diffraction analysis.
7 is a graph of results for X-ray diffraction analysis.
8 is a graph of results for X-ray photoelectron spectroscopy.
9 is a graph of results for X-ray photoelectron spectroscopy.
10 is a graph of results for X-ray photoelectron spectroscopy.
11 is a graph of results for Raman spectrum analysis.
12 is a graph of results for Raman spectrum analysis.
13 is a graph of results for thermogravimetric analysis.
14 is a graph showing the result of measuring the absorbed volume and pore size.
15 is a graph showing the result of measuring the absorbed volume and pore size.
16 is a TEM image.
17 is a TEM image.
18 is an image of an element mapping analysis result.
19 is a graph showing the results of measuring the purified voltage current.
20 is a graph showing the results of measuring the charge and discharge efficiency of the battery.
21 is a graph showing the results of measuring the capacity for cycling.
22 is a graph showing the result of measuring the discharge capacity ratio.
23 is a graph showing the result of measuring the cost and Coulomb efficiency.
24 is a graph showing the result of measuring a specific amount.
25 is a TEM image.
26 is a TEM image.
27 is a graph showing the result of measuring a specific amount.
28 is a TEM image.
29 is a TEM image.

The terms used in the present application are only used to describe specific embodiments, and are not intended to limit the present invention. Singular expressions include plural expressions unless the context clearly indicates otherwise. In the present application, terms such as "include" or "have" are intended to designate the existence of features, components, and the like described in the specification, and one or more other features or components may not be present or added. It does not mean nothing.

Unless defined otherwise, all terms used herein, including technical or scientific terms, have the same meaning as commonly understood by a person skilled in the art to which the present invention pertains. Terms such as those defined in a commonly used dictionary should be interpreted as having meanings consistent with meanings in the context of related technologies, and should not be interpreted as ideal or excessively formal meanings unless explicitly defined in the present application. Does not.

As used herein, the term "nano" may mean a size in nanometer (nm) units, and may mean, for example, a size of 1 to 1,000 nm, but is not limited thereto. Further, the term "nanoparticle" as used herein may mean a particle having an average particle diameter in nanometer (nm) units, for example, a particle having an average particle diameter of 1 to 1,000 nm. , But is not limited thereto.

Plug and play, or PnP for short, means that it runs when plugged in, meaning that it works without any configuration even if you attach a peripheral device while the computer is running. As described above, the characteristics of the present application also include these characteristics, and thus the apparatus and method of the present application are referred to as a plug and play type.

Hereinafter, with reference to the accompanying drawings, an apparatus for manufacturing a nanocomposite of the present application, a method for manufacturing a nanocomposite, and a lithium battery including a nanocomposite and a nanocomposite prepared using the same will be described. The apparatus for manufacturing a nanocomposite of the present application, a method for manufacturing a nanocomposite, and a range of a lithium battery including a nanocomposite and a nanocomposite prepared using the same are not limited by the accompanying drawings.

1 is a flow chart for a method of manufacturing a nanocomposite according to an aspect of the present application.

As shown in FIG. 1, a method of manufacturing a nanocomposite according to an aspect of the present application includes preparing a gas containing transition metal oxide nanoparticles using spark ablation (S110), transition metal A gas containing oxide nanoparticles is used as a working gas, and from a composite slurry containing a carbon-based compound and a conductive polymer, a transition metal oxide nanoparticle, a carbon-based compound and a conductive polymer are included through a mechanical spray. It includes a step (S120) of manufacturing a hybrid droplet and the step (S130) of irradiating ultraviolet rays (ultraviolet, UV) to the hybrid droplet.

Hereinafter, each step will be described in more detail.

The step of preparing the gas containing the transition metal oxide nanoparticles is any one of spark ablation, arc discharge, chemical vapor synthesis, and flame synthesis. Can be performed by Here, a description will be given based on a method using spark ablation. However, the present application is not limited to the spark ablation method, and the gas containing the transition metal oxide nanoparticles may be manufactured using various methods described above.

First, a gas containing transition metal oxide nanoparticles is manufactured using spark ablation (S110).

Here, the spark ablation method may, for example, form a high-temperature atmospheric pressure plasma channel between two transition metal electrodes in a gas atmosphere in a plasma reactor, to prepare transition metal oxide nanoparticles through an evaporation-condensation process. .

In particular, when describing the manufacturing apparatus described later, spark ablation will be described in more detail. However, it is preferable to use such a manufacturing apparatus.

