Abstract:
Nanocomposite materials comprising a metal oxide bonded to at least one graphene material. The nanocomposite materials exhibit a specific capacity of at least twice that of the metal oxide material without the graphene at a charge/discharge rate greater than about 10 C.

Description:
CROSS REFERENCE TO RELATED APPLICATIONS 
     This is a Divisional of U.S. patent application Ser. No. 13/559,528, filed Jul. 26, 2012, which is a Divisional of U.S. patent application Ser. No. 12/460,993, filed Jul. 27, 2009, now U.S. Pat No. 8,257,867, which claims the benefit of U.S. Provisional Patent Application No. 61/084,140, filed Jul. 28, 2008, entitled Metal Oxide-Graphene Hybrid Nanostructures and Method of Making, all of which are hereby incorporated by reference. 
    
    
     The invention was made with Government support under Contract DE-AC0676RLO 1830, awarded by the U.S. Department of Energy. The Government has certain rights in the invention. 
    
    
     TECHNICAL FIELD 
     This invention relates to nanocomposite materials of graphene bonded to metal oxides and methods for forming nanocomposite materials of graphene bonded to metal oxides. 
     BACKGROUND OF THE INVENTION 
     Graphene is generally described as a one-atom-thick planar sheet of sp2-bonded carbon atoms that are densely packed in a honeycomb crystal lattice. The carbon-carbon bond length in graphene is approximately 0.142 nm. Graphene is the basic structural element of some carbon allotropes including graphite, carbon nanotubes and fullerenes. Graphene exhibits unique properties, such as very high strength and very high conductivity. Those having ordinary skill in the art recognize that many types of materials and devices may be improved if graphene is successfully incorporated into those materials and devices, thereby allowing them to take advantage of graphene&#39;s unique properties. Thus, those having ordinary skill in the art recognize the need for new methods of fabricating graphene and composite materials that incorporated graphene. 
     Graphene has been produced by a variety of techniques. For example, graphene is produced by the chemical reduction of graphene oxide, as shown in Gomez-Navarro, C.; Weitz, R. T.; Bittner, A. M.; Scolari, M.; Mews, A.; Burghard, M.; Kern, K. Electronic Transport Properties of Individual Chemically Reduced Graphene Oxide Sheets. and  Nano Lett.  2007, 7, 3499-3503. Si, Y.; Samulski, E. T. Synthesis of Water Soluble Graphene.  Nano Lett.  2008, 8, 1679-1682. 
     While the resultant product shown in the forgoing methods is generally described as graphene, it is clear from the specific capacity of these materials that complete reduction is not achieved, because the resultant materials do not approach the theoretical specific capacity of neat graphene. Accordingly, at least a portion of the graphene is not reduced, and the resultant material contains at least some graphene oxide. As used herein, the term “graphene” should be understood to encompass materials such as these, that contain both graphene and small amounts of graphene oxide. 
     For example, functionalized graphene sheets (FGSs) prepared through the thermal expansion of graphite oxide as shown in McAllister, M. J.; LiO, J. L.; Adamson, D. H.; Schniepp, H. C.; Abdala, A. A.; Liu, J.; Herrera-Alonso, M.; Milius, D. L.; CarO, R.; Prud&#39;homme, R. K.; Aksay, I. A. Single Sheet Functionalized Graphene by Oxidation and Thermal Expansion of Graphite.  Chem. Mater.  2007, 19, 4396-4404 and Schniepp, H. C.; Li, J. L.; McAllister, M. J.; Sal, H.; Herrera-Alonso, M.; Adamson, D. H.; Prud&#39;homme, R. K.; Car, R.; Saville, D. A.; Aksay, I. A. Functionalized Single Graphene Sheets Derived from Splitting Graphite Oxide.  J. Phys. Chem. B  2006, 110, 8535-8539 have been shown to have tunable C/O ratios ranging from 15 to 500. The term “graphene” as used herein should be understood to include both pure graphene and graphene with small amounts of graphene oxide, as is the case with these materials. 
     Further, while graphene is generally described as a one-atom-thick planar sheet densely packed in a honeycomb crystal lattice, these one-atom-thick planar sheets are typically produced as part of an amalgamation of materials, often including materials with defects in the crystal lattice. For example, pentagonal and heptagonal cells constitute defects. If an isolated pentagonal cell is present, then the plane warps into a cone shape. Likewise, an isolated heptagon causes the sheet to become saddle-shaped. When producing graphene by known methods, these and other defects are typically present. 
     The IUPAC compendium of technology states: “previously, descriptions such as graphite layers, carbon layers, or carbon sheets have been used for the term graphene . . . it is not correct to use for a single layer a term which includes the term graphite, which would imply a three-dimensional structure. The term graphene should be used only when the reactions, structural relations or other properties of individual layers are discussed”. Accordingly, while it should be understood that while the terms “graphene” and “graphene layer” as used in the present invention refers only to materials that contain at least some individual layers of single layer sheets, the terms “graphene” and “graphene layer” as used herein should therefore be understood to also include materials where these single layer sheets are present as a part of materials that may additionally include graphite layers, carbon layers, and carbon sheets. 
