HIGHLY EFFICIENT ELECTRODES ENABLED BY SEGREGATED NETWORKS

Abstract

A composite for use as an electrode, the composition comprising a uniformly distributed spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and a particulate active material, and in which the composite is free of carbon black and has no additional polymeric binder.

Claims

1. A composite for use as an electrode, the composite comprising a spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and a particulate active material, without the need for additional binder, wherein the electrode remains crack free at a thickness of 50 μm or greater.

2. The composite of claim 1, wherein the carbon nanotubes, metallic nanowires or a combination thereof, form a continuous two-dimensional membrane which wraps around the particulate active material and acts as a scaffold to hold the particulate active material in place to form said segregated network.

3. The composite of claim 1, wherein the ratio of the length of the carbon nanotubes or metallic nanowires and the active material particles is at most 1:1.

4. (canceled)

5. The composite of claim 1, wherein the composite comprises from 0.1 wt % to 10 wt % of the spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof.

6. The composite of claim 1, wherein the metallic nanowires consist of silver, gold, platinum, palladium or nickel, or any metallic nanowire coated with a noble metal.

7. The composite of claim 1, wherein the particulate active material is selected from micron-sized silicon powder, lithium, sulphur, graphene, graphite, and lithium nickel manganese cobalt oxide (NMC, LiNi.sub.xMn.sub.yCo.sub.zO.sub.2 where x+y+z=1), lithium cobalt oxide (LCO), lithium nickel cobalt aluminium oxide (NCA), lithium iron phosphate (LFP), lithium titanium oxide (LTO) alloying materials (Si, Ge, Sn, P etc.), chalcogenides (S, Se, Te), metal halides (F, Cl, Br, I), and any other suitable battery material.

8. (canceled)

9. The composite of claim 1, wherein the composite comprises from 90 wt % to 99.9 wt % of the particulate active material.

10. (canceled)

11. A composite for use as a crack-free electrode having a thickness of at least 50 μm, the composite comprising a spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and a particulate active material, without the need for an additional binder, wherein the composite comprises from 0.1 wt % to 10 wt % of the spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and wherein the carbon nanotubes, metallic nanowires or a combination thereof, form a continuous two-dimensional membrane which wraps around the said particulate active material and acts as a scaffold to hold the particulate active material in place to form said segregated network.

12. (canceled)

13. A positive electrode or negative electrode comprising a spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and a particulate active material, without the need for additional binder, wherein the electrode remains crack free at a thickness of 50 μm or greater or a composite comprising a spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and a particulate active material, without the need for an additional binder, wherein the composite comprises from 0.1 wt % to 10 wt % of the spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and wherein the carbon nanotubes, metallic nanowires or a combination thereof, form a continuous two-dimensional membrane which wraps around the said particulate active material and acts as a scaffold to hold the particulate active material in place to form said segregated network.

14. The positive electrode of claim 13, wherein the carbon nanotube, metallic nanowires or combination thereof have a mass fraction (Mf) in the electrode of 0.01-25 wt %.

15. (canceled)

16. (canceled)

17. The negative electrode of claim 13, wherein the carbon nanotube, metallic nanowires or combination thereof have a mass fraction (Mf) in the electrode of 0.001-15 wt %.

18. (canceled)

19. (canceled)

20. The positive electrode and the negative electrode of claim 13, wherein the positive and negative electrodes each have a thickness of between 50 μm and 2000 μm.

21. (canceled)

22. A non-rechargeable battery or a rechargeable battery comprising an anode material, a cathode material, and an electrolyte, wherein the anode material and the cathode material are composed of a composite comprising a spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and a particulate active material, without the need for additional binder, wherein the electrode remains crack free at a thickness of 50 μm or greater or a composite comprising a spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and a particulate active material, without the need for an additional binder, wherein the composite comprises from 0.1 wt % to 10 wt % of the spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and wherein the carbon nanotubes, metallic nanowires or a combination thereof, form a continuous two-dimensional membrane which wraps around the said particulate active material and acts as a scaffold to hold the particulate active material in place to form said segregated network.

23. A method for producing a positive or a negative electrode comprising a spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and a particulate active material, without the need for additional binder, wherein the electrode remains crack free at a thickness of 50 μm or greater or a composite comprising a spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and a particulate active material, without the need for an additional binder, wherein the composite comprises from 0.1 wt % to 10 wt % of the spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and wherein the carbon nanotubes, metallic nanowires or a combination thereof, form a continuous two-dimensional membrane which wraps around the said particulate active material and acts as a scaffold to hold the particulate active material in place to form said segregated network, the method comprising mixing an aqueous dispersion of carbon nanotubes or metallic nanowires, or a combination thereof, with a particulate active material powder to form a mixture, and depositing the mixture onto a substrate to spontaneously form a segregated network that yields an electrode.

24. The method of claim 23, wherein the mixture of the carbon nanotubes or metallic nanowires, or combination thereof, with the particulate active material has a viscosity of approximately 0.1 Pa.Math.s at a shear rate of 100 s.sup.−1.

25. The method of claim 23, wherein the mixture is dried to form the spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof.

26. The method of claim 23, wherein the mixture is deposited onto the substrate by any one or more of the following techniques: slurry casting, blade coating, filtration, screen printing, spraying (electrospray, ultrasonic-spray, conventional aerosol spray), printing (ink jet printing or 3D printing), roll-to-roll coating or processing, or drop casting.

27. (canceled)

28. The method of claim 23, wherein the carbon nanotubes, metallic nanowires or combination thereof, are dispersed in either an organic solvent alone or an organic solvent water-stabilised with 0.2 wt % to 2 wt % surfactant.

29. (canceled)

30. (canceled)

31. A composite for use as an electrode having a thickness of greater than 100 μm, the composite comprising a spontaneously formed segregated network of carbon nanotubes, metallic nanowires or a combination thereof, and a particulate active material, without the need for additional binder, wherein the carbon nanotubes, metallic nanowires or a combination thereof, form a continuous two-dimensional membrane which wraps around particles of said particulate active material and acts as a scaffold to hold the particulate active material in place to form said segregated network.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0052] The invention will be more clearly understood from the following description of an embodiment thereof, given by way of example only, with reference to the accompanying drawings, in which:—

[0053] FIG. 1 illustrates fabrication of hierarchical composite electrodes. (A) Composite electrode fabrication by mixing aqueous CNT dispersions with particulate active material powders and slurry-casting onto substrates to yield robust, flexible electrodes. (B) Schematic of resultant hierarchical Si/CNT composite electrode, showing formation of 2D CNT-membranes between micron-sized Si (μ-Si) particles. (C-F) Cross-sectional SEM images of (C-E) μ-Si (5 μm)/CNT composite anodes with mass fraction (M.sub.f) varying from 0.5-7.5 wt % with (F) a standard composite of n-Si (80 nm)/CNT (M.sub.f=7.5 wt %) for comparison. For the segregated network composites, the development of nanotube membranes (arrows) can be clearly seen as M.sub.f increases (C to E). The schemes below illustrate the evolution of the CNT-membranes as the M.sub.f is increased and highlight the difference between normal and segregated network composites. (G-H) High magnification cross-sectional SEM images of μ-Si/7.5 wt % CNT composite anode showing a μ-Si particle wrapped by 2D CNT-membranes which consist of entangled, van der Waals bonded networks of CNT bundles/ropes. Clearly, the membranes are quasi-continuous and so can localize the silicon particles yet contain small (˜10 nm) pores which allow free movement of electrolyte.

[0054] FIG. 2 illustrates basic material/electrochemical characterizations. (A) SEM images of Si particles with various mean particle sizes (2-45 μm). (B) Representative stress-strain curves for 2 μm Si/CNT composite anodes with various CNT M.sub.f. For comparison, the curve for a 2 μm Si/PAA/CB composite (no CNT, composition given in panel) is also shown. (C) Tensile toughness and electrical conductivity of various Si/CNT composite anodes plotted versus CNT M.sub.f. In each case, the orange line indicates the properties of a traditional anode composed of 2 μm-Si/PAA/CB (composition given in panel). (D) Plot of conductivity versus toughness for Si/CNT composites compared to traditional of 2 μm-Si/PAA/CB composites (compositions given in panel). (E) First galvanostatic charge-discharge (GCD) curves of 2 μm Si/CNT composite anodes with various CNT M.sub.f, ranging from 0.5-10 wt %. Mass loading (M/A) for all electrodes are ˜3 mg/cm2. (F) First delithiation capacity (normalized to Si mass, C/MSi) of Si/CNT composites as a function of CNT M.sub.f. With addition of >2 wt % CNT, all composites anodes approach to the theoretical Si capacity (3579 mAh/g, dashed line). (G) First delithiation capacity for CNT composite anodes (with optimized CNT M.sub.f of 7.5 wt %, mg/cm.sup.2) and traditional anodes (Si/PAA/CB=80:10:10, M/A=1-2 mg/cm2) plotted versus Si particle size. Dash line indicates theoretical Si capacity.

