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All sourcesNASA NTRSDOE OSTI
DOE OSTI2023

Li 3– x Zr x (Ho/Lu) 1– x Cl 6 Solid Electrolytes Enable Ultrahigh-Loading Solid-State Batteries with a Prelithiated Si Anode

We report two new families of lithium metal chloride solid electrolytes Li 3–x Zr x (M) 1–x Cl 6 (0 ≤ x ≤ 0.8; M = Ho or Lu) with ionic conductivities of up to 1.8 mS cm –1 and a low activation energy of 0.34 eV. Structural elucidation via high-resolution neutron diffraction determines the Li ion distribution in trigonal Li 3 HoCl 6 , orthorhombic-I Li 3 LuCl 6 , and orthorhombic-II Li 2.4 Zr 0.6 (Ho/Lu) 0.4 Cl 6 . The last compound exhibits well-connected Li-ion pathways and abundant Li-ion carriers/vacancies to promote diffusion. All-solid-state batteries with Li 2.6 Zr 0.4 (Ho/Lu) 0.6 Cl 6 solid electrolytes and NCM85 cathodes exhibit stable cycling up to 4.6 V vs Li + /Li, which is even preserved up to 4.8 V. Stable cathode interphases are formed for both electrolytes upon cycling to 4.3, 4.6, and 4.8 V cutoff potentials, as identified by a ToF-SIMS analysis. Solid-state cells with a prelithiated Li 0.7 Si anode exhibit a significantly increased initial coulombic efficiency of 94.5% compared to Si and a high areal capacity of up to 16.3 mAh·cm –2 .

37 INORGANIC, ORGANIC, PHYSICAL, AND ANALYTICAL CH↗
DOE OSTI2024

Unlocking Li superionic conductivity in face-centred cubic oxides via face-sharing configurations

Oxides with a face-centred cubic (fcc) anion sublattice are generally not considered as solid-state electrolytes as the structural framework is thought to be unfavourable for lithium (Li) superionic conduction. Here we demonstrate Li superionic conductivity in fcc-type oxides in which face-sharing Li configurations have been created through cation over-stoichiometry in rocksalt-type lattices via excess Li. We find that the face-sharing Li configurations create a novel spinel with unconventional stoichiometry and raise the energy of Li, thereby promoting fast Li-ion conduction. The over-stoichiometric Li–In–Sn–O compound exhibits a total Li superionic conductivity of 3.38 × 10 -4 S cm -1 at room temperature with a low migration barrier of 255 meV. Our work unlocks the potential of designing Li superionic conductors in a prototypical structural framework with vast chemical flexibility, providing fertile ground for discovering new solid-state electrolytes.

36 MATERIALS SCIENCE↗
DOE OSTI2024

Degradation Mechanism of Phosphate‐Based Li‐NASICON Conductors in Alkaline Environment

NASICON-type Li conductors (Li-NASICON) have traditionally been regarded as promising candidates for solid-state Li-air battery applications because of their stability in water and ambient air. However, the presence of water in the cathode of a Li-air battery can induce a highly alkaline environment by modifying the discharge product from Li 2 O 2 to LiOH which can potentially degrade cathode and separator materials. This study investigates the alkaline stability of common Li-NASICON chemistries through a systematic experimental study of LiTi x Ge 2-x (PO 4 ) 3 (LTGP) with varying x = 0–2.0. Density functional theory calculations are combined to gain a mechanistic understanding of the alkaline instability. It is demonstrated that the instability of LTGP in an alkaline environment is mainly driven by the dissolution of PO 4 3– groups, which subsequently precipitate as Li 3 PO 4 . The introduction of Ti facilitates the formation of a Ti-rich compound on the surface that eventually passivates the material, but only after significant bulk degradation. Consequently, phosphate-based Li-NASICON materials exhibit limited alkaline stability, raising concerns about their viability in humid Li-air batteries.

