Patent Application
20230216040
This invention relates to coatings that enhance battery component performance.
Coatings play multiple roles in a wide variety of applications. They can be used as protective layers because they are mechanically strong or corrosion resistant [Ref. 1-3], prevent reflections or resist fogging, or they can prevent migration of substrate components (elements) or offer selected transport of one ion over others or electrons. They can prevent aggregation or sintering of particles. They can stabilize high surface area substrates or reduce surface free energies. They can stabilize specific phases. They can protect from infection or promote drug transport across membranes.
When used with active phases in battery components, some primary purposes of a coating are to promote selective ion/electron diffusion pathways, prevent corrosion through loss of active ions or unwanted chemical oxidation/reduction of active components. They may also offer mechanical properties that resist charge/discharge dimensional changes or prevent unwanted phase transitions or favor formation of desirable phases.
Coatings have been used successfully with silicon anodes to limit volume expansion during lithiation [Ref. 4-8]. They have been used to protect cathode materials from HF generated by hydrolysis of PF6 through formation of AlF3 and/or LiF. In Li—S systems, they have been used to limit or prevent sulfide shuttling that leads to loss of active material and formation of insulating layers [Ref. 9-13]. In high voltage cathodes, they have been used to prevent dissolution of Mn for example [Ref. 14-18].
Coatings have been used as synthetic solid electrolyte interfaces (SEIs) to prevent formation, or excessive growth, of SEIs for specific battery chemistries. Coatings have also been used to improve ionic and/or electronic conductivity of battery components. Finally, coatings have been used extensively to block dendrite propagation during cycling.
Coating methods most commonly target uniform and complete coating of substrates preferably limiting the formation of “pinholes,” as these are high energy defects likely permit unwanted processes even promoting them vs. uncoated substrates. To this end, multiple techniques have been explored to deposit uniform and thin coatings often based on solution (e.g. sol-gel or precipitation processing) or gas phase deposition methods. Gas phase deposition techniques including CVD, ALD and plasma assisted versions, and a number of sputtering technologies have all been explored with varying degrees of success.
Critical concerns focus on non-uniform coatings. The literature is replete with examples of coatings with defect pores [Ref. 5,6] that for example serve as the source of crack initiation leading to coating failure. Alternately, pores are also frequently associated with chemical pitting of substrates initiating corrosive failure. Pores (defects) can serve as nucleation sites for growth of and propagation of dendrites within ceramic electrolytes such as LLZO [Ref. 19].
Therefore, there is a need for improved coatings that enhance battery component performance.
We have unexpectedly found that coating active cathode and/or active anode materials with nanopowders that are solid electrolytes or that can transform to solid electrolytes during battery operation can substantially improve the performance of the coated active material by enhancing energy capacities, increasing long term stability, and eliminating or greatly reducing degradative processes in a number of unexpected ways. The coatings can be applied by mixing using ball milling, ultrasonic mixing or electrospray coating, and despite being porous offer a wide variety of greatly enhanced properties. Typically, porous coatings are especially prone to failure because the pores themselves can promote degradation of the active materials; yet, our findings described herein are the exact opposite. In some instances, coated cathode materials outperform any known examples of these same uncoated materials. The Li—S systems are especially stable compared to prior literature examples.
In one aspect, the present disclosure provides an electrode for an electrochemical device. The electrode comprises a lithium host material; and a porous coating on the lithium host material. The porous coating can comprise a solid-state ion conducting electrolyte material selected from:
In one embodiment, the electrode comprises: a plurality of first particles comprising a porous coating of one of the solid-state ion conducting electrolyte materials on the lithium host material, and a plurality of second particles comprising a porous coating of another of the solid-state ion conducting electrolyte materials on the lithium host material. The one of the solid-state ion conducting electrolyte material can be present in the first particles at a weight percentage between 5% and 30% based on a total weight of the one of the solid-state ion conducting electrolyte material and the lithium host material in the first particles, and the another of the solid-state ion conducting electrolyte materials can be present in the second particles at a weight percentage between 5% and 30% based on a total weight of the another of the solid-state ion conducting electrolyte material and the lithium host material in the second particles.
In one embodiment, the electrode has a thickness between 1 and 200 micrometers. In one embodiment, the porous coating has a thickness between about 20 nanometers and about 10 micrometers. In one embodiment, the porous coating comprises particles having an average particle size between 1 and 100 nanometers.
In one embodiment, the electrode is a cathode, and the lithium host material is selected from the group consisting of lithium metal oxides wherein the metal is one or more aluminum, cobalt, iron, manganese, nickel and vanadium, and lithium-containing phosphates having a general formula LiMPO4 wherein M is one or more of cobalt, iron, manganese, and nickel. In another embodiment, the electrode is a cathode, and the lithium host material comprises a lithium manganese oxide. In another embodiment, the electrode is a cathode, and the lithium host material comprises nano-sized lithium manganese oxide particles.
In one embodiment, the solid-state ion conducting electrolyte material comprises a lithium aluminum oxide. In another embodiment, the solid-state ion conducting electrolyte material comprises a lithium containing phosphate. In another embodiment, the solid-state ion conducting electrolyte material comprises a lithium-aluminum-titanium-silicon-phosphate. In another embodiment, the solid-state ion conducting electrolyte material comprises the ceramic electrolyte material.
In one embodiment, the electrode is a cathode, and the lithium host material has a formula LiNixMnyCozO2, wherein x+y+z=1 and x:y:z=1:1:1 (NMC 111), x:y:z=4:3:3 (NMC 433), x:y:z=5:2:2 (NMC 522), x:y:z=5:3:2 (NMC 532), x:y:z=6:2:2 (NMC 622), or x:y:z=8:1:1 (NMC 811). In another embodiment, the solid-state ion conducting electrolyte material comprises a lithium containing phosphate. In another embodiment, the solid-state ion conducting electrolyte comprises material a lithium-aluminum-titanium-silicon-phosphate.
In one embodiment, the electrode is a cathode, and the lithium host material has a formula LiNi1-x-yMnxAlyO2 (NMA) wherein x+y+z=1. In another embodiment, the electrode is a cathode, and the lithium host material comprises a sulfur containing material. In another embodiment, the solid-state ion conducting electrolyte material comprises a lithium containing phosphate. In another embodiment, the solid-state ion conducting electrolyte material comprises a lithium-aluminum-titanium-silicon-phosphate. In another embodiment, the solid-state ion conducting electrolyte material comprises LixSiPON wherein x is 1, 1.5, 3, or 6.
In one embodiment, the electrode is an anode, and the lithium host material is selected from the group consisting of lithium titanium oxides, silicon-containing materials, and high entropy oxides.
In one embodiment, the electrode is an anode, and the lithium host material is lithium titanium oxide.
In one embodiment, the solid-state ion conducting electrolyte material comprises a lithium aluminum oxide and LixSiON wherein x is 2, 4, or 6.
In one embodiment, the electrode is an anode, and the electrode comprises a plurality of first particles and a plurality of second particles, the first particles comprising a porous coating of lithium aluminum oxide on lithium titanium oxide, and the second particles comprising a porous coating of LixSiON wherein x is 2, 4, or 6 on lithium titanium oxide. In one embodiment, the lithium aluminum oxide coating is present on the first particles at a weight percentage between 1% and 10% based on a total weight of the lithium aluminum oxide coating and the lithium titanium oxide in the first particles, and the LixSiON coating is present on the second particles at a weight percentage between 1% and 20% based on a total weight of the LixSiON coating and the lithium titanium oxide in the second particles.
In one embodiment, the electrode has an areal loading density between 3 and 4 mg/cm2. In one embodiment, the electrode has a lithium ion diffusion coefficient of at least 1×10−12 cm2/s.
In one embodiment, the electrode further comprises: a conductive additive selected from the group consisting of silica depleted rice hull ash, graphite, carbon black, acetylene black, Ketjen black, channel black, furnace black, lamp black, thermal black, conductive fibers, metallic powders, conductive whiskers, conductive metal oxides, and mixtures thereof. In another embodiment, the electrode further comprises silica depleted rice hull ash.
In one embodiment, the electrode further comprises: a binder selected from the group consisting of polyvinylidene fluoride (PVDF), polyacrylic acid, poly(methylmethacrylate), poly(vinylacetate), polyvinyl alcohol, polyethyleneoxide, polyvinylpyrrolidone, polyvinyl ether, polyvinylchloride, polyacrylonitrile, polyvinylpyridine, styrene-butadiene rubber, acrylonitrile-butadiene rubber, polyethylene, polypropylene, ethylene-propylene-diene terpolymers (EPDM), cellulose, carboxymethylcellulose, starch, hydroxypropylcellulose, and mixtures thereof.
In another aspect, the present disclosure provides an electrochemical device comprising at least one of the embodiments of the electrodes described above as a cathode; an anode; and an electrolyte positioned between the cathode and the anode. In one embodiment, the electrochemical device has a columbic efficiency of 95% or greater.
In one embodiment of the electrochemical device, the anode comprises lithium metal. In one embodiment of the electrochemical device, the anode consists essentially of lithium metal.
