Patent Application
20210070630
The present application claims the priority of European patent application EP 18305518 filed on 26 Apr. 2018, the content of which being entirely incorporated herein by reference for all purposes. In case of any incoherency between the present application and the EP application that would affect the clarity of a term or expression, it should be made reference to the present application only.
The present invention relates to the new process of preparation of a Li-rich layered oxide based on Mn and optionally on Ni and/or Co in which F is incorporated within the crystal of the oxide (or “fluorinated oxide”). It also relates to the new fluorinated oxide its use as a component in a cathode of a battery.
Today's society relies on the use of electrochemical energy storage, mainly rechargeable Li-ion batteries, to power many objects like portable electronics and electric vehicles. With the ongoing technological revolution associated with electric mobility, integration of renewable energy sources, and connected objects, our dependence on batteries will become greater than ever. As the global demand for batteries increases, special focus remains on the popular Li-ion technology that surpasses its predecessors (lead-acid, nickel-cadmium, and nickel-metal hydride) in terms of energy density (Wh·L−1) and lifetime (years). It is becoming even more popular thanks to continual performance improvements and falling costs (estimated to drop below 100 € kW·h−1 by 2025).
These high expectations put pressure on the Li-ion technology which must preserve its supremacy by continually improving in energy density and sustainability, bearing in mind that today's cathodes are mainly based on cobalt—a chemical element with geopolitical and ethical concerns. Towards these goals, the lights are back to green with the recent discovery of anionic redox chemistry by our group, which allows extra energy storage via electrochemical activity of ligands, hence enabling a nearly doubled capacity in Li-rich Mn-based layered oxides, such as Li12Ni0.13Mn0.54Co0.13O2 (aka Li-rich NMC) and Li1.2Ni0.2Mn0.6O2, which serve as cobalt-lean alternatives for replacing today's LiCoO2 and LiNi1/3Mn1/3Co1/3O2 (NMC) cathodes.
Li-rich layered oxides have drawn great hopes as next generation cathode materials for high energy density Li-ion batteries, relying on both cationic and anionic redox processes. However, their practical implementation in the next generation of Li-ion batteries is plagued by difficulties in lowering their voltage decay upon cycling together with their origin oxygen release during oxidation which after their capacity fading afterwards with this effect being more pronounced for the practical and sustainable 3d metals such as Mn. Among that line the Li-rich layered oxides, Li2MnO3 having cheap and environmentally benign, Mn4+ could show a theoretical capacity of ˜460 mAh g−1 provided two lithium can be removed. In a layer notation usually used in the field of materials for cathodes, Li2MnO3 can be written as Li[Li1/3Mn2/3]O2, where one third of the position in the Mn-plane is replaced by Li to form an ordered LiMn2 slab, together with Li inter-slab layer stack into the C2/m space group. Till now such materials was shown attractive initial capacity that drastically decays upon cycling alike the pure disorder rocksalt structure reported by Pralong et al. (Nat. Mater. 2016, 15, 173-177). More information about Li-rich oxides may also be found in Electrochimica Acta 2013, 105, 200-208.
A classical way, widely practice over the years, to master materials surface degradation, is enlisting treatment with fluorine (see Li2Ni0.5Mn0.5O4, LiMn2O4-xFx and many others).
Incorporation of F into a Li-rich layered oxide based on Mn and optionally on Ni and/or Co is sought after to increase the voltage of the materials and to reduce the valence of the transition metals by substituting O2− by F. In most of cases the incorporation of F was attended by a ceramic process, mainly using LiF as a flux hence enabling a confocal deposit around the particles of the oxide. Occasionally, the incorporation of F into the oxide could be proved by tiny lattice parameters changes as reported for the spinel (Amatucci and Tarascon, U.S. Pat. No. 5,674,645 (1997)) or as recently claimed by Ceder's group (Nat. Commun. 2017, 8, 981) in a layered oxide (Li1.15Ni0.45Ti0.3Mo0.1O1.85F0.15). However, the incorporation of F into the oxide is not proven. A recent drive towards the incorporation of F into Li4Mn5O12 was recently attempted by P. G. Bruce via mechanical milling (Energy Environ. Sci. 2018, 11, 926-932). The hardness of this mechanical process results in the formation of a new phase within which F is an integer and cannot be changed. Moreover, ball-milling is likely to affect the crystallinity of the material and decrease too much the size of the particles.
