METHOD THEREOF

Field of the Invention

[001] The present invention relates to the technical area of electrochemical devices for obtaining and storing electrical energy. In particular, the present invention relates to an SBA-15/C anode for a lithium-ion battery and to a method of manufacturing said anode.

Background of the Invention

[002] Lithium-ion batteries (LIB) are widely used in electronic devices, electric vehicles, and for the storage of renewable energies such as photovoltaic and wind energies, among others. LIBs allow the storage of this energy for later use, being it possible to adapt them to different energy demand conditions.

[003] The current research work on LIBs is focused on obtaining high capacity anodes based on silicon (Si), since the theoretical capacity of said anodes is 3579 mAhg- ¹ , being significantly higher than that of graphite, which is more commonly used: 372 mAhg ^·1 . However, it is known that Si undergoes a significant process of volumetric expansion that causes a progressive pulverization and disconnection of electrical contact. This results in a loss of anode capacity during the first cycles of a LIB operation.

[004] The Si-metal-based anodes in a LIB undergo a volumetric expansion of approximately 300%, due to the formation of an alloy of general formula LixSiy. On the other hand, graphite undergoes a smaller expansion, of approximately 7%, as a consequence of an intercalation mechanism of Li ⁺ ions in the graphite layers. In the first case, the negative effect of this expansion has been partially solved using Si nanoparticles encapsulated in conductive carbon, or by reduction of pre synthesized S1O2 composites by magnesiothermal reduction.

[005] Patent application US 2017/260057 describes a process for the manufacture of nanoparticles of formula SiOx, where x is comprised between 0.8 and 1.2, by means of a fusion reaction between S1O2 and Si, at a temperature of at least 1410°C.

[006] The disadvantage of such strategies is the high cost of the process, since the reduction of S1O2 to Si has a high activation energy, and is therefore expensive. Additionally, the volumetric expansion of the Si particles thus formed represents a drawback on an industrial scale.

[007] Additionally, the charge/discharge capacity should be improved by an adequate ionic conductivity during the electrochemical process of Li ⁺ ion migration. To this end, the ionic and electrical conductivities of the electrode materials must be improved. In this way, the high specific capacity could be maintained, even at high current densities.

[008] Patent applications CN 106159222 and CN104701496 describe anodes for a LIB comprising a carbonaceous structure of high electrical conductivity, as well as Co and Sn nanoparticles. Although these anodes are manufactured from a material based on S1O2, said material is subsequently removed from the anodes. Application CN 104528740 is directed to a composite material comprising S1O2 and carbon, with a carbon content of less than 20%. None of these documents teaches or suggests the anodes and manufacturing methods of the present invention.

[009] Si02-based materials are attractive alternatives for the manufacture of Si- based anodes, since silica is one of the most abundant elements in Earth's crust and since S1O2 clays with complex porous nanostructures are well known. The synthesis of nanoporous materials from S1O2 is generally simple and inexpensive. In addition, these compounds could be used as a model material for complex natural clays, which could be used to store energy at a reduced cost. However, the main drawback of silica is the insulation characteristics thereof. Electron conduction is not possible with pure S1O2, thus limiting possible reduction to Si and other silicon products. The formation of said other products, in particular of LixSiy compounds, is decisive, since they provide ionic conductivity and allow limiting the volumetric expansion during the charging and discharging processes of a LIB. [010] There is therefore a need to provide an anode for a LIB that has improved electrical conductivity and volumetric expansion characteristics, and the manufacturing process of which is economically advantageous, compared to the existing alternatives of the prior art.

Summary of the Invention

[011] The present invention aims to solve the drawbacks of the prior art, by providing an anode for a LIB based on a composite material made from highly ordered S1O2, and including a conductive carbon structure, so as to improve ionic and electrical conductivities, thus avoiding long, complex and costly syntheses employed in similar inventions of the prior art.

[012] For this purpose, various mesoporous materials made from S1O2 can be used. By filling the pores of these materials with conductive carbon, conductivities are improved, since a conductive skeleton is generated that improves the conversion of S1O2 to Si and other products. Said other products are, in turn, advantageous during the operation of a LI B, since they mitigate the effect of the volumetric expansion during the lithiation process and improve the ionic diffusion of Li ⁺ .

[013] Accordingly, in one aspect of the present invention, it is an object thereof a composite material for lithium-ion battery anodes comprising a composite material comprising carbon nanofibers and S1O2. The composite material has a high carbon content, resulting in improved electrical conduction properties.

