Nanopowder Coatings That Enhance Lithium Battery Component Performance
20230216040 · 2023-07-06
Inventors
- Richard M. Laine (Ann Arbor, MI)
- ELENI TEMECHE (Ann Arbor, MI, US)
- TAYLOR BRANDT (Ann Arbor, MI, US)
- PHILYONG KIM (Ann Arbor, MI, US)
Cpc classification
H01M4/62
ELECTRICITY
H01M4/5825
ELECTRICITY
H01M4/525
ELECTRICITY
H01M4/505
ELECTRICITY
H01M4/131
ELECTRICITY
H01M2004/021
ELECTRICITY
Y02E60/10
GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
International classification
H01M4/36
ELECTRICITY
Abstract
An electrode for an electrochemical device is disclosed. 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: (i) lithium aluminum oxides, (ii) lithium containing phosphates, (iii) Li.sub.xPON wherein x is 1, 1.5, 3, or 6, (iv) Li.sub.xSiPON wherein x is 1, 1.5, 3, or 6, (v) Li.sub.xSiON wherein x is 2, 4, or 6, (vi) lithium lanthanum zirconium oxides, and (vii) mixtures of two or more of (i), (ii), (iii), (iv), (v), and (vi).
The porous coating comprising the solid-state ion conducting electrolyte material may be formed from one or more precursors that form the porous coating comprising the solid-state ion conducting electrolyte material upon cycling of the electrochemical device.
Claims
1. An electrode for an electrochemical device, the electrode comprising: a lithium host material; and a porous coating on the lithium host material, the porous coating comprising a solid-state ion conducting electrolyte material selected from the group consisting of: (i) lithium aluminum oxides, (ii) lithium containing phosphates, (iii) Li.sub.xPON wherein x is 1, 1.5, 3, or 6, (iv) Li.sub.xSiPON wherein x is 1, 1.5, 3, or 6, (v) Li.sub.xSiON wherein x is 2, 4, or 6, (vi) a ceramic electrolyte material having the formula Li.sub.uRe.sub.vM.sub.wA.sub.xO.sub.y 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.
2. The electrode of claim 1 wherein: the porous coating comprising the solid-state ion conducting electrolyte material is formed from one or more precursors that form the porous coating comprising the solid-state ion conducting electrolyte material upon cycling of the electrochemical device.
3. The electrode of claim 1 wherein 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.
4. The electrode of claim 3 wherein: the one of the solid-state ion conducting electrolyte material 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.
5. The electrode of claim 1 wherein: the electrode has a thickness between 1 and 200 micrometers, and the porous coating has a thickness between about 20 nanometers and about 10 micrometers, and the porous coating comprises particles having an average particle size between 1 and 100 nanometers.
6. The electrode of claim 1 wherein: the electrode is a cathode, and the lithium host material 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 LiMPO.sub.4 wherein M is one or more of cobalt, iron, manganese, and nickel, and (iii) materials having a formula LiNi.sub.xMn.sub.yCo.sub.zO.sub.2, 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).
7. The electrode of claim 1 wherein: the solid-state ion conducting electrolyte material comprises a lithium aluminum oxide.
8. The electrode of claim 1 wherein: the solid-state ion conducting electrolyte material comprises a lithium containing phosphate.
9. The electrode of claim 1 wherein: the solid-state ion conducting electrolyte material comprises Li.sub.xPON wherein x is 1, 1.5, 3, or 6.
10. The electrode of claim 1 wherein: the solid-state ion conducting electrolyte material comprises Li.sub.xSiPON wherein x is 1, 1.5, 3, or 6.
11. The electrode of claim 1 wherein: the solid-state ion conducting electrolyte material comprises Li.sub.xSiON wherein x is 2, 4, or 6.
12. The electrode of claim 1 wherein: the solid-state ion conducting electrolyte material comprises the ceramic electrolyte material.
13. The electrode of claim 1 wherein: 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.
14. The electrode of claim 1 further comprising: silica depleted rice hull ash.
15. An electrochemical device comprising: the electrode of claim 1 as a cathode; an anode; and an electrolyte positioned between the cathode and the anode.
16. An electrochemical device comprising: the electrode of claim 1 as a anode; a cathode; and an electrolyte positioned between the cathode and the anode.
17. A method for forming an electrode for an electrochemical device, the method comprising: (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.
18. The method of claim 17 wherein: the solid-state ion conducting electrolyte material is selected from the group consisting of: (i) lithium aluminum oxides, (ii) lithium containing phosphates, (iii) Li.sub.xPON wherein x is 1, 1.5, 3, or 6, (iv) Li.sub.xSiPON wherein x is 1, 1.5, 3, or 6, (v) Li.sub.xSiON wherein x is 2, 4, or 6, (vi) a ceramic electrolyte material having the formula Li.sub.uRe.sub.vM.sub.wA.sub.xO.sub.y 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.
19. A method for forming an electrode for an electrochemical device, the method comprising: (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.