In addition, the direct fluorination on Li2MnO3 via high temperature has failed due to the high affinity of lithium and fluorine, leading to the direct formation of LiF instead of oxide lattice substitution, while ball milling results in a full amorphization of the phase without any evidence for interstitial F as deduced by NMR.
In Electrochimica Acta 2013, 105, 200-208, a product of generic formula Li[Li0.2Mn0.54Ni0.13Co0.13]O2-xFx is prepared. In this product, the amount of Li is 1.2 whereas in formula (II) of claim 1 and in formula (I) of claim 2, x is below ⅔. Moreover, the detailed process of preparation of such product does not involve an oxygen-deficient oxide as a starting material. The same applies to US 2014/367609.
In this context, a problem to be solved is therefore to find a convenient and clean process to incorporate F into a layered oxide based on Mn and optionally on Ni and/or Co. Another problem is also in preparing a new layered oxide based on Mn and optionally on Ni and/or Co in which F is inserted within the crystal of the oxide which can be used efficiently in a high energy density Li-ion battery.
The invention relates to a process as defined in claims 1-14 and to an oxide as defined in claims 15-23. It also relates to a cathode as defined in claim 24, to a battery as defined in claim 25 and to the use of an oxyde-deficient oxide as defined in claim 26.
The process makes it possible to prepare a Li-rich layered oxide based on Mn and optionally on Ni and/or Co in which F is incorporated within the crystal of the oxide, consisting in incorporating fluorine into the oxygen vacancies of an oxygen-deficient oxide of formula (II):
[LixMnIVyNiIVzCoIVw]O2-u (II)
wherein:
In the context of the invention, the Li-rich layered oxide based on Mn and optionally on Ni and/or Co in which F is incorporated within the crystal of the oxide is designated throughout the present application (including the claims) by the term “fluorinated oxide”.
The process of preparation of the fluorinated oxide also consists in contacting an oxygen-deficient oxide of formula (II):
[LixMnIVyNiIVzCoIVw]O2-u (II)
wherein:
The fluorinated oxide may more particularly be characterized by formula (I):
[LixMnIVyNin′zCon″w]O2-uFt (I)
wherein:
The fluorinated oxide is a neutral compound. This implies more particularly that x, y, z, w, n′, n″, u and t are correlated to ensure electroneutrality. The following mathematical relationship may thus apply:
x+4y+n′z+n″w=2(2−u)+t
u corresponds to the number of oxygen vacancies present in the oxygen-deficient oxide of formula (II) that are required for the incorporation of fluorine into the crystal. u is less than ⅔ (u<⅔), more particularly less than ½ (u<½), and even more particularly less than ⅓ (u<⅓). As is evidenced for the fluorinated oxide of example 4, u may be less than 0.2, more particularly less than 0.15. The presence of the oxygen vacancies may be confirmed by analytical techniques such as EXAFS (Extended X-Ray Absorption Fine Structure), neutron diffraction and TEM (Transmission Electron Microscopy) or a combination of these techniques.
In the fluorinated oxide, the oxidation state of Mn is +IV. Mn is present to stabilize the fluorinated oxide and the oxygen-deficient oxide. The stoichiometry in Mn, y, should preferably be high enough so that the fluorinated oxide and the oxygen-deficient oxide exist in the form of layered structures. y is such that 0<y≤⅔. More particularly, ⅓<y≤⅔. n′ corresponds to the average oxidation state of Ni. n″ corresponds to the average oxidation state of Co. In the fluorinated oxide, n′ may range from +II to +IV and is preferably +IV. n″ may range from +III to +IV and is preferably +IV.
F is incorporated within the crystal of the fluorinated oxide. The fluorinated oxide exhibits an O1-type layered structure which may be confirmed by XRD. The amount of F in the fluorinated oxide depends on the number of oxygen vacancies (u) in the oxygen-deficient oxide. Thus, the following relationship applies: 0<t≤u. The amount of F also depends on the conditions of the process such as the duration of the contact between the oxygen-deficient oxide and the atmosphere comprising the fluorinated reactive species or the temperature at which the fluorination is performed. Under the conditions explored, it was possible to obtain t=u.
