Patent Publication Number: US-2023155168-A1

Title: All Solid-State Lithium-Ion Battery Incorporating Electrolyte-Infiltrated Composite Electrodes

Description:
REFERENCE TO RELATED APPLICATION 
     This is a divisional application of U.S. patent application Ser. No. 17/140,690 which was filed on Jan. 4, 2021 and which is incorporated herein by reference. 
    
    
     The invention was made with Government support under SBIR Grant No. N6833518C0685 awarded by the U.S. Navy to Bioenno Tech LLC. 
    
    
     FIELD OF THE INVENTION 
     The present invention generally relates to electrochemical devices and, more particularly, to electrolyte-infiltrated composite electrodes exhibiting a network of electrolyte which improves the cycling stability and lifetime of all solid-state lithium-ion electrochemical cells and batteries through establishing Li-ion transport pathways in the electrode and strengthening contact between the electrode layer and solid state-electrolyte membrane. 
     BACKGROUND OF THE INVENTION 
     Non-aqueous lithium electrochemical cells typically include an anode, a lithium electrolyte prepared from a lithium salt dissolved in organic solvents, and a cathode of an electrochemically active material. Organic solvents are added to solvate the lithium salt which provides mobile ions. During the electrochemical discharge process lithium ions are transported through the electrolyte from the anode to the cathode. As lithium ions are taken up by the cathode, there is a simultaneous release of electrical energy. 
     Solid-state electrolyte (SSE) can replace conventional organic liquid electrolytes, which are generally flammable and toxic. Conventional electrode materials and lithium metal anodes can be employed with a SSE. Lithium anodes have high inherent high capacities (C) which increase the cell voltage (V) and thereby improves the energy density of the battery (E=VC). There are two critical challenges to achieving high performance batteries using SSE, which are (1) low ionic conductivities of many SSE, and (2) the low mechanical strengths of electrolyte materials do not adequately prevent Li dendrite growth. SSE which are being explored are typically inorganic-based (depending on the lattice structure, they are garnet, perovskite, glass-ceramics etc.) and polymer-based. Solid polymer electrolytes can be manufactured by relatively simple, inexpensive techniques whereas fabricating solid inorganic electrolytes with well-defined compositions or lattice structures requires high temperature processes. Due to the high degree of coordination between Li ions and the polymer chain in sold-state polymer electrolytes, the chain-assisted Li +  transport mechanism is less robust at room temperature or below the melting temperature of the polymer. The attendant poor ionic conductivity is attributed to interference with Li ion transport. The addition of plasticizers to the solid-state polymer-based electrolyte improves the polymer chain mobility at room temperature which results in an increase in the ionic conductivity, but the plasticizers also reduce the mechanical strength of the solid-state polymer-based electrolyte. 
     So-called all-solid-state batteries contain exclusively solid materials, and in particular solid-state electrolytes, in contrast to conventional batteries containing liquid electrolytes. One of the main concerns of current all solid-state lithium-ion batteries (ASSLiB) is the poor contact between solid electrolyte and electrodes. The high contact resistance causes low rate capability and poor cycling stability. With solid polymer electrolytes, lithium dendrites, which develop as an electrochemical cell undergoes charging and discharging cycles, can penetrate through the ‘plasticizer-softened’ polymer electrolytes to short circuit the cell. 
     SUMMARY OF THE INVENTION 
     The present invention is based, in part, on the development of an electrolyte (ceramic-polymer nanocomposite)—infiltrated composite electrode that has a 3-dimensional polymer matrix with ceramic nanoparticles distributed or embedded in the matrix. In one aspect, the invention is directed to a ceramic-polymer-containing composite electrode that includes: (i) a polymer matrix, (ii) ceramic nanoparticles that are distributed in the polymer matrix, (iii) a lithium salt, (iv) a plasticizer, (v) an anode active material or cathode active material that is distributed in the polymer matrix, (vi) a conducting agent that is distributed in the polymer matrix, (vii) additional binder (optional), for instance, if the weight ratio of active material is high. 
