Patent Publication Number: US-2020280055-A1

Title: Process for producing particulates of graphene/carbon-encapsulated alkali metal, electrodes, and alkali metal battery

Description:
FIELD OF THE INVENTION 
     The present invention relates generally to the field of alkali metal battery (e.g. any lithium metal battery using lithium metal as an anode active material or sodium metal battery using sodium metal as an anode active material) and, more particularly, to a lithium or sodium metal secondary battery having multiple graphene/carbon particulates pre-loaded with lithium or sodium metal as an anode active material and a process for producing the particulates, electrode and battery. 
     BACKGROUND OF THE INVENTION 
     Rechargeable lithium-ion (Li-ion) and lithium metal batteries (e.g. Li-sulfur, Li metal-air, and lithium-metal oxide batteries) are considered promising power sources for electric vehicle (EV), hybrid electric vehicle (HEV), and portable electronic devices, such as lap-top computers and mobile phones. Lithium as a metal element has the highest capacity (3,861 mAh/g) compared to any other metal. Hence, in general, Li metal batteries have a significantly higher energy density than lithium ion batteries. Similarly, Na metal batteries have a higher energy than corresponding sodium ion batteries. 
     Historically, rechargeable lithium metal batteries were produced using non-lithiated compounds, such as TiS 2 , MoS 2 , MnO 2 , CoO 2 , and V 2 O 5 , as the cathode active materials, coupled with a lithium metal anode. When the battery was discharged, lithium ions were transferred from the lithium metal anode through the electrolyte to the cathode, and the cathode became lithiated. Unfortunately, upon repeated charges/discharges, the lithium metal resulted in the formation of dendrites at the anode that ultimately grew to penetrate through the separator, causing internal shorting and explosion. As a result of a series of accidents associated with this problem, the production of these types of secondary batteries was stopped in the early 1990&#39;s. 
     To overcome these safety issues, several alternative approaches were proposed in which either the electrolyte or the anode was modified. The first approach involves replacing Li metal by graphite (a Li insertion material) as the anode. The operation of such a battery involves shuttling Li ions between two Li insertion compounds at the anode and the cathode, respectively; hence, the name “Li-ion battery.” Presumably because of the presence of Li in its ionic rather than metallic state, Li-ion batteries are inherently safer than Li-metal batteries. The second approach entails replacing the liquid electrolyte by a dry polymer electrolyte, leading to the Li solid polymer electrolyte (Li-SPE) batteries. However, Li—SPE has seen very limited applications since it typically requires an operating temperature of up to 80° C. The third approach involves the use of a solid electrolyte that is presumably resistant to dendrite penetration, but the solid electrolyte normally exhibits excessively low lithium-ion conductivity at room temperature. Alternative to this solid electrolyte approach is the use of a rigid solid protective layer between the anode active material layer and the separator layer to stop dendrite penetration, but this typically ceramic material-based layer also has a low ion conductivity and is difficult and expensive to make and to implement in a lithium metal battery. Furthermore, the implementation of such a rigid and brittle layer is incompatible with the current lithium battery manufacturing process and equipment. 
     Although lithium-ion (Li-ion) batteries are promising energy storage devices for electric drive vehicles, state-of-the-art Li-ion batteries have yet to meet the cost and performance targets. Li-ion cells typically use a lithium transition-metal oxide or phosphate as a positive electrode (cathode) that de/re-intercalates Li +  at a high potential with respect to the carbon negative electrode (anode). The specific capacity of graphite anode is &lt;372 mAh/g and that of lithium transition-metal oxide or phosphate based cathode active material is typically in the range from 140-200 mAh/g. As a result, the specific energy of commercially available Li-ion cells is typically in the range from 120-220 Wh/kg, most typically 150-180 Wh/kg. These specific energy values are two to three times lower than what would be required for battery-powered electric vehicles to be widely accepted. 
     With the rapid development of hybrid (HEV), plug-in hybrid electric vehicles (HEV), and all-battery electric vehicles (EV), there is an urgent need for anode and cathode materials that provide a rechargeable battery with a significantly higher specific energy, higher energy density, higher rate capability, long cycle life, and safety. Among various advanced energy storage devices, alkali metal batteries, including Li-air (or Li—O 2 ), Na-air (or Na—O 2 ), Li—S, and Na—S batteries, are especially attractive due to their high specific energies. 
     The Li—O 2  battery is possibly the highest energy density electrochemical cell that can be configured today. The Li—O 2  cell has a theoretic energy density of 5.2 kWh/kg when oxygen mass is accounted for. A well configured Li—O 2  battery can achieve an energy density of 3,000 Wh/kg, 15-20 times greater than those of Li-ion batteries. However, current Li—O 2  batteries still suffer from poor energy efficiency, poor cycle efficiency, and dendrite formation and penetration issues. 
     One of the most promising energy storage devices is the lithium-sulfur (Li—S) cell since the theoretical capacity of Li is 3,861 mAh/g and that of S is 1,675 mAh/g. In its simplest form, a Li—S cell consists of elemental sulfur as the positive electrode and lithium as the negative electrode. The lithium-sulfur cell operates with a redox couple, described by the reaction S 8 +16Li⇄8Li 2 S that lies near 2.2 V with respect to Li + /Li o . This electrochemical potential is approximately ⅔ of that exhibited by conventional positive electrodes (e.g. LiMnO 4 ). However, this shortcoming is offset by the very high theoretical capacities of both Li and S. Thus, compared with conventional intercalation-based Li-ion batteries, Li—S cells have the opportunity to provide a significantly higher energy density (a product of capacity and voltage). Assuming complete reaction to Li 2 S, energy densities values can approach 2,500 Wh/kg and 2,800 Wh/l, respectively, based on the combined Li and S weights or volumes. If based on the total cell weight or volume, the energy densities can reach approximately 1,000 Wh/kg and 1,100 Wh/l, respectively. However, the current Li-sulfur cells reported by industry leaders in sulfur cathode technology have a maximum cell specific energy of 250-350 Wh/kg (based on the total cell weight), which is far below what is possible. In summary, despite its great potential, the practical realization of the Li—S battery has been hindered by several obstacles, such as dendrite-induced internal shorting, low active material utilization efficiency, high internal resistance, self-discharge, and rapid capacity fading on cycling. These technical barriers are due to the poor electrical conductivity of elemental sulfur, the high solubility of lithium polysulfides in organic electrolyte (which migrate to the anode side, resulting in the formation of inactivated Li 2 S in the anode), and Li dendrite formation and penetration. The most serious problem of Li metal secondary (rechargeable) batteries remains to be the dendrite formation and penetration. Sodium metal batteries have similar dendrite problems. 
     Carbon is known to have five unique crystalline structures, including diamond, fullerene (0-D nanographitic material), carbon nanotube or carbon nanofiber (1-D nanographitic material), graphene (2-D nanographitic material), and graphite (3-D graphitic material). The carbon nanotube (CNT) refers to a tubular structure grown with a single wall or multi-wall. Carbon nanotubes (CNTs) and carbon nanofibers (CNFs) have a diameter on the order of a few nanometers to a few hundred nanometers. Their longitudinal, hollow structures impart unique mechanical, electrical and chemical properties to the material. The CNT or CNF is a one-dimensional nanocarbon or 1-D nanographite material. 
     A single-layer graphene sheet is composed of carbon atoms occupying a two-dimensional hexagonal lattice. Multi-layer graphene is a platelet composed of more than one graphene plane. Individual single-layer graphene sheets and multi-layer graphene platelets are herein collectively called nanographene platelets (NGPs) or graphene materials. NGPs include pristine graphene (essentially 99% of carbon atoms), slightly oxidized graphene (&lt;5% by weight of oxygen), graphene oxide (≥5% by weight of oxygen), slightly fluorinated graphene (&lt;5% by weight of fluorine), graphene fluoride ((≥5% by weight of fluorine), other halogenated graphene, and chemically functionalized graphene. 
     Our research group pioneered the development of graphene materials and related production processes as early as 2002: (1) B. Z. Jang and W. C. Huang, “Nano-scaled Graphene Plates,” U.S. Pat. No. 7,071,258 (Jul. 4, 2006), application submitted on Oct. 21, 2002; (2) B. Z. Jang, et al. “Process for Producing Nano-scaled Graphene Plates,” U.S. patent application Ser. No. 10/858,814 (Jun. 3, 2004) (U.S. Pat. Pub. No. 2005/0271574); and (3) B. Z. Jang, A. Zhamu, and J. Guo, “Process for Producing Nano-scaled Platelets and Nanocomposites,” U.S. patent application Ser. No. 11/509,424 (Aug. 25, 2006) (U.S. Pat. Pub. No. 2008/0048152). 
     Our research group also presented the first review article on various processes for producing NGPs and NGP nanocomposites [Bor Z. Jang and A Zhamu, “Processing of Nanographene Platelets (NGPs) and NGP Nanocomposites: A Review,” J. Materials Sci. 43 (2008) 5092-5101]. Four main prior-art approaches have been followed to produce NGPs. The most commonly used process is chemical oxidation and reduction of graphite to produce graphene oxide (GO) and reduced graphene oxide (RGO). 
     This process, as schematically illustrated in  FIG. 1 , entails treating natural graphite powder with an intercalant and an oxidant (e.g., concentrated sulfuric acid and nitric acid, respectively) to obtain a graphite intercalation compound (GIC) or, actually, graphite oxide (GO). [William S. Hummers, Jr., et al., Preparation of Graphitic Oxide, Journal of the American Chemical Society, 1958, p. 1339.] Prior to intercalation or oxidation, graphite has an inter-graphene plane spacing of approximately 0.335 nm (L d =½d 002 =0.335 nm). With an intercalation and oxidation treatment, the inter-graphene spacing is increased to a value typically greater than 0.6 nm. This is the first expansion stage experienced by the graphite material during this chemical route. The obtained GIC or GO is then subjected to further expansion (often referred to as exfoliation) using either a thermal shock exposure or a solution-based, ultrasonication-assisted graphene layer exfoliation approach. 
     In the thermal shock exposure approach, the GIC or GO is exposed to a high temperature (typically 800-1,050° C.) for a short period of time (typically 15 to 60 seconds) to exfoliate or expand the GIC or GO for the formation of exfoliated or further expanded graphite, which is typically in the form of a “graphite worm” composed of graphite flakes that are still interconnected with one another. This thermal shock procedure can produce some separated graphite flakes or graphene sheets, but normally the majority of graphite flakes remain interconnected. Typically, the exfoliated graphite or graphite worm is then subjected to a flake separation treatment using air milling, mechanical shearing, or ultrasonication in water. Hence, approach 1 basically entails three distinct procedures: first expansion (oxidation or intercalation), further expansion (or “exfoliation”), and separation. 
     In the solution-based separation approach, the expanded or exfoliated GO powder is dispersed in water or aqueous alcohol solution, which is subjected to ultrasonication. It is important to note that in these processes, ultrasonification is used after intercalation and oxidation of graphite (i.e., after first expansion) and typically after thermal shock exposure of the resulting GIC or GO (after second expansion). Alternatively, the GO powder dispersed in water is subjected to an ion exchange or lengthy purification procedure in such a manner that the repulsive forces between ions residing in the inter-planar spaces overcome the inter-graphene van der Waals forces, resulting in graphene layer separations. 
