Rechargeable, high-density electrochemical device

Abstract

Rechargeable, high-density electrochemical devices are disclosed. These electrochemical devices may, for example, include high energy densities that store more energy in a given, limited volume than other batteries and still show acceptable power or current rate capability without any liquid or gel-type battery components. Certain embodiments may involve, for example, low volume or mass of all of the battery components other than the cathode, while simultaneously achieving high electrochemically active mass inside the positive cathode.

Description

TECHNICAL FIELD

This invention relates to rechargeable, high-density electrochemical devices. In particular, certain embodiments of the present invention relate to, for example, all-solid state, rechargeable batteries with high energy densities that have the capacity to store more energy in a limited volume and still show acceptable power or current rate capability without any liquid or gel-type battery components.

BACKGROUND OF THE INVENTION

The capacity of rechargeable and non-rechargeable batteries is defined by the positive cathode and the negative anode. When using a metallic lithium anode (e.g. in Li—MnO₂ coin cells) or a capacity rich Li-ion anode that, for example, may be based on silicon or tin, the capacity of the battery is dominated or limited by the specific capacity (measured in mAh/g or mAh/ccm) of the positive cathode. Reducing the volume of all of the other battery components, which is most useful for small batteries, or the mass of all of the other battery components, which is most useful for large batteries (e.g. in electric vehicles), while simultaneously increasing the electrochemically active mass inside the positive cathode is the most effective approach to increase the energy density (measured in Wh/liter, for example) of a battery for a given cathode-anode chemistry.

Increasing the electrochemically active mass inside the positive cathode means to either reduce any auxiliary phases inside the cathode, such as mechanical binders or ionic or electronic conduction enhancers, or fabricate the cathode thicker for a given cathode area. Due to the limiting diffusion kinetics and the associated limited current rate or power capability when the cathode thickness becomes substantial (>>20 μm), high energy density room temperature batteries, such as cell phone and laptop batteries, require a highly conductive, liquid-organic-solvent based lithium ion electrolyte to penetrate the cathodes of these batteries. However, the presence of the liquid organic solvent is the origin of most problems experienced with such batteries over the last twenty years such as, for instance, thermal runaway upon decomposition or short-circuiting of the battery upon heat-related failure, fire/fume/smoke/explosion upon certain battery failure modes, gas evolution and pressure build-up in the early electrochemical cycles, charge-discharge cycle limitation to 300-1000 cycles, limited operational temperature range (0° C.-60° C. in many cases), among others. In addition, constraining the volatile liquid organic solvent demands specific packaging architectures and cell housing often equipped with vents and valves that avoid cell over-pressurization during the early electrochemical cycles.

There is a need in the industry for batteries with higher energy densities. In particular, there is a need for all-solid-state rechargeable batteries without any liquid or gel-type battery components to store more energy in a limited volume that still show acceptable power and/or current rate capability. This results in a safer battery and allows for the use of simplified packaging and higher and lower temperature ranges of operation and storage.

SUMMARY OF INVENTION

Certain exemplary embodiments of this invention may include batteries with high energy density for a given cathode-anode chemistry. Certain embodiments, as discussed in further detail below, may involve, for example, low volume or mass of all of the battery components other than the cathode, while simultaneously achieving high electrochemically active mass inside the positive cathode.

An embodiment of a rechargeable electrochemical device with a positive composite cathode may include a solid-state electrochemically active material, a solid-state electronically conducting material which has an electronic conductivity that is at least three times higher than the electronic conductivity of said electrochemically active material before the electrochemically active material is initially charged, and a solid-state, inorganic, ionically conducting material which has an ionic conductivity that is at least three times higher than the ionic conductivity of said electrochemically active material before the electrochemically active material is initially charged.

Alternatively, an embodiment of a rechargeable electrochemical device with a positive composite cathode may include at least one solid-state electrochemically active material, at least one solid-state, ionically conducting material that is different from the electrochemically active material, and may not contain liquid or gel-like solvent.

An alternative embodiment of a rechargeable electrochemical device may include a solid state positive cathode, a negative anode, and a solid state electrolyte sandwiched between the cathode and the anode; wherein the electrochemical device contains a single electrochemical cell which has a rated capacity preferably of, for example, at least 2 mAh/cm² based on the geometric footprint of the positive cathode.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 illustrates a cross-sectional view of an exemplary Li-ion or Li-polymer battery that could be used in a cell phone.

FIG. 2 illustrates an exemplary electrochemical device with three solid phases including an electrochemically active cathode material, an ionic conductivity enhancer and an electronic conductivity enhancer.

FIG. 3 illustrates an exemplary electrochemical device with two solid phases including an electrochemically active cathode material and an electronic conductivity enhancer.

DETAILED DESCRIPTION OF PREFERRED EMBODIMENTS

It is to be understood that the present invention is not limited to the particular methodology, compounds, materials, manufacturing techniques, uses, and applications described herein, as these may vary. It is also to be understood that the terminology used herein is used for the purpose of describing particular embodiments only, and is not intended to limit the scope of the present invention. It must be noted that as used herein and in the appended claims, the singular forms “a,” “an,” and “the” include the plural reference unless the context clearly dictates otherwise. Thus, for example, a reference to “an element” is a reference to one or more elements, and includes equivalents thereof known to those skilled in the art. Similarly, for another example, a reference to “a step” or “a means” is a reference to one or more steps or means and may include sub-steps or subservient means. All conjunctions used are to be understood in the most inclusive sense possible. Thus, the word “or” should be understood as having the definition of a logical “or” rather than that of a logical “exclusive or” unless the context clearly necessitates otherwise. Structures described herein are to be understood also to refer to functional equivalents of such structures. Language that may be construed to express approximation should be so understood unless the context clearly dictates otherwise.

Unless defined otherwise, all technical and scientific terms used herein have the same meanings as commonly understood by one of ordinary skill in the art to which this invention belongs. Preferred methods, techniques, devices and materials are described although any methods, techniques, devices, or materials similar or equivalent to those described may be used in the practice or testing of the present invention. Structures described herein are to be understood also to refer to functional equivalents of such structures.

All patents and other publications are incorporated herein by reference for the purpose of describing and disclosing, for example, the methodologies described in such publications that might be useful in connection with the present invention. These publications are provided solely for their disclosure prior to the filing date of the present application. Nothing in this regard should be construed as an admission that the inventors are not entitled to antedate such disclosure by virtue of prior invention or for any other reason.

