Intermetallic negative electrodes for non-aqueous lithium cells and batteries

[0002] This application, pursuant to 37 C.F.R. 1.78(c), claims priority based on provisional application Ser. No. 60/247,404 filed on Nov. 10, 2000.

[0004] This invention relates to methods of operating intermetallic negative electrodes for non-aqueous lithium cells and batteries. More specifically, it relates to methods of operating modified compositions of copper-tin electrodes, Cu_6-xM_xSn₅, wherein x≦3 and in which M is one or more metals including silicon, and to methods using current collectors and grain growth inhibitors when used with such electrodes, and to controlled operating conditions for the lithium cells and batteries using such intermetallic electrodes. Preferred compositions useful in the inventive methods include Cu_6-xM_xSn₅electrodes in which the copper atoms are partially replaced by one or more transition metals and lithium in partial replacement M and Li or one or more of M including Li. Improved electrochemical performance with respect to delivered capacity and cycling stability of the lithium cells over those known in the art is obtained by controlling the structure of the lithiated Cu_6-xM_xSn₅electrodes and by controlling the voltage of the lithium cell such that the potential of the lithiated intermetallic negative electrode at the top of charge is less than 0.2 V but greater than 0 V vs. metallic lithium.

[0005] A significant problem in the field is that copper-tin electrodes, notably Cu₆Sn₅, lose capacity if cycled repeatedly to 0 V vs. metallic lithium. When cycled to 200 mV vs. lithium, the capacity retention is improved significantly, but at the expense of the delivered amount of capacity.

[0006] The invention relates to a method of using intermetallic negative electrodes based on copper-tin, Cu₆Sn₅, for non-aqueous electrochemical lithium cells and batteries. The invention relates more specifically to the use of modified electrode compositions, Cu_6-xM_xSn₅, wherein x≦3 and where M is one or more metals used in the inventive method, preferably a first row transition metal and lithium, that when cycled in an electrochemical cell the voltage of cell is controlled such that the potential of the lithiated intermetallic negative electrode at the top of charge is less than 0.2 V but greater than 0 V vs. metallic lithium. The Cu_6-xM_xSn₅electrodes optionally contain additional M metal (or metals) in the electrode either in finely divided, dispersed and intimately mixed form or as a substrate to act as current collector. The electrodes may also contain additional components to control porosity and current collection or to suppress grain growth in the electrode during electrochemical operation. Such modifications to the composition of copper-tin electrodes and to the regulation of the operating conditions of the cells improve the capacity and cycle life of lithium cells and batteries. The superior electrochemical performance is achieved by controlling the structure of the lithiated Cu_6-xM_xSn₅electrodes, either electronically by controlling the voltage of the lithium cell, or by limiting the installed capacity in the positive electrode.

[0007] The invention consists of certain novel features and a combination of parts hereinafter fully described, illustrated in the accompanying drawings, and particularly pointed out in the appended claims, it being understood that various changes in the details may be made without departing from the spirit, or sacrificing any of the advantages of the present invention.

[0008] FIGS. 1(a) and (b) depict a schematic idealized representation of a) Cu₆Sn₅with a NiAs-type structure and its transformation on reaction with lithium to b) Li₂CuSn with a lithiated zinc-blende-type structure, in which the CuSn component adopts the Zn and S atomic positions of the mineral zinc-blende, ZnS. The Cu atoms in the interstitial sites of the NiAs-type structure in a) have not been shown for clarity; these interstitial Cu atoms impart some Ni₂In-type structure to Cu₆Sn₅;

[0009] FIG. 2 shows in-situ X-ray diffraction data of a Cu₆Sn₅electrode in a Li/Cu₆Sn₅cell obtained at 2.8 V (initial open-circuit voltage), 0.8 V, 0.5 V, 0.4 V, 0.25 V, and 0.0 V during discharge, and at 0.3 V, 0.4 V, and 0.5 V during the subsequent charge;

[0010] FIG. 3 shows the X-ray diffraction pattern of a standard Cu₆Sn₅sample obtained with CuKα radiation at room temperature;

[0011] FIG. 4 shows the typical electrochemical profiles for the first five cycles of a Li/Cu₆Sn₅cell with the Cu₆Sn₅electrode laminated on a Ni substrate, cycled between 1.2 and 0 V;

