Patent Description:
Lithium-ion (Li-ion) batteries are a commonly used type of rechargeable battery with a global market predicted to grow to $200bn by <NUM>. Li-ion batteries are the technology of choice for electric vehicles that have multiple demands across technical performance to environmental impact, providing a viable pathway for a green automotive industry.

A typical lithium-ion battery is composed of multiple cells connected in series or in parallel. Each individual cell is usually composed of an anode (negative polarity electrode) and a cathode (positive polarity electrode), separated by a porous, electrically insulating membrane (called a separator), immersed into a liquid (called an electrolyte) enabling lithium ions transport.

In most systems, the electrodes are composed of an active electrode material - meaning that it is able to chemically react with lithium ions to store and release them reversibly in a controlled manner - mixed if necessary with an electrically conductive additive (such as carbon) and a polymeric binder. A slurry of these components is coated as a thin film on a current collector (typically a thin foil of copper or aluminium), thus forming the electrode upon drying.

In the known Li-ion battery technology, the safety limitations of graphite anodes upon battery charging is a serious impediment to its application in high-power electronics, automotive and industry. Among a wide range of potential alternatives proposed recently, lithium titanate (LTO) and mixed niobium oxides are the main contenders to replace graphite as the active material of choice for high power, fast-charge applications.

Batteries relying on a graphitic anode are fundamentally limited in terms of charging rate. Under nominal conditions, lithium ions are inserted into the anode active material upon charging. When charging rate increases, typical graphite voltage profiles are such that there is a high risk that overpotentials lead to the potential of sites on the anode to become < <NUM> V vs. Li/Li+, which leads to a phenomenon called lithium dendrite electroplating, whereby lithium ions instead deposit at the surface of the graphite electrode as lithium metal. This leads to irreversible loss of active lithium and hence rapid capacity fade of the cell. In some cases, these dendritic deposits can grow to such large sizes that they pierce the battery separator and lead to a short-circuit of the cell. This can trigger a catastrophic failure of the cell leading to a fire or an explosion. Accordingly, the fastest-charging batteries having graphitic anodes are limited to charging rates of <NUM>-<NUM> C, but often much less.

Lithium titanate (LTO) anodes do not suffer from dendrite electroplating at high charging rate thanks to their high potential (<NUM> V vs. Li/Li+), and have excellent cycle life as they do not suffer from significant volume expansion of the active material upon intercalation of Li ions due to their accommodating 3D crystal structure. LTO cells are typically regarded as high safety cells for these two reasons. However, LTO is a relatively poor electronic and ionic conductor, which leads to limited capacity retention at high rate and resultant power performance, unless the material is nanosized to increase specific surface area, and carbon-coated to increase electronic conductivity. This particle-level material engineering increases the porosity and specific surface area of the active material, and results in a significantly lower achievable packing density in an electrode. This is significant because it leads to low density electrodes and a higher fraction of electrochemically inactive material (e.g. binder, carbon additive), resulting in much lower gravimetric and volumetric energy densities.

A key measure of anode performance is the electrode volumetric capacity (mAh/cm<NUM>), that is, the amount of electric charges (that is lithium ions) that can be stored per unit volume of the anode. This is an important factor to determine the overall battery energy density on a volumetric basis (Wh/L) when combined with the cathode and appropriate cell design parameters. Electrode volumetric capacity can be approximated as the product of electrode density (g/cm<NUM>), active material specific capacity (mAh/g), and fraction of active material in the electrode. LTO anodes typically have relatively low specific capacities (c. <NUM> mAh/g, to be compared with c. <NUM> mAh/g for graphite) which, combined with their low electrode densities (typically <<NUM>/cm<NUM>) and low active material fractions (<<NUM>%) discussed above, lead to very low volumetric capacities (<<NUM> mAh/cm<NUM>) and therefore low battery energy density and high $/kWh cost in various applications. As a result, LTO batteries/cells are generally limited to specific niche applications, despite their long cycle life, fast-charging capability, and high safety.

Mixed niobium oxides have been known in academic literature for some time. Recently, some mixed niobium oxides have been of interest for use in Li-ion cells. For example, <NPL> and <NPL> disclose Zn<NUM>Nb<NUM>O<NUM> and Cu<NUM>Nb<NUM>O<NUM> as possible active electrode materials. These papers rely on complex particle-level engineering to purportedly achieve good properties, e.g. attempting to control particle porosity and morphology. <CIT> and <CIT> disclose various substituted and/or oxygen-deficient mixed niobium oxides which were found to have good properties for use as active electrode materials. However, there remains a need to identify further mixed niobium oxides with good properties for use as active electrode materials, in particular with good properties for use in Li-ion cells intended for high-power/fast-charging applications. Identifying such materials e.g. without the need for extensive particle-level engineering and/or without coatings is an important step to low-cost battery materials for mass market uptakes.

In a first aspect, the invention provides an electrode comprising a mixed niobium oxide as an active electrode material, wherein the mixed niobium oxide has the formula MIx-uMy(x/(<NUM>-y))MVzNb<NUM>-(x/(<NUM>-y))-zO<NUM>-u/<NUM> as defined in the claims.

The mixed niobium oxide may also have the formula BaMvzNb<NUM>-a-zO<NUM>-a as defined in the claims.

The mixed niobium oxide may also have the formula MbNb<NUM>-bO<NUM>-<NUM>. 5b+bc as defined in the claims.

The inventors have found that electrodes according to the first aspect retain a surprisingly high capacity even when delithiated at high rates of e.g. 5C and 10C, as shown by the present examples. These are important results in demonstrating the advantages of the mixed niobium oxides of the invention for use in high-power batteries designed for fast charge/discharge.

In a second aspect, the invention provides a metal-ion battery comprising a mixed niobium oxide as an active electrode material, wherein the mixed niobium oxide is as defined in the first aspect. Optionally the metal-ion battery is a lithium-ion battery or a sodium-ion battery, preferably a lithium-ion battery.

In a third aspect, the invention provides use of a mixed niobium oxide is as defined in the first aspect as an active electrode material in a metal-ion battery. Optionally the metal-ion battery is a lithium-ion battery or a sodium-ion battery, preferably a lithium-ion battery.

In a fourth aspect, the invention provides a method of making an electrode, comprising providing a mixed niobium oxide as defined in the first aspect; and depositing the mixed niobium oxide onto a current collector, thereby forming the electrode.

The principles of the invention will now be discussed with reference to the accompanying figures.

The term "mixed niobium oxide" refers to an oxide comprising niobium and at least one other cation. mixed niobium oxides have a high redox voltage vs. Lithium ><NUM>. 8V, enabling safe and long lifetime operation, crucial for fast charging battery cells. Moreover, niobium cations can have two redox reactions per atom, resulting in higher theoretical capacities than, for example, LTO.

The mixed niobium oxide may have the formula MIx-uMy(x/(<NUM>-y))MVzNb<NUM>-(x/(<NUM>-y))-zO<NUM>-u/<NUM>, wherein:.

The mixed niobium oxide may also have the formula BaMvzNb<NUM>-a-zO<NUM>-a, wherein
MV is a cation having an average oxidation state of <NUM>, wherein MV is selected from Mn, Fe, Al, Ga, Y, In, La, Yb, Cu, Zn, Mg, Ni, Co, Ca, Ce, Zr, Ti, Sn, Ge, Si, V, P, Ta, W, Mo, Cr, and mixtures thereof; <MAT> <MAT>.