25 ENERGY STORAGE↗
DOE OSTI2022

Fluorinated Rocksalt Cathode with Ultra-high Active Li Content for Lithium-ion Batteries

The key to increasing the energy density of lithium-ion batteries is to incorporate high contents of extractable Li into the cathode. Unfortunately, this triggers formidable challenges including structural instability and irreversible chemistry under operation. Here, we report a new kind of ultra-high Li compound: Li 4+x MoO 5 F x (1≤x≤3) for cathode with an unprecedented level of electrochemically active Li (>3 Li + per formula), delivering a reversible capacity up to 438 mAh g –1 . Unlike other reported Li-rich cathodes, Li 4+x MoO 5 F x presents distinguished structure stability to immunize against irreversible behaviors. In this work, through spectroscopic and electrochemical techniques, we find an anionic redox-dominated charge compensation with negligible oxygen release and voltage decay. Our theoretical analysis reveals a “reductive effect” of high-level fluorination stabilizes the anionic redox by reducing the oxygen ions in pure-Li conditions, enabling a facile, reversible, and high Li-portion cycling.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Mixed Ionic–Electronic Conductor of Perovskite Li x La y MO 3-δ toward Carbon-Free Cathode for Reversible Lithium–Air Batteries

Mixed ionic–electronic conductors (MIECs) can play a pivotal role in achieving high energies and power densities in rechargeable batteries owing to their ability to simultaneously conduct ions and electrons. In our study, a new strategy is proposed wherein late 3d transition metals (TMs) are substituted into a perovskite Li-ion conductor to transform it into a Li-containing MIEC. First-principles calculations show that perovskite Li x La y MO 3 with late 3d TMs have a low oxygen vacancy formation energy, implying high electron carrier concentrations corresponding to high electronic conductivity. The activation barriers for Li diffusion in Li x La y MO 3 (M = Ti, Cr, Mn, Fe, and Co) are below 0.411 eV, resulting in high Li-ion conductivity. The designed perovskites of Li0.34La 0.55 MnO 3-δ experimentally prove to have high electronic (2.04 × 10 -3 S cm -1 ) and Li-ion (8.53 × 10 -5 S cm -1 ) conductivities, and when applied in a carbon-free cathode of a Li–air cell, they deliver superior reversibility at 0.21 mAh cm -2 over 100 charge/discharge cycles while avoiding the degradation associated with carbonaceous materials. Finally, this strategy enables the effective design of Li-conducting MIEC and reversible Li–air batteries.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Polysulfide reduction and Li 2 S phase formation in the presence of lithium metal and solid electrolyte interphase layer

Lithium sulfur battery is an attractive next generation technology that can meet many demands of modern society. Unfortunately, the lithium sulfur battery faces unique issues related to the polysulfide shuttle effect, that is due to reduction products dissolving in the electrolyte and their subsequent reduction on the lithium metal electrode. This adds further problems to the already challenging needs of understanding and engineering a solid electrolyte interphase (SEI) layer with desired properties. One of the most important SEI properties is its passivation of lithium metal which is critically important to the overall battery performance. Passivation is difficult to measure experimentally without the influence of many factors. This study reports an investigation of the reduction of the intermediate Li 2 S 8 over lithium already passivated with Li 2 O, Li 2 CO 3 , LiOH, LiF and Li 2 S along with exploration of Li 2 S 8 reduction over pristine lithium nanoclusters using first principles computational models. Significant formation of Li 2 S phase nucleation is found to stabilize the reduction products of the Li 2 S 8 . Here, the formation of Li 2 S is explored in-depth with lithium nanocluster-based models determining a 2 V potential increase for the reduction of polysulfides due to the formation of Li 2 S. This investigation demonstrates passivation effects of important SEI components including Li 2 S.