At this time, the transition metal may include any one or more of tin (Sn), copper (Cu), and cobalt (Co), but is not limited thereto. For example, SnO nanoparticles can be produced by using a tin electrode (for example, a diameter of 6.0 mm) and a tin electrode. In addition, by using a tin electrode and a copper electrode (for example, a diameter of 5.5 mm), SnO-CuO nanoparticles can be produced. In addition, by using a tin electrode and a cobalt electrode (for example, a diameter of 5.0 mm), SnO-Cu ₃ O ₄ nanoparticles can be produced.

Then, hybrid droplets are prepared. Here, the method of manufacturing the hybrid droplets may be performed by a mechanical spray method or an electrospray method. Here, a description will be given based on a method using a mechanical injection method. However, the present application is not limited to the mechanical spraying method, and hybrid droplets may be manufactured using various methods described above.

Specifically, the transition metal oxide nanoparticles, the carbon-based compound and the conductive polymer, using a gas containing the transition metal oxide nanoparticles as a working gas, from a composite slurry containing a carbon-based compound and a conductive polymer, through mechanical injection To prepare a hybrid droplet containing (S120).

Gas containing transition metal oxide nanoparticles is used as the working gas. These gases carry transition metal oxide nanoparticles, and are mixed with a composite slurry containing a carbon-based compound and a conductive polymer.

In addition, the carbon-based compound preferably contains any one or more of carbon nanotubes (T) and graphene nanosheets (S). In addition, it is preferable that the conductive polymer includes polyaniline (PANi).

It is preferable that the composite slurry contains a carbon-based compound and a conductive polymer in a solvent. As a solvent, it is preferable to use DMSO.

For example, a composite slurry contained in DMSO may be used as a carbon nanotube: graphene nanosheet: polyaniline = 4: 4: 2 by mass ratio.

The composite slurry is continuously supplied to the mechanical injection device using a peristaltic pump, and by the nozzle pressure of the mechanical injection device, transition metal oxide nanoparticles are mechanically inserted into the slurry droplet.

However, the mechanical injection device is not particularly limited, and any device can be used as long as the device can provide an effect as intended by the present application. However, it is preferable to use a mechanical injection device provided in the description of the manufacturing apparatus described later.

 Through this, a transition metal oxide-carbon matrix-conductive polymer hybrid droplet can be prepared.

Then, ultraviolet rays are irradiated to the hybrid droplets (S130).

However, the device for irradiating ultraviolet rays is not particularly limited, and any device can be used as long as the device can provide an effect as intended by the present application. However, it is preferable to use a device that irradiates ultraviolet rays provided in the description of the manufacturing apparatus described later.

By irradiating ultraviolet rays, the hybrid droplets can be cured and dried. For example, a UV lamp of 254 nm can be used. In addition, it may be in the form of a hollow tube containing silica-gel.

Through this, a nanocomposite containing a transition metal oxide in a carbon-based matrix is provided, and the nanocomposite has a form coated with a conductive polymer.

And, the above-described manufacturing method may further include the step of removing residual reaction gas from the hybrid droplet irradiated with ultraviolet rays. At this time, the residual reaction gas may be removed using a hollow tube filled with pelletized activated carbon.

In addition, the above-described manufacturing method may further include the step of collecting the nanocomposite from which the residual reaction gas has been removed.

Each step in the method of manufacturing a nanocomposite is combined with a roll-to-roll system or a conveyor system, allowing continuous production of the nanocomposite.

According to another aspect of the present application, an apparatus for manufacturing a nanocomposite is provided. 2 and 3 are schematic views of a device for manufacturing a nanocomposite, which is one aspect of the present application, respectively. In addition, FIG. 4 is also a schematic diagram of an apparatus for manufacturing a nanocomposite, which is an aspect of the present application.

As shown in FIG. 4, a composite of a spark ablation unit 10, a carbon-based compound, and a conductive polymer for irradiating plasma between a plurality of transition metal electrodes under a gas atmosphere to produce a gas including transition metal oxide nanoparticles The slurry supply unit 25 for supplying the slurry, the spark ablation unit 10, and the slurry supply unit 25 are respectively fluidly connected, receiving gas containing transition metal oxide nanoparticles, and combining the carbon-based compound and the conductive polymer Receiving a slurry, a mechanical injection unit 20 for manufacturing a hybrid droplet, fluidly connected to the mechanical injection unit 20, a UV irradiation unit 30 for irradiating ultraviolet rays to the hybrid droplets, a reaction gas from a hybrid droplet irradiated with ultraviolet rays It includes a reaction gas removing unit (not shown) for removing the and a collecting unit (not shown) for collecting the nanocomposite from which the reaction gas is removed.

