Title of Invention: Synthetic method for preparation of a low surface area, single phase silver vanadium oxide
Abstract: A single phase silver vanadium oxide prepared from a mixture of a decomposable silver salt and vanadium oxide first heated at about 2xc2x0 C. to about 40xc2x0 C. above the decomposition temperature of the mixture followed by a second heating in a temperature range of about 490xc2x0 C. to about 520xc2x0 C. is described. The silver vanadium oxide material is coupled with a lithium anode and activated with a nonaquecus electrolyte to provide an improved high energy density electrochemical cell having increased pulse voltages and a reduction in voltage delay.
Brief Summary: 1. Field of the Invention
The present invention generally relates to the conversion of chemical energy to electrical energy, and more particularly, to an alkali metal electrochemical cell having a transition metal oxide cathode activated with a nonaqueous electrolyte. The transition metal oxide cathode active material is preferably silver vanadium oxide having a single phase with a surface area of about 0.2 m2/gram to about 0.80 m2/gram. The single phase silver vanadium oxide is produced in a decomposition reaction at a final decomposition temperature of about 490xc2x0 C. to about 520xc2x0 C.
2. Prior Art
U.S. Pat. Nos. 4,310,609 and 4,391,729 to Liang et al. disclose the preparation of silver vanadium oxide (SVO) as a cathode material for use in a nonaqueous electrolyte battery. These patents describe the preparation of silver vanadium oxide by a thermal decomposition reaction involving a final heat treatment step of about 360xc2x0 C.
U.S. Pat. No. 4,830,940 to Keister et al. describes a solid cathode, liquid organic electrolyte, lithium cell for delivering high current pulses. The solid cathode includes as an active material AgxV2Oy wherein x is in the range from about 0.5 to about 2.0 and y is in the range from about 4.5 to 6.0. Keister et al. reference the publication xe2x80x9cEffect of Silver Content On the Performance of Primary Lithium/Silver Vanadium Oxide Batteriesxe2x80x9d, E. S. Takeuchi and P. Keister, Electrochemical Society, Oct. 13-18, 1985, Las Vegas, Nev., Abstract No. 125, which describes the preparation of silver vanadium oxide at about 360xc2x0 C. from the thermal decomposition of silver nitrate and vanadium pentoxide.
U.S. Pat. No. 5,221,453 to Crespi discloses the preparation of silver vanadium oxide by a chemical addition reaction (combination of AgVO3 and V2O5 or Ag2O and V2O5) in a temperature range of about 300xc2x0 C. to about 700xc2x0 C. The chemical addition reaction is described as being distinct from the thermal decomposition reaction described by Liang et al. and Keister et al. A decomposition reaction is characterized by the evolution of nitrogen oxide gas when the reactants are V2O5 and AgNO3. A chemical addition reaction does not include the evolution of reaction by product gases.
In the publication R. A. Leising and E. S. Takeuchi, Chemistry of Materials, 5, 738-742 (1993) the preparation of silver vanadium oxide by the thermal decomposition of AgNO3 and V2O5 at temperatures of 320xc2x0 C., 375xc2x0 C., 450xc2x0 C. and 540xc2x0 C. is described. This publication also reports discharge results of experimental lithium cells containing silver vanadium oxide cathode active materials prepared at those various temperatures and activated with 1M LiAsF6 PC/DME electrolyte. The 375xc2x0 C. prepared SVO material gave slightly higher delivered capacity than the 450xc2x0 C. material, and significantly higher capacity than the SVO material prepared at 540xc2x0 C. As an illustration, the graph in FIG. 1, curve 10, was constructed from the discharge capacity versus synthesis temperature of lithium cells having silver vanadium oxide prepared in a thermal decomposition reaction of AgNO3 and V2O5 according to this publication. The delivered capacity of the variously prepared cells was measured using a constant resistance discharge over a short period of time (less than 2 days).
The present invention relates to a nonaqueous electrolyte, alkali metal/transition metal oxide electrochemical cell and, in particular, a lithium/silver vanadium oxide electrochemical cell designed for high current pulse discharge applications while exhibiting reduced or no appreciable voltage delay and reduced Rdc build-up. An example of such an application is an implantable cardiac defibrillator, where the battery may run under a light load, device monitoring mode for extended periods of time interrupted by high rate, current pulse discharge during device activation. Voltage delay is a phenomenon typically exhibited in a lithium/silver vanadium oxide cell that has been depleted of about 40% to about 70% of its capacity and is subjected to current pulse discharge applications. The occurrence of voltage delay is detrimental because it may result in delayed device activation and shortened device life.