     The unique electrical and mechanical properties of graphene have led to interest in its use in a variety of applications. For example, electrochemical energy storage has received great attention for potential applications in electric vehicles and renewable energy systems from intermittent wind and solar sources. Currently, Li-ion batteries are being considered as the leading candidates for hybrid, plug-in hybrid and all electrical vehicles, and possibly for utility applications as well. However, many potential electrode materials (e.g., oxide materials) in Li-ion batteries are limited by slow Li-ion diffusion, poor electron transport in electrodes, and increased resistance at the interface of electrode/electrolyte at high charging-discharging rates. 
     To improve the charge-discharge rate performance of Li-ion batteries, extensive work has focused on improving Li-ion and/or electron transport in electrodes. The use of nanostructures (e.g., nanoscale size or nanoporous structures) has been widely investigated to improve the Li-ion transport in electrodes by shortening Li-ion insertion/extraction pathway. In addition, a variety of approaches have also been developed to increase electron transport in the electrode materials, such as conductive coating (e.g., carbon), and uses of conductive additives (e.g., conductive oxide wires or networks, and conductive polymers). Recently, TiO 2  has been extensively studied to demonstrate the effectiveness of nanostructures and conductive coating in these devices. 
     TiO 2  is particularly interesting because it is an abundant, low cost, and environmentally benign material. TiO 2  is also structurally stable during Li-insertion/extraction and is intrinsically safe by avoiding Li electrochemical deposition. These properties make TiO 2  particularly attractive for large scale energy storage. 
     Another way to improve the Li-ion insertion properties is to introduce hybrid nanostructured electrodes that interconnect nanostructured electrode materials with conductive additive nanophases. For example, hybrid nanostructures, e.g., V 2 O 5 — carbon nanotube (CNT) or anatase TiO 2 -CNT hybrids, LiFePO 4 —RuO 2  nanocomposite, and anatase TiO 2 —RuO 2  nanocomposite, combined with conventional carbon additives (e.g., Super P carbon or acetylene black) have demonstrated an increased Li-ion insertion/extraction capacity in the hybrid electrodes at high charge/discharge rates. 
     While the hybrids or nanocomposites offer significant advantages, some of the candidate materials to improve the specific capacity, such as RuO 2  and CNTs, are inherently expensive. In addition, conventional carbon additives at high loading content (e.g., 20 wt % or more) are still needed to ensure good electron transport in fabricated electrodes. To improve high-rate performance and reduce cost of the electrochemically active materials, it is important to identify high surface area, inexpensive and highly conductive nanostructured materials that can be integrated with electrochemical active materials at nanoscale. 
     Those having ordinary skill in the art recognize that graphene may be the ideal conductive additive for applications such as these hybrid nanostructured electrodes because of its high surface area (theoretical value of 2630 m 2 /g), which promises improved interfacial contact, the potential for low manufacturing cost as compared to CNTs, and high specific capacity. Recently, high-surface-area graphene sheets were studied for direct Li-ion storage by expanding the layer spacing between the graphene sheets as described in Yoo, E.; Kim, J.; Hosono, E.; Zhou, H.-s.; Kudo, T.; Honma, I. Large Reversible Li Storage of Graphene Nanosheet Families for Use in Rechargeable Lithium Ion Batteries,  Nano Lett.  2008, 8, 2277-2282. In addition to these studies, graphene has also been used to form composite materials with SnO 2  for improving capacity and cyclic stability of the anode materials as described in Paek, S.-M.; Yoo, E.; Honma, I. Enhanced Cyclic Performance and Lithium Storage Capacity of SnO 2 /Graphene Nanoporous Electrodes with Three-Dimensionally Delaminated Flexible Structure,  Nano Lett.  2009, 9, 72-75. 
     While these results were promising, they fell short of producing materials exhibiting specific capacity approaching the theoretical possibilities. For example, while it has been shown that graphene may be combined with certain metal oxides, the graphene materials in these studies fall far short of the theoretical maximum conductivity of single-sheet graphene. Further, those having ordinary skill in the art recognize that the carbon:oxygen ratio and the specific surface area of graphene provide an excellent proxy to measure the relative abundance of high conductivity single-sheets in a given sample. This is because the C:O ratio is a good measure of the degree of “surface functionalization” which affects conductivity, and the surface area conveys the percentage of single-sheet graphene in the synthesized powder. 
     Accordingly, those having ordinary skill in the art recognize that improvements to these methods are required to achieve the potential of using graphene nanostructures in these and other applications. Specifically, those skilled in the art recognize the need for new methods that produce nanocomposite materials of graphene and metal oxides that exhibit greater specific capacity than demonstrated in these prior art methods. 