The mixed niobium oxide may also have the formula MbNb<NUM>-bO<NUM>-<NUM>. 5b+bc, wherein M is a cation selected from P, B, W, Mo, V, Ti, Si, and mixtures thereof;
c is half of the average oxidation state of M; <MAT> and <MAT>.

The mixed niobium oxides having the formulas defined herein are unified because they may adopt a crystal structure which is believed to contribute towards their advantageous properties for use as active electrode materials. In particular, the mixed niobium oxides may adopt a crystal structure having a Wadsley-Roth crystal structure comprising <NUM>×<NUM> octahedral blocks. Wadsley-Roth crystal structures are considered to be a crystallographic off-stoichiometry of the MO<NUM> (ReO<NUM>) crystal structure containing crystallographic shear, with simplified formula of MO<NUM>-x. As a result, these structures typically contain [MO<NUM>] octahedral subunits in their crystal structure. In the <NUM>×<NUM> octahedral block structure each block is connected through edge-sharing octahedra only. This structure was reported in <NUM> as having a monoclinic unit cell (a = <NUM>Å, b = <NUM>Å, c = <NUM>Å, β = <NUM>°, space group = C2/m). This and related structures have been reported in historic academic literature but no electrochemical lithiation or de-lithiation data has been provided (<NPL>; <NPL>; <NPL>; <NPL>; <NPL>; <NPL>). It is believed that the large block size is advantageous for rapid insertion and removal of lithium as compared to other Wadsley-Roth structures of smaller octahedral block sizes, with potentially higher stability than those with larger octahedral block sizes.

The polymorph of niobium oxide N-Nb<NUM>O<NUM> adopts a Wadsley-Roth crystal structure comprising <NUM>×<NUM> octahedral blocks. Accordingly, the crystal structure of the mixed niobium oxide, as determined by X-ray diffraction, preferably corresponds to the crystal structure of N-Nb<NUM>O<NUM>. The crystal structure of N-Nb<NUM>O<NUM> may be found at <NPL>.

Compared to the empirical formula of N-Nb<NUM>O<NUM>, the mixed niobium oxides according to the invention have a modified ratio of cations to anions. In the formula MIx-uMy(x/(<NUM>-y))MVzNb<NUM>-(x/(<NUM>-y))-zO<NUM>-u/<NUM> some Nb has been substituted by both MI and My, increasing the ratio of cations to anions. In the formula BaMvzNb<NUM>-a-zO<NUM>-a some Nb has been substituted by B causing the loss of oxygen from the crystal structure to maintain charge neutrality, also increasing the ratio of cations to anions; the crystal structure of materials having this formula may contain some tetrahedral boron cations between the <NUM>×<NUM> octahedral blocks. This modification is believed to contribute towards the advantageous properties of the mixed niobium oxides for use as active electrode materials. For instance, the modified cation to anion ratio is believed to stabilise the crystal structure.

The crystal structure of a material may be determined by analysis of X-ray diffraction (XRD) patterns, typically obtained from a Cu Kα source, as is widely known. For instance, XRD patterns obtained from a given material can be compared to known XRD patterns to confirm the crystal structure, e.g. via public databases such as the ICDD crystallography database. Rietveld analysis and Pawley analysis can also be used to determine the crystal structure of materials, in particular for the unit cell parameters. Therefore, the mixed niobium oxide may have a Wadsley-Roth crystal structure comprising <NUM>×<NUM> octahedral blocks, as determined by X-ray diffraction.

Here the term 'corresponds' is intended to reflect that peaks in an X-ray diffraction pattern may be shifted by no more than <NUM> degrees (preferably shifted by no more than <NUM> degrees, more preferably shifted by no more than <NUM> degrees) from corresponding peaks in an X-ray diffraction pattern of the material listed above.

The mixed niobium oxide may adopt a monoclinic crystal structure, for example having unit cell parameters a = <NUM>-<NUM>Å, b= <NUM>-<NUM>Å, c= <NUM>-<NUM>Å, α=<NUM>°, β=<NUM>-<NUM>°, γ=<NUM>°. Unit cell parameters may be determined by X-ray diffraction.

MI is a cation having an oxidation state of <NUM>. MI is selected from Li, Na, K, and mixtures thereof. Preferably, MI is selected from Li, Na, and mixtures thereof.

x is the atomic amount of MI, having the range <NUM> ≤ x ≤ <NUM>. x may be an integer, e.g. x = <NUM>, <NUM>, <NUM>, <NUM>, <NUM>, or <NUM>. Optionally, <NUM> ≤ x ≤ <NUM>, such as x = <NUM>, <NUM>, <NUM>, or <NUM>. Preferably, x = <NUM>.

The formula may be deficient in MI, e.g. if some of the <NUM>+ cation is lost via volatility since it typically has a low atomic weight. Accordingly, the atomic amount of x may be modified by variable <NUM> ≤ u ≤ <NUM>, where x > u, e.g. x ≥ u + <NUM>. Optionally <NUM> ≤ u ≤ <NUM> or <NUM> ≤ u ≤ <NUM>. Alternatively, u = <NUM>.

My is a cation having an average oxidation state of y. The term "average oxidation state" means that when more than one cation is present the oxidation state refers to My as a whole. For example, if <NUM>/<NUM> of My is W<NUM>+ and <NUM>/<NUM> of My is Fe<NUM>+, then y is <NUM> (<NUM>/<NUM> × <NUM> (the contribution from W) + <NUM>/<NUM> × <NUM> (the contribution from Fe)). However, My, MII, MIII, MIV, and MV may consist of a single cation, in which case the oxidation state is the oxidation state of that cation.

My is selected from Li, Na, K, Cu, Zn, Mg, Ca, Ni, Fe, Mn, Co, Cr, V, Al, B, Ga, Sc, Y, In, La, Yb, Ce, Zr, Ti, Sn, Ge, Si, P, Ta, W, Mo, and mixtures thereof. My may be selected from Li, Na, K, Cu, Zn, Mg, Ni, Fe, Mn, Co, Cr, V, Al, B, Ga, Zr, Ti, Si, P, Ta, and mixtures thereof; or Li, Na, Cu, Zn, Mg, Ni, Fe, Mn, Co, Cr, Al, B, Ga, Zr, Ti, and mixtures thereof. Optionally, My does not contain Li.

y has the range <NUM> ≤ y ≤ <NUM>, optionally <NUM> ≤ y ≤ <NUM>. y may be an integer, e.g. y = <NUM>, <NUM>, <NUM>, or <NUM>; preferably <NUM>, <NUM>, and <NUM>. When y is an integer, optionally all cations forming My have the same oxidation state.

When y is <NUM>, <NUM>, <NUM>, or <NUM>y may be selected from Li, Na, Cu, Zn, Mg, Ca, Ni, Fe, Mn, Co, Cr, Al, B, Ga, Sc, Y, In, La, Yb, Ce, Zr, Ti, Sn, Ge, and mixtures thereof.

When y is <NUM>, <NUM>, or <NUM>y may be selected from Cu, Zn, Mg, Ca, Ni, Fe, Mn, Co, Mn, Cr, Al, B, Ga, Sc, Y, In, La, Yb, Ce, Zr, Ti, Sn, Ge, and mixtures thereof.

The atomic amount of My depends on the amount of MI and the oxidation state of My, having the relationship x/(<NUM>-y).