In one embodiment of the electrochemical device, the electrolyte comprises a liquid electrolyte including a lithium compound in an organic solvent. The lithium compound can be selected from the group consisting of LiPF6, LiBF4, LiClO4, lithium bis(fluorosulfonyl)imide (LiFSI), LiN(CF3SO2)2 (LiTFSI), and LiCF3SO3 (LiTf), and the organic solvent can be selected from the group consisting of carbonate-based solvents, ether-based solvents, ionic liquids, and mixtures thereof. The carbonate based solvent can be selected from the group consisting of dimethyl carbonate, diethyl carbonate, ethyl methyl carbonate, dipropyl carbonate, methylpropyl carbonate, ethylpropyl carbonate, methylethyl carbonate, ethylene carbonate, propylene carbonate, butylene carbonate, fluoroethylene carbonate, and mixtures thereof. and the ether based solvent can be selected from the group consisting of diethyl ether, dibutyl ether, monoglyme, diglyme, tetraglyme, 2-methyltetrahydrofuran, tetrahydrofuran, 1,3-dioxolane, 1,2-dimethoxyethane, 1,4-dioxane, and mixtures thereof.
In one embodiment of the electrochemical device, the electrolyte comprises a solid ionically conductive polymer selected from the group consisting of poly(ethylene oxide) (PEO), polypropylene oxide (PPO), polyacrylonitrile (PAN), polyvinyl alcohol (PVA), polymethyl methacrylate (PMMA), polydimethyl siloxane (PDMS), polyvinyl pyrollidone (PVP), LixPON wherein x is 1, 1.5, 3, or 6, LixSiPON wherein x is 1, 1.5, 3, or 6, and combinations thereof.
In one embodiment of the electrochemical device, the electrolyte comprises a solid ionically conductive polymer selected from the group consisting of poly(ethylene oxide) (PEO), LixPON wherein x is 1, 1.5, 3, or 6, LixSiPON wherein x is 1, 1.5, 3, or 6, LixSiON wherein x is 2, 4, or 6, and combinations thereof.
In yet another aspect, the present disclosure provides an electrochemical device comprising at least one of the embodiments of the electrodes described above as an anode; a cathode; and an electrolyte positioned between the cathode and the anode. In one embodiment, the electrochemical device has a columbic efficiency of 95% or greater.
In one embodiment of the electrochemical device, the cathode comprises a cathode active material selected from (i) lithium metal oxides wherein the metal is one or more aluminum, cobalt, iron, manganese, nickel and vanadium, (ii) lithium-containing phosphates having a general formula LiMPO4 wherein M is one or more of cobalt, iron, manganese, and nickel, and (iii) materials having a formula LiNixMnyCozO2, wherein x+y+z=1 and x:y:z=1:1:1 (NMC 111), x:y:z=4:3:3 (NMC 433), x:y:z=5:2:2 (NMC 522), x:y:z=5:3:2 (NMC 532), x:y:z=6:2:2 (NMC 622), or x:y:z=8:1:1 (NMC 811). In one embodiment of the electrochemical device, the cathode comprises a sulfur containing material.
In one embodiment of the electrochemical device, the electrolyte comprises a liquid electrolyte including a lithium compound in an organic solvent. The lithium compound can be selected from the group consisting of LiPF6, LiBF4, LiClO4, lithium bis(fluorosulfonyl)imide (LiFSI), LiN(CF3SO2)2 (LiTFSI), and LiCF3SO3 (LiTf), and the organic solvent is selected from the group consisting of carbonate based solvents, ether based solvents, ionic liquids, and mixtures thereof. The carbonate based solvent can be selected from the group consisting of dimethyl carbonate, diethyl carbonate, ethyl methyl carbonate, dipropyl carbonate, methylpropyl carbonate, ethylpropyl carbonate, methylethyl carbonate, ethylene carbonate, propylene carbonate, butylene carbonate, fluoroethylene carbonate, and mixtures thereof. and the ether based solvent can be selected from the group consisting of diethyl ether, dibutyl ether, monoglyme, diglyme, tetraglyme, 2-methyltetrahydrofuran, tetrahydrofuran, 1,3-dioxolane, 1,2-dimethoxyethane, 1,4-dioxane, and mixtures thereof.
In one embodiment of the electrochemical device, the electrolyte comprises a solid ionically conductive polymer selected from the group consisting of poly(ethylene oxide) (PEO), polypropylene oxide (PPO), polyacrylonitrile (PAN), polyvinyl alcohol (PVA), polymethyl methacrylate (PMMA), polydimethyl siloxane (PDMS), polyvinyl pyrollidone (PVP), LixPON wherein x is 1, 1.5, 3, or 6, LixSiPON wherein x is 1, 1.5, 3, or 6, LixSiON wherein x is 2, 4, or 6, and combinations thereof.
In one embodiment of the electrochemical device, the electrolyte comprises a solid ionically conductive polymer selected from the group consisting of poly(ethylene oxide) (PEO), LixPON wherein x is 1, 1.5, 3, or 6, LixSiPON wherein x is 1, 1.5, 3, or 6, LixSiON wherein x is 2, 4, or 6, and combinations thereof.
In still another aspect, the present disclosure provides a method for forming an electrode for an electrochemical device wherein the method comprises: (a) forming a slurry including coated particles comprising a porous coating of a solid-state ion conducting electrolyte material on a lithium host material; and (b) casting a layer of the slurry on a surface to form the electrode. The solid-state ion conducting electrolyte material can be selected from:
In one embodiment of the method, the solid-state ion conducting electrolyte material is selected from the group consisting of: (i) lithium aluminum oxides, (ii) lithium containing phosphates, (iii) LixPON wherein x is 1, 1.5, 3, or 6, (iv) LixSiPON wherein x is 1, 1.5, 3, or 6, (v) LixSiON wherein x is 2, 4, or 6, (vi) a ceramic electrolyte material having the formula LiuRevMwAxOy wherein Re can be any combination of elements with a nominal valence of +3 including La, Nd, Pr, Pm, Sm, Sc, Eu, Gd, Tb, Dy, Y, Ho, Er, Tm, Yb, and Lu, M can be any combination of metals with a nominal valence of +3, +4, +5 or +6 including Zr, Ta, Nb, Sb, W, Hf, Sn, Ti, V, Bi, Ge, and Si, A can be any combination of dopant atoms with nominal valence of +1, +2, +3 or +4 including H, Na, K, Rb, Cs, Ba, Sr, Ca, Mg, Fe, Co, Ni, Cu, Zn, Ga, Al, B, and Mn, u can vary from 3-7.5, v can vary from 0-3, w can vary from 0-2, x can vary from 0-2; and y can vary from 11-12.5, and (vii) mixtures thereof.
In one embodiment of the method, step (a) comprises forming the coated particles by (i) forming a plurality of particles of the lithium host material, and (ii) forming the porous coating of the solid-state ion conducting electrolyte material on the plurality of particles of the lithium host material. The plurality of particles of the lithium host material can be formed by liquid-feed flame spray pyrolysis. In one embodiment of the method, the porous coating of the solid-state ion conducting electrolyte material is formed on the plurality of particles of the lithium host material by ball milling a mixture of the solid-state ion conducting electrolyte material and the plurality of particles of the lithium host material. In one embodiment of the method, the porous coating of the solid-state ion conducting electrolyte material is formed on the plurality of particles of the lithium host material ultrasonic mixing the solid-state ion conducting electrolyte material and the plurality of particles of the lithium host material. In one embodiment of the method, the porous coating of the solid-state ion conducting electrolyte material is formed on the plurality of particles of the lithium host material by an electrospray coating process.
In one embodiment of the method, the surface is a surface of a current collector. In one embodiment of the method, the layer of the slurry has a thickness between 1 and 200 micrometers. In one embodiment of the method, the layer of the slurry does not undergo a heat treatment.
In one embodiment of the method, the coated particles comprise: a plurality of first particles comprising a porous coating of one of the solid-state ion conducting electrolyte materials on the lithium host material, and a plurality of second particles comprising a porous coating of another of the solid-state ion conducting electrolyte materials on the lithium host material. In one embodiment of the method, the one of the solid-state ion conducting electrolyte materials is present in the first particles at a weight percentage between 5% and 30% based on a total weight of the one of the solid-state ion conducting electrolyte material and the lithium host material in the first particles, and the another of the solid-state ion conducting electrolyte materials is present in the second particles at a weight percentage between 5% and 30% based on a total weight of the another of the solid-state ion conducting electrolyte materials and the lithium host material in the second particles.
In one embodiment of the method, the porous coating has a thickness between about 20 nanometers and about 10 micrometers. In one embodiment of the method, the porous coating comprises particles having an average particle size between 1 and 100 nanometers.
In one embodiment of the method, the lithium host material is selected from the group consisting of lithium metal oxides wherein the metal is one or more aluminum, cobalt, iron, manganese, nickel and vanadium, and lithium-containing phosphates having a general formula LiMPO4 wherein M is one or more of cobalt, iron, manganese, and nickel. In one embodiment of the method, the lithium host material comprises a lithium manganese oxide.
In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a lithium aluminum oxide. In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a lithium containing phosphate. In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a lithium-aluminum-titanium-silicon-phosphate.
In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a ceramic electrolyte material having the formula LiuRevMwAxOy wherein Re can be any combination of elements with a nominal valence of +3 including La, Nd, Pr, Pm, Sm, Sc, Eu, Gd, Tb, Dy, Y, Ho, Er, Tm, Yb, and Lu, M can be any combination of metals with a nominal valence of +3, +4, +5 or +6 including Zr, Ta, Nb, Sb, W, Hf, Sn, Ti, V, Bi, Ge, and Si, A can be any combination of dopant atoms with nominal valence of +1, +2, +3 or +4 including H, Na, K, Rb, Cs, Ba, Sr, Ca, Mg, Fe, Co, Ni, Cu, Zn, Ga, Al, B, and Mn, u can vary from 3-7.5, v can vary from 0-3, w can vary from 0-2, x can vary from 0-2; and y can vary from 11-12.5.