The fluorinated oxide may be based on Mn only (w=z=0), Mn and Ni only (w=0) or Mn and Co only (z=0). Mn needs to be present (y>0). The fluorinated oxide may be one disclosed in the examples. An example of a fluorinated oxide based on Mn only is LixMn2/3O2-uFt.
The process of the invention involves the thermal decomposition of the fluorinated agent which generates fluorinated reactive species. Without being bound by any theory, the fluorinated reactive species may be for instance radicals F° or ionic fluorine F. The fluorinating agent may be selected in the group consisting of HF, F2, XeF2, TbF4, CeF4, CoF3, AgF2, MoF3, AgF, CuF2, FeF3, CuF, VF3 and CrF3. The fluorinating agent may also be a fluorinated organic compound. It may be for instance a fluorinated polymer such as PVDF or PTFE. XeF2 proves to be a good fluorinating agent as the fluorinated reactive species are generated at temperatures below 100° C. TbF4 and CeF4 are also good fluorinating agents as the decomposition products comprising Tb or Ce may be recycled for the preparation of the fluorinating agent.
The process is thus performed by contacting the oxygen-deficient oxide of formula (II) with an atmosphere comprising the fluorinated reactive species generated by the thermal decomposition of the fluorinating agent. The thermal decomposition of the fluorinating agent may be conducted at a temperature which is comprised between 30° C. and 500° C.
When the fluorinating agent is XeF2, the temperature of decomposition may be more particularly between 80° C. and 100° C. When the fluorinating agent is TbF4 or CeF4, the temperature of decomposition may be more particularly between 100° C. and 500° C. The duration of the fluorination depends on the nature of the fluorinating agent and of the concentration in the atmosphere of the fluorinated reactive species. When the fluorinating agent is XeF2, the duration may be between 10 hours and 72 hours.
As the oxygen-deficient oxide of formula (II) may be sensitive to O2 or H2O, the atmosphere preferably consists of an inert gas comprising the fluorinated reactive species generated by the decomposition of the fluorinating agent. The inert gas may for instance be argon or nitrogen.
A particular process of preparation of the fluorinated oxide consists in placing the oxygen-deficient oxide of formula (II) and the fluorinating agent in a confined vessel and in decomposing the fluorinated agent, so as to generate the fluorinated reactive species.
The process may be performed by using the oxygen-deficient oxide as such. The process may also be performed by using a composite material comprising the oxygen-deficient oxide obtained by the electrochemical delithiation applied to a composite material comprising the oxide of formula (III) which is described below. Example 4 illustrates this particular process.
Unlike known processes, the process of the invention makes it also possible to obtain a fluorinated oxide with a low amount of LiF. This may be deduced from XRD wherein the XRD diagram of the fluorinated oxide does not exhibit the contribution of crystalline LiF.
This may also be deduced from a spectrum obtained by 19F solid-state MAS NMR spectroscopy for which the intensity of the peak of LiF(ILiF) is such that:
0<ILiF/IF≤0.50, more particularly ≤0.30
wherein:
Thus, the invention also relates to a fluorinated oxide as described in claim 17 or claim 18.
Following the incorporation of fluorine, the fluorine within the crystal is surrounded by the metal(s) in its close vicinity. The peak of fluorine incorporated within the crystal of the fluorinated oxide thus exhibits a chemical shift δF around −150 ppm. δF may be between −140 ppm and −160 ppm.
The peak of LiF is usually centred at a chemical shift δF around −204 ppm. δF may be between −200 ppm and −210 ppm. The position of the peak of LiF may be confirmed by a spectrum of pure LiF conducted in the same analytical conditions. The intensities are measured from the baseline of the corresponding peak. Deconvolution may be applied for the case the peaks are overlapped with other peaks.
The incorporation of fluorine in the crystal may also be deduced from a spectrum obtained by 7Li NMR for which broad peak is present and centred at a positive chemical shift (δLi>0 ppm). The peak is centred at a chemical shift δLi comprised between 100 ppm and 200 ppm. The width at half peak may be between 150 ppm and 200 ppm.