     In another aspect, the invention is directed to a ceramic-polymer-infiltrated composite electrolyte membrane that includes: (i) a polymer matrix, (ii) ceramic nanoparticles with diameters that range from 10 to 2000 nm that are distributed in the polymer matrix, (iii) a plasticizer (iv) a lithium salt, wherein the ceramic nanoparticles are selected from the group consisting of ceramic materials having the basic formula Li 7 La 3 Zr 2 O 12 (LLZO) and its dopant derivatives, such as Al x Li 7-x La 3 Zr 2-y-z Ta y Nb z O 12  where x ranges from 0 to 0.85, y ranges from 0 to 0.50 and z ranges from 0 to 0.75, wherein at least one of x, y and z is not equal to 0, and mixtures thereof. Incorporating ceramic nanoparticles to enhance the mechanical strengths of polymer electrolytes can suppress Li dendrite growth, which significantly improves the cycling stability of batteries based on ceramic-polymer composite solid electrolytes. Moreover, nano-sized ceramic particles have excellent miscibility with the polymer materials and the particles afford ionic transport channels which facilitate ion transport within the ceramic-polymer solid electrolyte layer. The ceramic-polymer composite electrolyte exhibits high ionic conductivity over a wide temperature window. 
     In a further aspect, the invention is directed to an electrochemical cell which includes: (a) an electrolyte-infiltrated composite anode that includes: (i) a first polymer matrix, (ii) first ceramic nanoparticles that are distributed in the first polymer matrix, (iii) a lithium salt, (iv) a plasticizer, (v) an anode active material that is distributed in the first polymer matrix, (vi) a first conducting agent that is distributed in the first polymer matrix, and (vii) additional binder if weight ratio of active material is high (&gt;80 wt %); 
     (b) an electrolyte-infiltrated composite cathode that includes: (i) a second polymer matrix that can be same as the first polymer matrix for the composite anode, (ii) a second ceramic nanoparticles that can be same as the first ceramic nanoparticles for the composite anode and that are distributed in the second polymer matrix, (iii) a lithium salt, (iv) a plasticizer, (v) a cathode active material that is distributed in the second polymer matrix, (vi) a second conducting agent that can be same as the first conducting agent for the composite anode and that is distributed in the second polymer matrix, and (vii) additional binder if the weight ratio of active material is high (&gt;80 wt %); and 
     (c) interposed between the anode and the cathode, a solid-state electrolyte which comprises a ceramic-polymer composite electrolyte membrane that includes: (i) a third polymer matrix that can be same as the polymer matrix for the composite electrodes, (ii) third ceramic nanoparticles with diameters that range from 10 to 2000 nm that can be same as the ceramic nanoparticles for the composite electrodes and that are distributed in the third polymer matrix, (iii) a plasticizer and (iv) a lithium salt, wherein the third ceramic nanoparticles are selected from the group consisting of ceramic materials having the basic formula Li 7 La 3 Zr 2 O 12  (LLZO) and its derivatives, such as Al x Li 7-x La 3 Zr 2-y-z Ta y Nb z O 12  where x ranges from 0 to 0.85, y ranges from 0 to 0.50 and z ranges from 0 to 0.75, wherein at least one of x, y and z is not equal to 0, and mixtures thereof. The presence of undoped LLZO (Li 7 La 3 Zr 2 O 12 ) and/or doped LLZO enhances the ionic conductivity of the electrolyte membrane. Particularly preferred doped LLZO has (i) Al and Ta or (ii) Nb. The ceramic-polymer composite electrolyte is a solid-state electrolyte that exhibits excellent chemical and electrochemical stability with respect to the anode and cathode. 
     In this electrochemical cell, the cathode&#39;s polymeric networking structure of electrolyte serves as ionic conductive pathways for electrons and Li +  transport for active material particles during the lithiated/delithiated process. This continuous Li +  conductive network in the cathode composite produces a cathode with higher energy/power performance. The crosslinking structure of the polymeric network or polymer matrix strongly binds all of the cathode components. The composite anode and composite cathode form good physical interfacial contacts with the composite electrolyte membrane for improved rate performance and cycling stability. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         FIG.  1 A  depicts the networking structure of the electrolyte and resultant electrolyte-infiltrated composite electrode. 
         FIG.  1 B  is an apparatus for producing electrolyte-infiltrated composite cathodes and anodes. 
         FIG.  1 C  depicts a gradient of nanoparticles within the electrolyte-infiltrated composite; 
         FIG.  2    is a specific designed module for in-situ polymerization of a solid-state electrolyte. 
         FIG.  3 A  is a cross sectional illustration of an electrochemical cell. 
         FIG.  3 B  depicts a coil cell. 
         FIG.  3 C  depicts a pouch cell. 
         FIG.  3 D  is a cross-section scanning electrode microscopy (SEM) image of an electrochemical cell containing an electrolyte-infiltrated cathode, electrolyte-infiltrated anode and polymer (e.g., PEGDA)—ceramic (e.g., LLZO) SSE. 
