Engineering Papers⌕ Search

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.

At least 307 records · Page 17
All sourcesNASA NTRSDOE OSTI
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↗
DOE OSTI2022

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

Abstract 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. 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.

Pei, Yi↗
DOE OSTI2025

Development of an interatomic potential for the Ta–Li system

A new interatomic potential for the Ta–Li system is introduced to facilitate the study of phase stability, mechanical properties and non-equilibrium dynamics after Li implantation in Ta. Here, this potential is based on a generalization of the embedded atom method (GEAM) and includes contributions from embedding energy, explicit two- and three-body interactions, and nonlocal many-body interaction terms. The parameters of the potential are optimized using energies and atomic forces for a wide range of configurations obtained from ab initio density functional theory (DFT) calculations. The potential is rigorously validated across a range of physical properties, including elastic constants, equations of state, phonon dispersion curves, point defect properties, and melting temperatures for different compositions. Although our potential is trained on a small dataset, its accuracy is comparable to that of available machine learning potentials for Li and Ta. Our simulations show that at temperatures below 500 K, Li atoms in Ta–Li alloys form clusters separated by Ta-rich domains, and we find no evidence of ordered phase formation. For Li concentrations below a few percent, Li atoms preferentially segregate to surfaces and grain boundaries. However, in alloys containing more than ~10% Li, the accumulation of Li in symmetric-tilt grain boundaries can lead to one of the following effects: formation of amorphous-like regions, changes in grain boundary structural units, or lateral movement of the grain boundary.

GEAM potential↗
DOE OSTI2020

Definition of Redox Centers in Reactions of Lithium Intercalation in Li 3 RuO 4 Polymorphs

Cathodes based on layered LiMO 2 are the limiting components in the path toward Li-ion batteries with energy densities suitable for electric vehicles. Introducing an over-stoichiometry of Li increases storage capacity beyond a conventional mechanism of formal transition metal redox. However, the role and fate of the oxide ligands in such intriguing additional capacity remain unclear. This reactivity was predicted in Li 3 RuO 4 , making it a valuable model system. For this study, a comprehensive analysis of the redox activity of both Ru and O under different electrochemical conditions was carried out, and the effect of Li/Ru ordering was evaluated. Li 3 RuO 4 displays highly reversible Li intercalation to Li 4 RuO 4 below 2.5 V vs Li + /Li 0 , with conventional reactivity through the formal Ru 5+ -Ru 4+ couple. In turn, it can also undergo anodic Li extraction at 3.9 V, which involves O states to a much greater extent than Ru. This reaction competes with side processes such as electrolyte decomposition and, to a much lesser extent, oxygen loss. Although the associated capacity is reversible, reintercalation unlocks a different, conventional pathway also involving the formal Ru 5+ -Ru 4+ couple despite operating above 2.5 V, leading to chemical hysteresis. This new pathway is both chemically and electrochemically reversible in subsequent cycles. This work exemplifies both the challenge of stabilizing highly depleted O states, even with 4d metals, and the ability of solids to access the same redox couple at two very different potential windows depending on the underlying structural changes. It highlights the importance of properly defining the covalency of oxides when defining charge compensation in view of the design of materials with high capacity for Li storage.

37 INORGANIC, ORGANIC, PHYSICAL, AND ANALYTICAL CH↗
DOE OSTI2021

Evolution of Oxygen Ligands upon Large Redox Swings of Li 3 IrO 4

The limits of intercalation electrochemistry continue to be tested in the quest for ever increasing gains in the storage capability of Li-ion cathodes. The subsequent push for multi-electron reactivity has led to the recognition of the extremely versatile role of oxide ligands in charge compensation when there is a large redox swing. Li 3 IrO 4 is a unique model of such activity because it can reversibly cycle between Li 1 IrO 4 and Li 4.7 IrO 4 . In this study, X-ray spectroscopy, magnetic measurements and computational simulations uncover the evolution of O states in the different steps, compared to the involvement of Ir. While the process between Li 1 IrO 4 and Li 3 IrO 4 is dominated by the unconventional lattice oxygen redox, the process between Li 3 IrO 4 and Li 4.7 IrO 4 involves a conventional change of the formal oxidation state of Ir, which affects O due to the high covalency. The O states of Li 3 IrO 4 exhibit a very high reversibility after the whole 3.7-electron process, completely restoring the pristine state.