The oxygen-deficient oxide (II) is characterized by XRD. The oxygen-deficient oxide (II) may exhibit a layered prismatic-like structure. The oxygen-deficient oxide of formula (II) may be prepared by the electrochemical delithiation of the oxide of formula (III):
Li[Lix′MnIVyNin′zCon″]O2 (III)
wherein:
The oxide of formula (III) is neutral. This implies that x′, y, z, w, n′, n″ are correlated to ensure electroneutrality. The following mathematical relationship may thus apply:
x′+4y+n′z+n″w=3
The electrochemical delithiation triggers the creation of oxygen vacancies in the oxide of formula (III). The oxygen-deficient oxide of formula (II) is characterized by the presence of peroxo-like species (O2m− with m=1 or 2) as can be confirmed by X-ray photoelectron spectroscopy (XPS). These species were shown to be stable after fluorination, so that the fluorinated oxide may also contain peroxo-like species.
An example of oxide of formula (III) is Li2MnO3 (example 1) which corresponds to Li[Li1/3Mn2/3]O2 (x′=⅓; w=z=0).
The electrochemical delithiation consists in subjecting the oxide of formula (III) to an electrochemical oxidation up to a potential that makes it possible to fully oxidize the transition metals without irreversibly damaging the structure of the oxide. This potential may preferably range from 4.5 V to 5.0 V vs Li+/Li. In practice, the electrochemical delithiation may conveniently consist in using an electrode made of a composite material comprising the oxide of formula (III). The composite material is prepared by compounding the oxide of formula (III) with conductive carbon. The composite material usually comprises more than 50.0 wt % of the oxide of formula (III). The composite material may comprise less than 50.0 wt % of the conductive material. The proportion of the oxide may be comprised between 70.0 wt % and 90.0 wt %. The proportion of the conductive material may be comprised between 10.0 wt % and 30.0 wt %. It is preferable to thoroughly compound the two solids so as to obtain a composite material wherein the solids are intimately mixed. Ball milling may conveniently be used to prepare the composite material as is disclosed in the examples (example 4).
The oxide of formula (III) is prepared by the solvothermal precipitation which is described below:
a) under stirring, an aqueous solution of LiOH is added drop-by-drop to an aqueous solution containing MnSO4.H2O, (NH4)2S2O8 and optionally a salts of NiII and/or a salt of Co. The following salts of NiII and CoII may be used: NiSO4.6H2O and CoSO4.7H2O.
The solution is characterized by a molar ratio R═[S2O82−]/([Mn2+]+[Ni2+] and/or [Co2+]) comprised between 1.1 and 1.6, more particularly between 1.1 and 1.3.
The total amount of LiOH added is such that the molar ratio R′═Li+/([Mn2+]+[Ni2+] and/or [Co2+]) is higher than 10, preferably comprised between 10 and 11. If R′ is less than 10, a minor spinel LiMn2O4 impurity phase may be formed. The duration of the addition of the solution of LiOH is comprised between 5 and 15 minutes. The solutions may be at a temperature comprised between 10 and 30° C.
b) The solution obtained at the end of step a) is heated at a temperature higher than 100° C. so as to obtain a precipitate. The mixture may be heated at a temperature between 100° C. and 250° C., more particularly at a temperature between 150° C. and 220° C. The duration of the heating may be comprised between 6 hours and 48 hours. The temperature and the duration may be modified to control the particle size and the degree of disorder within the stacking of the ordered Li1/3Mn2/3 sheets. With the increase of the temperature up to 200° C., the particle size and the stacking disorder tend to increase while at 250° C., the stacking disorder decreases. Similarly for the reaction duration, while increasing the duration up to 24 h will increase the particles size and the stacking disorder, in contrast, up to 48 h will lead to decrease the stacking disorder.
c) The oxide of formula (III) obtained in step b) is recovered and dried.
The oxide of formula (III) may optionally be washed with water. Drying is performed at a temperature higher than 50° C. The temperature of drying may be comprised between 50° C. and 150° C. Vacuum may also be applied during drying to help remove the physisorbed water. A vacuum with a pressure lower than 10-3 mbar may be applied.
The solvothermal precipitation makes it possible to obtain easily the oxide of formula (III) in the form of nanoparticles with a controlled morphology and size and exhibiting good electrical conductivity (see e.g. example 1). The solvothermal process thus appears superior to the ceramic process which requires annealing at high temperature (400° C.) for a long period of time (3 weeks or more). This process helps prepare an homogeneous oxide that is used in the electrochemical delithiation. The nanoparticles of the oxide of formula (III) may be characterized by an average size dXRD comprised between 10 and 50 nm, wherein dXRD is the isotropic average size of the crystalline domains. dXRD is determined by XRD by structural refinement using the Thompson-Cox-Hastings pseudo-Voigt peak shape.