[0055] FIG. 3 illustrates the full mechanical data for Si/CNT composites and controlled sample prepared using conventional PAA binder (2 μm Si/10% PAA, orange dash lines). (A) Electrical conductivity (black open circles, left y-axis) and tensile toughness (i.e. tensile energy density required to break film, blue square, right y-axis) of μ-Si anodes (2 μm Si) prepared by a traditional polymeric binder (PAA) and carbon black (CB) combination. Here CB M.sub.f (0-10 wt %) was varied while PAA M.sub.f was fixed at 10 wt %. Electrical conductivity is improved as the CB M.sub.f increases (at a fixed 10 wt % PAA) while toughness is decreased dramatically, showing the trade-off relationship between conductivity and mechanical properties. The mechanical properties of the samples with CB M.sub.f>5 wt % was too low to measure. (B) Universal tensile stress, (C) Young's Modulus, and (D) strain at break of the samples versus CNT wt %. Similar to the electrical conductivity, with the addition of CNT, all the mechanical properties have been dramatically improved. It is clear that all of the mechanical properties of the CNT-based composites are much higher than those for the conventional electrode (orange dash lines) at the similar binder composition. For example, 2 μm Si/CNT composite with 7.5 wt % CNT displays ×10 higher values for all the mechanical properties than 2 μm Si/PAA (10 wt % PAA) electrode. Furthermore, much smaller amounts of CNT (1-2 wt %) are required to reach the corresponding level of the mechanical properties for the 2 μm Si/PAA (10 wt % PAA) electrode. (E) Bar chart comparing toughness/electrical conductivities for the traditional anodes and μ-Si/CNT composite anodes with various compositions.

[0056] FIG. 4 illustrates a stability and performance-cost evaluation for Si/CNT anodes with various Si particle sizes. (A) Cycling performance of Si/CNT composite anodes with various Si sizes and a CNT Mf of 7.5 wt %. A traditional 2 μm-Si/PAA/CB (80:10:10) anode is shown for comparison. (B) Si specific capacity of the composite anodes plotted versus Si particle size. (C) Material and resultant electrode costs with different Si particle sizes. For simplicity but fair comparison, all the material costs were surveyed based on the similar lab-scale value (all ˜100 g base). The electrode costs (Si/CNT composites or Si/PAA/CB anodes) are calculated from their electrode composition (Si/CNT=92.5:7.5 or Si/PAA/CB=80:10:10). (D) Cost-effectiveness of composite electrodes as a function of Si particle size. (E-F) SEM images of (E) 2 μm Si particles and (F) a cross section of a composite anode fabricated from 2 μm Si/7.5 wt % CNT.

[0057] FIG. 5 illustrates the electrochemical characterization of μ-Si/CNT anodes with high mass loading. In all composite anodes, 2 μm Si was used with optimized CNT Mf of 7.5 wt %. (A) Photos comparing our composite anode and traditional 2 μm-Si/PAA/CB (80:10:10) anode. The traditional anodes show crack formation at thicknesses above their CCT (98 μm), while composite anodes display very high CCT (>>300 μm) allowing the formation of very thick electrodes. The cross-sectional SEM image shows the highest loading composite anode (Thickness=310 μm and M/A=21.5 mg/cm.sup.2). (B) Electrode thickness as a function of M/A for μ-Si/CNT composite anodes. The dashed line shows the upper thickness limit for 2 μm-Si/PAA/CB anodes. (C) First GCD curves of μ-Si/CNT composite anodes at a ˜ 1/30 C-rate for a range of M/A between 2.3-14.3 mg/cm.sup.2. The composite anodes with M/A>15 mg/cm.sup.2 couldn't be tested in half-cells, due to the insufficient Li supply from the Li-metal counter electrode. (D) Bottom: C/A of the μ-Si/CNT composite anodes as a function of M/A. High-performance literature data are included for comparison with the details indicated in Table 2. Top: Si specific capacity (normalized to Si mass, C/MSi) of composite anodes with various M/A. The dash lines indicate theoretical Si capacity of 3579 mAh/g. (E) Half-cell cycling performance for various M/A composite anodes at ˜ 1/15 C-rate. (F) Post-mortem SEM images of the cycled composite anode. Inset photo shows severe degradation of Li-metal after cycling, while the composite anode maintained its structural integrity. (G) C/A of μ-Si/CNT composite anodes with various M/A depending on areal current density (I/A).

[0058] FIG. 6 illustrates voltage profiles of high C/A μ-Si/CNT composite anode in a half-cell, and the photo of Li-metal counter electrode after cycling. Above 10 cycles, the half-cell made of high C/A electrode (>30 mAh/cm.sup.2) suddenly stopped working normally; the potential of the cell was not rising anymore during the delithiation process. After disassembling these cells, a thick/brittle black film was observed on the surface of the Li-metal counter electrode. This Li-metal degradation (corrosion) possibly limited the cyclability in the high C/A electrodes.

[0059] FIG. 7 illustrates the electrical and mechanical properties of NMC/CNT composites (NMC=Lithium Nickel Manganese Cobalt oxide, for example in ratio LiNi.sub.0.8Mn.sub.0.1Co.sub.0.1O.sub.2) and controlled samples prepared by conventional PVDF binder with CB combination. (A) Electrical conductivity (a) of NMC/CNT composites and controlled samples as a function of CNT wt % (or PVDF/CB wt %). Upon the addition of CNT, electrode conductivity has been increased significantly. It should be emphasized that the claimed NMC/CNT composites show much higher conductivity than the conventional electrodes using PVDF/CB at the equivalent composition (NMC/10 wt % CNT=3200 S/m and NMC/5 wt % PVDF/5 wt % CB=10 S/m, ×300 higher). Also, a very small amount of CNT can replace the large portion of PVDF/CB to reach a similar level of conductivity (NMC/0.2 wt % CNT=64 S/m and NMC/12.5 wt % PVDF/12.5 wt % CB=53 S/m). (B) Percolation plot showing the electrode conductivity versus ϕ−ϕ.sub.c,e, where ϕ is the CNT volume fraction,

ϕ.sub.CNT=ρ.sub.composite.Math.M.sub.f,CNT/ρ.sub.CNT  (1)

where ϕ.sub.c,e is the electrical percolation threshold (critical volume fraction at which the first conducting path is formed in the matrix). The line is a fit to the percolation scaling law,

σ=σ.sub.0(ϕ−ϕ.sub.c,e).sup.n.sup.e  (2)

where σ.sub.0, and n.sub.e are the conductivity of the CNT film alone, and the electrical percolation exponent, respectively. The percolation equation fits very well, giving the values of ϕ.sub.c,e=0.06 vol % (i.e., 0.054 wt %), and n.sub.e=1.06. The percolation threshold is much lower than the value observed from CB (ϕ.sub.c,e=3-25 wt %), supporting well the reason for the much higher electrical conductivity than the conventional electrode even using a very small amount of CNTs.

[0060] The conductivities discussed above were measured in the plane of the electrode as is relatively common. However, it is known that out-of-plane conductivity is more relevant to the performance of battery electrodes. Out-of-plane conductivity is seldom reported as it is harder to measure than in-plane conductivity. Out-of-plane conductivity for a subset of 2 um Si/CNT composites. Out-of-plane conductivities of 0.2 S/m for Mf=1% and ˜1 S/m for Mf˜10% were measured. This result is important because once electrode out-of-plane conductivity reaches 1 S/m, performance is optimized in virtually all circumstances, even for very thick electrodes. Here, optimized means that performance is not degraded due to the additional electrical resistance associated with thick electrodes. This is also shown in FIGS. 2C and 2D, where the segregated network of the electrode of the claimed invention shows higher toughness and conductivity at lower Mf than the non-segregated network (80 nm Si).

(C) Universal tensile stress, (D) Young's Modulus, (E) strain at break, and (F) tensile toughness (energy absorbed up to break) of the NMC samples versus CNT wt % (or PVDF/CB wt %). (G) Mechanical percolation plot showing toughness increase versus ϕ−ϕ.sub.c,m where ϕ.sub.c,m is the mechanical percolation threshold and T.sub.0 is the toughness of CNT-free film. The lines represent percolation-like scaling behavior via,

T=T.sub.0+T.sub.net(ϕ−ϕ.sub.c,m).sup.n.sup.t  (3)

[0061] where T.sub.net is the toughness of CNT film, and n.sub.t is the mechanical percolation exponent, respectively. Fitting the toughness data to percolation theory yields: ϕ.sub.c,m=0.12 vol % (i.e. 0.1 wt %), n.sub.t=1.6. Similar to μ-Si/CNT composites, NMC/CNT composites show much higher mechanical properties than those for the conventional electrodes at the equivalent compositions. For example, all the mechanical properties for NMC/10 wt % CNT were >100 times greater than the traditional electrodes at the equivalent electrode compositions (NMC/5 wt % PVDF/5 wt % CB), or even ˜5 times higher at the very low CNT contents (0.2-0.5 wt %) used in electrodes. These results are important as increases in toughness such as these are required to enable the production of very thick (>100 um) crack free electrodes.