Certain embodiments of the present invention, for example, include an all-solid state, high energy density battery cell that does not contain any liquid or gel-like components, unlike traditional cell phone batteries and coin cells. Gel-like components consist of, for example, solvents that have viscosities so high they do not flow like a common liquid. The high energy density may be accomplished through a combination of features, such as, for example:

• • 1. maximizing the cathode thickness per unit cathode area while keeping the charge and discharge current capability within acceptable performance limits;
  • 2. optimizing the loading or volume percentage of the electrochemically active mass inside the cathode, which may include a composite rather than a single phase of electrochemically active material to make up 100% of the cathode volume;
  • 3. utilizing a composite electrochemically active material which contains all-solid state lithium ion conduction and electron conduction enhancing phases; and/or
  • 4. minimizing the volume fraction of all of the other battery cell components, such as the substrate, electrolyte, negative anode, current collectors and terminals and the packaging.Regarding item 1, certain embodiments of the present invention, for example, may include an electrochemical device with a cathode thickness of about 100-1000 μm, whereas the cathode thickness of cell phone type batteries may be, for example, approximately 100 μm. Regarding item 2, an example electrochemical device may preferably use a loading of the electrochemically active material of higher than about 50 vol %. To enhance the power and current rate capability of the cell (items 1 and 3), the remaining, for instance, 50 vol % of the composite cathode may be filled with two materials: (a) a lithium ion conduction enhancing material, which is chemically stable with the electrochemically active cathode material during fabrication and battery operation and storage while showing an ionic conductivity that is at least three times higher than that of the electrochemically active material; and (b) an electron conduction enhancing material which has an electronic conductivity that is at least three times higher than that of the electrochemically active material. Regarding item 4, the device of certain embodiments of the present invention may be configured, among other parts, with: (i) a thin metal cathode current collector, such as, for instance, 10 μm Al foil, which also serves as an optional substrate (or no such current collector if the positive cathode is conductive enough along its outside surface to which the positive terminal may be connected); (ii) a thin-film electrolyte, such as, for instance, 1-3 μm thick Lipon; and (iii) a thin metal anode, such as, for instance, 10-50 μm of metallic lithium. One or more elements of item 4 may be fabricated into the device of certain embodiments of the present invention by physical vapor deposition (PVD) processing or heat-pressure lamination using readily available Li foil. Finally, the device of certain embodiments of the present invention may be, for example, packaged using a thin-film encapsulation of about 3 μm in thickness, as previously disclosed, for example, in U.S. Pat. Appl. Pub. No. 2009/0181303, which is incorporated herein by reference in its entirety.

In certain embodiments, the absence of any volatile liquid organic solvents inside the composite cathode and/or the electrolyte can be highly conducive to improved safety and higher temperature limits for operation and storage of the electrochemical device, which include lead-free solder reflow conditions during which temperature excursions of up to 265° C. may occur for several minutes.

Lower cost versions of a high-capacity cell of certain embodiments of the present invention may include electrolyte alternatives comprising a thicker ceramic layer, or multi-layers, that are entirely or partially fabricated by non-PVD or non-chemical vapor deposition (CVD) methods, such as traditional ceramic or wet chemical processing. Examples of these electrolyte alternatives may include compacted Li₂S—SiS₂ or Li₂S—P₂S₅ based glass electrolyte powder (˜100 μm layer thickness), Li₃N—LiTi₂(PO₄)₃ dual layer ceramic plate (˜100 μm thickness), single-sided Lipon protected LiAl₂Ti(PO₄)₃ or Li_0.35La_0.55TiO₃ plates (˜100 μm thickness) or compacted (pressed) Li₇La₃Zr₂O₁₂ powder (˜50 μm thickness). Analogous to the composite cathode, a composite anode may be used for certain embodiments of the present invention and may include ceramic compacted, Li_ySn-activated, nano-sized Li₄Ti₅O₁₂ powder (1.5V vs. Li⁺/Li; results include 1.5V voltage reduction of the fully fabricated electrochemical cell of certain embodiments of the present invention when compared to those 4V cells that employ a metal lithium anode) wherein Li_ySn serves as a lithium ion and electron conduction enhancing second phase in the volume un-changing Li_xTi₅O₁₂ (4≤x≤7) anode phase. Other composite anodes may also be employed.

Although the fabrication of solid state, high capacity cells with ceramic and/or wet chemistry fabricated electrolytes and/or anodes may be attractive because of their cost and manufacturing throughput, they do not include the power and energy density performance of the cells according to certain embodiments of the present invention that use a thin-film electrolyte and a metal anode consisting entirely of the electrochemically active species of the cell (such as metallic lithium for Li-ion batteries). These lower cost batteries are less desirable because the ceramic and/or wet chemistry fabricated electrolyte and/or composite anode are typically thicker (which may increase cell resistance and add non-energy containing volume to cell, both of which are undesirable characteristics) and provide lower cell voltages (which may cause lower energy and lower power, both of which are undesirable characteristics).

Good cathode performance for certain embodiments of the present invention (for both pure cathodes and composite cathodes) may require, for example, a high, effective diffusion coefficient inside the cathode. Such a diffusion coefficient inside the cathode allows for, upon cell discharge, as many electrochemically active species (ions and electrons) as possible to be inserted into the cathode in the shortest time possible and into cathode locations that are farthest away from the diffusion originating plane, which is the cathode-electrolyte interface. In a simplified picture, one may use the one-dimensional solution of Fick's second law of diffusion wherein for a given diffusion coefficient, D, a wave-front of diffusing species penetrates a body after a diffusion period t by depth X (sometimes called diffusion length) according toX=2(D*t)^1/2  (1)

Equation (1) is an accurate estimate for the combined diffusion of ions and electrons. In many practical electrochemically active cathode materials, the electronic conductivity is much higher than that of the electrochemically active ions. For example, the electronic conductivity in charged Li_xCoO₂ (x<0.7) is about 1 S/cm at ambient temperatures while that of the lithium ions is less than 10⁻⁷ S/cm. Therefore, it may be beneficial to enhance the lithium ion conductivity of the cathode by admixing appropriate lithium ion conduction enhancing materials, thereby forming a cathode composite.

In certain embodiments, using the ionic conductivity as the determining, independent variable for equation (1), the diffusion coefficient D may be replaced by part of Fick's law of diffusion, which isD=RT/(c*z*F²*dE/dx)*j  (2)that relates D to the gas constant R, the absolute temperature T, the local concentration of diffusing species c, the charge number z of these species (z=1 for Li⁺ ions), the Faraday constant F, the local electric field strength dE/dx, and the current density j of the diffusing species. The resulting equation after inserting equation (2) into equation (1) and squaring both sides of the resulting equation isX²=4*RT/(c*z*F²*dE/dx)*t*j  (3)wherein the diffusion period t could also be interpreted as the continuous discharge or charge time that it takes at a given current density j to discharge or charge the rated capacity of a cathode wherein the rated capacity is proportional to the thickness X of the cathode for a given cathode composition of electrochemically active cathode material, ionic conductivity enhancing material and electronic conductivity enhancing material. The rated capacity of a cathode is, for example, the discharge capacity of a battery supplied at ambient conditions following a full battery charge. The resulting equation after converting the current density j into the conductivity G using Ohm's law with resistance R and voltage E across the entire cathode, which in turn has the cross-sectional diffusion area A,R=E/(j*A)  (4)and the definition for the conductivity G (=inverse resistivity)G=1/R*X/A  (5)isj=E*G/X  (6)The resulting equation after inserting equation (6) into equation (2) and considering the voltage drop across the entire thickness X of the cathode isX²=4*RT/(c*z*F²*dE/dX)*t*E*G/X  (7)or, after rearranging equation (7),X³=4*RT/(c*z*F²*dE/dX)*t*E*G  (8)For a constant electric field gradient throughout the cathode, which may be the case for electronically well conducting cathodes, dE/dx becomes E/X such that equation (8) simplifies toX²=4*RT/(c*z*F²)*t*G  (9)Therefore,X²˜t*G  (10)

Equation (10) may be considered a design rule for cathodes if, for example, for a given diffusion period (or discharge or charge time) t through thickness X of an electrochemical cell, the ionic conductivity G of the cathode may be increased four-fold before one may afford to double the thickness X of the cathode in order to double its capacity per footprint under otherwise constant parameters (i.e., the same electrochemically active material, same volumetric loading of electrochemically active material, same cross-sectional area of the cathode, among others). The discharge time capability of batteries may be given its reciprocal value, the so-called C-rate, which defines how often a battery or electrochemical cell is able to mathematically discharge its rated capacity in one hour when mathematically neglecting the charge periods in between discharges.