20. The method of claim 19 wherein: the solid-state ion conducting electrolyte material is selected from the group consisting of: (i) lithium aluminum oxides, (ii) lithium containing phosphates, (iii) Li.sub.xPON wherein x is 1, 1.5, 3, or 6, (iv) Li.sub.xSiPON wherein x is 1, 1.5, 3, or 6, (v) Li.sub.xSiON wherein x is 2, 4, or 6, (vi) a ceramic electrolyte material having the formula Li.sub.uRe.sub.vM.sub.wA.sub.xO.sub.y 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.
Description
BRIEF DESCRIPTION OF THE DRAWINGS
[0081] 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.
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DETAILED DESCRIPTION OF THE INVENTION
[0140] 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.
[0141] 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.
[0142] 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.
[0143] 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.
[0144]
[0145] 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
[0146] 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 LiMPO.sub.4 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 LiNi.sub.xMn.sub.yCo.sub.zO.sub.2, 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 LiNi.sub.1-x-yMn.sub.xAl.sub.yO.sub.2 (NMA) wherein x+y+z=1. The lithium host material 133 may comprise a sulfur containing material, such as a material including S.sub.8.
[0147] 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) Li.sub.xPON wherein x is 1, 1.5, 3, or 6, (iv) Li.sub.xSiPON wherein x is 1, 1.5, 3, or 6, (v) Li.sub.xSiON wherein x is 2, 4, or 6, (vi) a ceramic electrolyte material having the formula Li.sub.uRe.sub.vM.sub.wA.sub.xO.sub.y 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.
[0148] 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.
[0149] 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.
[0150] 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.
[0151] 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.
[0152] 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 LiPF.sub.6, LiBF.sub.4, LiClO.sub.4, lithium bis(fluorosulfonyl)imide (LiFSI), LiN(CF.sub.3SO.sub.2).sub.2 (LiTFSI), and LiCF.sub.3SO.sub.3 (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.
[0153] 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.
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[0155] Looking at
[0156] 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.
[0157] 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.
[0158] 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.
[0159] 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.
[0160] The solid state electrolyte 216 of the lithium metal battery 210 can include any solid material capable of storing and transporting Li.sup.+ ions between the anode 218 and the cathode 214.
[0161] 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), Li.sub.xPON wherein x is 1, 1.5, 3, or 6, Li.sub.xSiPON wherein x is 1, 1.5, 3, or 6, Li.sub.xSiON wherein x is 2, 4, or 6, and combinations thereof.
[0162] Another suitable solid state electrolyte 216 of the lithium metal battery 210 includes an electrolyte material having the formula Li.sub.uRe.sub.vM.sub.wA.sub.xO.sub.y, wherein
[0163] 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;
[0164] 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;
[0165] 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;
[0166] u can vary from 3-7.5;
[0167] v can vary from 0-3;
[0168] w can vary from 0-2;
[0169] x can vary from 0-2; and
[0170] y can vary from 11-12.5.
The electrolyte material may be a lithium lanthanum zirconium oxide.
[0171] 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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[0173] Looking at
[0174] The lithium host material 333 may comprise one or more lithium host materials selected from lithium titanium oxide (Li.sub.4Ti.sub.5O.sub.12, LTO), silicon-containing materials, such as silicon (e.g., silicene), silicon carbides (e.g., SiC), silicon nitrides (Si.sub.3N.sub.4), silicon nitride oxides (e.g., Si.sub.2N.sub.2O), and high entropy oxides (e.g., (Co.sub.0.2Cu.sub.0.2Mg.sub.0.2Ni.sub.0.2Zn.sub.0.2)O).
[0175] The porous coating 335 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
[0176] 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 LiCoO.sub.2 (LCO), LiFeO.sub.2, LiMnO.sub.2 (LMO), LiMn.sub.2O.sub.4, LiNiO.sub.2 (LNO), LiNi.sub.xCo.sub.yO.sub.2, LiMn.sub.xCo.sub.yO.sub.2, LiMn.sub.xNi.sub.yO.sub.2, LiMn.sub.xNi.sub.yO.sub.4, LiNi.sub.xCo.sub.yAl.sub.zO.sub.2 (NCA), LiNi.sub.1/3Mn.sub.1/3Co.sub.1/3O.sub.2 and others. Another example of a cathode active material is a lithium-containing phosphate having a general formula LiMPO.sub.4 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 LiNi.sub.xMn.sub.yCo.sub.zO.sub.2, 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 LiNi.sub.1-x-yMn.sub.xAl.sub.yO.sub.2 (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.
[0177] 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.
[0178] 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.
[0179] The lithium ion battery 310 includes a liquid electrolyte. The liquid electrolyte may comprise any of the liquid electrolytes listed above for battery 110.
[0180] 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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[0182] Looking at
[0183] The lithium host material 433 may comprise one or more lithium host materials selected from lithium titanium oxide (Li.sub.4Ti.sub.5O.sub.12, LTO), silicon-containing materials, such as silicon (e.g., silicene), silicon carbides (e.g., SiC), silicon nitrides (Si.sub.3N.sub.4), silicon nitride oxides (e.g., Si.sub.2N.sub.2O), and high entropy oxides (e.g., (Co.sub.0.2Cu.sub.0.2Mg.sub.0.2Ni.sub.0.2Zn.sub.0.2)O).