The desirable decrease in voltage delay is realized in lithium cells that, according to the present invention, contain a low surface area, single phase silver vanadium oxide prepared in a decomposition reaction at a temperature above the decomposition temperature of the mixture of starting materials followed by a second heating at a temperature in the range of about 490xc2x0 C. to about 520xc2x0 C. and are activated with a nonaqueous electrolyte.
A particularly preferred transition metal oxide cathode active material comprises a single phase silver vanadium oxide having the general formula AgxV2Oy wherein in the xcex5-phase x=1.0 and y=5.5. According to the present invention, this material is produced in a decomposition reaction by first heating the mixture of starting materials to a temperature above the decomposition temperature of the mixture followed by a second heating at a final heating temperature of about 490xc2x0 to about 520xc2x0 C. This particularly preferred SVO material is in contrast to xcex2-phase silver vanadium oxide having in the general formula x=0.35 and y=5.18 and xcex3-phase silver vanadium oxide having in the general formula x=0.74 and y=5.37. The surface area of this material is about 0.2 m2/gram to about 0.80 m2/gram.
A typically used electrolyte for activating this electrochemical couple comprises 1M LiAsF6 dissolved in a 50:50 mixture, by volume, of PC and DME. The increase in usable cell capacity, and subsequent increase in battery life in such a cell is unexpected based on the published capacity data for 450xc2x0 C. and 540xc2x0 C. SVO discharged under quick discharge conditions. Again, in the previously discussed Leising et al. publication, the 450xc2x0 C. SVO gave less capacity than SVO prepared at 375xc2x0 C., and it could be inferred that the further the preparation temperature is from 375xc2x0 C., the less capacity the cell will provide.
Detailed Description: As used herein, the term xe2x80x9cpulsexe2x80x9d means a short burst of electrical current of a greater amplitude than that of a prepulse current immediately prior to the pulse. A pulse train consists of at least two pulses of electrical current delivered in relatively short succession with or without open circuit rest between the pulses.
Lower pulse voltages caused by voltage delay, even if only temporary, are undesirable since they can cause circuit failure in device applications, and effectively result in shorter cell life. Rdc build-up also reduces the life of an electrochemical cell by lowering the pulse voltage during high rate discharge. As is well known by those skilled in the art, an implantable cardiac defibrillator is a device that requires a power source for a generally medium rate, constant resistance load component provided by circuits performing such functions as, for example, the heart sensing and pacing functions. From time to time, the cardiac defibrillator may require a generally high rate, pulse discharge load component that occurs, for example, during charging of a capacitor in the defibrillator for the purpose of delivering an electrical shock to the heart to treat tachyarrhythmias, the irregular, rapid heartbeats that can be fatal if left uncorrected. Accordingly, reduction and even elimination of voltage delay during a current pulse application is important for proper device operation and extended device life.
The electrochemical cell of the present invention is particularly suited for powering an implantable medical device such as a cardiac defibrillator and the like. The cell comprises an anode of a metal selected from Groups IA, IIA and IIIB of the Periodic Table of the Elements, including lithium, sodium, potassium, etc., and their alloys and intermetallic compounds including, for example, Lixe2x80x94Si, Lixe2x80x94Al, Lixe2x80x94B and Lixe2x80x94Sixe2x80x94B alloys and intermetallic compounds. The preferred anode comprises lithium. An alternate anode comprises a lithium alloy, such as lithium-aluminum alloy. The greater the amount of aluminum present by weight in the alloy, however, the lower the energy density of the cell.
The form of the anode may vary, but preferably the anode is a thin metal sheet or foil of the anode metal, pressed or rolled on a metallic anode current collector, i.e., preferably comprising nickel, to form an anode component. In the exemplary cell of the present invention, the anode component has an extended tab or lead of the same material as the anode current collector, i.e., preferably nickel, integrally formed therewith such as by welding and contacted by a weld to a cell case of conductive material in a case-negative electrical configuration. Alternatively, the anode may be formed in some other geometry, such as a bobbin shape, cylinder or pellet to allow an alternate low surface cell design.