The spark ablation unit may form a high-temperature atmospheric pressure plasma channel between two transition metal electrodes under a gas atmosphere, and thus produce transition metal oxide nanoparticles through an evaporation-condensation process.

In addition, through atmospheric pressure spark ablation between the two electrodes, a metal gas is generated under normal temperature gas, and the metal gas is formed into nano-sized transition metal oxide particles through nucleation-condensation. The nano-sized can prevent the volume of the transition metal oxide from changing or agglomerating during the charging and discharging cycles.

At this time, only one spark ablation unit may be included, but if necessary, two or more spark ablation units may be included. 3 shows a schematic view of an apparatus for manufacturing a nanocomposite including three spark ablation parts. Transition metal oxide nanoparticles of various combinations may be provided using a plurality of spark ablation units. At this time, it is preferable that the plurality of spark ablation parts are connected in parallel.

For example, if a tin electrode and a tin electrode are used, SnO nanoparticles can be produced. In addition, by using a tin electrode and a copper electrode, SnO-CuO nanoparticles can be produced. In addition, by using a tin electrode and a cobalt electrode, SnO-Cu ₃ O ₄ nanoparticles can be produced. Through various combinations of the above-described spark ablation unit, SnO and SnO-CuO nanoparticles, SnO and SnO-Cu ₃ O ₄ nanoparticles, and the like can be prepared.

Through this, it is possible to provide a custom-made manufacturing apparatus capable of easily selecting a combination desired by a user to be used as an anode of a lithium battery described later.

The thus prepared transition metal oxide nanoparticles are carried on a gas and moved to a mechanical injection unit. In addition, the composite slurry supplied from the slurry supply unit containing the carbon-based compound and the conductive polymer moves to the mechanical injection unit.

Using the pressure at the nozzle side of the mechanical injection unit, the transition metal oxide nanoparticles can be physically inserted into a slurry droplet containing a carbon-based compound and a conductive polymer to produce a hybrid droplet.

The UV irradiation unit may irradiate ultraviolet rays to the hybrid droplets to cure and dry the hybrid droplets.

In addition, the reaction gas removal unit removes the residual reaction gas from the hybrid droplets irradiated with ultraviolet rays, and the collection unit collects the nanocomposite from which the residual reaction gas is removed.

Here, it is preferable that each component is connected in series.

According to another aspect of the present application, for the anode of a lithium battery, there is provided a nanocomposite comprising a composite of transition metal oxide nanoparticles and a carbon-based matrix and a coating layer made of a conductive polymer formed on the composite.

Here, the transition metal may include any one or more of tin (Sn), copper (Cu), and cobalt (Co). In addition, the carbon-based matrix may include any one or more of carbon nanotubes and graphene nanosheets. The conductive polymer may be polyaniline (PANi).

Here, in the nanocomposite, the carbon-based matrix and the transition metal oxide nanoparticles are combined like an agglomerate, and the agglomerate is coated with a conductive polymer. Through this, it is possible to provide an anode material having excellent electrical properties.

This prevents unnecessary agglomeration or volume change of the transition metal oxide nanoparticles, and through the conductive polymer, it is possible to optimize the charge transfer between the transition metal oxide nanoparticle particles. In addition, when used as an anode of a lithium battery, stability can be greatly improved even during electrochemically cycling.

According to another aspect of the present application, an anode comprising the nanocomposite described above, a cathode disposed opposite to the anode, a separator disposed between the anode and the cathode, and an electrolyte interposed between the anode and the cathode; to provide.

Hereinafter, the present application will be described in more detail through examples and experimental examples.

[Experimental Example 1]

First, SnO ₂ and TS / PANi prepared using spark ablation were mixed to prepare SnO ₂ -TS / PANi.