     There are several major problems associated with this conventional chemical production process:
         (1) The process requires the use of large quantities of several undesirable chemicals, such as sulfuric acid, nitric acid, and potassium permanganate or sodium chlorate.   (2) The chemical treatment process requires a long intercalation and oxidation time, typically 5 hours to five days.   (3) Strong acids consume a significant amount of graphite during this long intercalation or oxidation process by “eating their way into the graphite” (converting graphite into carbon dioxide, which is lost in the process). It is not unusual to lose 20-50% by weight of the graphite material immersed in strong acids and oxidizers.   (4) The thermal exfoliation requires a high temperature (typically 800-1,200° C.) and, hence, is a highly energy-intensive process.   (5) Both heat- and solution-induced exfoliation approaches require a very tedious washing and purification step. For instance, typically 2.5 kg of water is used to wash and recover 1 gram of GIC, producing huge quantities of waste water that need to be properly treated.   (6) In both the heat- and solution-induced exfoliation approaches, the resulting products are GO platelets that must undergo a further chemical reduction treatment to reduce the oxygen content. Typically even after reduction, the electrical conductivity of GO platelets remains much lower than that of pristine graphene. Furthermore, the reduction procedure often involves the utilization of toxic chemicals, such as hydrazine.   (7) Furthermore, the quantity of intercalation solution retained on the flakes after draining may range from 20 to 150 parts of solution by weight per 100 parts by weight of graphite flakes (pph) and more typically about 50 to 120 pph. During the high-temperature exfoliation, the residual intercalant species retained by the flakes decompose to produce various species of sulfuric and nitrous compounds (e.g., NO x  and SO x ), which are undesirable. The effluents require expensive remediation procedures in order not to have an adverse environmental impact.       

     Hence, an urgent need exists to have a graphene production process that requires a reduced amount of undesirable chemical (or elimination of these chemicals all together), shortened process time, less energy consumption, lower degree of graphene oxidation, reduced or eliminated effluents of undesirable chemical species into the drainage (e.g., sulfuric acid) or into the air (e.g., SO 2  and NO 2 ). The process should be able to produce more pristine (less oxidized and damaged), more electrically conductive, and larger/wider graphene sheets. Furthermore, one should be able to readily make these graphene sheets into a foam structure. 
     Our recent research has yielded a process for chemical-free production of isolated nanographene platelets that is novel in that is does not follow the established methods for production of nanographene platelets outlined above. In addition, the process is of enhanced utility in that it is cost effective, and provided novel graphene materials with significantly reduced environmental impact. Furthermore, as herein disclosed, we have combined the chemical-free production of graphene and the formation of porous graphene-carbon hybrid particulates into one single operation. These porous particulates also contain a lithium- or sodium-attracting metal inside the pores of these particulates to promote entry of lithium metal or sodium metal during a battery charge procedure. 
     For the purpose of defining the claims of the instant application, NGPs or graphene materials include discrete sheets/platelets of single-layer and multi-layer (typically less than 10 layers) pristine graphene, graphene oxide, reduced graphene oxide (RGO), graphene fluoride, graphene chloride, graphene bromide, graphene iodide, hydrogenated graphene, nitrogenated graphene, chemically functionalized graphene, doped graphene (e.g. doped by B or N). Pristine graphene has essentially 0% oxygen. RGO typically has an oxygen content of 0.001%-5% by weight. Graphene oxide (including RGO) can have 0.001%-50% by weight of oxygen. Other than pristine graphene, all the graphene materials have 0.001%-50% by weight of non-carbon elements (e.g. O, H, N, B, F, Cl, Br, I, etc.). These materials are herein referred to as non-pristine graphene materials. The presently invented graphene-carbon foam can contain pristine or non-pristine graphene and the invented method allows for this flexibility. 
     It is an object of the present invention to provide a cost-effective process for producing highly conductive, mechanically robust graphene/carbon porous particles (individual porous particulates, not part of a graphene foam). The particulate contains a lithium-attracting or sodium-attracting metal residing therein, in the form of minute particles or thin coating in physical contact with the pore wall of the porous graphene/carbon particulate structure. This process does not involve the use of an environmentally unfriendly chemical. This process enables the flexible design and control of the porosity level and pore sizes in such a manner that a lithium-attracting metal or sodium-attracting metal is readily and easily accommodated in these pores to promote and facilitate fast entry and uniform deposition of lithium ions or sodium ions if the resulting graphene/carbon-metal particulates are used as an anode active material of a lithium metal or sodium metal battery. 
     It is another object of the present invention to provide graphene/carbon hybrid particulates having a graphene/carbon shell encapsulating or embracing a porous core. The porous pore may be composed of one single pore or a plurality of pores. Such graphene/carbon particulates, if containing a select alkali metal-attracting metal, are conducive to being used as a supporting substrate for lithium in the anode of a lithium metal secondary battery to suppress the formation of lithium or sodium dendrites. The encapsulating shell typically comprises multiple graphene sheets that are chemically bonded by a carbon material in such a manner that the encapsulating shell is not permeable to the electrolyte of the intended lithium metal cell or sodium metal cell, but is permeable to lithium ions or sodium ions. 
     A specific object of the present invention is to provide porous graphene-carbon-metal hybrid particulates (including both lithium- or sodium-loaded particulates and those porous particulates without lithium or sodium pre-loaded therein) for use as an anode active material for a lithium metal and sodium metal secondary batteries that exhibit long and stable charge-discharge cycle life without exhibiting lithium or sodium dendrite problems. 
     SUMMARY OF THE INVENTION 
     The present invention provides porous graphene/carbon particulates for an alkali metal battery (lithium or sodium metal battery) and a process for producing such particulates directly from particles of a graphitic material and particles of an alkali metal attracting metal-coated polymer. This process is stunningly simple, fast, cost-effective, and environmentally benign. The invention also provides a lithium metal battery and a sodium metal containing such particulates as an anode active material. 
     In a preferred embodiment, the invention provides a porous graphene/carbon particulate comprising a graphene/carbon shell encapsulating a porous core, wherein the porous core comprises one or a plurality of pores and pore walls and a lithium-attracting metal or sodium-attracting metal residing in the pores or deposited on the pore walls; wherein the lithium-attracting metal is selected from Au, Ag, Mg, Zn, Ti, Na, K, Al, Fe, Mn, Co, Ni, Sn, V, Cr, or an alloy thereof or the sodium-attracting metal is selected from Au, Ag, Mg, Zn, Ti, Li, K, Al, Fe, Mn, Co, Ni, Sn, V, Cr, or an alloy thereof, and is in an amount of 0.1% to 90% of the total particulate weight, and the graphene/carbon shell comprises single-layer or few-layer graphene sheets chemically bonded by a carbon material having a carbon material-to-graphene weight ratio from 1/200 to 1/2, wherein the few-layer graphene sheets have 2-10 layers of stacked graphene planes having an inter-plane spacing d 002  from 0.3354 nm to 0.40 nm as measured by X-ray diffraction and the single-layer or few-layer graphene sheets contain a pristine graphene material having essentially zero % of non-carbon elements, or a non-pristine graphene material having 0.001% to 25% by weight of non-carbon elements. 
     The non-pristine graphene may be selected from graphene oxide, reduced graphene oxide, graphene fluoride, graphene chloride, graphene bromide, graphene iodide, hydrogenated graphene, nitrogenated graphene, doped graphene, chemically functionalized graphene, or a combination thereof. 
     In some preferred embodiments, the porous graphene/carbon particulate further contains lithium metal or sodium metal residing in at least a pore of the particulate and in physical contact with the lithium-attracting metal or sodium-attracting metal to form a lithium-preloaded or sodium-preloaded graphene/carbon particulate. 
     The porous particulate is preferably pre-loaded with lithium or sodium metal (impregnated into the core to partially or completely fill the pores of the particulate) before the battery is made. Alternatively, the anode of the intended alkali metal battery contains a lithium source or a sodium source, in addition to the porous graphene/carbon particulates. The lithium source is preferably selected from foil, particles, or filaments of lithium metal or lithium alloy having no less than 80% by weight of lithium element in the lithium alloy. The sodium source is preferably selected from foil, particles, or filaments of sodium metal or sodium alloy having no less than 80% by weight of sodium element in the sodium alloy. 
     In the lithium or sodium metal battery, each cell contains an anode layer comprising the invented porous graphene/carbon particulates, which are pre-loaded with lithium or sodium. When the battery is discharged, lithium or sodium ions are released from the particulates and moved through an electrolyte/separator to the cathode comprising a cathode active material layer. The resulting partially or fully porous particulates will accommodate lithium or sodium when the battery is subsequently recharged. In some embodiments, the lithium or sodium metal battery further comprises a separate, discrete anode current collector (e.g. Cu foil) in contact with the anode. Typically, there is a separate, discrete cathode current collector (e.g. Al foil) in contact with the cathode active material layer (containing cathode active material, such as MoS 2 , TiO 2 , V 2 O 5 , LiV 3 O 8 , S, Se, etc.), which is supported by (coated on) the Al foil. 
     In some embodiments, the porous graphene/carbon particulate, when measured without the lithium- or sodium-attracting metal, has a density from 0.005 to 1.7 g/cm 3  and a specific surface area from 50 to 2,630 m 2 /g. In certain embodiments, the particulate, when measured without the metal, has a density from 0.1 to 1.7 g/cm 3  and an average pore size from 2 nm to 50 μm, preferably from 100 nm to 10 μm. In some embodiments, the porous particulate has a physical density higher than  0 . 8  g/cm 3  and a specific surface area greater than 800 m 2 /g. In some embodiments, the porous graphene/carbon particulate has a physical density higher than 1.0 g/cm 3  and a specific surface area greater than 500 m 2 /g. 
     The graphene/carbon shell may comprise a non-pristine graphene material having a content of non-carbon elements in the range from 0.01% to 20% by weight and the non-carbon elements include an element selected from oxygen, fluorine, chlorine, bromine, iodine, nitrogen, hydrogen, or boron. 
     The invention also provides an alkali metal battery anode containing one or a plurality of the invented porous particulates as an anode active material. In certain embodiments, the alkali metal battery comprises a cathode, an anode containing the invented porous particulates, a lithium source or a sodium source in ionic contact with the anode, and an electrolyte in ionic contact with both the cathode and the anode. The lithium source may be selected from foil, particles, or filaments of lithium metal or lithium alloy having no less than 80% by weight of lithium element in the lithium alloy; or the sodium source is selected from foil, particles, or filaments of sodium metal or sodium alloy having no less than 80% by weight of sodium element in the sodium alloy. 
     The invention also provides (a) an alkali metal battery anode containing one or a plurality of the presently invented lithium-preloaded or sodium-preloaded graphene/carbon particulates as an anode active material and (b) an alkali metal battery comprising such an anode, a cathode, and an electrolyte in ionic contact with both the cathode and the anode. 
     The alkali metal battery may be a lithium metal battery, lithium-sulfur battery, lithium-selenium battery, lithium-air battery, sodium metal battery, sodium-sulfur battery, sodium-selenium battery, or sodium-air battery. 
     Th invention further provides a powder mass comprising one or a plurality of particulates as described above. The powder mass may preferably comprise one or a plurality of the invented pporous particulates that are partially or fully impregnated or infiltrated with lithium or sodium, the so-called lithium-preloaded or sodium-preloaded graphene/carbon particulates. 
     The invention also provides a lithium-ion battery comprising an anode, a cathode, an electrolyte in ionic contact with the anode and the cathode, wherein the anode comprises a first anode active material, comprising one or a plurality of the invented lithium-preloaded graphene/carbon particulates, and a second anode active material, wherein the lithium-preloaded graphene/carbon particulates act as a lithium source for the second anode active material when an electrolyte is introduced into such an anode (comprising the two types of anode active material) or during a charge/discharge cycle of the lithium-ion battery. The lithium- or sodium-preloaded graphene/carbon particulates act to prelithiate or lithiate the second (or primary) anode active material. In other words, the presently invented lithium- or sodium-preloaded graphene/carbon particulates can serve as a prelithiating agent for any anode active material in a conventional lithium-ion battery or sodium-ion battery. 