         FIGS.  4 A- 4 C  are charge-discharge profiles of coin cells comparing the performance of cells with different cathode formulations. 
         FIGS.  5 A- 5 C  are cycling stability profiles of coin cells comparing the performance of cells with different cathode formulations. 
         FIGS.  6 A- 6 C  are cycling stability profiles of coin cells comparing the performance of cells with different anode formulations. 
         FIGS.  7 A and  7 B  are the charge-discharge profiles and cycling stability profiles, respectively, for coin cells. 
     
    
    
     DETAILED DESCRIPTION OF PREFERRED EMBODIMENTS 
     This invention is directed to ceramic-polymer electrolyte infiltrated composite electrodes (cathodes and anodes) that are particularly suited for used in lithium-ion electrochemical cells and batteries. The electrode has a polymer-based electrolyte forming a 3 dimensional-like networking structure in which (1) active materials (cathode or anode), (2) conducting agent, and (3) lithium salt and (4) ceramic nanoparticles are homogeneously distributed throughout the network. The electrode can include a plasticizer and a binder, if required. 
     The active materials for anodes include any compatible anodic material which functions as an anode in solid lithium-ion electrochemical cells. Preferred anode active materials are graphite based and silicon-based materials. 
     The active materials for cathodes include any compatible cathodic material which functions as a positive pole in a solid lithium electrochemical cell. Preferred cathode active materials which are compatible with the polymer-based electrolyte comprise, for example, LiFePO 4  (LFP), LiNi 0.8 Co 0.1 Mn 0.1 O 2  (NCM811), LiNi 0.5 Co 0.2 Mn 0.3 O 2  (NCM 523) and LiNi 0.6 Co 0.2 Mn 0.2 O 2  (NCM 622) and mixtures thereof. 
     The conducting agent is an electronically conductive material that is preferably made of carbon, in particular elemental carbon. The electronically conducting agent can be, for example, carbon black. 
     The lithium salt is any lithium salt suitable for solid lithium electrochemical cells. These include, for example, bis(trifluoromethane)sulfonimide lithium salt (LiTFSI), lithium hexafluorophosphate (LiPF 6 ), lithium hexafluoroarsenate (LiAsF 6 ), LiClO 4 , lithium bis(oxalato)borate (LiBoB), and mixtures thereof. 
     The polymer matrix component of the electrolyte is formed from a mixture of monomers, oligomers or partial polymers thereof (collectively referred to as polymer precursors). Preferred polymer matrices comprise poly(ethylene oxide) (PEO), poly(ethylene glycol diacrylate) (PEGDA), poly(acrylonitrile (PAN), polysiloxane, poly(vinylidene fluoride-co-hexafluoropropylene) [P(VDF-HFP)], poly(methyl methacrylate) (PMMA), and mixtures thereof. 
     The ceramic nanoparticles comprise lithium metal oxides with diameters that range from 10 nm to 2000 nm. Preferred ceramic nanoparticles include Li 7 La 3 Zr 2 O 12  (LLZO) and derivatives thereof wherein specific quantities of Al, Ta and/or Nb are substituted at the Zr sites. Derivatives include, for example, Al x Li 7-x La 3 Zr 2-y-z Ta y Nb z O 12  where x ranges from 0 to 0.85, y ranges from 0 to 0.50 and z ranges from 0 to 0.75, wherein at least one of x, y and z is not equal to 0, and mixtures thereof. Particularly preferred ceramic nanoparticles are Al x Li 7-x La 3 Zr 1.75 Ta 0.25 O 12  (x ranges from 0.01 to 0.85) and Li 7 La 3 Zr 2-z Nb z O 12  (z ranges from 0.01 to 0.60) which exhibit improved the ionic transport in the electrodes. 
     LLZO and derivatives thereof are commercially available from Millipore Sigma (St. Louis, Mo.) and MSE Supplies (Tucson, Ariz.). Derivatives of LLZO can be manufactured by standard solid-state techniques using different proportions of Al 2 O 3 , Ta 2 O 5 , and/or Nb 2 O 5 . For example, Al x Li 7-x La 3 Zr 1.75 Ta 0.25 O 12  wherein x ranges from 0 to 0.85 is synthesized by mixing stoichiometric amounts of starting powders including LiOH.H 2 O, La 2 O 3 , ZrO 2 , Al 2 O 3  and Ta 2 O 5  and milling the mixture via high energy ball milling in ethanol media for 8-12 hrs. Zirconia balls (average diameter of 5 mm) balls at a ball-to-powder weight ratio of about 20:1 and about 360 rpm milling speed. After milling, the collected slurry is dried (80° C., 2-3 hrs.), crushed, and sieved (through a 200 mesh), and calcined at about 900° C. for 6 hours to fully decompose LiOH. The as-calcined powders are then ball-milled again in ethanol for 6-12 hrs. Planetary ball mill was used, followed by drying process. The dried powders were pressed into pellets with diameters of about 9.5 mm at about 300 MPa, and then sintered with a temperature range from 800° C. to 1150° C. for about 4 hrs. to obtain particles with size from 100 nm to 2000 nm. Both calcination and sintering processes are carried out with samples in alumina crucibles covered by alumina lids, and the pellets are embedded in corresponding mother powder in order to mitigate losses of volatile components and accidental contamination. 