     The present invention fulfills that need, and provides such improved composite nanostructures of graphene layers and metal oxides that exhibit specific capacities heretofore unknown in the prior art. The present invention further provides improved and novel methods for forming these composite nanostructures, and improved and novel devices that take advantage of the new and unique properties exhibited by these materials. The present invention meets these objectives by making nanostructures of graphene layers and metal oxides where the C:O ratio of the graphene layers in these nanostructures is between 15-500:1, and preferably 20-500:1, and the surface area of the graphene layers in these nanostructures is 400-2630 m2/g, and preferably 600-2630 m2/g, as measured by BET nitrogen adsorption at 77K. While those having ordinary skill in the art have recognized the desirability of having C:O ratios and surface areas this high in the graphene of nanostructures of graphene and metal oxides, the prior art methods have failed to produce them. 
     SUMMARY OF THE INVENTION 
     The present invention thus includes a nanocomposite material comprising a metal oxide bonded to at least one graphene layer. The metal oxide is preferably M x O y , and where M is selected from the group consisting of Ti, Sn, Ni, Mn, V, Si, Co and combinations thereof. The nanocomposite materials of the present invention are readily distinguished from the prior art because they exhibit a specific capacity of at least twice that of the metal oxide material without the graphene at a charge/discharge rate greater than about 10 C. 
     For example, while not meant to be limiting, an example where titania is used as the metal oxide, the resulting nanocomposite material has a specific capacity at least twice that of a titania material without graphene at a charge/discharge rate greater than about 10 C. Continuing the example, where titania is used as the metal oxide, the titania may be provided in a mesoporous form, and the mesoporous titania may further be provided in a rutile crystalline structure, or in an anatase crystalline structure. 
     The nanocomposite material of the present invention preferably is provided as graphene layers with metal oxides uniformly distributed throughout the nanoarchitecture of the layers. Preferably, but not meant to be limiting, the nanocomposite material of the present invention provides a metal oxide bonded to at least one graphene layer that has a thickness between 0.5 and 50 nm. More preferably, but also not meant to be liming, the nanocomposite material of the present invention provides a metal oxide bonded to at least one graphene layer that has a thickness between 2 and 10 nm. Preferably, the carbon to oxygen ratio (C:O) of the graphene in the nanostructures of the present invention is between 15-500:1, and more preferably between 20-500:1. Preferably, the surface area of the graphene in the nanostructures of the present invention is between 400-2630 m2/g, and more preferably between 600-2630 m2/g, as measured by BET nitrogen adsorption at 77K. 
     Another aspect of the present invention is a method for forming the nanocomposite materials of graphene bonded to metal oxide. The method consists of the steps of providing graphene in a first suspension; dispersing the graphene with a surfactant; adding a metal oxide precursor to the dispersed graphene to form a second suspension; and precipitating the metal oxide from the second suspension onto at least one surface of the dispersed graphene. In this manner, a nanocomposite material of at least one metal oxide bonded to at least one graphene layer is thereby formed. The nanocomposite materials formed in this manner are readily distinguished from materials formed by prior art methods because they exhibit a specific capacity of at least twice that of the metal oxide material without the graphene at a charge/discharge rate greater than about 10 C. 
     Preferably, but not meant to be limiting, the first suspension is, at least in part, an aqueous suspension and the surfactant is an anionic surfactant. Also not meant to be limiting, a preferred anionic sulfate surfactant is sodium dodecyl sulfate. The method of the present invention may further comprise the step of heating the second suspension from 50 to 500 degrees C. to condense the metal oxide on the graphene surface. The method of the present invention may also further comprise the step of heating the second suspension from 50 to 500 degrees C. to remove the surfactant. 
     The present invention also encompasses an energy storage device comprising a nanocomposite material having an active metal oxide compound and one graphene layer arranged in a nanoarchitecture. The energy storage devices of the present invention are readily distinguished from prior art energy storage devices because they exhibit a specific capacity of at least twice that of the metal oxide material without the graphene at a charge/discharge rate greater than about 10 C. 
     For example, while not meant to be limiting, an example where titania is used as the metal oxide, the energy storage device of the present invention has a specific capacity at least twice that of a titania material without graphene at a charge/discharge rate greater than about 10 C. 
     Preferably, but not meant to be limiting, the energy storage device of the present invention is provided as having at least one component having a nanocomposite material having graphene layers with metal oxides uniformly distributed throughout the nanoarchitecture of the layers. Also preferably, but not meant to be limiting, the energy storage device of the present invention is an electrochemical device having an anode, a cathode, an electrolyte, and a current collector, wherein at least one of the anode, cathode, electrolyte, and current collector is fabricated, at least in part, from a nanocomposite material having graphene layers with metal oxides uniformly distributed throughout the nanoarchitecture of the layers. 
     In embodiments where the energy storage device of the present invention includes a cathode fabricated, at least in part, from a nanocomposite material having graphene layers with metal oxides uniformly distributed throughout the nanoarchitecture of the layers, the graphene in the cathode is preferably, but not meant to be limiting, 5% or less of the total weight of the cathode, and more preferably, but also not meant to be limiting, 2.5% or less of the total weight of the cathode. In this manner, the energy storage devices of the present invention are distinguished from prior art devices which are characterized by having more than 5% of the total weight of the cathode as carbon with no graphene. 