Equation (10) also represents that for a given conductivity G inside the cathode, increasing the cathode thickness can cause a much slower (i.e., longer) discharge time capability (lower C-rate). For example, the discharge time for full discharge of a given rated capacity may increase approximately four-fold (C-rate drops to about 25%) when doubling the thickness of the cathode. Maintaining a given rated capacity while doubling the cathode thickness implies that the thickness increase can be accomplished either by adding electrochemical inert material to the cathode, doubling its porosity or changing the electro-active material inside the cathode.

Equation (10) further teaches that adding electrochemically inert material to the cathode, such as mere ionic or electronic conductivity enhancers that do not store electrochemical capacity or energy and therefore merely increase the thickness of the cathode by ΔX without increasing the capacity or energy of the cathode, comes with a price: it therefore may be appropriate in certain embodiments to add the inert material if it may increase the ionic conductivity of the (composite) cathode to G*(X+ΔX)²/X² in order to maintain or, even better, shorten the discharge or charge time because(X+ΔX)²˜t*G[(X+ΔX)²/X²]  (11)

The importance of, and need for, a great ionic conductivity inside certain embodiments of the cathode is evident. Since the electrochemically active cathode material such as, for instance, commercially available LiCoO₂, may not provide a sufficiently high lithium ion conductivity itself (e.g., it may exhibit at ambient temperatures <10⁻⁷ S/cm throughout its electrochemically active range between 4.2V-2.0V vs. Li⁺/Li) one may, for instance, fabricate composite cathodes with lithium ion conductivity enhancing materials which have a lithium ion conductivity that is substantially higher than that of the electrochemically active cathode material.

After the selection of appropriate lithium ion conduction enhancing material, such as, for example, lithium lanthanum titanate (Li_0.35La_0.55TiO₃ has G=10⁻³ S/cm (bulk) and G=2*10⁻⁵ S/cm (grain boundary) at 25° C., an example of which is discussed in Y. Inaguma et al., Solid State Communications 86 (1993) p. 689, which is incorporated herein by reference in its entirety), lithium lanthanum zirconate (Li₇La₃Zr₂O₁₂ exhibits 7.7*10⁻⁴ S/cm at 25° C., an example of which is discussed in R. Murugan et al., Angewandte Chemie International Edition 46 (2007) 7778, which is incorporated herein by reference in its entirety), lithium aluminum titanium, phosphate (Li_1.3Ti_1.7Al_0.3(PO₄)₃ shows 7*10⁻⁴ S/cm at 25° C., an example of which is discussed in G. Adachi et. al, U.S. Pat. No. 4,985,317, which is incorporated herein by reference in its entirety), or lithium thio-phosphate (80 at % Li₂S-20 at % P₂S₅[═Li₈P₂S₉; “Thio-LISICON II”] shows 7.4*10⁻⁴ S/cm at 25° C., an example of which is discussed in Senga Minoru et. al, U.S. Pat. Appl. Publ. No. 2007/0160911, which is incorporated herein by reference in its entirety), it is important in certain circumstances to ensure that the morphology, which comprises particle size and particle size distribution, of the lithium ion conductivity enhancing material is tuned to the particle size and distribution of the electrochemically active cathode material inside the composite cathode. This approach may provide a positive three-dimensional network of lithium ion conductivity inside said composite cathode. Porosity within the composite cathode may offset the effectiveness of materials with great conductivity (applies to ions and electrons) due to poor conduction paths or inter-grain contact area, which in turn may be maximized for optimum conduction between the grains and throughout the composite cathode. This objective may be well accomplished with particle sizes preferably in the range of approximately 0.1-10 μm, and most preferably 0.5-5 μm, for both the ionic conductivity enhancing material and the electrochemically active material within the cathode. Much larger particles than 10 μm may entail the risk of shadowing or interrupting the ionic conduction path in the ionic network and also the electron conduction path in the electronic network.

Alternatively or additionally, the ionic conductivity of the electrochemically active material itself may be enhanced. This may be achieved by, for example, doping its bulk grain (intra-grain) portion with other, appropriate chemical elements and/or by chemically or mechanically modifying its grain boundaries, which may be the premier ionic conduction gateways between the grains inside a solid state cathode. Chemical modification via reaction with appropriate chemicals may be a preferred method according to certain embodiments of the present invention. Fast ionic grain boundary conduction is most effective in providing ions to and from the locations of the electrochemical reactions responsible for capacity and energy storage, which are inside the grain bulk. If the so-enhanced electrochemically active material in grain bulk and/or grain boundary, for example LiCoO₂, inside the cathode shows a sufficiently high lithium ion conductivity, then the addition of an inert phase that merely provides enhanced lithium ion conductivity, such as, for instance, lithium lanthanum titanate (Li_0.35La_0.55TiO₃), may become unnecessary. However, it may be important to ensure that the cathode is electronically conducting well, for example with an electronic conductivity that is much higher than the lithium ion conductivity inside the cathode. Otherwise, the electronic conductivity of the cathode may limit the effectiveness of the lithium ion conductivity, and thus the lithium diffusion through the cathode may occur only at the pace of the limiting electronic conductivity, according to equation (9) when applying to electrons instead of ions.

Electron conductivity enhancing materials are relatively inexpensive such as, for example, carbon or nickel powder. These materials are fairly stable up to at least 500° C. with commonly used electrochemically active materials (e.g., LiCoO₂) and selected ionic conductivity enhancing materials, such as, for example, lithium lanthanum titanate (Li_0.35La_0.55TiO₃) or lithium lanthanum zirconate (Li₇La₃Zr₂O₁₂). It is preferred according to certain embodiments of the present invention to have these electronic conductivity enhancing materials available in an appropriate particle size distribution that is conducive to maximizing the electronic conductivity of the composite cathode, most preferably at the lowest admixed volume fraction of electron conductivity enhancing material. If one used larger particles, such as, for example, 50 μm Ni, then these particles may provide the composite cathode with a good electronic conductivity but may unnecessarily remove valuable volume inside the composite cathode that may not be filled with the more important electrochemically active cathode material (which provides energy) and/or the optional lithium ion conductivity enhancing material (may enhance the power capability at that energy level).

Alternatively or additionally, the electronic conductivity of the electrochemically active material itself may be enhanced. This may be achieved by, for example, doping its bulk grain (intra-grain) portion with other, appropriate chemical elements and/or by chemically or mechanically modifying its grain boundaries, which may be the premier electronic conduction gateways between the grains inside a solid state cathode. Chemical modification via reaction with appropriate chemicals may be a preferred method according to certain embodiments of the present invention. Fast electronic grain boundary conduction is most effective in providing electrons to and from the locations of the electrochemical reactions responsible for capacity and energy storage, which are inside the grain bulk. If the so-enhanced electrochemically active material in grain bulk and/or grain boundary, for example LiCoO₂, inside the cathode shows a sufficiently high electronic conductivity, then the addition of an inert phase that merely provides enhanced electronic conductivity without supplying substantial electrochemical storage capacity in the positive cathode, such as, for instance, nickel or carbon powder, may become unnecessary.