     The plasticizer is a compound that is preferably solid at room temperature (20° C.) and serves as a liquid medium in which the polymer precursors can polymerize to form a polymer matrix. Preferred plasticizers are organic compounds such as succinonitrile (SCN), sulfolane (SL), ethylene carbonate (EC), dimethyl sulfoxide (DMSO), glutaronitrile (GN), propylene carbonate (PC), and mixtures thereof. 
     Binders such as polyvinylidene fluoride (PVDF) and polyacrylic acid (PAA) can be used as necessary. PVDF is used if the weight ratio of active material is high. In the case of anodes, binders can be used if the active material is about 80 wt % or more and in the case of cathodes binders can be used if the active material is about 80 wt % or more. 
     Anodes of the present invention typically include 60 to 96 wt % anode material, 1 to 15 wt % conducting agent, 0.1 to 10 wt % lithium salt, 0.1 to 5 wt % ceramic nanoparticles, 0.1 to 10 wt % plasticizer, 0.1 to 5 wt % polymer matrix and 0 to 15 wt %, binder. 
     Cathodes of the present invention typically include 60 to 96 wt % cathode material, 1 to 15 wt % conducting agent, 0.1 to 10 wt % lithium salt, 0.1 to 5 wt % ceramic nanoparticles, 0.1 to 10 wt % plasticizer, 0.1 to 5 wt % polymer matrix and 0 to 15 wt %, binder. 
     The composite electrode as depicted in  FIG.  1 A  has a polymer network or matrix with cathode or anode active materials, conducting agents, lithium ions and ceramic nanoparticles that distributed or infiltrated within the matrix. The composite electrode with its 3-D polymer network structure exhibits (i) enhanced ion-transport and (ii) improved contact with solid electrolytes. Lithium-ion batteries incorporating these composite electrodes will have high energy densities, excellent rate performances and long cycle lifetimes. 
       FIG.  1 B  shows a tape-casting system  2  for preparing the composite electrode. The anode or cathode active materials, conducting agent and binder are preferably dried under vacuum before being added into tank  6 . A mixture of polymer precursor and plasticizer is added to tank  6  to form a precursor slurry, which also contains 0.001 wt % to 1.0 wt % of a photoinitiator such as phenyl bis(2,4,6-trimethylbenzoyl)phosphine oxide (819). An adjustable doctor blade  12  coats a wet film  8  of the precursor slurry of the desired thickness onto the current collector foil  10  which is supported by stationary roll  14 . UV radiation directed to wet film  8  from UV source  16  initiates in-situ radical polymerization to crosslink the polymer precursor in the electrode composite  18 . The monomer or polymer precursors polymerize and/or crosslinked, which establishes polymer network that has strong interactions with the other components in the electrode. Therefore, the polymer matrix can act as binder and completely or partial replace the traditional binder such as PVDF. It has been found that ceramic nanoparticles accumulate toward the top of the composite electrode  18  so that a ceramic nanoparticle gradient is established within layer  18  along the direction of the thickness. As shown in  FIG.  1 C , a cathode substrate  10  is laminated with a layer of composite electrode wherein polymer matrix  60  is formed on substrate  10  and the nanoparticles  62  are not homogeneously distributed. The upper side of the composite electrode on which the anode is disposed has a higher concentration of ceramic nanoparticles which acts as a barrier to lithium dendrite growth. To fabricate electrodes with the ceramic nanoparticles homogeneously distributed therein, the polymer precursors should be cured rapidly or adjusted to have a higher viscosity in order to prevent potential migration of the nanoparticles in the course of processing. 