In one embodiment of the method, the lithium host material has a formula LiNixMnyCozO2, wherein x+y+z=1 and x:y:z=1:1:1 (NMC 111), x:y:z=4:3:3 (NMC 433), x:y:z=5:2:2 (NMC 522), x:y:z=5:3:2 (NMC 532), x:y:z=6:2:2 (NMC 622), or x:y:z=8:1:1 (NMC 811). In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a lithium containing phosphate. In one embodiment of the method, the lithium host material has a formula LiNi1-x-yMnxAlyO2 (NMA) wherein x+y+z=1. In one embodiment of the method, the lithium host material comprises a sulfur containing material.
In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a lithium containing phosphate. In one embodiment of the method, the solid-state ion conducting electrolyte material comprises LixSiPON wherein x is 1, 1.5, 3, or 6. In one embodiment of the method, the lithium host material is selected from the group consisting of lithium titanium oxides, silicon-containing materials, and high entropy oxides. In one embodiment of the method, the lithium host material is lithium titanium oxide. In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a lithium aluminum oxide and LixSiON wherein x is 2, 4, or 6.
In one embodiment of the method, the coated particles comprise a plurality of first particles and a plurality of second particles, the first particles comprising a porous coating of lithium aluminum oxide on lithium titanium oxide, and the second particles comprising a porous coating of LixSiON wherein x is 2, 4, or 6 on lithium titanium oxide. In one embodiment of the method, the lithium host material comprises nano-sized particles.
In yet another aspect, the present disclosure provides a method for forming an electrode for an electrochemical device wherein the method comprises: (a) forming a slurry including coated particles comprising a lithium host material and a coating of one or more precursors that form a porous coating of a solid-state ion conducting electrolyte material on the lithium host material upon cycling of the electrochemical device; and (b) casting a layer of the slurry on a surface to form the electrode. The solid-state ion conducting electrolyte material can be selected from:
In one embodiment of the method, the porous coating comprises particles having an average particle size between 1 and 100 nanometers.
In one embodiment of the method, the lithium host material is selected from the group consisting of lithium metal oxides wherein the metal is one or more aluminum, cobalt, iron, manganese, nickel and vanadium, and lithium-containing phosphates having a general formula LiMPO4 wherein M is one or more of cobalt, iron, manganese, and nickel.
In one embodiment of the method, the lithium host material comprises a lithium manganese oxide.
In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a lithium aluminum oxide. In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a lithium containing phosphate.
In one embodiment of the method, the lithium host material has a formula LiNixMnyCozO2, wherein x+y+z=1 and x:y:z=1:1:1 (NMC 111), x:y:z=4:3:3 (NMC 433), x:y:z=5:2:2 (NMC 522), x:y:z=5:3:2 (NMC 532), x:y:z=6:2:2 (NMC 622), or x:y:z=8:1:1 (NMC 811).
In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a lithium containing phosphate.
In one embodiment of the method, the lithium host material has a formula LiNi1-x-yMnxAlyO2 (NMA) wherein x+y+z=1. In one embodiment of the method, the lithium host material comprises a sulfur containing material.
In one embodiment of the method, the solid-state ion conducting electrolyte material comprises a lithium containing phosphate. In one embodiment of the method, the solid-state ion conducting electrolyte material comprises LixSiPON wherein x is 1, 1.5, 3, or 6.
In one embodiment of the method, the lithium host material is selected from the group consisting of lithium titanium oxides, silicon-containing materials, and high entropy oxides. In one embodiment of the method, the lithium host material is lithium titanium oxide.
In one embodiment of the method, the lithium host material comprises nano-sized particles.
These and other features, aspects, and advantages of the present disclosure will become better understood upon consideration of the following detailed description, drawings, and appended claims.
The patent or application file contains at least one drawing executed in color. Copies of this patent or patent application publication with color drawing(s) will be provided by the Office upon request and payment of the necessary fee.
Before the present invention is described in further detail, it is to be understood that the invention is not limited to the particular embodiments described. It is also to be understood that the terminology used herein is for the purpose of describing particular embodiments only, and is not intended to be limiting. The scope of the present invention will be limited only by the claims. As used herein, the singular forms “a”, “an”, and “the” include plural embodiments unless the context clearly dictates otherwise.
It should be apparent to those skilled in the art that many additional modifications beside those already described are possible without departing from the inventive concepts. In interpreting this disclosure, all terms should be interpreted in the broadest possible manner consistent with the context. Variations of the term “comprising”, “including”, or “having” should be interpreted as referring to elements, components, or steps in a non-exclusive manner, so the referenced elements, components, or steps may be combined with other elements, components, or steps that are not expressly referenced. Embodiments referenced as “comprising”, “including”, or “having” certain elements are also contemplated as “consisting essentially of” and “consisting of” those elements, unless the context clearly dictates otherwise. It should be appreciated that aspects of the disclosure that are described with respect to a system are applicable to the methods, and vice versa, unless the context explicitly dictates otherwise.
Numeric ranges disclosed herein are inclusive of their endpoints. For example, a numeric range of between 1 and 10 includes the values 1 and 10. When a series of numeric ranges are disclosed for a given value, the present disclosure expressly contemplates ranges including all combinations of the upper and lower bounds of those ranges. For example, a numeric range of between 1 and 10 or between 2 and 9 is intended to include the numeric ranges of between 1 and 9 and between 2 and 10.
The present invention provides a method of introducing high surface area nanopowders to the surfaces of catholyte and anolyte active materials by a process that can be milling using ultrasonic agitation or ball milling or electrostatic spraying wherein the catholyte or anolyte materials with or without other additives including carbon, and binders are mixed for a period of time such that the active materials become uniformly coated with the nanopowders at mass fractions that enhance the activity and stability of the active materials while also not significantly diminishing their capacities. Thereafter, mixtures of nanoparticles plus active material are formulated in a coating that can include a binder and an electrolyte which can be a liquid or a solid polymer electrolyte or a ceramic thin film electrolyte whose performance itself by the presence of nanoparticle electrolyte results in enhancements measured as extensions of cycle life by 50-200% and improvements in capacities by 5-50% against uncoated materials over similar cycle lives.
A suitable active material for the cathode 114 of the lithium metal battery 110 is a lithium host material capable of storing and subsequently releasing lithium ions. Looking at
The lithium host material 133 may comprise a lithium host material selected from the group consisting of lithium metal oxides wherein the metal is one or more aluminum, cobalt, iron, manganese, nickel and vanadium; and lithium-containing phosphates having a general formula LiMPO4 wherein M is one or more of cobalt, iron, manganese, and nickel. The lithium host material 133 may comprise a lithium manganese oxide. The lithium host material 133 may comprise a lithium host material having a formula LiNixMnyCozO2, wherein x+y+z=1 and x:y:z=1:1:1 (NMC 111), x:y:z=4:3:3 (NMC 433), x:y:z=5:2:2 (NMC 522), x:y:z=5:3:2 (NMC 532), x:y:z=6:2:2 (NMC 622), or x:y:z=8:1:1 (NMC 811). The lithium host material 133 may comprise a lithium host material having a formula LiNi1-x-yMnxAlyO2 (NMA) wherein x+y+z=1. The lithium host material 133 may comprise a sulfur containing material, such as a material including S8.
The porous coating 135 may comprise a solid-state ion conducting electrolyte material selected from the group consisting of: (i) lithium aluminum oxides, (ii) lithium containing phosphates, (iii) LixPON wherein x is 1, 1.5, 3, or 6, (iv) LixSiPON wherein x is 1, 1.5, 3, or 6, (v) LixSiON wherein x is 2, 4, or 6, (vi) a ceramic electrolyte material having the formula LiuRevMwAxOy wherein Re can be any combination of elements with a nominal valence of +3 including La, Nd, Pr, Pm, Sm, Sc, Eu, Gd, Tb, Dy, Y, Ho, Er, Tm, Yb, and Lu, M can be any combination of metals with a nominal valence of +3, +4, +5 or +6 including Zr, Ta, Nb, Sb, W, Hf, Sn, Ti, V, Bi, Ge, and Si, A can be any combination of dopant atoms with nominal valence of +1, +2, +3 or +4 including H, Na, K, Rb, Cs, Ba, Sr, Ca, Mg, Fe, Co, Ni, Cu, Zn, Ga, Al, B, and Mn, u can vary from 3-7.5, v can vary from 0-3, w can vary from 0-2, x can vary from 0-2; and y can vary from 11-12.5, and (vii) mixtures thereof.
In some aspects, the cathode 114 may include a conductive additive. Many different conductive additives, e.g., Co, Mn, Ni, Cr, Al, or Li, may be substituted or additionally added into the structure to influence electronic conductivity, ordering of the layer, stability on delithiation and cycling performance of the cathode materials. Other suitable conductive additives include silica depleted rice hull ash, graphite, carbon black, acetylene black, Ketjen black, channel black, furnace black, lamp black, thermal black, conductive fibers, metallic powders, conductive whiskers, conductive metal oxides, and mixtures thereof.
In some aspects, the cathode 114 may include a binder. Non-limiting examples of the binder include: polyvinylidene fluoride (PVDF), polyacrylic acid, poly(methylmethacrylate), poly(vinylacetate), polyvinyl alcohol, polyethyleneoxide, polyvinylpyrrolidone, polyvinyl ether, polyvinylchloride, polyacrylonitrile, polyvinylpyridine, styrene-butadiene rubber, acrylonitrile-butadiene rubber, polyethylene, polypropylene, ethylene-propylene-diene terpolymers (EPDM), cellulose, carboxymethylcellulose, starch, hydroxypropylcellulose, and mixtures thereof.
The anode 118 of the lithium metal battery 110 may comprise lithium metal. In one embodiment, the anode 118 of the lithium metal battery 110 consists essentially of lithium metal.