25 ENERGY STORAGE↗
DOE OSTI2025

First-principles elucidation of defect-mediated Li transport in hexagonal boron nitride

Hexagonal boron nitride (hBN) is a promising candidate as a protective membrane or separator in Li-ion and Li–S batteries, given its excellent chemical stability, mechanical robustness, and high thermal conductivity. In addition, hBN can be functionalized by introducing defects and dopants, or be directly integrated into other active components of batteries, which further augments its appeal to the field. Here, we use first-principles simulations to evaluate the role of atomic defects in hBN in regulating the Li-ion diffusion mechanism and associated kinetics. Specifically, the following four distinct types of vacancy defects are considered: isolated single B and N vacancies, a B–N vacancy pair, and a B 3 N vacancy cluster. It is found that these defect sites generally favor Li intercalation and out-of-plane diffusion but slow down in-plane Li-ion diffusion due to a strong Li trapping effect at the defect sites. Such a trapping effect is, however, highly local such that it does not necessarily affect the overall Li-ion conductivity in defected hBN layers. The present systematic evaluation of the impact of atomic defects on Li ion migration and accompanied charge analysis of hBN lattice in response to Li-ion diffusion provide a mechanistic understanding of Li-ion transport behavior in defected hBN and highlight the potential of defect engineering to achieve optimal material performance.

37 INORGANIC, ORGANIC, PHYSICAL, AND ANALYTICAL CH↗
DOE OSTI2023

Multidimensional visualization of the dynamic evolution of Li metal via in situ/operando methods

The growing demands for high-energy density electrical energy storage devices stimulate the coupling of conversion-type cathodes and lithium (Li) metal anodes. While promising, the use of these “Li-free” cathodes brings new challenges to the Li anode interface, as Li needs to be dissolved first during cell operation. In this study, we have achieved a direct visualization and comprehensive analysis of the dynamic evolution of the Li interface. The critical metrics of the interfacial resistance, Li growth, and solid electrolyte interface (SEI) distribution during the initial dissolution/deposition processes were systematically investigated by employing multidimensional analysis methods. They include three-electrode impedance tests, in situ atomic force microscopy, scanning electrochemical microscopy, and cryogenic scanning transmission electron microscopy. The high-resolution imaging and real-time observations show that a loose, diffuse, and unevenly distributed SEI is formed during the initial dissolution process. This leads to the dramatically fast growth of Li during the subsequent deposition, deviating from Fick’s law, which exacerbates the interfacial impedance. The compactness of the interfacial structure and enrichment of electrolyte species at the surface during the initial deposition play critical roles in the long-term stability of Li anodes, as revealed by operando confocal Raman spectroscopic mapping. In conclusion, our observations relate to ion transfer, morphological and structural evolution, and Li (de)solvation at Li interfaces, revealing the underlying pathways influenced by the initial dissolution process, which promotes a reconsideration of anode investigations and effective protection strategies.

25 ENERGY STORAGE↗
DOE OSTI2023

Superconductivity in the Li-B-C system at 100 GPa

Layer Li-B-C compounds have been shown to have feasible superconductivity. Using the adaptive genetic algorithm, we predict the structures of the Li-B-C system at 100 GPa. Here we identify several low-enthalpy metallic phases with stoichiometries of Li B 2 C, Li B 3 C, Li 2 BC 2 , Li 3 B 2 C 3 , Li 3 BC, and Li 5 BC. Using a fast screening method of electron-phonon interaction, we find that Li B 3 C is a promising candidate for superconductivity. The consecutive calculations using the full Brillouin zone confirm the existence of the strong electron-phonon coupling (EPC) in this system. The anharmonic B-C phonon modes near the zone center provide the major contribution to the EPC. The EPC constant is 1.40, and the estimated critical temperature is 22 K. In this paper, we indicate that superconductivity can also happen without a layered structural motif in the Li-B-C system. We also demonstrate an effective strategy for crystal structure prediction of superconducting materials.

75 CONDENSED MATTER PHYSICS, SUPERCONDUCTIVITY AND↗
DOE OSTI2020

Experimental Performance Evaluation of a Hyper-Branched Polymer Electrolyte for Rechargeable Li-Air Batteries