     As an example, to prefabricate an electrolyte-infiltrated composite anode by tape-casting method without using a binder, a precursor slurry comprising 1 wt % to 10 wt % carbon black, 60 wt % to 96 wt % graphite and 1 wt % to 20 wt % polymer precursor are mixed at 50° C. to 70° C. for at least 12 hours in N-Methyl-2-pyrrolidone (NMP) solvent. Typical solvent-to-solid ratio is 1 ml to 0.5 g˜1.0 g solid. The slurry is printed on an anode current collector, typically copper foil, by tape-casting method and the printed sheets are under UV light for 10 minutes. Finally, the sheets are dried, calendared and cut. 
     As an example, to fabricate an electrolyte-infiltrated composite cathode by a tape-casting method without using a binder, 1 wt % to 10 wt % carbon black, 60 wt % to 96 wt % LFP and 1 wt % to 20 wt % polymer precursors are mixed in N-Methyl-2-pyrrolidone (NMP) solvent. Typical solvent-to-solid ratio is 1 ml to 0.6 g˜1.2 g solid. The slurry is printed on cathode current collector, typically aluminum foil, by tape-casting method and the printed sheets are under UV light for 10 minutes. Finally, the sheets are dried, calendared and cut. 
     The ceramic-polymer nanocomposite exhibits outstanding ionic conductivities of over 1×10 −3  S/cm from a temperature range of −30° C. to 10° C. and that is higher than 1×10 −3  S/cm when measured at a temperature of 20° C. or higher and wide electrochemical window of up to 4.8V at room temperature. Moreover, it is thermally stable below 150° C. and low glass transition temperature of −60° C. Finally, this electrolyte shows low interfacial resistance, good compatibility with both lithium metal as anode material, other anode materials and cathode materials, with enhanced mechanical strength with a Young&#39;s modulus that exceeds 50 MPa. 
     Anodes and cathodes of the present invention can be used in solid-state lithium ion electrochemical cells and batteries with solid-state polymer electrolytes. A particularly preferred solid-state electrolyte is a ceramic-polymer composite electrolyte membrane that comprises: (i) a polymer matrix, (ii) ceramic nanoparticles with diameters that range from 10 to 2000 nm that are distributed in the polymer matrix, (iii) a plasticizer (iv) a lithium salt, wherein the ceramic nanoparticles are selected from the group consisting of ceramic materials having the basic formula Li 7 La 3 Zr 2 O 12 (LLZO) and derivatives thereof wherein specific quantities of Al, Ta and/or Nb are substituted at the Zr sites. Derivatives include, for example, Al x Li 7-x La 3 Zr 2-y-z Ta y Nb z O 12  where x ranges from 0 to 0.85, y ranges from 0 to 0.50 and z ranges from 0 to 0.75, wherein at least one of x, y and z is not equal to 0, and mixtures thereof. Particularly preferred ceramic nanoparticles are Al x Li 7-x La 3 Zr 1.75 Ta 0.25 O 12  (x ranges from 0.01 to 0.85) and Li 7 La 3 Zr 2-z Nb z O 12  (z ranges from 0.01 to 0.60). 
     The polymer matrix, ceramic nanoparticles, plasticizer and lithium salt used for the electrolyte membrane can be the same as those used in preparing the inventive ceramic-polymer composite electrodes. The ceramic-polymer composite electrolyte membrane typically includes 20 to 60 wt % lithium salt, 5 to 60 wt % ceramic nanoparticles, 10 to 60 wt % plasticizer, and 10 to 50 wt % polymer matrix. The electrolyte membrane exhibits an ionic conductivity of higher than 1×10 −4  S/cm when measured at a temperature in the range of −20° C. to 10° C. and higher than 1×10 −3  S/cm when measured at a temperature 20° C. or higher. 
       FIG.  2    illustrates a mold structure for making the solid-state electrolyte. A precursor solution consisting of polymer precursor, ceramic nanoparticles, plasticizer, lithium salt and binder is mixed and poured onto the specifically designed module which has a precisely controlled geometry. The module serves as a mold and is made from a sheet of plastic wherein the aperture or opening with specific dimensions formed. A typical module has a rectangular aperture having (L×W×H) dimensions of 6.2 cm×4.6 cm×0.2 mm, respectively, which is specifically designed for special prototype. In-situ polymerization yields a free-standing solid-state electrolyte that can be peeled off the module. A large size solid-state electrolyte is assembled with comparable size cathode and anode sheets, to fabricate all solid-state lithium-ion pouch cells with targeted performance of 3.6V/2.0 Ah that can be further assembled into battery packs of with 28V/5 Ah or 28/25 Ah specifications. UV radiation is applied to the film for polymerization to produce a layer of solid-state electrolyte. For fabricating electrochemical coin cells or pouch cells, the wet film is typically 30 to 900 μm thick. 