[0184] The porous coating 435 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
[0185] An example cathode active material for the cathode 414 is a cathode active material listed above for battery 310.
[0186] 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.
[0187] 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.
[0188] 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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[0190] Looking at
[0191] 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.
[0192] 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.
[0193] Looking at
[0194] The lithium host material 553 may comprise one or more of the lithium host materials listed above for lithium host material 333.
[0195] The porous coating 555 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
[0196] 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.
[0197] The lithium ion battery 510 includes a liquid electrolyte. The liquid electrolyte may comprise any of the liquid electrolytes listed above for battery 110.
[0198] 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.
[0199]
[0200] Looking at
[0201] 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.
[0202] 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.
[0203] Looking at
[0204] The lithium host material 653 may comprise one or more of the lithium host materials listed above for lithium host material 333.
[0205] The porous coating 655 may comprise one or more of the solid-state ion conducting electrolyte materials listed above for porous coating 135.
[0206] 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.
[0207] 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.
EXAMPLES
[0208] 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.
[0209] 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.sup.+ content to promote superior properties.
[0210] 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.
Example 1—Coatings on Cathodes—LMNO
1. Overview of Example 1
[0211] In Example 1, a lithium manganese oxide (LMNO) powder (Li.sub.1.1Mn.sub.1.5Ni.sub.0.5O.sub.4 from Nano One) was coated with nano-size particles of Al.sub.2O.sub.3, Li.sub.7La.sub.3Zr.sub.2O.sub.12 (LLZO), LiAlO.sub.2, and Li.sub.1.7Al.sub.0.3Ti.sub.1.7Si.sub.0.4P.sub.2.6O.sub.12, a lithium-aluminum-titanium-silicon-phosphate (LATSP). Lithium-aluminum-titanium-silicon-phosphates have a general composition Li.sub.1+x+yAl.sub.xTi.sub.2-xSi.sub.yP.sub.3-yO.sub.12 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 Li.sub.1.1Mn.sub.1.5Ni.sub.0.5O.sub.4 (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 Li.sub.1.1Mn.sub.1.5Ni.sub.0.5O.sub.4 (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 ZrO.sub.2 beads (3 mm, 6 g). The slurries were then coated on Al foil.
[0212] Half-cells were assembled using LMNO (Li.sub.1.1Mn.sub.1.5Ni.sub.0.5O.sub.4)+5 wt. % Al.sub.2O.sub.3, LiAlO.sub.2, LLZO, or LATSP (Li.sub.1.7Al.sub.0.3Ti.sub.1.7Si.sub.0.4P.sub.2.6O.sub.12) 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 LiPF.sub.6 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
[0213]
[0214] 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 (
[0215]
[0216]
[0217]
[0218]
[0219]
[0220]
[0221] The core scan of LMNO (Li.sub.1.1Mn.sub.1.5Ni.sub.0.5O.sub.4)−10 wt. % LATSP (Li.sub.1.7Al.sub.0.3Ti.sub.1.7Si.sub.0.4P.sub.2.6O.sub.12) 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 (
[0222] 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.
[0223]
[0224]
[0225]
TABLE-US-00001 TABLE A XPS analysis of LMNO + Al.sub.2O.sub.3 electrode after cycling. Binding energy LMNO- LMNO- Elements (eV) 5Al.sub.2O.sub.3 10Al.sub.2O.sub.3 Ni 2p 854 0.1 0.2 F 1s 684 3.1 8.0 Mn 2p 642 0.1 0.04 O 1s 530 23.1 8.8 C 1s 284 50 39.2 P 2p 133 3.3 1.5 Al 2p 73 0.6 3.2 Li 1s 58 19.6 39.1
[0226]
[0227] The Al 2p spectra shows an unexpected trend. The symmetric peak centered at ˜73 eV for the LMNO (Li.sub.1.1Mn.sub.1.5Ni.sub.0.5O.sub.4)−10 wt. % Al.sub.2O.sub.3 is characteristic of LiAlO.sub.2, indicating the lithiation of alumina after extensive cycling. The binding energy shifts to higher values on cycling for LMNO (Li.sub.1.1Mn.sub.1.5Ni.sub.0.5O.sub.4)−5 wt. % Al.sub.2O.sub.3(
[0228] The mechanism of substitution proposed by Van Landschoot et al. [Ref. 22] is:
Al.sub.2O.sub.3+2HF.fwdarw.Al.sub.2O.sub.2F.sub.2+H.sub.2O
and further reaction with HF leads to Al.sub.2OF.sub.4 and ultimately AlF.sub.3. Based on the Al 2p binding energy value ˜75 eV, we would expect that only Al.sub.2O.sub.2F.sub.2 forms. The full transformation of Al.sub.2O.sub.3 into fluorinated species is not achieved after 100 cycles for Al.sub.2O.sub.3 (10 wt. %) coated electrodes as the Al—O.sup.2− signal at 73 eV is still seen. We, therefore, expect that the full fluorination to AlF.sub.3 requires a much larger number of cycles, thus indicating that nano-Al.sub.2O.sub.3 is a long-standing protective coating.
