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All sourcesNASA NTRSDOE OSTI
NASA NTRS1987

Rare-earth substitution in (BiYCa)3(FeSiGe)5O12 bubble films

The substitution of Y by Sm, Tb, Gd, and Ho in (BiYCa)3 FeSiGe)5O12 bubble garnet is shown to have large effects on the growth-induced anisotropy (GIA). The presently accepted film composition intended for 6-or 8-micron-period bubble memory devices demands partial substitution of Y by Gd and Ho. However, comparing films grown under the same growth conditions, it is observed that YGdHoBilG films posess less (GIA) than their Gd, Ho-free counterparts. Thus, to satisfy (GIA) requirements, the supercooling during growth must be increased by 20 K to 80 K with undesirable effects on defect densities. A new film composition containing Sm, Tb, and Gd has been formulated to satisfy all known material property specifications for 6- or 8-micron-period memory devices. It can be grown with only 45-50 K supercooling.

Luther, L. C.↗
NASA NTRS2010

Modeling of the Magnetosphere of Mercury at the Time of the First MESSENGER Flyby

The MESSENGER spacecraft flyby of Mercury on 14 January 2008 provided a new opportunity to study the intrinsic magnetic field of the innermost planet and its interaction with the solar wind, The model presented in this paper is based on the solution of the three-dimensional, bi-f1uid equations for solar wind protons and electrons in the absence of mass loading, In this study we provide new estimates of Mercury's intrinsic magnetic field and the solar wind conditions that prevailed at the time of the flyby. We show that the location of the boundary layers and the strength of the magnetic field along the spacecraft trajectory can be reproduced with a solar wind ram pressure P(sub sw) = 6.8 nPa and a planetary magnetic dipole having a magnitude of 210 R(sub M)(exp 3)- nT and an offset of 0.18 R(sub M) to the north of the equator, where R(sub M) is Mercury's radius. Analysis of the plasma flow reveals the existence of a stable drift belt around the planet; such a belt can account for the locations of diamagnetic decreases observed by the MESSENGER Magnetometer. Moreover, we determine that the ion impact rate at the n011hern cusp was four times higher than at the southern cusp, a result that provides a possible explanation for the observed north-south asymmetry in exospheric sodium in the neutral tail.

Benna, Mehdi↗
DOE OSTI2024

Off-shell pion properties: Electromagnetic form factors and light-front wave functions

The off-shell pion electromagnetic form factors are explored with corresponding off-shell light-front wave functions modeled by constituent quark and antiquark. We apply the Mandelstam approach for the microscopic computation of the form factors relating the model parameters with the pion decay constant and charge radius. Analyzing the existing data on the cross sections for the Sullivan process, 1 H(e,e',π + )⁢n, Charged pion form factor between Q 2 = 0.60, and 2.45 GeV 2 . I. Measurements of the cross section for the 1 H⁡(e,e'⁢π + )⁢n reaction, we extract the off-shell pion form factor using the relation derived from the generalized Ward-Takahashi identity for the pion electromagnetic current. They are compared with our previous results from exactly solvable manifestly covariant model of a (3+1)-dimensional fermion field theory. We find that the adopted constituent quark model reproduces the extracted off-shell form factor F 1 ⁡(Q 2 ,t) from the experimental data within a few percent difference and matches well with our previous theoretical simulation which exhibits a variation of about 10% for the extracted off-shell pion form factor g(Q 2 ,t). We also identify the pion valence parton distribution function (PDF) and transverse momentum distribution (TMD) in terms of the light-front wave function and discuss their off-shell properties.

72 PHYSICS OF ELEMENTARY PARTICLES AND FIELDS↗
NASA NTRS2020

The Destruction and Recreation of the X-Ray Corona in a Changing-look Active Galactic Nucleus

We present the drastic transformation of the X-ray properties of the active galactic nucleus 1ES 1927+654, following a changing-look event. After the optical/UV outburst the power-law component, produced in the X-ray corona, disappeared, and the spectrum of 1ES 1927+65 instead became dominated by a blackbody component (kT ∼ 80− 120 eV). This implies that the X-ray corona, ubiquitously found in AGN, was destroyed in the event. Our dense ∼ 450 day long X-ray monitoring shows that the source is extremely variable in the X-ray band. On long time scales the source varies up to ∼ 4 dex in ∼ 100 days, while on short timescales up to ∼ 2 dex in ∼ 8 hours. The luminosity of the source is found to first show a strong dip down to ∼ 10(exp 40) erg/s, and then a constant increase in luminosity to levels exceeding the pre-outburst level &300 days after the optical event detection, rising up asymptotically to ∼ 2 × 10(exp 44) erg/s. As the X-ray luminosity of the source increases, the X-ray corona is recreated, and a very steep power-law component (Γ ≃ 3) reappears, and dominates the emission for 0.3–2 keV luminosities & 10(exp 43.7) erg/s, ∼ 300 days after the beginning of the event. We discuss possible origins of this event, and speculate that our observations could be explained by the interaction between the accretion flow and debris from a tidally disrupted star. Our results show that changing-look events can be associated with dramatic and rapid transformations of the innermost regions of accreting SMBHs.