A hyper-branched polymer (HBP) electrolyte is synthesized for rechargeable lithium-air (Li-air) battery cell and experimentally evaluated its performance in actual battery cell environment. Several real-world battery cells were fabricated with synthesized HBP electrolyte, pure lithium metal as anode and an oxygen permeable air cathode to evaluate reproducibility of the rechargeable Li-air battery cell. The effect of various conditions such as various HBP based electrolytes, discharge current -0.1~0.5 mA, cathode preparation processes and carbon contents on the battery cell performance were experimentally evaluated using the fabricated battery cells under dry air condition. Detailed HBP electrolyte synthesis procedures and experimental performance evaluation of Li-air battery cell for various conditions are presented. The experimental results showed that different conditions and processes significantly affect the Li-air battery performance. Upon taking into account the effect of different conditions and processes, optimized HBP electrolyte materials, cathode process and conditions were determined. Several Li-air battery cells were fabricated with optimized conditions and optimized battery cell materials to determine the reproducibility and performance consistency. Experimental results showed that over 55–65 h of discharge occurred over 2.5 V terminal cell voltage with all three optimized Li-air battery cells. It implied that the optimized Li-air battery cells were reproducible and were able to hold charge over 2.5 V for more than 2 days. Experimental results of the Li-air battery cell with further refined optimized materials revealed that the battery cell can discharge more than 10 days (i.e., more than 250 h) at or above 2.0 V. The experimental results also showed that the Li-air battery discharge time got shorter as the discharge-charge cycle increases due to increase in internal resistances of battery cell materials. The experimental results confirmed that the lithium-air battery cell can be reproduced without loss of performance and can hold charge more than 10 days at or over 2.0 V. The investigation results obtained may usher a pathway to manufacture a long-life rechargeable Li-air battery cell in the near future.

25 ENERGY STORAGE↗
DOE OSTI2021

WIYN Open Cluster Study. LXXXV. Li in NGC 2243: Implications for Stellar and Galactic Evolution

High-dispersion spectra in the Li λ6708 region have been obtained and analyzed in the old, metal-deficient cluster NGC 2243. From Hydra spectra for 29 astrometric and radial velocity members, we derive rotational velocities, as well as [Fe/H], [Ca/H], [Si/H], and [Ni/H] based on 17, 1, 1, and 3 lines, respectively. Using ROBOSPECT, an automatic equivalent width measurement program, we derive [Fe/H] = −0.54 ± 0.11 (MAD), for an internal precision for the cluster [Fe/H] below 0.03 dex. Given the more restricted line set, comparable values for [Ca/H], [Si/H], and [Ni/H] are −0.48 ± 0.19, −0.44 ± 0.11, and −0.61 ± 0.06, respectively. With E(B − V) = 0.055, appropriate isochrones imply (m − M) = 13.2 ± 0.1 and an age of 3.6 ± 0.2 Gyr. Using available VLT spectra and published Li abundances, we construct an Li sample of over 100 stars extending from the tip of the giant branch to 0.5 mag below the Li dip. The Li dip is well populated and, when combined with results for NGC 6819 and Hyades/Praesepe, implies a mass/metallicity slope of 0.4 M {sub ⊙}/dex for the high-mass edge of the Li dip. The A(Li) distribution among giants reflects the degree of Li variation among the turnoff stars above the Li dip, itself a function of stellar mass and metallicity and strongly anticorrelated with a v {sub rot} distribution that dramatically narrows with age. Potential implications of these patterns for the interpretation of Li among dwarf and giant field populations, especially selection biases tied to age and metallicity, are discussed.

71 CLASSICAL AND QUANTUM MECHANICS, GENERAL PHYSIC↗
DOE OSTI2020

A polymeric composite protective layer for stable Li metal anodes

Lithium (Li) metal is a promising anode for high-performance secondary lithium batteries with high energy density due to its highest theoretical specific capacity and lowest electrochemical potential among anode materials. However, the dendritic growth and detrimental reactions with electrolyte during Li plating raise safety concerns and lead to premature failure. Herein, we report that a homogeneous nanocomposite protective layer, prepared by uniformly dispersing AlPO 4 nanoparticles into the vinylidene fluoride-co-hexafluoropropylene matrix, can effectively prevent dendrite growth and lead to superior cycling performance due to synergistic influence of homogeneous Li plating and electronic insulation of polymeric layer. The results reveal that the protected Li anode is able to sustain repeated Li plating/stripping for >750 cycles under a high current density of 3 mA cm -2 and under a practical specific capacity of 2 mAh cm -2 . Moreover, full-cell Li-ion battery is constructed by using LiFePO 4 and protected Li as a cathode and anode, respectively, rendering a stable capacity after 400 charge/discharge cycles. The current work presents a promising approach to stabilize Li metal anodes for next-generation Li secondary batteries.