Example 2—Coatings on Cathodes—NMC
[0229] Half-cells were assembled using LiNi.sub.xMn.sub.yCo.sub.zO.sub.2, wherein x+y+z=1 and x:y:z=6:2:2 (NMC 622)+5 wt. %, 10 wt. %, and 20 wt. % LATSP (Li.sub.1.7Al.sub.0.3Ti.sub.1.7Si.sub.0.4P.sub.2.6O.sub.12) 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 LiPF.sub.6 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.
[0230]
[0231]
Example 3—Coatings on Anodes—Nanopowder Coatings on Li.SUB.4.Ti.SUB.5.O.SUB.12 .(LTO)
1. Overview of Example 3
[0232] 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.sup.+/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 Li.sub.4Ti.sub.5O.sub.12 (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].
[0233] Spinel LTO anodes can facilitate up to three Li.sup.+ ions per formula unit and deliver theoretical capacities ˜175 mAh g.sup.−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.sup.−13 S cm.sup.−1) [Ref. 52]. attributed to the Ti.sup.4+ valence state and low Li.sup.+ diffusion coefficient (10.sup.−9-10.sup.−14 cm.sup.2 s.sup.−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.sup.+ diffusivity [Ref. 42,55-57 The most common method focuses on doping with metallic (Cr.sup.3+, Ca.sup.2+, Ga.sup.3+, Mg.sup.2+, Ta.sup.5+, and Al.sup.3+) [Ref. 58-61] and nonmetallic (Br.sup.−, Cl.sup.−, and F.sup.−) [Ref. 62-64] ions to increase lattice electrical conductivity through partial reduction of Ti.sup.4+ to Ti.sup.3+.
[0234] 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].
[0235] 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.sup.+ 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.
[0236] 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).
[0237] Recent publications indicate that the introduction of appropriate amounts of solid electrolytes [LiAlO.sub.2, Li.sub.1.3Al.sub.0.3Ti.sub.1.7(PO.sub.4).sub.3 (LATP), and Li.sub.0.33La.sub.0.56TiO.sub.3] 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.sup.+ 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.sup.−5 S/cm) [Ref. 78] and electronic conductivities (5×10.sup.−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.
[0238] Recently, we demonstrated that LF-FSP derived LiAlO.sub.2 ceramic electrolytes offer optimal ionic conductivities (˜10.sup.−6 S/cm) and electronic conductivities of 6.7×10.sup.−10 S/cm at ambient, both 3 orders of magnitude higher than those reported for LTO (Table 1) [Ref. 80]. Hence, LTO-LiAlO.sub.2 composite anodes were prepared via simple ball-milling. We coincidentally reported the synthesis and characterization of a novel polymer electrolyte (Li.sub.6SiON) 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 Li.sub.6SiON polymer electrolyte, we realized that it might also be possible to use this precursor to coat LTO NPs. The Li.sub.6SiON electrolyte offers a room temperature (Table 1) ionic conductivity of 10.sup.−6 S/cm and electrical conductivity of 10.sup.−7 S/cm six orders of magnitude greater than that of LTO.
TABLE-US-00002 TABLE 1 Ionic and Electronic Conductivities of LTO, LiAlO.sub.2, and Li.sub.6SiON at Ambient Ionic conductivity Electronic Compounds (S/cm) conductivity (S/cm) Ref. LTO 10.sup.−13-10.sup.−9 <10.sup.−13 52, 53 LiAlO.sub.2 10.sup.−6 10.sup.−10 80 Li.sub.6SiON 10.sup.−6 10.sup.−7 81
[0239] In this Example, we synthesized high surface area (˜38 m.sup.2/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 LiAlO.sub.2 NPs (APS=64 nm; 5 and 10 wt. %) and coated with Li.sub.6SiON polymer precursors (5 and 10 wt. %).
[0240] To the best of our knowledge, this is the first time three component composite anodes, e.g., LTO-5 wt. % LiAlO.sub.2-10 wt. % Li.sub.6SiON, 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.
2. Experimental Section
2.1 Synthesis of LTO NPs
Materials
[0241] Lithium hydroxide monohydrate (LiOH.Math.H.sub.2O) and propionic acid [(CH.sub.3CH.sub.2COOH), 99%] were purchased from Sigma-Aldrich (Milwaukee, Wis.). Titanium isopropoxide [Ti(OiPr).sub.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 (LiNH.sub.2) 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 m.sup.2/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 LiPF.sub.6 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.
[0242] The synthesis procedures for titanatrane {Ti(OCH.sub.2CH.sub.2).sub.3N—[OCH.sub.2CH.sub.2N(CH.sub.2CH.sub.2OH).sub.2]} and lithium propionate [LiO.sub.2CCH.sub.2CH.sub.3] are discussed in our previous work [Ref. 82].
Characterization
[0243] 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.sup.−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).
[0244] Specific surface area (SSA) analyses. SSA data was obtained using a Micromeritics ASAP 2020 sorption analyzer. Before sample analysis at −196° C. (77 K)/N.sub.2, 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/cm.sup.3) was used.
[0245] 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.
[0246] 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.sup.−1/air (60 mL min.sup.−1).
[0247] 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.sup.−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 4f.sub.7/2 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.
[0248] 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.sup.+) using a multi-channel Maccor battery test system (MACCOR, USA).