An example material for the separator 121 of the battery 110 can a permeable polymer such as a polyolefin. Example polyolefins include polyethylene, polypropylene, and combinations thereof.
The lithium metal battery 110 includes a liquid electrolyte. The liquid electrolyte may comprise a lithium compound in an organic solvent. The lithium compound may be selected from LiPF6, LiBF4, LiClO4, lithium bis(fluorosulfonyl)imide (LiFSI), LiN(CF3SO2)2 (LiTFSI), and LiCF3SO3 (LiTf). The organic solvent may be selected from carbonate based solvents, ether based solvents, ionic liquids, and mixtures thereof. The carbonate based solvent may be selected from the group consisting of dimethyl carbonate, diethyl carbonate, ethyl methyl carbonate, dipropyl carbonate, methylpropyl carbonate, ethylpropyl carbonate, methylethyl carbonate, ethylene carbonate, propylene carbonate, butylene carbonate, and fluoroethylene carbonate; and the ether based solvent is selected from the group consisting of diethyl ether, dibutyl ether, monoglyme, diglyme, tetraglyme, 2-methyltetrahydrofuran, tetrahydrofuran, 1,3-dioxolane, 1,2-dimethoxyethane, and 1,4-dioxane.
The current collector 112 and the current collector 122 can comprise a conductive material. For example, the current collector 112 and the current collector 122 may comprise molybdenum, aluminum, nickel, copper, combinations and alloys thereof or stainless steel.
Looking at
The lithium host material 233 may comprise one or more of the lithium host materials listed above for lithium host material 133. The porous coating 235 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
The cathode 214 of the lithium metal battery 210 may include one or more of the conductive additives listed above for battery 110. The cathode 214 of the lithium metal battery 210 may include one or more of the binders listed above for battery 110.
The anode 220 of the lithium metal battery 210 may comprise lithium metal. In one embodiment, the anode 220 of the lithium metal battery 210 consists essentially of lithium metal.
The current collector 212 and the current collector 222 can comprise a conductive material. For example, the current collector 212 and the current collector 222 may comprise molybdenum, aluminum, nickel, copper, combinations and alloys thereof or stainless steel.
The solid state electrolyte 216 of the lithium metal battery 210 can include any solid material capable of storing and transporting Li+ ions between the anode 218 and the cathode 214.
One example solid state electrolyte 216 of the lithium metal battery 210 can be a solid polymer electrolyte containing one or more ionically conductive polymers selected from poly(ethylene oxide) (PEO), polypropylene oxide (PPO), polyacrylonitrile (PAN), polyvinyl alcohol (PVA), polymethyl methacrylate (PMMA), polydimethyl siloxane (PDMS), polyvinyl pyrollidone (PVP), LixPON wherein x is 1, 1.5, 3, or 6, LixSiPON wherein x is 1, 1.5, 3, or 6, LixSiON wherein x is 2, 4, or 6, and combinations thereof.
Another suitable solid state electrolyte 216 of the lithium metal battery 210 includes an electrolyte material having the formula LiuRevMwAxOy, wherein
Re can be any combination of elements with a nominal valence of +3 including La, Nd, Pr, Pm, Sm, Sc, Eu, Gd, Tb, Dy, Y, Ho, Er, Tm, Yb, and Lu;
M can be any combination of metals with a nominal valence of +3, +4, +5 or +6 including Zr, Ta, Nb, Sb, W, Hf, Sn, Ti, V, Bi, Ge, and Si;
A can be any combination of dopant atoms with nominal valence of +1, +2, +3 or +4 including H, Na, K, Rb, Cs, Ba, Sr, Ca, Mg, Fe, Co, Ni, Cu, Zn, Ga, Al, B, and Mn;
u can vary from 3-7.5;
v can vary from 0-3;
w can vary from 0-2;
x can vary from 0-2; and
y can vary from 11-12.5.
The electrolyte material may be a lithium lanthanum zirconium oxide.
Another example solid state electrolyte 216 can include any combination oxide or phosphate materials with a garnet, perovskite, NaSICON, or LiSICON phase.
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The lithium host material 333 may comprise one or more lithium host materials selected from lithium titanium oxide (Li4Ti5O12, LTO), silicon-containing materials, such as silicon (e.g., silicene), silicon carbides (e.g., SiC), silicon nitrides (Si3N4), silicon nitride oxides (e.g., Si2N2O), and high entropy oxides (e.g., (Co0.2Cu0.2Mg0.2Ni0.2Zn0.2)O).
The porous coating 335 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
An example cathode active material for the cathode 314 is a lithium metal oxide wherein the metal is one or more aluminum, cobalt, iron, manganese, nickel and vanadium. Non-limiting example lithium metal oxides are LiCoO2 (LCO), LiFeO2, LiMnO2 (LMO), LiMn2O4, LiNiO2 (LNO), LiNixCoyO2, LiMnxCoyO2, LiMnxNiyO2, LiMnxNiyO4, LiNixCoyAlzO2 (NCA), LiNi1/3Mn1/3Co1/3O2 and others. Another example of a cathode active material is a lithium-containing phosphate having a general formula LiMPO4 wherein M is one or more of cobalt, iron, manganese, and nickel, such as lithium iron phosphate (LFP) and lithium iron fluorophosphates. The cathode can comprise a cathode active material having a formula LiNixMnyCozO2, wherein x+y+z=1 and x:y:z=1:1:1 (NMC 111), x:y:z=4:3:3 (NMC 433), x:y:z=5:2:2 (NMC 522), x:y:z=5:3:2 (NMC 532), x:y:z=6:2:2 (NMC 622), or x:y:z=8:1:1 (NMC 811). The cathode can comprise a cathode active material having a formula LiNi1-x-yMnxAlyO2 (NMA) wherein x+y+z=1. Another example of a cathode active material is porous carbon (for a lithium air battery). Another example of a cathode active material is a sulfur containing material (for a lithium sulfur battery). The cathode active material can be a mixture of any number of these cathode active materials.
The cathode 314 of the lithium ion battery 310 may include one or more of the conductive additives listed above for battery 110. The cathode 314 of the lithium ion battery 310 may include one or more of the binders listed above for battery 110.
An example material for the separator 321 of the lithium ion battery 310 can a permeable polymer such as a polyolefin. Example polyolefins include polyethylene, polypropylene, and combinations thereof.
The lithium ion battery 310 includes a liquid electrolyte. The liquid electrolyte may comprise any of the liquid electrolytes listed above for battery 110.
The current collector 312 and the current collector 322 can comprise a conductive material. For example, the current collector 312 and the current collector 322 may comprise molybdenum, aluminum, nickel, copper, combinations and alloys thereof or stainless steel.
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The lithium host material 433 may comprise one or more lithium host materials selected from lithium titanium oxide (Li4Ti5O12, LTO), silicon-containing materials, such as silicon (e.g., silicene), silicon carbides (e.g., SiC), silicon nitrides (Si3N4), silicon nitride oxides (e.g., Si2N2O), and high entropy oxides (e.g., (Co0.2Cu0.2Mg0.2Ni0.2Zn0.2)O).
The porous coating 435 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
An example cathode active material for the cathode 414 is a cathode active material listed above for battery 310.
The cathode 414 of the lithium ion battery 410 may include one or more of the conductive additives listed above for battery 110. The cathode 414 of the lithium ion battery 410 may include one or more of the binders listed above for battery 110.
The solid state electrolyte 416 of the lithium ion battery 410 can include one or more of the solid state electrolytes listed above for battery 210.
The current collector 412 and the current collector 422 can comprise a conductive material. For example, the current collector 412 and the current collector 422 may comprise molybdenum, aluminum, nickel, copper, combinations and alloys thereof or stainless steel.
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The lithium host material 533 may comprise one or more of the lithium host materials listed above for lithium host material 133. The porous coating 535 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
The cathode 514 may include one or more of the conductive additives listed above for battery 110. The cathode 514 may include one or more of the binders listed above for battery 110.
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The lithium host material 553 may comprise one or more of the lithium host materials listed above for lithium host material 333.
The porous coating 555 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
An example material for the separator 521 of the lithium ion battery 510 can a permeable polymer such as a polyolefin. Example polyolefins include polyethylene, polypropylene, and combinations thereof.
The lithium ion battery 510 includes a liquid electrolyte. The liquid electrolyte may comprise any of the liquid electrolytes listed above for battery 110.
The current collector 512 and the current collector 522 can comprise a conductive material. For example, the current collector 512 and the current collector 522 may comprise molybdenum, aluminum, nickel, copper, combinations and alloys thereof or stainless steel.
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The lithium host material 633 may comprise one or more of the lithium host materials listed above for lithium host material 133. The porous coating 635 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
The cathode 614 may include one or more of the conductive additives listed above for battery 110. The cathode 614 may include one or more of the binders listed above for battery 110.
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The lithium host material 653 may comprise one or more of the lithium host materials listed above for lithium host material 333.
The porous coating 655 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
The solid state electrolyte 616 of the lithium ion battery 610 can include one or more of the solid state electrolytes listed above for battery 210.
The current collector 612 and the current collector 622 can comprise a conductive material. For example, the current collector 612 and the current collector 622 may comprise molybdenum, aluminum, nickel, copper, combinations and alloys thereof or stainless steel.
The following Examples are provided in order to demonstrate and further illustrate certain embodiments and aspects of the present invention and are not to be construed as limiting the scope of the invention.
Given all of the above anticipated issues with porous coatings, it is counterintuitive to envision that porous coatings on active battery components can actually provide much superior cell performance when the coating material comprises nanopowders coated by simple (ultrasonic or ball) milling (or electrospray coating) at contents of from 5-30 wt. %. In some instances, the coating does not actually have to have Li+ content to promote superior properties.