The control of the size of the particles of the oxide of formula (III) ensures to also get a control of the size and morphology of the particles of the fluorinated oxide. Thus, an advantage of the process of the invention is to control the size and morphology of the fluorinated oxide. The fluorinated oxide may thus be in the form of nanoparticles. More particularly, the particles of the fluorinated oxide may be characterized by a D50 comprised below 100 nm, D50 being the median diameter determined from a distribution (in volume) obtained by laser diffraction. Laser particle sizer like Horiba LA-910 may be used following the guidelines of the constructor. Moreover, as for the oxide of formula (III), dXRD for the fluorinated oxide may also be comprised between 10 and 50 nm, wherein dXRD is the isotropic average size of the crystalline domains. The determination of D50 may be performed when the oxide is dispersed in water.
The nanoparticles of the oxide of formula (III) can be described as secondary particles consisting of primary particles aggregrated, the size dSEM (as measured with SEM) of the primary particles being between 30 and 200 nm. The secondary particles are of different shapes (spheres, hexagones, rods, . . . ). This applies also to the fluorinated oxide.
The oxide of formula (III) exhibits an O3-like structure.
In the inorganic oxides disclosed above (fluorinated oxide, oxygen-deficient oxide and oxide of formula (III)), part of the Li+ may be substituted by Mg2+ with adjustment of the composition to ensure electroneutrality.
The fluorinated oxide may be used as a component of a cathode of a battery. The cathode typically comprises or consists in a composite material C comprising the fluorinated oxide, at least one conductive material and optionally at least one polymer binder. The composite material C usually comprises more than 50.0 wt % of the fluorinated oxide. The composite material C may comprise less than 50.0 wt % of the conductive material. The proportion of the fluorinated oxide may be comprised between 70.0 wt % and 90.0 wt %. The proportion of the conductive material may be comprised between 10.0 wt % and 30.0 wt %.
The conductive material is typically conductive carbon, such as carbon black (e.g. Carbon black, Super P® commercialized by Alfa Aesar). The polymer binder is typically a vinylidenefluoride-based (co)polymer. The polymer binder may for instance be a polymer of VDF or a copolymer of VDF and HFP wherein VDF is vinylidene fluoride and HFP is hexafluoropropylene.
The cathode may be prepared by the process which comprises the following steps:
The slurry is prepared by mixing the fluorinated oxide, the conductive material, the polymer binder, if any, and the solvent. The polymer binder is preferably dissolved in the solvent. The solvent is suitable to dissolve the polymer binder. It may be N-methylpyrrolidone. An example of process of preparation of a cathode may be more particularly found on pages 19-20 of WO 2013/180781.
The invention also relates to a battery comprising the cathode. The battery usually comprises the cathode, an anode, an electrolyte ensuring electronic insulation and ionic conduction and a separator if the electrolyte is liquid.
The electrolyte may be solid and composed of inorganic lithium conductors or lithium conductive polymers with or without lithium salts. The electrolyte may also be liquid and composed of lithium salts dissolved in a blend of solvent with optionally the use of additives. The lithium salt is preferably selected from the group consisting of LiPF6, LiBF4, LiClO4, lithium bis(oxalato)borate (“LiBOB”), LiN(SO2F)2, LiN(CF3SO2)2, LiN(C2F5SO2)2, Li[N(CF3SO2)(RFSO2)]n with RF being C2F5, C4F9, CF3OCF2CF2, LiAsF6, LiC(CF3SO2)3 and mixtures thereof. More preferably, the salt is LiPF6. The lithium salt is preferably dissolved in the organic carbonate-based solvent. The organic carbonate-based solvent may be selected in the group consisting of unsaturated cyclic carbonates (e.g. ethylene carbonate (EC), propylene carbonate (PC), butylene carbonate, fluoroethylene carbonate and fluoropropylene carbonate) and unsaturated acyclic carbonates (e.g. dimethylcarbonate (DMC), diethylcarbonate (DEC), ethylmethylcarbonate (EMC), and fluorinated acyclic carbonates). Other suitable solvents that may be used in combination with carbonates are esters (e.g. propyl propionate (PP), ethyl propionate (EP)).