Methods
[0249] 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].
[0250] 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/O.sub.2, hereafter referred to as pristine LTO.
2.2. Preparation of LTO/LiAlO.SUB.2./Li.SUB.6.SiON Composites
[0251] LiAlO.sub.2 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=(C.sub.6H.sub.6O.sub.2).sub.2Si]. SP reacts with xLiNH.sub.2 to provide in oligomeric mixtures denoted as Li.sub.xSiON (x=2, 4, and 6) polymers with varying Li and N contents per Scheme 1 shown in
[0252] In our effort to enhance the electrical conductivity of LTO, composite anodes were processed by adding selected wt. % LiAlO.sub.2 solid and Li.sub.6SiON polymer electrolytes during electrode formulation per Table 2.
TABLE-US-00003 TABLE 2 Lists of Pristine and Composite Electrodes (wt. %) Electrodes LiAlO.sub.2 (wt. %) Li.sub.6SiON (wt. %) LTO 0 0 LTO-5 wt. % LiAlO.sub.2 5 0 LTO-10 wt. % LiAlO.sub.2 10 0 LTO-5 wt. % Li.sub.6SiON 0 5 LTO-10 wt. % Li.sub.6SiON 0 10 LTO-5 wt. % LiAlO.sub.2- 5 5 5 wt. % Li.sub.6SiON LTO-5 wt. % LiAlO.sub.2- 5 10 10 wt. % Li.sub.6SiON LTO-10 wt. % LiAlO.sub.2- 10 5 5 wt. % Li.sub.6SiON LTO-10 wt. % LiAlO.sub.2- 10 10 10 wt. % Li.sub.6SiON
[0253] The LTO and LiAlO.sub.2 NPs (5 and 10 wt. %) were dry ground for ˜30 minutes in air to ensure uniform mixing. The LTO-LiAlO.sub.2 mixtures, dispersed in anhydrous ethanol (5 mL), were ball-milled for 24 hours using ZrO.sub.2 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 Li.sub.6SiON 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 LiAlO.sub.2 and Li.sub.6SiON electrolytes, composite electrodes are synthesized by mixing the LTO-LiAlO.sub.2 powders with LTO-Li.sub.6SiON powders. Scheme 2 in
[0254] 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.
[0255] The LTO-Li.sub.6SiON mixtures were ultrasonicated for 10-15 min/N.sub.2 to give homogeneous slurries. The LTO-LiAlO.sub.2 mixtures were ball milled for 24 hours using ZrO.sub.2 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/cm.sup.2. 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 LiPF.sub.6 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 H.sub.2O contents below 0.5 ppm. The coin cells were compressed using a ˜0.1 kpsi uniaxial pressure (MTI).
3. Results and Discussion
[0256] 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 LiAlO.sub.2 solid electrolyte and Li.sub.6SiON polymer electrolyte additives on the rate performance of the LTO were also investigated.
3.1 Structure and Morphology of LTO Composites
[0257]
[0258] The XRD powder patterns of LTO-pristine, LTO-LiAlO.sub.2, and LTO-Li.sub.6SiON composites are shown in
[0259]
[0260]
[0261] The FTIR spectra of LTO-pristine and LTO-composite powders are presented in
[0262] The two broad absorption bands centered at 650 and 465 cm.sup.−1, respectively, are due to the symmetric and asymmetric stretching vibrations of lattice [MO.sub.6] octahedral groups confirming the presence of spinel LTO [Ref. 56].
[0263] High performance LTO anodes are available using nanostructured materials because such materials offer larger contact areas with electrolyte, shorter diffusion distances for Li.sup.+ 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.
[0264]
TABLE-US-00004 TABLE S1 Lists of SSAs and APSs of the LTO-composite powders SSA APS Electrodes (m.sup.2/g) (nm) LTO 37 ± 0.8 46 LTO-5 wt. % LiAlO.sub.2 35 ± 0.2 48 LTO-10 wt. % LiAlO.sub.2 31 ± 0.5 54 LTO-5 wt. % Li.sub.6SiON 36 ± 0.3 47 LTO-10 wt. % Li.sub.6SiON 37 ± 0.8 47
[0265] As noted above, high surface area is an important characteristic of nanostructured materials. The BET SSA of pristine LTO is 37±0.8 m.sup.2/g. The calculated APS using the BET surface area is ˜46 nm for the pristine LTO. The LTO-10 wt. % LiAlO.sub.2 sample shows a slight decrease to 31 m.sup.2/g and increase in APS (54 nm) attributed to the relatively larger LiAlO.sub.2 APS (64 nm) [Ref. 80].
[0266]
[0267] The thermal stability of the composite powders was investigated by TGA.