     In the above-described lithium-ion battery, the second anode active material may be selected from the group consisting of: (A) silicon (Si), germanium (Ge), tin (Sn), lead (Pb), antimony (Sb), bismuth (Bi), zinc (Zn), aluminum (Al), titanium (Ti), nickel (Ni), cobalt (Co), and cadmium (Cd); (B) alloys or intermetallic compounds of Si, Ge, Sn, Pb, Sb, Bi, Zn, Al, Ti, Ni, Co, or Cd with other elements; (C) oxides, carbides, nitrides, sulfides, phosphides, selenides, and tellurides of Si, Ge, Sn, Pb, Sb, Bi, Zn, Al, Ti, Fe, Ni, Co, or Cd, and their mixtures, composites, or lithium-containing composites; (D) salts and hydroxides of Sn; (E) lithium titanate, lithium manganate, lithium aluminate, lithium-containing titanium oxide, lithium transition metal oxide; (F) graphite or carbon particles, filaments, fibers, nanofibers, nanotubes, or nanowires; and combinations thereof. 
     The invention also provides a sodium-ion battery comprising an anode, a cathode, an electrolyte in ionic contact with the anode and the cathode, wherein the anode comprises a first anode active material, comprising one or a plurality of the sodium-preloaded graphene/carbon particulates, and a second anode active material, wherein the sodium-preloaded graphene/carbon particulates act as a sodium source for the second anode active material when an electrolyte is introduce into such an anode or during a charge/discharge cycle of said sodium-ion battery. In such a sodium-ion battery, the second anode active material is selected from the group consisting of: (a) silicon (Si), germanium (Ge), tin (Sn), lead (Pb), antimony (Sb), bismuth (Bi), zinc (Zn), aluminum (Al), titanium (Ti), nickel (Ni), cobalt (Co), and cadmium (Cd); (b) alloys or intermetallic compounds of Si, Ge, Sn, Pb, Sb, Bi, Zn, Al, Ti, Ni, Co, or Cd with other elements; (c) oxides, carbides, nitrides, sulfides, phosphides, selenides, and tellurides of Si, Ge, Sn, Pb, Sb, Bi, Zn, Al, Ti, Fe, Ni, Co, or Cd, and their mixtures, composites, or lithium-containing composites; (d) graphite or carbon particles, filaments, fibers, nanofibers, nanotubes, or nanowires; and (e) combinations thereof. 
     Thus, the invention further provides a method of prelithiating or pre-sodiating a lithium-ion battery or sodium-ion battery, the method comprising an operation of combining lithium-preloaded or sodium-preloaded graphene/carbon particulates, as a first anode active material, and a second anode active material in an anode of a lithium-ion battery or sodium-ion battery and introducing an electrolyte into the anode. This step of introducing electrolyte into the anode may be accomplished before or after such an anode is incorporated as a cathode and a separator to form a battery cell. 
     Also provided in the invention is a process for producing porous graphene/carbon particulates for an alkali metal battery, the process comprising:
         (a) Depositing particles or coating of a lithium-attracting metal or sodium-attracting metal onto surfaces of polymer particles to obtain metal-deposited polymer carrier particles, wherein the lithium-attracting or sodium-attracting metal is selected from Au, Ag, Mg, Zn, Ti, Li, Na, K, Al, Fe, Mn, Co, Ni, Sn, V, Cr, or an alloy thereof;   (b) mixing multiple particles of a graphitic material, the metal-deposited polymer carrier particles, and an optional ball-milling media to form a mixture in an impacting chamber of an energy impacting apparatus;   (c) operating the energy impacting apparatus with a frequency and an intensity for a length of time sufficient for peeling off graphene sheets from the graphitic material and transferring the graphene sheets to surfaces of the metal-deposited polymer carrier particles to produce graphene-embraced metal-deposited polymer particles inside the impacting chamber;   (d) recovering the graphene-embraced metal-deposited polymer particles from the impacting chamber; and   (e) pyrolyzing the graphene-embraced metal-deposited polymer particles to thermally convert the polymer into pores and carbon or graphite that bonds the graphene sheets to form porous graphene/carbon particulates, wherein at least a porous graphene/carbon particulate comprises a graphene/carbon shell encapsulating a porous core, wherein the porous core comprises one or a plurality of pores and pore walls and said lithium-attracting metal or sodium-attracting metal resides in said pores or is deposited on the pore walls.       

     It may be noted that for the purpose of defining the scope of the claims, the lithium- or sodium-attracting metal recited in Step (a) includes a precursor to this metal; such a precursor may be later chemically or thermally converted to the desired metal. For instance, the polymer particle surfaces may be coated with HAuCl 4 , which is thermally converted to Au when the underlying polymer is thermally carbonized. Another example is to deposit zinc chloride on polymer particle surfaces (e.g. via salt solution dipping and drying) and use hydrogen and methane to chemically convert this precursor to Zn metal at a later stage (e.g. before or after graphene deposition). There are many metal precursors to metals that are well-known in the art. 
     The graphitic material may be selected from pristine graphite, graphite oxide, graphite fluoride, graphite chloride, graphite bromide, graphite iodide, hydrogenated graphite, nitrogenated graphite, chemically functionalized graphite, or a combination thereof. 
     The invented process may further comprise a step of impregnating lithium metal or sodium metal into at least a pore of the porous graphene/carbon particulates, wherein the lithium metal or sodium metal partially or completely fills the pore(s) and is in physical contact with the lithium-attracting metal or sodium-attracting metal to form lithium-preloaded or sodium-preloaded graphene/carbon particulates. 
     Preferably, the energy impacting apparatus is selected from a double cone mixer, double cone blender, vibratory ball mill, planetary ball mill, high energy mill, basket mill, agitator ball mill, cryogenic ball mill, microball mill, tumbler ball mill, attritor, continuous ball mill, stirred ball mill, pressurized ball mill, plasma-assisted ball mill, freezer mill, vibratory sieve, bead mill, nanobead mill, ultrasonic homogenizer mill, centrifugal planetary mixer, vacuum ball mill, or resonant acoustic mixer. 
     In certain preferred embodiments, the procedure of operating the energy impacting apparatus is conducted in a continuous manner using a continuous energy impacting device. 
     The milling media may be selected from particles of a metal or metal alloy, a glass, a ceramic, a polymer, or a combination thereof. 
     In the invented process, the polymer particles or the milling media may contain a material selected from the group consisting of polyamides, polycarbonate, polyester, polyethylene, high-density polyethylene, low-density polyethylene, polyethylene terephthalate, polypropylene, polystyrene, high impact polystyrene, polyurethanes, polyvinylchloride, polyvinylidene chloride, acrylonitrile butadiene styrene, polyepoxide, polymethyl methacrylate, polytetrafluoroethylene, phenolics (or phenol formaldehyde, melamine formaldehyde, urea-formaldehyde, polyetheretherketone, maleimide/bismaleimide, polyethrimide, polyimide, plastarch materials, polylactic acid, furan, silicone, polysulfone, natural rubber, bromo isobutylene isoprene rubber, polybutadiene, chloro isobutylene isoprene rubber, polychloroprene rubber, chlorosulphonated polyethylene, epichlorohydrin, ethylene propylene, ethylene propylene diene monomer (EPDM), fluorinated hydrocarbon rubber, fluoro silicone rubber, hydrogenated nitrile butadiene, polyisoprene rubber, isobutylene isoprene butyl rubber, methyl vinyl silicone rubber, acrylonitrile butadiene rubber, styrene butadiene rubber, styrene ethylene/butylene styrene rubber, polysiloxane rubber, polysiloxane rubber, and combinations thereof. 
     The process may further comprise a step of incorporating said porous graphene/carbon particulates in an electrode for a lithium metal battery, lithium-sulfur battery, lithium-selenium battery, lithium-air battery, sodium metal battery, sodium-sulfur battery, sodium-selenium battery, or sodium-air battery. 
     In certain embodiments, the process may further comprise a step of incorporating the lithium-preloaded or sodium-preloaded graphene/carbon particulates in an anode electrode as a prelithiating agent or a pre-sodiating agent for a lithium metal battery, lithium-sulfur battery, lithium-selenium battery, lithium-air battery, sodium metal battery, sodium-sulfur battery, sodium-selenium battery, or sodium-air battery. 
     In the invented process, the step of pyrolyzing may be conducted at a temperature selected from 200° C. to 3,200° C. In certain embodiments, the step of pyrolyzing comprises carbonizing the polymer to become a carbon (typically at a carbonization temperature from 200° C. to 2,500° C.) or carbonizing the polymer into a carbon material and graphitizing the resulting carbon material (typically at a temperature higher than 2,500° C.) into a graphite. The resulting carbon material or graphite typically acts to chemically bond graphene sheets together to form an encapsulating shell that is permeable to lithium or sodium ions, but not the electrolyte. 
     In certain embodiments, Step (a) of ther invented process comprises depositing a precursor to lithium-attracting metal or sodium-attracting metal onto surfaces of polymer particles and Step (e) comprises thermally converting the precursor to said lithium-attracting metal or sodium-attracting metal. 
     In certain embodiments, Step (a) comprises depositing a precursor to lithium-attracting metal or sodium-attracting metal onto surfaces of polymer particles and then chemically or thermally converting the precursor to the lithium-attracting metal or sodium-attracting metal. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         FIG. 1  A flow chart showing the most commonly used prior art process of producing highly oxidized graphene sheets (NGPs) that entails tedious chemical oxidation/intercalation, rinsing, and high-temperature exfoliation procedures. 
         FIG. 2(A)  A flow chart showing the presently invented process for producing porous graphene/carbon hybrid particles having a lithium- or sodium metal-attracting metal included in the pores of the particulates. 
         FIG. 2(B)  Schematic of the heat-induced conversion of polymer into carbon, which bonds graphene sheets together to form porous graphene/carbon hybrid particulates. 
         FIG. 2(C)  The graphene/carbon hybrid particulates containing a lithium- or sodium-attracting metal residing in the pores (e.g. coated on internal shell surfaces) of the particulate. Lithium or sodium metal is attracted to fully or partially fill the pores of the particulate 
         FIG. 2(D)  Schematic of a prior art lithium metal battery cell. 
         FIG. 3(A)  Ragone plots (gravimetric power density vs. energy density) of two sets of lithium metal cells: (a) first cell containing porous nitrogen-doped graphene-carbon-metal (Zn) hybrid particulates, in physical contact with a lithium foil, as the anode active material; (b) the second cell containing no lithium-attracting metal (Zn). 
         FIG. 3(B)  The cycling behaviors of two sets of lithium metal cells: (a) first cell containing nitrogen-doped graphene-carbon-metal (Zn) hybrid particulates, in physical contact with a lithium foil, as the anode active material; (b) the second cell containing no lithium-attracting metal (Zn). 
         FIG. 4  The battery cell capacity decay curves of two sodium metal cells: one cell containing pristine graphene-carbon-metal (Mg) particulates and a sheet of Na foil as the anode active material and NaFePO 4  as the cathode active material, and the other cell containing pristine graphene-carbon particulates (but no sodium-attracting metal included therein) and a sheet of Na foil as the anode active material. 
     
    
    
     DESCRIPTION OF THE PREFERRED EMBODIMENTS 
     As schematically illustrated in  FIG. 2(D) , a prior art lithium metal cell is typically composed of an anode current collector  202  (e.g. Cu foil 8-12 μm thick), an anode active material layer  204  (e.g. a foil of lithium metal or lithium-rich metal alloy), a porous separator  230 , a cathode active material layer  208  (containing a cathode active material, such as V 2 O 5  and MoS 2  particles  234 , and conductive additives that are all bonded by a resin binder, not shown), a cathode current collector  206  (e.g. Al foil), and an electrolyte disposed in ionic contact with both the anode active material layer  204  (also simply referred to as the “anode layer”) and the cathode active material layer  208  (or simply “cathode layer”). The entire cell is encased in a protective housing, such as a thin plastic-aluminum foil laminate-based envelop. A prior art sodium metal cell is similarly configured, but the anode active material layer is a foil of sodium metal or sodium-rich metal, or particles of sodium. 