Appropriate particle sizes and distribution may be generated using, for example, high energy ball milling that may grind raw powders down to nano/sub-micron sized particles. Specific particle size distribution of a given material could be accomplished by mixing separately ground powder batches for which different grinding parameters were applied. Since the so-obtained powder of one material (e.g., the lithium ion conductivity enhancing material) has a specific particle size distribution, this powder may be mixed with another material (e.g., the electrochemically active cathode material) that has a particle size distribution that has been created in a similar fashion. Finally, the electron conductivity enhancing material (specific particle size distribution made in a similar manner as employed for the lithium ion conductivity enhancing material) may be added to the powder mix. Then, homogenizing the powder mix may be achieved in various ways, such as, for example, by low-energy ball milling using low concentrations of low-density grinding media such as Si₃N₄ or Al₂O₃, which may or may not further change the particle size distribution of one or more materials within the powder mixture.

EXAMPLE EMBODIMENTS OF THE PRESENT INVENTION

Example 1

According to an embodiment of the present invention, a commercially available LiCoO₂ powder may be used to determine its electronic conductivity at ambient conditions prior to its initial charge by (a) cold pressing 7 tons of a 0.5 mm thick and 10 mm in diameter powder pellet, which may achieve 76% of the theoretical density of 5.06 g/ccm and (b) by cold pressing 7 tons of 0.5 mm thick and 10 mm in diameter powder pellet followed by sintering the pellet at 900° C. for 1 h in air, which may achieve 72% of the theoretical density of 5.06 g/ccm. The so-obtained pellets may then be coated with 0.3 μm thick, PVD fabricated, lithium ion blocking gold electrodes on both pellet faces and subjected to electronic resistance measurements using electrochemical impedance spectroscopy and 10 mV of amplitude. The electronic conductivity of an exemplary cold pressed LiCoO₂ pellet obtained 2.7*10⁻⁵ S/cm while the pellet that may be annealed at 900° C. exhibited an electronic conductivity of 7.1*10⁻⁴ S/cm.

Example 2

According to an embodiment of the present invention, the electronic conductivity of a commercially available Ni powder (2-3 μm grain size) may be determined from a cold pressed a 7 ton Ni pellet that was 0.5 mm thick and 10 mm in dia. The density may be 80% of the theoretical density (8.91 g/ccm). The so-obtained Ni pellet may be sandwiched between two copper electrodes and subjected to 10 mVDC. However, the electronic resistance may be so low (<<1 Ohm) that the currents fall outside the capability of the test equipment (10A). Instead of determining the exact electronic conductivity, the electronic conductivity may be approximated by the literature value for Ni, which at 25° C. is about 10⁵ S/cm. This value is more than 10 orders of magnitude greater than that of LiCoO₂ prior to the initial charge.

Example 3

According to an embodiment of the present invention, the commercially available LiCoO₂ powder from Example 1 may be used to determine its ionic conductivity at ambient conditions prior to its initial charge by (a) cold pressing 7 tons of a 0.5 mm thick and 10 mm in diameter powder pellet and by (b) cold pressing 7 tons of a 0.5 mm thick and 10 mm in diameter powder pellet followed by sintering of the pellet at 700° C. for 1 h in air, which may achieve 73% of the theoretical density of 5.06 g/ccm. The so-obtained pellets may be coated with a 3 μm thick electron blocking Lipon electrolyte layer on each pellet face. In addition, two metallic Li electrodes may be PVD fabricated onto the Lipon electrolyte layers opposite to the sandwiched LiCoO₂ pellet. This ionic conductivity test cell may be subjected to ohmic resistance measurements by applying various voltages between 1-5 VDC to the lithium electrodes whereupon lithium plating or stripping may occur. In this setup, only lithium ions may conduct through the LiCoO₂ pellet while its electronic conduction was completely arrested. The resulting, instant currents may show ohmic behavior and were calculated into resistances. Subtracting the known, combined resistances of the two 3 μm Lipon layers connected in series (from other separate experiments) enabled the extraction of the ionic conductivity of LiCoO₂ prior to its initial charge. The ionic conductivity of both an exemplary cold pressed LiCoO₂ pellet and the cold pressed LiCoO₂ pellet that was subsequently annealed at 700° C. for 1 h in air was 2*10⁻⁸ S/cm when measured at 25° C., which is more than three orders of magnitude lower than the electronic conductivity of LiCoO₂ at 25° C. Therefore, LiCoO₂ in this example demonstrates a predominantly electronically conducting material with a poor lithium ion conductivity.

Example 4

According to an embodiment of the present invention, Li_0.35La_0.55TiO₃ may be synthesized by standard powder reaction from the starting compounds LiOH, La₂O₃, and TiO₂. The final powder, Li_0.35La_0.55TiO₃, may be virtually free of impurity phases as verified by XRD. This powder may then be (a) cold pressed a 7 ton, 0.4 mm thick and 10 mm diameter powder pellet, which achieved 64% of the theoretical density of 4.99 g/ccm, and (b) cold pressed a 7 ton, 0.4 mm thick and 10 mm diameter powder pellet and subsequently sintered at 1100° C. for 1 h in air, which may achieve 70% of the theoretical density of 4.99 g/ccm. The so-obtained pellets may be applied with a PVD fabricated gold electrode on each pellet face. The ionic conductivity of the Li_0.35La_0.55TiO₃ pellets may be determined by electrochemical impedance spectroscopy that can reveal a grain boundary (inter-grain) conductivity of 5.6*10⁻⁸ S/cm measured at 25° C. for the cold pressed pellet while the bulk (intra-grain) conductivity may not be determined due the limited frequency capability of the test setup, which in turn may require frequencies of about 10 MHz range. The grain boundary conductivity of Li_0.35La_0.35TiO₃ pellets annealed at 700° C. for 1 h in air was determined to about 1.8*10⁻⁷ S/cm when measured at 25° C. The 1100° C. fabricated pellet, however, may allow the deconvolution into bulk (inter-grain) and grain boundary (intra-grain) conductivity, which can amount to 5.6*10⁻⁴ S/cm and 2.4*10⁻⁶ S/cm, respectively. These conductivities may be more than two orders of magnitude larger than the lithium ion conductivity of LiCoO₂ prior to its initial charge (see Example 3).

Example 5

According to an embodiment of the present invention, a composite cathode may be fabricated with, for example, a mixture of 80 wt % LiCoO₂ and 20 wt % Ni without the addition of an ionic conduction enhancer such as Li_0.35La_0.55TiO₃. The mixture may be cold pressed into a composite cathode pellet of the dimensions 0.3 mm×10 mm in diameter Other pellets may be further treated by sintering the pellets at 700° C. for 1 h in air. The resulting cold pressed or sintered composite cathode pellets may remain electronically well conducting (>10⁻² S/cm). When fabricated into full electrochemical cells comprising 1.5 μm thick Lipon electrolyte and a 10 μm metal Li anode, both pellet types may be found to suffer from severe current rate limitations as early as during the initial charge step at a constant voltage of 4.2V. At 25° C. the current may decay to about 1 μA within minutes, which may cause charge times of more than 10,000 h (more than 1 year) in the case of a 10 mAh cell. Such a cell, for example, may contain 83 mg of LiCoO₂. The mere composition of electrochemically active cathode material (LiCoO₂), which exhibits ionic and electronic conductivities sufficient, for example, for small cathode thicknesses, such as, for example, less than 30 μm, which are routinely built in thin-film form in certain embodiments of the present invention. Furthermore, electronic conduction enhancer (Ni) may not lead to electrochemically well active composite cathodes when used in substantial thicknesses (>>30 μm) for high capacity cells (>1 mAh/cm²). Therefore, at least one critical component may be missing from the composite cathode to attain useful battery performance.