When the electrolyte is liquid, a separator is needed. The separator is typically a microporous membrane of polyolefin (e.g. polyethylene or polypropylene) or a non-woven separator. The separator may be coated with ceramics to increase safety.
The anode is usually made of a lithium metal foil or of a lithium alloy composition including notably those described in U.S. Pat. No. 6,203,944 or in WO 00/03444. Lithium ion batteries are made using either: 1) graphitic carbons able to intercalate lithium, typically existing in forms such as powders, flakes, fibers or spheres (for example, mesocarbon microbeads) hosting lithium. The use of prelithiated graphite (as described for example in U.S. Pat. No. 5,759,715) is preferred. 2) lithium titanates of formula Li4Ti5O2; 3) lithium-silicon alloys, generally known as lithium silicides with high Li/Si ratios, in particular lithium silicides of formula Li4.4Si; 4) lithium-germanium alloys, including crystalline phases of formula Li4.4Ge.
Li4/3Mn2/3O2 (or Li2MnO3) is prepared by the solvothermal precipitation process. The protocol comprises dissolving a solution containing 5 mL of MilliQ water with 0.003 moles of MnSO4.H2O and 0.0045 moles (NH4)2S2O8 with a fixed ratio of R═[S2O82−]/[Mn2+]=1.5. The solution was stirred at room temperature for 10 minutes in a 25 mL Teflon lined container, 10 mL 3M of LiOH were added drop-by-drop and the solution was stirred for another 10 minutes. After sealing, the solution was heated at a fixed temperature of 200° C. for 24 h. After cooling to room temperature, the powder was recovered from the solution using centrifugation and washed several times with MilliQ water, and dried at 80° C. for 10 h. The recovered powder was further outgassed at 100° C. under vacuum for 10 h.
The structural analysis of as-prepared compound was first investigated by X-ray diffraction (XRD). The XRD pattern is characteristic of a monoclinic C2/m structure for as-prepared compound. Elemental composition analysis by using ICP-OES showed the Li/Mn ratio is 1.97, confirming as-prepared compound having a chemical formula Li4/3Mn2/3O2. The morphology and particles size were studied by scanning electron microscopy (SEM), demonstrating the that the particles of Li4/3Mn2/3O2 are nanometric with an average articles size of ˜50 nm, as is shown on
A cathode was prepared by mixing 70 wt % of the compound of Example 1 and 30 wt % of Super P® carbon by weight, mixed by SPEX high-energy ball mill for 20 minutes. Lithium deinsertion-insertion reactions are written as follows:
Li4/3Mn2/3O2=⅔MnO2+4/3Li+4/3e−+⅓O2
Based on the 4/3Li+ extraction, the theoretical capacity (or amount of charge) that can be stored is 460 mAh·g−1. The cathode obtained was used in a lithium battery comprising a lithium metal anode and using the electrolyte of 1 M Lithium hexafluorophosphate (LiPF6) in a mixture of Ethylene Carbonate (EC)/Propylene Carbonate (PC)/Dimethyl Carbonate (DMC) (1:1:3 vol. %). This battery was operated at a current density of C/20 (1C=460 mA·g−1) within a potential range of 2-4.8 V vs. Li+/Li. The first charge capacity is ˜350 mAh·g−1, it then drops to ˜250 mAh·g−1 while discharging, showing a large irreversible capacity loss. Upon cycling, the capacity stabilizes around 150-160 mAh·g−1 over 40 cycles, as shown on
According to previous studies, oxygen loss may occur on charge in the Li-rich layered oxide electrodes. To check this point, gas pressure analysis was carried out upon the first charge/discharge cycle. As LixMn2/3O2-u was charged, the pressure increased. From the pressure increase and mass spectrometry analysis, it can be deduced that approximately 0.157 gas molecules are released per initial Li4/3Mn2/3O2 with the nature of the gas being CO2 (m/z=44) and O2 (m/z=32) at the very end of oxidation. As expected for a four-electron O2−/O2 transformation, this would lead to an irreversible loss of ˜0.2 electrons, hence a stoichiometry for the charged product close to Li0.27Mn2/3O1.9. ICP-OES analysis confirmed the Li/Mn ratio is 0.37(3) for the charged product, in good agreement with electrochemistry.