[0012] FIG. 5 shows the typical electrochemical profiles for the first five cycles of a Li/Cu₅ZnSn₅cell with the Cu₅ZnSn₅electrode laminated on a Ni substrate, cycled between 1.2 and 0 V;

[0013] FIG. 6 shows the typical electrochemical profiles for the first five cycles of a Li/Cu₅NiSn₅cell with the Cu₅NiSn₅electrode laminated on a Ni substrate, cycled between 1.2 and 0 V;

[0014] FIG. 7 shows the typical electrochemical profiles for the first five cycles of a Li/Cu₅FeSn₅cell with the Cu₅FeSn₅electrode laminated on a Ni substrate, cycled between 1.2 and 0 V;

[0015] FIG. 8 shows the typical electrochemical profiles for the first five cycles of a Li/Cu₅MnSn₅cell with the Cu₅MnSn₅electrode laminated on a Ni substrate, cycled between 1.2 and 0.01 V;

[0016] FIG. 9 shows a collective plot of capacity vs. cycle number for Li/Cu₆Sn₅, Li/Cu₅ZnSn₅Li/Cu₅NiSn₅and Li/Cu₅FeSn₅cells (Ni substrates) cycled between 1.2 and 0 V;

[0017] FIG. 10 shows a collective plot of capacity vs. cycle number for Li/Cu₅FeSn₅cells cycled between 1.2 and 0 V (Ni substrate), and between 1.2 and 0.01 V and between 1.2 and 0.10 V (Cu substrate);

[0018] FIG. 11 shows a collective plot of capacity vs. cycle number for Li/Cu₅FeSn₅cells cycled between 1.2 and 0 V; between 1.2 and 0.01 V; between 1.2 and 0.05 V; and between 1.2 and 0.10 V (Ni substrate);

[0019] FIG. 12 shows a collective plot of capacity vs. cycle number for Li/Cu₅FeSn₅and Li/Cu₅MnSn₅cells cycled between 1.2 and 0.01 V (Ni substrate);

[0020] FIG. 13 shows a characteristic voltage profile of a Cu₆Sn₅/LiNi_0.8Co_0.2O₂cell cycled between 3.5 and 0.5 V;

[0021] FIG. 14 depicts a schematic representation of an electrochemical cell; and

[0022] FIG. 15 is a schematic representation of a microprocessor controlled circuit, in which M is the microprocessor.

[0023] The present invention relates to modified copper-tin electrodes of general formula Cu_6-xM_xSn₅that are of interest as the negative electrodes for non-aqueous electrochemical lithium cells and batteries. State-of-the-art lithium-ion cells use a lithiated graphite negative electrode, coupled to a lithium transition metal oxide positive electrode, commonly LiCoO₂, via an electrolyte that consists of a lithium salt such as LiPF₆, dissolved in an organic solvent such as a 50:50 mix of dimethyl carbonate (DMC) and diethyl carbonate (DEC). The electrochemical discharge and charge reaction occurs by a process by which lithium ions are shuttled between the two host electrodes with concomitant reduction and oxidation taking place at the electrodes. The ideal reaction is represented:

[0024] Li_xC+Li_1-xCoO₂⇄C+LiCoO₂

[0025] The lithiated graphite electrode operates close to the potential of metallic lithium, which raises problems with respect to the reactivity of this electrode with flammable organic-based electrolytes and the consequent safety of lithium-ion cells. There are therefore important reasons to develop safer negative electrodes for such cells and batteries, and particularly electrodes that operate a few hundred millivolts above the potential of metallic lithium.

