SEARCH · Engineering Papers
Results for “Li”
Search indexed NASA NTRS and DOE OSTI research on propulsion, heat transfer, battery materials and energy systems. Follow report and document links to the original sources.
Quote a phrase for an exact phrase match. Source license links do not imply unrestricted reuse.
Li 2 FeCl 4 as a Cost-Effective and Durable Cathode for Solid-State Li-Ion Batteries
Not provided.
Solvent-Free Melt-Processed Cathode Mitigates Li Anode Instability in Polymer-Based Solid-State Batteries
Solvent-free manufacturing of battery components is a promising alternative to traditional slurry processing for reducing the cost and environmental impact. In this work, we used twin-screw melt extrusion to fabricate a polymer-based high voltage composite cathode. The melt-processed cathode is dense (near zero porosity) and thick (65 μm) and has high active material loading (80 wt %). The active particles are distributed uniformly throughout the melt-processed cathode, unlike the traditional slurry-cast cathode, which exhibits inhomogeneous particle distribution. In the melt-processed cathode, polymer and carbon form separate phases, whereas in the slurry-cast cathode they blend into a single phase. Due to these structural differences, the melt-processed cathode shows smooth charge–discharge profiles, while the slurry-cast cathode shows noisy charging and soft-shorting behavior. In conclusion, this work highlights that twin-screw extrusion as a scalable, solvent-free manufacturing method is advantageous in producing uniform cathodes, which mitigates anode instability.
Cation-disordered rocksalt-type high-entropy cathodes for Li-ion batteries
Explore the source record for details and available documents.
Lithium vanadium oxide (Li 1.1 V 3 O 8 ) thick porous electrodes with high rate capacity: utilization and evolution upon extended cycling elucidated via operando energy dispersive X-ray diffraction and continuum simulation
The phase distribution of lithiated LVO in thick (~500 μm) porous electrodes (TPEs) designed to facilitate both ion and electron transport was determined using synchrotron-based operando energy dispersive X-ray diffraction (EDXRD). Probing 3 positions in the TPE while cycling at a 1C rate revealed a homogeneous phase transition across the thickness of the electrode at the 1st and 95th cycles. Additionally, continuum modelling indicated uniform lithiation across the TPE in agreement with the EDXRD results and ascribed decreasing accessible active material to be the cause of loss in delivered capacity between the 1st and 95th cycles. The model was supported by the observation of significant particle fracture by SEM consistent with loss of electrical contact. Overall, the combination of operando EDXRD, continuum modeling, and ex situ measurements enabled a deeper understanding of lithium vanadium oxide transport properties under high rate extended cycling within a thick highly porous electrode architecture.
Perovskite Na-ion conductors developed from analogous Li 3 x La 2/3− x TiO 3 (LLTO): chemo-mechanical and defect engineering
New Na-ion conductors Na 0.5 La 0.5 ZrO 3 and Na 0.25 La 0.25 Ba 0.5 ZrO 3 with expanded lattices were developed based on perovskite LLTO, successfully increasing the conductivities vs. unexpanded (Na,La)TiO 3 by up to ∼50×.
Pore and grain chemistry during sintering of garnet-type Li 6.4 La 3 Zr 1.4 Ta 0.6 O 12 solid-state electrolytes
Graphic illustrating the chemical reactions that occur during sintering of LLZTO pellets up to 1100 °C.
Li-ion conductivity in Li[subscript 2]OHCl[subscript 1;#8722;x]Br[subscript x] solid electrolytes: g
Explore the source record for details and available documents.
Strain Sensitivity of Li -ion Conductivity in β - Li 3 PS 4 Solid Electrolyte
Not Available
“Flower-like” Li 4 Ti 5 O 12 -multiwalled carbon nanotube composite structures with performance as highrate anode-materials for li-ion battery applications and methods of synthesis thereof
A method of fabricating nanocomposite anode material embodying a lithium titanate (LTO)-multi-walled carbon nanotube (MWNT) composite intended for use in a lithium-ion battery includes providing multi-walled carbon nanotube (MWNTs), including nanotube surfaces, onto which functional oxygenated carboxylic acid moieties are arranged, generating 3D flower-like, lithium titanate (LTO) microspheres, including thin nanosheets and anchoring the acid-functionalized MWNTs onto surfaces of the 3D LTO microspheres by π-π interaction strategy to realize the nanocomposite anode material.