     Lithium electrochemical cells and batteries employing the large size solid-state electrolyte will have excellent rate performance as well as outstanding cycling stability (&gt;1000 cycles) over a wide range of temperatures. Batteries with the novel ceramic-polymer nanocomposite electrolyte will meet severe specifications for wide temperature working ranges, quick charging requirement, and high energy density. 
     An exemplary electrochemical cell includes a LFP cathode, a solid-state electrolyte, and a graphite anode, with a single layer or multi-layer structure. The anode and solid electrolyte define a first interface where graphite and solid electrolyte meet and form intimate contacts. Similarly, the cathode and solid electrolyte define a second interface where LFP and solid electrolyte meet and form intimate contacts. With the use of a networking-structure electrolyte in the electrodes, the intimate contacts afford good ion transport and reduce interfacial resistance. 
     Lithium electrochemical coin cells are manufactured by positioning an anode, electrolyte, cathode, spacers, and springs between two electrode shells and crimping the entire assembly. A high-pressure crimper typically applies a pressure of about 100 to 1500 psi. 
       FIG.  3 A  depicts an electrochemical cell  20  that comprises an LFP cathode  22  and lithium metal anode  24  with a ceramic-polymer nanocomposite solid-state electrolyte  26  interposed in-between. The anode  24  and electrolyte  26  layers define a first interface where the lithium metal and electrolyte materials meet and form intimate contacts. Similarly, the cathode  22  and electrolyte  26  layers define a second interface where the LFP and electrolyte materials meet and form intimate contacts. The intimate contacts afford good ion transport and reduce interface resistance. The electrochemical cell can be encapsulated to form a “coin cell” as shown in  FIG.  3 B . The coin cell has current collectors on the exterior surfaces of the cathode and anode. Electrochemical cells can be stacked into batteries. 
     Electrochemical cells can be encapsulated to form a “pouch cell” type battery as shown in  FIG.  3 C  which includes a plurality of unit cells. In this configuration, the pouch cell includes LFP cathode sheets  30  and  32  that are connected to cathode current collector  52 , anode graphite sheets  36  and  38  that are connected to anode current collector  54 , LFP cathode sheets  42  and  44  that are connected to cathode current collector  56 , and anode graphite sheets  48  and  50  that are connected to anode current collector  58 . Solid electrolytes  34 ,  40 , and  46  are positioned between the anodes and cathodes as shown. 
     After the cathode, the electrolyte and the anode are stacked and the cell is assembled, the entire structure is calendared to ensure intimate contact between the layers. Calendaring techniques include plain plate calendar and hot isostatic pressing or the combination of both. High temperature is also applied during calendaring process as the polymer becomes “soft” at high temperatures so that it becomes easier and more effective to compress the structure and create compact contacts between polymer and electrode. The temperature is selected based on the formulation of the solid electrolyte which ranges from 60° C. to 180° C. 
     When conducting plain plate calendar for coin cells, the cell is placed between two dies of the crimping machine, where two dies are wrapped by copper plate for initiating high temperature. After heating, the coin cell is crimped at a crimping pressure that typically ranges from 500 psi to 10000 psi. 
     Lithium electrochemical pouch cells are assembled by stacking the anode, electrolyte and cathode and then welding the cathode sheets and welding the anode sheets. The entire structure is placed in a cell case, which is typically a laminated aluminum case, for final sealing. 
     When conducting plain plate calendar for pouch cell, the cell is placed between two metal plates with heating available for both plates. After heating, pressure that typically ranges from 200 psi to 1500 psi is applied. 
     When conducting hot isostatic pressing for pouch cells, the assembled cell is sealed in a vacuum waterproof bag and is put inside the isostatic pressing machine. After heating, high isostatic pressure typically ranging from 2,000 psi to 80,000 psi is applied. 
     Pouch cells can be calendared by using plain plate calendar, hot isostatic pressing or the combination of both. 
       FIG.  3 D  shows the cross-sectional scanning electron image (SEM) of a cell core comprising a composite cathode sheet, solid electrolyte and anode sheet. The cathode sheet, solid electrolyte layer and anode sheet are clearly distinguishable. The optical response spectrum is determined by the solid electrolyte. 
     Coin cells containing different cathode formulations designated C1, C2 and C3 were evaluated. For each cell, lithium metal sheet was used as the anode. The solid-state electrolyte membrane positioned between the anode and cathode comprised 12.5 wt % polymer matrix that was derived from PEGDA, 37.5 wt % EC, 33 wt % LiTFSI, 17 wt % Al 0.15 Li 6.85 La 3 Zr 1.75 Ta 0.25 O 12  with diameters that ranged from 10 to 2000 nm. 