Specifically, two Sn electrodes having a diameter of 6.0 mm were used, a high temperature atmospheric pressure plasma channel at 5000 ° C. was formed between the two electrodes, and SnO ₂ nanoparticles were prepared under an air flow rate of 1.57 L / min. Carbon nanotubes (T) (short with a double wall; Iljin Nanotech, Korea), graphene nanosheets (S) (Graphene Supermarket, USA) / PANi (Sigma-Aldrich, USA) slurry (solvent DMSO (Sigma-Aldrich, USA; mass ratio of T, S and PANi at 1% w / v ] is 4: 4: 2) droplets were prepared. Slurry was supplied using a peristaltic pump (JIH Pump, China), and SnO ₂ nanoparticles were injected into the slurry droplets using a spray device. The hybrid droplet was cured using a 254-nm UV lamp, and the hybrid droplet was dried using a silica gel hollow tube. After removing the residual gas, the nanocomposite was collected. In addition, except for T and S, SnO ₂ / PANi was prepared in a similar manner to the method described above.

The size distribution of SnO ₂ / PANi and SnO ₂ -TS / PANi was measured using a scanning mobility particle sizer (SMPS; 3936, TSI, USA). The results are shown in FIG. 5.

As shown in FIG. 5, each of PANi and TS / PANi including SnO ₂ NPs did not show a double- or multi-shape distribution, and showed one distribution. It was confirmed that SnO ₂ and PANi or SnO ₂ and TS / PANi were combined to form a complex even during the spraying process and the UV irradiation process.

In addition, as shown in the table inserted in FIG. 5, due to the additional binding of S, the increase in the geometric mean diameter (GMD) is the geometric standard deviation (GSD) and the total number concentration (total number concentration). , TNC).

In addition, the mass distribution of SnO ₂ , TS and PANi was measured using a piezobalance particle monitor (3522, Kanomax, Japan). As a result, it was measured to be 0.38, 0.48, and 0.14, respectively.

[Experimental Example 2]

Additional experiments were performed using SnO ₂ / PANi and SnO ₂ -TS / PANi prepared in Experimental Example 1. In addition, a control group, PANi alone, was also used.

)에서 넓은 밴드가 관측되었으며, 이는 PANi 결정질이 존재하는 것을 의미하였다. SnO₂ 또는 SnO₂-TS가 혼합됨에 따라서 밴드의 강도는 감소하였다. Cassiterite 구조를 갖는 정방정계 SnO₂의 피크 특징이 SnO₂/PANi에서 나타났으며, 이는 공기 분위기하에서 스파크 애블레이션이 결정질 SnO₂ NPs을 제조하는데 적절함을 증명하였다.Peak characteristics were observed through X-ray diffraction analysis (D / MAX-2500, Rigaku, Japan). The results are shown in FIG. 6. As shown in FIG. 65, in the case of PANi, ~ 25 ^o (2

), A wide band was observed, indicating that PANi crystalline was present. The strength of the band decreased as SnO ₂ or SnO ₂ -TS was mixed. The peak characteristics of the tetragonal SnO ₂ having a Cassiterite structure were seen in SnO ₂ / PANi, demonstrating that spark ablation under air atmosphere is suitable for preparing crystalline SnO ₂ NPs.

The average crystal size measured by the Scherrer equation was 3.9 nm, which was similar to the nano size effective to suppress severe volume change during the charge-discharge cycle.

In addition, although TS was mixed, the (110) band corresponding to TS was not measured, and the SnO ₂ peak was significantly weakened, and it was confirmed that this was due to interference from PANi coexisting with the interaction of SnO ₂ and TS. So, of SnO ₂ It was confirmed that both the crystallinity and the graphitization of TS were lowered.

These results meant that even when SnO ₂ , TS, or PANi was mixed, no relocation occurred, and the single-path complex was bound.

In addition, SnO ₂ -T / PANi and SnO ₂ -S / PANi were prepared in the same manner as described above. SnO ₂ -T / PANi and SnO ₂ -S / PANi were analyzed by X-ray diffraction analysis. 7 shows a result graph for X-ray diffraction analysis for SnO ₂ -T / PANi and SnO ₂ -S / PANi. Results similar to SnO ₂ -TS / PANi in FIG. 6 were shown.

[Experimental Example 3]

X-ray photoelectron spectroscopy (XPS; Axis-HIS, Kratos Analytical, Japan) was performed for SnO ₂ -TS / PANi and SnO ₂ / PANi, and the result graphs are shown in FIGS. 8 and 9. Shown.

As shown in Fig. 8, characteristic SnO ₂ spectra were matched. Carbon - characteristic bands for containing substituent (CC [284.8 eV], CO [286.2 eV], and OC = O [288.6 eV]) is, 495.6 corresponding to Sn ₃ d _3/2, and 3 d _5/2 was observed and the core-level band for SnO ₂ with 487.2 eV, was greatly extinguished. These results indicated that most of the SnO ₂ nanoparticles were located in the TS matrix, and were covered by PANi in the nanocomposite due to the capillary phenomenon of the voids in the TS matrix.