[0062] FIG. 8 illustrates the electrochemical performance of NMC/CNT cathodes in half-cell measurement. (A) Discharge rate-capability of NMC/CNT cathodes with various CNT M.sub.f(0.25-2 wt %, all cathode M/A=˜20 mg/cm.sup.2). For NMC, much lower CNT M.sub.f(0.25-2 wt %) have been employed than in the anode system (˜7.5 wt %) of the claimed invention, under the consideration of CNT's volume fraction (CNT vol %) in the electrodes. Since the NMC-based cathodes typically have higher electrode density (˜2 g/cc) than Si-based anodes (˜0.7 g/cc), which could lead to the higher CNT vol % at the equivalent CNT wt %. Interestingly, the electrochemical performance of the claimed NMC/CNT cathodes does not obviously change above 0.5 wt % CNT as shown in (A). At the lowest current density, all of 0.5-2 wt % CNT electrodes display high C/M of ˜190 mAh/g, close the theoretical capacity of NMC (NMC811=˜200 mAh/g up to 4.3 V vs Li/Li.sup.+), then showing similar rate-performance at higher current densities. This might be due to the extremely low electrical percolation threshold of CNT (i.e., 0.054 wt %, FIG. 7), thus providing sufficient conductivity above 0.5 wt %. (B) Top: Bar chart comparing tensile toughness of NMC/CNT and NMC/PVDF/CB. Bottom: Electrode thickness as a function of M/A for NMC/CNT composite cathodes. (C) Cross-sectional SEM image of the highest loading NMC/CNT composite. 0.5 wt % CNT was used to build up thickness, thus high C/A electrodes. The toughness for NMC/CNT composite cathode was >10 times greater than the traditional electrodes even at such a lower CNT content. This mechanical reinforcement increases the CCT, allowing the production of mechanically robust electrodes with thicknesses as high as ˜800 μm for NMC/CNT, much larger than achievable with traditional binders (<175 μm). (D) Second charge/discharge profiles of the NMC/CNT composite cathodes at a ˜ 1/20 C-rate for a range of M/A between 20-155 mg/cm.sup.2. (E) Discharge C/A of the composite cathodes as a function of M/A. The C/A of NMC/CNT cathodes scaled linearly with electrode M/A over the entire thickness range, reaching 30 mAh/cm.sup.2, showing superlative performance than any of other studies. High-performance literature data are included for comparison with the details indicated in Table 4. The black stars (Li-cathode Lit 1) indicate high-C/A cathodes prepared by slurry-casting method and grey filled stars (Li-cathode Lit 2) indicate high-C/A cathodes prepared by special techniques such as using specific substrates (porous foam) or non-scalable/or complicated process (vacuum-filtration, template, sintering methods etc.). The slope in (E) indicates gravimetric capacity of ˜190 mAh/g, confirming high electrochemical utilization, even at the high thicknesses. (F) C/A of NMC/CNT composite cathodes with various M/A depending on areal current density.

[0063] FIG. 9 illustrates the electrochemical performance of full-cell lithium-ion batteries made by pairing μ-Si/CNT composite anodes with NMC/CNT composite cathodes. Total anode/cathode masses, (M/A)A+C varied from 47 to 167 mg/cm.sup.2, with full-cell C/A, ranging from 8 to 29 mAh/cm.sup.2. (A) Second discharge voltage-capacity curves for full-cells of varying (M/A)A+C tested at ˜ 1/15 C-rate. (B) Cycling stability of full-cells with various (M/A)A+C (˜ 1/15 C-rate). Commercial high-energy batteries typically have a maximum full-cell C/A of ˜4 mAh/cm.sup.2, as indicated by the violet hatched area. (C) Rate performance of full-cells with various (M/A)A+C with a traditional NMC-graphite full-cell for comparison. (D) Bar chart showing the contributions of active and inactive components as (M/A)C+A is increased, with data for the traditional full-cell from (C) shown for comparison. The low-rate areal capacity of the cell is given in the x-axis legend. (E) Specific energy as a function of full-cell C/A (this work=black stars) with various literature data for comparison (open symbols, see Table 6). The dashed lines are plots of equation 1.

[0064] FIG. 10. Cycling performance of high C/A full-cell (˜11 mAh/cm.sup.2) at a different rate. Right y-axis indicates Si anode specific capacity in full cells, showing high utilization of Si.

DETAILED DESCRIPTION OF THE DRAWINGS

[0065] Here, it is shown that the production of very thick electrodes which retain almost all of their intrinsic capabilities can be achieved via simultaneously boosting the electrical/mechanical properties of granular electrode materials by using, for example, carbon nanotubes (CNT), specifically in the form of segregated networks, as both binder and conductive additive, without any additional polymer or CB. By adding nanotubes (or metallic nanowires or a combination thereof) to high-performance anode/cathode materials such as silicon and LiNi.sub.xMn.sub.yCo.sub.zO.sub.2(NMC), a new type of hierarchical composite is shown where the nanotubes arrange themselves into networked membranes that envelop the active material particles. These networks significantly improve the mechanical properties, allowing the fabrication of crack free, thick electrodes, and ensure their stability, even during repeated charge/discharge. At the same time the electrode conductivity is dramatically increased, facilitating fast charge distribution, even in thick electrodes. The production of extremely thick electrodes (up to 2000 μm) with C.sub.SP approaching theoretical values for each electrode material, enables the production of full cells with areal capacities and specific energies considerably higher than any previous reports. The production involves simple and scalable production techniques, which can be applied to both anodes and cathodes and is compatible with any high-performance electrode material.

[0066] Materials and Methods

[0067] Slurry-Casting

[0068] The hierarchical composite electrodes were prepared via a conventional slurry-casting method using a uniform CNT aqueous dispersion (0.2 wt % SWCNT in water, ˜0.2 wt % PVP as a surfactant, Tuball, OCSiAl) and battery active materials (AMs) without adding any additional polymeric binder or carbon black (CB).

[0069] For anodes, the uniform CNT dispersion was mixed with micron-sized Si powder (μ-Si) with a range of particle sizes (1-3 μm: denoted as 2 μm and 5, 10, 30, 45 μm size, all purchased from US Research Nanomaterials) and ground into a uniform slurry using a mortar and pestle. The CNT mass fraction, (M.sub.f) in the resultant electrodes was controlled in the range of 0.05-20 wt % by simply changing the mass ratio between the μ-Si and CNT dispersion. For instance, 8 ml of CNT dispersion was mixed with 200 mg of μ-Si in order to obtain the electrode with 7.5 wt % CNT. Then the slurry was cast onto copper (Cu) foil using a doctor blade, then slowly dried at 40° C. for 2 hours and followed by vacuum drying at 100° C. for 12 hours. Alternatively, the doctor blade film formation step could be replaced by a vacuum filtration step. To remove a surfactant from the as-received CNT dispersion (˜0.2 wt % PVP), the dried electrodes were then heat-treated in Ar gas at 700° C. for 2 hours. By changing the height of doctor blade (200-2000 μm) while keeping the CNT M.sub.f, electrodes with various thickness were obtained, ranging from 30-310 μm (M/A=0.9-21.5 mg/cm.sup.2).

[0070] For cathodes, NMC (LiNi.sub.0.8Mn.sub.0.1Co.sub.0.1O.sub.2, MTI Corp.) was employed to mix with the uniform CNT aqueous dispersion. Typically, 5 ml of CNT was ground with 2 g of NMC to obtain the electrode with 0.5 wt % CNT. The resultant slurry was cast onto aluminium (Al) foil and dried at the same manner. CNT M.sub.f was controlled to be in the range between 0.01-10 wt % and varied electrode thickness, ranging from 40-800 μm (M/A=6-155 mg/cm.sup.2). The composite anode/cathode were denoted as “μ-Si/CNT” and “NMC/CNT”, respectively.

[0071] For the sake of comparison, nano-sized Si (n-Si) with different sizes (˜25 nm and ˜80 nm, US Research Nanomaterials) were employed to fabricate corresponding anodes by mixing with CNT dispersion in desired compositions and thicknesses.

[0072] In addition, traditional electrodes were also prepared using CB (Timical Super C65, MTI Corp.) and conventional binders, either PAA for Si anode or PVDF (EQ-Lib-PVDF, MTI Corp) for NMC cathode. Electrode thickness and composition were also controlled in the same manner.

[0073] Material Characterization

[0074] The morphology and micro-structure of Si/CNT anodes (or NMC/CNT cathodes) were examined by FE-SEM (Zeiss Ultra Plus, Zeiss) in a high vacuum mode with an acceleration voltage of 5 keV. The mass (M) and thickness (t) of the electrodes were determined using a microbalance (MSA6, Sartorious) and a digital micro-meter after subtracting the mass or thickness of the Al/Cu foils.

[0075] The structural properties of samples were characterized by X-ray diffraction (XRD, Bruker D5000 powder diffractometer) with a monochromatic Mo Kα radiation source (A=0.15406 nm). XRD patterns were collected between 10°<θ<80°, with a step size of 2θ=0.05° and a count time of 12 s/step.