The electrochemical reaction at the cathode involves conversion of ions which migrate from the anode to the cathode into atomic or molecular forms. The cathode active material of the present invention comprises a low surface area, a single phase mixed metal oxide. A preferred single phase mixed metal oxide according to the present invention begins by thoroughly mixing silver nitrate with vanadium pentoxide. This mixture is first heated to about 2xc2x0 C. to about 40xc2x0 C. above the mixture""s decomposition temperature. Preferably, the mixture is heated to about 300xc2x0 C., which is about 20xc2x0 C. above the decomposition temperature of the mixture, but below the decomposition temperature of the silver nitrate constituent alone. The mixture of starting materials is held at this temperature for about 5 hours to about 16 hours, or until the mixture has completely decomposed. After thoroughly grinding the resulting decomposed admixture, it is heated to a temperature of about 50xc2x0 C. to about 250xc2x0 C. above the decomposition temperature of the admixture for about 12 to 48 hours, or to about 490xc2x0 C. to about 520xc2x0 C. for about 48 hours for the silver nitrate and vanadium pentoxide admixture.
Table 1 below lists a summary of thermal analysis data for various ones of the starting materials of the present invention.
Table 2 below lists a summary of the thermal analysis data for various decomposable mixtures of the starting materials set forth in Table 1.
According to the present invention, any one of the decomposable starting materials is provided in a mixture with a metal, a metal oxide or a mixed metal oxide comprising at least a first and a second metals or their oxides and possibly a third metal or metal oxide, or a mixture of a first and a second metals or their metal oxides incorporated in the matrix of a host metal oxide. The cathode active material may also comprise a metal sulfide. The mixture is ground to ensure homogeneity and subsequently thermally treated to provide the novel low surface area, single phase mixed metal oxide cathode active material. Thus, the present synthesis protocol occurs in an oxygen-containing atmosphere at a decomposition heating temperature of about 80xc2x0 C. to about 310xc2x0 C. depending on the decomposable starting material constituent. The exact temperature at which decomposition begins is dictated by the starting materials.
Table 3 indicates the temperatures appropriate for the decomposition heating step using different silver precursor materials according to the present invention.
Those skilled in this art will readily recognize that various combinations of nitrates, nitrites, carbonates, sulfides and ammonium salts not listed in Table 2 are useful for preparation of single phase metal oxides according to the present invention. These include, but are not limited to, silver lactate and vanadium oxide; silver triflate and vanadium oxide; silver pentafluoropropionate and vanadium oxide; silver laurate and vanadium oxide; silver myristate and vanadium oxide; silver palmitate and vanadium oxide; silver stearate and vanadium oxide; manganese nitrate and vanadium oxide; manganese carbonate and vanadium oxide; manganese nitrite and vanadium oxide; silver sulfide and vanadium oxide; copper(II) sulfide and vanadium oxide; manganese sulfide and vanadium oxide; silver nitrate, manganese nitrate and vanadium oxide; copper nitrate, manganese nitrate and vanadium oxide; silver carbonate, copper carbonate and vanadium oxide; silver carbonate, manganese carbonate and vanadium oxide; copper carbonate, manganese carbonate and vanadium oxide; silver nitrate, copper nitrate and vanadium oxide; silver nitrate, manganese nitrite and vanadium oxide; copper nitrate, manganese nitrate and vanadium oxide; silver sulfide, copper(II) sulfide and vanadium oxide; silver sulfide, manganese sulfide and vanadium oxide; copper sulfide, manganese sulfide and vanadium oxide; silver sulfide, copper nitrate and vanadium oxide; silver sulfide, copper nitrite and vanadium oxide; silver sulfide, copper carbonate and vanadium oxide; silver nitrate, copper sulfide and vanadium oxide; silver nitrate, copper sulfide and vanadium oxide; silver carbonate, copper sulfide and vanadium oxide; silver sulfide, manganese nitrate and vanadium oxide; silver sulfide, manganese nitrite and vanadium oxide; silver sulfide, manganese carbonate and vanadium oxide, and combinations and mixtures thereof.
Those skilled in the art will also understand that Table 2 lists the various reactants in 1:1 mole ratios and their corresponding melting point and decomposition temperature. However, the mole ratio can be changed which will consequently change the melting point and decomposition temperature of the resulting mixtures.
One preferred low surface area, single phase mixed metal oxide substantially comprises an active material having the general formula SMxV2Oy wherein SM is a metal selected from Groups IB to VIIB and VIII of the Periodic Table of Elements and wherein x is about 0.30 to 2.0 and y is about 4.5 to 6.0 in the general formula. By way of illustration, and in no way intended to be limiting, one exemplary single phase cathode active material substantially comprises silver vanadium oxide (SVO) having the general formula AgxV2Oy in any one of its phases, i.e., phase silver vanadium oxide having in the general formula x=0.35 and y=5.8, xcex3-phase silver vanadium oxide having in the general formula x=0.74 and y=5.37 and xcex5-phase silver vanadium oxide having in the general formula x=1.0 and y=5.5, the latter phase being most preferred.