[0026] Copper-tin, Cu₆Sn₅, is one such electrode that holds promise for replacing graphite as the negative electrode for lithium-ion cells. It has already been discovered that Cu₆Sn₅reacts with lithium essentially in two steps:

[0027] Reaction 1: x Li+Cu₆Sn₅⇄Li_xCu₆Sn₅,

[0028] where x is approximately 9, and

[0029] Reaction 2: (22−x)Li+Li_xCu₆Sn₅⇄5 Li_4.4Sn+6 Cu

[0030] During Reaction 1, the nickel-arsenide (NiAs) related structure of a Cu₆Sn₅electrode transforms in an electrochemical cell at approximately 0.4 V vs. metallic lithium to a structure that closely resembles that of Li₂CuSn. Ideally, this transformation is represented by a reaction in which a small amount of Cu extrusion is necessary:

[0031] Reaction 1a: 10 Li+Cu₆Sn₅⇄5 Li₂CuSn+Cu

[0032] in which one-sixth of the copper is extruded from the Cu₆Sn₅structure. Ideal Li₂CuSn has a lithiated zinc-blende type structure with cubic symmetry, in which the CuSn component adopts the crystallographic configuration of zinc-blende (ZnS); the lithium atoms occupy two crystallographically independent sites within the zinc-blende framework. In this transformation, which may be regarded as topotactic, despite an approximate 50% increase in crystallographic volume, 50% of the Sn atoms are displaced into neighboring interstitial sites of the Cu₆Sn₅structure to create the [CuSn] zinc-blende framework as shown in FIG. 1. Thus there is a close structural relationship between the NiAs-related structure of Cu₆Sn₅and the CuSn framework of the zinc-blende framework that facilitates the transformation of the one structure type to the other.

[0033] When the reaction goes to completion, i.e., to 0 V vs. metallic lithium, as shown by the ideal Reaction 2 above, all the copper is extruded from the Li₂CuSn structure; the final lithiated tin product is Li_4.4Sn that, like Li₂CuSn, has cubic symmetry. Note that in practice, however, under the dynamic, non-equilibrium conditions of an operating cell, there may be a small amount residual copper in a Li_2+xCu_1-xSn component of the electrode at 0 V vs. metallic lithium, for example, when x=0.95. The theoretical electrode capacity for the complete lithiation of Cu₆Sn₅to Li_4.4Sn, i.e., Reactions 1 and 2 is 605 mAh/g. Reaction 2 is only partially reversible, as evident from a steady capacity loss that occurs on long term cycling. The prior art has shown that by restricting the reaction to the topotactic process in Reaction 1a, when the lower voltage of a Li/Cu₆Sn₅cell is restricted to 0.2 V vs. metallic lithium, a great improvement in cycling stability can be achieved, but at the expense of considerable capacity. Typically a rechargeable capacity of approximately 200 mAh/g can be achieved, which is only 33% of the full theoretical electrode capacity.

[0034] Without being bound by theory, the applicants believe that the capacity loss, when Cu₆Sn₅electrodes are reacted with lithium to 0 V vs. metallic lithium, can be attributed in part to the formation of the end member of the binary Li_xSn system, i.e., Li_4.4Sn (alternatively Li₂₂Sn₅) after all the copper has been extruded from the Li₂CuSn structure. In this respect, it is to be noted that the Li_xSn has several binary phases that have the compositions, in order of increasing lithium content, Li₂Sn₅, LiSn, Li₇Sn₃, Li₅Sn₂, Li₁₃Sn₅, Li₇Sn₂and Li₂₂Sn₅. The Li:Sn ratios in each of these phases is thus 0.4:1, 1:1; 2.33:1; 2.5:1; 2.6:1; 3.5:1; and 4.4:1, respectively. Each of these phases has a distinct crystallographic structure. As the lithium content increases, so does the unit cell volume per Sn atom. On lithiating metallic Sn to Li_4.4Sn, the crystallographic volume per Sn atom increases by a factor of approximately 3.5, which is far too severe for a metallic Sn electrode to be cycled without appreciable capacity loss.

[0035] In the lithium-copper-tin system, it is believed that the volumetric changes to the unit cell can be controlled if the lithium content per Cu₆Sn₅unit is controlled, ideally to 3 Li per Sn atom. For example, in an ideal case, it is believed that the Cu₆Sn₅electrode may operate by the following reaction pathway:

[0036] Reaction 1a: 10 Li+Cu₆Sn₅⇄5 Li₂CuSn+Cu

[0037] Reaction 2a: x Li+Li₂CuSn⇄Li_2+xCu_1-xSn+x Cu

[0038] For x=1, Reaction 2a becomes

[0039] Li+Li₂CuSn⇄“Li₃Sn”+Cu

[0040] in which the lithiated product “Li₃Sn” would have a structure resembling the well known Li₃Sb-type structure, in which the Sb atoms constitute a face-centered-cubic array of atoms. Further reaction, of lithium with “Li₃Sn” results in the formation of Li_4.4Sn, which also has a cubic structure according to the reaction

[0041] Reaction 3a: 1.4 Li+“Li₃Sn”→Li_4.4Sn

[0042] that occurs possibly via a Li₇Sn₂(Li_3.5Sn) intermediate composition.