     In embodiments where the energy storage device of the present invention includes an anode fabricated, at least in part, from a nanocomposite material having graphene layers with metal oxides uniformly distributed throughout the nanoarchitecture of the layers, the graphene in the anode is preferably, but not meant to be limiting, 10% or less of the total weight of anode, and more preferably, but also not meant to be limiting, 5% or less of the total weight of anode. In this manner, the energy storage devices of the present invention are distinguished from prior art devices which are characterized by having more than 10% of the total weight of the anode as carbon with no graphene. 
     One embodiment where the present invention is an energy storage device is as a lithium ion battery. In this embodiment, the lithium ion battery has at least one electrode with at least one graphene layer bonded to titania to form a nanocomposite material, and the nanocomposite material has a specific capacity at least twice that of a titania material without graphene at a charge/discharge rate greater than about 10 C. The electrode of this lithium ion battery may further have multiple nanocomposite material layers uniformly distributed throughout the electrode. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
       The following detailed description of the embodiments of the invention will be more readily understood when taken in conjunction with the following drawing, wherein: 
         FIG. 1  is a schematic illustration of the present invention showing anionic sulfate surfactant mediated stabilization of graphene and growth of TiO 2 -FGS hybrid nanostructures. 
         FIG. 2  is a graph showing high energy resolution photoemission spectra of the C  1   s  region in functionalized graphene sheets (FGS) used in one embodiment of the present invention. 
         FIG. 3  are Raman spectra of rutile TiO 2 -FGS and FGS in one embodiment of the present invention. 
         FIG. 4(   a ) is a photograph of FGS (left) and SDS-FGS aqueous dispersions (right);  FIG. 4(   b ) is a graph of the UV-Vis absorbance of the SDS-FGS aqueous dispersion. 
         FIG. 5  is an XRD pattern of one embodiment of the present invention, an anatase TiO 2 -FGS and rutile TiO 2 -FGS hybrid material. Standard diffraction peaks of anatase TiO 2  (JCPDS No. 21-1272) and rutile TiO 2  (JCPDS No. 21-1276) are shown as vertical bars. 
         FIG. 6(   a )-( g ) are TEM and SEM images of the nanocomposite materials of various embodiments of the present invention at selected magnifications. 
         FIG. 7(   a )-( f ) are graphs showing the electrical performance of one embodiment of the present invention.  FIG. 7(   a ) shows the voltage profiles for control rutile TiO 2  and rutile TiO 2 -FGS (0.5 wt % FGS) hybrid nanostructures at C/5 charge-discharge rates.  FIG. 7(   b ) shows the specific capacity of control rutile TiO 2  and the rutile TiO 2 -FGS hybrids at different charge/discharge rates; 
         FIG. 7(   c ) shows the cycling performance of the rutile TiO 2 -FGS up to 100 cycles at 1 C charge/discharge rates after testing at various rates shown in  FIG. 7(   b ).  FIG. 7(   d ) shows the voltage profiles for control anatase TiO 2  and anatase TiO 2 -FGS (2.5 wt % FGS) hybrid nanostructures at C/5 charge-discharge rates.  FIG. 7(   e ) shows the specific capacity of control anatase TiO 2  and the anatase TiO 2 -FGS hybrids at different charge/discharge rates;  FIG. 7(   f ) shows the cycling performance of the anatase TiO 2 -FGS up to 100 cycles at 1 C charge/discharge rates after testing at various rates shown in  FIG. 7(   e ). 
         FIG. 8  is a graph showing a plot of coulombic efficiency versus cycle number of TiO 2 -FGS hybrids of one embodiment of the present invention at various charge/discharge rate between 1˜3 V vs. Li/Li + . 
         FIG. 9  is a graph showing the capacity of functionalized graphene sheets of one embodiment of the present invention as function of cycling numbers between 1˜3 V vs. Li/Li + . 
         FIG. 10(   a ) is a graph showing the impedance measurement of coin cells using the electrode materials of control rutile TiO 2  and rutile TiO 2 -FGS hybrids with different weight percentage of FGSs.  FIG. 10(   b ) is a graph showing the specific capacity of rutile TiO 2 -CNT and rutile TiO 2 -FGS at 30 C rate with different percentages of graphene. 
         FIG. 11  is a graph showing the specific capacity of control rutile TiO 2  (10 wt % Super P) and rutile TiO 2 -FGS hybrids (10 wt % FGS) at different charge/discharge rates. The rutile TiO 2 -FGS hybrid electrode was prepared by mixing the calcined hybrid with PVDF binder at a mass ratio of 90:10. The control TiO 2  electrode was prepared by mixing control TiO 2  powder, Super P and PVDF binder at a mass ratio of 80:10:10. 
         FIG. 12  is an SEM image of TiO 2 /FGS hybrid materials made in one embodiment of the present invention without using SDS as a stabilizer. As shown, TiO 2  and FGS domains are separated from each other with minor TiO 2  coated on FGS. 