The preparation technique of a low surface area, single phase mixed metal oxide according to the present invention produces an active material displaying increased capacity and decreased voltage delay in comparison to a mixed phase metal oxide such as silver vanadium oxide prepared using a decomposition synthesis from AgNO3 and V2O5 starting materials carried out according to the previously referenced U.S. Pat. No. 4,391,729 to Liang et al. The discharge capacity and decreased voltage delay of the single phase metal oxide of the present invention is also an improvement over that of silver vanadium oxide typically prepared from Ag2O and V2O5 by a chemical addition reaction such as is described in U.S. Pat. No. 5,498,494 to Takeuchi et al., which is assigned to the assignee of the present invention and incorporated herein by reference.
Advantages of the use of this low surface area, single phase material include increased capacity and decreased voltage delay for pulse discharge applications. An example of such an application is the implantable cardiac defibrillator, where the battery may run under a light load for extended periods of time interrupted by high rate pulse discharge. The occurrence of voltage delay under these conditions is detrimental in that it may shorten device life.
Another preferred single phase composite cathode material is prepared from a homogeneous admixture of vanadium oxide and a second decomposable metal compound, metal or metal oxide and a third decomposable metal compound, metal or metal oxide wherein at least one of the second and third metal constituents is a decomposable form of silver and copper. According to the present invention, the homogeneous admixture is formed from V2Oz wherein zxe2x89xa65 combined with a mixture of either copper nitrate, copper nitrite or an ammonium salt of copper and a silver oxide or, a mixture of copper oxide and silver nitrate, silver nitrite or an ammonium salt of silver to provide the single phase metal oxide having the formula CuxAgyV2Oz (CSVO), preferably with xxe2x89xa6y. In this preparation technique, the oxide starting materials may include Ag2Oz wherein z=2 to 1 and CuOz wherein z=0 to 1. Thus, this composite cathode active material may be described as a metal-metal oxide-metal oxide, or a metal-metal-metal oxide and the range of material compositions found for CuxAgyV2Oz is preferably about 0.01xe2x89xa6xxe2x89xa61.0, about 0.01xe2x89xa6yxe2x89xa61.0 and about 5.01xe2x89xa6zxe2x89xa66.5. Another embodiment of the present invention has vanadium oxide combined with both a decomposable compound of silver and copper. Typical single phase forms of CSVO are Cu0.16Ag0.67V2Oz with z being about 5.5 and Cu0.5Ag0.5V2Oz with z being about 5.75. U.S. Pat. No. 5,472,810 to Takeuchi et al. and U.S. Pat. No. 5,516,340 to Takeuchi et al. describe the prior art preparation of CSVO.
The above described active materials are formed into an electrode for incorporation into an electrochemical cell by mixing one or more of them with a conductive additive such as acetylene black, carbon black and/or graphite. Metallic materials such as nickel, aluminum, titanium and stainless steel in powder form are also useful as conductive diluents when mixed with the above listed active materials. The electrode further comprises a binder material which is preferably a fluoro-resin powder such as powdered polytetrafluoroethylene (PTFE) or powdered polyvinylidene fluoride (PVDF). More specifically, a preferred cathode active material comprises SVO in any one of its many phases, or mixtures thereof, mixed with a binder material and a conductive diluent.
A preferred cathode active admixture according to the present invention comprises from about 80% to 99%, by weight, of a cathode active material comprising SVO mixed with a suitable binder and a conductor diluent. The resulting blended cathode active mixture may be formed into a free-standing sheet prior to being contacted with a current collector to form the cathode electrode. The manner in which the cathode active mixture is prepared into a free-standing sheet is thoroughly described in U.S. Pat. No. 5,435,874 to Takeuchi et al., which is assigned to the assignee of the present invention and incorporated herein by reference. Further, cathode components for incorporation into the cell. may also be prepared by rolling, spreading or pressing the cathode active mixture of the present invention onto a suitable current collector. Cathodes prepared as described above may be in the form of one or more plates operatively associated with at least one or more plates of anode material, or in the form of a strip wound with a corresponding strip of anode material in a structure similar to a xe2x80x9cjellyrollxe2x80x9d.