In addition, X-ray photoelectron spectroscopy was performed on SnO ₂ -T / PANi and SnO ₂ -S / PANi, and the result graph is shown in FIG. 10. Although the carbon matrix has a different configuration, it was confirmed that it has a structure similar to that shown in FIG. 8.

[Experimental Example 3]

Using a Raman spectroscopy method (Raman spectroscopy, XploRA Plus, Horiba, Japan), it was confirmed to what extent the carbon-based compounds on each surface of SnO ₂ -T / PANi and SnO ₂ -S / PANi were formed. As a result, the graph is shown in FIG. 11.

As shown in FIG. 11, bands corresponding to CN stretching and C = N stretching of imines of SnO ₂ / PANi were observed at ˜1360 cm ⁻¹ and 1430 cm ⁻¹ , respectively, and SnO ₂ -TS / For PANi, carbon peaks of typical graphite were observed at ~ 1330 cm ^-1 ( D band) and ~ 1580 cm ^-1 ( G band). Through this, it was confirmed that the surface of each sample was mostly made of a carbon-based compound.

In addition, Raman spectrum analysis was performed on SnO ₂ -T / PANi and SnO ₂ -S / PANi, and the result graph is shown in FIG. 12. As shown in FIG. 12, it was confirmed that results similar to those shown in FIG. 11 were shown.

[Experimental Example 4]

In order to confirm the rate of decomposition according to temperature, for each of SnO ₂ , SnO ₂ / PANi and SnO ₂ -TS / PANi, thermogravimetric analysis (TGA), Diamond TG in a nitrogen atmosphere at a range of 20-800 ° C. / DTA, Perkin Elmer, USA), and the resulting graph is shown in FIG. 13.

As shown in Figure 13, SnO ₂ -TS / PANi exhibited a weight loss of 26.2% with respect to the vaporization of the pyrolysable component. SnO ₂ / PANi showed a 16.4% loss compared to the weight ratio of PANi in SnO ₂ -TS / PANi using a piezobalance particle analyzer. There was no large mass loss after the high temperature treatment, which was due to UV curing and drying.

[Experimental Example 5]

Using a porosimeter (porosimeter, ASAP 2010, Micromeritics, USA), the dispersion degree of the volume and pore size absorbed in SnO ₂ -TS / PANi and SnO ₂ / PANi was measured. The resulting graph is shown in FIG. 14.

As shown in FIG. 14, SnO ₂ -TS / PANi has a significantly increased dispersion of absorbed volume and pore size compared to SnO ₂ / PANi, which TS forms a porous matrix, compensating for volumetric expansion, , It was possible to improve the transport of charges during electrochemical cycling.

In addition, the dispersion degree of the absorbed volume and pore size for SnO ₂ -T / PANi and SnO ₂ -S / PANi was measured. The resulting graph is shown in FIG. 15. As shown in FIG. 15, it has been confirmed that a configuration capable of performing a plug and play method is provided. SnO ₂ -TS / absorption PANi contours of the SnO ₂ -S / absorption contour of PANi than was observed also SnO ₂ -T / PANi absorption contours of similar. Through this, it was confirmed that T forms a backbone rather than S to form a nanocomposite.

[Experimental Example 6]

Transmission electron microscopy TEM (Tecnai G ² F20 S-TWIN, FEI, USA) was photographed with low and high magnification, SnO ₂ nanoparticles, and the images are shown in FIGS. 16A and 16B, respectively. As shown in FIG. 16A, SnO ₂ nanoparticles formed an aggregate of 4.4 ± 1.2 nm by Brownian motion, and the part corresponding to the middle layer of PANi was blurred. Through this, a process of UV curing and drying the SnO ₂ / PANi droplets was performed, and it was confirmed that the SnO ₂ nanoparticles were encapsulated by the PANi overlapping layer. As shown in Fig. 16B, the lattice stripes corresponding to the (110) plane of the tetragonal SnO ₂ were 0.33 nm.

In addition, using TEM, SnO ₂ -TS / PANi was photographed at low magnification and high magnification, and the images are shown in FIGS. 17A and 17B, respectively. As shown in FIG. 17A, when TS was included, the morphology was transformed into a three-dimensional aggregate, and SnO ₂ was hardly observed. Through this, it was confirmed that SnO ₂ penetrated into the TS matrix.