     
    
    
     DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS 
     For the purposes of promoting an understanding of the principles of the invention, reference will now be made to the embodiments illustrated in the drawings and specific language will be used to describe the same. It will nevertheless be understood that no limitations of the inventive scope is thereby intended, as the scope of this invention should be evaluated with reference to the claims appended hereto. Alterations and further modifications in the illustrated devices, and such further applications of the principles of the invention as illustrated herein are contemplated as would normally occur to one skilled in the art to which the invention relates. 
     A series of experiments were conducted to demonstrate certain embodiments of the present invention. In these experiments, anionic sulfate surfactants were used to assist the stabilization of graphene in aqueous solutions and facilitate the self-assembly of in-situ grown nanocrystalline TiO 2 , rutile and anatase, with graphene. These nanostructured TiO 2 -graphene hybrid materials were then used for investigation of Li-ion insertion properties. The hybrid materials showed significantly enhanced Li-ion insertion/extraction in TiO 2 . The specific capacity was more than doubled at high charge rates, as compared with the pure TiO 2  phase. The improved capacity at high charge-discharge rate may be attributed to increased electrode conductivity in the presence of a percolated graphene network embedded into the metal oxide electrodes. While not to be limiting, these are among the features that distinguish the methods, materials, and devices of the present invention from the prior art. 
     These experiments thereby demonstrated that the use of graphene as a conductive additive in self-assembled hybrid nanostructures enhances high rate performance of electrochemical active materials. While the metal oxide TiO 2  was selected as a model electrochemical active oxide material, the method of the present invention is equally applicable to all metal oxides. 
     These experiments utilized a one-step synthesis approach to prepare metal oxide-graphene hybrid nanostructures. In these experiments, the reduced and highly conductive form of graphene is hydrophobic and oxides are hydrophilic. The present invention&#39;s use of surfactants not only solved the hydrophobic/hydrophilic incompatibility problem, but also provides a molecular template for controlled nucleation and growth of the nanostructured inorganics, resulting in a uniform coating of the metal oxide on the graphene surfaces. 
     This approach, schematically illustrated in  FIG. 1 , starts with the dispersion of the graphene layers with an anionic sulfate surfactant. For example, but not meant to be limiting, sodium dodecyl sulfate. The method then proceeds with the self-assembly of surfactants with the metal oxide precursor and the in-situ precipitation of metal oxide precursors to produce the desired oxide phase and morphology. 
     In a typical preparation of rutile TiO 2 -FGS hybrid materials (e.g., 0.5 wt % FGS), 2.4 mg FGSs and 3 mL SDS aqueous solution (0.5 mol/L) were mixed together. The mixture was diluted to 15 mL and sonicated for 10-15 min using a BRANSON SONIFER S-450A, 400W. 25 mL TiCl 3  (0.12 mol/L) aqueous solution was then added into as-prepared SDS-FGS dispersions while stirring. Then, 2.5 mL H 2 O 2  (1 wt %) was added dropwise followed by de-ionized water under vigorous stirring until reaching a total volume of 80 mL. In a similar manner, 0.8, 26.4, and 60 mg FGSs were used to prepare the hybrid materials with 0.17, 5, and 10 wt % FGS, respectively. 
     Rutile TiO 2 -CNT (0.5 wt % carbon nanotubes) hybrid materials were also prepared using corresponding single-wall CNTs (2.4 mg) according to the above method. 
     In a typical preparation of anatase TiO 2 -FGS hybrid materials (e.g., 2.5 wt % FGS), 13 mg FGS and 0.6 mL SDS aqueous solution (0.5 mol/L) were mixed and sonicated to prepare an SDS-FGS dispersion. 25 mL TiCl 3  (0.12 mol/L) aqueous solution was added into as-prepared SDS-FGS dispersions while stirring followed by the addition of 5 mL 0.6 M Na 2 SO 4 . 2.5 mL H 2 O 2  (1 wt %) was then added dropwise followed by addition of de-ionized water under vigorous stirring until reaching a total volume of 80 mL. 
     All of these resulting mixtures were further stirred in a sealed polypropylene flask at 90° C. for 16 h. The precipitates were separated by centrifuge followed by washing with de-ionized water and ethanol. The centrifuging and washing processes were repeated 3 times. The product was then dried in a vacuum oven at 70° C. overnight and subsequently calcined in static air at 400° C. for 2 h. 
     The thermal gravimetric analysis (TGA) indicated approximately 50 wt % percentage loss of FGSs during calcination in air at 400° C. for 2 h. The weight percentage of the graphene in the hybrid materials was thus correspondingly normalized, which is consistent with TGA of the hybrid materials. 