In order to prevent internal short circuit conditions, the cathode is separated from the anode material by a suitable separator material. The separator is of electrically insulative material, and the separator material also is chemically unreactive with the anode and cathode active materials and both chemically unreactive with and insoluble in the electrolyte. In addition, the separator material has a degree of porosity sufficient to allow flow there through of the electrolyte during the electrochemical reaction of the cell. Illustrative separator materials include fabrics woven from fluoropolymeric fibers including polyvinylidine fluoride, polyethylene tetrafluoroethylene, and polyethylenechlorotrifluoroethylene used either alone or laminated with a fluoropolymeric microporous film, non-woven glass, polypropylene, polyethylene, glass fiber materials, ceramics, a polytetrafluoroethylene membrane commercially available under the designation ZITEX (Chemplast Inc.), a polypropylene membrane commercially available under the designation CELGARD (Celanese Plastic Company, Inc.) and a membrane commercially available under the designation DEXIGLAS (C. H. Dexter, Div., Dexter Corp.). The separator may also be composed of non-woven glass, glass fiber materials and ceramic materials.
The form of the separator typically is a sheet which is placed between the anode and cathode electrodes and in a manner preventing physical contact there between. Such is the case when the anode is folded in a serpentine-like structure with a plurality of cathode plates disposed intermediate the anode folds and received in a cell casing or when the electrode combination is rolled or otherwise formed into a cylindrical xe2x80x9cjellyrollxe2x80x9d configuration.
The electrochemical cell of the present invention further includes a nonaqueous, lonically conductive electrolyte operatively associated with the anode and the cathode electrodes. The electrolyte serves as a medium for migration of ions between the anode and the cathode during the electrochemical reactions of the cell, and nonaqueous solvents suitable for the present invention are chosen so as to exhibit those physical properties necessary for ionic transport (low viscosity, low surface tension and wettability). Suitable nonaqueous solvents are comprised of an inorganic salt dissolved in a nonaqueous solvent and more preferably an alkali metal salt dissolved in a mixture of aprotic organic solvents comprising a low viscosity solvent including organic esters, ethers and dialkyl carbonates, and mixtures thereof, and a high permittivity solvent including cyclic carbonates, cyclic esters and cyclic amides, and mixtures thereof. Low viscosity solvents include tetrahydrofuran (THF), diisopropylether, methyl acetate (MA), diglyme, triglyme, tetraglyme, 1,2-dimethoxyethane (DME), 1,2-diethoxyethane (DEE), 1-ethoxy,2-methoxyethane (EME), dimethyl carbonate (DMC), diethyl carbonate (DEC), dipropyl carbonate (DPC), ethylmethyl carbonate (EMC), methylpropyl carbonate (MPC) and ethylpropyl carbonate (EPC), and mixtures thereof. High permittivity solvents include propylene carbonate (PC), ethylene carbonate (EC), butylene carbonate (BC), acetonitrile, dimethyl sulfoxide, dimethyl formamide, dimethyl acetamide, xcex3-valerolactone, xcex3-butyrolactone (GBL) and N-methyl-pyrrolidinone (NMP), and mixtures thereof.
The preferred electrolyte comprises an inorganic alkali metal salt, and in the case of an anode comprising lithium, the alkali metal salt of the electrolyte is a lithium based salt. Known lithium salts that are useful as a vehicle for transport of alkali metal ions from the anode to the cathode include LiPF6, LiBF4, LiAsF6, LiSbF6, LiClO4, LiAlCl4, LiGaCl4, LiC(SO2CF3)3, LiN(SO2CF3)2, LiSCN, LiO3SCF2CF3, LiC6F5SO3, LiO2CCF3, LiSO3F, LiNO3, LiO2, LiB(C6H5)4 and LiCF3SO3, and mixtures thereof. Suitable salt concentrations typically range between about 0.8 to 1.5 molar, and a preferred electrolyte for a lithium/transition metal oxide electrochemical cell includes LiAsF6 or LiPF6 dissolved in a 50:50 mixture, by volume, of PC and DME.
In the present invention, the preferred electrochemical cell has an anode of lithium metal and a cathode of the transition mixed metal oxide AgV2O5.5 prepared in a thermal decomposition reaction by heating the mixture of starting materials to a first temperature above the decomposition temperature of the mixture followed by heating to a second temperature of about 490xc2x0 C. to about 520xc2x0 C., as previously described in detail. The activating electrolyte is 1.0M to 1.4M LiAsF6 dissolved in an aprotic solvent mixture comprising at least one of the above listed low viscosity solvents and at least one of the above listed high permittivity solvents having an organic carbonate additive provided therein. The preferred aprotic solvent mixture comprises a 50/50 mixture, by volume, of propylene carbonate and dimethoxyethane.