[0076] Raman spectra of composite electrodes were acquired using a Witec Alpha 300 R with a 532 nm excitation laser and a spectral grating with 600 lines mm.sup.−1. Characteristic spectra were obtained by averaging 20 discrete point spectra for each sample. Raman maps were generated for AM/CNT composites by acquiring 120×120 discrete spectra over an area of 60×60 μm. Maps representing the presence of CNT and AM (either Si or NMC) were generated by mapping the intensity of the CNT G band and the AM's characteristic band (Si at 520 cm.sup.−1 or NMC A.sub.1g band).

[0077] The electrical conductivity of electrodes was measured using a four-point probe technique. The samples were prepared by the same slurry-casting method but they were coated onto a glass plate instead of Al/Cu foils to exclude the substrates' conductivity. Then, four parallel contact lines were deposited on the electrode surface using silver paint (Agar Scientific). The resistance of samples was measured using a Keithley 2400 source meter. The conductivity of samples was then calculated using the samples' geometric information (x-y length and thickness) obtained by digital caliper/micro-meter. The mechanical measurements were conducted from free-standing samples using a Zwick Z0.5 Pro-Line Tensile Tester (100 N Load Cell) at a strain rate of 0.5 mm/min. The films were prepared by simply peeling off the electrodes from the substrate. Each data point was obtained by averaging the results from four measurements.

[0078] Electrochemical Characterization

[0079] The electrochemical properties of the electrodes were investigated using 2032-type coin cells (MTI Corp.) assembled in an Ar-filled glovebox (UNIlab Pro, Mbraun). Each working electrode was punched into discs with diameter=12 mm. A Celgard 2320 was used as the separator for all coin cells.

[0080] For the half-cell electrochemical characterisation, the coin cells were assembled by pairing the working electrode with a Li-metal disc (diameter: 14 mm, MTI Corp.), the latter was used as the counter/reference electrode. 1.2 M lithium hexafluorophosphate (LiPF.sub.6) in ethylene carbonate/diethyl carbonate/fluoroethylene carbonate (EC/DEC/FEC, 3:6:1 in v/v/v, BASF) with 2 wt % vinylene carbonate (VC, Sigma Aldrich) was used as the electrolyte for half-cell measurement.

[0081] The electrochemical properties of the Si anodes were measured within a voltage range of 0.005-1.2 V using Galvanostatic charge/discharge mode by a potentiostat (VMP3, Biologic). The NMC cathodes were measured within a voltage range of 3-4.3 V in the same manner. It should be noted that the terms between charging/discharging are based on the full-cell LiB system. For the anode, charging/discharging correspond to the lithiation/delithiation process, respectively. The areal capacities (C/A) of the electrodes were obtained by dividing the measured cell capacity by the geometric electrode area (1.13 cm.sup.2). To investigate the maximum accessible C/A of the electrodes, the cells were tested at a reasonably slow condition of 1/30 C-rate. The cyclabilities of the electrodes were evaluated at 1/15 C-rate after initial formation cycle at 1/30 C-rate. The discharge rate-capabilities of the electrodes were investigated using asymmetric charge/discharge conditions; the cells were charged at a fixed 1/30 C-rate then discharged at varied rates. For the post-mortem analysis, the cycled cells were carefully disassembled inside a glove box under inert atmosphere. The cycled electrodes were then rinsed with dimethyl carbonate (DMC) several times and dried inside the glove box at room temperature.

[0082] The full-cells were assembled by pairing our μ-Si/CNT anodes with NMC/CNT cathodes with various C/A (or M/A). The same sized cathode/anode disc (1.13 cm.sup.2) were used to match the C/A of both electrodes, which were previously determined in the half-cell experiments. For full-cells, 1.2 M LiPF.sub.6 in ethylene methyl carbonate/fluoroethylene carbonate (EMC/FEC, 95:5 in wt %, BASF) was used as the electrolyte. The N/P ratio, defined by the capacity ratio between the anode and cathode, was balanced to be ˜1.1 (See Table 5 for the details of cathodes/anodes in full-cells). The assembled full-cells were then cycled at 1/15 C within a voltage range of 2.5-4.3 V after the initial formation cycle at 1/30 C-rate. The total C/A of the full-cell, (full-cell C/A), was obtained by dividing the measured cell capacity by the geometric electrode area (1.13 cm.sup.2). The rate capabilities of the full cells were investigated using asymmetric charge/discharge conditions; the full cells were charged at ˜ 1/30 C-rate then discharged at varied discharge current densities. For the sake of comparison, a traditional full-cell (C/A=˜3.5 mAh/cm.sup.2) was also assembled and tested in the same manner by pairing the NMC cathode (C/A=3.5 mAh/cm.sup.2) and graphite anode (C/A=3.8 mAh/cm.sup.2) prepared by CB-binder combination.

TABLE-US-00001 TABLE 1 Literature comparison of high areal capacity Li-ion battery electrodes Electrode areal Electrode type Method capacity Ref Anode Si nanowire- Vacuum filtration 11 mAh cm.sup.−2 Adv Energy Mater graphene (Non-scalable) 6, 1600918-n/a composite (2016). Si-graphene Vacuum filtration 6.5 mAh cm.sup.−2 Nano Lett 15, composite (Non-scalable) 6222-6228 (2015) Si nanowire CVD growth 7.1 mAh cm.sup.−2 J Power Sources (Non-scalable) 316, 1-7 (2016) Si nanowire CVD growth 15 mAh cm.sup.−2 Nano Lett 15, (Non-scalable) 3907-3916 (2015) Si graphene CVD growth 8.3 mAh cm.sup.−2 Energ Environ Sci composite (Non-scalable) 9, 2025-2030 (2016) Si nanowires CVD growth 9 mAh cm.sup.−2 Sci Rep-Uk 6 (Non-scalable) (2016) Cathode LiFePO.sub.4 Slurry-coating onto porous 8.4 mAh cm.sup.−2 J Power Sources Al foam 334, 78-85 (2016) (Using special substrate) LiFePO.sub.4 Slurry-coating onto porous 8.8 mAh cm.sup.−2 Rsc Adv 5, 16702- metal foam 16706 (2015) (Using special substrate) CNF-CNT- Vacuum-filtration 10.5 mAh cm.sup.−2 Adv Funct Mater LiFePO.sub.4 (Non-scalable) 25, 6029-6040 (2015) NCM111 Slurry-coating onto porous 12.5 mAh cm.sup.−2 J Power Sources metal foam substrate 196, 8714-8718 (Using special substrate) (2011) LiCoO.sub.2 Magnetic templating 12~13.5 mAh cm.sup.−2 Nature Energy 1, (Complicated/non-scalable 16099 (2016) process) LiFePO.sub.4 coated Coating onto CNT foam ~26 mAh cm.sup.−2 Adv Energy Mater onto conductive (Using special substrate) 1, 1012-1017 CNT textile (2011) LiCoO.sub.2 Mechanically pressing method 49 mAh cm.sup.−2 Adv Mater 22, (Complicated/non-scalable E139-+ (2010) process) Full Cell NMC111 cathode Slurry-coating onto metal 10.5 mAh cm.sup.−2 J Power Sources Graphite anode foam (Using special 196, 8714-8718 substrate) (2011)

[0083] Results

[0084] To produce high-performance electrodes at low cost, micron-sized silicon (μ-Si) particles were chosen as the active material (AM). Such particles combine the high specific capacity of silicon (3579 mAh/g, maximum metastable alloying composition of Li.sub.15Si.sub.4 at ambient temperature) with a cost that is much lower than silicon nanoparticles (n-Si). However, μ-Si is rarely used due to stability problems. Here it is shown that μ-Si, or indeed other electrode materials, can be fabricated into high-performance composite electrodes by replacing traditional combinations (i.e. polymeric binder and CB-conductivity enhancer) with low-loading networks of CNTs. Importantly, these composite electrodes are produced by a simple, industry-compatible slurry-casting technique, whereby mixing a single-wall CNT aqueous dispersion with μ-Si to form a uniform viscous slurry, allows direct casting onto Al/Cu substrates to yield robust composite films (FIG. 1A). The CNTs could also be replaced by, or combined with, metallic nanowires.

[0085] These composites contain CNT networks which are very different both to those found in polymer-nanotube composites and those typically reported in papers on battery electrodes. Since the AM particle size (>1 μm for μ-Si) is larger than the nanotube length (˜1 μm), such composites cannot form standard nanotube networks. Rather, the excluded-volume associated with the particles drives the spontaneous formation of a segregated network, where the CNTs spontaneously form networked 2-dimensional membranes which wrap and interconnect the AM particles (FIG. 1B), even at extremely low CNT mass-fractions (M.sub.f). Cross-sectional SEM images of μ-Si/CNT (here 5 μm Si particles) anodes at the different CNT M.sub.f show the progressive development of 2D CNT-membranes, with hierarchical structure appearing at ˜1 wt % and membranes becoming progressively denser/thicker as more CNTs are added (FIG. 1C-E). Critically, such hierarchical structures do not form for composites containing small particles (FIG. 1F) and clearly require large particle-size/nanotube-length ratios. High-magnification imaging shows the membranes to effectively wrap the Si particles and consist of entangled, van der Waals bonded networks of CNT bundles/rope (FIG. 1G-H). Such membranes are expected to be particularly useful in battery electrodes due to their ability to simultaneously enhance conductivity and mechanical toughness, facilitate particle expansion as well as localizing Si fragments in the event of pulverization while allowing easy access of electrolyte ions.