C. Ricci↗
DOE OSTI2020

Materials Data on Ba10Ho5(Cu5O11)3 by Materials Project

Ba10Ho5(Cu5O11)3 crystallizes in the triclinic P-1 space group. The structure is three-dimensional. there are five inequivalent Ba2+ sites. In the first Ba2+ site, Ba2+ is bonded in a 9-coordinate geometry to nine O2- atoms. There are a spread of Ba–O bond distances ranging from 2.72–3.03 Å. In the second Ba2+ site, Ba2+ is bonded in a 9-coordinate geometry to nine O2- atoms. There are a spread of Ba–O bond distances ranging from 2.72–3.01 Å. In the third Ba2+ site, Ba2+ is bonded in a 10-coordinate geometry to ten O2- atoms. There are a spread of Ba–O bond distances ranging from 2.77–3.09 Å. In the fourth Ba2+ site, Ba2+ is bonded in a 9-coordinate geometry to nine O2- atoms. There are a spread of Ba–O bond distances ranging from 2.72–3.01 Å. In the fifth Ba2+ site, Ba2+ is bonded in a 9-coordinate geometry to nine O2- atoms. There are a spread of Ba–O bond distances ranging from 2.72–3.03 Å. There are three inequivalent Ho3+ sites. In the first Ho3+ site, Ho3+ is bonded in a body-centered cubic geometry to eight O2- atoms. There are a spread of Ho–O bond distances ranging from 2.39–2.44 Å. In the second Ho3+ site, Ho3+ is bonded in a body-centered cubic geometry to eight O2- atoms. There are a spread of Ho–O bond distances ranging from 2.39–2.44 Å. In the third Ho3+ site, Ho3+ is bonded in a body-centered cubic geometry to eight O2- atoms. There are four shorter (2.39 Å) and four longer (2.43 Å) Ho–O bond lengths. There are eight inequivalent Cu+2.07+ sites. In the first Cu+2.07+ site, Cu+2.07+ is bonded to five O2- atoms to form corner-sharing CuO5 square pyramids. There are a spread of Cu–O bond distances ranging from 1.94–2.35 Å. In the second Cu+2.07+ site, Cu+2.07+ is bonded to five O2- atoms to form distorted corner-sharing CuO5 square pyramids. There are a spread of Cu–O bond distances ranging from 1.94–2.46 Å. In the third Cu+2.07+ site, Cu+2.07+ is bonded to five O2- atoms to form distorted corner-sharing CuO5 square pyramids. There are a spread of Cu–O bond distances ranging from 1.94–2.48 Å. In the fourth Cu+2.07+ site, Cu+2.07+ is bonded to five O2- atoms to form distorted corner-sharing CuO5 square pyramids. There are a spread of Cu–O bond distances ranging from 1.93–2.48 Å. In the fifth Cu+2.07+ site, Cu+2.07+ is bonded to five O2- atoms to form distorted corner-sharing CuO5 square pyramids. There are a spread of Cu–O bond distances ranging from 1.93–2.46 Å. In the sixth Cu+2.07+ site, Cu+2.07+ is bonded in a square co-planar geometry to four O2- atoms. There is two shorter (1.90 Å) and two longer (1.91 Å) Cu–O bond length. In the seventh Cu+2.07+ site, Cu+2.07+ is bonded in a T-shaped geometry to three O2- atoms. There is two shorter (1.84 Å) and one longer (1.92 Å) Cu–O bond length. In the eighth Cu+2.07+ site, Cu+2.07+ is bonded in a T-shaped geometry to three O2- atoms. There is two shorter (1.83 Å) and one longer (1.88 Å) Cu–O bond length. There are seventeen inequivalent O2- sites. In the first O2- site, O2- is bonded in a 4-coordinate geometry to two Ba2+, two Ho3+, and two Cu+2.07+ atoms. In the second O2- site, O2- is bonded in a 4-coordinate geometry to two Ba2+, two equivalent Ho3+, and two Cu+2.07+ atoms. In the third O2- site, O2- is bonded in a 6-coordinate geometry to two Ba2+, two Ho3+, and two Cu+2.07+ atoms. In the fourth O2- site, O2- is bonded in a 4-coordinate geometry to two Ba2+, two Ho3+, and two Cu+2.07+ atoms. In the fifth O2- site, O2- is bonded in a 4-coordinate geometry to two Ba2+, two Ho3+, and two Cu+2.07+ atoms. In the sixth O2- site, O2- is bonded to four Ba2+ and two Cu+2.07+ atoms to form distorted corner-sharing OBa4Cu2 octahedra. The corner-sharing octahedra tilt angles range from 0–11°. In the seventh O2- site, O2- is bonded in a 6-coordinate geometry to four Ba2+ and two Cu+2.07+ atoms. In the eighth O2- site, O2- is bonded in a 6-coordinate geometry to four Ba2+ and two Cu+2.07+ atoms. In the ninth O2- site, O2- is bonded in a 6-coordinate geometry to four Ba2+ and two Cu+2.07+ atoms. In the tenth O2- site, O2- is bonded in a 6-coordinate geometry to four Ba2+ and two Cu+2.07+ atoms. In the eleventh O2- site, O2- is bonded in a 4-coordinate geometry to two Ba2+, two Ho3+, and two Cu+2.07+ atoms. In the twelfth O2- site, O2- is bonded in a 4-coordinate geometry to two Ba2+, two equivalent Ho3+, and two Cu+2.07+ atoms. In the thirteenth O2- site, O2- is bonded in a 4-coordinate geometry to two Ba2+, two Ho3+, and two Cu+2.07+ atoms. In the fourteenth O2- site, O2- is bonded in a 4-coordinate geometry to two Ba2+, two Ho3+, and two Cu+2.07+ atoms. In the fifteenth O2- site, O2- is bonded in a 4-coordinate geometry to two Ba2+, two Ho3+, and two Cu+2.07+ atoms. In the sixteenth O2- site, O2- is bonded in a distorted linear geometry to four Ba2+ and two Cu+2.07+ atoms. In the seventeenth O2- site, O2- is bonded in a distorted linear geometry to four Ba2+ and two equivalent Cu+2.07+ atoms.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Remote heteroepitaxy of GaN microrod heterostructures for deformable light-emitting diodes and wafer recycle