25 ENERGY STORAGE↗
DOE OSTI2024

Lithium Dendrite-Free Li 7 N 2 I-LiOH Solid Electrolytes for High Energy Lithium Batteries

All-solid-state lithium batteries (ASSLBs) hold great potential to improve the safety and energy density of today’s lithium-ion batteries by using non-flammable inorganic solid electrolytes. Solid electrolytes (SEs) are believed to prevent Li dendrite growth because of high mechanical strength and high Li+ transference numbers. Significant advances in SE have been achieved, among which, Li7La3Zr2O12 (LLZO) and Li2S–P2S5 (LPS) are the most promising SEs for bulk-type solid-state lithium batteries because of high ionic conductivities (>10-4 S/cm2). However, in contrast to our expectations, the growth of lithium dendrites is not suppressed but is facilitated in LLZOs and LPSs regardless of dopants, porosity, and crystallinity of the electrolytes. Despite the unity Li transference number and over two-times of shear modulus than that of Li metal, the critical current densities for Li plating and stripping in these SEs are less than 1.0 mA cm-2, which is one-fourth to one-tenth of that in liquid electrolytes at room temperature. The incompatibility between LLZO and LPS with Li metal seriously limits the energy density of all-solid-state batteries. The mechanism for lithium dendrite formation and growth in SEs are still disputable. Lack of understanding of the Li dendrite formation mechanism seriously impeded the development of solid-state lithium batteries. The development of the criterion for Li dendrite suppression is essential for the success of solid electrolyte lithium batteries. In this project, a criterion for Li dendrite suppression will be developed through thermodynamics and kinetics analysis of lithium dendrite nucleation/growth, which will guide the solid-state electrolyte design. Li7N2I-LiOH, Li5NI2-LiOH and Li3YCl6 solid electrolyte with high ionic conductivity and low electronic conductivity were used to validate the criterion for lithium dendrite suppression. Different surface modifications were also explored to enhance the dendrite suppression capability of SSEs.

25 ENERGY STORAGE↗
DOE OSTI2024

Superionic conducting vacancy-rich β-Li 3 N electrolyte for stable cycling of all-solid-state lithium metal batteries

The advancement of all-solid-state lithium metal batteries requires breakthroughs in solid-state electrolytes (SSEs) for the suppression of lithium dendrite growth at high current densities and high capacities (>3 mAh cm -2 ) and innovation of SSEs in terms of crystal structure, ionic conductivity and rigidness. Here we report a superionic conducting, highly lithium-compatible and air-stable vacancy-rich β-Li 3 N SSE. This vacancy-rich β-Li 3 N SSE shows a high ionic conductivity of 2.14 × 10 -3 S cm -1 at 25 °C and surpasses almost all the reported nitride-based SSEs. A Li- and N-vacancy-mediated fast lithium-ion migration mechanism is unravelled regarding vacancy-triggered reduced activation energy and increased mobile lithium-ion population. All-solid-state lithium symmetric cells using vacancy-rich β-Li 3 N achieve breakthroughs in high critical current densities up to 45 mA cm -2 and high capacities up to 7.5 mAh cm -2 , and ultra-stable lithium stripping and plating processes over 2,000 cycles. The high lithium compatibility mechanism of vacancy-rich β-Li 3 N is unveiled as intrinsic stability to lithium metal. In addition, β-Li 3 N possesses excellent air stability through the formation of protection surfaces. All-solid-state lithium metal batteries using the vacancy-rich β-Li 3 N as SSE interlayers and lithium cobalt oxide (LCO) and Ni-rich LiNi 0.83 Co 0.11 Mn 0.06 O 2 (NCM83) cathodes exhibit excellent battery performance. Extremely stable cycling performance is demonstrated with high capacity retentions of 82.05% with 95.2 mAh g -1 over 5,000 cycles at 1.0 C for LCO and 92.5% with 153.6 mAh g -1 over 3,500 cycles at 1.0 C for NCM83. Utilizing the vacancy-rich β-Li 3 N SSE and NCM83 cathodes, the all-solid-state lithium metal batteries successfully accomplished mild rapid charge and discharge rates up to 5.0 C, retaining 60.47% of the capacity. Notably, these batteries exhibited a high areal capacity, registering approximately 5.0 mAh cm -2 for the compact pellet-type cells and around 2.2 mAh cm -2 for the all-solid-state lithium metal pouch cells.