The following Examples demonstrate that the introduction of lithium ion conducting nanopowders to both cathode and anode materials in the form of imperfect (porous) but uniform coatings provide enhanced performance and/or reduced degradation during cycling to voltages normal for that active material. Another important point is that these coatings can be made by simple ball milling for example which is easily scalable and cost effective as opposed to gas phase coating techniques.
In Example 1, a lithium manganese oxide (LMNO) powder (Li1.1Mn1.5Ni0.5O4 from Nano One) was coated with nano-size particles of Al2O3, Li7La3Zr2O12 (LLZO), LiAlO2, and Li1.7Al0.3Ti1.7Si0.4P2.6O12, a lithium-aluminum-titanium-silicon-phosphate (LATSP). Lithium-aluminum-titanium-silicon-phosphates have a general composition Li1+x+yAlxTi2-xSiyP3-yO12 wherein 0≤x≤1 and 0≤y≤1. Unlike most coating processes, the method involved the use of a soft and scalable ball milling technique in which 5-20 wt. % of the active and inactive nanoparticles were introduced to LMNO just before electrode fabrication. The Li1.1Mn1.5Ni0.5O4 (Nano One) powder and carbon black (C-65 having a primary particle size less than 50 nm.) were heated to 100° C./24 hours/vacuum. The electrode slurries were prepared by mixing Li1.1Mn1.5Ni0.5O4 (60-80 wt. %), C65 (5-10 wt. %), nanoparticles (5-20 wt. %), and polyvinylidene fluoride (PVDF) (10 wt. %) in 1-methyl pyrrolidin-2-one. The mixtures were then ball-milled for 24-48 hours using ZrO2 beads (3 mm, 6 g). The slurries were then coated on Al foil.
Half-cells were assembled using LMNO (Li1.1Mn1.5Ni0.5O4)+5 wt. % Al2O3, LiAlO2, LLZO, or LATSP (Li1.7Al0.3Ti1.7Si0.4P2.6O12) nanoparticles as the catholyte, lithium metal as the anode, and Celgard polypropylene membrane (25 μm) as a separator. For initial studies, the electrolyte system was 1.1 M LiPF6 mixed solvent (1:1:1 wt. % ratio) EC:DEC:EMC with 10 wt. % fluoroethylene carbonate (FEC). Before cell assembly, the metallic Li (16 mm W×750 μm T) was scraped to expose a clean surface. The 2032 coin cells were compressed using a ˜0.1 kpsi uniaxial pressure. The electrochemical values of three half-cells were averaged as shown in
The half-cell shows an initial charge capacity of 150 mAh/g at 0.3 C. The discharge capacity gradually decreases to 120 mAh/g after 50 cycles (
The core scan of LMNO (Li1.1Mn1.5Ni0.5O4)−10 wt. % LATSP (Li1.7Al0.3Ti1.7Si0.4P2.6O12) electrode after 100 cycles shows the presence of double P 2p peaks centered at 132 and 135 eV corresponding to the presence of P—O—F and P—F bonds (
However, it is worth noting that a shift can be observed between the BEs measured for pure salts, and the BEs measured for small amounts of lithium salts at the electrodes' surfaces. This phenomenon is due to the XPS differential charging effect induced by the presence of insulating species at the surfaces of conducting electrodes.
The Al 2p spectra shows an unexpected trend. The symmetric peak centered at ˜73 eV for the LMNO (Li1.1Mn1.5Ni0.5O4)−10 wt. % Al2O3 is characteristic of LiAlO2, indicating the lithiation of alumina after extensive cycling. The binding energy shifts to higher values on cycling for LMNO (Li1.1Mn1.5Ni0.5O4)−5 wt. % Al2O3(
The mechanism of substitution proposed by Van Landschoot et al. [Ref. 22] is:
Al2O3+2HF→Al2O2F2+H2O
and further reaction with HF leads to Al2OF4 and ultimately AlF3. Based on the Al 2p binding energy value ˜75 eV, we would expect that only Al2O2F2 forms. The full transformation of Al2O3 into fluorinated species is not achieved after 100 cycles for Al2O3 (10 wt. %) coated electrodes as the Al—O2− signal at 73 eV is still seen. We, therefore, expect that the full fluorination to AlF3 requires a much larger number of cycles, thus indicating that nano-Al2O3 is a long-standing protective coating.
Half-cells were assembled using LiNixMnyCozO2, wherein x+y+z=1 and x:y:z=6:2:2 (NMC 622)+5 wt. %, 10 wt. %, and 20 wt. % LATSP (Li1.7Al0.3Ti1.7Si0.4P2.6O12) as catholyte, lithium metal as the anode, and Celgard polypropylene membrane (25 μm) as a separator. For initial studies, the electrolyte system was 1.1 M LiPF6 mixed solvent (1:1:1 wt. % ratio) ethylene carbonate (EC), dimethyl carbonate (DMC), and ethyl methyl carbonate (EMC) with 10 wt. % fluoroethylene carbonate (FEC). Before cell assembly, the metallic Li (16 mm W×750 μm T) was scraped to expose a clean surface. The 2032 coin cells were compressed using a ˜0.1 kpsi uniaxial pressure.
Lithium-ion batteries (LIBs) are used extensively in electronics, electric vehicles, stationary power storage, and a multitude of related renewable energy applications attributed to their high energy and power densities [Ref. 31,32]. However, in current designs, LIBs based on commercial carbonaceous anode materials cannot meet the fast charge capabilities required for many large-scale applications due to serious safety problems associated with high charge/discharge rates [Ref. 33,34]. Given the low galvanostatic potential (˜0 vs Li+/Li) of current graphitic anodes, [Ref. 35,36] higher charging rates may cause (especially uneven) lithium plating generating internal short-circuits leading to catastrophic failure of traditional LIBs [Ref. 7,8]. Thus, to enable fast charging and improve LIB safety; numerous noncarbonaceous anodes have been explored [Ref. 39-41]. Among the possible alternate anode materials, lithium titanium oxides, such as Li4Ti5O12 (LTO), have been considered very promising due to excellent thermal stability, high structural stability, good cyclability at high current densities, and negligible irreversible capacity [Ref. 42-44].
Spinel LTO anodes can facilitate up to three Li+ ions per formula unit and deliver theoretical capacities ˜175 mAh g−1 without significant volume changes (<1%) when cycled [Ref. 45-47]. Graphite anodes in contrast expand up to 10 vol % during charging [Ref. 42]. This negligible volume change (zero-strain) property of LTO provides high structural stability, potentially enabling high charge/discharge rates thereby improving LIBs' versatility [Ref. 42,48,49]. In addition, LTO's operating potential is greater than the reduction voltage of conventional electrolyte solvents (propylene carbonate and ethylene carbonate), an attractive feature for rate performance [Ref. 50,51] Unfortunately, pristine spinel LTO exhibits poor electronic conductivity (10−13 S cm−1) [Ref. 52]. attributed to the Ti4+ valence state and low Li+ diffusion coefficient (10−9-10−14 cm2 s−1) resulting in capacity loss and poor rate capability, which limits its usage in practical applications [Ref. 52-54]. To date, numerous methods have been explored to ameliorate the electronic conductivity and Li+ diffusivity [Ref. 42,55-57 The most common method focuses on doping with metallic (Cr3+, Ca2+, Ga3+, Mg2+, Ta5+, and Al3+) [Ref. 58-61] and nonmetallic (Br−, Cl−, and F−) [Ref. 62-64] ions to increase lattice electrical conductivity through partial reduction of Ti4+ to Ti3+.
Several efforts have been investigated to increase the electrical conductivity of LTO through surface modifications via conductive coatings [Ref. 65-68]. Although carbon-coatings offer a very efficient way to improve LTO anode rate capabilities, they also decrease cell's volumetric energy densities [Ref. 42,69]. Furthermore, fabrication of uniform and optimized carbon coated LTO using economically facile techniques remains challenging [Ref. 42].
Syntheses of nano LTO particles including nanorods, nanotubes, and nanowires offers an efficient strategy to improve LTO electrochemical performance [Ref. 70-72]. It is well-known that nanostructured active materials can enhance both electron and Li+ migration by shortening diffusion pathways and providing excess surface lithium storage ascribed to their large surface areas and small sizes [Ref. 32,67]. In addition, LTO NPs will have larger contact area between the electrolyte and electrode, resulting in improved intercalation kinetics. These phenomena contribute to enhance the rate capabilities of nanostructured LTO compared to bulk LTO. Multiple synthesis methods have been explored in efforts to prepare spinel LTO including sol-gel, hydrothermal synthesis, solution-combustion, and spray pyrolysis [Ref. 73-76]. However, these routes often offer low yields, involve complicated procedures, high costs, and toxic precursors detracting from commercialization practicality.
Therefore, the synthesis of nanoscale LTO materials with controlled morphologies, phase purity, and using low-cost methods is highly desirable for assembly of LTO batteries. This Example prepares LTO NPs using liquid-feed flame spray pyrolysis (LF-FSP).
Recent publications indicate that the introduction of appropriate amounts of solid electrolytes [LiAlO2, Li1.3Al0.3Ti1.7(PO4)3 (LATP), and Li0.33La0.56TiO3] into a LTO anode is an effective, low-cost route to improve the electronic and ion transport of LTO [Ref. 54, 69, 77]. Thus, Han et al. [Ref. 74] reported that added LATP can coat and/or bridge LTO particles, thereby facilitating Li+ diffusion from electrolyte to the active material and improving electron migration to the current collector (Cu) by virtue of LATP's high ionic (6.2×10−5 S/cm) [Ref. 78] and electronic conductivities (5×10−11 S/cm) [Ref. 79]. However, these studies use solid-state reaction methods (calcining >700° C.) to synthesize LTO-solid electrolyte composites, which makes it difficult to obtain nanostructured LTO particles as a result of particle necking.