[0268]
3.2 Surface Characterization
[0269] The surface chemical composition and binding energies of the LTO-pristine and LTO-composite electrodes were analyzed by XPS. The survey spectra (
TABLE-US-00005 TABLE S2 XPS analysis of pristine LTO, LTO-LiAlO.sub.2 electrodes. At. % Binding LTO-5 LTO-10 energy LTO- wt. % wt. % Elements (eV) pristine LiAlO.sub.2 LiAlO.sub.2 F 1s 685 2.3 2.6 2.4 O 1s 526 18.2 19.1 16 Ti 2p 455 5.6 6.3 6 C 1s 281 27.1 21 20 Al 2p 70 — 3.3 7.3 Li 1s 58 46.8 47.7 48.3
TABLE-US-00006 TABLE S3 XPS analysis of pristine LTO, LTO-Li.sub.6SiON electrodes. Binding At. % energy LTO-5 wt. % LTO-10 wt. % Elements (eV) Li.sub.6SiON Li.sub.6SiON F 1s 685 3.5 2.85 O 1s 526 16 14.5 Ti 2p 455 5.8 6.6 N 1s 397 — 3.2 C 1s 281 25.6 22.75 Si 2p 99 1.9 2.3 Li 1s 58 47.2 47.8
[0270]
[0271] The core level spectra of the Al 2p (74.8 eV) peak increases with increasing LiAlO.sub.2 content (10 wt. %), a consequence of LiAlO.sub.2 particles associated with the surface of LTO particles (
[0272] The survey spectra (
TABLE-US-00007 TABLE S4 XPS analysis of LTO-5LiAlO.sub.2+ Li.sub.6SiON (5 and 10 wt. %) electrodes At. % Binding LTO-5 wt. % LTO-5 wt. % energy LiAlO.sub.2−5 LiAlO.sub.2− Elements (eV) wt. % Li.sub.6SiON 10 wt. % Li.sub.6SiON F 1s 684 5.6 4.8 O 1s 527 22.5 16.1 Ti 2p 455 5.1 6.6 N 1s 397 1 1 C 1s 281 32.2 32.7 Si 2p 99 1.3 1.5 Al 2p 73 4.8 6.2 Li 1s 58 27.5 31.1
[0273]
TABLE-US-00008 TABLE S5 Average atomic percentage (At. %) based on EDX analysis for LTO-composite electrodes. At. % Electrodes C F O Ti Al Si N LTO-pristine 29.7 6.3 48.4 15.6 — LTO-5 wt. % LiAlO.sub.2 29.6 4.9 47.5 16.8 1.2 LTO-10 wt. % LiAlO.sub.2 28.3 7.0 50.3 12 2.4 LTO-5 wt. % Li.sub.6SiON 23.7 8.2 52.5 13 — 1.4 1.2 LTO-10 wt. % Li.sub.6SiON 23.1 7.5 50 15.4 — 2.2 1.8
[0274]
3.3 Electrochemical Characterization
[0275] 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.sup.+ in solid, ω is the angular frequency, f is the frequency, and σ is the Warburg factor which is related to Z.sub.re obtained from the slope of the line in
[0276] All of the Nyquist spectra (
TABLE-US-00009 TABLE S6 Comparison of Li.sup.+ diffusivities for various LTO-composite electrodes. Electrodes D.sub.Li(cm.sup.2/s) Ref. LTO-LiAlO.sub.2 (5 wt. %) 1.19 × 10.sup.−13 94 LTO-LIAlO.sub.2 (10 wt. %) 3.51 × 10.sup.−15 94 LTO-Li.sub.0.33La.sub.0.56TiO.sub.3 (5 wt. %) 1.92 × 10.sup.−14 95 LTO-Li.sub.0.33La.sub.0.56TiO.sub.3 (10 wt. %) 1.23 × 10.sup.−14 95
[0277] The calculated Li.sup.+ diffusion coefficients for pristine LTO, LTO-LiAlO.sub.2, and LTO-Li.sub.6SiON are listed in Table 3. LTO-5 wt. % LiAlO.sub.2-10 wt. % Li.sub.6SiON has the highest diffusion coefficient (˜2.7×10.sup.−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.
TABLE-US-00010 TABLE 3 List of Diffusivities and Potential Gap for Pristine and Composite LTO Electrodes Electrodes D.sub.Li(cm.sup.2/s) Δ φ.sub.p (mV) LTO-pristine 4.6 ± 0.5 × 10.sup.−14 400 LTO-5 wt. % LiAlO.sub.2 6.1 ± 0.7 × 10.sup.−13 340 LTO-10 wt. % LiAlO.sub.2 4.8 ± 0.2 × 10.sup.−14 410 LTO-5 wt. % Li.sub.6SiON 6.7 ± 0.6 × 10.sup.−14 380 LTO-10 wt. % Li.sub.6SiON 1.2 ± 0.3 × 10.sup.−12 320 LTO-5 wt. % LiAlO.sub.2 − 5 wt. % 2.3 ± 0.3 × 10.sup.−13 300 Li.sub.6SiON LTO-5 wt. % LiAlO.sub.2 . 10 wt. % 2.7 ± 0.3 × 10.sup.−12 290 Li.sub.6SiON LTO-10 wt. % LiAlO.sub.2 − 5 3.0 ± 0.5 × 10.sup.−14 350 wt. % Li.sub.6SiON LTO-10 wt. % LiAlO.sub.2 − 10 1.3 ± 0.6 × 10.sup.−14 370 wt. % Li.sub.6SiON
[0278]
[0279] The electrochemical performance of LTO-pristine, LTO-LiAlO.sub.2, LTO-Li.sub.6SiON, and LTO-LiAlO.sub.2—Li.sub.6SiON 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 (
[0280] The discharge capacity for pristine LTO half-cell decreases to ˜125 mAh/g at 5 C. However, capacities for LTO-5 wt. % LiAlO.sub.2 and LTO-10 wt. % Li.sub.6SiON fade slowly remaining stable at 146 and 160 mAh/g at 5 C, respectively. The LTO-5 wt. % LiAlO.sub.2-10 wt. % Li.sub.6SiON exhibits a discharge capacity (˜140 mAh/g) at 5 C. On the whole, the LTO-Li.sub.6SiON and LTO-LiAlO.sub.2 electrodes reveal enhanced rate capacity relative to pristine LTO.