[0043] The close structural relationship between Cu₆Sn₅and the CuSn zinc-blende framework of Li₂CuSn has already been stressed above. This close structural relationship is believed to contribute to the good reversibility of Reaction 1a. In Reaction 2a, the electrochemical reaction occurs by lithium insertion into the face-centered-cubic Sn array and simultaneous extrusion of metallic copper from the structure to yield “Li₃Sn”, in which the inserted Li atoms simply occupy the copper positions in the Li₂CuSn structure. With this arrangement, therefore, an idealized Li₃Sn product can be regarded as being isostructural with Li₂CuSn and with the known cubic Li₃Sb structure. In practice, however, it is not yet clear if the ideal Li₃Sn structure is produced, or whether the transformation to the Li_4.4Sn phase occurs slightly earlier during the reaction. However, it is believed that the strong structural relationship that exists between Li₂CuSn and Li_2+xCu_1-xSn phases with the retention of a face-centered cubic Sn array is an important factor that contributes to the good reversibility of the Li/Li₂CuSn and indeed Li/Cu₆Sn₅cells. The theoretical capacity for combined Reactions 1a and 2a, i.e., for the reaction leading to 3 Li per Sn atom, or 15 Li per Cu₆Sn₅unit is 412 mAh/g. This capacity value is 50% more than the theoretical capacity of the electrode when the Cu₆Sn₅electrode is reacted with lithium to form Li₂CuSn (275 mAh/g). Reaction 1a occurs at approximately 0.4 V against metallic lithium, whereas Reaction 2a occurs below 0.4 V, but above 0 V against metallic lithium. Reactions that occur after the extrusion of all the copper from Li₂CuSn lead to binary Li_xSn phases, such as Li_4.4Sn. It is further believed that the formation of these binary phases in which the ideal face-centered-cubic array of Sn atoms no longer exists plays a significant role in suppressing the reconstruction of this array on reversing the direction of current and hence the rechargeability of the lithium cells. Thus, it is believed that in order to optimize the rechargeability of cells with Cu₆Sn₅negative electrodes, such as Cu₆Sn₅/LlCoO₂cells, the voltage of the lithiated Cu₆Sn₅electrode should be controlled during charge to be less than 0.2 V and greater than 0 V vs. metallic lithium.

[0044] Evidence for such a reaction mechanism has been gathered from an in-situ X-ray diffraction study of Li/Cu₆Sn₅cells employing a Ni substrate for the Cu₆Sn₅electrode. The results of this in-situ X-ray diffraction study are shown in FIG. 2. This figure shows the X-ray diffraction pattern of the Cu₆Sn₅electrode when the cell was in its original state with an open circuit potential of 2.8 V, and thereafter at various states of discharge and charge vs. a metallic Li electrode, namely during discharge at 0.8 V, 0.5 V, 0.4 V, 0.25 V, 0.0 V, and then on the subsequent charge at 0.3 V, 0.4 V and 0.5 V. In the X-ray diffraction patterns at 2.8 V, 0.8 V and 0.5 V during the initial discharge, the Cu₆Sn₅peaks are clearly visible, for example, at approximately 43 ° 2θ. At 0.4 V, the peaks due to the Li₂CuSn peaks appear, for example, at approximately 40.1 ° 2θ. At 0.0 V the broad peak at approximately 38.2 ° 2θ can be attributed to Li_4.4Sn. Of particular significance, however, is that on discharge between 0.4 and 0.0 V the Li₂CuSn peak at 40.1 ° 2θ maintains its intensity but shifts gradually toward 38.2 ° 2θ, and on the subsequent charge between 0.0 and 0.5 V, the peak shifts gradually back from 38.2 ° 2θ to 40.1 ° 2θ. Such X-ray diffraction data are strongly suggestive of a solid solution system Li_2+xCu_1-xSn in which the Sn array remains intact for 0<x<1, i.e., to a composition approaching Li₃Sn. In practice, it is believed that a small amount of copper may be necessary to stabilize the face-centered-cubic Sn array. Of particular significance also is that during this complete reaction from Li₂CuSn (with a lattice parameter, a≈6.28 Å) to a “Li₃Sn” structure (with a <6.6 Å) in which a face-centered-cubic array of Sn atoms is maintained, the volume expansion is less than 16% per Sn atom. By contrast, the transformation of Li₂CuSn to Li_4.4Sn necessitates the breaking of Sn—Sn bonds and the face-centered-cubic array; in this instance, the volume expansion per tin atom is significantly larger, approximately 56.7%. The large increase in unit cell volume is accounted for by a large cubic supercell in the Li_4.4Sn structure, with a lattice parameter of a≈19.8 Å. Thus, there is a significant advantage in cycling Cu₆Sn₅electrodes to compositions before the Li_4.4Sn structure is reached.