     Cathode C1 comprised 10 wt % carbon black, 80 wt % LFP, 1.67 wt % LiTFSI, 0.82 wt % Al 0.15 Li 6.85 La 3 Zr 1.75 Ta 0.25 O 12  with diameters that ranged from 10 to 2000 nm, 1.88 wt % EC, 0.63 wt % polymer matrix that is derived from PEGDA and 5 wt % PVDF. 
     Cathode C2 comprised 10 wt % carbon black, 80 wt % LFP, 3.34 wt % LiTFSI, 1.66 wt % Al 0.15 Li 6.85 La 3 Zr 1.75 Ta 0.25 O 12 . with diameters that ranged from 10 to 2000 nm, 3.75 wt % EC, 1.25 wt % polymer matrix that is derived from PEGDA and 0 wt % PVDF. 
     Cathode C3 comprised 10 wt % carbon black, 75 wt % LFP, 5 wt % LiTFSI, 2.5 wt % Al 0.15 Li 6.85 La 3 Zr 1.75 Ta 0.25 O 12  with diameters that ranged from 10 to 2000 nm, 5.62 wt % EC, 1.88 wt % polymer matrix that is derived from PEGDA and 0 wt % PVDF. 
       FIGS.  4 A,  4 B and  4 C  are the rate performance and  FIGS.  5 A,  5 B and  5 C  are the cycling stability data for electrochemical data cells using cathode C1, C2 and C3, respectively. Cathode C1 presents high specific capacity of 140 mAh/g when the test current rates are 0.1 C, 0.2 C and 0.5 C, and only negligible reduction in capacity when current is 1.0 C. For cycle stability, cathode C1 exhibits nearly no capacity reduction before 100 cycles and close to 80% capacity retention near 250 cycles. The coin cell is not stable after 250 cycles. 
     For medium and high electrolyte weight ratio cathodes C2 and C3, the coin cells exhibit lower specific capacities in the rate performance tests. For the testing current rate of 0.1 C, 0.2 C, 0.5 C, 1.0 C, the specific capacities of the coin cells using cathode C2 is 105 mAh/g, 106 mAh/g, 101 mAh/g, 97 mAh/g, respectively, and the specific capacity of coin cell using cathode C3 is 118 mAh/g, 117 mAh/g, 106 mAh/g and 96 mAh/g, respectively. The slightly lower specific capacity is caused by the heavier electrolyte component compared to other components within the electrode. On average, the total weight of cathode sheets with high electrolyte weight ratio is 30% more than that of the non-electrolyte containing cathode sheets. The specific capacity drops as the test current rate is enhanced for both coin cells and the trend is consistent to previous coin cells results. The cathode C2-based coin cell exhibits more rapid decrease in specific capacity during the cycling stability test, which retains below 50% specific capacity after 200 cycles. However, the cathode C3-based coin cell exhibits extended cycling stability in return, although it also shows lower specific capacity during the rate performance test. It is shown that the coin cell still has 80% of original capacity at 250 cycles and 60% of original capacity at 400 cycles. The coin cell can be charged/discharged at 0.5 C after 500 cycles without failure and retains 53% of original coin cell capacity. In view of the fact that each coin cell is charged/discharged at 0.5 C for the cycling stability test which is greatly higher than that normally used in cycling stability studies, it is expected that an electrolyte-filled composite cathode will enhance overall stability for ASSLiBs, although the electrode is heavier and the specific capacity is lower. The cathode with high weight ratio of electrolyte has better performance in rate performance and cycling stability. 
     Further investigation regarding graphite infiltrated by SSE was conducted where the structure of coin cell was an electrolyte-infiltrated composites graphite anode/SSE/lithium. 
     Coin cells containing different anode formulations designated A1, A2 and A3 which have different levels of polymer matrix were evaluated. Three different anode formulations were evaluated where A1, A2 and A3 are low, medium and high electrolyte weight ratio respectively. For each coin cell, lithium metal sheet is used as the reference electrode for electrode characterization. 
     The solid-state electrolyte membrane positioned between the anode and cathode comprised 12.5 wt % polymer matrix that is derived from PEGDA, 37.5 wt % EC, 33 wt % LiTFSI, 17 wt % Al 0.15 Li 6.85 La 3 Zr 1.75 Ta 0.25 O 12  with diameters that ranged from 10 to 2000 nm. 