The electrode comprising 70 wt. % Li4/3Mn2/3O2 and 30 wt. % carbon was charged at 4.80 V vs. Li+/Li at a current rate of C/20 to obtain the oxygen-deficient Li0.27Mn2/3O1.9 electrode, and the electrode was recovered and washed by dimethyl ether (DME), dried under vacuum in an argon-filled glove-box. Then, the recovered Li0.27Mn2/3O1.9 electrode powder sample was placed in a pre-fluorinated nickel crucible, the desired amount of XeF2 was separately placed in a Teflon-line container and loaded the nickel crucible into the Teflon lined container, then sealed into an autoclave in the argon-filled glove-box. The autoclave was heated at 90° C. for 12 hours, and the powder was recovered in the argon-filled glove-box.
Elemental composition analysis using ICP-OES confirmed the Li/Mn ratio is unchanged before and after fluorination at 0.37 and 0.36, respectively. Insight into the local structural environments in Li0.4MnO2.85F0.15 sample is obtained using 19F and 7Li solid-state MAS NMR spectroscopy, in comparison with oxide Li4/3Mn2/3O2 and oxygen-deficient Li0.27Mn2/3O1.9 sample, shown in
The cathode is disclosed in Example 4 and is obtained after the reaction with XeF2. The cathode was used in a lithium battery comprising a lithium metal anode and using the electrolyte of 1 M Lithium hexafluorophosphate (LiPF6) in the mixture of Ethylene Carbonate (EC)/Propylene Carbonate (PC)/Dimethyl Carbonate (DMC) (1:1:3 vol. %).
The electrode was initially activated by discharging to 2 V vs. Li+/Li at a current density of C/20. This battery has been operated at a current density of C/20 within a potential range of 2-4.5 V vs. Li+/Li. The first charge capacity is ˜240 mAh·g−1, it maintains at ˜230 mAh·g−1 while discharging, indicating a good reversible capacity. Upon cycling, the capacity stabilizes around ˜190 mAh·g−1 over 20 cycles demonstrating a good reversibility of the system.
A Li-battery was also electrochemically characterized as in example 5 and in comparative example 6 except that the working electrode was prepared with the pure Li4/3Mn2/3O2 obtained in example 1. The Li4/3Mn2/3O2 obtained in example 1 is first activated for 1 cycle at a current density of C/20 within a potential range of 2-4.8 V vs. Li+/Li. This battery was operated at a current density of C/20 within a potential range of 2-4.5 V vs. Li+/Li. It appears that the compound of Example 1 (Li4/3Mn2/3O2) and the fluorinated oxide of Example 4 (Li0.27Mn2/3O1.9F0.1) after activation, showing modified smooth electrochemical signature for Li0.27Mn2/3O1.9F0.1 with slightly improved average potential and capacity for the initial cycles. Upon cycling, the capacity stabilizes around ˜160 mAh·g−1 over 20 cycles. On the other hand, as can be seen on
Besides Li-rich Li4/3Mn2/3O2, the possibility of a partial substitution of Mn by Ni and Co was also explored by the soft chemical synthesis disclosed before (solvothermal process). The Ni-substituted and Co-substituted Li4/3Mn2/3O2 are also prepared by the solvothermal precipitation described before. The protocol comprises dissolving a solution containing 5 mL of MilliQ water with desired amount of MnSO4.H2O and NiSO4.6H2O (or CoSO4.7H2O), and the amount of (NH4)2S2O8 was added and mixed at a fixed ratio of R═[S2O8]2−/M2+=1.5 (M=Mn+Ni or Mn+Co), the mixture was stirred at room temperature for 10 minutes in a 25 mL Teflon lined container, and 10 mL 3M of LiOH was added drop-by-drop and stirring for another 10 minutes. After sealing, the solution was heated at a fixed temperature of 200° C. for 24 h. After cooling to room temperature, the powder was recovered from the solution using centrifugation and washed several times with MilliQ water, and dried at 80° C. for 10 h. The recovered powder was further outgassed at 100° C. under vacuum for 10 h.
The structural analysis for as-prepared compounds was first investigated by X-ray diffraction (XRD). The XRD patterns obtained are shown in
| Number | Date | Country | Kind |
|---|---|---|---|
| 18305518.5 | Apr 2018 | EP | regional |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2019/060659 | 4/25/2019 | WO | 00 |