[0045] This invention relates to compositional changes to Cu₆Sn₅electrodes and to operating voltage conditions to improve the capacity and cycling stability of such electrodes in non-aqueous electrochemical cells.

[0046] In the first embodiment of the invention, the Cu₆Sn₅electrode is partially substituted by one or more other metals, M including Si, in Cu_6-xM_xSn₅preferably one or more transition metals, and more preferably one or more first row transition metals. In particular, the M atoms can be selected those first-row transition metals with lower atomic number than copper, such as Zn, Ni, Co, Fe, Mn, Cr, V, Ti and Sc to act as a sink for electrons associated with the incoming lithium atoms. The substitution of Cu atoms by M atoms is at most 50% (i.e., x_max=3), and preferably between 0.1 and 16.6% (i.e., x≦1). In a second embodiment of the invention, the non-aqueous lithium cells containing such intermetallic electrodes are operated such that the intermetallic electrodes are reacted electrochemically between 1.5 V and above 0 V with respect to metallic lithium, preferably between 1.5 and 0.01 volts, more preferably between 1.2 and 0.01 volts and most preferably between 1.2 and 0.1 volts.

[0047] In a third embodiment of the invention, the M atoms of the Cu_6-xM_xSn₅electrode can include Li atoms to counter the irreversible capacity loss that is encountered during the first cycle of Li/Cu_6-xM_xSn₅cells. This irreversible capacity loss is believed to be associated first, with a passivating layer containing lithium on the surface of the lithiated Cu_6-xM_xSn₅electrode and second, with the inability of all the lithium to be extracted from the lithiated Cu_6-xM_xSn₅electrode on reversing the current. It is believed that the irreversible capacity loss can be countered if the initial Cu_6-xM_xSn₅electrode contains at least a small amount of lithium, either within the Cu_6-xM_xSn₅structure, or outside it, prior to the assembly of the Li/Cu_6-xM_xSn₅cell.

[0048] The structures of intermetallic compounds are very often not represented by ideal structural configurations. Rather, they may be represented by disordered or partially disordered structures. The Cu_6-xM_xSn₅electrodes and lithiated electrode structures of this invention, notably those having the NiAs, Ni₂In and lithiated zinc-blende-type structures, should therefore not be restricted to ideal ordered structural configurations. For example, in a lithiated Cu_6-xM_xSn₅zinc-blende-type structure the Li, Cu and M atoms may be randomly disordered, or at least partially disordered over three lithium sites in a Li₃Sb-type structure in which the Sn atoms occupy the face-centered-cubic Sb sites. Therefore, in a fourth embodiment, the invention includes randomly disordered and partially disordered Cu_6-xM_xSn₅and lithiated Cu_6-xM_xSn₅electrode structures.