Li 3 VP 3 O 9 N as a Multielectron Redox Cathode for Li-Ion Battery
Explore the source record for details and available documents.
OVERVIEW OF RECENT COMPATIBILITY ASSESSMENTS IN FLOWING EXPERIMENTS: Sn, Li, Pb-Li AND MOLTEN SALTS
Explore the source record for details and available documents.
“Flower-like” LI 4 TI 5 O 12 -multiwalled carbon nanotube composite structures with performance as highrate anode-materials for Li-ion battery applications and methods of synthesis thereof
A method of fabricating nanocomposite anode material embodying a lithium titanate (LTO)-multi-walled carbon nanotube (MWNT) composite intended for use in a lithium-ion battery includes providing multi-walled carbon nanotube (MWNTs), including nanotube surfaces, onto which functional oxygenated carboxylic acid moieties are arranged, generating 3D flower-like, lithium titanate (LTO) microspheres, including thin nanosheets and anchoring the acid-functionalized MWNTs onto surfaces of the 3D LTO microspheres by π-π interaction strategy to realize the nanocomposite anode material.
Materials Data on Li by Materials Project
Li is alpha Samarium structured and crystallizes in the trigonal R-3m space group. The structure is three-dimensional. there are five inequivalent Li sites. In the first Li site, Li is bonded to twelve Li atoms to form a mixture of edge, face, and corner-sharing LiLi12 cuboctahedra. There are six shorter (3.04 Å) and six longer (3.06 Å) Li–Li bond lengths. In the second Li site, Li is bonded to twelve Li atoms to form a mixture of edge, face, and corner-sharing LiLi12 cuboctahedra. All Li–Li bond lengths are 3.06 Å. In the third Li site, Li is bonded to twelve Li atoms to form a mixture of edge, face, and corner-sharing LiLi12 cuboctahedra. There are six shorter (3.04 Å) and six longer (3.06 Å) Li–Li bond lengths. In the fourth Li site, Li is bonded to twelve Li atoms to form a mixture of edge, face, and corner-sharing LiLi12 cuboctahedra. There are six shorter (3.04 Å) and six longer (3.06 Å) Li–Li bond lengths. In the fifth Li site, Li is bonded to twelve Li atoms to form a mixture of edge, face, and corner-sharing LiLi12 cuboctahedra. There are three shorter (3.04 Å) and six longer (3.06 Å) Li–Li bond lengths.
Li-Metal Anode in Dilute Electrolyte LiFSI/TMP: Electrochemical Stability Using Ab Initio Molecular Dynamics
Ab initio molecular dynamics simulations were performed for Li + conducting electrolytes based on trimethyl phosphates (TMP) and lithium bis(fluorosulfonyl)imide (Li + FSI – ) salt in contact with a Li-metal electrode. We focused on the transient-state behavior at the electrolyte, interfacial electrolyte–Li-metal electrode, and lithium reference electrode–electrolyte–Li-metal electrode to study dynamics and activation energy barriers of the Li + ion, electrochemical and thermal stability of the interface electrode-electrolyte, and potential behavior of the Li-metal electrode, respectively. Our results show that in the most stable state, Li + ions are tetrahedrally coordinated to three TMPs and one FSI – . The inner solvation shell of a Li-ion is composed of three TMP and one FSI – in one contact ion-pair and four TMPs in a solvent-separated ion-pair. On the other hand, Li-ions transport through electrolyte cages takes place when they are coordinated with three or less molecules that could be a combination of TMPs and FSI – . The decomposition pathway of the LiFSI salt when in direct contact with the Li-metal anode starts with defluorination of FSI – , rapidly losing F– to the lithium surface, forming LiF species. The remaining FSO 2 NSO 2 –2 with the addition of 2e – from the Li-metal decomposes into SO 2 –2 and NFSO 2 –2 . SO 2 –2 deposits on the Li-surface and decomposes into Li 2 O and Li 2 S. The remaining NFSO 2 –2 defluorinates, losing F – ion to the lithium surface, resulting in LiF and the remaining NSO 2 –1 deposits on the lithium surface and decomposes in the following picoseconds, forming several binary compounds such as Li 3 N, Li 2 S and Li 2 O. In contrast, when the salt is solvated by the TMP molecules, avoiding a direct contact with the Li metal electrode, only one defluorination occurs, decomposing the FSI – into FSO 2 NSO 2 –2 and a F – . The two anions remain stable as they are solvated by the TMP molecules. Furthermore, we also analyzed the open circuit potential energy (OCPE) of the Li-metal electrode during the SEI formation. OCPE is calculated from the average local potential profile difference within the Li-metal electrode and a pristine Li-crystal reference electrode (LRE). When no SEI is formed, the Li-metal electrode has an average OCPE of +0.36 eV vs LRE. Due to the formation of a SEI, the Li-metal electrode has an average OCPE between -0.07 and -0.21 eV vs LRE. The OCPE of the Li-metal electrode decreases by ~0.42 eV when a SEI is formed.