25 ENERGY STORAGE↗
DOE OSTI2022

Li-Ion Diffusion Correlations in LiAlGeO 4 : Quasielastic Neutron Scattering and Ab Initio Simulation

Here, we investigated the impact of Li stoichiometry and host flexibility on Li + diffusion processes in LiAlGeO 4 at the microscopic level using quasielastic neutron scattering (QENS) and ab initio molecular dynamics (AIMD) simulations. Using sufficiently long AIMD trajectories, we could simulate the observed QENS signal and identify the localized dynamics of Li in crystalline LiAlGeO 4 . Such information is vital to identify the bottleneck of diffusion processes and design materials for battery application. Our AIMD simulations in LiAlGeO 4 reveal that the Li + conductivity can be significantly improved by manipulating the Li stoichiometry and/or host flexibility via amorphization. We determined that excess Li stoichiometry enhances the Coulomb repulsion of neighboring Li sites and softens the host structure to enable faster Li + diffusion along the hexagonal c-axis. In the amorphous structure, random orientations of AlO 4 and GeO 4 polyhedral units create a wide distribution of intersite distances and significantly soften the host structure, greatly enhancing the Li + diffusion. The simulations are used to understand the nature of diffusion, especially the role of the host structure, the possible hopping pathways, and the diffusion behavior in various structures of LiAlGeO 4 .

localized dynamics↗
DOE OSTI2022

Dual Passivation of Cathode and Anode through Electrode–Electrolyte Interface Engineering Enables Long-Lifespan Li Metal–SPAN Batteries

The reliability and durability of lithium metal (Li 0 )–sulfur batteries are largely limited by the undesired Li 0 plating-stripping irreversibility and the detrimental polysulfide dissolution, yet approaches that can simultaneously address the above anodic and cathodic problems are scarce. In this study, we report the stable operation of a Li 0 -SPAN (sulfurized polyacrylonitrile) battery via an anode–cathode dual-passivation approach. By combination of a fluorinated localized high concentration electrolyte (LHCE) and a Li 3 N-forming additive (TMS-N 3 ), robust and highly conductive electrode passivation layers are formed in situ on the surface of both the Li 0 anode and the SPAN cathode. The resulting highly reversible, dendrite-free, and high-density Li 0 plating morphology enables a high Coulombic efficiency of 99.4%. Advanced tender energy X-ray spectroscopy also reveals the eliminated Li 2 S formation and minimized polysulfide dissolution in SPAN cathodes, leading to a high capacity of 580 mAh/g SPAN and stable cycling with negligible capacity decay (0.7%) for 800 cycles. This electrode–electrolyte interphase engineering strategy has tackled the major limitations of Li–S batteries in both ether- and carbonate-based electrolyte systems and under a wide temperature range from –10 to +50 °C, thus providing insightful guidelines for the rational design of highly durable and high-energy-density Li 0 -S batteries.