[0086] Traditional polymer/CB-loaded battery electrodes combine moderate electrical conductivity with relatively poor mechanical toughness (toughness has been linked to electrode stability). Importantly, in Si/polymer/CB composite electrodes, the inventors found conductivity and toughness to be anti-correlated, making it impossible to prepare conductive yet tough electrodes (see FIG. 3). However, because of the excellent electrical and mechanical properties of nanotube networks, the segregated-network composites of the invention are expected to display much greater electrical and mechanical performance. Composites of CNT mixed with both μ-Si and n-Si particles were prepared for comparison (size range, 20 nm to 45 μm, see FIG. 2A), in each case varying the CNT M.sub.f. Both tensile toughness and electrical conductivity displayed very large increases at relatively low loading levels (FIG. 2B-C and see full mechanical data in FIG. 3). Importantly, the CNT loading required to obtain a given toughness or conductivity value fell with increasing silicon particle size as would be expected for segregated network composites. Toughness and conductivity for Si/CNT composites were ×500 and ×1000 times greater than the traditional electrodes at the near equivalent compositions while Si/CNT composites showed conductivity/toughness combinations many order magnitudes better than traditional composites (FIG. 2D).

[0087] These composites were found to perform very well as lithium-ion battery anodes (FIG. 2E). Interestingly, for different Si particle sizes, the 1.sup.st-cycle delithiation capacity (normalized to Si mass, C/M.sub.Si) versus CNT content data (FIG. 2F) followed a master curve, increasing rapidly before saturating very close to the theoretical capacity of Si (3579 mAh/g) for M.sub.f above ˜2 wt %. Near-theoretical values of C/M.sub.Si (FIG. 2G) with very high 1st Columbic efficiencies of 85-90% were found for all particle sizes once M.sub.f>2 wt %. This contrasts with traditional Si/polymer/CB anodes which showed a large fall-off in the high 1.sup.st cycle capacity as the Si particle size was increased (FIG. 2G). Anodes based on Si particles with sizes as high as 45 μm have never before been observed to approach theoretical capacity, demonstrating the superiority of the segregated network.

[0088] While all composite anodes were much more stable than traditional polymer/CB-loaded anodes, a significant fall-off in capacity with cycle number for larger μ-Si particle sizes was observed (FIG. 4A). However, the 20.sup.th-cycle capacity was found to remain very close to the theoretical capacity up to a particle size of 2 μm after which a significant degradation occurred (FIG. 4B). While this implies that small particles perform better, materials cost must also be considered. The cost of Si particles falls significantly with particle size (FIG. 4C) while, as low-cost CNTs are used, the total electrode cost is not significantly greater than Si/polymer/CB anodes. This allows one to calculate the charge stored per electrode cost for Si/CNT (7.5 wt %) anodes for each particle size as shown in FIG. 4D. This clearly shows the 2 μm sized Si particles (see FIG. 4E-F for SEM images) to be the most cost-effective material as calculated from their electrode composition (Si/CNT=92.5:7.5 or Si/PAA/CB=80:10:10). It is worth noting that the micro-sized Si particles roughly ×10-fold less cost than the nano-sized Si products due to the simple/scalable manufacturing processes, thus resulting in a great advantage for the cost-effectiveness.

[0089] At this point, spontaneously formed segregated network composites of 2 μm Si particles mixed with CNT have been shown herein to display high conductivity, toughness and capacity without the high cost associated with nanoscale active materials. Here, these properties are utilized to achieve high-performance anodes. As described above, high areal capacity (C/A) requires large specific capacity (C/M) coupled with high mass loading (M/A). Importantly, the high toughness of the claimed composites should lead to significant increases in CCT. The measurements showed a traditional μ-Si/polymer/CB combination with low toughness to display a CCT of ˜98 μm, leading to severe cracking of thicker films (FIG. 5A). However, the enhanced toughness of μ-Si/CNT composites (>500-fold higher) leads to high CCTs, allowing the production of anodes with thickness in excess of 300 μm (cathode thickness >1000 μm), without any cracking (FIG. 5A).

[0090] This allows the production of extremely thick μ-Si/CNT anodes with record C/A of up to 45 mAh/cm.sup.2 (FIG. 5C). Importantly, the C/A of the claimed composite anodes scaled linearly with mass loading over the entire thickness range (bottom in FIG. 5D) reaching values well beyond the state-of-the-art (comparison with open stars and see literatures in Tables 2 and 3).