Recently, we demonstrated that LF-FSP derived LiAlO2 ceramic electrolytes offer optimal ionic conductivities (˜10−6 S/cm) and electronic conductivities of 6.7×10−10 S/cm at ambient, both 3 orders of magnitude higher than those reported for LTO (Table 1) [Ref. 80]. Hence, LTO-LiAlO2 composite anodes were prepared via simple ball-milling. We coincidentally reported the synthesis and characterization of a novel polymer electrolyte (Li6SiON) derived from rice hull ash (RHA), an agricultural waste, providing a green route to all-solid-state batteries (Scheme 1) [Ref. 81]. In our effort to synthesize the Li6SiON polymer electrolyte, we realized that it might also be possible to use this precursor to coat LTO NPs. The Li6SiON electrolyte offers a room temperature (Table 1) ionic conductivity of 10−6 S/cm and electrical conductivity of 10−7 S/cm six orders of magnitude greater than that of LTO.
In this Example, we synthesized high surface area (˜38 m2/g) spinel LTO NPs using LF-FSP. Contrary to the typical solid-state reaction, this method eliminates glass forming, grinding, and ball milling steps. In addition, LF-FSP derived LTO NPs are agglomerated but not necked which is crucial for facile dispersion and tape-casting. To enhance the electrical conductivity of LTO anodes, the LTO was mixed with flame made LiAlO2 NPs (APS=64 nm; 5 and 10 wt. %) and coated with Li6SiON polymer precursors (5 and 10 wt. %).
To the best of our knowledge, this is the first time three component composite anodes, e.g., LTO-5 wt. % LiAlO2-10 wt. % Li6SiON, have been explored as an approach to improving LTO's rate capabilities. The composite anode exhibited a specific capacity of ˜217 mAh/g at 5 C for 500 cycles. The modified LTO NPs were characterized via XRD, XPS, SEM, EIS, and performance tests, as described in the following sections.
Lithium hydroxide monohydrate (LiOH·H2O) and propionic acid [(CH3CH2COOH), 99%] were purchased from Sigma-Aldrich (Milwaukee, Wis.). Titanium isopropoxide [Ti(OiPr)4] and hexane were purchased from Fischer Scientific (Pittsburgh, Pa.). Absolute ethanol was purchased from Decon Labs (King of Prussia, Pa.). RHA was provided by Wadham Energy LP (Williams, Calif.). The solvent and reactants, 2-Methyl-2,4-pentanediol (hexylene glycol, HG) and lithium amide (LiNH2) were purchased from Acros Organics. Lithium metal foil (˜750 μm), polyvinylidene fluoride [PVDF, (Mw˜534 kg/mol)], sodium hydroxide (NaOH), hydrochloric acid (HCl), and tetrahydrofuran (THF) were purchased from Sigma-Aldrich (St Louis, Mo.). Super C65 conductive carbon powder (˜62 m2/g), Celgard 2400 polypropylene separator membrane (˜25 μm), and coin cell parts were purchased from MTI Corporation (Richmond, Calif.). The mixed solvent of ethylene carbonate (EC), dimethyl carbonate (DMC), and ethyl methyl carbonate (EMC) (1:1:1 wt. %) containing 1 M LiPF6 as the Li salt with the addition of 10 wt. % fluoroethylene carbonate (FEC) was purchased from Soulbrain (Northville, Mich.). THF was distilled over sodium benzophenone ketyl prior to use. All other chemicals were used as received.
The synthesis procedures for titanatrane {Ti(OCH2CH2)3N—[OCH2CH2N(CH2CH2OH)2]} and lithium propionate [LiO2CCH2CH3] are discussed in our previous work [Ref. 82].
X-ray diffraction (XRD). A Rigaku Rotating Anode Goniometer (Rigaku Denki., LTD., Tokyo, Japan) was used to identify the phases and characterize the degree of crystallinity of as produced NPs using Cu Kα (λ=1.54 Å) radiation operating at a working voltage of 40 kV and a current of 100 mA. Scans were continuous from 10 to 70° 2θ using a scan rate of 5° min−1 in 0.01 increments. The presence of crystallographic phases and their wt. % fractions were refined by using PDXL 2018 (Version 2.8.4). For Rietveld refinement, a model was imported from the Inorganic Crystal Structure Database (ICSD).
Specific surface area (SSA) analyses. SSA data was obtained using a Micromeritics ASAP 2020 sorption analyzer. Before sample analysis at −196° C. (77 K)/N2, NPs samples (400 mg) were degassed at 300° C./5 h. BET method using ten data multipoint with relative pressures of 0.05-0.30 was used to determine SSAs. Average particle sizes (APS) of the as-produced NPs were determined by converting their respective SSAs using the equation APS=6/(SSA×p), where the net density of LTO (3.5 g/cm3) was used.
Scanning electron microscopy (SEM). A JSM-IT300HR In Touch Scope SEM (JEOL USA, Inc.) was used to analyze the microstructure of as-produced NPs and composite electrodes.
Thermogravimetric analysis (TGA). Q600 simultaneous TGA/DSC (TA Instruments, Inc.) was used to analyze the thermal stability and fraction of volatile components of as-produced NPs. The samples (15-25 mg), hand-pressed in a 3-mm dual-action die, were placed in alumina pans and ramped to 700° C. at 10° C. min−1/air (60 mL min−1).
X-ray photoelectron spectroscopy (XPS) Kratos Axis Ultra (Kratos Analytical) was used to determine the elements present. XPS system at room temperature under 3.1×10−8 Pa using monochromatic Al source (14 kV and 8 mA) was used to record the core level atoms. Binding energies of all the elements were calibrated relative to the gold with Au 4f7/2 at 84 eV. For each sample, a wide-scan survey was done on three separate points for better accuracy. All the data were analyzed by CASAXPS software.
Electrochemical impedance spectroscopy (EIS) was measured using a SP-300 (Bio-Logic Science Instruments, Knoxville, Tenn.) over a frequency range of 100 kHz to 0.01 Hz with an AC amplitude of 10 mV. The open-circuit voltage (OCV˜2.7 V) and cyclic voltammetry (CV) tests were carried out using the SP-300 potentiostats/galvanostat. The charge-discharge measurements on the half-cell were performed between 0.0-2.5 V (vs Li/Li+) using a multi-channel Maccor battery test system (MACCOR, USA).
Lithium propionate (26.5 g) and titanatrane (236.8 g) were dissolved in anhydrous ethanol (1650 mL) to give a 3 wt. % ceramic yield solution. To avoid the loss of lithium during the combustion process, excess lithium propionate (100 wt. %) was used. The LF-FSP method was used to produce LTO NPs. A detailed description of LF-FSP process can be found elsewhere [Ref. 53].
The as-produced LTO NPs (10 g) were dispersed in anhydrous ethanol (350 mL) with 2 wt. % poly(acrylic acid) using an ultrasonic horn (Vibra-cell VC 505 Sonics & Mater. Inc.) for 10-15 minutes operating at 100 W. The suspension was left to settle for 5 hours to remove impurities and allow larger particles to settle. To remove the impurities the suspension was left to settle for 5 hours and the recovered supernatant was dried at 100° C./24 and heated to 700° C./2 h/O2, hereafter referred to as pristine LTO.
LiAlO2 NPs were also synthesized using the LF-FSP method as discussed in our previous work [Ref. 80]. We recently reported the direct distillative extraction of silica from RHA as the spirosiloxane, [SP=(C6H6O2)2Si]. SP reacts with xLiNH2 to provide in oligomeric mixtures denoted as LixSiON (x=2, 4, and 6) polymers with varying Li and N contents per Scheme 1 shown in
In our effort to enhance the electrical conductivity of LTO, composite anodes were processed by adding selected wt. % LiAlO2 solid and Li6SiON polymer electrolytes during electrode formulation per Table 2.
The LTO and LiAlO2 NPs (5 and 10 wt. %) were dry ground for ˜30 minutes in air to ensure uniform mixing. The LTO-LiAlO2 mixtures, dispersed in anhydrous ethanol (5 mL), were ball-milled for 24 hours using ZrO2 beads (6 g, 3 mm) in 20 mL vial under nitrogen. The slurries were then heated at 100° C./24 h/vacuum. In a separate step, LTO NPs and Li6SiON polymer precursor (5 and 10 wt. %) dissolved in THF then ultrasonicated at 100 W for 5-10 minutes. The recovered mixtures were then dried at 100° C./24 h/vacuum. To evaluate the synergistic effects of the LiAlO2 and Li6SiON electrolytes, composite electrodes are synthesized by mixing the LTO-LiAlO2 powders with LTO-Li6SiON powders. Scheme 2 in
Before electrode fabrication, pristine LTO and carbon black (C65) were heated to 100° C./24 h/vacuum to remove trace moisture and eliminate oxygenated carbon species. Electrode slurries were prepared by mixing pristine LTO or LTO composites (80 wt. %), C65 (10 wt. %), and polyvinylidene fluoride (PVDF) (10 wt. %) in 1-methyl pyrrolidin-2-one.