[014] In another aspect of the present invention, it is an object thereof an anode for a lithium-ion battery, comprising a composite material comprising carbon nanofibers and S1O2. The composite material has a high carbon content, resulting in improved electrical conduction properties thereof.

[015] In still another aspect, it is an object of the present invention a lithium-ion battery comprising an anode that comprises a composite material comprising carbon nanofibers and S1O2. [016] In an embodiment of said aspects of the present invention mentioned above, said composite material has a porous structure comprising mesopores interconnected by micropores, wherein said carbon nanofibers occupy the pore space of said porous structure.

[017] In another preferred embodiment of said above-mentioned aspects of the present invention, the carbon content in said composite material is about 45% by weight.

[018] In a preferred embodiment of said above-mentioned aspects of the present invention, said mesopores have a mean diameter of about 5 nm and said micropores have a mean diameter of about 1 nm.

[019] In a preferred embodiment of said aspects of the invention mentioned above, a chemical reduction reaction of S1O2 to Si occurs at said anode.

[020] In still another aspect of the present invention, it is an object thereof a method of manufacturing an anode for a lithium-ion battery according to the first aspect of the present invention, wherein the method comprises the steps of: a) providing a porous material from a S1O2 source,

b) impregnating said porous material with a solution comprising a carbon source and an acid, and

c) drying the porous material obtained in b).

[021] In one embodiment of said aspect of the present invention, said carbon source is sucrose.

[022] In one embodiment of said aspect of the present invention, said acid is sulfuric acid.

[023] In an embodiment of said aspect of the present invention, the drying stage c) is carried out at 900°C under an argon atmosphere.

[024] In still another aspect of the present invention, it is an object thereof an anode for a lithium battery obtained by the method of the invention. Brief Description of the Figures

[025] Figure 1 shows the nitrogen adsorption/desorption isotherms of synthesized materials and the hysteresis curves corresponding to the different porous structures of the materials obtained according to an exemplary embodiment of the present invention.

[026] Figure 2 shows the results of thermogravimetric analysis in air of a composite material according to an exemplary embodiment of the present invention.

[027] Figures 3a-3f show SEM micrographs of the materials obtained in an exemplary embodiment of the present invention.

[028] Figures 4a-4c show experimental results of electrochemical measurements performed on the composite material obtained in an exemplary embodiment of the present invention.

[029] Figures 5a-5b show the experimental results of electrochemical measurements performed on the composite material obtained in a first comparative experiment.

[030] Figures 6a-6b show the experimental results of electrochemical measurements performed on the composite material obtained in a second comparative experiment.

Detailed Description of the Invention

[031] The present invention will be described in detail below, with reference to the figures and examples, which are included only for the purpose of illustrating the invention and are not to be construed as limiting thereof.

[032] The term "approximately" as used herein when referring to a measurable value means that it comprises variations of ± 10% from the specified amount.

[033] As used herein, the terms "comprises", "has" and "includes" and their conjugations, mean "including but not limited to". [034] The anode for a lithium-ion battery of the present invention can be obtained from a starting porous material comprising S1O2, treated with a carbon source in order to obtain a composite material.

[035] In an embodiment of the invention, the starting porous material is a material made from S1O2 known as SBA-15. Said compound has a porous structure of mesopores interconnected by micropores.

[036] In order to obtain the composite material of the present invention, SBA-15 is impregnated with a solution of sucrose (carbon source) and sulfuric acid. Next, the material so obtained is dried and heat treated under an argon atmosphere at 900°C for 5 h, thus obtaining a mixed three-dimensional material comprising a carbonaceous structure formed by carbon nanofibers, said structure being surrounded by S1O2.

[037] The composite material thus formed is designated as SBA-15/C. The advantage of using this composite material as an anode in lithium-ion batteries lies in a surprising synergistic effect between S1O2 and the carbonaceous structure.