     The prior art lithium or sodium metal cell is typically made by a process that includes the following steps: (a) The first step is mixing and dispersing particles of the cathode active material (e.g. activated carbon), a conductive filler (e.g. acetylene black), a resin binder (e.g. PVDF) in a solvent (e.g. NMP) to form a cathode slurry; (b) The second step includes coating the cathode slurry on the surface(s) of an Al foil and drying the slurry to form a dried cathode electrode coated on the Al foil; (c) The third step includes laminating a Cu foil (as an anode current collector), a sheet of Li or Na foil (or lithium alloy or sodium alloy foil), a porous separator layer, and a cathode electrode-coated Al foil sheet together to form a 5-layer assembly, which is cut and slit into desired sizes and stacked to form a rectangular structure (as an example of shape) or rolled into a cylindrical cell structure; (d) The rectangular or cylindrical laminated structure is then encased in an aluminum-plastic laminated envelope or steel casing; and (e) A liquid electrolyte is then injected into the laminated structure to make a lithium battery cell. 
     Due to the high specific capacity of lithium metal and sodium metal, the highest battery energy density can be achieved by alkali metal rechargeable batteries that utilize a lithium metal or sodium metal as the anode active material, provided that a solution to the safety problem can be formulated. These cells include (a) the traditional Li or Na metal battery having a Li insertion or Na insertion compound in the cathode, (b) the Li-air or Na—O 2  cell that uses oxygen, instead of metal oxide, as a cathode (and Li or sodium metal as an anode instead of graphite or hard carbon), (c) the Li-sulfur or Na-S cell, (d) the lithium-selenium cell or sodium-selenium cell, and (e) the Li-graphene or Na-graphene cell using graphene as the main cathode active material. 
     The Li—O 2  battery is possibly the highest energy density electrochemical cell that can be configured today. The Li—O 2  cell has a theoretic energy density of 5,200 Wh/kg when oxygen mass is accounted for. A well configured Li—O 2  battery can achieve an energy density of 3,000 Wh/kg, which is 15-20 times greater than those of Li-ion batteries. However, current Li—O 2  batteries still suffer from poor energy efficiency, poor cycle efficiency, and dendrite formation issues. In the Li—S cell, elemental sulfur (S) as a cathode material exhibits a high theoretical Li storage capacity of 1,672 mAh/g. With a Li metal anode, the Li—S battery has a theoretical energy density of ˜1,600 Wh/kg (per total weight of active materials). Despite its great potential, the practical realization of the Li—S battery has been hindered by several obstacles, such as low utilization of active material, high internal resistance, self-discharge, and rapid capacity fading on cycling. These technical barriers are due to the poor electrical conductivity of elemental sulfur, the high solubility of lithium polysulfides in organic electrolyte, the formation of inactivated Li 2 S, and the formation of Li dendrites on the anode. Despite great efforts worldwide, dendrite formation remains the single most critical scientific and technological barrier against widespread implementation of all kinds of high energy density batteries having a Li metal anode. 
     We have discovered a highly dendrite-resistant, graphene/carbon/metal particulate-enabled Li metal cell or Na metal cell configuration that exhibits a high energy and/or high power density. Each battery cell contains multiple porous graphene/carbon particulates as an anode active material, wherein a lithium- or sodium-attracting metal,  11  in  FIG. 2(C) , is deposited on the pore walls or lodged inside the pores of these porous particulates. These graphene/carbon particulates are composed of graphene sheets (e.g.  12  in  FIG. 2(B) ) that are bonded by a carbon binder (e.g.  16   a  and  16   b ), having pores (e.g.  18   a  and  18   b  in  FIG. 2(B) ) to accommodate the lithium- or sodium-attracting metal,  11  in  FIG. 2(C) . This carbon binder is derived from a carbon precursor (e.g. polymer particle  14 ). This polymer particle, if having a low carbon yield (e.g. polyethylene particle), can be pyrolyzed to produce macroscopic pores (e.g.  18   a ), having a size that can be&gt;10 μm or can be made into smaller pores if the polymer particle size is smaller. A high carbon yield polymer (e.g. polyimide) can be pyrolyzed to produce mesoscopic pores having a pore size range of 2-500 nm or even micron-scaled pores having a pore size from 0.5 μm to 10 μm (e.g.  18   b ). 
     The lithium- or sodium-attracting metal material can contain a metal selected from Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Zn, Zr, Mo, Pd, Ag, Cd, Au, Pt, W, Al, Sn, In, Pb, Bi, Na, Li, Mg, Ca, an alloy thereof, or a mixture thereof. Any transition metal can be used, but preferably, the metal is selected from Cu, Al, Ti, Sn, Ag, Au, Fe, Mn, Zn, or an alloy thereof. 
     The porous graphene/carbon-metal particulates can be lithiated (loaded with Li; e.g.  24   a  in  FIG. 2(C)  or sodiated (loaded with Na; e.g.  24   b ) before or after the cell is made. For instance, when the cell is made, a foil or particles of lithium or sodium metal (or metal alloy) may be implemented at the anode (e.g. between a layer of multiple porous graphene/carbon-metal particulates and a porous separator) to supply this layer of porous particulates with lithium or sodium. This lithiation or sodiation procedure can occur when the lithium or sodium foil layer is in close contact with the layer of porous graphene/carbon particulates and a liquid electrolyte is introduced into the anode or the entire cell. 
     Additionally, during the first battery discharge cycle, lithium (or sodium) is ionized, supplying lithium (or sodium) ions (Li +  or Na + ) into electrolyte. These Li +  or Na +  ions migrate to the cathode side and get captured by and stored in the cathode active material (e.g. vanadium oxide, MoS 2 , S, etc.). During the subsequent re-charge cycle of the battery, Li +  or Na +  ions are released by the cathode active material and migrate back to the anode. These Li +  or Na +  ions naturally diffuse through the pore walls to reach the lithium- or sodium-attracting metal lodged inside the pores or on the inner pore walls of the porous particulates. In this manner, the particulates are said to be lithiated or sodiated. 
     Alternatively, the porous graphene/carbon particulates can be lithiated or sodiated (herein referred to as “prelithiated” or “pre-sodiated”) electrochemically prior to being incorporated as an anode layer into the cell structure. This can be accomplished by bringing a mass of porous graphene/carbon-metal particles in contact with a lithium or sodium foil in the presence of a liquid electrolyte, or by implementing a layer of graphene/carbon-metal particulates as a working electrode and a lithium/sodium foil or rod as a counter-electrode in an electrochemical reactor chamber containing a liquid electrolyte. By introducing an electric current between the working electrode and the counter-electrode, one can introduce lithium or sodium into the pores of the particulates, wherein Li +  or Na +  ions diffuse into the pores of the particulates to initially form a lithium or sodium alloy with the lithium- or sodium-attracting metal pre-lodged therein. Presumably, such an initially formed alloy can acts as a buffer zone or as a heterogeneous nucleating seed to promote growth of lithium or sodium metal in the pores. Without the inclusion of a lithium- or sodium-attracting metal in the pores, the lithium or sodium metal has a tendency to get deposited on exterior surfaces of the graphene/carbon particulates, often leading to some dendrites of Li or Na. 
     Graphene is a single-atom thick layer of sp 2  carbon atoms arranged in a honeycomb-like lattice. Graphene can be readily prepared from graphite, activated carbon, graphite fibers, carbon black, and mesophase carbon beads. Single-layer graphene and its slightly oxidized version (GO) can have a specific surface area (SSA) as high as 2670 m 2 /g. It is this high surface area that dramatically reduces the effective electrode current density, which in turn significantly reduces or eliminates the possibility of Li dendrite formation. However, we have unexpectedly observed that it is difficult for the returning lithium ions or sodium ions (those that return from the cathode back to the anode during battery charge) to uniformly deposit to graphene sheets and well-adhere to these graphene sheets in a porous graphene structure alone without the presence of a lithium- or sodium-attracting metal. Lithium or sodium has a high tendency to not adhere well to graphene surfaces or to get detached therefrom, thereby becoming isolated lithium or sodium clusters that no longer participate in reversible lithium/sodium storage. We have further surprisingly observed that such a lithium-or sodium-attracting metal, if present on the internal graphene surface or residing in pores of a graphene/carbon particulate, provides a safe and reliable site to receive and accommodate lithium/sodium during the battery charging step. The resulting lithium alloy or sodium alloy is also capable of reversibly releasing lithium or sodium ions into electrolyte that travel to the cathode side during the subsequent battery discharging step. 
     The present invention provides a method of producing graphene-carbon hybrid directly from particles of a graphitic material and metal-decorated particles of a polymer (including metal precursor polymer particles). As schematically illustrated in  FIG. 2(A) , the method begins with mixing multiple particles of a graphitic material and multiple particles of a solid polymer carrier material to form a mixture, wherein the surfaces of polymer particles are deposited (decorated) with a lithium- or sodium-attracting metal, in the form of a thin metal film or ultrafine particles (e.g. 1-100 nm). The mixture is enclosed in an impacting chamber of an energy impacting apparatus (e.g. a vibratory ball mill, planetary ball mill, high energy mill, basket mill, agitator ball mill, cryo ball mill, microball mill, tumbler ball mill, continuous ball mill, stirred ball mill, attritor mill, pressurized ball mill, freezer mill, vibratory sieve, bead mill, nanobead mill, ultrasonic homogenizer mill, centrifugal planetary mixer, vacuum ball mill, or resonant acoustic mixer). Optionally, milling balls (milling media, such as stainless steel balls or zirconia balls) may also be added. When in operation, this energy impacting device imparts kinetic energy to the solid particles contained therein, allowing polymer particles and/or milling balls to impinge upon graphite particles with high intensity and high frequency. 
     In typical operational conditions, such impacting events result in peeling off of graphene sheets from the graphitic material and transferring the graphene sheets to surfaces of the solid polymer carrier particles. These graphene sheets wrap around the metal-decorated polymer particles to form graphene-coated metal-decorated polymer particles inside the impacting chamber. This is herein referred to as the “direct transfer” process, meaning that graphene sheets are directly transferred from graphite particles to surfaces of metal-decorated polymer particles without being mediated by any third-party entities. 
     Alternatively, a plurality of impacting balls or milling media can be added to the impacting chamber of the energy impacting apparatus. These impacting balls, accelerated by the impacting apparatus, impinge upon the surfaces/edges of graphite particles with a high kinetic energy at a favorable angle to peel off graphene sheets from graphite particles. These graphene sheets are tentatively transferred to surfaces of these impacting balls. These graphene-supporting impacting balls subsequently collide with metal-decorated polymer particles and transfer the supported graphene sheets to the surfaces of these metal-decorated polymer particles. This sequence of events is herein referred to as the “indirect transfer” process. These events occur in very high frequency and, hence, most of the metal-decorated polymer particles are covered by graphene sheets typically in less than one hour. In some embodiments of the indirect transfer process, step (c) includes operating a magnet to separate the impacting balls or media from the graphene-coated metal-decorated polymer particles. 
     The isolated, individual graphene coated metal-decorated polymer particles are then pyrolyzed to thermally convert the polymer into carbon or graphite that bonds the encapsulating graphene sheets to form porous graphene-carbon hybrid particulates having a lithium- or sodium-attracting metal included therein. The pyrolyzation procedure may be preferably conducted in a fluidized bed or a flow gaseous fluid environment to prevent individual graphene/carbon particulates from sticking together. 