In addition, the pressure suddenly changes in the spray nozzle, so that the SnO ₂ nanoparticles are smashed into fine particles of SnO ₂ less than 10 nm, and the cohesive strength between the SnO ₂ fine particles in the aggregate is reduced. Fragmented SnO ₂ particles are dispersed between TS matrices, forming SnO ₂ -TS. And, SnO ₂ -TS is encapsulated by PANi, and through UV curing and drying, SnO ₂ -TS / PANi is formed.

As shown in FIG. 17B, two lattice stripes (0.33 nm (square SnO ₂ ) and 0.34 nm (graphite carbon)) were observed, and it was confirmed that SnO ₂ was redispersed in the TS matrix.

Through the redistribution of the fine-sized SnO ₂ described above, it was confirmed that it can be variously configured for a high-performance lithium energy storage device.

[Experimental Example 7]

Elemental mapping analysis for SnO ₂ -TS / PANi using energy-dispersive X-ray spectroscopy (EDX; JED-2300, JEOL, Japan) to further determine whether SnO ₂ penetrated into TS It was carried out, each image obtained is shown in Figure 18.

18, it was confirmed that SnO ₂ penetrated into TS.

[Experimental Example 8]

In order to test the performance of the nanocomposite of the present application as a material for the anode of a lithium battery, the following experiment was additionally performed.

The SnO ₂ -TS / PANi nanocomposite is mixed with carbon black (CB) and polyvinylidene fluoride (PVDF) (c: CB: PVDF in a mass ratio of 8: 1: 1) mixed with a solvent N- methylpyrrolidinone, and paste. After preparing (paste), it was uniformly coated on a Cu foil. It was dried in a vacuum oven at 75 ^o C for 24 hours. Lithium was selected as the counter electrode, and a polypropylene monolayer (2400, Celgard, USA) was used as a separator, and a solution of lithium hexafluorophosphate (746738, Sigma-Aldrich, USA) was used. Used as electrolyte. The entire manufacturing process of the coin cell was performed in a glovebox in an argon atmosphere.

The cyclic voltammetry (CV) values of the anodes up to the first 5 times were measured and are shown in FIG. 19. As shown in FIG. 19, ~ 0.93 V and 0.42 in a cathodic cycle corresponding to a period in which a solid electrolyte interphase (SEI) for reducing Li _x Sn from SnO ₂ to Sn and Li _x C is formed. V showed two peaks.

In the first anodic cycle, two broad bands were observed at ~ 1.3 V and 0.5 V corresponding to lithium released from Li _x Sn and Li _x C. In the next four cycles, no specific change was observed for the CV curve. Through this, it was confirmed that the anode manufactured by the above-described method can secure cycle stability.

[Experimental Example 9]

The efficiency was measured while charging-discharging, and shown in FIG. 20. As shown in FIG. 20, at a current density of 0.1 A g ⁻¹ , a coulomb efficiency of 71.6% was observed from the charge / discharge curve. Capacity loss was related to the SEI film formed on the SnO ₂ -TS / PANi anode containing Li ₂ O. In the subsequent cycle, the difference in charge / discharge capacity was greatly reduced, and the Coulomb efficiency increased to more than 97%.

[Experimental Example 10]

The constant current cycling performance of TS / PANi, SnO ₂ / PANi, and SnO ₂ -TS / PANi at a current density of 0.1 A g ⁻¹ was measured, and shown in FIG. 21.

As shown in FIG. 21, the decreasing cost gradually increased from the 20th cycle. After the 100th cycle, 840 mAh g ^-1 was reached, which is related to the thermal formation of Sn-N bonds on the surfaces of SnO ₂ and TS due to the interference of PANi, through which SnO ₂ particles are strongly adsorbed to the TS surface, It prevents the formation of aggregates of SnO ₂ .

During cycling, the stacked SnO ₂ -TS / PANi through thermal curing is redesigned because of improved contact between SnO ₂ -TS / PANi and the electrolyte.

In addition, the SnO ₂ -T / PANi and SnO ₂ -S / PANi anodes show results similar to those of FIG. 21 even if the cycling properties are changed according to the structure.

On the other hand, even if PANi is stacked on SnO ₂ nanoparticles, the specific amount of SnO ₂ / PANi decreases significantly during cycling, reaching 100 mAh g ⁻¹ after 100 th. Through this, not only, as well as to re-disperse the aggregates of SnO ₂ of mixing the TS, thereby preventing dispersion inhibitory effect of SnO ₂ nanoparticles during cycling.