MV is an optional cation having an average oxidation state of <NUM>. Optionally, MV is a cation having an oxidation state of <NUM>, wherein all cations forming MV have the same oxidation state of <NUM>.

The atomic amount of MV is z, having the range <NUM> ≤ z ≤ <NUM>. Optionally, <NUM> ≤ z ≤ <NUM>. z may be > <NUM>, e.g. > <NUM>. Alternatively, z=<NUM> in which case MV is not present.

MV is selected from Mn, Fe, Al, Ga, Y, In, La, Yb, Cu, Zn, Mg, Ni, Co, Ca, Ce, Zr, Ti, Sn, Ge, Si, V, P, Ta, W, Mo, Cr, and mixtures thereof. MV may be selected from Ce, Zr, Ti, Sn, Ge, Si, V, P, Ta, W, Mo, Cr, V, P, Ta, and mixtures thereof; or V, P, Ta, and mixtures thereof. Optionally all cations forming MV have an oxidation state of <NUM>.

When y = <NUM>, the mixed niobium oxide may have the formula MIx-uNIx/<NUM>MVzNb<NUM>-x/<NUM>-zO<NUM>-u/<NUM>, wherein NI is a cation having an oxidation state of <NUM>. NI may be selected from Li, Na, K and mixtures thereof; preferably Li, Na, and mixtures thereof.

When y = <NUM>, the mixed niobium oxide may have the formula MIx-uMIIx/<NUM>MVzNb<NUM>-x/<NUM>-zO<NUM>-u/<NUM>, wherein MII is a cation having an average oxidation state of <NUM>. MII may be selected from Cu, Zn, Mg, Ni, Fe, Mn, Co, Ca , and mixtures thereof; or Cu, Zn, Mg, Ni, and mixtures thereof; or Zn, Mg, Ni, and mixtures thereof. Optionally all cations forming MII have an oxidation state of <NUM>.

When y = <NUM>, the mixed niobium oxide may have the formula MIx-uMIIIx/<NUM>MVzNb<NUM>-x/<NUM>-zO<NUM>-u/<NUM>, wherein MIII is a cation having an average oxidation state of <NUM>. MIII may be selected from Mn, Cr, V, Fe, Al, B, Ga, Y, In, La, Yb, Ce, and mixtures thereof; or Mn, Cr, Fe, Al, B, Ga, Y, and mixtures thereof; or Cr, Al, Fe, and mixtures thereof. Optionally all cations forming MIII have an oxidation state of <NUM>.

When y = <NUM>, the mixed niobium oxide may have the formula MIx-uMIVxMVzNb<NUM>-x-zO<NUM>-u/<NUM>, wherein MIV is a cation having an average oxidation state of <NUM>. MIV may be selected from Zr, Ti, Mn, Ce, Sn, Ge, V, Si, and mixtures thereof; or Zr, Ti, Sn, Ge, V, and mixtures thereof; or Ti, V, and mixtures thereof. Optionally all cations forming MIV have an oxidation state of <NUM>.

The atomic amount of B in BaMvzNb<NUM>-a-zO<NUM>-a is a, having the range <NUM> < a ≤ <NUM>, for example <NUM> < a ≤ <NUM>. Optionally, <NUM> ≤ a ≤ <NUM> or <NUM> ≤ a ≤ <NUM>. a may be an integer. Preferably a = <NUM>. Up to <NUM> at. % of the cations may be partially substituted by at least one cation selected from P, K, Fe, Ti, Zr, Sn, Ge, Zn, Mg, Al, Ga, Y, W, Mo, Cr, V, Si, Ni, Mn, Ta, Li, Na, and mixtures thereof; or Ti, W, Mo, Cr, Zn, Al, Fe, P, and mixtures thereof.

In MbNb<NUM>-bO<NUM>-<NUM>. 5b+bc as described above, M is a cation selected from P, B, W, Mo, V, Ti, Si, and mixtures thereof. M may be selected from P, W, B, Ti, and mixtures thereof; or P, W, and mixtures thereof. Preferably M comprises P and/or W. Up to <NUM> at. % of the cations may be partially substituted by at least one cation selected from K, Fe, Zr, Sn, Ge, Zn, Mg, Al, Ga, Y, Cr, Ni, Mn, Ta, Li, Na and mixtures thereof; or Cr, Zn, Al, Fe, and mixtures thereof. b is <NUM> < b ≤ <NUM>, or <NUM> ≤ b ≤ <NUM>, or <NUM> ≤ b ≤ <NUM>. c is half of the average oxidation state of M and is <NUM> ≤ c ≤ <NUM>, or <NUM> ≤ c ≤ <NUM>, or <NUM>.

In an X-ray diffraction pattern of MbNb<NUM>-bO<NUM>-<NUM>. 5b+bc from a CuKa source, the most intense peak between <NUM> - <NUM>° 2θ may have a full width half maximum of > <NUM>; optionally > <NUM>, > <NUM>, and/or < <NUM> (e.g. ><NUM> to <<NUM>). <FIG> shows an XRD pattern of a sample having this peak. It is believed that samples with this peak encompass the presence of some connecting tetrahedral cations between the <NUM>×<NUM> octahedral blocks within the Wadsley-Roth crystal structure. Materials having this crystal structure were found to have particularly high capacity.

It will be understood that the discussion of the variables of the formula (e.g. M, MI, x, u, My, y, Mv, z, a, b, c) is intended to be read in combination. For example, the mixed niobium oxide may have the formula MIx-uMy(x/(<NUM>-y))MVzNb<NUM>-(x/(<NUM>-y))-zO<NUM>-u/<NUM>, wherein:.

For example, the mixed niobium oxide may have the formula MIxMy(x/(<NUM>-y))Nb<NUM>-(x/(<NUM>-y))O<NUM>, wherein:.

Optionally, the mixed niobium oxide only contains Li if a further cation other than Li and Nb is present. An example of such a material is Li<NUM>Cr<NUM>Nb<NUM>O<NUM>, where Cr is the cation other than Li and Nb. In addition, the mixed niobium oxide may be free from Li. It will be understood that the mixed niobium oxides, including those free from Li, may reversibly intercalate Li in situ when acting as an active electrode material in a lithium-ion battery.

The cations in the mixed niobium oxide may be partially substituted by further cations of different oxidation state, for example up to <NUM> at. %, <NUM> at. %, or <NUM> at. % of cations may be substituted. Substitution by a cation of different oxidation state forms a charge imbalanced material. The charge imbalance may be compensated for by oxygen deficiency (for substitution by a cation of lower oxidation state) or excess (for substitution by a cation of higher oxidation state). Alternately or in addition, the charge imbalance may be compensated for by oxidation or reduction of cations.

The oxygen anions may be partially substituted by an alternative electronegative anion such as F, Cl, Br, S, Se, N, and mixtures thereof. Optionally up to <NUM> at. % or <NUM> at% of the oxygen anions may be partially substituted by an alternative electronegative anion.

The mixed niobium oxide is preferably in particulate form. The mixed niobium oxide may have a D<NUM> particle diameter in the range of <NUM>-<NUM>, or <NUM>-<NUM>, or <NUM>-<NUM>. These particle sizes are advantageous because they are easy to process and fabricate into electrodes. Moreover, these particle sizes avoid the need to use complex and/or expensive methods for providing nanosized particles. Nanosized particles (e.g. particles having a D<NUM> particle diameter of <NUM> or less) are typically more complex to synthesise and require additional safety considerations.