Example 6

This example demonstrates an exemplary potential improvement over Example 5. According to an embodiment of the present invention, the powders used from Examples 1-4 may be mixed in the following weight percentage ratio: 40 wt % LiCoO₂ (theoretical density=5.06 g/ccm), 40 wt % Li_0.35La_0.55TiO₃ (theoretical density=4.99 g/ccm), and 20 wt % Ni (theoretical density=8.91 g/ccm). The powder mixture may be cold pressed into a 0.3 mm×10 mm in diameter composite cathode pellet of 80% of the theoretical density, which may be calculated from equation (12):Theoretical density of composite cathode pellet (g/ccm)=100%/(40 wt %/5.06 g/ccm+40 wt %/4.99 g/ccm+20 wt %/8.91 g/ccm)=5.50 g/ccm  (12)The electronic conductivity of an exemplary composite cathode pellet using two sandwiching copper plates was greater than 10⁻² S/cm while no new phases were detected by XRD other than the starting constituents LiCoO₂, Li_0.35La_0.55TiO₃, and Ni. The ionic conductivity of the composite cathode may be estimated from the volume fraction of the Li_0.35La_0.55TiO₃ within the composite cathode, which is given by equation (13):vol % of Li_0.35La_0.55TiO₃=40 wt %*5.50 g/ccm/4.99 g/ccm=44 vol %  (13)In a first approximation it may be assumed that pellet the following approximation holds true inside the composite cathode:Density of composite cathode/actual density of Li_0.35La_0.55TiO₃≈theoretical density of composite cathode/theoretical density of Li_0.35La_0.55TiO₃  (14)so that equation (13) provides a good estimate for the actual vol % of Li_0.35La_0.55TiO₃ inside the composite cathode. It may be further assumed that the lithium ion conductivity for an ideal grain size composition inside the composite cathode may be determined by the vol % of the dominant lithium ion conductor according toActual vol % Li_0.35La_0.55TiO₃*5.6*10⁻⁸ S/cm=2.5*10⁻⁸ S/cm  (15)

This lithium ion conductivity, example, based on the lithium ion grain boundary conductivity of Li_0.35La_0.55TiO₃ when cold pressed into a composite cathode pellet and not further heat treated, may be too low for practical purposes and may be similar to lithium ion conductivity of pure LiCoO₂ (see Example 3). Therefore, the composite cathode pellet may be heat treated at 700° C. at which the composite cathode may be provided with 0.44*1.8*10⁻⁷ S/cm=7.9*10⁻⁸ S/cm. This may still not be enough lithium ionic conductivity for practical applications (see Example 14). Annealing the composite cathode pellet at 900° C. may cause some reaction of LiCoO₂ with Ni to form NiO and LiCoO₂ decomposition side phases. The improvement in lithium ion conductivity may be minor and/or may rise to about 4*10⁻⁷ S/cm.

It may be evident that the lithium ionic grain boundary conductivity of the enhancer material can be improved when inside the composite cathode. The composite cathode may, for example, not be processed above a certain temperature (e.g., 900° C.) before undesirable chemical reactions can set in between the constituents of the composite cathode.

These certain exemplary improvements may be accomplished by grinding and milling the powder of the lithium ion conductivity enhancer to smaller grain sizes (<2 μm) and/or by appropriately modifying its grain surfaces, mechanically or chemically, to increase its lithium ion grain boundary conductivity. This so-surface-modified lithium ion conductivity enhancer material may exhibit a grain boundary conductivity of about 10⁻⁴ S/cm when cold pressed into composite cathode pellets and followed by an anneal step at 700° C. for 1 h in air. An overall lithium ion conductivity of an exemplary composite cathode of about 10⁻⁴ S/cm may permit continuous current draws of C/30, which translates into 0.2 mA for 6 mAh cells, which may have a 300 μm thick composite cathode (see Example 13).

Example 7

According to an embodiment of the present invention, a 10 mm diameter electrochemical cell providing 2 mAh/cm² capacity based on the geometric footprint of the positive cathode may be fabricated with a composite cathode consisting of 40 wt % LiCoO₂ (theoretical density=5.06 g/ccm), 40 wt % Li_0.35La_0.55TiO₃ (theoretical density=4.99 g/ccm), and 20 wt % Ni (theoretical density=8.91 g/ccm). The geometric footprint of a cathode is, for example, the surface area that one obtains when looking onto a surface along its surface normal or along the main axis of a device which has a geometric area that is measured while assuming a perfectly smooth surface. With this loading of the electrochemical active cathode material (LiCoO₂) the composite cathode can be fabricated with 11.2 mg LiCoO₂ thereby leading to a thickness, preferably of about 28 mg/(0.785 cm²*80%*5.50 g/ccm)=81 μm.

Example 8

According to an embodiment of the present invention, a 10 mm diameter electrochemical cell providing 2 mAh/cm² capacity may be fabricated with a composite cathode consisting of 20 wt % LiCoO₂ (theoretical density=5.06 g/ccm), 60 wt % Li_0.35La_0.55TiO₃ (theoretical density=4.99 g/ccm), and 20 wt % Ni (theoretical density=8.91 g/ccm). With this loading of the electrochemical active cathode material (LiCoO₂), the composite cathode can be fabricated with 11.2 mg LiCoO₂, thereby leading to a thickness of about 56 mg/(0.785 cm²*80%*5.49 g/ccm)=162 μm.

Example 9

According to an embodiment of the present invention, a 10 mm diameter electrochemical cell providing 4 mAh/cm² capacity may be fabricated with a composite cathode consisting of 40 wt % LiCoO₂ (theoretical density=5.06 g/ccm), 40 wt % Li_0.35La_0.55TiO₃ (theoretical density=4.99 g/ccm), and 20 wt % Ni (theoretical density=8.91 g/ccm). With this loading of the electrochemical active cathode material (LiCoO₂), the composite cathode can be fabricated with 22.4 mg LiCoO₂, thereby leading to a thickness of about 56 mg/(0.785 cm²*80%*5.50 g/ccm)=162 μm.

Example 10

According to an embodiment of the present invention, a 10 mm diameter electrochemical cell providing 4 mAh/cm² capacity may be fabricated with a composite cathode consisting of 20 wt % LiCoO₂ (theoretical density=5.06 g/ccm), 60 wt % Li_0.35La_0.55TiO₃ (theoretical density=4.99 g/ccm), and 20 wt % Ni (theoretical density=8.91 g/ccm). With this loading of the electrochemical active cathode material (LiCoO₂), the composite cathode can be fabricated with 22.4 mg LiCoO₂, thereby leading to a thickness of about 112 mg/(0.785 cm²*80%*5.49 g/ccm)=325 μm.