Through these results, SnO ₂ in the matrix It was confirmed that the dispersibility of the nanoparticles is an important parameter in a material used as an anode.

[Experimental Example 11]

The discharge capability ratio of SnO ₂ -TS / PANi and SnO ₂ / PANi was measured, and is shown in FIG. 22. As shown in Figure 22, it was confirmed that the discharge capacity ratio of SnO ₂ -TS / PANi is inversely proportional to the current density. In addition, SnO ₂ -TS / PANi showed a significantly larger capacity compared to SnO ₂ / PANi. When the current density became the initial value (0.1 A g ^-1 ), the capacity could be recovered.

[Experimental Example 12]

To confirm the cycle stability of the SnO ₂ -TS / PANi anode, the specific capacity and coulomb efficiency were measured for 500 cycles at a current density of 0.5 A g ⁻¹ , and the resultant graph is shown in FIG. 23.

As shown in FIG. 23, after 500 cycles, the final capacity was constant at ˜840 mAh g ⁻¹ , and the coulomb efficiency was ˜100%, and through this, it was confirmed that excellent cycle stability could be secured.

In addition, in order to confirm the fine shape of the anode before and after 500 cycles, it was photographed using a scanning electron microscope (SEM; JSM-6500F, JEOL, Japan), and the image is shown in the insertion diagram of FIG. 23. Did.

As shown in the insertion diagram of FIG. 23, the structure before and after 500 cycles did not differ significantly, and through this, the complex of SnO ₂ -TS / PANi was suitable to accommodate the volume expansion of SnO ₂ nanoparticles during the cycle. I could confirm.

[Experimental Example 13]

The specific amounts of SnO ₂ -TS / PANi anode, SnO ₂ -T / PANi anode, and SnO ₂ -S / PANi anode for 120 cycles at a current density of 0.1 A g ⁻¹ were measured and shown in FIG. 24. In addition, TEM images of SnO ₂ -T / PANi anode and SnO ₂ -S / PANi anode are shown in FIGS. 25 and 26, respectively. In addition, by measuring the capacity at the current density for each is shown in Table 1 below.

Sample Current density (Ag ^-1 ) cycle Capacity (mAhg ^-1 ) SnO ₂ -TS / PANi 0.1 100 822 0.5 683 SnO ₂ -T / PANi 0.1 735 0.5 588 SnO ₂ -S / PANi 0.1 562 0.5 451

25 and 26, it was confirmed that the SnO ₂ -T / PANi aggregate and the SnO-S / PANi aggregate were similarly redispersed in the matrix.

[Experimental Example 14]

In the step of performing spark ablation among the above-described experimental examples, a Cu electrode or a Co electrode was used instead of the Sn electrode, and other experimental conditions were performed in the same manner, by performing additional experiments, SnO ₂ -CuO-TS / PANi anode and SnO-Co ₃ O ₄ -PANi anode were prepared.

A 0.1 g ^-1 and current density for 120 cycles SnO ₂ -TS / PANi anode, SnO ₂ -CuO-TS / PANi anode and shown in SnO-Co ₃ O ₄ 27 measures the specific capacity of the anode -PANi Did. In addition, TEM images of SnO ₂ -CuO-TS / PANi anode and SnO-Co ₃ O ₄ -PANi anode are shown in FIGS. 28 and 29, respectively. In addition, by measuring the capacity at the current density for each is shown in Table 2 below.

Sample Current density (Ag ^-1 ) cycle Capacity (mAhg ^-1 ) SnO ₂ -CuO-TS / PANi 0.1 100 958 0.5 769 SnO-Co ₃ O ₄ -PANi 0.1 885 0.5 704 SnO ₂ -TS / PANi 0.1 822 0.5 683

As shown in FIG. 27, the SnO ₂ -CuO-TS / PANi anode and the SnO-Co ₃ O ₄ -PANi anode have improved stability compared to the SnO ₂ -TS / PANi anode, which is co-dispersed in the TS matrix. CuO or Co ₃ O ₄ particles acted as catalysts to accelerate Li ₂ O decomposition and Sn oxidation during discharge. As shown in FIGS. 28 and 29, SnO ₂ -CuO aggregates and SnO- in the matrix It was confirmed that the Co ₃ O ₄ aggregates were similarly redispersed. Through this, it was confirmed that the series-connected spark ablation, mechanical spraying, and UV irradiation processes are suitable for re-assembleable plug and play for manufacturing a customized anode.