25 ENERGY STORAGE↗
DOE OSTI2020

Materials Data on Li(Fe3Ge2)2 by Materials Project

LiFe6Ge4 crystallizes in the trigonal R-3m space group. The structure is three-dimensional. Li is bonded to twelve Fe and eight Ge atoms to form distorted face-sharing LiFe12Ge8 hexagonal bipyramids. All Li–Fe bond lengths are 3.25 Å. There are two shorter (2.48 Å) and six longer (2.91 Å) Li–Ge bond lengths. There are three inequivalent Fe sites. In the first Fe site, Fe is bonded in a 5-coordinate geometry to two equivalent Li, six Fe, and five Ge atoms. There are a spread of Fe–Fe bond distances ranging from 2.46–2.80 Å. There are a spread of Fe–Ge bond distances ranging from 2.48–2.56 Å. In the second Fe site, Fe is bonded in a 5-coordinate geometry to two equivalent Li, six equivalent Fe, and five Ge atoms. There are a spread of Fe–Ge bond distances ranging from 2.48–2.56 Å. In the third Fe site, Fe is bonded in a 5-coordinate geometry to two equivalent Li, six equivalent Fe, and five Ge atoms. Both Fe–Li bond lengths are 3.25 Å. There are a spread of Fe–Fe bond distances ranging from 2.46–2.80 Å. There are a spread of Fe–Ge bond distances ranging from 2.48–2.56 Å. There are two inequivalent Ge sites. In the first Ge site, Ge is bonded in a 1-coordinate geometry to one Li and nine Fe atoms. In the second Ge site, Ge is bonded in a 12-coordinate geometry to three equivalent Li and six Fe atoms.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Materials Data on Li(CoO2)2 by Materials Project

Li(CoO2)2 is Spinel structured and crystallizes in the triclinic P1 space group. The structure is three-dimensional. there are eight inequivalent Li1+ sites. In the first Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 58–63°. There is two shorter (1.93 Å) and two longer (1.95 Å) Li–O bond length. In the second Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 57–61°. There are a spread of Li–O bond distances ranging from 1.93–1.96 Å. In the third Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 57–62°. There is two shorter (1.93 Å) and two longer (1.95 Å) Li–O bond length. In the fourth Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 58–61°. There are a spread of Li–O bond distances ranging from 1.92–1.95 Å. In the fifth Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 57–61°. There are a spread of Li–O bond distances ranging from 1.92–1.96 Å. In the sixth Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 58–62°. There is three shorter (1.94 Å) and one longer (1.95 Å) Li–O bond length. In the seventh Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 58–62°. There are a spread of Li–O bond distances ranging from 1.92–1.95 Å. In the eighth Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 57–61°. There are a spread of Li–O bond distances ranging from 1.93–1.96 Å. There are sixteen inequivalent Co+3.50+ sites. In the first Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.88–1.92 Å. In the second Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.87–1.92 Å. In the third Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.87–1.93 Å. In the fourth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.90–1.95 Å. In the fifth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.89–1.95 Å. In the sixth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.86–1.95 Å. In the seventh Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.90–1.95 Å. In the eighth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.91–1.95 Å. In the ninth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.88–1.91 Å. In the tenth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.89–1.95 Å. In the eleventh Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.87–1.93 Å. In the twelfth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.91–1.93 Å. In the thirteenth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.88–1.91 Å. In the fourteenth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.86–1.93 Å. In the fifteenth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.89–1.96 Å. In the sixteenth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.90–1.95 Å. There are thirty-two inequivalent O2- sites. In the first O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the second O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the third O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the fourth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the fifth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the sixth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the seventh O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the eighth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the ninth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the tenth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 tetrahedra. In the eleventh O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 tetrahedra. In the twelfth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the thirteenth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the fourteenth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the fifteenth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the sixteenth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the seventeenth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 tetrahedra. In the eighteenth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the nineteenth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the twentieth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 tetrahedra. In the twenty-first O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the twenty-second O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the twenty-third O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the twenty-fourth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the twenty-fifth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the twenty-sixth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the twenty-seventh O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the twenty-eighth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the twenty-ninth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the thirtieth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the thirty-first O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the thirty-second O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Materials Data on Li(BH)6 by Materials Project