[0281] 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. % LiAlO.sub.2, LTO-10 wt. % LiAlO.sub.2, LTO-5 wt. % Li.sub.6SiON, and LTO-10 wt. % Li.sub.6SiON electrodes, respectively. The reversible capacities of LTO-Li.sub.6SiON decrease slowly compared to those for LTO-LiAlO.sub.2 and the pristine LTO electrodes. However, the LTO-10 wt. % LiAlO.sub.2-5 wt. % Li.sub.6SiON and LTO-10 wt. % LiAlO.sub.2-10 wt. % Li.sub.6SiON 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. % LiAlO.sub.2-5 wt. % Li.sub.6SiON and LTO-10 wt. % LiAlO.sub.2-10 wt. % Li.sub.6SiON capacities (
[0282] This might be ascribed to the larger quantity LiAlO.sub.2, 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-LiAlO.sub.2 (10 wt. %) composite electrodes [Ref. 77]. In addition, as discussed above in the diffusivity section, the LTO-10 wt. % LiAlO.sub.2-10 wt. % Li.sub.6SiON composite did not show a high Li.sup.+ diffusivity coefficient when compared to the LTO-5 wt. % LiAlO.sub.2-10 wt. % Li.sub.6SiON electrode.
[0283]
[0284] The reversible capacities found for LTO-5 wt. % LiAlO.sub.2-10 wt. % Li.sub.6SiON (260 mAh/g) and LTO-10 wt. % Li.sub.6SiON (231 mAh/g) are much higher than those of LTO-pristine electrodes (202 mAh/g) at 0.5 C as demonstrated in
[0285]
[0286]
TABLE-US-00011 TABLE 4 Comparison of Discharge Capacities of LTO-Composite Anode Materials at 5 C discharge capacities Electrodes (mAh/g) Ref. LTO-LiAlO.sub.2 (5 wt. %) 127 77 LTO-LiAlO.sub.2 (10 wt. %) ~50 77 LTO-Li.sub.0.33La.sub.0.56TiO.sub.3 146 69 (5 wt. %) LTO-Li.sub.0.33La.sub.0.56TiO.sub.3 137 69 (10 wt. %) Li.sub.4Ti.sub.4.9La.sub.0.1O.sub.12 181 91 LTO-TiO.sub.2 1 17 92 LTO-TiO.sub.2/C 140 93 LTO-5 wt. % LiAlO.sub.2 190 this Example LTO-10 wt. % Li.sub.6SiON 206 this Example LTO-5 wt. % LiAlO.sub.2− 10 wt. % 217 this Example Li.sub.6SiON
[0287]
TABLE-US-00012 TABLE S7 List of impedance values for pristine and composite LTO-Li half-cells Electrodes R.sub.e(Ω) R.sub.ct(Ω) LTO-pristine 3.5 60 LTO-5 wt. % LiAlO.sub.2 2.8 6 LTO-10 wt. % LiAlO.sub.2 3.3 75 LTO-5 wt. % Li.sub.6SiON 3.8 20 LTO-10 wt. % Li.sub.6SiON 3.6 15 LTO-5 wt. % LiAlO.sub.2 −10 3.0 8.5 wt. % Li.sub.6SiON
[0288] The high rate performance of the LTO-5 wt. % LiAlO.sub.2-10 wt. % Li.sub.6SiON electrodes is attributed to: [0289] 1. Optimal amounts of LiAlO.sub.2 (5 wt. %) and Li.sub.6SiON (10 wt. %) between or on the LTO particle surfaces enhancing the ionic conductivity as demonstrated by the increase in lithium ion diffusivity. (Table 3). [0290] 2. Li.sub.6SiON polymer electrolyte reorganizing LTO surface bonding, resulting in an increase in the electronic conductivity due to the local change imbalance. [0291] 3. Diminishing electrode polarization, via introduction of appropriate LiAlO.sub.2 and Li.sub.6SiON electrolyte contents. [0292] 4. The enhanced electrical conductivities of electrolyte additives coupled with uniform particle morphology and high surface area of LTO NPs resulted in long-term cycling stability over 500 cycles delivering reversible capacity of ˜217 mAh/g at 5 C (
4. Conclusions
[0293] 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 LiAlO.sub.2 and Li.sub.6SiON 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 LiAlO.sub.2 and Li.sub.6SiON electrolyte, the LTO composite electrodes with optimal LiAlO.sub.2 (5 wt. %) and Li.sub.6SiON (10 wt. %) electrolyte additives exhibit excellent rate performance delivering reversible capacity of 260 and 140 mAh/g at 0.5 and 10 C, respectively.