     Decoration or deposition of a Li- or Na-attracting metal onto polymer particle surfaces prior to being subjected to ball milling may be accomplished via using various depositing or coating means (e.g. melt dipping, solution deposition, chemical vapor deposition, physical vapor deposition, sputtering, electrochemical deposition, etc.). Alternatively, one may choose to deposit a metal-containing precursor (e.g. an organo-metallic molecule) onto the polymer particle surfaces prior to graphene encapsulation of the precursor-decorated polymer particles. During the subsequent pyrolyzation (heat treatments) of the graphene-encapsulated precursor-decorated polymer particles, the precursor is thermally converted or reduced to a metal phase, which typically resides in the pores of the particulates or adhering to the pore walls of the particulates. 
     Such graphene-carbon-metal particulates may be formed (e.g. along with a binder) into a shape and dimensions of a desired electrode (an anode). Such an electrode can be prelithiated or attached to a lithium foil and then directly impregnated with an electrolyte to form an electrolyte-impregnated electrode layer (e.g. anode). The anode layer, a separator, and a cathode layer can then be laminated (with or without an anode current collector and/or cathode current collector) to form a lithium battery cell, which is then packaged in an envelop or casing (e.g. laminated plastic-aluminum housing). Alternatively, an un-impregnated anode layer, a separator layer, and an un-impregnated cathode layer are laminated together (with or without externally added current collectors) to form a battery cell, which is inserted in a housing and impregnated with an electrolyte to form a packaged lithium battery cell. A sodium cell may be produced in a similar manner. 
     For the formation of the carbon component of the graphene/carbon hybrid particulates, one can choose polymer particles that have a high carbon yield or char yield (e.g. &gt;30% by weight of a polymer being converted to a solid carbon phase; instead of becoming part of a volatile gas). The high carbon-yield polymer may be selected from phenolic resin, poly furfuryl alcohol, polyacrylonitrile, polyimide, polyamide, polyoxadiazole, polybenzoxazole, polybenzobisoxazole, polythiazole, polybenzothiazole, polybenzobisthiazole, poly(p-phenylene vinylene), polybenzimidazole, polybenzobisimidazole, a copolymer thereof, a polymer blend thereof, or a combination thereof. When pyrolyzed, particles of these polymers become porous, as illustrated in the bottom portion of  FIG. 2(B) . 
     If a lower carbon content (higher graphene proportion relative to carbon proportion) and higher porosity proportion are desired in the graphene-carbon hybrid particulates, the polymer can contain a low carbon-yield polymer selected from polyethylene, polypropylene, polybutylene, polyvinyl chloride, polycarbonate, acrylonitrile-butadiene (ABS), polyester, polyvinyl alcohol, poly vinylidene fluoride (PVDF), polytetrafluoroethylene (PTFE), polyphenylene oxide (PPO), poly methyl methacrylate (PMMA), a copolymer thereof, a polymer blend thereof, or a combination thereof. When pyrolyzed, particles of these polymers become porous, as illustrated in the middle portion of  FIG. 2(B) . 
     These polymers (of both high and low carbon yields), when heated at a temperature of 200-2,500° C., are converted into a carbon material, which is preferentially nucleated near graphene sheet edges. Such a carbon material naturally bridges the gaps between graphene sheets, forming interconnected electron-conducting pathways. In actuality, the resulting graphene-carbon hybrid particulates contain an encapsulating layer of carbon-bonded graphene sheets that enable continuous transport of electrons and phonons (quantized lattice vibrations) between graphene sheets or domains without interruptions. When further heated at a temperature higher than 2,500° C., the carbon phase can get graphitized to further increase both the electric conductivity and thermal conductivity. The amount of non-carbon elements is also decreased to typically below 1% by weight if the graphitization time exceeds 1 hour. 
     It may be noted that an organic polymer typically contains a significant amount of non-carbon elements, which can be reduced or eliminated via heat treatments. As such, pyrolyzation of a polymer causes the formation and evolution of volatile gas molecules, such as CO 2  and H 2 O, which lead to the formation of pores in the resulting polymeric carbon phase. However, such pores also have a high tendency to get collapsed if the polymer is not constrained when being carbonized (the carbon structure can shrink while non-carbon elements are being released). We have surprising discovered that the graphene sheets wrapped around a polymer particle are capable of constraining the carbon pore walls from being collapsed. In the meantime, some carbon species also permeate to the gaps between graphene sheets where these species bond the graphene sheets together. The pore sizes and pore volume (porosity level) of the resulting graphene/carbon particulates mainly depend upon the starting polymer size and the carbon yield of the polymer. 
     The graphitic material, as a source of graphene sheets, may be selected from natural graphite, synthetic graphite, highly oriented pyrolytic graphite, graphite fiber, graphitic nanofiber, graphite fluoride, oxidized graphite, chemically modified graphite, exfoliated graphite, recompressed exfoliated graphite, expanded graphite, mesocarbon microbead, or a combination thereof. In this regard, there are several additional surprising elements associated with the presently invented process:
         (1) Graphene sheets can be peeled off from natural graphite by using polymer particles alone, without utilizing the heavier and harder impacting balls (such as zirconium dioxide or steel balls commonly used in a ball mill, for instance). The peeled-off graphene sheets are directly transferred to metal-decorated polymer particle surfaces and are firmly wrapped around the polymer particles.   (2) It is also surprising that impacting polymer particles are capable of peeling off graphene sheets from artificial graphite, such as mesocarbon microbeads (MCMBs), which are known to have a skin layer of amorphous carbon.   (3) With the assistance of harder impacting balls, the graphene-like planes of carbon atoms constituting the internal structure of a carbon or graphite fiber can also be peeled off and transferred to the metal-decorated polymer particle surfaces. This has never been taught or suggested in prior art.   (4) The present invention provides a strikingly simple, fast, scalable, environmentally benign, and cost-effective process that avoids essentially all of the drawbacks associated with prior art processes of producing graphene sheets. The graphene sheets are immediately transferred to and wrapped around the metal-decorated polymer particles, which are then readily converted to graphene-carbon hybrid particulates.       

     A certain desired degree of hydrophilicity can be imparted to the pore walls of the graphene-carbon hybrid particulates if the starting graphite is intentionally oxidized to some degree (e.g. to contain 2-15% by weight of oxygen). Alternatively, one can attach oxygen-containing functional groups to the carbon phase if the carbonization treatment is allowed to occur in a slightly oxidizing environment. 
     If a high electrical or thermal conductivity is desired, the graphitic material may be selected from a non-intercalated and non-oxidized graphitic material that has never been previously exposed to a chemical or oxidation treatment prior to being placed into the impacting chamber. Alternatively or additionally, the graphene-carbon particulates can be subjected to graphitization treatment at a temperature higher than 2,500° C. 
     X-ray diffraction patterns were obtained with an X-ray diffractometer equipped with CuKcv radiation. The shift and broadening of diffraction peaks were calibrated using a silicon powder standard. The degree of graphitization, g, was calculated from the X-ray pattern using the Mering&#39;s Eq, d 002 =0.3354 g+0.344 (1−g), where d 002  is the interlayer spacing of graphite or graphene crystal in nm. This equation is valid only when d 002  is equal or less than approximately 0.3440 nm. The graphene/carbon particulate having a d 002  higher than 0.3440 nm reflects the presence of oxygen- or fluorine-containing functional groups (such as —F, —OH, &gt;O, and —COOH on graphene molecular plane surfaces or edges) that act as a spacer to increase the inter-graphene spacing. 
     Another structural index that can be used to characterize the degree of ordering of the stacked and bonded graphene planes in the foam walls of graphene and conventional graphite crystals is the “mosaic spread,” which is expressed by the full width at half maximum of a rocking curve (X-ray diffraction intensity) of the (002) or (004) reflection. This degree of ordering characterizes the graphite or graphene crystal size (or grain size), amounts of grain boundaries and other defects, and the degree of preferred grain orientation. A nearly perfect single crystal of graphite is characterized by having a mosaic spread value of 0.2-0.4. Most of our graphene shells have a mosaic spread value in this range of 0.2-0.4 (if produced with a heat treatment temperature (HTT) no less than 2,500° C.). However, some values are in the range from 0.4-0.7 if the HTT is between 1,500 and 2,500° C., and in the range from 0.7-1.0 if the HTT is between 300 and 1,500° C. 
     In-depth studies using a combination of SEM, TEM, selected area diffraction , X-ray diffraction, AFM, Raman spectroscopy, and FTIR indicate that the graphene shells are composed of several huge graphene planes (with length/width typically »20 nm, more typically »100 nm, often »1 μm, and, in some cases, »10 μm). These giant graphene planes are stacked and bonded along the thickness direction (crystallographic c-axis direction) often through not just the van der Waals forces (as in conventional graphite crystallites), but also covalent bonds, if the final heat treatment temperature is lower than 2,500° C. In these cases, wishing not to be limited by theory, but Raman and FTIR spectroscopy studies appear to indicate the co-existence of sp 2  (dominating) and sp 3  (weak but existing) electronic configurations, not just the conventional sp 2  in graphite. 
     The graphene-carbon hybrid contain single-layer or few-layer graphene sheets chemically bonded by a carbon material having a carbon material-to-graphene weight ratio from 1/100 to 1/2, wherein the few-layer graphene sheets have 2-10 layers of stacked graphene planes having an inter-plane spacing d 002  from 0.3354 nm to 0.36 nm as measured by X-ray diffraction and the single-layer or few-layer graphene sheets contain a pristine graphene material having essentially zero % of non-carbon elements, or a non-pristine graphene material having 0.01% to 25% by weight of non-carbon elements (more typically &lt;15%) wherein the non-pristine graphene is selected from graphene oxide, reduced graphene oxide, graphene fluoride, graphene chloride, graphene bromide, graphene iodide, hydrogenated graphene, nitrogenated graphene, chemically functionalized graphene, or a combination thereof. A plurality of single-layer or few layer graphene sheets embracing the underlying polymer particles can overlap with one another to form a stack of graphene sheets. The stack can have a thickness greater than 5 nm and, in some cases, greater than 10 nm or even greater than 100 nm, if deemed necessary. 
     The graphene-carbon hybrid particulates, without the Li- or Na-attracting metal, typically have a density from 0.001 to 1.7 g/cm 3 , a specific surface area from 50 to 2,630 m 2 /g. In a preferred embodiment, the encapsulating shell contains stacked graphene planes having an inter-planar spacing d 002  from 0.3354 nm to 0.40 nm as measured by X-ray diffraction. 
     The gaps between the free ends of the graphene sheets are bonded by the carbon phase converted from a polymer. Due to these unique chemical composition (including oxygen or fluorine content, etc.), morphology, crystal structure (including inter-graphene spacing), and structural features (e.g. degree of orientations, few defects, chemical bonding and no gap between graphene sheets, and substantially no interruptions along graphene plane directions), the graphene-carbon hybrid particulates have a unique combination of outstanding thermal conductivity, electrical conductivity, mechanical strength, stiffness (elastic modulus), and resistance to permeation by the liquid electrolyte. 
     The aforementioned features and characteristics make the graphene-carbon-metal hybrid particulates an ideal battery anode active material or a lithiating agent for the following reasons.
         1) Since graphene sheets are bonded by a carbon phase to form an integral shell structure, such an encapsulating shell can prevent liquid electrolyte from permeating into the pore structure to get in direct contact with lithium metal, which is otherwise a source of interfacial instability.   2) Such integral graphene sheets bridged with a carbon phase also provide a network of electron-conducting pathways without interruption, allowing for low resistance to electron transport and enabling the option of reducing or eliminating the addition of an electron conductivity additive in the anode.   3) The lithium- or sodium-attracting metal included in the pores of the particulate enable the stable and safe storage of lithium or sodium metal that comes back from the cathode side during a recharge operation of the battery.   4) The porous graphene/carbon particulates pre-loaded with lithium or sodium metal, may be used as a prelithiating agent for an anode active material of a lithium-ion battery to overcome the loss of lithium or sodium ions due to the formation of solid-liquid interface (SEI) during battery charge/discharge cycles.   5) Thus, the presently invented process exhibits a host of many totally unexpected advantages over the conventional lithium or sodium metal battery cell production process.       