Petaloid-shaped ZnO coated carbon felt as a controllable host to construct hierarchical Li composite anode
Prestoring Li metal into the 3D host via thermal infusion strategy has been considered as an effective approach on suppressing Li dendrites growth of Li-metal anode during cycling. However, the fast Li infusing process generally induces uncontrollable and undesirable structures during the formation of composite Li metal anode. It is widely accepted that both physical and chemical interactions between the molten Li and the hosts provide driving forces for Li infusing into the host, but which one plays the dominant role has not been explored clearly. In this work, a 3D carbon felt coated by petaloid zinc oxide (CFZO) is designed as a controllable host for prestoring Li metal via thermal infusion method. It is revealed that the morphology induced physical driving force plays a more important role than the chemical reaction between ZnO and molten Li in the thermal infusion process. The physical driving force originates from the capillarity effect, depending on the roughness of the host according to Wenzel's model. An adjustable Li infusing process can be controlled to fabricate the Li composite electrode with a hierarchical structure (with dense Li-rich layer and porous Li-poor layer). The unique structure of the CFZO-Li not only provides enough spaces for Li deposition, but also disperses local current density to induce a uniform Li deposition behavior, thus Li dendrites can be suppressed effectively. As a result, CFZO-Li anode exhibits promising cycle stability when coupled with both Li-containing (LiNi 0.8 Co 0.15 Al 0.05 O 2 ) and Li-free (sulfur) cathodes.
Materials Data on Li(FeGe)6 by Materials Project
Li(FeGe)6 crystallizes in the hexagonal P6/mmm space group. The structure is three-dimensional. there are two inequivalent Li sites. In the first Li site, Li is bonded to twelve equivalent Fe and eight Ge atoms to form distorted corner-sharing LiFe12Ge8 hexagonal bipyramids. All Li–Fe bond lengths are 3.22 Å. There are two shorter (2.70 Å) and six longer (2.86 Å) Li–Ge bond lengths. In the second Li site, Li is bonded to twelve Fe and eight Ge atoms to form a mixture of distorted corner and face-sharing LiFe12Ge8 hexagonal bipyramids. There are six shorter (3.20 Å) and six longer (3.22 Å) Li–Fe bond lengths. There are two shorter (2.69 Å) and six longer (2.88 Å) Li–Ge bond lengths. There are two inequivalent Fe sites. In the first Fe site, Fe is bonded in a 12-coordinate geometry to two Li, four Fe, and six Ge atoms. All Fe–Fe bond lengths are 2.51 Å. There are four shorter (2.47 Å) and two longer (2.61 Å) Fe–Ge bond lengths. In the second Fe site, Fe is bonded in a 12-coordinate geometry to two equivalent Li, four equivalent Fe, and six Ge atoms. There are a spread of Fe–Ge bond distances ranging from 2.46–2.60 Å. There are four inequivalent Ge sites. In the first Ge site, Ge is bonded in a 8-coordinate geometry to one Li, six Fe, and one Ge atom. The Ge–Ge bond length is 2.61 Å. In the second Ge site, Ge is bonded in a 7-coordinate geometry to one Li and six Fe atoms. In the third Ge site, Ge is bonded in a 8-coordinate geometry to two equivalent Li and six Fe atoms. In the fourth Ge site, Ge is bonded in a 8-coordinate geometry to one Li, six equivalent Fe, and one Ge atom. The Ge–Ge bond length is 2.59 Å.