Example 11

According to an embodiment of the present invention, a 10 mm diameter electrochemical cell providing 5 mAh/cm² capacity may be fabricated with a composite cathode consisting of 40 wt % LiCoO₂ (theoretical density=5.06 g/ccm), 40 wt/o Li_0.35La_0.55TiO₃ (theoretical density=4.99 g/ccm), and 20 wt % Ni (theoretical density=8.91 g/ccm). With this loading of the electrochemical active cathode material (LiCoO₂), the composite cathode can be fabricated with 28 mg LiCoO₂, thereby leading to a thickness of about 70 mg/(0.785 cm²*80%*5.50 g/ccm)=203 μm.

Example 12

According to an embodiment of the present invention, a 10 mm diameter electrochemical cell providing 5 mAh/cm² capacity may be fabricated with a composite cathode consisting of 20 wt % LiCoO₂ (theoretical density=5.06 g/ccm), 60 wt %/Li_0.35La_0.55TiO₃ (theoretical density=4.99 g/ccm), and 20 wt % Ni (theoretical density=8.91 g/ccm). With this loading of the electrochemical active cathode material (LiCoO₂), the composite cathode can be fabricated with 28 mg LiCoO₂, thereby leading to a thickness of about 140 mg/(0.785 cm²*80%*5.49 g/ccm)=406 μm.

Example 13

According to an embodiment of the present invention, the cell of Example 11 wherein the 28 mg of LiCoO₂ material may be replaced by 28 mg of Li_1.2Ni_0.175Co_0.10Mn_0.525O₂ (see, e.g., U.S. Pat. Appl. Publ. No. 2010/086853, which is incorporated herein by reference in its entirety), which may improve the capacity of the cell by 70% when cycled between 4.6-2.0V and while concomitantly enhancing the capacity per unit area from 5 mAh/cm² to more than approximately 8.5 mAh/cm². Since the theoretical densities of LiCoO₂ and Li_1.2Ni_0.175Co_0.10Mn_0.525O₂ are similar, the actual densities of the fabricated composite cathode pellets in the cells are also similar, and therefore both composite cathode pellet thicknesses may be approximately 200 μm.

Example 14

According to an embodiment of the present invention, after rearranging equation (9),X²=4*RT/(c*z*F²)*t*G  (16)toX²*c*z*F²/(4*RT)=t*G  (17)whereinc=vol % of active cathode loading in composite cathode*concentration of mobile ionic species in the given active cathode material   (18)For the case wherein the active cathode material is LiCoO₂, c=vol % of active cathode loading in composite cathode*2.3*10⁻² mol/ccm (100% dense composite cathode assumed), z=1, F=96485 C/mol, R=8.3143 J/(K*mol), T=298 K, and(Thickness of composite cathode)²*vol % active cathode loading in composite cathode*2.2*10⁴ sec/(Ohm*ccm)=discharge time*lithium ion conductivity in composite cathode  (19)

In the case of a 5001 μm thick composite cathode with a 40 vol % loading, for example, a 10 hours (36,000 sec) discharge or charge time (C/10 rate) requires a minimum lithium ion conductivity inside the composite cathode of about 6*10⁻⁴ S/cm while a C/30 rate (30 hours discharge time or charge time) demands only about 2*10⁻⁴ S/cm.

Doubling the cathode loading (80 vol % active loading), for example, while maintaining a given capacity allows the composite cathode to be fabricated in about ½ the cathode thickness or 250 μm. As a result, the C/10 rate capability may require only about 3*10⁻⁴ S/cm while the C/30 scenario may only need about 1*10⁻⁴ S/cm.

Because creating composite cathodes with high lithium ion conductivity at, for example, 10⁻⁴ S/cm, is difficult, one option, for a given capacity in a given composite cathode and for a given discharge or charge time at a given temperature, may be to maximize the vol % loading of the active electrochemical material inside the composite cathode while concurrently minimizing the thickness of the composite cathode.

For a given capacity Q in the given composite cathode which has a given ionic conductivity, the discharge or charge time t determines the maximum continuous discharge or charge current according tomaximum continuous discharge or charge current=Q/t  (20)

Example 15

According to an embodiment of the present invention, a cell similar to the cell in example 7, but in which the Li_0.35La_0.55TiO₃ powder has an average grain size of less than 2 μm, may have an improved grain boundary conductivity in a manner that it enables the cell to be continuously discharged to about 2 mAh/cm² within 10 hours or less within its reversibility range of 4.2-2.0V. Reversibility range is, for example, the commonly accepted voltage range within which a given electrode is “substantially” stable at a given temperature. Higher temperatures may typically reduce reversibility range of electrodes. For example, at 25° C., the reversibility range of LiCoO₂ is commonly accepted as 4.2-2.0V vs. Li⁺/Li, which is equivalent to a stoichiometry range from about Li_1.0CoO₂ (2.0V vs. Li⁺/Li) to about Li_0.5CoO₂ (4.2V vs. Li⁺/Li).

Example 16

According to an embodiment of the present invention, a cell similar to the cell in example 9, but in which the Li_0.35La_0.55TiO₃ powder has an average grain size of less than 1 μm, may have an improved grain boundary conductivity that enables the cell to be continuously discharged to about 4 mAh/cm² within 10 hours or less within 4.2-2.0V.

Example 17

According to an embodiment of the present invention, a cell similar to the cell in example 11, but in which the Li_0.35La_0.55TiO₃ powder has an average grain size of less than 0.5 μm, which may have an improved grain boundary conductivity that enables the cell to be continuously (and fully) discharged to about 5 mAh/cm² in 10 hours or less within 4.2-2.0V.

Example 18

According to an embodiment of the present invention, the electrochemical cell of Example 7 may be configured with a 1.5 μm thick Lipon electrolyte, a 10 μm thick metal Li anode, a 10 μm Al cathode current collector foil, a 10 μm Cu anode current collector foil and a polymeric pouch encapsulation of 100 μm wall thickness above and below the electrochemical cell. Such characteristics provide a volumetric capacity density (which is calculated, for example, by dividing the rated capacity by the fully packaged battery volume) of about 59 Ah/liter in a fully packaged state and a volumetric energy density (which is calculated, for example, by dividing the product of rated capacity times the rated voltage by the fully packaged battery volume) of about 236 Wh/liter, after taking into account that the Li anode increases its thickness to a total of about 22 μm and the composite cathode to a total of about 82 μm when the cell is charged to 4.2V. A “fully packaged state”, for example, is the state of a battery that includes all of the peripherals inherent to the battery, which includes, for example, current collectors, terminals, primary encapsulation (if the housing is not already included in the encapsulation), and the housing.

Example 19

According to an embodiment of the present invention, the electrochemical cell of Example 9 may be configured with a 1.5 μm thick Lipon electrolyte, a 10 μm thick metal Li anode, a 10 μm Al cathode current collector foil, a 10 μm Cu anode current collector foil, and a polymeric pouch encapsulation of 100 μm wall thickness above and below the electrochemical cell. Such characteristics provide a volumetric capacity density of about 92 Ah/liter in a fully packaged state and a volumetric energy density of about 368 Wh/liter, after taking into account that the Li anode increases its thickness to a total of about 34 μm and the composite cathode to a total of about 163 μm when the cell is charged to 4.2V.