     Electrolyte is an important ingredient in a battery. A wide range of electrolytes can be used for practicing the instant invention. Most preferred are non-aqueous liquid, polymer gel, and solid-state electrolytes although other types can be used. Polymer, polymer gel, and solid-state electrolytes are preferred over liquid electrolyte. 
     The non-aqueous electrolyte to be employed herein may be produced by dissolving an electrolytic salt in a non-aqueous solvent. Any known non-aqueous solvent which has been employed as a solvent for a lithium secondary battery can be employed. A non-aqueous solvent mainly consisting of a mixed solvent comprising ethylene carbonate (EC) and at least one kind of non-aqueous solvent whose melting point is lower than that of aforementioned ethylene carbonate and whose donor number is  18  or less (hereinafter referred to as a second solvent) may be preferably employed. This non-aqueous solvent is advantageous in that it is (a) effective in suppressing the reductive or oxidative decomposition of electrolyte; and (b) high in conductivity. A non-aqueous electrolyte solely composed of ethylene carbonate (EC) is advantageous in that it is relatively stable against carbonaceous filament materials. However, the melting point of EC is relatively high, 39 to 40° C., and the viscosity thereof is relatively high, so that the conductivity thereof is low, thus making EC alone unsuited for use as a secondary battery electrolyte to be operated at room temperature or lower. The second solvent to be used in a mixture with EC functions to make the viscosity of the solvent mixture lower than that of EC alone, thereby promoting the ion conductivity of the mixed solvent. Furthermore, when the second solvent having a donor number of 18 or less (the donor number of ethylene carbonate is 16.4) is employed, the aforementioned ethylene carbonate can be easily and selectively solvated with lithium ion, so that the reduction reaction of the second solvent with the carbonaceous material well developed in graphitization is assumed to be suppressed. Further, when the donor number of the second solvent is controlled to not more than 18, the oxidative decomposition potential to the lithium electrode can be easily increased to 4 V or more, so that it is possible to manufacture a lithium secondary battery of high voltage. 
     Preferable second solvents are dimethyl carbonate (DMC), methylethyl carbonate (MEC), diethyl carbonate (DEC), ethyl propionate, methyl propionate, propylene carbonate (PC), gamma.-butyrolactone (y-BL), acetonitrile (AN), ethyl acetate (EA), propyl formate (PF), methyl formate (MF), toluene, xylene and methyl acetate (MA). These second solvents may be employed singly or in a combination of two or more. More desirably, this second solvent should be selected from those having a donor number of 16.5 or less. The viscosity of this second solvent should preferably be 28 cps or less at 25° C. 
     The electrolytic salts to be incorporated into a non-aqueous electrolyte may be selected from a lithium salt such as lithium perchlorate (LiClO 4 ), lithium hexafluorophosphate (LiPF 6 ), lithium borofluoride (LiBF 4 ), lithium hexafluoroarsenide (LiAsF 6 ), lithium trifluoro-methanesulfonate (LiCF 3 SO 3 ) and bis-trifluoromethyl sulfonylimide lithium [LiN(CF 3 SO 2 ) 2 ]. Among them, LiPF 6 , LiBF 4  and LiN(CF 3 SO 2 ) 2  are preferred. The content of aforementioned electrolytic salts in the non-aqueous solvent is preferably 0.5 to 3.5 mol/l. 
     For sodium metal batteries, the organic electrolyte may contain an alkali metal salt preferably selected from sodium perchlorate (NaClO 4 ), potassium perchlorate (KClO 4 ), sodium hexafluorophosphate (NaPF 6 ), potassium hexafluorophosphate (KPF 6 ), sodium borofluoride (NaBF 4 ), potassium borofluoride (KBF 4 ), sodium hexafluoroarsenide, potassium hexafluoroarsenide, sodium trifluoro-methanesulfonate (NaCF 3 SO 3 ), potassium trifluoro-methanesulfonate (KCF 3 SO 3 ), bis-trifluoromethyl sulfonylimide sodium (NaN(CF 3 SO 2 ) 2 ), bis-trifluoromethyl sulfonylimide potassium (KN(CF 3 SO 2 ) 2 ), an ionic liquid salt, or a combination thereof. 
     The ionic liquid is composed of ions only. Ionic liquids are low melting temperature salts that are in a molten or liquid state when above a desired temperature. For instance, a salt is considered as an ionic liquid if its melting point is below 100° C. If the melting temperature is equal to or lower than room temperature (25° C.), the salt is referred to as a room temperature ionic liquid (RTIL). The IL salts are characterized by weak interactions, due to the combination of a large cation and a charge-delocalized anion. This results in a low tendency to crystallize due to flexibility (anion) and asymmetry (cation). 
     A typical and well-known ionic liquid is formed by the combination of a 1-ethyl-3-methylimidazolium (EMI) cation and an N,N-bis(trifluoromethane)sulphonamide (TFSI) anion. This combination gives a fluid with an ionic conductivity comparable to many organic electrolyte solutions and a low decomposition propensity and low vapor pressure up to ˜300-400° C. This implies a generally low volatility and non-flammability and, hence, a much safer electrolyte for batteries. 
     Ionic liquids are basically composed of organic ions that come in an essentially unlimited number of structural variations owing to the preparation ease of a large variety of their components. Thus, various kinds of salts can be used to design the ionic liquid that has the desired properties for a given application. These include, among others, imidazolium, pyrrolidinium and quaternary ammonium salts as cations and bis(trifluoromethanesulphonyl) imide, bis(fluorosulphonyl)imide, and hexafluorophosphate as anions. Based on their compositions, ionic liquids come in different classes that basically include aprotic, protic and zwitterionic types, each one suitable for a specific application. 
     Common cations of room temperature ionic liquids (RTILs) include, but not limited to, tetraalkylammonium, di-, tri-, and tetra-alkylimidazolium, alkylpyridinium, dialkyl-pyrrolidinium, dialkylpiperidinium, tetraalkylphosphonium, and trialkylsulfonium. Common anions of RTILs include, but not limited to, BF 4   − , B(CN) 4   − , CH 3 BF 3   − , CH2CHBF 3   − , CF 3 BF 3   − , C 2 F 5 BF 3   − , n-C 3 F 7 BF 3   − , n-C 4 F 9 BF 3   − , PF 6   − , CF 3 CO 2   − , CF 3 SO 3   − , N(SO 2 CF 3 ) 2   − , N(COCF 3 )(SO 2 CF 3 ) − , N(SO 2 F) 2   − , N(CN) 2   − , C(CN) 3   − , SCN − , SeCN − , CuCl 2   − , AlCl 4   − , F(HF) 2.3   − , etc. Relatively speaking, the combination of imidazolium- or sulfonium-based cations and complex halide anions such as AlCl 4   −1 , BF 4   − , CF 3 CO 2   − , CF 3 SO 3   − , NTf 2   − , N(SO 2 F) 2   − , or F(HF) 2.3   −  results in RTILs with good working conductivities. 
     RTILs can possess archetypical properties such as high intrinsic ionic conductivity, high thermal stability, low volatility, low (practically zero) vapor pressure, non-flammability, the ability to remain liquid at a wide range of temperatures above and below room temperature, high polarity, high viscosity, and wide electrochemical windows. These properties, except for the high viscosity, are desirable attributes when it comes to using an RTIL as an electrolyte ingredient (a salt and/or a solvent) in a battery. 
     The cathode active material may be selected from a wide variety of oxides, such as lithium-containing nickel oxide, cobalt oxide, nickel-cobalt oxide, vanadium oxide, and lithium iron phosphate. These oxides may contain a dopant, which is typically a metal element or several metal elements. The cathode active material may also be selected from chalcogen compounds, such as titanium disulfate, molybdenum disulfate, and metal sulfides. More preferred are lithium cobalt oxide (e.g., Li x CoO 2  where 0.8≤x≤1), lithium nickel oxide (e.g., LiNiO 2 ), lithium manganese oxide (e.g., LiMn 2 O 4  and LiMnO 2 ), lithium iron phosphate, lithium manganese-iron phosphate, lithium vanadium phosphate, and the like. Sulfur or lithium polysulfide may also be used in a Li—S cell. 
     The rechargeable lithium metal batteries can make use of non-lithiated compounds, such as TiS 2 , MoS 2 , MnO 2 , CoO 2 , V 3 O 8 , and V 2 O 5 , as the cathode active materials. The lithium vanadium oxide may be selected from the group consisting of VO 2 , Li x VO 2 , V 2 O 5 , Li x V 2 O 5 , V 3 O 8 , Li x V 3 O 8 , Li x V 3 O 7 , V 4 O 9 , Li x V 4 O 9 , V 6 O 13 , Li x V 6 O 13 , their doped versions, their derivatives, and combinations thereof, wherein 0.1&lt;x&lt;5. In general, the inorganic material-based cathode materials may be selected from a metal carbide, metal nitride, metal boride, metal dichalcogenide, or a combination thereof. Preferably, the desired metal oxide or inorganic material is selected from an oxide, dichalcogenide, trichalcogenide, sulfide, selenide, or telluride of niobium, zirconium, molybdenum, hafnium, tantalum, tungsten, titanium, vanadium, chromium, cobalt, manganese, iron, or nickel in a nanowire, nanodisc, nanoribbon, or nanoplatelet form. These materials can be in the form of a simple mixture with sheets of a graphene material, but preferably in a nanoparticle or nanocoating form that that is physically or chemically bonded to a surface of the graphene sheets. 
     Preferably, the cathode active material for a sodium metal battery contains a sodium intercalation compound or a potassium intercalation compound selected from NaFePO 4 , KFePO 4 , Na (1−x) K x PO 4 , Na 0.7 FePO 4 , Na 1.5 VOPO 4 F 0.5 , Na 3 V 2 (PO 4 ) 3 , Na 3 V 2 (PO 4 ) 2 F 3 , Na 2 FePO 4 F , NaFeF 3 , NaVPO 4 F, KVPO 4 F, Na 3 V 2 (PO 4 ) 2 F 3 , Na 1.5 VOPO 4 F 0.5 , Na 3 V 2 (PO 4 ) 3 , NaV 6 O 15 , Na x VO 2 , Na 0.33 V 2 O 5 , Na x CoO 2 , Na 2/3 [Ni 1/3 Mn 2/3 ]O 2 , Na x (Fe 1/2 Mn 1/2 )O 2 , Na x MnO 2 , Na x K (1−x) MnO 2 Na 0.44 MnO 2 , Na 0.44 MnO 2 /C, Na 4 Mn 9 O 18 , NaFe 2 Mn(PO 4 ) 3 , Na 2 Ti 3 O 7 , Ni 1/3 Mn 1/3 CO 1/3 O 2 , Cu 0.56 Ni 0.44 HCF, NiHCF, Na x MnO 2 , NaCrO 2 , KCrO 2 , Na 3 Ti 2 (PO 4 ) 3 , NiCo 2 O 4 , Ni 3 S 2 /FeS 2 , Sb 2 O 4 , Na 4 Fe(CN) 6 /C, NaV 1−x Cr x PO 4 F, Se z S y  (y/z=0.01 to 100), Se, Alluaudites, or a combination thereof, wherein x is from 0.1 to 1.0. 