TABLE-US-00002 TABLE 2 Literature comparison of the C/A for Si-based anodes. Other details such as the method, electrode composition, mass loading and specific capacity, are also included. For the M/A, the values were sorted based on the total electrode mass (Si + binder + conductive agent, M.sub.Total/A,) as well as on the only active material mass (M.sub.Si/A). Specific capacity values are presented in a same manner (both C/M.sub.Total and C/M.sub.Si). The first anode of the first line (in bold), is an anode for the claimed invention. Mass loading Max. areal Fabrication Electrode (M.sub.Total/A and Specific capacity capacity method composition M.sub.Si/A) (C/M.sub.Total and C/M.sub.Si) (C/A) Slurry-casting method μ-Si/CNT μ-Si:CNT = Total: 14.3 mg/cm.sup.2 ~3150 mAh/g @ 0.03 C 45.4 mAh/cm.sup.2 composite by 92.5:7.5 (μ-Si: 13.2 mg/cm.sup.2) (μ-Si: ~3300 mAh/g) slurry-casting Ca-Alginate Si:Ca-Alginate:CB 5.7 mg/cm.sup.2 2416 mAh/g @ 0.05 C 14 mAh/cm.sup.2 binder 70:15:15 (Si: 4 mg/cm.sup.2) (Si: 3450 mAh/g @ 1.sup.st cycle Si: 3150 mAh/g @ 2.sup.nd cycle) PAA-grafted Si Si-PAA:PAA:AB = 5.77 mg/cm.sup.2 2379 mAh/g @ 0.05 C 13.7 mAh/cm.sup.2 78:2:20) (Si: 4.5 mg/cm.sup.2) (Si: ~3050 mAh/g @ 0.05 C) Mesoporous Si Si:CB:Na-CMC = 10 mg/cm.sup.2 600 mAh/g @ 0.06 mA cm.sup.−2 6 mAh/cm.sup.2 sponge 40:40:20 (Si: 4 mg/cm.sup.2) (Si: 1500 mAh/g) Graphene coated Gr-Si:Li-PAA = 3.125 mg/cm.sup.2 1856 mAh/g @ 0.5 C 5.8 mAh/cm.sup.2 Si by CVD 80:20 (Gr-Si: 2.5 mg/cm.sup.2) (Gr-Si: 2320 mAh/g) Carbon coated Si C—Si:CB:Na-alginate = 7.14 mg/cm.sup.2 630 mAh/g @ 0.1 C 4.5 mAh/cm.sup.2 70:15:15 (C—Si: 5 mg/cm.sup.2) (Gr-Si: ~900 mAh/g) PAA-PVA gel Si:CB:PAA-PVA binder = 4 mg/cm.sup.2 1075 mAh/g @ 4 A/g 4.3 mAh/cm.sup.2 polymer binder 60:20:20 (Si: 2.4 mg/cm.sup.2) (Si: 1791 mAh/g) Self-healing Si:CB:binder = 2.4 mg/cm.sup.2 1733 mAh/g @ 0.1 mA/cm.sup.2 4.2 mAh/cm.sup.2 binder 63.3:3.3:33.3 (Si: 1.6 mg/cm.sup.2) (Si: 2600 mAh/g) PAA/PANI IPN Si:PAA/PANI IPN = 1.6 mg/cm.sup.2 2250 mAh/g @ 0.1 C 3.8 mAh/cm.sup.2 conducting 60:40 (Si: 1 mg/cm.sup.2) (Si: 3750 mAh/g) polymer binder Pomegranate Si:CB:PVDF = 3.9 mg/cm.sup.2 941 mAh/g @ 0.03 mA/cm.sup.2 3.7 mAh/cm.sup.2 structured Si 80:10:10 (Si: 3.12 mg/cm.sup.2) (Si: 1176 mAh/g) Organogel Si:CB:binder = 1.6 mg/cm.sup.2 2215 mAh/g 3.6 mAh/cm.sup.2 electrolyte binder 80:10:10 (Si: 1.3 mg/cm.sup.2) @ 0.07 mA cm.sup.−2 (Si: 2770 mAh/g) PEDOT:PSS + Si:CB:PEDOT:PSS:CMC = 1.5 mg/cm.sup.2 2205 mAh/g @ 0.2 A/g 3.3 mAh/cm.sup.2 CMC binder 70:10:10:10 (Si: 1.05 mg/cm.sup.2) (Si: 3150 mAh/g) SPEEK-PSI-Li Si:CB:SPEEK-PSI-Li 2 mg/cm.sup.2 1650 mAh/g @ 0.2 A/g 3.3 mAh/cm.sup.2 binder 60:20:20 (Si: 1.2 mg/cm.sup.2) (Si: 2750 mAh/g) PEDOT:PSS Si:PEDOT/PSS = 1.5 mg/cm.sup.2 2200 mAh/g @ 0.5 A/g 3.3 mAh/cm.sup.2 conducting 80:20 (Si: 1.2 mg/cm.sup.2) (Si: 2750 mAh/g) polymer Nonfilling carbon Si:CB:PVDF = 2.5 mg/cm.sup.2 1281 mAh/g @ 0.05 mA/cm.sup.2 3.2 mAh/cm.sup.2 coated porous Si 80:10:10 (Si: 2.01 mg/cm.sup.2) (Si: 1602 mAh/g) Si nanocrystal Si:CB:PVDF = 2.14 mg/cm.sup.2 1340 mAh/g @ 0.2 A/g.sup.1 2.9 mAh/cm.sup.2 embedded SiO.sub.x 70:15:15 (Si: 1.5 mg/cm.sup.2) (Si: 1914 mAh/g) nanocomposite Defect abundant Si:graphite:CB:binder = 3.4 mg/cm.sup.2 756 mAh/g @ 0.1 A/g.sup.1 2.7 mAh/cm.sup.2 Si Nanorods 56:14:15:15 (Si: 1.9 mg/cm.sup.2) (Si: 1421 mAh/g) PPyE conducting Si:PPyE = 2 mg/cm.sup.2 1243 mAh/g @ 0.226 mA/cm.sup.2 2.5 mAh/cm.sup.2 polymer 66.6:33.3 (Si: 1.34 mg/cm.sup.2) (Si: 1866 mAh/g) CNT and Si:CNT/PEDOT = 2 mg/cm.sup.2 1100 mAh/g @ 0.2 A/g 2.2 mAh/cm.sup.2 PEDOT:PSS 57:43 (Si: 1 mg/cm.sup.2) (Si: 2180 mAh/g) binder Si-based Si:CB:PVDF = 3.75 mg/cm.sup.2 480 mAh/g @ 0.05 C 1.8 mAh/cm.sup.2 multicomponent 80:10:10 (Si: 3 mg/cm.sup.2) (Si: 600 mAh/g) anodes Self-healing Si:binder:SuperP = 1.5 mg/cm.sup.2 933 mAh/g @ 0.3 A/g 1.4 mAh/cm.sup.2 binder 60:20:20 (Si: 0.9 mg/cm.sup.2) (Si: 1500 mAh/g) Use of special techniques (CVD growth onto foam substrate or vacuum filtration) CVD growth of Si Si film via CVD Si/C fiber: 12.8 ~1172 mAh/g 15 mAh/cm.sup.2 nanowires onto mg/cm.sup.2 @ 0.1 mA cm.sup.−2 carbon fiber foam (Si: 9 mg/cm.sup.2) (Si: ~1666 mAh/g) Si nanowire- Si:graphene = 6 mg/cm.sup.2 1830 mAh/g @ 0.2 A/g 11 mAh/cm.sup.2 graphene 80:20 (Si: 4.8 mg/cm.sup.2) (Si: 2291 mAh/g composite papers @ 0.2 A/g) CVD growth of Si Si film via CVD Si/C fiber: 8.7 Si: 4090 mAh/g 9 mAh/cm.sup.2 nanowires onto mg/cm.sup.2 @ 0.5 mA/cm.sup.2 carbon fiber foam Si: 2.2 mg/cm.sup.2 CVD growth of Si Si film via CVD Si: 3.2 mg/cm.sup.2 Si: 2593 mAh/g 8.3 mAh/cm.sup.2 onto graphene foam @ 0.5 mA/cm.sup.2 DC sputtering Si film via Si: 2.1 mg/cm.sup.2 Si: 3500 mAh/g 7.5 mAh/cm.sup.2 onto Cu foil sputtering @ 0.5 mA/cm.sup.2 CVD growth of Si Si film via CVD Si: 2.47 mg/cm.sup.2 Si: 2874 mAh/g @ 0.02 C 7.1 mAh/cm.sup.2 nano wires Si-graphene Si:graphene = 3.7 mg/cm.sup.2 2745 mAh/g @ 0.8 A/g 6.5 mAh/cm.sup.2 composite by 64:36 (Si: 2.4 mg/cm.sup.2) (Si: 1757 mAh/g) vacuum filtration

TABLE-US-00003 TABLE 3 Cyclability comparison among high C/A Si-anode studies with high C/A (>4 mAh/cm.sup.2), selected from Table 2. The first line in bold is the anode of the claimed invention. Mass loading Fabrication (M.sub.Total/A and Max. areal method M.sub.Si/A) capacity (C/A) Capacity retention μ-Si/CNT Total: 14.3 mg/cm.sup.2 45.4 mAh/cm.sup.2 14.3 mg/cm.sup.2 anode: composite by (μ-Si: 13.2 mg/cm.sup.2) 45 .fwdarw. 40 mAh/cm.sup.2 @ 2.sup.nd slurry-casting (cell dead after 2 cycles due to Li-metal degradation) 10.3 mg/cm.sup.2 anode: 32 .fwdarw. 28 mAh/cm.sup.2 @ 10.sup.th 7.9 mg/cm.sup.2 anode: 24 .fwdarw. 23 mAh/cm.sup.2 @ 10.sup.th 5.7 mg/cm.sup.2 anode: 17 .fwdarw. 15 mAh/cm.sup.2 @ 20.sup.th 3.8 mg/cm.sup.2 anode: 13 .fwdarw. 10 mAh/cm.sup.2 @ 30.sup.th 2.8 mg/cm.sup.2 anode: 8 .fwdarw. 6.5 mAh/cm.sup.2 @ 30.sup.th 0.9 mg/cm.sup.2 anode: 2.7 .fwdarw. 2.4 mAh/cm.sup.2 @ 50.sup.th CVD growth of Si/C fiber: 12.8 mg/cm.sup.2 15 mAh/cm.sup.2 8.63 .fwdarw. 5.26 mAh/cm.sup.2 @ 100.sup.th Si nanowires onto Si: 9 mg/cm.sup.2 carbon foam Ca-Alginate 5.7 mg/cm.sup.2 14 mAh/cm.sup.2 12.5 .fwdarw. 10 mAh/cm.sup.2 @ 50.sup.th binder (Si: 4 mg/cm.sup.2) .fwdarw. 9 mAh/cm.sup.2 @ 100.sup.th Si nanowire- 6 mg/cm.sup.2 11.0 mAh/cm.sup.2 Not shown for high C/A electrode graphene (Si: 4.8 mg/cm.sup.2) composite papers CVD growth of Si: 2.2 mg/cm.sup.2 9 mAh/cm.sup.2 9 .fwdarw. 4 mAh/cm.sup.2 @ 50.sup.th Si nanowires onto carbon fiber foam CVD growth of Si: 2.47 mg/cm.sup.2 7.1 mAh/cm.sup.2 5.3 .fwdarw. 3.3 mAh/cm.sup.2 @ 50.sup.th Si nanowires .fwdarw. 2.5 mAh/cm.sup.2 @ 100.sup.th Si-graphene 3.7 mg/cm.sup.2 6.5 mAh/cm.sup.2 6.5 .fwdarw. 6.2 mAh/cm.sup.2 @ 50.sup.th composite by (Si: 2.4 mg/cm.sup.2) .fwdarw. 5.8 mAh/cm.sup.2 @ 80.sup.th vacuum filtration Mesoporous Si 10 mg/cm.sup.2 ~6 mAh/cm.sup.2 5 .fwdarw. 4.2 mAh/cm.sup.2 @ 35.sup.th sponge (Si: 4 mg/cm.sup.2) Graphene coated 3.125 mg/cm.sup.2 ~5.8 mAh/cm.sup.2 5.5 .fwdarw. 3.9 mAh/cm.sup.2 @ 50.sup.th Si by CVD (Gr-Si: 2.5 mg/cm.sup.2) .fwdarw. 3 mAh/cm.sup.2 @ 100.sup.th PAA-PVA gel 4 mg/cm.sup.2 4.5 mAh/cm.sup.2 4.5 .fwdarw. 4.1 mAh/cm.sup.2 @ 50.sup.th polymer binder (Si: 2.4 mg/cm.sup.2)

[0091] Crucially, this can be achieved while retaining the specific capacity close to its theoretical value (top in FIG. 5D). Such extremely thick electrodes are relatively stable (FIG. 5E), probably because the CNT membrane allows expansion and contraction of the μ-Si without any electrode cracking. Post-mortem analysis after cycling (FIG. 5F) shows that the CNT-membrane has been preserved with a little change in the hierarchical structure, while Li-metal counter electrode shows severe degradation (see Li-metal degradation issue in FIG. 6). From this, it is expected that the CNT membrane will limit the loss of small μ-Si particles which might result from pulverization. Unsurprisingly, for such thick electrodes and large AM particles, some capacity falloff at high rates is not observed (FIG. 5G). However, it is not as significant as might be expected, presumably because the high conductivity associated with the segregated nanotube network allows fast charge distribution.