     The samples were characterized by XRD patterns obtained on a Philips Xpert X-ray diffractometer using Cu K α  radiation at λ=1.54 Å. The TEM imaging was performed on a JEOL JSM-2010 TEM operated at 200 kV. SEM images were obtained on an FEI Helios Nanolab dual-beam focused ion beam/scanning electron microscope (FIB/SEM) operated at 2 kV. XPS characterization was performed using a Physical Electronics Quantum 2000 Scanning ESCA Microprobe with a focused monochromatic Al K α  X-ray (1486.7 eV) source and a spherical section analyzer. Electrochemical experiments were performed with coin cells (Type 2335, half-cell) using Li foil as counter electrode. The working electrode was prepared using the mixture of calcined TiO 2 -FGS or control TiO 2 , Super P and poly (vinylidene fluoride) (PVDF) binder dispersed in N-methylpyrrolidone (NMP) solution, For the preparation of rutile TiO 2  electrode (less than 5 wt % graphene), the mass ratio of rutile TiO 2 -hybrid or control rutile TiO 2 , Super P and PVDF was 80:10:10. For the preparation of anatase TiO 2  electrode, the mass ratio was 70:20:10 and 80:10:10 for control anatase TiO 2  and anatase TiO 2 -FGS hybrid (2.5 wt % FGS), respectively. 
     Rutile TiO 2 -FGS hybrid (10 wt % FGS) electrode was prepared with a mass ratio of hybrid and PVDF binder at 90:10 without Super P. The resultant slurry was then uniformly coated on an aluminum foil current collector and dried overnight in air. The electrolyte used was 1 M LiPF 6  dissolved in a mixture of ethyl carbonate (EC) and dimethyl carbonate (DMC) with the volume ratio of 1:1. The coin cells were assembled in an argon-filled glove box. The electrochemical performance of TiO 2 -graphene was characterized with an Arbin Battery Testing System at room temperature. The electrochemical tests were performed between 3˜1 V vs. Li + /Li and C-rate currents applied were calculated based on a rutile TiO 2  theoretical capacity of 168 mAh/g. 
     Functionalized graphene sheets (FGSs) used in this study were prepared through the thermal expansion of graphite oxide according to the method shown in McAllister, M. J.; LiO, J. L.; Adamson, D. H.; Schniepp, H. C.; Abdala, A. A.; Liu, J.; Herrera-Alonso, M.; Milius, D. L.; CarO, R.; Prud&#39;homme, R. K.; Aksay, I. A. Single Sheet Functionalized Graphene by Oxidation and Thermal Expansion of Graphite.  Chem. Mater.  2007, 19, 4396-4404 and Schniepp, H. C.; Li, J. L.; McAllister, M. J.; Sai, H.; Herrera-Alonso, M.; Adamson, D. H.; Prud&#39;homme, R. K.; Car, R.; Saville, D. A.; Aksay, I. A. Functionalized Single Graphene Sheets Derived from Splitting Graphite Oxide.  J. Phys. Chem. B  2006, 110, 8535-8539. As discussed previously, in comparison to the graphene produced by the chemical reduction of graphene oxide, graphene prepared by the thermal expansion approach can have tunable C/O ratios ranging from 15 to 500 and thus its conductivity can be tuned to higher values. 
     FGSs processing starts with chemical oxidation of graphite flakes to increase the c-axis spacing from 0.34 to 0.7 nm. The resultant graphite oxide is then split by a rapid thermal expansion to yield separated graphene sheets. X-ray photoemission spectroscopy (XPS) of FGSs shows a sharp C 1 s peak indicating good sp 2  conjugation as shown in  FIG. 2 . A small shoulder at 286 eV indicates the existence of some C—O bonds corresponding to the epoxy and hydroxyl functional groups on FGSs. 
     Sodium dodecyl sulfate (SDS)-FGS aqueous dispersions were prepared by ultrasonication. Similar to the colloidal stabilization of CNTs using SDS shown in Bonard, J. M.; Stora, T.; Salvetat, J. P.; Maier, F.; Stockli, T.; Duschl, C.; Forro, L.; deHeer, W. A.; Chatelain, A. Purification and Size-Selection of Carbon Nanotubes.  Adv. Mater.  1997, 9, 827-831 and Richard, C.; Balavoine, F.; Schultz, P.; Ebbesen, T. W.; Mioskowski, C. Supramolecular Self-Assembly of Lipid Derivatives on Carbon Nanotubes,  Science  2003, 300, 775-778, the SDS-FGS aqueous dispersions were stable. Only minor sedimentation was observed after a week at room temperature as shown in  FIG. 4   a.    
     UV-Vis spectrum of the SDS-FGS dispersion showed an absorption peak at 275 nm with a broad absorption background ( FIG. 4   b ) consistent with that of aqueous stable graphene sheets. Raman spectra of FGS and calcined TiO 2 -FGS showed similar G and D bands structure of carbon, indicating that the structure of graphene is maintained during the synthesis procedure, as shown in  FIG. 3 . 
     A mild, low-temperature (below 100° C.) crystallization process was carried out to form crystalline TiO 2  with controlled crystalline phase (i.e., rutile and anatase) on the graphene sheets. The low temperature condition was also important in preventing aggregation of graphene sheets at elevated temperatures. Consistent with previous studies, by the low-temperature oxidative hydrolysis and crystallization, rutile TiO 2 -FGS is obtained with a minor anatase phase. To obtain anatase TiO 2 -FGS, additional sodium sulfate was added to the solution to promote the formation of the anatase phase. XRD patterns of the TiO 2 -FGS hybrids shown in  FIG. 5  show the formation of nanocrystalline rutile and anatase metal oxides with an estimated crystalline domain size of 6 and 5 nm, respectively. 