Example 4—Coatings on Li—S Cells
1. Preparation of C—S Composites
[0294] First, polyacrylonitrile (MW 150 g/mol PAN) (200 mg) and S.sub.8 (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 m.sup.2 g.sup.−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).
[0295] 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..fwdarw.400° C./5 h at 5° C./min in N.sub.2” and then “400° C..fwdarw.30° C. at 5° C./min in N.sub.2”.
[0296] Table B shows the detailed information about C—S pellets after heating and soaking in CS.sub.2.
TABLE-US-00013 TABLE B S contents in C-S pellets after heat-treatment. Pellet before heating Pellet after heating Composition Mass Mass S content (wt. %) Sample (mg) (mg) (wt. %) C:P:S 1 971 450 46 46 (5:20:75) 2 946 446 47 3 1002 464 46 4 985 447 45 5 999 462 46 6 987 466 47 C: high surface area C (1700 m.sup.2 g.sup.−1), P: PAN, and S: sulfur. The heating regime to form C-S bonds: “30° C..fwdarw.400° C./5 h at 5° C./min in N.sub.2” and then “400° C..fwdarw.30° C. at 5° C./min in N.sub.2”.
[0297] 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 CS.sub.2 for 24 hours. This S extraction process was repeated two times with fresh CS.sub.2. 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.
2. Slurry Preparation for S Electrodes with or without LATSP
[0298] Table C shows the information about slurries.
TABLE-US-00014 TABLE C Starting Chemical Components For The Film Casting PAN-C-S composite *LATSP PVDF C65 Sample (mg) (mg) (mg) (mg) 1 700 0 150 150 2 550 150 150 150 *Solid electrolyte, ball-milled during slurry preparation for 24 hours.
[0299] 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.
[0300] 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.
[0301] 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.
[0302] The S electrodes were thermo-pressed at 5 ksi/50° C./5 min before Li—S half-cell assembly.
3. Li—S Half-Cells for Performance Evaluation
[0303] 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 LiPF.sub.6 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.
[0304]
[0305] 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.
[0306] The initial discharge capacity was ˜1706 mAh/g which decreased to ˜1070 mAh/g after the 1st cycle. As shown in
[0307]
[0308] 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.
[0309] The initial discharge capacity was ˜1730 mAh/g and this capacity decreased to ˜1110 mAh/g after the 1.sup.st cycle. As shown in
[0310] 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.sup.−1 at 0.5 C as shown in
[0311] In a nutshell,
[0312] 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.
[0313] We also tested the use of LiAlO.sub.2 nanopowder as shown in
[0314] 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.
[0315] 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
4. LiSi.SUB.x.PON Coated Li—S Half Cells
[0316] For comparison, we also used a solid polymer electrolyte, Li.sub.6SiPON, for coating.
[0317] 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.
[0318] 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
[0319] To summarize these studies, reference is made to
Example 5—Assembly of all Solid State Batteries (ASSB)
[0320] LTO-20 wt. % LATSP electrodes were investigated as an alternative anode as they demonstrate good rate performance and optimal Li.sup.+ diffusivity. NMC 622}−20 wt. % LATSP (Li.sub.1.7Al.sub.0.3Ti.sub.1.7Si.sub.0.4P.sub.2.6O.sub.12) electrodes were used as the catholyte and 60 wt. % PEO/Li.sub.6PON 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.
[0321]
[0322] 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.
[0323] 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 Mn.sup.2+ that dissolves in liquid electrolytes degrading capacity, the high surface area, the high energy surfaces of the NPs will give up Li.sup.+ to the surroundings resulting in surfaces that are highly negatively charged. Given that Mn.sup.2+ is a di-cation, one expects that such species will electrostatically bind more strongly to NP surfaces than Li.sup.+ 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.sup.− 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.
Example 6—Nano LMNO (n-LMNO) Cathodes
[0324] In this Example, overlithiated LMNO (Li.sub.1.26Mn.sub.1.5Ni.sub.0.5O.sub.4) nano-size particles (synthesized using LF-FSP) were coated with LiAlO.sub.2 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.
[0325] Half-cells were assembled using n-LMNO+0 wt. %, 5 wt. %, 10 wt. %, or 20 wt. % nano-LiAlO.sub.2 (same nano-LiAlO.sub.2 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 LiPF.sub.6 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
[0326]
[0327] 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 [
[0328]
[0329] The half-cell shows an initial charge and discharge capacity of 179 and 114 mAh/g at 0.3 C, respectively [
[0330]
[0331]
[0332] As shown in
[0333] 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 1.sup.st cycle columbic efficiency, perhaps the excess charge capacity from the n-LMNO+x wt. % LiAlO.sub.2 (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).
[0334] It is important to also note that the 20 wt. % LiAlO.sub.2 promoted system is the most stable of the half cells tested demonstrating that imperfect nano-nano systems also offer superior behavior to uncoated systems.
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[0430] 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.
[0431] Thus, the present invention provides coatings that enhance battery component performance.
[0432] 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.
[0433] 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.