Although described above with reference to preferred embodiments of the present application, those skilled in the art may variously modify and change the present application without departing from the spirit and scope of the present invention described in the following claims. You will understand that you can.

1: Manufacturing device of nanocomposite
10: spark ablation section
20: mechanical injection
25: slurry supply
30: UV irradiation unit

Claims (17)

Preparing a gas containing transition metal oxide nanoparticles;
After mixing the gas containing the transition metal oxide nanoparticles into a composite slurry comprising a carbon-based compound and a conductive polymer, the transition metal oxide nanoparticles, carbon-based by a mechanical spray method or an electrospray method Preparing a hybrid droplet comprising a compound and a conductive polymer; And
And irradiating ultraviolet rays (ultraviolet, UV) to the hybrid droplets, thereby curing and drying the hybrid droplets to produce a nanocomposite,
The nanocomposite is a method of manufacturing a nanocomposite comprising a carbon-based matrix in which transition metal oxide nanoparticles are dispersed and a conductive polymer coating layer formed on the carbon-based matrix. The method of claim 1, wherein the transition metal comprises any one or more of tin (Sn), copper (Cu), and cobalt (Co). The method of claim 1, wherein the step of manufacturing the gas containing the transition metal oxide nanoparticles includes spark ablation, arc discharge, chemical vapor synthesis, and flame synthesis. synthesis) is a method for producing a nanocomposite. The method of claim 1, wherein the carbon-based compound comprises any one or more of carbon nanotubes and graphene nanosheets. The method of claim 1, wherein the conductive polymer is polyaniline (PANi). delete The method of claim 1, wherein the manufacturing method further comprises the step of removing the reaction gas from the ultraviolet-irradiated hybrid droplets and collecting the nanocomposite. According to claim 1, Each step in the manufacturing method of the nanocomposite is combined with a roll-to-roll (roll-to-roll) system or a conveyor system, the method of manufacturing a nanocomposite capable of continuous production of the nanocomposite. A spark ablation unit for irradiating plasma between a plurality of transition metal electrodes under a gas atmosphere to produce a gas including transition metal oxide nanoparticles;
Slurry supply unit for supplying a composite slurry of a carbon-based compound and a conductive polymer;
The spark ablation part and the slurry supply part are respectively fluidly connected, the gas containing the transition metal oxide nanoparticles is supplied, and the complex slurry of the carbon-based compound and the conductive polymer is continuously supplied using a peristaltic pump, and the hybrid liquid A mechanical spray to manufacture an enemy (mechanical spray);
A UV irradiation unit fluidly connected to the mechanical injection unit and irradiating ultraviolet rays to the prepared hybrid droplets to cure and dry the hybrid droplets;
A reaction gas removal unit for removing reaction gas from the hybrid droplets irradiated with the ultraviolet rays; And
It includes a collection unit for collecting the nano-composite from which the reaction gas is removed,
The nanocomposite is a device for manufacturing a nanocomposite comprising a carbon-based matrix in which transition metal oxide nanoparticles are dispersed and penetrated and a conductive polymer coating layer formed on the carbon-based matrix. The apparatus for manufacturing a nanocomposite according to claim 9, wherein the spark ablation unit, the mechanical injection unit, and the UV irradiation unit are connected in series. The apparatus for manufacturing a nanocomposite according to claim 9, wherein the spark ablation unit is a plurality of spark ablation devices connected in parallel. 10. The method of claim 9, The UV irradiation unit manufacturing apparatus of the nanocomposite to dry the solvent. For anode of lithium battery,
Nanocomposite comprising a carbon-based matrix in which transition metal oxide nanoparticles are dispersed and penetrated and a coating layer made of a conductive polymer formed on the carbon-based matrix. The nanocomposite of claim 13, wherein the transition metal comprises any one or more of tin (Sn), copper (Cu), and cobalt (Co). The nanocomposite of claim 13, wherein the carbon-based matrix comprises any one or more of carbon nanotubes and graphene nanosheets. The nanocomposite of claim 13, wherein the conductive polymer is polyaniline (PANi). An anode comprising the nanocomposite of any one of claims 13 to 16;
A cathode disposed opposite the anode;
A separator disposed between the anode and the cathode; And
A lithium battery comprising an electrolyte interposed between the anode and the cathode.

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