The assembly of the cell described herein is preferably in the form of a wound element cell. That is, the fabricated cathode, anode and separator are wound together in a xe2x80x9cjellyrollxe2x80x9d type configuration or xe2x80x9cwound element cell stackxe2x80x9d such that the anode is on the outside of the roll to make electrical contact with the cell case in a case-negative configuration. Using suitable top and bottom insulators, the wound cell stack is inserted into a metallic case of a suitable size dimension. The metallic case may comprise materials such as stainless steel, mild steel, nickel-plated mild steel, titanium, tantalum or aluminum, but not limited thereto, so long as the metallic material is compatible for use with components of the cell.
The cell header comprises a metallic disc-shaped body with a first hole to accommodate a glass-to-metal seal/terminal pin feedthrough and a second hole for electrolyte filling. The glass used is of a corrosion resistant type having up to about 50% by weight silicon such as CABAL 12, TA 23 or FUSITE 425 or FUSITE 435. The positive terminal pin feedthrough preferably comprises titanium although molybdenum, aluminum, nickel alloy, or stainless steel can also be used. The cell header comprises elements having compatibility with the other components of the electrochemical cell and is resistant to corrosion. The cathode lead is welded to the positive terminal pin in the glass-to-metal seal and the header is welded to the case containing the electrode stack. The cell is thereafter filled with the electrolyte solution comprising at least one of the carbonate additives described hereinabove and hermetically sealed such as by close-welding a stainless steel ball over the fill hole, but not limited thereto.
The above assembly describes a case-negative cell, which is the preferred construction of the exemplary cell of the present invention. As is well known to those skilled in the art, the exemplary electrochemical system of the present invention can also be constructed in a case-positive configuration.
The following examples describes the manner and process of an electrochemical cell according to the present invention, and they set forth the best mode contemplated by the inventors for carrying out the invention, but they are not to be construed as limiting.
An improved silver vanadium oxide cathode material was synthesized by a multistep thermal decomposition method including a final heating temperature of 500xc2x0 C. Specifically, a mixture of silver nitrate (AgNO3) and vanadium pentoxide (V2O5) in a 1:1 mole ratio was heated in the presence of air using the following protocol:
Step 1 Heated mixture to above its decomposition temperature, i.e., to about 300xc2x0 C. for about 16 hours,
Step 2 Cooled the resulting decomposed admixture to room temperature and ground thoroughly, and
Step 3 Heated decomposed admixture to about 500xc2x0 C. for about 12 to 48 hours.
During step 1 of the synthesis the thermal decomposition of AgNO3 occurs, and NOx gas is liberated until a temperature of about 300xc2x0 C. Grinding following the 300xc2x0 C. step to mix the sample after decomposition of the silver salt is critical in forming a homogeneous SVO material. The high temperature of step 3 produces a single phase material with low surface area. The combination of these steps produces a homogeneous xcex5-phase SVO cathode material having x=1.0 and y=5.5 in the general formula AgxV2Oy, as determined by differential thermal analysis (DTA) which has a surface area, as determined by BET surface area analysis, of about 0.2 m2/gram to about 0.80 m2/gram. The result of the DTA analysis is presented in FIG. 2, curve 20, where it is clear that a unitary phase product is produced.
It must be noted that the temperature given in step 1 of scheme 1 is appropriate for the use of silver nitrate in the reaction. As indicated above, silver nitrate decomposes below 300xc2x0 C. in the presence of vanadium oxide. Thus, the temperature of step 1 was specifically set above the decomposition point of the silver nitrate/vanadium oxide mixture. When using a different silver precursor, the temperature of step 1 needs to be changed to above the reaction temperature of the mixture of the silver precursor mixed with vanadium oxide.
As a comparison to SVO synthesized at a final temperature of 500xc2x0 C., the reaction of silver oxide (Ag2O) with vanadium oxide (V2O5) in a 1:2 mole ratio was performed according to the protocol set forth in Example I, even though silver oxide only reacts with vanadium oxide above 300xc2x0 C. The resulting product of this reaction was analyzed by DTA, as presented in FIG. 3, curve 30, where it is clear that a mixture of phases exist in the SVO product.