The LTO-Li6SiON mixtures were ultrasonicated for 10-15 min/N2 to give homogeneous slurries. The LTO-LiAlO2 mixtures were ball milled for 24 hours using ZrO2 beads (6 g) in 20 mL vials and then coated onto current collector (Cu foils, 16 μm). After drying at 80° C./12 h/vacuum, the electrodes were cut into 8 mm discs, and thermo-pressed at 40-50 MPa/50° C./5 min using a heated benchtop press (Carver, Inc.) to improve packing density. The electrodes have areal loading densities ranging from 3 to 4 mg/cm2. LTO-composite-Li half cells were assembled following the standard coin cell procedure discussed elsewhere [Ref. 84]. Briefly, NMC622 was used a cathode, Celgard 2400 polypropylene membrane as a separator, and a solution of 1.1 M LiPF6 in a mixture solvent of EC:DC:DMC (weight ratio of 1:1:1) with 10 wt. % FEC additives as the electrolyte. The assembly process was conducted in an argon-filled glove box having 02 and H2O contents below 0.5 ppm. The coin cells were compressed using a ˜0.1 kpsi uniaxial pressure (MTI).
In this section, we primarily characterize pristine LTO NPs and composite anodes by XRD, FTIR, SEM, and TGA. In the second part, we discuss the electrochemical properties of half-cells assembled using the LTO-composite electrodes. The effect of the LiAlO2 solid electrolyte and Li6SiON polymer electrolyte additives on the rate performance of the LTO were also investigated.
The XRD powder patterns of LTO-pristine, LTO-LiAlO2, and LTO-Li6SiON composites are shown in
The FTIR spectra of LTO-pristine and LTO-composite powders are presented in
The two broad absorption bands centered at 650 and 465 cm−1, respectively, are due to the symmetric and asymmetric stretching vibrations of lattice [MO6] octahedral groups confirming the presence of spinel LTO [Ref. 56].
High performance LTO anodes are available using nanostructured materials because such materials offer larger contact areas with electrolyte, shorter diffusion distances for Li+ and electrons, and excess near-surface lithium storage in comparison with micron-size LTO anodes [Ref. 57, 71]. The solid-state reaction method is simple; however, product quality is not satisfactory due to particle inhomogeneities, large APSs, and irregular morphologies. In contrast, we are able to the design and prepare uniform, nanoscale LTO electrodes for high performance applications.
As noted above, high surface area is an important characteristic of nanostructured materials. The BET SSA of pristine LTO is 37±0.8 m2/g. The calculated APS using the BET surface area is ˜46 nm for the pristine LTO. The LTO-10 wt. % LiAlO2 sample shows a slight decrease to 31 m2/g and increase in APS (54 nm) attributed to the relatively larger LiAlO2 APS (64 nm) [Ref. 80].
The thermal stability of the composite powders was investigated by TGA.
The surface chemical composition and binding energies of the LTO-pristine and LTO-composite electrodes were analyzed by XPS. The survey spectra (
The core level spectra of the Al 2p (74.8 eV) peak increases with increasing LiAlO2 content (10 wt. %), a consequence of LiAlO2 particles associated with the surface of LTO particles (
The survey spectra (
Electrochemical impedance spectroscopy (EIS) was performed on the LTO composite electrode-Li half-cells before cycling. The corresponding Nyquist plots are presented in
where R is the gas constant, T is the absolute temperature, F is the Faraday constant, A is the area of the electrode, n is the number of electrons per molecule during oxidation, Cu is the concentration of Li+ in solid, ω is the angular frequency, f is the frequency, and σ is the Warburg factor which is related to Zre obtained from the slope of the line in
All of the Nyquist spectra (
The calculated Li+ diffusion coefficients for pristine LTO, LTO-LiAlO2, and LTO-Li6SiON are listed in Table 3. LTO-5 wt. % LiAlO2-10 wt. % Li6SiON has the highest diffusion coefficient (˜2.7×10−12) among the LTO electrodes reported here. This study demonstrates that introduction of an appropriate amount of solid electrolyte enhances the electrochemical performance of LTO.
The electrochemical performance of LTO-pristine, LTO-LiAlO2, LTO-Li6SiON, and LTO-LiAlO2—Li6SiON electrodes was investigated by galvanostatic cycling test at different C-rates (0.5, 1, and 5 C) between 1 and 2.5 V. Pristine LTO (
The discharge capacity for pristine LTO half-cell decreases to ˜125 mAh/g at 5 C. However, capacities for LTO-5 wt. % LiAlO2 and LTO-10 wt. % Li6SiON fade slowly remaining stable at 146 and 160 mAh/g at 5 C, respectively. The LTO-5 wt. % LiAlO2-10 wt. % Li6SiON exhibits a discharge capacity (˜140 mAh/g) at 5 C. On the whole, the LTO-Li6SiON and LTO-LiAlO2 electrodes reveal enhanced rate capacity relative to pristine LTO.
After 100 cycles, the specific capacities are 155±0.7, 142±, 156±0.5, and 162±0.2 mAh/g at 0.5 C for the half-cells assembled with LTO-5 wt. % LiAlO2, LTO-10 wt. % LiAlO2, LTO-5 wt. % Li6SiON, and LTO-10 wt. % Li6SiON electrodes, respectively. The reversible capacities of LTO-Li6SiON decrease slowly compared to those for LTO-LiAlO2 and the pristine LTO electrodes. However, the LTO-10 wt. % LiAlO2-5 wt. % Li6SiON and LTO-10 wt. % LiAlO2-10 wt. % Li6SiON composite electrodes show relatively low discharge capacities of 127 and 131 mAh/g after 100 cycles. To understand the reason why the LTO-10 wt. % LiAlO2-5 wt. % Li6SiON and LTO-10 wt. % LiAlO2-10 wt. % Li6SiON capacities (
This might be ascribed to the larger quantity LiAlO2, which significantly reduces the amount of active material LTO, resulting in lower capacity retention. This is consistent with what is reported in the literature for LTO-LiAlO2 (10 wt. %) composite electrodes [Ref. 77]. In addition, as discussed above in the diffusivity section, the LTO-10 wt. % LiAlO2-10 wt. % Li6SiON composite did not show a high Li+ diffusivity coefficient when compared to the LTO-5 wt. % LiAlO2-10 wt. % Li6SiON electrode.
The reversible capacities found for LTO-5 wt. % LiAlO2-10 wt. % Li6SiON (260 mAh/g) and LTO-10 wt. % Li6SiON (231 mAh/g) are much higher than those of LTO-pristine electrodes (202 mAh/g) at 0.5 C as demonstrated in
The high rate performance of the LTO-5 wt. % LiAlO2-10 wt. % Li6SiON electrodes is attributed to:
In this Example, a facile LF-FSP method enabled the synthesis of high surface area, phase pure LTO NPs using a low-cost precursor. Pristine LTO was mixed with LiAlO2 and Li6SiON electrolytes to improve the ionic and electronic conductivity by simple ball-milling and ultrasonication methods. The microstructure studies show that the composite powders are homogeneous with particle sizes <60 nm. XPS and EDX studies further confirm that the surface of the LTO particles is uniformly coated with the polymer electrolyte. By virtue of the high electrical conductivity of LiAlO2 and Li6SiON electrolyte, the LTO composite electrodes with optimal LiAlO2 (5 wt. %) and Li6SiON (10 wt. %) electrolyte additives exhibit excellent rate performance delivering reversible capacity of 260 and 140 mAh/g at 0.5 and 10 C, respectively.
First, polyacrylonitrile (MW 150 g/mol PAN) (200 mg) and S8 (750 mg) were mixed and ground together using a mortar and pestle for 5 minutes. After that, 50 mg of high surface area carbon (C) (1700 m2 g−1) was added to the mixture and ground together again for 5 minutes, and then PAN-C—S pellets were pressed from this powder at 5 ksi/RT/5 min using a benchtop press (Carver, Inc.) using a 13 mm die set (Across International).
The PAN-C—S pellets were wrapped separately in Al foil to minimize S evaporation during heating. They were placed in a crucible, which was also wrapped in Al foil. The heating regime was “30° C.→400° C./5 h at 5° C./min in N2” and then “400° C.→30° C. at 5° C./min in N2”.
Table B shows the detailed information about C—S pellets after heating and soaking in CS2.
The S content in the heated PAN-C—S pellets was about 46 wt. %. The heated PAN-C—S pellets were ground using a mortar and pestle and put in folded filter paper. Thereafter, they were soaked in CS2 for 24 hours. This S extraction process was repeated two times with fresh CS2. The C—S composites were then vacuum dried at 80° C. for XPS analysis (to determine the S content) and slurry preparation. The average S content is about 42 wt. % by XPS.
Table C shows the information about slurries.
First, 15 wt. % PVDF (MW: 534 kg/mol) was dissolved in 5.5 ml of distilled N-methyl-2-pyrrolidone (NMP) in a 20 ml-vial. Then 70 wt. % C—S composites in Table B and 15 wt. % carbon (Super C65, MTI Corporation) were added to the solution. In the other 20 ml-vial (Sample 2 in Table C), 15 wt. % LATSP was added to the C—S composite aiming for suppressing uncontrolled lithium polysulfides diffusion during battery cycling.
The vials were shaken for several minutes until nothing stuck to the bottom of the vials. They were sealed with tape and ball-milled with a tumbler (Model: 71637284, Fasco Industries, inc.) for 24 hours to break up agglomerates and obtain a homogeneous suspension.
The samples were cast on Al foil and the thickness of the as-cast film was controlled by adjusting the gap (160 μm) between the wire wound rod coater and Al substrate. The dried film will be cut into small round pieces with a diameter of 1.2 cm using a hammer and arch punch.
The S electrodes were thermo-pressed at 5 ksi/50° C./5 min before Li—S half-cell assembly.