     The organic material or polymeric material-based cathode materials may be selected from Poly(anthraquinonyl sulfide) (PAQS), a lithium oxocarbon, 3,4,9,10-perylenetetracarboxylic dianhydride (PTCDA), poly(anthraquinonyl sulfide), pyrene-4,5,9,10-tetraone (PYT), polymer-bound PYT, Quino(triazene), redox-active organic material, Tetracyanoquinodimethane (TCNQ), tetracyanoethylene (TCNE), 2,3,6,7,10,11-hexamethoxytriphenylene (HMTP), poly(5-amino-1,4-dyhydroxy anthraquinone) (PADAQ), phosphazene disulfide polymer ([(NPS 2 ) 3 ]n), lithiated  1 ,4,5,8-naphthalenetetraol formaldehyde polymer, Hexaazatrinaphtylene (HATN), Hexaazatriphenylene hexacarbonitrile (HAT(CN) 6 ), 5-B enzylidene hydantoin, Isatine lithium salt, Pyromellitic diimide lithium salt, tetrahydroxy-p-benzoquinone derivatives (THQLi 4 ), N,N′-diphenyl-2,3,5,6-tetraketopiperazine (PHP), N,N′-diallyl-2,3,5,6-tetraketopiperazine (AP), N,N′-dipropyl-2,3,5,6-tetraketopiperazine (PRP), a thioether polymer, a quinone compound, 1,4-benzoquinone, 5,7,12,14-pentacenetetrone (PT), 5-amino-2,3-dihydro-1,4-dyhydroxy anthraquinone (ADDAQ), 5-amino-1,4-dyhydroxy anthraquinone (ADAM), calixquinone, Li 4 C 6 O 6 , Li 2 C 6 O 6 , Li 6 C 6 O 6 , Na x C 6 O 6  (x=1−3), Na 2 (C 6 H 2 O 4 ), Na 2 C 8 H 4 O 4  (Na terephthalate), Na 2 C 6 H 4 O 4 (Na trans-trans-muconate), or a combination thereof. 
     The thioether polymer is selected from Poly[methanetetryl-tetra(thiomethylene)] (PMTTM), Poly(2,4-dithiopentanylene) (PDTP), a polymer containing Poly(ethene-1,1,2,2-tetrathiol) (PETT) as a main-chain thioether polymers, a side-chain thioether polymer having a main-chain consisting of conjugating aromatic moieties, and having a thioether side chain as a pendant, Poly(2-phenyl-1,3-dithiolane) (PPDT), Poly(1,4-di(1,3-dithiolan-2-yl)benzene) (PDDTB), poly(tetrahydrobenzodithiophene) (PTHBDT), poly[1,2,4,5-tetrakis(propylthio) benzene] (PTKPTB, or poly[3,4(ethylenedithio)thiophene] (PEDTT). 
     The organic material that can be used as a cathode active material in a lithium metal battery or sodium metal battery may include a phthalocyanine compound selected from copper phthalocyanine, zinc phthalocyanine, tin phthalocyanine, iron phthalocyanine, lead phthalocyanine, nickel phthalocyanine, vanadyl phthalocyanine, fluorochromium phthalocyanine, magnesium phthalocyanine, manganous phthalocyanine, dilithium phthalocyanine, aluminum phthalocyanine chloride, cadmium phthalocyanine, chlorogallium phthalocyanine, cobalt phthalocyanine, silver phthalocyanine, a metal-free phthalocyanine, a chemical derivative thereof, or a combination thereof. 
     The following examples are used to illustrate some specific details about the best modes of practicing the instant invention and should not be construed as limiting the scope of the invention. 
     EXAMPLE 1 
     Production of Graphene-Carbon Hybrid Particulates from Flake Graphite via Polypropylene Powder-Based Solid Polymer Carrier Particles 
     In an experiment, 1 kg of metal-decorated polypropylene (PP) pellets, 50 grams of flake graphite, 50 mesh (average particle size 0.18 mm; Asbury Carbons, Asbury NJ) and 250 grams of magnetic steel balls were placed in a high-energy ball mill container. For incorporation of higher melting point metals (e.g. Au, Ag, Ni, Co, Mn, Fe, and Ti) as a lithium- or sodium-attracting metal in porous graphene-carbon particulates, a small but controlled amount of the desired metal was deposited on the surfaces of carrier polymer particles using sputtering or chemical solution deposition of a precursor material (e.g. HAuCl 4 , which upon heating at a desired temperature, becomes Au metal). These metal-decorated polymer particles were then utilized as the impacting media (with or without using any externally added milling media, such as zirconia beads). 
     The ball mill was operated at 300 rpm for 2 hours. The container lid was removed and stainless steel balls were removed via a magnet. The polymer carrier material was found to be coated with a dark graphene layer. Carrier material was placed over a 50 mesh sieve and a small amount of unprocessed flake graphite was removed. 
     A sample of the coated carrier material was then immersed in tetrachloroethylene at 80° C. for 24 hours to dissolve PP and allow graphene sheets to disperse in the organic solvent for the purpose of determining the nature of graphene sheets produced. After solvent removal, isolated graphene sheet powder was recovered and was found to be mostly few-layer graphene sheets. The remaining graphene-coated PP carrier particles were then heat-treated in a chamber containing flowing nitrogen gas at 350° C. and then at 600° C. for 2 hours to produce a sample of separate graphene-carbon particulates. 
     In a separate experiment, the same batch of metal-decorated PP pellets and flake graphite particles (without the impacting steel balls) were placed in the same high-energy ball mill container and the ball mill was operated under the same conditions for the same period of time. The results were compared with those obtained from impacting ball-assisted operation. The separate graphene sheets isolated from PP particles, upon PP dissolution, are mostly single-layer graphene. The graphene-carbon particulates produced from this process have a higher level of porosity (lower physical density). 
     Although polypropylene (PP) is herein used as an example, the carrier material for graphene-carbon hybrid foam production is not limited to PP. It could be any polymer provided the polymer can be made into a particulate form. We have also conducted experiments using particles of thermoplastic, thermoset, rubber, wax, mastic, gum, and organic resin, etc. as carrier particles without using externally added impacting balls. It may be noted that un-cured or partially cured thermosetting resins (such as epoxide and imide-based oligomers or rubber) can be made into a particle form at room temperature or lower (e.g. cryogenic temperature). Hence, even partially cured thermosetting resin particles can be used as a polymer carrier. 
     Graphene sheets were peeled off from graphite particle surfaces, sticking to the metal-decorated surface and embracing the underlying polymer particles. These particles were subjected to pyrolyzation (carbonization) to convert polymer into carbon. Surprisingly, carbon atoms were able to permeate around the metal coating layer to bond together graphene sheets, thereby forming a graphene-carbon-metal hybrid particulate structure. 
     In order to determine the relative stability of the graphene-carbon-metal hybrid particulate-based anode structure, the voltage profiles of symmetric layered Li-metal-decorated graphene/carbon particulate-containing layer electrode cells, symmetric layered Li-(metal free) graphene/carbon particulate electrode cells, and the bare Li foil counterparts were obtained through over 200 cycles at nominal current density of 1 mA/cm 2  (foam specific surface area not taken into account, just plain electrode surface area). The graphene/carbon particulate-containing layer electrode was made by the conventional slurry coating procedure using PVDF as a binder. 
     The symmetric layered Li-graphene/carbon particulate electrode cells exhibited stable voltage profiles with negligible hysteresis, whereas the bare Li foils displayed a rapid increase in hysteresis during cycling, by almost 100% after 100 cycles. The hysteresis growth rate of the symmetric layered Li-(metal free) graphene/carbon electrode cell is significantly greater than that of the symmetric layered Li-metal-decorated graphene/carbon particulate-containing layer electrode cell, but lower than that of the bare Li foil cell. For symmetric layered Li-metal-decorated graphene/carbon particulate-containing layer electrode cells, flat voltage plateau at both the charging and discharging states can be retained throughout the whole cycle without obvious increases in hysteresis. This is a significant improvement compared with bare Li electrodes, which showed fluctuating voltage profiles with consistently higher overpotential at both the initial and final stages of each stripping/plating process. After 300 cycles, there is no sign of dendrite formation and the lithium deposition is very even in symmetric layered Li-metal-decorated graphene/carbon particulate-containing layer electrode cells. For the symmetric layered Li-(metal-free) metal-decorated graphene/carbon particulate-containing layer electrode cells, some lithium tends to deposit unevenly on external surfaces of pores, instead of fully entering the pores. Typically, for bare Li foil electrodes, dendrite begins to develop in less than 30 cycles. 
     EXAMPLE 2 
     Graphene-Carbon Hybrid Particulates Using Expanded Graphite (&gt;100 nm in Thickness) as the Graphene Source and Acrylonitrile-Butadiene-Styrene Copolymer (ABS) as the Polymer Solid Carrier Particles 
     The ABS particles were decorated with a small amount of lithium- or sodium-attracting metal (0.1% to 30% by weight of Mg, Zn, Na, and Sn) using electroplating or sputtering. Then, in an experiment, 100 grams of metal-decorated ABS pellets, as solid carrier material particles, were placed in a plastic container along with 5 grams of expanded graphite. This container was part of an attritor mill, which was operated for 30 minutes-2 hours. After processing, metal-decorated particles of the carrier material were found to be coated with a thin layer of carbon. A small sample of carrier material was placed in acetone and subjected to ultrasound energy to speed dissolution of the ABS. The solution was filtered using an appropriate filter and washed four times with additional acetone. Subsequent to washing, filtrate was dried in a vacuum oven set at 60° C. for 2 hours. This sample was examined by optical microscopy and Raman spectroscopy, and found to be graphene. The remaining graphene-coated metal-decorated ABS particles were then carbonized to prepare graphene-carbon particulates under different temperature conditions. 
     EXAMPLE 3 
     Production of Porous Graphene-Carbon Hybrid Particulates From Mesocarbon Microbeads (Mcmbs) as the Graphene Source Material and Polyacrylonitrile (PAN) Fibers (as Solid Carrier Particles) 
     The PAN fiber segments were deposited with a small amount of lithium- or sodium-attracting metal (0.1% to 35% by weight of Mg, Zn, Na, K, Li, and Sn). In one example, 100 grams of metal-decorated PAN fiber segments (2 mm long as the carrier particles), 5 grams of MCMBs (China Steel Chemical Co., Taiwan), and 50 grams of zirconia beads were placed in a vibratory ball mill and processed for 2 hours. After the process was completed, the vibratory mill was then opened and the metal-decorated particles (fiber segments) of the carrier material (PAN) were found to be coated with a dark coating of graphene sheets. The zirconia particles, having distinctly different sizes and colors were manually removed. The graphene-coated metal-decorated PAN fibers were then subjected to a heat treatment at 250° C. for 1 hour (in room air), 350° C. for 2 hours, and 1,000° C. for 2 hours (under an argon gas atmosphere) to obtain porous graphene-carbon particles. Half of the carbonized particulates were then heated to 2,850° C. and maintained at this temperature for 0.5 hours. 
     EXAMPLE 4 
     Particles of Cured Phenolic Resin as the Polymer Carrier in a Tumbler Mill 
     In one experiment, 10 grams of Ag-coated or Au-coated phenolic resin particles were placed in a tumbler mill container along with 0.25 grams of HOPG powder derived from graphitized polyimide and a magnetic stainless steel impactor. The same experiment was performed, but the mill container did not contain any impactor balls. These processes were carried out in a 1%-humidity “dry room” to reduce the condensation of water onto the completed product. The mill was operated for 30-120 minutes. After operation, the contents of the container were sorted to recover graphene-coated metal-decorated resin particles by removing residual HOPG powder and impactor balls (when used). 
     The resulting graphene-wrapped, metal-decorated resin particles in both cases (with or without impactor balls) were examined using both digital optical microscopy and scanning electron microscopy (SEM). It was observed that the thickness of the graphene sheets wrapped around resin particles increases with the milling operation time and, given the same duration of operation, the impactor-assisted operation leads to thicker graphene coating. 