Example 20

According to an embodiment of the present invention, the electrochemical cell of Example 11 may be configured with a 1.5 μm thick Lipon electrolyte, a 10 μm thick metal Li anode, a 10 μm Al cathode current collector foil, a 10 μm Cu anode current collector foil, and a polymeric pouch encapsulation of 100 μm wall thickness above and below the electrochemical cell. Such characteristics provide a volumetric capacity density of about 103 Ah/liter in a fully packaged state and a volumetric energy density of about 412 Wh/liter, after taking into account that the Li anode increases its thickness to a total of about 40 μm and the composite cathode to a total of about 205 μm when the cell is charged to 4.2V.

Example 21

According to an embodiment of the present invention, the energy densities given in Examples 18, 19, and 20 increase to about 354 Wh/liter, about 552 Wh/liter, and about 618 Wh/liter, respectively, when increasing the loading of the electrochemically active cathode material (LiCoO₂) in each example from about 40 wt % to about 60 wt % and reducing the lithium conductivity enhancing material (Li_0.35La_0.55TiO₃, which has very similar density as LiCoO₂ so that that the thickness of the composite cathode remains virtually the same) from about 40 wt % to about 20 wt %.

Example 22

According to an embodiment of the present invention, a 618 Wh/liter cell from Example 21 contains about 5.89 mAh and may be configured with a 50 μm thick Li₇La₃Zr₂O₁₂ electrolyte, a 50 μm thick Li_ySn-activated, a nano-sized Li₄Ti₅O₁₂ Li-ion anode, a 10 μm Al cathode current collector foil, a 10 μm Cu anode current collector foil, and polymeric pouch encapsulation of 100 μm wall thickness above and below the electrochemical cell. This configuration provides the cell with a volumetric capacity density of about 135 Ah/liter in a fully packaged state and a volumetric energy density of about 338 Wh/liter, while the anode thickness remains approximately constant at about 50 nm and the composite cathode may reach a total thickness of about 205 μm when the cell is charged to 4.2V. The midpoint voltage, however, may change from 4.0V (Example 21) to about 2.5V.

Example 23

According to an embodiment of the present invention, a composite cathode may be fabricated consisting of a mixture of 60 wt % LiCoO₂, 20 wt % Ni, and 20 wt % of chemically surface modified Li_0.35La_0.55TiO₃. The chemical surface modification of Li_0.35La_0.55TiO₃ may be accomplished by separate and prior reaction with LiIO₄*2H₂O, Polypyrrole, Li₃N, Ni or carbon at temperatures between 250° C.-900° C. The mixture may then be cold pressed into a composite cathode pellet of the dimensions 0.3 mm×10 mm in diameter and subsequently annealed at 250° C.-500° C. for 1 h in air. The resulting annealed composite cathode pellets remains electronically well conducting (>10⁻² S/cm). When fabricated into full electrochemical cells comprising 1.5 μm thick Lipon electrolyte and a 10 μm metal Li anode, the composite cathode may supply the cell with continuous charge and discharge currents greater than C/30 of between 4.2-2.0V. The chemical surface modification substantially enhances the lithium ion conductivity of the ionic conductivity enhancer material (Li_0.35La_0.55TiO₃) by about three orders of magnitude from a lithium ion grain boundary (intra-grain) conductivity of 10⁻⁷ S/cm to a lithium ion grain boundary conductivity value close to 10⁻⁴ S/cm.

Example 24

According to an embodiment of the present invention, a composite cathode consisting of a mixture of about 80 wt % chemically surface modified LiCoO₂ and about 20 wt % Ni without the addition of any ionic conduction enhancer such as Li_0.35La_0.55TiO₃ may be fabricated. The chemical surface modification of LiCoO₂ may be accomplished by separate and prior reaction with LiIO₄*2H₂O or Polypyrrole at temperatures between about 250° C.-900° C. The mixture may then be cold pressed into a composite cathode pellet of the dimensions 0.3 mm×10 mm in diameter and subsequently annealed at about 250° C.-500° C. for 1 h in air. The resulting annealed composite cathode pellets may remain electronically well conducting (>10⁻² S/cm). When fabricated into full electrochemical cells comprising 1.5 μm thick Lipon electrolyte and a 10 μm metal Li anode, these composite cathodes in these cells may sustain continuous charge and discharge currents greater than C/30 of between 4.2-2.0V. It is evident that the chemical surface modification substantially enhances the lithium ion conductivity of the electrochemically active material (LiCoO₂) by more than approximately 3 orders of magnitude from about 2*10⁻⁸ S/cm to a value close to about 10⁻⁴ S/cm. This approach allows the fabrication of composite cathodes, which have an ionic conductivity enhancer that may be the electrochemically active material itself, thereby rendering a separately provided ionic conductivity enhancer that has no electrochemical storage capacity (e.g., Li_0.35La_0.55TiO₃) redundant.

Example 25

According to an embodiment of the present invention, a 10 mm diameter electrochemical cell that utilizes the composite cathode from Example 24 may be fabricated. The composite cathode may have an actual cold pressed density of about 4.43 g/ccm, which is about 80% of its theoretical density of about 5.54 g/ccm, and a thickness of about 350 μm. This composite cathode supplies the cell with about 13.7 mAh of capacity. This cell may be further configured with a 1.5 μm thick Lipon electrolyte, a 10 μm thick metal Li anode, a 10 μm Al cathode current collector foil, a 10 μm Cu anode current collector foil and polymeric pouch encapsulation of 100 μm wall thickness above and below the electrochemical cell. This construction provides the cell with a volumetric capacity density of about 254 Ah/liter in a fully packaged state and a volumetric energy density of about 1018 Wh/liter, after taking into account that the Li anode will increase its thickness to a total of about 92 μm and the composite cathode to a total of about 355 μm when the cell is charged to 4.2V. Such an electrochemical cell may have an improved grain boundary conductivity that enables the cell to be continuously (and fully) discharged to about 17 mAh/cm² in 10 hours or less within 4.2-2.0V.

FIG. 1 shows a prior art cross-sectional view of a Li-ion or Li-polymer battery as used in cell phone batteries. The composite cathode 110 is typically approximately 100 μm thick and composed of four phases, three of which are solid state phases and the fourth of which is a liquid phase. The electrochemically active cathode material 111 may be solid state LiCoO₂ (or derivative) powder and the electronic conductivity enhancer 113 can be graphitic carbon. Polymeric binder 114, such as PVDF, binds the previous two solid state phases to the Al foil substrate 130. A non-aqueous liquid electrolyte 112, which is an organic solvent with dissolved lithium salt, is soaked into the pores of the composite cathode 110. Liquid electrolyte 112 has a high lithium ion conductivity of 10⁻²-10⁻³ S/cm at 25° C., when 100% of the measurement volume is electrolyte. Liquid electrolyte 112 may reach almost every volume element inside the composite cathode, except for those volume elements that are already taken by the electrochemically active cathode material 111, the electronic conductivity enhancer 113 and, to some extent, the polymeric binder 114. The composite cathode 110 may have an effective overall lithium ion conductivity throughout its bulk of approximately 10⁻³-10⁻⁴ S/cm at 25° C. given that the electrolyte 112 can be present in, for example, only about 30% of the composite cathode volume and additionally may, for example, have torturous pathways to overcome in the pores to unfold its lithium conductivity.