[0049] Intermetallic compounds are often non-stoichiometric compounds. In this respect, the structure of the intermetallic Cu₆Sn₅compound can be regarded as having a non-stoichiometric nickel-arsenide (NiAs) type structure in which one-sixth of the copper atoms partially occupy the interstitial trigonal bipyramidal sites of the CuSn (Cu₅Sn₅) NiAs-type framework. In this instance, Cu₆Sn₅can be designated by the non-stoichiometric formula Cu_1.2Sn. On the other hand, occupation of all the trigonal bipyramidal interstitial sites would yield a Ni₂In-type structure; from this viewpoint, the Cu₆Sn₅structure can be regarded as having a defect Ni₂In-type structure. It is possible, therefore, that small compositional and structural variations may be possible in the Cu_6-xM_xSn₅electrodes of the invention. The invention includes such variations in the composition of the Cu_6-xM_xSn₅electrode, specifically in the ratio of (Cu+M) atoms to Sn atoms, preferably such that the (Cu+M):Sn ratio falls within the range 1.5:1 to 1.0:1 thus allowing for non-stoichiometric Cu_6-xM_xSn₅electrodes that are either slightly (Cu+M) rich or (Cu+M) deficient with respect to the number of Sn atoms.

[0050] When lithium cells are operated such that the intermetallic Cu_6-xM_xSn₅electrodes are operated below approximately 0.2 volts with respect to metallic lithium, copper atoms and M atoms are extruded from a Sn array of atoms. It is believed that the addition of surplus Cu and M in finely-divided, dispersed and intimately mixed form in the initial electrode serves to enhance the reversibility of the reaction in the event that some of the extruded Cu and M become electronically disconnected from the electrode. In a fifth embodiment of the invention, therefore, the intermetallic electrodes may be fabricated prior to use to contain an additional amount of Cu and M in finely-divided, dispersed and intimately mixed form, up to about 10% by weight. In a sixth embodiment of the invention, the current collecting substrate can be optionally comprised of a metallic foil of the M metal to provide chemical compatibility between the substrate and the extruded M atoms of the intermetallic electrode.

[0051] In order to prevent or suppress electrochemical sintering and grain growth of the intermetallic component, the lithiated intermetallic component or the extruded metal component of the electrode during electrochemical cycling, a grain-growth inhibiting component can be added to the electrode in finely divided powder form with an average particle size, for example, of less than about 5 microns and, for example, less than 15% by weight. The grain-growth inhibitor is preferentially carbon, which may also act to provide additional capacity to the cell, and to provide porosity to the electrode to allow access of the electrolyte to the individual intermetallic particles. The carbon additive is preferentially graphite.

[0052] When the inventive electrodes are used as a negative electrode in a non-aqueous lithium electrochemical cell, the positive electrode can be selected from any suitable and compatible electrode material such that the electrochemical couple yields a cell potential of greater than 1 V. Preferred positive electrode materials are those known in the art, particularly those derived from lithium-metal-oxides with layered or spinel-type structures, such as LiCoO₂, LiNiO₂, LiMnO₂, LiMn₂O₄, LiFePO₄or derivatives thereof, such as substituted or modified compounds, for example, LiNi_0.8Co_0.2O₂, LiMn_0.9Co_0.1O₂, LiMn_0.5Ni_0.5O₂, Li_1.05Mn_1.95O₄, LiCoPO₄and LiMn_0.4Fe_0.6PO₄.

[0053] We have found that structural control of lithiated Cu_6-xM_xSn₅electrodes provides electrochemical cells with enhanced capacity and cycle life to those known in the art, and that structural control can be achieved by regulating the voltage of the cells such that the potential of the lithiated intermetallic negative electrode at the top of charge is less than 0.2 V but greater than 0 V vs. metallic lithium. Voltage control of the cells, and therefore structural control of the lithiated Cu_6-xM_xSn₅electrodes can be imposed either electronically, for example, by microprocessor devices, or it can be imposed chemically, for example, by limiting the installed capacity of the positive electrode, such that the potential of the lithiated intermetallic negative electrode is always greater than 0 V vs. metallic lithium. For example, in a Cu₆Sn₅/electrolyte/LiCoO₂cell, an amount of the positive LiCoO₂electrode can be installed in the cell such that the composition of the lithiated Cu_6-xM_xSn₅electrode at the top of charge never exceeds 3 Li per Sn. The following examples describe the principles of the invention as contemplated by the inventors, but they are not to be construed as limiting examples.