The mixed niobium oxide may have a D<NUM> particle diameter of at least <NUM>, or at least <NUM>, or at least <NUM>, or at least <NUM>. By maintaining a D<NUM> particle diameter within these ranges, the potential for parasitic reactions in a Li ion cell is reduced from having reduced surface area, and it is easier to process with less binder in the electrode slurry.

The mixed niobium oxide may have a D<NUM> particle diameter of no more than <NUM>, no more than <NUM>, no more than <NUM>, or no more than <NUM>. By maintaining a D<NUM> particle diameter within these ranges, the proportion of the particle size distribution with large particle sizes is minimised, making the material easier to manufacture into a homogenous electrode.

The term "particle diameter" refers to the equivalent spherical diameter (esd), i.e. the diameter of a sphere having the same volume as a given particle, where the particle volume is understood to include the volume of any intra-particle pores. The terms "Dn" and "Dn particle diameter" refer to the diameter below which n% by volume of the particle population is found, i.e. the terms "D<NUM>" and "D<NUM> particle diameter" refer to the volume-based median particle diameter below which <NUM>% by volume of the particle population is found. Where a material comprises primary crystallites agglomerated into secondary particles, it will be understood that the particle diameter refers to the diameter of the secondary particles. Particle diameters can be determined by laser diffraction. Particle diameters can be determined in accordance with ISO <NUM>:<NUM>, for example using Mie theory.

The mixed niobium oxide may have a BET surface area in the range of <NUM>-<NUM><NUM>/g, or <NUM>-<NUM><NUM>/g, or <NUM>-<NUM><NUM>/g. In general, a low BET surface area is preferred in order to minimise the reaction of the mixed niobium oxide with the electrolyte, e.g. minimising the formation of solid electrolyte interphase (SEI) layers during the first charge-discharge cycle of an electrode comprising the material. However, a BET surface area which is too low results in unacceptably low charging rate and capacity due to the inaccessibility of the bulk of the mixed niobium oxide to metal ions in the surrounding electrolyte.

The term "BET surface area" refers to the surface area per unit mass calculated from a measurement of the physical adsorption of gas molecules on a solid surface, using the Brunauer-Emmett-Teller theory. For example, BET surface areas can be determined in accordance with ISO <NUM>:<NUM>.

The mixed niobium oxide may be coated with carbon, e.g. to improve its surface electronic conductivity and/or to prevent reactions with electrolyte.

The mixed niobium oxide may have a protective coating; optionally the protective coating comprises niobium oxide, aluminium oxide, zirconium oxide, organic or inorganic fluorides, organic or inorganic phosphates, titanium oxide, lithiated versions thereof, and mixtures thereof.

In the first aspect the mixed niobium oxide forms the active electrode material of an electrode, preferably of an anode for a lithium-ion battery. However, any of the mixed niobium oxides defined herein may be provided as an active electrode material suitable for incorporating into an electrode. For example, the mixed niobium oxides disclosed herein may be provided as raw materials, not as part of an electrode, e.g. for sale to electrode manufacturers.

The electrode is of the form of an electrode composition in electrical contact with a current collector, where the electrode composition comprises the mixed niobium oxide. A current collector is typically a metal foil, e.g. copper or aluminium foil.

Optionally, the mixed niobium oxide forms at least <NUM> wt. %,<NUM> wt. %, or <NUM> wt. % of the total active electrode material in the electrode. The mixed niobium oxide may form the sole active electrode material in the electrode.

The electrode composition may further comprise at least one other component selected from a binder, a conductive additive, a different active electrode material (e.g. a further mixed niobium oxide as defined herein), and mixtures thereof. For instance, one electrode composition comprises about <NUM> wt% mixed niobium oxide, about <NUM> wt% conductive additive (e.g. carbon black), and about <NUM> wt% binder (e.g. poly(vinyldifluoride)), based on the total dry weight of the electrode composition.

Examples of suitable binders include polyvinylidene fluoride and its copolymers (PVDF), polytetrafluoroethylene (PTFE) and its copolymers, polyacrylonitrile (PAN), poly(methyl)methacrylate or poly(butyl)methacrylate, polyvinyl chloride (PVC), polyvinyl fomal, polyetheramide, polymethacrylic acid, polyacrylamide, polyitaconic acid, polystyrene sulfonic acid, polyacrylic acid (PAA) and alkali metal salts thereof, modified polyacrylic acid (mPAA) and alkali metal salts thereof, cellulose-based polymers, carboxymethylcellulose (CMC), modified carboxymethylcellulose (mCMC), sodium carboxymethylcellulose (Na-CMC), polyvinylalcohol (PVA), alginates and alkali metal salts thereof, butadieneacrylonitrile rubber (NBR), hydrogenated form of NBR (HNBR), styrene-butadiene rubber (SBR) and polyimide. The binder may be present in the electrode composition at <NUM>-<NUM> wt%, or <NUM>-<NUM> wt%, or <NUM>-<NUM> wt%, based on the total dry weight of the electrode composition.

Conductive additives are preferably non-active materials which are included so as to improve electrical conductivity between the active electrode material and between the active electrode material and the current collector. The conductive additives may suitably be selected from graphite, carbon black, carbon fibers, vapor-grown carbon fibres (VGCF), carbon nanotubes, graphene, acetylene black, ketjen black, metal fibers, metal powders and conductive metal oxides. Preferred conductive additives include carbon black and carbon nanotubes. Conductive additives may be present in the electrode composition at <NUM>-<NUM> wt%, <NUM>-<NUM> wt%, or <NUM>-<NUM> wt%, based on the total dry weight of the electrode composition.

The active electrode material may be present in the electrode composition at <NUM>-<NUM> wt%, <NUM>-<NUM> wt%, or <NUM>-<NUM> wt%, based on the total dry weight of the electrode composition. When the active electrode material is present at <NUM> wt. % of the electrode composition it may for a solid-state electrode.

When a different active electrode material is present in addition to the mixed niobium oxide, it may be selected from lithium titanium oxide, titanium niobium oxide, a different mixed niobium oxide, graphite, hard carbon, soft carbon, silicon, doped versions thereof, and mixtures thereof.

The mixed niobium oxide may be in combination with a lithium titanium oxide to form an active electrode material.

The lithium titanium oxide preferably has a spinel or ramsdellite crystal structure, e.g. as determined by X-ray diffraction. An example of a lithium titanium oxide having a spinel crystal structure is Li<NUM>Ti<NUM>O<NUM>. An example of a lithium titanium oxide having a ramsdellite crystal structure is Li<NUM>Ti<NUM>O<NUM>. These materials have been shown to have good properties for use as active electrode materials. Therefore, the lithium titanium oxide may have a crystal structure as determined by X-ray diffraction corresponding to Li<NUM>Ti<NUM>O<NUM> and/or Li<NUM>Ti<NUM>O<NUM>. The lithium titanium oxide may be selected from Li<NUM>Ti<NUM>O<NUM>, Li<NUM>Ti<NUM>O<NUM>, and mixtures thereof.

The lithium titanium oxide may be doped with additional cations or anions. The lithium titanium oxide may be oxygen deficient. The lithium titanium oxide may comprise a coating, optionally wherein the coating is selected from carbon, polymers, metals, metal oxides, metalloids, phosphates, and fluorides.

The lithium titanium oxide may be synthesised by conventional ceramic techniques, for example solid-state synthesis or sol-gel synthesis. Alternatively, the lithium titanium oxide may be obtained from a commercial supplier.