Li(BH)4(BH)2 crystallizes in the monoclinic P2_1/c space group. The structure is zero-dimensional and consists of eight boranediylradical molecules and four Li(BH)4 clusters. In each Li(BH)4 cluster, Li is bonded in a 5-coordinate geometry to four H atoms. There are a spread of Li–H bond distances ranging from 1.94–2.26 Å. There are four inequivalent B sites. In the first B site, B is bonded in a single-bond geometry to one H atom. The B–H bond length is 1.20 Å. In the second B site, B is bonded in a single-bond geometry to one H atom. The B–H bond length is 1.20 Å. In the third B site, B is bonded in a single-bond geometry to one H atom. The B–H bond length is 1.20 Å. In the fourth B site, B is bonded in a single-bond geometry to one H atom. The B–H bond length is 1.21 Å. There are four inequivalent H sites. In the first H site, H is bonded in a bent 120 degrees geometry to one Li and one B atom. In the second H site, H is bonded in a distorted L-shaped geometry to one Li and one B atom. In the third H site, H is bonded in an L-shaped geometry to one Li and one B atom. In the fourth H site, H is bonded in a water-like geometry to one Li and one B atom.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Materials Data on Li(CoO2)2 by Materials Project

Li(CoO2)2 is Spinel structured and crystallizes in the triclinic P1 space group. The structure is three-dimensional. there are eight inequivalent Li1+ sites. In the first Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 53–65°. There are a spread of Li–O bond distances ranging from 1.92–2.02 Å. In the second Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 55–66°. There are a spread of Li–O bond distances ranging from 1.94–2.01 Å. In the third Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 54–65°. There are a spread of Li–O bond distances ranging from 1.93–2.00 Å. In the fourth Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 55–66°. There are a spread of Li–O bond distances ranging from 1.94–1.99 Å. In the fifth Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 55–65°. There are a spread of Li–O bond distances ranging from 1.93–2.00 Å. In the sixth Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 54–63°. There are a spread of Li–O bond distances ranging from 1.95–2.02 Å. In the seventh Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 54–65°. There are a spread of Li–O bond distances ranging from 1.98–2.02 Å. In the eighth Li1+ site, Li1+ is bonded to four O2- atoms to form LiO4 tetrahedra that share corners with twelve CoO6 octahedra. The corner-sharing octahedra tilt angles range from 53–64°. There are a spread of Li–O bond distances ranging from 1.97–2.02 Å. There are sixteen inequivalent Co+3.50+ sites. In the first Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.87–1.94 Å. In the second Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.86–1.93 Å. In the third Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.87–1.93 Å. In the fourth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.96–2.06 Å. In the fifth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.88–1.93 Å. In the sixth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.94–2.06 Å. In the seventh Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.95–2.07 Å. In the eighth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.87–1.92 Å. In the ninth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.99–2.05 Å. In the tenth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.92–2.06 Å. In the eleventh Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.88–1.93 Å. In the twelfth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.87–1.92 Å. In the thirteenth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.97–2.06 Å. In the fourteenth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.86–1.92 Å. In the fifteenth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.97–2.04 Å. In the sixteenth Co+3.50+ site, Co+3.50+ is bonded to six O2- atoms to form CoO6 octahedra that share corners with six LiO4 tetrahedra and edges with six CoO6 octahedra. There are a spread of Co–O bond distances ranging from 1.98–2.06 Å. There are thirty-two inequivalent O2- sites. In the first O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form distorted corner-sharing OLiCo3 trigonal pyramids. In the second O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the third O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the fourth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 tetrahedra. In the fifth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the sixth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the seventh O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the eighth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the ninth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 tetrahedra. In the tenth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form a mixture of distorted edge and corner-sharing OLiCo3 trigonal pyramids. In the eleventh O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the twelfth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form distorted corner-sharing OLiCo3 trigonal pyramids. In the thirteenth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form distorted corner-sharing OLiCo3 trigonal pyramids. In the fourteenth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the fifteenth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the sixteenth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the seventeenth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the eighteenth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the nineteenth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the twentieth O2- site, O2- is bonded in a rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the twenty-first O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the twenty-second O2- site, O2- is bonded in a rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the twenty-third O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the twenty-fourth O2- site, O2- is bonded to one Li1+ and three Co+3.50+ atoms to form distorted corner-sharing OLiCo3 trigonal pyramids. In the twenty-fifth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the twenty-sixth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the twenty-seventh O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the twenty-eighth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the twenty-ninth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the thirtieth O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the thirty-first O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms. In the thirty-second O2- site, O2- is bonded in a distorted rectangular see-saw-like geometry to one Li1+ and three Co+3.50+ atoms.