Another sample was prepared using Ag2O and V2O5 in a 1:2 mole ratio according to the protocol set forth in Example I, except that the temperature of step 1 was changed to 440xc2x0 C. This material was also thermally analyzed by DTA, and the results are presented in FIG. 4, curve 40. This material displays a single endotherm assigned to xcex5-phase SVO. Thus, the temperature of step 1 is important in preparing a homogeneous SVO material, and must be set above the reaction temperature of the silver precursor with vanadium oxide.
Silver vanadium oxide was prepared from a mixture of silver vanadate (AgVO3) and V2O5 in a 2:1 mole ratio. FIG. 5, curve 50, shows the DTA of the reaction product from these starting materials prepared according to the protocol set forth in Example I. Like SVO prepared from silver oxide, this sample displays multiple isotherms, indicating the presence of mixed phases, when a 300xc2x0 C. temperature is used in step 1.
FIG. 6, curve 60, shows the DTA of SVO prepared from a 2:1 mole ratio of AgVO3 and V2O5 using protocol 1 with a 450xc2x0 C. temperature used for the thermal treatment in step 1. This sample displays a single peak in the DTA curve.
The discharge performance of a low surface area, single phase mixed metal oxide cathode material in comparison to a prior art material was tested in hermetically-sealed electrochemical cells. Test cells according to the present invention used a single phase SVO prepared at a final heating temperature of about 500xc2x0 C. for 48 hours and having a surface area of about 0.6 m2/g. In comparison, control cells contained SVO manufactured at a final heating temperature of about 375xc2x0 C. for 48 hours and according to Liang et al. having a surface area of about 1.1 m2/g. The present invention and prior art test cells contained cathodes consisting of a mixture of 94% of SVO (by weight) along with 3% PTFE, 2% graphite, and 1% carbon black, pressed onto an expanded titanium current collector. A total of 7.92 grams of cathode mix was utilized in each cell. The cathodes were separated from an anode of lithium metal contacted to an expanded nickel current collector by a polypropylene separator. The cells were filled with 1M LiAsF6 PC/DME electrolyte.
Pulse testing of the Li/SVO cells was accomplished under long-term test conditions which mimic use of the cell in an implantable medical device such as a cardiac defibrillator. The cells were subjected to constant current pulses of 2.0 Amps for 10 seconds in duration with 15 seconds of rest between pulses. During discharge the current pulses were applied in groups of 4 every 106 days with a constant resistance background load of 33.2 kxcexa9 at 37xc2x0 C. Pulse testing consisted of pulses applied about every 106 days superimposed on a 33.2 kxcexa9 background load. This is referred to as 36-month or 3-year accelerated discharge data (ADD) testing.
FIG. 7 displays a graphic overlay of the prepulse voltage, pulse 1 minima and pulse 4 minima for each group of cells. The voltage delay plotted in FIG. 8 is equal to the pulse 1 final voltage minus pulse 1 minima voltage. All graphs plot the average of four cells in each group. In particular, curve 70 was constructed from the prepulse voltage of the cell group including the prior art SVO material having a surface area of about 1.1 m2/g and curve 72 was constructed from the present invention cell group including the SVO material having a surface area of about 0.6 m2/g. Curves 74 and 76 were constructed from the average P1 minima potentials of those cell groups and curve 78 and 80 were constructed from the average P4 minima voltages of the respective cell groups.
In FIG. 8, curve 82 was constructed from the average voltage delay of the prior art cell group including the 1.1 m2/g SVO material discharged under the 36-month ADD test and curve 84 was constructed from the average voltage delay of the prior art cell group including the 0.6 m2/g SVO material discharged under the same regime.
A second set of prior art and present invention cells were discharged under a 60-month ADD test. The 60-month ADD test is still in progress at the time of filing this application. Again, the prior art SVO material was prepared according to Liang et al. and had a surface area of about 1.1 m2/g produced at a final heating temperature of 375xc2x0 C. for 48 hours while the present invention SVO material was prepared at a final heating temperature of about 500xc2x0 C. for about 48 hours and had a surface area of about 0.5 m2/g. The testing utilized 2.0 Amp pulses, 10 seconds in duration applied 15 seconds apart in groups of four applied every 6 months with a 56.2 kxcexa9 load.
FIG. 9 dispalays a graphic overlay of the prepulse voltage, pulse 1 minima and pulse 4 minima for each group of cells. In particular, curve 90 was constructed for the prepulse voltage of the prior art cells having SVO material with a surface area of about 1.1 m2/g and curve 92 was constructed from the present invention cell group including the SVO material having a surface area of about 0.6 m2/g. Curves 94 and 96 were constructed from the average P1 minima potentials of those cell groups and curve 98 and 100 were constructed from the average P4 minima voltages of the respective cell groups.