[0054] A standard Cu₆Sn₅sample (control) was synthesized by reacting metallic tin and metallic copper in stoichiometric amounts at 400° C. under argon for 12 hours. The sample was ground by mechanical milling to an average particle size of less than 10 microns. The X-ray diffraction data, collected on a Siemens D5000 powder diffractometer with CuKα radiation showed that the Cu₆Sn₅product was an essentially single-phase product as shown in FIG. 3.

[0055] Substituted Cu_6-xM_xSn₅compounds with M=Zn, Ni, Fe, and Mn were synthesized in the same fashion as the Cu₆Sn₅sample in example 1 with the required amounts of Cu, M, and Sn metals for x=1. The samples were ground by mechanical milling to an average particle size of less than 10 microns. The X-ray diffraction data showed that all the products were essentially single-phase compounds isostructural with Cu₆Sn₅.

[0056] The intermetallic Cu₆Sn₅and Cu_6-xM_xSn₅materials were evaluated as electrodes in coin cells (size 1225) 12 mm diameter and 2.5 mm high against a counter lithium electrode. The cells had the configuration: Li/1M LiPF₆in ethylene carbonate, diethyl carbonate (50:50)/intermetallic electrode, in which the intermetallic electrode consisted of Cu₆Sn₅, Cu₅ZnSn₅, Cu₅NiSn₅, Cu₅FeSn₅and Cu₅MnSn₅. For the intermetallic electrodes, blends were made containing approximately 6 mg of the intermetallic compound, i.e., approximately 81% by weight of the electrode, intimately mixed with approximately 10% by weight of Kynar 2801 binder and approximately 9% by weight of carbon (XC-72) in tetrahydrofuran (THF). The electrode blends were laminated onto either thin copper or nickel foil substrate current collectors. Metallic lithium foil was used as the counter electrode. Li/Cu₆Sn₅and Li/Cu_6-xM_xSn₅cells were discharged and charged at constant current (typically 0.1 mA) within the voltage ranges 1.2 to 0 V, 1.2 to 0.01 V, 1.2 to 0.05 V, and 1.2 to 0.10 V.

[0057] Typical electrochemical data for Li/Cu₆Sn₅and Li/Cu_6-xM_xSn₅cells are provided in various plots, as shown in FIG. 4: a Li/Cu₆Sn₅cell, nickel substrate, voltage limits 1.2 to 0 V; FIG. 5: a Li/Cu₅ZnSn₅cell, nickel substrate, voltage limits 1.2 to 0 V; FIG. 6: a Li/Cu₅NiSn₅cell, nickel substrate, voltage limits 1.2 to 0 V; FIG. 7: a Li/Cu₅FeSn₅cell, nickel substrate, voltage limits 1.2 to 0 V; FIG. 8: a Li/Cu₅MnSn₅cell, nickel substrate, voltage limits 1.2 to 0.01 V; FIG. 9: a collective plot of capacity vs. cycle number for Li/Cu₆Sn₅, Li/Cu₅ZnSn₅Li/Cu₅NiSn₅and Li/Cu₅FeSn₅cells (Ni substrates) cycled between 1.2 and 0 V; FIG. 10: a collective plot of capacity vs. cycle number for Li/Cu₅FeSn₅cells cycled between 1.2 and 0 V (Ni substrate), and between 1.2 and 0.01 V and between 1.2 and 0.10 V (Cu substrate); FIG. 11: a collective plot of capacity vs. cycle number for Li/Cu₅FeSn₅cells cycled between 1.2 and 0 V; between 1.2 and 0.01 V; between 1.2 and 0.05 V; and between 1.2 and 0.10 V (Ni substrate); FIG. 12: a collective plot of capacity vs. cycle number for Li/Cu₅FeSn₅and Li/Cu₅MnSn₅cells cycled between 1.2 and 0.01 V (Ni substrate).

[0058] These data, particularly the capacity vs. cycle no. plots in FIGS. 9, 10, 11 and 12 show that standard Li/Cu₆Sn₅cells lose capacity rapidly when cycled between 1.2 and 0 V vs. Li, as do Li/Cu_6-xM_xSn₅cells where M=Zn, Ni, and Fe. By contrast, when Li/Cu_6-xM_xSn₅cells are cycled between 1.2 and either 0.1, 0.05, or 0.01 V vs. Li, the cycling stability is markedly improved (FIGS. 10, 11, and 12), particularly when M=Fe or Mn. Of significance is that the greatest stability is achieved when cells are cycled with Cu_6-xM_xSn₅electrode capacities less than 400 mAh/g, i.e., corresponding to the reaction with less than 3 Li per Sn.