     A mass of graphene-wrapped, metal-coated resin particles were then subjected to pyrolysis treatments at 400° C. in a fluidized bed and then 1,000° C. in a furnace to produce graphene/carbon particles containing Ag or Au coated on internal surfaces of graphene. 
     EXAMPLE 5 
     Natural Graphite Particles as the Graphene Source, Polyethylene (PE) and Nylon 6/6 Beads as the Solid Carrier Particles, and Optional Ceramic or Glass Beads as Added Impacting Balls 
     The polymer particles were electrochemically deposited with a small amount of lithium- or sodium-attracting metal (0.1% to 15% by weight of Mg, Zn, Mn, and Sn). In a subsequent experiment, 0.5 kg of metal-decorated PE or nylon beads, 50 grams of natural graphite (source of graphene sheets) and 250 grams of zirconia powder (impacting balls) were placed in containers of a planetary ball mill. The ball mill was operated at 300 rpm for 4 hours. The container lid was removed and zirconia beads (different sizes and weights than graphene-coated PE beads) were removed through a vibratory screen. The metal-decorated polymer particles were found to be coated with a dark graphene layer. The resulting graphene-encapsulated, metal-decorated PE particles were placed over a 50 mesh sieve and a small amount of unprocessed flake graphite was removed. In a separate experiment, glass beads were used as the impacting balls; other ball-milling operation conditions remained the same. 
     A mass of graphene-coated PE pellets and a mass of graphene-coated nylon beads were separately subjected to pyrolyzation (by heating the powder in a fluidized bed chamber from 100° C. to 650° C.). SEM examination of the resulting particulates indicates that carbon phases are present near the edges of graphene sheets and these carbon phases act to bond the graphene sheets together. The carbon-bonded graphene sheets form a skeleton of graphene-carbon hybrid pore walls having pores being present in what used to be the space occupied by the original polymer particles, as schematically illustrated in  FIG. 2(A) . 
     EXAMPLES 6 
     Micron-Sized Rubber Particles as the Solid Polymer Carrier Particles 
     The experiment began with preparation of micron-sized rubber particles. A mixture of methylhydro dimethyl-siloxane polymer (20 g) and polydimethylsiloxane, vinyldimethyl terminated polymer (30 g) was obtained by using a homogenizer under ambient conditions for 1 minute. Tween 80 (4.6 g) was added and the mixture was homogenized for 20 seconds. Platinum-divinyltetramethyldisiloxane complex (0.5 g in 15 g methanol) was added and mixed for 10 seconds. This mixture was added to 350 g of distilled water and a stable latex was obtained by homogenization for 15 minutes. The latex was heated to 60° C. for 15 hours. The latex was then de-emulsified with anhydrous sodium sulfate (20 g) and the silicone rubber particles were obtained by filtration under a vacuum, washing with distilled water, and drying under vacuum at 25° C. The particle size distribution of the resulting rubber particles was 3-11 μm. 
     In one example, 10 grams of metal-decorated rubber particles, 2 grams of natural graphite, and 5 grams of zirconia beads were placed in a vibratory ball mill and processed for 2 hours. After the process was completed, the vibratory mill was then opened and the rubber particles were found to be coated with a dark coating of graphene sheets. The zirconia particles were manually removed. The graphene-coated, metal-decorated rubber particles were then subjected to a heat treatment at 350° C. in a flowing nitrogen environment for 1 hour, 650° C. for 2 hours, and then 1,000° C. for 1 hour in a tube furnace to obtain porous graphene/carbon particulates. 
     EXAMPLES 7 
     Preparation of Porous Graphene Fluoride/Carbon Hybrid Particulates 
     In a typical procedure, a powder mass of graphene/carbon hybrid particulates prepared in Example 6 was fluorinated by vapors of chlorine trifluoride in a sealed autoclave reactor to yield fluorinated graphene-carbon hybrid particulates. Different durations of fluorination time were allowed for achieving different degrees of fluorination. Compared to pristine graphene/carbon and reduced graphene oxide/carbon-based porous particulates, the graphene fluoride/carbon hybrid particulates were found to be more chemically compatible with the commonly used electrolytes in lithium-ion battery industry. 
     EXAMPLE 8 
     Preparation of Graphene Oxide/Carbon Hybrid Particulates and Nitrogenated Graphene-Carbon Hybrid Particulates 
     Several samples of graphene/carbon particulates prepared in Example 3 were immersed in a 30% H 2 O 2 -water solution for a period of 2-48 hours to obtain graphene oxide (GO)/carbon particulates, having an oxygen content of 2-25% by weight. 
     Some GO/carbon particulates were mixed with different proportions of urea and the mixtures were heated in a microwave reactor (900 W) for 0.5 to 5 minutes. The products were washed several times with deionized water and vacuum dried. The products obtained were nitrogenated graphene/carbon particulates. The nitrogen contents were from 3 wt. % to 17.5 wt. %, as measured by elemental analysis. 
     EXAMPLE 9 
     Characterization of Various Graphene/Carbon Particulates 
     The internal structures (crystal structure and orientation) of several series of graphene/carbon particulates were investigated using X-ray diffraction. The X-ray diffraction curve of natural graphite typically exhibits a peak at approximately  2 θ=26°, corresponds to an inter-graphene spacing (d 002 ) of approximately 0.3345 nm. The graphene shells of the hybrid particulates exhibit a d 002  spacing typically from 0.3345 nm to 0.40 nm, but more typically up to 0.34 nm. 
     With a heat treatment temperature of 2,750° C. of the particulates for one hour, the d 002  spacing is decreased to approximately to 0.3354 nm, identical to that of a graphite single crystal. In addition, a second diffraction peak with a high intensity appears at 2θ=55° corresponding to X-ray diffraction from (004) plane. The (004) peak intensity relative to the (002) intensity on the same diffraction curve, or the I(004)/I(002) ratio, is a good indication of the degree of crystal perfection and preferred orientation of graphene planes. The (004) peak is either non-existing or relatively weak, with the I(004)/I(002) ratio &lt;0.1, for all graphitic materials heat treated at a temperature lower than 2,800° C. The I(004)/I(002) ratio for the graphitic materials heat treated at 3,000-3,250° C. (e.g., highly oriented pyrolytic graphite, HOPG) is in the range from 0.2-0.5. In contrast, a graphene foam prepared with a final HTT of 2,750° C. for one hour exhibits a I(004)/I(002) ratio of 0.78 and a Mosaic spread value of 0.21. 
     The “mosaic spread” value is obtained from the full width at half maximum of the (002) reflection in an X-ray diffraction intensity curve. This index for the degree of ordering characterizes the graphite or graphene crystal size (or grain size), amounts of grain boundaries and other defects, and the degree of preferred grain orientation. A nearly perfect single crystal of graphite is characterized by having a mosaic spread value of 0.2-0.4. Some of our graphene/carbon particulates have a mosaic spread value in this range of 0.3-0.6 when produced using a final heat treatment temperature no less than 2,500° C. 
     The following are a summary of some of the more significant results:
         1) In general, the addition of impacting balls helps to accelerate the process of peeling off graphene sheets from graphite particles. However, this option necessitates the separation of these impacting balls after graphene-coated metal-decorated polymer particles are made.   2) When no impacting balls (e.g. ceramic, glass, metal balls, etc.) are used, harder polymer particles (e.g. PE, PP, nylon, ABS, polystyrene, high impact polystyrene, etc. and their filler-reinforced versions) are more capable of peeling off graphene sheets from graphite particles, as compared to softer polymer particles (e.g. rubber, PVC, polyvinyl alcohol, latex particles).   3) Without externally added impacting balls, softer polymer particles tend to result in graphene-coated particles having 0.001% to 5% by weight of graphene (mostly single-layer graphene sheets) and harder polymer balls tend to lead to graphene-coated particles having 0.01% to 30% by weight of graphene (mostly single-layer and few layer graphene sheets), given the same 1 hour of operating time.   4) With externally added impacting balls, all metal-decorated polymer balls are capable of supporting from 0.001% to approximately 40% by weight of graphene sheets (mostly few-layer graphene, &lt;10 layers, if over 30% by weight of graphene sheets).   5) The presently invented method also allows for convenient and flexible control over the chemical composition (e.g. F, O, and N contents, etc.), responsive to various battery electrolytes used.       

     EXAMPLE 10 
     Evaluation of Various Lithium Metal And Sodium Metal Cells 
     In a conventional cell, an electrode (e.g. cathode) is typically composed of 85% an electrode active material (e.g. MoS 2 , V 2 O 5 , inorganic nanodiscs, etc.), 5% Super-P (acetylene black-based conductive additive), and 10% PTFE, which were mixed in NMP solvent to form a slurry. The slurry was then coated on Al foil. The thickness of electrode was around 50-150 μm. A wide variety of cathode active materials were implemented to produce lithium metal batteries and sodium metal batteries. Anode layers were similarly made using graphene/carbon particulates as an anode active material. Some of the porous particulates were pre-loaded with lithium or sodium metal. Several lithium-ion cells were also made that comprised lithium-preloaded graphene/carbon particulates as a first anode active material and a conventional anode material (e.g. particles of graphite or Si) as a second anode active material in the anode. The graphene/carbon particles pre-loaded with lithium were used as a prelithiating agent for the conventional anode active material. 
     For each sample, both coin-size and pouch cells were assembled in a glove box. The charge storage capacity was measured with galvanostatic experiments using an Arbin SCTS electrochemical testing instrument. Cyclic voltammetry (CV) and electrochemical impedance spectroscopy (EIS) were conducted on an electrochemical workstation (CHI 660 System, USA). 
     For each sample, several current density (representing charge/discharge rates) were imposed to determine the electrochemical responses, allowing for calculations of energy density and power density values required of the construction of a Ragone plot (power density vs. energy density). 
     Shown in  FIG. 3(A)  are Ragone plots (gravimetric power density vs. energy density) of two sets of lithium metal cells: (a) first cell containing a layer of porous nitrogen-doped graphene-carbon-metal (Zn) particulates bonded by PVDF, in physical contact with a lithium foil, as the anode active material; (b) the second cell containing no lithium-attracting metal (Zn) inside the porous graphene/carbon particulates. These plots indicate that the energy density and power density ranges of these two cells are comparable. However, SEM examination of the cell samples, taken after 30 charge-discharge cycles, indicates that the sample containing a Li-attracting metal has essentially all the lithium ions returning from the cathode during charge being encased inside pores of the particulates, having no tendency to form lithium dendrites. In contrast, for the cell containing no lithium-attracting metal, lithium metal tends to get re-plated on external surfaces of graphene/carbon particulates in a less uniform manner. Further surprisingly, as shown in  FIG. 3(B) , the cell containing nitrogen-doped graphene/carbon-metal (Zn) hybrid particulates exhibits a more stable cycling behavior. 
     Shown in  FIG. 4  are battery cell capacity decay curves of two sodium metal cells. One cell contains a layer of pristine graphene/carbon-metal (Mg) particulates and a sheet of Na foil as the anode active material, and NaFePO 4  as the cathode active material. For comparison, a sodium metal cell containing pristine graphene/carbon particulates (but no sodium-attracting metal included therein) and a sheet of Na foil as the anode active material is also investigated. The cell having a sodium-attracting metal residing in pores of graphene/carbon particulates shows a significantly more stable cycling behavior. 
     In conclusion, we have successfully developed a new, novel, unexpected, and patently distinct class of highly conducting graphene/carbon-metal hybrid particulates that can be used in a lithium metal battery or sodium metal battery for overcoming the dendrite issues. This class of new materials has now made it possible to use lithium metal and sodium metal batteries that have much higher energy densities as compared to the conventional lithium-ion cells. Additionally, the graphene/carbon-metal hybrid particulates, preloaded with lithium or sodium, may be used as a prelithiating agent or pre-sodiating agent for a conventional lithium-ion battery or sodium-ion battery, respectively.