     Typical morphology of FGSs is shown in the transmission electron microscopy (TEM) image of  FIG. 6   a . The free standing 2D FGSs are not perfectly flat but display intrinsic microscopic roughening and out-of-plane deformations (wrinkles). More than 80% of the FGSs have been shown to be single sheets by AFM characterization, when they were deposited onto an atomically smooth, highly oriented pyrolytic carbon (HOPG) template. Some regions appeared as multilayers in the TEM images, which may represent the regions that either have not been fully exfoliated or the regions that have restacked together due to capillary and van der Waals forces experienced during the drying process. 
       FIGS. 6   b  to  6   e  show TEM and scanning electron microscopy (SEM) images of as-grown rutile TiO 2 -FGS hybrid nanostructures.  FIGS. 6   b  and  6   c  show planar views of FGSs covered with nanostructured TiO 2 . Both the edge of graphene and the nanostructure of the TiO 2  are clearly observable in the higher magnification image of  FIG. 6   c.    
     The nanostructured TiO 2  is composed of rod-like rutile nanocrystals organized in parallel interspaced with the SDS surfactants. The SEM image of  FIG. 6   d  shows randomly oriented rod-like nanostructured rutile lying on the FGS. The cross-section TEM image further confirms that the nanostructured rutile mostly lies on the FGS with the rod length parallel to the graphene surface ( FIG. 6   e ).  FIGS. 6   f  and  6   g  show plane-view TEM images of anatase TiO 2 -FGS hybrid nanostructures. FGSs underneath are covered with spherical aggregated anatase TiO 2  nanoparticles. The dark field TEM image ( FIG. 6   g ) further confirms crystalline TiO 2  nanoparticles (bright regions) with a diameter of 5 nm spreading over the graphene surface. 
     It is important to note that the SDS surfactant determines the interfacial interactions between graphene and the oxide materials in promoting the formation of TiO 2 -hybrid nanostructures. When the surfactant molecules are added, they can adsorb onto graphene through the hydrophobic tails making FGSs highly dispersed and interact with the oxide precursor through the hydrophilic head groups. The cooperative interactions between the surfactant, the graphene, and the oxide precursors lead to the homogeneous mixing of the components, in which the hydrophobic graphene most likely resides in the hydrophobic domains of the SDS micelles. As nanocrystalline TiO 2  formed, as-grown nanoparticles are then coated to the graphene surfaces since sulfate head groups have strong bonding with TiO 2 . Without the surfactant, some of the surface functional sites (e.g., carboxylate, epoxy, and hydroxyl groups) on FGSs may provide bonding to TiO 2  nanoparticles. However, only a very small amount of the metal oxides will then be attached to graphene through such interactions due to the low number density of these functional groups on FGSs. Thus, in the control samples without the surfactant, FGSs are barely covered with the metal oxides along with phase separation from TiO 2  as shown in  FIG. 12 . This indicates the important role of SDS in the formation of the self-assembled hybrid nanostructures. 
     To examine the effectiveness of FGSs in improving the rate capability of the electrode, we investigated the Li-ion insertion/extraction properties in the TiO 2 -FGS hybrid materials. The electrodes were fabricated in a conventional way by mixing the hybrid materials with Super P carbon additive and a PVDF binder and thus tested in Li-ion battery coin cell. The rutile TiO 2 -FGS hybrid showed a slope profile of voltage-capacity relationship at both the charge and discharge state as shown in  FIG. 7   a , similar to that of control rutile TiO 2  and nanostructured rutile studied previously as reported in Hu, Y. S.; Kienle, L.; Guo, Y. G.; Maier, J. High Lithium Electroactivity of Nanometer-Sized Rutile TiO 2   . Adv. Mater.  2006, 18, 1421-1426. As shown in  FIG. 7   b , with the incorporation of FGSs, the specific capacity of rutile TiO 2  in the hybrids (0.5 wt % FGS) increased at all charge/discharge rates compared with the control rutile TiO 2 . The relative increase in specific capacity is especially larger at higher rates. For instance, at a rate of 30 C (2 min of charging or discharging), the specific capacity of the rutile TiO 2 -FGS hybrid material is 87 mAh/g which is more than double the high rate capacity (35 mAh/g) of the control rutile TiO 2  as shown in  FIG. 7   b.    
     The voltage-capacity profile of anatase TiO 2 -FGS (2.5 wt % FGS) at C/5 rate shows plateaus around 1.8 V (discharge process) and 1.9 V (charge process) is shown in  FIG. 7   d , which is similar to that of control anatase TiO 2  and nanostructured anatase. The plateaus are related to the phase transition between the tetragonal and orthorhombic phases with Li insertion into anatase TiO 2 . Similar to rutile TiO 2 -FGS, the specific capacity of the anatase TiO 2 -FGS hybrid is enhanced at all charge-discharge rates as shown in  FIG. 7   e . The specific capacity of the anatase TiO 2 -FGS at the rate of 30 C is as high as 96 mAh/g compared with 25 mAh/g of control anatase TiO 2 . Furthermore, the coulombic efficiencies of TiO 2 -FGS hybrids at various charge/discharge rates are greater than 98% as shown in  FIG. 8 . Both rutile and anatase TiO 2 -FGS hybrids show good capacity retention of the Li-ion insertion/extraction with over 90% capacity retention after 100 cycles at a 1 C rate, as shown in  FIGS. 7   c  and  7   f.    