25 ENERGY STORAGE↗
DOE OSTI2020

Current Density Regulated Atomic to Nanoscale Process on Li Deposition and Solid Electrolyte Interphase Revealed by Cryogenic Transmission Electron Microscopy

Current density has been perceived to play a critical rule for controlling Li deposition morphology and solid electrolyte interphase (SEI). However, the atomic level mechanism of current density on Li deposition and the SEI remains unclear. In this work, based on cryogenic transmission electron microscopy imaging combined with energy dispersive X-ray spectroscopy and electron energy loss spectroscopy electronic structure analyses, we reveal the atomic level correlation of Li deposition morphology and SEI with current density. We discover that increasing current density leads to increased overpotential for Li nucleation and growth, leading to the transition from growth-limited to nucleation-limited mode for Li dendrite. Independence of current density, the electrochemically deposited Li metal (EDLi) exhibits crystalline whisker-like morphology. The SEI formed at low current density (0.1 mA cm -2 ) is monolithic amorphous; while, a current density of above 2 mA cm -2 leads to a mosaic structured SEI, featuring an amorphous matrix with Li 2 O and LiF dispersoids, and the thickness of the SEI increases with the increase of current density. Uniquely, the Li 2 O particles is spatially located at the top surface of the SEI, while LiF is spatially adjacent to the Li-SEI interface. These results highlight the possible tuning of crucial structural and chemical features of EDLi and SEI through altering deposit conditions and consequently direct correlation with electrochemical performance.

37 INORGANIC, ORGANIC, PHYSICAL, AND ANALYTICAL CH↗
DOE OSTI2025

Unusual Li 2 O sublimation promotes single-crystal growth and sintering

Li 2 O is rarely used for cathode material synthesis due to its high melting point (1,438 °C). Here we discover that Li 2 O can sublimate at 800-1,000 °C under ambient pressure, opening new possibilities for cathode synthesis. We propose a mechanism that enables synthesis of single crystals-such as LiNi 0.8 Mn 0.1 Co 0.1 O 2 (NMC811) or LiNi 0.9 Mn 0.05 Co 0.05 O 2 (NMC90)-without direct contact with Li 2 O salts. We show that Li 2 O vapour successfully converts spent polycrystalline NMC811 into segregated single crystals without milling or post-treatment. The Li 2 O vapour, derived from Li 2 O solids, diffuses rapidly and reacts with precursors, mimicking a molten-salt environment, which facilitates single-crystal growth. The chemical lithiation process continuously drives Li 2 O sublimation, sintering the crystals. Single crystals derived from Li 2 O and fresh precursors or spent polycrystals exhibit outstanding cycling after 1,000 cycles in full cells. The demonstrated Li 2 O sublimation and its universal role in promoting single-crystal growth provides an effective approach for single-crystal synthesis, scale-up and recycling.

25 ENERGY STORAGE↗
DOE OSTI2021

Theoretical evidence of water serving as a promoter for lithium superoxide disproportionation in Li-O 2 batteries

Experimental evidence has demonstrated that the presence of water in non-aqueous electrolytes significantly affects Li-O 2 electrochemistry. Understanding the reaction mechanism for Li 2 O 2 formation in the presence of water impurities is important to understand Li-O 2 battery performance. A recent experiment has found that very small amounts of water (as low as 40 ppm) can significantly affect the product formation in Li-O 2 batteries as opposed to essentially no water (1 ppm). Although experimental as well as theoretical work has proposed mechanisms of Li 2 O 2 formation in the presence of much larger amounts of water, none of the mechanisms provide an explanation for the observations for very small amounts of water. In this work, density functional theory (DFT) was utilized to obtain a mechanistic understanding of the Li-O 2 discharge chemistry in a dimethoxyethane (DME) electrolyte containing an isolated water and no water. The reaction pathways for Li 2 O 2 formation from LiO 2 on a model system were carefully evaluated with different level of theories, i.e. PBE (PW), B3LYP/6-31G(2df,p), B3LYP/6-311++G(2df,p) and G4MP2. The results indicate that the LiO 2 disproportionation reaction to Li 2 O 2 can be promoted by the water in DME electrolyte, which explains why there is a significant difference compared to when no water is present in the experimentally observed discharge product distributions. Ab initio molecular dynamics calculations were also used to investigate the disproportionation of LiO 2 dimer in explicit DME. This work adds to the fundamental understanding of the discharge chemistry of a Li-O 2 battery.

25 ENERGY STORAGE↗