[0092] The key to the performance enhancements described above lies in the development of the segregated nanotube/nanowire network to give a porous membrane which wraps the AM particles. Such network formation is not limited to μ-Si AM particles but can be achieved for any particulate material with particle size greater than the nanotube length. This has been demonstrated herein for LiNi.sub.0.8Mn.sub.0.1Co.sub.0.1O.sub.2 cathode material (denoted as NMC, see electrical and mechanical properties set out in FIG. 7). The optimized NMC/CNT composite cathodes (M.sub.f=0.5 wt %) also reach theoretical capacity (˜190 mAh/g @ 1/20 C) for the entire thickness range (up to 800 μm, M/A=155 mg/cm.sup.2, see electrochemical characterization in FIG. 8), leading to C/A as high as 30 mAh/cm.sup.2, larger than any other reports (see comparison Table 4).

TABLE-US-00004 TABLE 4 Literature comparison of the C/A for Li-containing metal-oxide cathodes (Li.sub.xM.sub.yO.sub.z, M = Ni, Mn, Co, Fe, etc. or the combination of more than two components). Other details are also included. For the M/A and specific capacity, we sorted out the values based on the total electrode mass (MTotal/A,) as well as on only the active material mass (MAM/A). The composite in the first row (in bold) is the NMC/CNT composite of the claimed invention. Mass loading Fabrication Electrode (M.sub.Total/A and Specific capacity Max. areal method composition M.sub.AM/A) (C/M.sub.Total and C/M.sub.AM) capacity (C/A) Slurry-casting method NMC/CNT NMC811:CNT = Total: 155 mg/cm.sup.2 190 mAh/g @ 1/20 C 29.5 mAh/cm.sup.2 composite by 99.5:0.5 (NMC: ~154 mg/cm.sup.2) (NMC: ~191 mAh/g) slurry-casting Slurry-casted NMC111:CB:graphite:PVDF = 72 mg/cm.sup.2 137 mAh/g 9.9 mAh/cm.sup.2 NMC111 90:3:4:3 (NMC: 64.8 mg/cm.sup.2) @ 15.5 mA/g electrode (NMC: 152 mAh/g) 67 mg/cm.sup.2 ~120 mAh/g ~8 mAh/cm.sup.2 52 mg/cm.sup.2 ~125 mAh/g ~6.5 mAh/cm.sup.2 Slurry-casted NMC622:CB:PVDF = 41 mg/cm.sup.2 161 mAh/g @ 0.1 C 6.6 mAh/cm.sup.2 NMC622 91.5:4.4:4.1 (NMC: 37.6 mg/cm.sup.2) (NMC: 176 mAh/g) electrode 34.1 mg/cm.sup.2  161 mAh/g 5.5 mAh/cm.sup.2 27.4 mg/cm.sup.2  161 mAh/g 4.4 mAh/cm.sup.2 Slurry-casted NMC111:CB:PVDF = 28 mg/cm.sup.2 132 mAh/g @ 0.1 C 3.7 mAh/cm.sup.2 NMC111 85:7:8 (NMC: 24 mg/cm.sup.2) (NMC: 154 mAh/g) electrode Use of special techniques or substrates (CNT film, thick carbon/metal foam substrates, etc.) LiFePO.sub.4 coated LFP:CB:PVDF = 240 mg/cm.sup.2 108 mAh/g ~26 mAh/cm.sup.2 onto conductive 70:20:10 (LFP: 168 mg/cm.sup.2) @ 0.5 mA/g CNT textile (LFP: 155 mAh/g) Thick LFP, LTO LFP or LTO:CB = LFP: 150 mg/cm.sup.2 150 mAh/g @ 0.05 C 21 mAh/cm.sup.2 by Plasma 90:10 (LFP) Sintering LTO: 152 mg/cm.sup.2 167 mAh/g @ 0.05 C 25.5 mAh/cm.sup.2 (LTO) Thick LiCoO.sub.2 by LCO:binder = Unknown 140 mAh/g @ 0.05 C 12~13.5 mAh/cm.sup.2 magnetic 97.5:2.5 (Estimated M/A: ~96 templating mg/cm.sup.2) Electro- LMNO:MWCNT:PAN = 80 mg/cm.sup.2 162 mAh/g @ 0.2 C 13 mAh/cm.sup.2 spraying/spinning 72:3.6:24.4 (LMNO: 57 mg/cm.sup.2) (LMNO: 220 mg/cm.sup.2) (for multi- of LMNO stacked film) Slurry-coating NCM:PVDF:CB:Graphite = 106 mg/cm.sup.2 118 mAh/g @ 1/50 C 12.5 mAh/cm.sup.2 NCM111 onto 84:9:3.5:3.5 (NCM: 89 mg/cm.sup.2) (NCM: 140 mAh/g) porous metal foam substrate Vacuum-filtrated LFP:CNT:CNF = 112.5 mg/cm.sup.2 93 mAh/g @ 0.2 C 10.5 mAh/cm.sup.2 CNF-CNT- 80:15:5 (LFP: 90 mg/cm.sup.2) (LFP: 116 mAh/g) LiFePO.sub.4 film Slurry-coating LFP/C:CB:PVDF = 75.1 mg/cm.sup.2 117 mAh/g 8.8 mAh/cm.sup.2 LiFePO.sub.4 onto 75:15:10 (LFP: 56.3 mg/cm.sup.2) @ 1 mA/cm.sup.2 porous metal (LFP: 156 mAh/g) foam substrate Slurry-coating LFP:CB:CMC/PMA = 72 mg/cm.sup.2 117 mAh/g @ 0.2 C 8.4 mAh/cm.sup.2 LiFePO.sub.4 onto 100:6.8:5 (LFP: 64.4 mg/cm.sup.2) (LFP: 130 mAh/g) porous Al foam LiCoO.sub.2 NW free- LCO:Graphene = Total: 40 mg/cm.sup.2 125 mAh/g 5 mAh/cm.sup.2 standing film by 83.3:16.6 (LCO: 33.32 mg/cm.sup.2) (LCO: 150 mAh/g) vacuum-filtration LiCoO.sub.2/CNT LCO:CB:PVDF = 16.1 mg/cm.sup.2 91 mAh/g @ 0.25 C 1.46 mAh/cm.sup.2 free-standing film 77.5:12.5:10 (LCO: 12.5 mg/cm.sup.2) (LCO: 117 mAh/g) by vacuum-filtration (CNT as substrate)

[0093] The ability to produce both anodes and cathodes with very high areal capacities allows one to produce high-performance full-cells. By keeping the anode/cathode thickness ratios at the level required to match areal capacities but increasing the total anode plus cathode mass loading, (M/A)A+c, full-cells were produced with record C/A up to 29 mAh/cm.sup.2 (FIG. 9A, and Table 5). It is worth noting that the full-cell C/A is limited by the cathode (Maximum cathode C/A=30 mAh/cm.sup.2 and anode C/A=45 mAh/cm.sup.2), reinforcing the need to developing high-C.sub.SP cathode materials. These electrodes were surprisingly stable (FIG. 5B and see long-term cycles in FIG. 10) and had rate performances similar to the individual electrodes (FIG. 5C), yielding performance far beyond traditional NMC-graphite electrodes. One advantage of these composites is that because the electrodes can be made so thick, the inactive component (Al/Cu foils, separator etc.) becomes a very small fraction of the whole, thus increasing the overall energy density (FIG. 5D).

TABLE-US-00005 TABLE 5 Details of the full-cells with various total electrode mass loading, (M/A).sub.A+C = Anode M/A + Cathode M/A. The anode/cathode M/A indicate mass per unit area of each electrode excluding Al or Cu substrate. (M/A).sub.A+C Full-cell C/A Full-cell C/M *Full-cell E/A **Full-cell E.sub.SP (mg/cm.sup.2) (mAh/cm.sup.2) (mAh/g) (mWh/cm.sup.2) (Wh/kg) 47.1 8.1 171.9 27.4 441 (Anode, 3.1 + Cathode, 44) 64.3 10.9 169.5 37.1 473 (Anode, 4.4 + Cathode, 59.9) 119.5 20.6 172.4 70.1 522 (Anode, 8.5 + Cathode, 111) 166.5 28.8 172.9 98.3 542 (Anode, 11.5 + Cathode, 155) *The full-cell areal energy (E/A, mWh/cm.sup.2) was calculated as follows, [00001]$\begin{array}{cc}E/A=\frac{\int V\left(t\right).Math.I\mathrm{dt}}{A}& \left(4\right)\end{array}$where V, I, t and A, are cell voltage, applied discharge current, discharge time and the cell electrode area, respectively. **The full-cell specific energy (E.sub.SP, Wh/kg) was calculated as follows, [00002]$\begin{array}{cc}{E}_{\mathrm{SP}}=\frac{E}{M_{\mathrm{Total\_cell}}}=\frac{E/A}{M_{\mathrm{Total\_cell}}/A}=\frac{E/A}{\frac{M_{\mathrm{Cathode}}}{A}+\frac{M_{\mathrm{Anode}}}{A}+\frac{M_{\mathrm{Inactive}}}{A}}& \left(5\right)\end{array}$