After vacuum drying at 80° C. for 24 hours, the PAN-C—S electrodes were transferred to an Ar-filled glovebox. Half-cells were assembled using the S electrodes as cathode and Li metal as the anode. Before cell assembly, the metallic Li (16 mm W×750 μm T) was scraped to expose a clean surface in the glovebox. The electrolyte system was 1.1 M LiPF6 mixed solvent (1:1:1 wt. % ratio) ethylene carbonate (EC):dimethyl carbonate (DMC):ethyl methyl carbonate (EMC) with 10 wt. % fluoroethylene carbonate (FEC). A Celgard 2400 polypropylene membrane separator was introduced. The 2032-coin cells were compressed using a ˜0.1 ksi uniaxial pressure.
The half-cell was cycled from 1 to 3 V for 102 cycles and the galvanostatic cycling profile shows that the cell was cycled for the first 2 cycles at 0.1 C, for 20 cycles at 0.25, 0.5, 1, 2C and the last 20 cycles at 0.25 C.
The initial discharge capacity was ˜1706 mAh/g which decreased to ˜1070 mAh/g after the 1st cycle. As shown in
The half-cell was cycled from 1 to 3 V for 102 cycles and with the first 2 cycles at 0.1 C, then 20 cycles at 0.25, 0.5, 1, 2 C and the last 20 cycles at 0.25 C.
The initial discharge capacity was ˜1730 mAh/g and this capacity decreased to ˜1110 mAh/g after the 1st cycle. As shown in
The results suggest 15 wt. % LATSP in S cathodes can make a more stable Li—S system and the discharge capacity of a Li—S half-cell with 15 wt. % LATSP can be ≥1000 mAh g−1 at 0.5 C as shown in
In a nutshell,
Viewed in this way, adding LATSP nanopowders to C—S composites can be promising because they can trap LiPSs effectively and improve the slow redox reaction between Li-ions and S during battery cycling unlike normal metal oxides used only for capturing LiPSs in S cathodes.
We also tested the use of LiAlO2 nanopowder as shown in
The half-cell was scheduled from 1 to 3 V for 102 cycles and monitored for 95 cycles. The galvanostatic cycling profile shows that the cell was cycled for the first 2 cycles at 0.1 C, for 20 cycles at 0.25, 0.5, 1C, and 2 C, and the last 13 cycles at 0.25 C.
The obtained initial discharge capacity was ˜1084 mAh/g and this discharge capacity de-creased to ˜761 mAh/g after the 1st cycle. As shown in
For comparison, we also used a solid polymer electrolyte, Li6SiPON, for coating.
The half-cell was scheduled from 1 to 3 V for 102 cycles and monitored for 102 cycles. The galvanostatic cycling profile shows that the cell was cycled for the first 2 cycles at 0.1 C, for 20 cycles at 0.25, 0.5, 1C, and 2 C, and the last 20 cycles at 0.25 C.
The obtained initial discharge capacity was ˜476 mAh/g and this discharge capacity in-creased to ˜977 mAh/g after the 1st cycle. As shown in
To summarize these studies, reference is made to
LTO-20 wt. % LATSP electrodes were investigated as an alternative anode as they demonstrate good rate performance and optimal Li+ diffusivity. NMC 622}−20 wt. % LATSP (Li1.7Al0.3Ti1.7Si0.4P2.6O12) electrodes were used as the catholyte and 60 wt. % PEO/Li6PON was used as a polymer electrolyte and separator. The full cells were warm pressed at 10 kpsi/50° C./5 minutes. The full cell was dried at 60° C./12 hours/vacuum prior to assembly in the glove box. Three stainless steel spacers were used to ensure good contact between the coin cell parts.
The ASSB shows an initial discharge capacity of 160 mAh/g at 0.01 C. However, this capacity was not reversible as the charge capacity is ˜80 mAh/g. The discharge capacity decreases to 100 mAh/g as the C-rate increases to 0.1 C. A charge capacity of ˜80 mAh/g was maintained for the 20 cycles. The discharge and charge capacities decreased to 90 and 70 mAh/g at 0.5 C. The ASSB capacity recovers back to ˜100 mAh/g discharge capacity when the C-rate is decreased to 0.1 C. The ASSB demonstrates high columbic efficiency attributed to the gap between charge and discharge capacities.
Without intending to be bound by theory, coatings as presented in the above examples likely function via a variety of mechanisms. Among these, the introduction of high surface area lithium-ion sources directly coating the catholyte and anolyte active materials almost certainly improves the concentration of lithium ions at the interface with the active material thereby enhancing transport across interfaces. However, other operative mechanisms are also likely. For example, for catholytes that generate Mn2+ that dissolves in liquid electrolytes degrading capacity, the high surface area, the high energy surfaces of the NPs will give up Li+ to the surroundings resulting in surfaces that are highly negatively charged. Given that Mn2+ is a di-cation, one expects that such species will electrostatically bind more strongly to NP surfaces than Li+ becoming trapped and are thereby prevented from degrading anolytes. For the Li—S system, one can envision that polysulfides might also wrap around the NPs if sufficient positive ion cites remain or to underlying metal cations or simply be trapped in the narrow pores of the NP coating. In addition, the high surface area NPs can be anticipated to trap free F− preventing or minimizing corrosion. Perhaps most important is that the presence of NPs at surfaces can be anticipated to strongly effect the electrostatic field near interfaces thereby changing the character of the individual double layer.
In this Example, overlithiated LMNO (Li1.26Mn1.5Ni0.5O4) nano-size particles (synthesized using LF-FSP) were coated with LiAlO2 nano-size particles. To differentiate this material from LMNO (Nano One) in Example 1, the nano-size, overlithiated LMNO will be referred to as “n-LMNO.” Unlike most coating processes, the method involved the use of a soft and scalable ball milling technique in which 5 wt. %-20 wt. % of the active nanoparticles were introduced to n-LMNO just before electrode fabrication. The n-LMNO powder and carbon black (C-65) were heated to 100° C./24 hours/vacuum. The electrode slurries were prepared by mixing n-LMNO (60-80 wt. %), C65 (5-10 wt. %), nanoparticles (5-20 wt. %), and PVDF (10 wt. %) in 1-methyl pyrrolidin-2-one. The mixtures were then ball-milled for 24 hours using yttria-stabilized zirconia beads (3 mm, 6 g). The slurries were then coated on Al foil.
Half-cells were assembled using n-LMNO+0 wt. %, 5 wt. %, 10 wt. %, or 20 wt. % nano-LiAlO2 (same nano-LiAlO2 as used in Example 1 above) as catholyte, Li as the anode, and Celgard (25 μm) as a separator. For initial studies, the electrolyte system was 1.1 M LiPF6 mixed solvent (6:2:2 vol. % ratio) EC:DEC:EMC with an added 10 wt. % FEC and 0.02M lithium bis(oxalato)borate. Before cell assembly, the metallic Li (16 mm W×750 μm T) was scraped to expose a clean surface. The 2032 coin cells were compressed using a ˜0.1 kpsi uniaxial pressure. The electrochemical values of duplicate half-cells were averaged as shown in
The half-cell shows an initial charge and discharge capacity of 155 and 113 mAh/g at 0.3 C, respectively. The discharge capacity gradually decreases to 96 mAh/g after 50 cycles [
The half-cell shows an initial charge and discharge capacity of 179 and 114 mAh/g at 0.3 C, respectively [
As shown in
It stands to reason that if the system did not have a Li (usually in excess), perhaps this high first cycle capacity could contribute/start forming a Li reservoir on/in a Li-poor anode (i.e., Cu foil). This new Li reservoir could enable an anode-free system, starting only with an anode current collector with no active material. Additionally, in a system where the anode is known to also show low 1st cycle columbic efficiency, perhaps the excess charge capacity from the n-LMNO+x wt. % LiAlO2 (x=10, 20) could be sacrificed as irreversible capacity loss on the anode side (i.e., Si-based anode). The opportunity in this scenario would be donating excess Li from the cathode to be consumed in irreversible SEI formation on high-capacity anodes (i.e., Si-based anodes).
It is important to also note that the 20 wt. % LiAlO2 promoted system is the most stable of the half cells tested demonstrating that imperfect nano-nano systems also offer superior behavior to uncoated systems.
The citation of any document or reference is not to be construed as an admission that it is prior art with respect to the present invention.
Thus, the present invention provides coatings that enhance battery component performance.
In light of the principles and example embodiments described and illustrated herein, it will be recognized that the example embodiments can be modified in arrangement and detail without departing from such principles. Also, the foregoing discussion has focused on particular embodiments, but other configurations are also contemplated. In particular, even though expressions such as “in one embodiment”, “in another embodiment,” or the like are used herein, these phrases are meant to generally reference embodiment possibilities, and are not intended to limit the invention to particular embodiment configurations. As used herein, these terms may reference the same or different embodiments that are combinable into other embodiments. As a rule, any embodiment referenced herein is freely combinable with any one or more of the other embodiments referenced herein, and any number of features of different embodiments are combinable with one another, unless indicated otherwise.
Although the invention has been described in considerable detail with reference to certain embodiments, one skilled in the art will appreciate that the present invention can be used in alternative embodiments to those described, which have been presented for purposes of illustration and not of limitation. Therefore, the scope of the appended claims should not be limited to the description of the embodiments contained herein.
This application claims priority to U.S. Patent Application No. 63/296,601 filed Jan. 5, 2022.
This invention was made with government support under DMR1926199 awarded by the National Science Foundation—Division of Materials Research. The government has certain rights in the invention.
| Number | Date | Country | |
|---|---|---|---|
| 63296601 | Jan 2022 | US |