The lithium titanium oxide is in preferably in particulate form. The lithium titanium oxide may have a D<NUM> particle diameter in the range of <NUM>-<NUM>, or <NUM>-<NUM>, or <NUM>-<NUM>. The lithium titanium oxide may have a D<NUM> particle diameter of at least <NUM>, or at least <NUM>, or at least <NUM>. The lithium titanium oxide may have a D<NUM> particle diameter of no more than <NUM>, no more than <NUM>, or no more than <NUM>. By maintaining a D<NUM> particle diameter in this range the packing of lithium titanium oxide particles in the mixture with mixed niobium oxide particles is improved.

Lithium titanium oxides are typically used in battery anodes at small particle sizes due to the low electronic conductivity of the material. In contrast, the mixed niobium oxide as defined herein may be used at larger particle sizes since it typically has a higher lithium ion diffusion coefficient than lithium titanium oxide. Advantageously, in the composition the lithium titanium oxide may have a smaller particle size than the mixed niobium oxide, for example such that the ratio of the D<NUM> particle diameter of the lithium titanium oxide to the D<NUM> particle diameter of the mixed niobium oxide is in the range of <NUM>:<NUM> to <NUM>:<NUM>, or <NUM>:<NUM> to <NUM>:<NUM>. In this way, the smaller lithium titanium oxide particles may be accommodated in the voids between the larger mixed niobium oxide particles, increasing the packing efficiency of the composition.

The lithium titanium oxide may have a BET surface area in the range of <NUM>-<NUM><NUM>/g, or <NUM>-<NUM><NUM>/g, or <NUM>-<NUM><NUM>/g.

The ratio by mass of the lithium titanium oxide to the mixed niobium oxide may be in the range of <NUM> : <NUM> to <NUM> : <NUM>, preferably in the range of <NUM> : <NUM> to <NUM> : <NUM>. In one implementation the active electrode material comprises a higher proportion of the lithium titanium oxide than the mixed niobium oxide, e.g. the ratio by mass of at least <NUM>:<NUM>, at least <NUM>:<NUM>, or at least <NUM>:<NUM>. Advantageously, this allows the mixed niobium oxide to be incrementally introduced into existing electrodes based on lithium titanium oxides without requiring a large change in manufacturing techniques, providing an efficient way of improving the properties of existing electrodes. In another implementation the active electrode material has a higher proportion of the mixed niobium oxide than the lithium titanium oxide, e.g. such that the ratio by mass of the lithium titanium oxide to the mixed niobium oxide is less than <NUM>:<NUM>, or less than <NUM>:<NUM>, or less than <NUM>:<NUM>. Advantageously, this allows for the cost of the active electrode material to be reduced by replacing some of the mixed niobium oxide with lithium titanium oxide.

The mixed niobium oxide may be in combination with a niobium oxide to form an active electrode material. The niobium oxide may be selected from Nb<NUM>O<NUM>, NbO<NUM>, NbO, and Nb<NUM>O<NUM>. Preferably, the niobium oxide is Nb<NUM>O<NUM>.

The niobium oxide may be doped with additional cations or anions, for example provided that the crystal structure of the niobium oxide corresponds to the crystal structure of an oxide consisting of Nb and O, e.g. Nb<NUM>O<NUM>, NbO<NUM>, NbO, and Nb<NUM>O<NUM>. The niobium oxide may be oxygen deficient. The niobium oxide may comprise a coating, optionally wherein the coating is selected from carbon, polymers, metals, metal oxides, metalloids, phosphates, and fluorides.

The niobium oxide may have the crystal structure of Nb<NUM>O<NUM>, NbO<NUM>, NbO, or Nb<NUM>O<NUM> as determined by X-ray diffraction. For example, the niobium oxide may have the crystal structure of orthorhombic Nb<NUM>O<NUM> or the crystal structure of monoclinic Nb<NUM>O<NUM>. Preferably, the niobium oxide has the crystal structure of monoclinic Nb<NUM>O<NUM>, most preferably the crystal structure of H-Nb<NUM>O<NUM>. Further information on crystal structures of Nb<NUM>O<NUM> may be found at <NPL>.

The niobium oxide may be synthesised by conventional ceramic techniques, for example solid-state synthesis or sol-gel synthesis. Alternatively, the niobium oxide may be obtained from a commercial supplier.

The niobium oxide is in preferably in particulate form. The niobium oxide may have a D<NUM> particle diameter in the range of <NUM>-<NUM>, or <NUM>-<NUM>, or <NUM>-<NUM>. The niobium oxide may have a D<NUM> particle diameter of at least <NUM>, or at least <NUM>, or at least <NUM>. The niobium oxide may have a D<NUM> particle diameter of no more than <NUM>, no more than <NUM>, or no more than <NUM>. By maintaining a D<NUM> particle diameter in this range the packing of niobium oxide particles in the mixture with mixed niobium oxide particles is improved.

The niobium oxide may have a BET surface area in the range of <NUM>-<NUM><NUM>/g, or <NUM>-<NUM><NUM>/g, or <NUM>-<NUM><NUM>/g.

The ratio by mass of the niobium oxide to the mixed niobium oxide may be in the range of <NUM> : <NUM> to <NUM> : <NUM>, or in the range of <NUM> : <NUM> to <NUM> : <NUM>, or preferably in the range of <NUM> : <NUM> to <NUM> : <NUM>.

The invention also provides the use of the mixed niobium oxides defined herein in an anode for a metal-ion battery, optionally wherein the metal-ion battery is a lithium-ion or sodium-ion battery, preferably a lithium-ion battery. Lithium-ion batteries include liquid-based batteries, polymer-based batteries, semisolid-based batteries and full solid-state-based batteries.

A further implementation of the invention is an electrochemical device comprising an anode, a cathode, and an electrolyte disposed between the anode and the cathode, wherein the anode comprises an active electrode material according to the first aspect of the invention; optionally wherein the electrochemical device is metal-ion battery such as a lithium-ion battery or a sodium-ion battery. For example, the anode may be an electrode in accordance with the first aspect of the invention. Preferably, the electrochemical device is a lithium-ion battery having a reversible anode active material specific capacity of greater than <NUM> mAh/g at <NUM> mA/g, wherein the battery can be charged and discharged at current densities relative to the anode active material of <NUM> mA/g or more, or <NUM> mA/g or more, or <NUM> mA/g or more, or <NUM> mA/g or more whilst retaining greater than <NUM>% of the initial cell capacity at <NUM> mA/g. It has been found that use of the active electrode materials of the first aspect of the invention can enable the production of a lithium-ion battery with this combination of properties, representing a lithium-ion battery that is particularly suitable for use in applications where high charge and discharge current densities are desired. Notably, the examples have shown that active electrode materials according to the first aspect of the invention have excellent capacity retention at high C-rates.

The electrochemical device preferably has an N/P ratio ><NUM>, wherein N/P is defined as: <MAT> wherein:.

The first lithiation/delithiation capacity is measured on an equivalent half-cell. An equivalent half-cell can be understood to utilise the same electrode composition deposited at the same areal loading and active fraction as the full cell. For the anode, the first constant current C/<NUM> lithiation (discharge, negative current) capacity (vs Li/Li+) at <NUM> is measured. For the cathode, the first constant current C/<NUM> delithiation (charge, positive current) capacity (vs Li/Li+) at <NUM> is measured.