Further shown in FIG. 1 are the non-aqueous liquid electrolyte 112 soaked, perforated polymeric separator 120 (typically 13-50 μm thick) and a typical Li-ion or Li-polymer anode 140. A Li-ion or Li-polymer anode 140 is typically around 100 μm thick and consists of electrochemical anode material 141, usually provided through graphitic carbon, a polymeric binder 142 that is optimized for graphitic carbon, and non-aqueous liquid electrolyte 112. Additional cell components exist, such as the Cu anode current collector foil and cell packaging, but are not included in FIG. 1.

FIG. 2 shows one of the exemplary embodiments of the present invention. Composite cathode 210 may be composed of, for example, at least three solid state phases (without any liquid phases present): (1) at least one solid-state electrochemically active cathode material 211 such as, for instance, LiCoO₂; (2) at least one solid-state electronically conducting material 213, such as, for instance, Ni, which has an electronic conductivity that may be at least three times higher than the electronic conductivity of said electrochemically active cathode material 211 prior to its initial charge; and (3) at least one solid-state, inorganic, ionically conducting material 212, such as, for instance, Li_0.35La_0.55TiO₃, which may have an ionic conductivity that may be at least three times higher than the ionic conductivity of the electrochemically active cathode material 211 prior to its initial charge.

Composite cathode 210 of certain embodiments of the present invention may not require any pores for a liquid non-aqueous electrolyte and thus may be fabricated in a denser fashion (e.g., typical residual porosity of less than 20%) and annealed at higher temperatures for improved grain boundary bonding. Composite cathode 210 of certain embodiments of the present invention may be easily fabricated with increased thickness (e.g., 100-1000 μm) and good mechanical properties. In certain embodiments of the present invention, composite cathode 210 may have sufficient rigidity so that it is able to serve as its own substrate or substrate for the other cell components, such as, for instance, 1.5 μm thick solid-state thin-film electrolyte 220 and thin-film metallic lithium anode 240.

FIG. 3 shows another alternative preferred embodiment of the present invention. Composite cathode 310 may be composed of at least two solid state phases (without any liquid phases present): (1) at least one solid-state electrochemically active cathode material 311 such as, for instance, surface modified LiCoO₂ with strongly enhanced lithium ion grain boundary conductivity; and (2) at least one solid-state electronically conducting material 313, such as, for instance Ni, which has an electronic conductivity that may be at least three times higher than the electronic conductivity of said electrochemically active cathode material 311 prior to its initial charge. The provision of surface modified LiCoO₂ with strongly enhanced lithium ion grain boundary conductivity may make obsolete the need for a separate, solid-state, inorganic, ionically conducting material, such as element 212 in FIG. 2.

Composite cathode 310 of certain embodiments of the present invention may not require any pores for a liquid non-aqueous electrolyte and thus may be fabricated in a denser fashion (typical residual porosity of less than 20%) and annealed at higher temperatures for improved grain boundary bonding. Composite cathode 310 of certain embodiments of the present invention may be easily fabricated with increased thickness (e.g., 100-1000 μm) and good mechanical properties. In most cases, composite cathode 310 of certain embodiments of the present invention may have sufficient rigidity so that it is able to serve as its own substrate or substrate for the other cell components, such as, for instance, 1.5 μm thick solid-state thin-film electrolyte 320 and thin-film metallic lithium anode 340.

The embodiments and examples described above are exemplary only. One skilled in the art may recognize variations from the embodiments specifically described here, which are intended to be within the scope of this disclosure and invention. As such, the invention is limited only by the following claims. Thus, it is intended that the present invention cover the modifications of this invention provided they come within the scope of the appended claims and their equivalents.

Claims

1. A rechargeable electrochemical device comprising: a solid-state cathode comprising: an electrochemically active material having an electronic conductivity and an ionic conductivity, the electrochemically active material having a modified surface with enhanced lithium ion grain boundary conductivity, such that the ionic conductivity of the electrochemically active material with the modified surface is at least three times higher than an ionic conductivity of the electrochemically active material without the modified surface, wherein the solid-state composite cathode does not include a liquid and does not include a gel, andthe modified surface is a chemically modified surface achieved with reacting the electrochemically active material with a surface modifying chemical.

2. The rechargeable electrochemical device of claim 1, wherein the solid-state cathode further comprises an electronically conducting material having an electronic conductivity at least three times higher than the electronic conductivity of the electrochemically active material in a pre-charged state.

3. The rechargeable electrochemical device of claim 2, wherein the electronically conducting material is nickel.

4. The rechargeable electrochemical device of claim 2, wherein the electrochemically active material is 80 wt. % or greater of the solid-state composite cathode.

5. The rechargeable electrochemical device of claim 1, wherein a particle size of the electrochemically active material is between 0.1-10 μm.

6. The rechargeable electrochemical device of claim 1, wherein the electrochemically active material is surface modified LiCoO2.

7. The rechargeable electrochemical device of claim 1, wherein the electronic conductivity of the electrochemically active material is enhanced by doping a bulk grain portion of the electrochemically active material.

8. The rechargeable electrochemical device of claim 1, further comprising a solid-state electrolyte, which does not comprise a liquid and which does not comprise a gel.

9. The rechargeable electrochemical device of claim 1, wherein the surface modifying chemical is LiIO4*2H2O or polypyrrole.

10. A rechargeable electrochemical device comprising: a solid-state composite cathode consisting of: an electrochemically active material having an electronic conductivity and an ionic conductivity, the electrochemically active material having a modified surface such that the ionic conductivity of the electrochemically active material with the modified surface is at least three times higher than an ionic conductivity of the bulk grain of the electrochemically active material, andan electronically conducting material having an electronic conductivity at least three times higher than the electronic conductivity of the electrochemically active material in a pre-charged state.

11. The rechargeable electrochemical device of claim 10, wherein the electronically conducting material is nickel and the electrochemically active material is LiCoO2.

12. The rechargeable electrochemical device of claim 10, wherein the modified surface of the electrochemically active material is a mechanically modified surface.

13. The rechargeable electrochemical device of claim 10, wherein the modified surface of the electrochemically active material is a chemically modified surface by reaction of the electrochemically active material with a surface modifying chemical.

14. A rechargeable electrochemical device comprising: a solid-state composite cathode including: an electrochemically active material consisting essentially of LiCoO2, the electrochemically active material having an electronic conductivity and an ionic conductivity, the electrochemically active material having a mechanically modified surface having enhanced lithium ion grain boundary conductivity, such that the ionic conductivity of the electrochemically active material with the modified surface is at least three times higher than an ionic conductivity of bulk electrochemically active material without the modified surface, wherein the solid-state composite cathode does not include a liquid and does not include a gel;a negative anode; anda solid-state electrolyte sandwiched between the solid state composite cathode and the negative anode.

15. The rechargeable electrochemical device of claim 14, wherein a particle size of the electrochemically active material is between 0.1 μm-10 μm.

16. The rechargeable electrochemical device of claim 14, wherein the solid-state composite cathode further comprises an electronically conducting material having an electronic conductivity at least three times higher than the electronic conductivity of the electrochemically active material in a pre-charged state.

17. The rechargeable electrochemical device of claim 16, wherein the electronically conducting material is nickel.

18. The rechargeable electrochemical device of claim 16, wherein the electrochemically active material is 80 wt. % or greater of the solid-state composite cathode.

19. The rechargeable electrochemical device of claim 16, further comprising a volumetric capacity density of at least 250 Ah/liter in a fully packaged state.

20. The rechargeable electrochemical device of claim 16, further comprising a volumetric energy density of at least 1000 Wh/liter in a fully packaged state.