Materials Data on Li(FeO2)2 by Materials Project
Li(FeO2)2 is Spinel-like structured and crystallizes in the monoclinic Cc space group. The structure is three-dimensional. there are two inequivalent Li sites. In the first Li site, Li is bonded to four O atoms to form LiO4 tetrahedra that share corners with twelve FeO6 octahedra. The corner-sharing octahedra tilt angles range from 57–64°. There are a spread of Li–O bond distances ranging from 1.94–2.03 Å. In the second Li site, Li is bonded to four O atoms to form distorted LiO4 trigonal pyramids that share corners with six FeO6 octahedra and edges with three FeO6 octahedra. The corner-sharing octahedra tilt angles range from 60–65°. There are a spread of Li–O bond distances ranging from 1.78–1.95 Å. There are four inequivalent Fe sites. In the first Fe site, Fe is bonded to six O atoms to form FeO6 octahedra that share corners with two equivalent FeO6 octahedra, corners with three equivalent LiO4 tetrahedra, a cornercorner with one LiO4 trigonal pyramid, edges with five FeO6 octahedra, and an edgeedge with one LiO4 trigonal pyramid. The corner-sharing octahedra tilt angles range from 50–52°. There are a spread of Fe–O bond distances ranging from 1.92–1.99 Å. In the second Fe site, Fe is bonded to six O atoms to form FeO6 octahedra that share corners with six FeO6 octahedra, corners with three equivalent LiO4 tetrahedra, corners with three equivalent LiO4 trigonal pyramids, and edges with three FeO6 octahedra. The corner-sharing octahedra tilt angles range from 49–55°. There are a spread of Fe–O bond distances ranging from 2.02–2.11 Å. In the third Fe site, Fe is bonded to six O atoms to form FeO6 octahedra that share corners with two equivalent FeO6 octahedra, corners with three equivalent LiO4 tetrahedra, a cornercorner with one LiO4 trigonal pyramid, edges with five FeO6 octahedra, and an edgeedge with one LiO4 trigonal pyramid. The corner-sharing octahedra tilt angles range from 49–52°. There are a spread of Fe–O bond distances ranging from 1.92–1.98 Å. In the fourth Fe site, Fe is bonded to six O atoms to form FeO6 octahedra that share corners with two equivalent FeO6 octahedra, corners with three equivalent LiO4 tetrahedra, a cornercorner with one LiO4 trigonal pyramid, edges with five FeO6 octahedra, and an edgeedge with one LiO4 trigonal pyramid. The corner-sharing octahedral tilt angles are 55°. There are a spread of Fe–O bond distances ranging from 1.99–2.06 Å. There are eight inequivalent O sites. In the first O site, O is bonded in a rectangular see-saw-like geometry to one Li and three Fe atoms. In the second O site, O is bonded in a rectangular see-saw-like geometry to one Li and three Fe atoms. In the third O site, O is bonded to one Li and three Fe atoms to form a mixture of distorted edge and corner-sharing OLiFe3 tetrahedra. In the fourth O site, O is bonded in a rectangular see-saw-like geometry to one Li and three Fe atoms. In the fifth O site, O is bonded to one Li and three Fe atoms to form distorted corner-sharing OLiFe3 tetrahedra. In the sixth O site, O is bonded in a rectangular see-saw-like geometry to one Li and three Fe atoms. In the seventh O site, O is bonded to one Li and three Fe atoms to form a mixture of distorted edge and corner-sharing OLiFe3 tetrahedra. In the eighth O site, O is bonded to one Li and three Fe atoms to form a mixture of distorted edge and corner-sharing OLiFe3 tetrahedra.