N/P is preferably greater than one, e.g. ≥<NUM>. N/P may be in the range of ><NUM>-<NUM>, or <NUM>-<NUM>, or most preferably <NUM>-<NUM>.

The cathode comprises an active cathode material which may be selected from nickel-based layered oxides of the class LiNi1xMxO<NUM> where M = Co, Mn, Al such as NMCs - lithium nickel manganese cobalt oxides, NCAs - lithium cobalt aluminium oxides, and LCOs - lithium cobalt oxides; and LNMOs - lithium nickel manganese oxides (e.g. LiNi<NUM>Mn<NUM>O<NUM>). For example, the active cathode material may be a lithium nickel manganese cobalt oxide. Active cathode materials are widely available from commercial suppliers. Active cathode materials may be doped with additional cations and/or anions.

The choice of the active electrode material can affect the appropriate voltage range, including for determining the first lithiation/delithiation capacity. For example, appropriate voltage ranges may be LNMO: <NUM>-3V, upper cut off <NUM>. 2V; NCA, NMC, and LCO: <NUM>-<NUM>. 7V, upper cut off <NUM>. 5V; mixed niobium oxide: <NUM>-0V, lower cut off 0V. Narrower ranges may be LNMO: <NUM>-3V, upper cut off 5V; NCA, NMC, and LCO: <NUM>-<NUM>. 7V, upper cut off <NUM>. 3V; mixed niobium oxide: 3V-<NUM>. 0V, lower cut off <NUM>.

An appropriate voltage range may be determined empirically. For example, the voltage profile correlates to the change in energy state of the anode and cathode materials associated with removal or insertion of electrons and ions. The cut-off voltage for the cell may be selected to fall before a specific inflection point in the voltage profile which corresponds to a rise in energy state of one or both electrodes beyond a critical level which leads the crystal structure to decay to a lower energy structure at a rate which is significantly harmful to the cell's performance. The absolute voltage at which this happens is a function of the electrode potentials of both electrodes, but can be calculated by use of a common reference electrode and need not be determined experimentally for well-established material families with reliable standard electrochemical behaviour.

The cathode active material is preferably in particulate form, e.g. having a D<NUM> particle diameter in the range of <NUM>-<NUM>, or <NUM>-<NUM>, or <NUM>-<NUM>.

The electrolyte may include any material suitable for metal-ion battery operation, preferably lithium-ion battery operation. For example, the electrolyte may be a non-aqueous solution (e.g., an organic electrolytic solution). The electrolyte may include one or more non-aqueous solvents and a salt that is at least partially dissolved in the solvent. For example, the solvent may include an organic solvent, such as, e.g., ethylene carbonate (EC) and/or other carbonate based solvents, or butyrate, or acetate, or mixtures thereof. The solvent may include <NUM> LiPF<NUM> dissolved in an aprotic solvent mixture, such as a <NUM>:<NUM> by weight of a mixture of ethylene carbonate and other carbonate based solvents or butyrate or acetate. Salts suitable for use in the invention include LiPF<NUM>, LiSbF<NUM>, LiBF<NUM>, LiTFSI, LiFSI, LiAlCl<NUM>, LiAsF<NUM>, LiClO<NUM>, LiGaCl<NUM>, LiC(SO<NUM>CF<NUM>)<NUM>, LiN(CF<NUM>SO<NUM>)<NUM>, Li(CF<NUM>SO<NUM>), LiB(C<NUM>H<NUM>O<NUM>)<NUM>, LiBOB (lithium bis(oxalate) borate), and LiDFOB (lithium difluoro (oxalate) borate). Low-viscosity solvents (e.g., organic solvents) suitable for use in the electrolyte may include, but are not limited to ethyl methyl carbonate (EMC), dioxlane (DOL), ethyl acetate (EA); propylene acetate (PA); butyl acetate (BA); methyl butyrate (MB); ethyl butyrate (EB); dimethyl carbonate (DMC); diethyl carbonate (DEC); <NUM>,<NUM>-dimethoxyethane (DME); tetrahydrofuran (THF); methyl acetate (MA); diglyme (DGL); triglyme; tetraglyme; cyclic carbonates; cyclic esters; cyclic amides; propylene carbonate (PC); methyl propyl carbonate (MPC); acetonitrile; dimethyl sulfoxide (DMS); dimethyl formamide; dimethyl acetamide; gamma-butyrolactone (GBL); and N-methyl-pyrrolidinone (NMP); as well as various mixtures or combinations thereof.

The mixed niobium oxide may be synthesised by conventional ceramic techniques. For example, it may be made by one or more of solid-state synthesis or sol-gel synthesis. The mixed niobium oxide may additionally be synthesised by one or more of alternative techniques commonly used, such as hydrothermal or microwave hydrothermal synthesis, solvothermal or microwave solvothermal synthesis, coprecipitation synthesis, spark or microwave plasma synthesis, combustion synthesis, electrospinning, spray pyrolysis, chemical vapour deposition, atomic layer deposition, and mechanical alloying.

The mixed niobium oxide may be provided by a method comprising steps of: providing one or more precursor materials; mixing said precursor materials to form a precursor material mixture; and heat treating the precursor material mixture in a temperature range from <NUM> - <NUM> or <NUM> - <NUM>, thereby providing the mixed niobium oxide.

To provide a mixed niobium oxide comprising an additional electronegative anion than oxygen the method may further comprise the steps of: mixing the mixed niobium oxide with a precursor comprising an additional electronegative anion to provide a further precursor material mixture; and heat treating the further precursor material mixture in a temperature range from <NUM> - <NUM> or <NUM> - <NUM> optionally under reducing conditions, thereby providing the mixed niobium oxide comprising an additional electronegative anion.

For example, to provide a mixed niobium oxide comprising N, the method may further comprise the steps of: mixing the mixed niobium oxide with a precursor comprising N (for example melamine or urea) to provide a further precursor material mixture; and heat treating the further precursor material mixture in a temperature range from <NUM> - <NUM> under reducing conditions (for example under N<NUM>), thereby providing the mixed niobium oxide comprising N.

For example, to provide a mixed niobium oxide comprising F, the method may further comprise the steps of: mixing the mixed niobium oxide with a precursor comprising F (for example polyvinylidene fluoride or NH<NUM>F) to provide a further precursor material mixture; and heat treating the further precursor material mixture in a temperature range from <NUM> - <NUM> under oxidising conditions (for example in air), thereby providing the mixed niobium oxide comprising F.

The method may comprise the further step of heat treating the mixed niobium oxide in a temperature range from <NUM> - <NUM> or <NUM> - <NUM> under reducing conditions, thereby inducing oxygen vacancies in the mixed niobium oxide.