In FIG. 8, 102 was constructed for the average voltage delay of the prior art cell group including the 1.1 m2/g SVO material discharged under the 60-month ADD test and curve 104 was constructed from the average voltage delay of the present invention cell group having the 0.6 m2/g SVO material discharged under the same regime.
As can be seen from the graphs in FIGS. 7 to 9, the cells with SVO prepared. at 500xc2x0 C. have much higher pulse voltages and less voltage delay than the cells containing SVO prepared at 375xc2x0 C., particularly during latter stages of cell discharge. As described in the SUMMARY OF THE INVENTION section, voltage delay is a phenomenon that typically occurs in Li/SVO cells that have been depleted of about 40% to about 70% of their capacity. The greater the separation between P1 minima voltage and P4 minima voltage, the greater the voltage delay.
Thus, according to the present invention, the use of SVO prepared from a multistep synthesis with a final temperature of 490xc2x0 C. to 520xc2x0 C. and having a surface area of about 0.2 m2/g to about 0.8 m2/g provides the benefits of increased pulse voltages and less voltage delay in comparison to SVO material prepared at a final heating temperature of 375xc2x0 C. according to the prior art. Lower pulse voltages caused by voltage delay, even if only temporary, are undesirable since they can cause circuit failure in device applications, and effectively result in shorter cell life.
FIG. 10 displays an overlay of Differential Thermal Analysis (DTA) curves for SVO materials prepared at 375xc2x0 C., 450xc2x0 C., 510xc2x0 C. and 540xc2x0 C. This experiment was conducted by heating the SVO samples at a rate of 20xc2x0 C./min. under an argon purge. The presence of peaks in the DTA curves indicates phase transitions that are characteristic for known phases of SVO. Thus, DTA is a good technique for detecting the presence of impurity phases in SVO cathode materials. As can be seen in FIG. 10, as the temperature of the SVO synthesis increased from 375xc2x0 C. to 510xc2x0 C., the amount of impurity materials, silver vanadate (AgVO3) and xcex3-phase decreases. From these curves it is clear that there is advantage to using the 500xc2x0 C. to 520xc2x0 C. temperature range for synthesis of SVO over the previously reported temperatures of 375xc2x0 C. or 450xc2x0 C. In addition to the lower surface area provided by the higher temperature synthesis, the present invention provides increased purity in terms of purer AgV2O5.5 in the product SVO material. These DTA curves also show that SVO prepared at 540xc2x0 C., above the preferred range of 500xc2x0 C. to 520xc2x0 C., contain an increased amount of silver vanadate impurity and a loss of the peak due to xcex5-phase SVO, the desired SVO material.
The desirable increase in pulse voltages and decrease in voltage delay for lithium cells containing SVO prepared with a final temperature of about 490xc2x0 C. to about 520xc2x0 C. are new and unexpected results which can be traced to the lower surface area of these materials. The relationship between long-term test results and surface area of the SVO material is a new finding, where lower surface SVO displays a significant advantage over the prior art material. In addition, the increase in usable cell capacity, and subsequent increase in battery life using this improved cathode material for long-term test is unexpected based on the published capacity data for 450xc2x0 C. SVO discharged under quick discharge conditions.
The previously discussed publication by R. A. Leising and E. S. Takeuchi, Chemistry of Materials, 5,738-742 (1993) discloses that the 375xc2x0 C. prepared SVO material gave slightly higher delivered capacity than the 450xc2x0 C. material and significantly higher capacity than the SVO material prepared at 540xc2x0 C.
Thus, the increase in pulse voltages and desirable decrease in voltage delay found for lithium cells containing silver vanadium oxide cathode active material prepared in a temperature range of about 490xc2x0 C. to about 520xc2x0 C. and activated with an electrolyte comprising 1M LiAsF6 dissolved in a 50:50 mixture, by volume, of PC and DME are new and unexpected results attributable to the present invention.
It is appreciated that various modifications to the present inventive concepts described herein may be apparent to those of ordinary skill in the art without disparting from the spirit and scope of the present invention as defined by the herein appended claims.

{'bibliographic_information': "{'document_kind': 'B1', 'document_number': '06566007', 'document_date': '20030520', 'publishing_country_or_organization': 'US', 'title_of_invention': 'Synthetic method for preparation of a low surface area, single phase silver vanadium oxide'}", 'source_file': './grant/2003/pg030520.xml', 'source_data': 'USPTO-Grant'}