36 MATERIALS SCIENCE↗
DOE OSTI2022

Elastic Lattice Enabling Reversible Tetrahedral Li Storage Sites in a High-Capacity Manganese Oxide Cathode

The key to breaking through the capacity limitation imposed by intercalation chemistry lies in the ability to harness more active sites that can reversibly accommodate more ions (e.g., Li + ) and electrons within a finite space. However, excessive Li-ion insertion into the Li layer of layered cathodes results in fast performance decay due to the huge lattice change and irreversible phase transformation. Here, in this study, an ultrahigh reversible capacity is demonstrated by a layered oxide cathode purely based on manganese. Through a wealth of characterizations, it is clarified that the presence of low-content Li 2 MnO 3 domains not only reduces the amount of irreversible O loss; but also regulates Mn migration in LiMnO 2 domains, enabling elastic lattice with high reversibility for tetrahedral sites Li-ion storage in Li layers. This work utilizes bulk cation disorder to create stable Li-ion-storage tetrahedral sites and an elastic lattice for layered materials, with a reversible capacity of 600 mA h g –1 , demonstrated in th range 0.6–4.9 V versus Li/Li + at 10 mA g –1 . Admittedly, discharging to 0.6 V might be too low for practical use, but this exploration is still of great importance as it conceptually demonstrates the limit of Li-ions insertion into layered oxide materials.

25 ENERGY STORAGE↗
DOE OSTI2023

Elucidating the mechanism underlying the augmented capacity of MoO 2 as an anode material in Li-ion batteries

Transition-metal oxide anode materials have been observed to possess an intriguing surplus of capacity beyond the expected values based on conversion reaction. However, the mechanisms behind this phenomenon have remained contentious and elusive. Here, this study focuses on synthesized nanosized molybdenum dioxide and its electrochemical performance as an anode material for Li-ion batteries. Our findings reveal a substantial increase in capacity upon cycling, achieving approximately 1688 mA h g -1 , nearly double the theoretical capacity, after 700 cycles at a 1C rate. To elucidate the mechanisms underlying this augmented capacity, a comprehensive analysis employing in situ and ex situ X-ray diffraction, X-ray absorption spectroscopy, scanning electron microscopy, and transmission electron microscopy was conducted at various stages of the Li-ion cell cycling. Our results indicate that no conversion reaction occurs during the initial discharge phase, with Li 2 O and Mo remaining undetected. Instead, Li 0.98 MoO 2 is generated upon lithiation. Further materials characterization employing electron energy loss spectroscopy and energy-dispersive X-ray spectroscopy on the cycled electrode suggests the potential formation of a metallic Li-rich layer at the interface of the Li-ion intercalated phase subsequent to the formation of Li 0.98 MoO 2 , contributing to the surplus Li storage. Moreover, electrochemical impedance spectroscopy coupled with ex situ SEM and TEM analyses reveals that alterations in particle size and morphology, along with changes in the solid electrolyte interphase (SEI) resistance, are instrumental in the capacity variation observed upon cycling.

25 ENERGY STORAGE↗