     Anode A1 comprised 10 wt % carbon black, 75 wt % graphite, 1.67 wt % LiTFSI, 0.83 wt %, Li 7 La 3 Zr 1.75 Nb 0.25 O 12  with diameters that ranged from 10 to 2000 nm, 1.88 wt % EC, 0.62 wt % polymer matrix that is derived from PEGDA and 10 wt % PVDF. 
     Anode A2 comprised 10 wt % carbon black, 75 wt % graphite, 3.34 wt % LiTFSI, 1.66 wt % Li 7 La 3 Zr 1.75 Nb 0.25 O 12  with diameters that ranged from 10 to 2000 nm, 3.75 wt % EC, 1.25 wt % polymer matrix that is derived from PEGDA and 5 wt % PVDF 
     Anode A3 comprised 5 wt % carbon black, 80 wt % graphite, 5 wt % LiTFSI, 2.5 wt % Li 7 La 3 Zr 1.75 Nb 0.25 O 12  with diameters that ranged from 10 to 2000 nm, 5.62 wt % EC, 1.88 wt % polymer matrix that is derived from PEGDA and 0 wt % PVDF. 
       FIGS.  6 A,  6 B, and  6 C  are data of cycling stability experiments of corresponding half-cells based on the three different anode compositions. All these half-cells were charged/discharged at 0.1 C˜1.0 C for rate performance tests and 0.5 C for cycling stability tests. The experimental specific capacity of graphite is around 340 mAh/g. In the first 6 cycles where the charge/discharge rate is 0.1 C (rate performance test), coin cell using anode A3 anode has lowest specific charge/discharge capacity of around 150 mAh/g among all three types of coin cells. Coin cell using A1 and A2 anodes exhibit over 300 mAh/g in specific charge/discharge capacity which is close to the theoretical value of graphite. The specific capacity drops gradually for all three of the coin cells as the cycling number increases. In the cycling stability test, coin cell using anode A2 has higher specific capacity than coin cells using anode A3. After 500 cycles, both coin cells exhibit a specific capacity around 130 mAh/g, which retains around 43% of the original value. The anode with medium weight ratio of electrolyte has better performance in rate performance and cycling stability. 
       FIG.  7 A  and  FIG.  7 B  are rate performance and cycling stability data for the full-cells which comprised electrolyte-infiltrated composite electrodes. Cells were charged/discharged at 0.1 C˜1.0 C for rate performance test and 0.5 C for cycling stability test. When the coin cell is charged and discharged at 0.1 C, 0.2 C, 0.5 C and 1.0 C, the specific capacity is around 123 mAh, 115 mAh/g, 110 mAh/g and 105 mAh/g, respectively. In the first 600 cycles, the specific capacity drops from 150 mAh/g gradually to around 100 mAh/g, which is nearly ⅓ attenuation. After 600 cycles, however, the specific capacity increases reversely to above 160 mAh/g and reaches the highest point in 835 cycles. After 835 cycles, the specific capacity then decreases and in around 1100 cycles, the specific capacity is nearly 140 mAh/g. In summary, the specific capacity after 1100 cycles shows a little enhancement as compared to the cell&#39;s original value. The charge/discharge process is taken continuously over 6 months which indicates that the cell possesses both long lifetime and cycling stability. Possible reasons for the specific capacity increase between 600 cycles and 835 cycles are (1) element doping that leads to an increase in the number of defect sites and vacancies as Li +  active sites on the surface of the graphite (the possible elements may be N and F from LiTFSI) and (2) disordered carbon structure in the graphite may create many unoccupied sites and lithium atoms may fill these sites through the production process of SSE and greatly enhance the specific capacity. 
     All solid-state pouch cells with multiple unit cells in parallel were prototyped using the 3D-networking composite electrode. The basic configuration of the prototypes is presented in  FIG.  3 C . Double-side printed LFP sheets and graphite sheets as well as SSE layer are stacked. A complete all solid-state standard pouch cell with dimensions of 6.3 cm×4.7 cm×9.34 mm exhibits total capacity over 2 Ah and retains over 70% after 200 cycles. With the balance between capacity and energy density, the optimized mass energy density and volume energy density of the all solid-state pouch cell prototype could reach over 100 Wh/kg and 250 Wh/L. 
     The foregoing has described the principles, preferred embodiment and modes of operation of the present invention. However, the invention should not be construed as limited to the particular embodiments discussed. Instead, the above-described embodiments should be regarded as illustrative rather than restrictive, and it should be appreciated that variations may be made in those embodiments by workers skilled in the art without departing from the scope of present invention as defined by the following claims.