[038] Pure S1O2 has a high theoretical specific capacity of 950 mAhg- ¹ , related to the reduction of S1O2 to Si by reaction with Li during the charging of a lithium-ion battery. However, as it is an insulating material, it does not conduct electricity and has a capacitive response. Incorporation of a carbonaceous structure in the S1O2 material treated at high temperature, according to an embodiment of the present invention, generates an electronic and ionic conductive interface. For this reason, and from the thermodynamic point of view, during an electrochemical process S1O2 can incorporate electrical charge in the form of Li ⁺ ions and electrons, to be reduced to Si, according to the partial reactions (1) to (4):

(1) Theoretical capacity: 663 mAh g ^_1

(2) Theoretical capacity: 483 mAh g ^_1

(3) 2 Li ⁺ + 2e ^~ + Si0 ₂ ® i Li ₄ Si0 ₄ + ^Si Theoretical capacity: 679 mAh g ^_1

(4) 4Li ⁺ + 4e + Si0 ₂ ® 2 Li ₂ 0 + Si Theoretical capacity: 1 142 mAh g ^_1 [039] Once Si is formed according to the above partial reactions, Li storage can be produced according to the following partial reaction:

4Si + 15Li ⁺ + 15e- - > LiisSi ₄ (4) Theoretical capacity = 3579 mAhg- ¹

[040] The composite material SBA-15/C has a specific capacity of 450 mAhg ^·1 , superior to that of graphite commercially used in similar applications. Surprisingly, it is observed that it is possible to discharge the anode manufactured from the composite material at high current rates, without meaningfully changing its specific capacity.

[041] It should be noted that Argentina has soil rich in silicon oxide, as well as sucrose from sugar cane. For this reason, the composite material for the anode of the present invention can be obtained economically in the Argentine territory.

Example

Experimental method:

1) Synthesis of materials

[042] The SBA-15 material was synthesized according to the method reported by Zhao et al. (see e.g. Cano, L. A..; Garcia Blanco, A. A.; Lener, G.; Marchetti, S. G.; Sapag, K. Catal. Today 2016, Zhao, D.; Huo, Q.; Feng, J.; Chmelka, B. F.; Stucky, G. D. J. Am. Chem. Soc. 1998, 120, 6024-6036; Zhao, D. Science (80-J (1998), 279, 548-552)

[043] Pluronic triblock copolymer P123 (E020-P070-E020) was used as a structuring organic compound. 12 g of P123 were dissolved in 360 ml of ultra-pure water and 60 ml of 37% w/w HCI solution. The mixture was stirred for 3 h at 40°C until a clear solution was obtained. To this solution, 27 ml of tetraethylorthosilicate (TEOS) was added dropwise as a silica source. Once the TEOS was added, the mixture was allowed at 40°C under stirring for 24 h. The mixture was then allowed to age 24 h without stirring at 40°C. The solid was filtered and washed at room temperature with ultra-pure water. Then, the solid was dried at 80°C and calcined at 500°C for 6 h, using a heating ramp rate of 1 ⁰ C/min starting from room temperature.

[044] The synthesis of the composite material SBA-15/C was carried out by impregnation with a sucrose solution in sulfuric acid medium. A ratio of 2:1 sucrose/SBA-15 and 5 ml of ultra-pure water per gram of sucrose was used. The mixture SBA- 15/sucrose was stirred for 2 h, then 0.14 ml of H2SO4 (98% w/w) was added per ml of water and it was left under stirring for 1 h. The mixture was dried in air at 80°C for 6 h. Subsequently, a thermal treatment was carried out in a N2 inert atmosphere from room temperature up to 700°C for 5 h with a heating ramp rate of 2°C/min. The resulting sample was divided into two parts. One part was subjected to another thermal treatment at 900°C in a N2 inert atmosphere to obtain the composite material SBA-15/C. The other part was treated with NaOH at 60°C for 5 h in order to dissolve the S1O2 matrix. This carbonaceous structure was subjected to thermal treatment in N2 at 900°C for 5 h to obtain a material known as CMK-3 (see Shin, HJ, Ryoo, R.; Kruk, M.; Jaroniec, M. Chem. Commun. 1 , (2001), 349-350. The final temperature control is of utmost importance in order to desorb functional groups and obtain a material with optimal electrical conduction.

2) Characterization

[045] The adsorption/desorption isotherms were obtained with N2 at 77K using a Quantachrome Autosorb 1-MP equipment. Before making the measurements, samples were degassed in vacuum at 250°C for 12 h. The textural properties, such as specific surface area (S _g ), micropore volume (V _PP ), total pore volume (TPV) and pore size distribution (W _P ) were calculated from the experimental data; S _g and V _PP were obtained by the BET method and the as-plot method respectively. W _P was calculated using the VBS method (see Villarroel-Rocha, J.; Barrera, D.; Sapag, K. Microporous Mesoporous Mater. 200( 2014), 68-78). Thermogravimetric analysis was performed in air from room temperature to 1300°C to determine the S1O2/C ratio in the composite material.