[0059] For the purpose of demonstrating the utility of Cu_6-xM_xSn₅as a negative electrode in an electrochemical cell containing a lithium-transition-metal oxide positive electrode, a Cu₆Sn₅(x=0) electrode was coupled against a LiNi_0.8Co_0.2O₂electrode. The cell had the configuration: Cu₆Sn₅/1M LiPF₆in ethylene carbonate, diethyl carbonate (50:50)/LiNi_0.8Co_0.2O₂, in which the installed capacity of the cathode was limited to prevent the Cu₆Sn₅electrode from being fully lithiated to a composition Li₂₂Cu₆Sn₅(i.e., 5Li_4.4Sn+6Cu), thereby controlling the potential of the fully charged Cu₆Sn₅electrode to be greater than 0 V vs. metallic lithium; in this respect, the masses of the Cu₆Sn₅and LiNi_0.8Co_0.2O₂electrodes were calculated to be such that complete extraction of lithium from the LiNi_0.8Co_0.2O₂electrode would yield a Li:Sn ratio of 2:1 in the charged, lithiated Cu₆Sn₅electrode. For the Cu₆Sn₅electrode, a blend was made containing approximately 12 mg of Cu₆Sn₅, i.e., approximately 84% by weight of the electrode, intimately mixed with approximately 8% by weight of Kynar 2801 binder and approximately 8% by weight of carbon (4% acetylene black, 4% SFG-6) in N-methylpyrrolidone (NMP). For the LiNi_0.8Co_0.2O₂electrode, a blend was made containing approximately 18 mg of LiNi_0.8Co_0.2O₂i.e., approximately 84% by weight of the electrode, intimately mixed with approximately 8% by weight of Kynar 2801 binder and approximately 8% by weight of carbon (4% acetylene black, 4% SFG-6) in NMP. The Cu₆Sn₅and LiNi_0.8Co_0.2O₂electrode blends were laminated onto thin copper and aluminum foil substrate current collectors, respectively. The cell was charged and discharged at constant current (typically 0.1 mA) within the voltage range 3.5 to 0.5 V, as shown in FIG. 13.

[0060] Intermetallic Cu_6-xM_xSn₅electrodes, where M is one or more metal elements, preferably a transition metal element or elements have been discovered to impart excellent electrochemical behavior in lithium cells with respect to delivered capacity and cycling stability when the cells are cycled between voltage limits such that the lower voltage limit of the Cu_6-xM_xSn₅electrode is kept above 0 V vs. metallic lithium. The new electrodes provide a significant improvement over the delivered capacity and cycling capability of state-of-the-art copper-tin electrodes.

[0061] As previously stated, the invention relates to an intermetallic negative electrode for a non-aqueous electrochemical lithium cell 10, as seen in FIG. 14, having a negative electrode 12 separated from a positive electrode 16 by an electrolyte 14, all contained in an insulating housing 18 with suitable terminals (not shown) being provided in electronic contact with the negative electrode 12 and the positive electrode 16. Binders and other materials normally associated with both the electrolyte and the negative and positive electrodes are well known in the art and are not described herein, but are included as is understood by those of ordinary skill in this art. A schematic illustration of one example of a cell circuit that contains a microprocessor, M, to control the potential of the cell during charge is shown in FIG. 15.

[0062] We believe that the invention includes an intermetallic negative electrode for a non-aqueous electrochemical lithium cell, the negative electrode being defined by the general formula Cu_6-xM_xSn₅in which 0<x≦3, and in which M is one or more metals including silicon, such that when cycled in the electrochemical cell with a non-aqueous electrolyte and a positive electrode, the voltage of the electrochemical cell is controlled such that the potential of the lithiated intermetallic negative electrode at the top of charge is less than 0.2 V but greater than 0 V vs. metallic lithium.

[0063] While there has been disclosed what is considered to be the preferred embodiment of the present invention, it is understood that various changes in the details may be made without departing from the spirit, or sacrificing any of the advantages of the present invention.