The precursor materials for making the mixed niobium oxide may include one or more metal oxides, metal hydroxides, metal salts or ammonium salts. For example, the precursor materials may include one or more metal oxides or metal salts of different oxidation states and/or of different crystal structure. Examples of suitable precursor materials include but are not limited to: Nb<NUM>O<NUM>, Nb(OH)<NUM>, Niobic Acid, NbO, Ammonium Niobate Oxalate, NH<NUM>H<NUM>PO<NUM>, (NH<NUM>)<NUM>PO<NUM>, (NH<NUM>)<NUM>PO<NUM>, P<NUM>O<NUM>, H<NUM>PO<NUM>, Ta<NUM>O<NUM>, WO<NUM>, ZrO<NUM>, TiO<NUM>, MoO<NUM>, V<NUM>O<NUM>, ZrO<NUM>, CuO, ZnO, Al<NUM>O<NUM>, K<NUM>O, KOH, CaO, GeO<NUM>, Ga<NUM>O<NUM>, SnO<NUM>, CoO, Co<NUM>O<NUM>, Fe<NUM>O<NUM>, Fe<NUM>O<NUM>, MnO, MnO<NUM>, NiO, Ni<NUM>O<NUM>, H<NUM>BO<NUM>, ZnO, Li<NUM>CO<NUM>, Na<NUM>CO<NUM>, H<NUM>BO<NUM>, NiO, Mg<NUM>(CO<NUM>)<NUM>(OH)<NUM>. <NUM><NUM>O, and and MgO. The precursor materials may not comprise a metal oxide, or may comprise ion sources other than oxides. For example, the precursor materials may comprise metal salts (e.g. NO<NUM>-, SO<NUM>-) or other compounds (e.g. oxalates, carbonates). For the substitution of the oxygen anion with other electronegative anions, the precursors may include one or more organic compounds, polymers, inorganic salts, organic salts, gases, or ammonium salts; examples include but are not limited to: melamine, NH<NUM>HCO<NUM>, NH<NUM>, NH<NUM>F, PVDF, PTFE, NH<NUM>Cl, NH<NUM>Br, NH<NUM>I, Br<NUM>, Cl<NUM>, I<NUM>, ammonium oxychloride amide, and hexamethylenetetramine.

When it is desired to make a mixed niobium oxide comprising a cation of a specific oxidation state a precursor comprising that cation at that oxidation state may be selected. For example, when making a mixed niobium oxide comprising Mn<NUM>+, MnO may be used as the precursor. When making a mixed niobium oxide comprising Mn<NUM>+, MnO<NUM> may be used as the precursor.

Some or all of the precursor materials may be particulate materials. Where they are particulate materials, preferably they have a D<NUM> particle diameter of less than <NUM> in diameter, for example from <NUM> to <NUM>. Providing particulate materials with such a particle diameter can help to promote more intimate mixing of precursor materials, thereby resulting in more efficient solid-state reaction during the heat treatment step. However, it is not essential that the precursor materials have an initial particle size of <<NUM> in diameter, as the particle size of the one or more precursor materials may be mechanically reduced during the step of mixing said precursor materials to form a precursor material mixture.

The step of mixing the precursor materials to form a precursor material mixture and/or further precursor material mixture may be performed by a process selected from: dry or wet/solvated planetary ball milling, rolling ball milling, high energy ball milling, bead milling, pin milling, a classification step, high shear milling, air jet milling, steam jet milling, planetary mixing, powder plending, and/or impact milling. The force used for mixing/milling may depend on the morphology of the precursor materials. For example, where some or all of the precursor materials have larger particle sizes (e.g. a D<NUM> particle diameter of greater than <NUM>), the milling force may be selected to reduce the particle diameter of the precursor materials such that the such that the particle diameter of the precursor material mixture is reduced to <NUM> in diameter or lower. When the particle diameter of particles in the precursor material mixture is <NUM> or less, this can promote a more efficient solid-state reaction of the precursor materials in the precursor material mixture during the heat treatment step. The solid-state synthesis may also be undertaken in pellets formed at high pressure (><NUM> MPa) from the precursor powders.

The step of heat treating the precursor material mixture and/or the further precursor material mixture may be performed for a time of from <NUM> hour to <NUM> hours, more preferably from <NUM> hours to <NUM> hours. For example, the heat treatment step may be performed for <NUM> hour or more, <NUM> hours or more, <NUM> hours or more, <NUM> hours or more, or <NUM> hours or more. The heat treatment step may be performed for <NUM> hours or less, <NUM> hours or less, <NUM> hours or less, or <NUM> hours or less.

The step of heat treating the precursor material mixture may be performed in a gaseous atmosphere, preferably air. Suitable gaseous atmospheres include: air, N<NUM>, Ar, He, CO<NUM>, CO, O<NUM>, H<NUM>, NH<NUM> and mixtures thereof. The gaseous atmosphere may be a reducing atmosphere. Where it is desired to make an oxygen-deficient material, preferably the step of heat treating the precursor material mixture is performed in an inert or reducing atmosphere.

The step of heat treating the further precursor material mixture may be performed under reducing conditions. Reducing conditions include under an inert gas such as nitrogen, helium, argon; or under a mixture of an inert gas and hydrogen; or under vacuum. Preferably, the step of heat treating the further precursor material mixture comprises heating under inert gas.

The further step of heat treating the mixed niobium oxide and/or the mixed niobium oxide comprising additional electronegative anions optionally under reducing conditions may be performed for a time of from <NUM> hour to <NUM> hours, more preferably from <NUM> hours to <NUM> hours. For example, the heat treatment step may be performed for <NUM> hour or more, <NUM> hours or more, <NUM> hours or more, <NUM> hours or more, or <NUM> hours or more. The further step heat treating may be performed for <NUM> hours or less, <NUM> hours or less, <NUM> hours or less, or <NUM> hours or less. Reducing conditions include under an inert gas such as nitrogen, helium, argon; or under a mixture of an inert gas and hydrogen; or under vacuum. Preferably heating under reducing conditions comprises heating under inert gas.

In some methods it may be beneficial to perform a two-step heat treatment. For example, the precursor material mixture and/or the further precursor material mixture may be heated at a first temperature for a first length of time, follow by heating at a second temperature for a second length of time. Preferably the second temperature is higher than the first temperature. Performing such a two-step heat treatment may assist the solid-state reaction to form the desired crystal structure. This may be carried out in sequence, or may be carried out with an intermediate re-grinding step.

The method may include one or more post-processing steps after formation of the mixed niobium oxide. In some cases, the method may include a post-processing step of heat treating the mixed niobium oxide, sometimes referred to as 'annealing'. This post-processing heat treatment step may be performed in a different gaseous atmosphere to the step of heat treating the precursor material mixture to form the mixed niobium oxide. The post-processing heat treatment step may be performed in an inert or reducing gaseous atmosphere. Such a post-processing heat treatment step may be performed at temperatures of above <NUM>, for example at about <NUM>. Inclusion of a post-processing heat treatment step may be beneficial to e.g. form deficiencies or defects in the mixed niobium oxide, for example to induce oxygen deficiency; or to carry out anion exchange on the formed mixed niobium oxide e.g. N exchange for the O anion.

The method may include a step of milling and/or classifying the mixed niobium oxide (e.g. impact milling, jet milling, steam jet milling, high energy milling, high shear milling, pin milling, air classification, wheel classification, sieving, cyclonic separation, bead milling) to provide a material with any of the particle size parameters given above.

The invention provides a method of making an electrode, the method comprising providing a mixed niobium oxide as defined herein; and depositing the mixed niobium oxide onto a current collector, thereby forming the electrode. Providing the mixed niobium oxide may include synthesising the mixed niobium oxide by the methods provided herein. The depositing step may include forming a slurry of the mixed niobium oxide and a solvent. The slurry may comprise at least one other component selected from a binder, a conductive additive, a different active electrode material, and mixtures thereof. The slurry may be deposited onto a current collector and the solvent removed, thereby forming an electrode layer on the current collector. Further steps, such as heat treatment to cure any binders and/or calendaring of the electrode layer may be carried out as appropriate. For example, the solvent may be removed by drying e.g. at temperatures of <NUM>-<NUM>. The electrode may be calendared to a density of <NUM>-<NUM> or <NUM>-<NUM> cm-<NUM>. The electrode layer may have a thickness in the range of from <NUM> to <NUM>, preferably <NUM> to <NUM>, preferably <NUM> to <NUM>, preferably <NUM> to <NUM>, preferably <NUM> to <NUM>, preferably <NUM> to <NUM>.