3) Electrochemical measurements [046] The study of the electrochemical performance of the anodes was carried out with a Swagelok type T cell, using a metallic lithium disk of 8 mm in diameter as counter-electrode. The working electrode was prepared with the tested material, PVDF as binder and super P carbon as conductive material, in a 80:10:10 ratio. The mixture of the tested material was deposited on a copper foil as a current collector and dried at 80°C for 12 h.

Results:

1) Characterization

[047] Figure 1 shows the isotherms of nitrogen adsorption/desorption at 77 K of the synthesized materials. There, the hysteresis curves corresponding to the mesoporous structure can be observed. The slope at low relative pressures correspond to the microporous structure, characteristic of SBA-15 and CMK-3 materials.

[048] The mean diameter of mesopores was 8 nm and 5 nm for SBA-15 and CMK- 3 respectively, while the mean diameter of micropores was approximately 1 nm for both materials.

[049] As mentioned above, CMK-3 is obtained by filling pores of SBA-15 with a carbonaceous structure. Therefore, CMK-3 represents the inverse replica of SBA- 15. Therefore, having successfully obtained CMK-3 indicates that SBA-15/C material has pores filled with carbonaceous material.

[050] Figure 2 shows the thermogravimetric analysis of SBA-15/C in air. A mass loss of 45% at 600°C is observed due to decomposition of C to CO2. Therefore, the S1O2/C ratio in the material was 55/45. Therefore, the C content is significantly higher than that of the composite materials described in the prior art.

[051] Figures 3a-3f show SEM micrographs of SBA-15/C and CMK-3 in different magnifications. With respect to SBA-15, uniform particles of around 300 nm are observed (Figs. 3a and 3b) and the interlaminar S1O2/C structure can also be observed at nanometric scale (Fig. 3c). [052] On the other hand, SEM micrographs of CMK-3 show a particle size of 200 nm (Figs. 3d and 3e) and the characteristic nanometric interlaminate that generates the porous structure of the material (Fig. 3f).

2) Electrochemical Performance

[053] To determine the electrochemical performance of SBA-15/C, experiments were performed comparing SBA-15/C with carbonless SBA-15 and CMK-3, which is the carbonaceous structure of the composite material of the present invention. In all cases, for the preparation of the electrodes, the 80:10: 10 ratio was maintained between tested material, binder (PVDF) and super-P carbon, respectively. a) SBA-15/C

[054] As described above, composite material SBA-15/C is a three-dimensional array of S1O2 nanotubes of 8 nm in diameter interconnected by nanotubes of ca. 1 nm in diameter. The nanotubes are filled with carbon treated at 900°C in inert gas to obtain a conductive material so that the electrons can diffuse through the material to contact S1O2 and reduce it to generate Si in-operation. In addition, it should be mentioned that the metallic Si is semiconductor, so that the carbon coating allows maximizing the conductivity in charging/discharging processes.

[055] Figure 4a shows the specific capacity obtained from galvanostatic charge/discharge profiles of SBA-15/C as a function of the number of charge/discharge cycles performed. An irreversible initial charge capacity of 1300 mAhg- ¹ can be observed. From cycle number 2 and up to cycle number 300, a 450 mAhg ^·1 stable charge/discharge capacity is observed, with an average coulombic efficiency of 93%, calculated between cycles 3 and 300.

[056] Figure 4b shows the derivative of charge with respect to potential as a function of the potential. From this derivative, the processes that occur during charging/discharging can be observed. In charge cycle number 1 , a cathodic peak around 0.75 V is observed, corresponding to the formation of the solid/electrolyte interface (SEI) and also a wide peak near 0.1 V that can be attributed to the reduction from S1O2 to metallic Si and lithium silicate and lithium oxide, as indicated in partial reactions (1) to (4) above. In the anodic current of cycle number 1 , the peaks of a reversible process associated with delithiation can be observed. From cycle number 2, a potential peak of 0.45 V is observed in the cathodic current, corresponding to the reversible reduction of S1O2 and shoulders at lower potentials, probably due to the formation of Li-Si alloys, and peaks at 0.29, 0.48 and 0.8 V in the anodic current associated with delithiation processes.

[057] In Figure 4c one of the most important characteristics of the composite material of the present invention is shown: the discharge capacity at different discharge rates ("rate capability").