[0094] where M.sub.cathode, M.sub.Anode and M.sub.Inactive are the mass for the cathode, anode, and inactive components (Al/Cu foils and separator), respectively. To calculate E.sub.SP in a practical way, the total mass of the electrodes as well as the inactive components, including Al/Cu foils and separator, were considered. Here M/A for Al, Cu and separator are 4, 9 and 2 mg/cm.sup.2, respectively, thus total M.sub.Inactive/A is 15 mg/cm.sup.2. Then Esp can be calculated from the values for the full-cell areal energy and M/A for the cathode/anode. Considering the mass of both electrodes and inactive components, the specific energy, E.sub.SP, for the full-cells, along with high-C/A cells from other studies were calculated and plotted versus the corresponding full-cell areal capacity, (C/A).sub.cell in FIG. 9E (see calculations in Table 6). This plot shows that the high-C/A full-cells delivered much higher E.sub.SP (up to 540 Wh/kg) than any other reports (<310 Wh/kg), highlighting their superlative performance. The relationship between E.sub.SP and (C/A).sub.Cell can be illustrated via a simple relationship:

[00003]$\begin{array}{cc}{E}_{\mathrm{SP}}=\frac{V}{\frac{1}{C_{\mathrm{SP},\mathrm{Cathode}}}+\frac{1}{C_{\mathrm{SP},\mathrm{Anode}}}+\frac{{\left(M/A\right)}_{\mathrm{Inactive}}}{{\left(C/A\right)}_{\mathrm{Cell}}}}& \left(6\right)\end{array}$

[0095] where V, C.sub.SP,Cathode, C.sub.SP,Anode and (M/A).sub.Inactive are the average operating voltage, cathode/anode gravimetric capacity and the inactive components' M/A. Plotting equation 6 for each system shows the curves saturate at high (C/A).sub.Cell at a value determined by C.sub.SP of the lower performing electrode, generally the cathode. As shown in FIG. 9E, the curve representing the data of the battery of the claimed invention approaches 540 Wh/kg at the highest (C/A).sub.Cell achieved (29 mAh/cm.sup.2), close to saturation. This means that the composite architecture has allowed the inventors to approach the absolute maximum C.sub.SP possible for the cathode material used. This implies that once more advanced cathode materials (e.g. Li.sub.2S) become widely available, this approach would be expected to allow commensurate increases in E.sub.SP.

TABLE-US-00006 TABLE 6 Literature comparison of full-cell LiBs with the high C/A. M.sub.Total/A is the areal loading mass of the total electrode components (AM + conducting agent + binder). The composite in the first row (in bold) is the composite of the claimed invention. Materials & methods Cathode M.sub.Total/A Anode M.sub.Total/A Full-cell C/A *Full-cell E.sub.SP Li.sub.xMn.sub.yO.sub.z—Si μ-Si/CNT Total: Total: 8~29 mAh/cm.sup.2 441~542 Wh/kg   NMC/CNT 44~155 mg/cm.sup.2 3~11.5 mg/cm.sup.2 by slurry-casting (NMC: 99.5 wt %) (μ-Si: 92.5 wt %) LCO nanowire (NW) Total: 40 mg/cm.sup.2 Total: 3 mg/cm.sup.2 5 mAh/cm.sup.2 310 Wh/kg Si NW by filtration (LCO: 83.3 wt %) (Si: 80 wt %) LCO Si-graphene Total: ~23 mg/cm.sup.2 Total: 1.5 mg/cm.sup.2 3 mAh/cm.sup.2 273 Wh/kg by slurry-casting (LCO: ~95 wt %) (Si-graphene: 80 wt %) NMC/LCO Total: 29.5 mg/cm.sup.2 Total: 4.46 mg/cm.sup.2 ~4 mAh/cm.sup.2 294 Wh/kg SiO—C (NMC/LCO: 97.25 wt %) (SiO—C: 90 wt %) by slurry-casting Li.sub.xMn.sub.yO.sub.z-Graphite NMC111 Total: 82 mg/cm.sup.2 Total: 38 mg/cm.sup.2 ~9.6 mAh/cm.sup.2 256 Wh/kg Graphite (NMC111: 90 wt. %) (Graphite: 90 wt. %) by slurry-casting 67 mg/cm.sup.2 33 mg/cm.sup.2 ~8 mAh/cm.sup.2 250 Wh/kg 52 mg/cm.sup.2 25 mg/cm.sup.2 ~6.5 mAh/cm.sup.2 254 Wh/kg 42 mg/cm.sup.2 20 mg/cm.sup.2 ~4.9 mAh/cm.sup.2 229 Wh/kg 30 mg/cm.sup.2 15 mg/cm.sup.2 ~3.4 mAh/cm.sup.2 204 Wh/kg 18 mg/cm.sup.2 9 mg/cm.sup.2 ~2.1 mAh/cm.sup.2 180 Wh/kg NMC622 Total: 41.1 mg/cm.sup.2 Total: 24.5 mg/cm.sup.2 6.6 mAh/cm.sup.2 295 Wh/kg Graphite (NMC622: 91.5 wt. %) (Graphite: 95.7 wt. %) by slurry-casting 34.1 mg/cm.sup.2 20 mg/cm.sup.2 5.5 mAh/cm.sup.2 287 Wh/kg 27.4 mg/cm.sup.2 16.6 mg/cm.sup.2 4.4 mAh/cm.sup.2 268 Wh/kg 20.8 mg/cm.sup.2 13.1 mg/cm.sup.2 3.3 mAh/cm.sup.2 243 Wh/kg 13.7 mg/cm.sup.2 7.6 mg/cm.sup.2 2.2 mAh/cm.sup.2 218 Wh/kg NMC111 Total: 105 mg/cm.sup.2 Total: 30 mg/cm.sup.2 10.5 mAh/cm.sup.2 252 Wh/kg Graphite (NMC111: 84 wt. %) (Graphite: 93 wt. %) onto metal foam by slurry-casting *Full-cell E.sub.SP for references was also calculated based on the total mass of the electrodes as well as the inactive components (Al/Cu foils and separator); the values for the inactive components' M/A were considered to be same as ours (total M.sub.Inactive/A: 15 mg/cm.sup.2).

[0096] While nanotubes have been used before to improve electrode conductivity, segregated networks—which are much more appropriate to realistic electrode materials—have not been reported, nor have spontaneously formed segregated networks. In addition to unprecedented conductivity enhancement, these spontaneously formed segregated networks dramatically increase mechanical robustness, promoting stability and allowing the production of extremely thick electrodes. In addition, wrapping the AM particles in a flexible, porous 2-dimensional membrane facilitates stable, repeatable, expansion/contraction of the lithium-storing material without impeding lithium diffusion. In addition, these membranes should keep silicon fragments localized even after pulverization, further promoting stability.

[0097] Compared to electrodes prepared from traditional mixtures of active material and polymer-binder and conductive-additive, the spontaneously formed segregated networks of the composite of the claimed invention make an electrode comprising said composite having very high mechanical toughness, without cracking. This toughness allows very thick electrodes to be made because it prevents crack formation during charging/discharging (mud-cracking effect) and improves stability. These thick electrodes store more Li ions and yield higher energy density.

[0098] Compared to electrodes prepared from traditional mixtures of active material and polymer-binder and conductive-additive, these networks make the electrode have very high conductivity. This conductivity allows the electrode to reach its theoretical Li storage capacity (Li ions per unit mass). The very high conductivity facilitates this maximisation of capacity, even for very thick electrodes.

[0099] The segregated network of the composite of the claimed invention spontaneously forms a 2D membrane which acts as a scaffold to hold the active material particles in place.

[0100] All the above can be achieved using CNT contents of 0.25-7.5 wt % (or metallic nanowires or a combination thereof). This is much less than the 20 wt % or even 30 wt % of the polymer-binder and conductive-additive used in traditional batteries. The dispersion of the CNT in the composite provides the architecture for an electrode where the filler particles are segregated on the surfaces of the active particles instead of being randomly distributed throughout the bulk of the material. The CNTs spontaneously self-organise or self-arrange themselves around the particulate active materials to form the membranes which are locally 2-dimensional but extend throughout the electrode wrapping all particles. The 2D membranes wrap around the particles and fill space within the electrode architecture. The membranes can be considered to be a fractal object with fractal dimensions of between 2 and 3. The length of the particles are larger than the CNTs (or metallic nanowires) by a factor of, at most, 1:2. Without any (additional) polymeric binders or carbon black in the composite, more active material can be added to the composite to reach the theoretical maximum capacity when used in thick electrodes without cracking.

[0101] In the specification the terms “comprise, comprises, comprised and comprising” or any variation thereof and the terms include, includes, included and including” or any variation thereof are considered to be totally interchangeable and they should all be afforded the widest possible interpretation and vice versa.

[0102] The invention is not limited to the embodiments hereinbefore described but may be varied in both construction and detail.