     To identify the capacity contribution from FGSs, the Li-ion insertion/extraction behavior of the FGSs was also studied. The initial capacity of FGS of 100 mAh/g with 50% irreversible loss is observed between 1˜3 V potential window applied, which is consistent with a recent study of Li-ion storage in graphene described in Yoo, E.; Kim, J.; Hosono, E.; Zhou, H.-s.; Kudo, T.; Honma, I. Large Reversible Li Storage of Graphene Nanosheet Families for Use in Rechargeable Lithium Ion Batteries.  Nano Lett.  2008, 8, 2277-2282. However, the specific capacity of FGS rapidly decreases to 25 mAh/g within 10 cycles. Al higher charge/discharge rates, FGS has almost negligible Li-ion insertion as shown in  FIG. 9 . For 1 wt % FGS hybrids, the capacity contribution from FGS itself after 2 cycles can be a maximum value of 0.4 mAh/g. Thus, the increase of the specific capacity at high rate is not attributed to the capacity of the graphene additive itself in the hybrid materials. 
     To further understand the improved high-rate performance, electrochemical impedance spectroscopy measurements on rutile TiO 2 -FGS hybrid materials were performed after cycles. The Nyquist plots of the rutile TiO 2 -FGS electrode materials with different percentage of graphene cycled in electrolyte, as shown in  FIG. 10(   a ), all show depressed semicycles at high frequencies. As electrolyte and electrode fabrication are similar between each electrode, the high frequency semicircle should relate to the internal resistance of the electrode. We estimate that the resistivity of the cells decreased from 93Ω for the pure TiO 2  to 73 Ω with the addition of only 0.5 wt % graphene. 
     By increasing the graphene percentage in the hybrid materials further, the specific capacity is slightly increased, e.g., to 93 mAh/g in the hybrid material with 5 wt % FGS, indicating that a kinetic capacity limitation may be reached by only improving the electrode conductivity with the incorporation of FGSs as shown in  FIG. 10(   b ). Rutile TiO 2 -CNT hybrids prepared and tested under similar conditions showed poorer performance at identical carbon loadings than the rutile TiO 2 -FGS hybrid anodes, as shown in the yellow bar in  FIG. 10(   b ). Similarly, hybrid nanostructures prepared using solution reduced graphene oxides also showed even poorer performance, indicating the importance of the highly conductive graphene phase of FGSs. 
     To study the properties of electrode materials without any Super P carbon, Li-ion insertion/extraction properties of the rutile TiO 2 -FGS (10 wt % graphene) were compared with control rutile TiO 2  with 10 wt % Super P at high charge-discharge rates. The hybrid material showed a much higher capacity at all charge-discharge rate, as shown in  FIG. 11 . This result indeed confirms that the graphene in the self-assembled hybrid materials is more effective than the commonly used Super P carbon materials in improving high rate performance of the electrode materials. 
     The high rate performance is important for applications where fast charge and discharge is needed, such as in load leveling utility applications. The simple self-assembly approach, and the potential low manufacturing cost of graphene of the present invention, thus provide a new pathway for large scale applications of novel hybrid nanocomposite materials for energy storage. 
     While the invention has been illustrated and described in detail in the drawings and foregoing description, the same is to be considered as illustrative and not restrictive in character. Only certain embodiments have been shown and described, and all changes, equivalents, and modifications that come within the spirit of the invention described herein are desired to be protected. Any experiments, experimental examples, or experimental results provided herein are intended to be illustrative of the present invention and should not be considered limiting or restrictive with regard to the invention scope. Further, any theory, mechanism of operation, proof, or finding stated herein is meant to further enhance understanding of the present invention and is not intended to limit the present invention in any way to such theory, mechanism of operation, proof, or finding. 
     Thus, the specifics of this description and the attached drawings should not be interpreted to limit the scope of this invention to the specifics thereof. Rather, the scope of this invention should be evaluated with reference to the claims appended hereto. In reading the claims it is intended that when words such as “a”, “an”, “at least one”, and “at least a portion” are used there is no intention to limit the claims to only one item unless specifically stated to the contrary in the claims. Further, when the language “at least a portion” and/or “a portion” is used, the claims may include a portion and/or the entire items unless specifically stated to the contrary. Likewise, where the term “input” or “output” is used in connection with an electric device or fluid processing unit, it should be understood to comprehend singular or plural and one or more signal channels or fluid lines as appropriate in the context. Finally, all publications, patents, and patent applications cited in this specification are herein incorporated by reference to the extent not inconsistent with the present disclosure as if each were specifically and individually indicated to be incorporated by reference and set forth in its entirety herein.