[058] In the first 5 cycles, the charging current was adjusted for the electrode to charge in 20 hours (C/20) and the discharge current was adjusted so that the electrode was discharged in 20 hours (C/20). There, the specific discharge capacity was 498 mAhg- ¹ . It should be noted that the composite material has a mass ratio S1O2/C of 55/45. Considering S1O2 as an active species and excluding from consideration the carbonaceous material, it can be concluded that the theoretical capacity of the material containing Si should be 905.5 mAhg ^·1 . If, on the other hand, a capacity of 250 mAhg ^·1 is attributed to the carbonaceous material (see results for CMK3 below), a theoretical capacity of 701 mAhg ^·1 is obtained for the material comprising silica.

[059] In the following points, the current was adjusted for a charge in 2 hours (C/2) and discharges at different rates. It can be observed that the capacity is little altered; it was even possible to discharge the electrode in 15 min maintaining a capacity of 400 mAhg ^·1 . This represents an important tool for application to high power batteries, such as those used in vehicles.

[060] The last set of points shows that the electrode was not altered after the previous experiments, since the discharge capacity at C/2 is maintained.

[061] To determine whether the electrochemical properties found correspond to a synergistic effect between the parts that make up the material, comparative experiments were carried out with SBA-15 without carbonizing and with the carbonaceous structure that is generated within the pores of SBA-15/C, i.e. the CMK-3 material. These comparative experiments will be detailed below. b) SBA-15

[062] The specific capacity obtained from galvanostatic charging/discharging profiles of SBA-15 without carbon is shown in Figure 5a. There, an initial irreversible charge capacity of 175 mAhg- ¹ can be observed in the first cycle. In the first discharge cycle the capacity was 30 Ahg ^·1 and then the capacity remained around 25 mAhg ¹ . This confirms the low energy storage capacity of SBA-15 in the absence of the carbonaceous material from the carbonization of sucrose.

[063] On the other hand, Figure 5b shows the derivative of charge with respect to potential for the same material. Peaks associated with irreversible processes are observed in the first charge cycle, probably due to the formation of SEI and other irreversible reductions, and then a pseudo-capacitive behavior is observed. b) CMK-3

[064] The carbonaceous matrix of the composite material SBA-15/C is called CMK- 3. As described above, this material has a porous structure of mesoporous nanotubes 5 nm in diameter, joined by microporous nanotubes of 1 nm in diameter.

[065] Figure 6a shows the specific capacity obtained from the galvanostatic charge/discharge profiles of CMK-3. An initial charge capacity of 3000 mAhg ^·1 (not shown in the graph due to scale issues) and an initial discharge capacity of 446 mAhg ^·1 showing an irreversible capacity of 2554 mAhg-1 were found. The charging and discharging values are stabilized after cycle number 50 and remain constant up to cycle number 100 in values of 250 mAhg ^·1 .

[066] Figure 6b shows the derivative of charge with respect to potential for the CMK3 material. Peaks of cathodic current at 0.68 and 0.9 V are found in cycle number one. These correspond to irreversible processes associated with the formation of the solid/electrolyte interface in the mesopores and in the micropores.

[067] It should be noted that this material has an apparent specific surface area of 1050 m ² /g, so the filling of pores with electrolyte results in a significant current consumption due to electrolyte decomposition and reduction of superficial functional groups which is evidenced in the high Initial specific capacity. [068] Subsequent cycles in the dQ/dE plot in Figure 6b do not show any specific lithium ion storage process, but rather an apparent pseudo-capacitive behavior of the material with good ion storage capacity, probably due to the charging of the double layer.

[069] The results obtained in the previous examples show a synergistic effect during use of composite material SBA-15/C as an anode. The conductive material obtained allows the in-operation reduction of S1O2 to Si. Without wishing to be bound to theory, it can be considered that the underlying carbon structure functions as a connecting tree, which allows the access of electrons to most of the S1O2 matrix, allowing its massive reduction. The existence of reversible processes at low potentials suggests that Si would store Li ions through the formation of Li-Si alloys, showing a high capacity and power and great recyclability, which would have important economic incidences in the manufacture of batteries.

[070] As mentioned above, in the prior art, Si-anodes have been proposed that must be obtained by previous reduction of S1O2. This reduction process is an activated process that requires high temperatures and/or drastic reducing agents, and so it is expensive.

[071] The method of the present invention is an economically favorable alternative, since it does not involve any of the mentioned extreme conditions.

[072] Those skilled in the art will recognize or may determine, using only routine experimentation, many equivalents of the specific procedures, embodiments, claims and examples described herein. Said equivalents are considered to be within the scope of the present invention and covered by the appended claims.