Alternatively, the slurry may be formed into a freestanding film or mat comprising the mixed niobium oxide, for instance by casting the slurry onto a suitable casting template, removing the solvent and then removing the casting template. The resulting film or mat is in the form of a cohesive, freestanding mass which may then be bonded to a current collector by known methods.

The mixed niobium oxides were synthesised by a solid-state route. Appropriate amounts of Nb<NUM>O<NUM> and precursor materials were mixed and milled, e.g., using a pestle and mortar or impact mill, to form a homogeneous precursor mixture. The resulting mixtures were heat treated in an alumina crucible to high temperatures (> <NUM>) for <NUM> - <NUM>, using a heating rate of between <NUM> - <NUM> °/min. The process was repeated until the desired single phase (<NUM>×<NUM> Wadsley-Roth block structure) was observed within the X-ray diffraction pattern. Specifically, stoichiometric amounts of precursor materials (Nb<NUM>O<NUM>, Li<NUM>CO<NUM>, Na<NUM>CO<NUM>, H<NUM>BO<NUM>, TiO<NUM>, Al<NUM>O<NUM>, Fe<NUM>O<NUM>, Cr<NUM>O<NUM>, NiO and Mg<NUM>(CO<NUM>)<NUM>(OH)<NUM>. <NUM><NUM>O) were mixed and milled either in by hand for <NUM> mins in a pestle and mortar (ca. <NUM>) or using an impact mill at <NUM>,<NUM> rpm for <NUM> mins (ca. The resulting powders were placed in an alumina crucible and heat treated within a muffle furnace in air at T<NUM> = <NUM> - <NUM>, optionally <NUM> - <NUM>, for <NUM> - <NUM>. A heating rate of <NUM>/min was used for all heating steps. An additional milling and heat treatment step T<NUM> was optionally carried out to improve phase purity. Following this, a final milling step was utilised using a pestle and mortar or impact mill for de-agglomeration. The compositions and synthesis parameters are summarised within Table <NUM>.

The phase purity of samples was analysed using a Rigaku Miniflex powder X-ray diffractometer in the 2θ range (<NUM>-<NUM>°) at <NUM>°/min scan rate, or a Bruker D8 Powder diffractometer in the 2θ range <NUM>-<NUM> or <NUM>-<NUM>° (step size <NUM>°, time per step <NUM>).

<FIG> and <FIG> show the measured XRD diffraction patterns for selected Samples. <FIG> shows TEM micrographs which show the highly crystalline structure achieved. Table <NUM> provides unit cell parameters derived from Pawley refinement based on the N-Nb<NUM>O<NUM> structure.

Li-ion cell charge rate is usually expressed as a "C-rate". A 1C charge rate means a charge current such that the cell is fully charged in <NUM>, 10C charge means that the battery is fully charged in <NUM>/10th of an hour (<NUM> minutes). C-rate hereon is defined from the reversible capacity observed of the anode within the voltage limits applied in its second cycle de-lithiation, i.e. for an anode that exhibits <NUM> mAh cm-<NUM> capacity within the voltage limits of <NUM> - <NUM> V, a 1C rate corresponds to a current density applied of <NUM> mA cm-<NUM>. In a typical material as described herein, this corresponds to ~<NUM> mA/g of active material.

Electrochemical tests were carried out in half-coin cells (CR2032 size) for analysis. In half-coin tests, the active material is tested in an electrode versus a Li metal electrode to assess its fundamental performance. In the below examples, the active material composition to be tested was combined with N-Methyl Pyrrolidone (NMP), carbon black (Super P) acting as a conductive additive, and poly(vinyldifluoride) (PVDF) binder and mixed to form a slurry using a lab-scale centrifugal planetary mixer. The non-NMP composition of the slurries was <NUM> wt% active material, <NUM> wt% conductive additive, <NUM> wt% binder. The slurry was coated on an Al foil current collector to the desired loading of <NUM> - <NUM> m-<NUM> by doctor blade coating and dried by heating. The electrodes were then calendared to a density of <NUM> - <NUM> cm-<NUM> at <NUM> to achieve targeted porosities of <NUM>-<NUM>%. Electrodes were punched out at the desired size and combined with a separator (Celgard porous PP/PE), Li metal, and electrolyte (<NUM> LiPF<NUM> in EC/DEC) inside a steel coin cell casing and sealed under pressure. Cycling was then carried out at <NUM> at low current rates (C/<NUM>) for <NUM> full cycles of lithiation and de-lithiation between <NUM> - <NUM> V. Afterwards, the cells were tested for their performance at increasing current densities. During these tests, the cells were cycled asymmetric at <NUM>, with a slow lithiation (C/<NUM>) followed by increasing de-lithiation rates (e.g. 1C, 5C, 10C) to provide the capacity retention.

Data has been averaged from <NUM> to <NUM> cells prepared from the same electrode coating, with the error shown from the standard deviation. Accordingly, the data represent a robust study showing the improvements achieved by the materials according to the invention compared to prior materials. These data are shown in Tables <NUM> and <NUM>. Voltage vs. state of charge/discharge curves for samples <NUM> and <NUM> are shown in <FIG>.

Homogeneous, smooth coatings on both Cu and Al current collector foils, the coatings being free of visible defects or aggregates may also be prepared as above for these samples with a centrifugal planetary mixer to a composition of up to <NUM> wt% active material, <NUM> wt% conductive additive, <NUM> wt% binder. These can be prepared with both PVDF (i.e. NMP-based) and CMC:SBR-based (i.e. water-based) binder systems. The coatings can be calendared at <NUM> for PVDF and <NUM> for CMC:SBR to porosities of <NUM>-<NUM>% at loadings from <NUM> to <NUM> mAh cm-<NUM>. This is important to demonstrate the viability of these materials in both high energy and high-power applications, with high active material content.

Claim 1:
An electrode comprising a mixed niobium oxide as an active electrode material, wherein the electrode is of the form of an electrode composition in electrical contact with a current collector, where the electrode composition comprises the mixed niobium oxide, wherein the mixed niobium oxide has the formula MIx-uMy(x/(<NUM>-y))MVzNb<NUM>-(x/(<NUM>-y))-zO<NUM>-u/<NUM>, wherein:
MI is a cation having an oxidation state of <NUM>, wherein MI is selected from Li, Na, K, and mixtures thereof;
My is a cation having an average oxidation state of y, wherein My is selected from Li, Na, K, Cu, Zn, Mg, Ca, Ni, Fe, Mn, Co, Cr, V, Al, B, Ga, Sc, Y, In, La, Yb, Ce, Zr, Ti, Sn, Ge, Si, P, Ta, W, Mo, and mixtures thereof;
MV is a cation having an average oxidation state of <NUM>, wherein MV is selected from Mn, Fe, Al, Ga, Y, In, La, Yb, Cu, Zn, Mg, Ni, Co, Ca, Ce, Zr, Ti, Sn, Ge, Si, V, P, Ta, W, Mo, Cr, and
mixtures thereof; <MAT> <MAT> <MAT> <MAT> <MAT>