There have been rapidly increasing demands for flexible lighting apparatus, and micrometer-scale light-emitting diodes (LEDs) are regarded as one of the promising lighting sources for deformable device applications. Herein, we demonstrate a method of creating a deformable LED, based on remote heteroepitaxy of GaN microrod (MR) p - n junction arrays on c -Al 2 O 3 wafer across graphene. The use of graphene allows the transfer of MR LED arrays onto a copper plate, and spatially separate MR arrays offer ideal device geometry suitable for deformable LED in various shapes without serious device performance degradation. Moreover, remote heteroepitaxy also allows the wafer to be reused, allowing reproducible production of MR LEDs using a single substrate without noticeable device degradation. The remote heteroepitaxial relation is determined by high-resolution scanning transmission electron microscopy, and the density functional theory simulations clarify how the remote heteroepitaxy is made possible through graphene.

36 MATERIALS SCIENCE↗
NASA NTRS1991

Theoretical branching ratios for the 5I7 to 5I7 levels of Ho(3+) in the garnets A3B2C3O12 (A = Y,La,Lu,Gd; B = Al,Lu,Sc,Ga; C = Al,Ga)

Results are reported from an experimental study investigating triply ionized holmium in 10 garnets using the point-change model to predict theoretical energy levels and temperature-dependent branching ratios for the 5I7 to 5I8 manifolds for temperatures between 50 and 400 K. Plots were made for the largest lines at 300 K. YScAG was plotted twice, once for each set of X-ray data available. Energy levels are predicted based on theoretical crystal-field parameters, and good agreement to experiment is found. It is suggested that the present set of theoretical crystal-field parameters provides good estimates of the energy levels for the other hosts on which there are no experimental optical data. X-ray and index-of-refraction data are used to evaluate the performance of 10 lasers via a quantum mechanical model to predict the position of the energy levels and the temperature-dependent branching rations of the 5I7 to 5I8 levels of holmium. The fractional population inversion required for threshold is also evaluated.

Filer, Elizabeth D.↗
DOE OSTI2025

Quantum critical electro-optic and piezo-electric nonlinearities

Although electro-optic (EO) nonlinearities are essential for many quantum and classical photonics applications, a major challenge is inefficient modulation in cryogenic environments. Guided by the connection between phase transitions and nonlinearity, we identify the quantum paraelectric perovskite SrTiO 3 as a strong cryogenic EO [>500 picometers per volt (pm/V)] and piezo-electric material (>90 picocoulombs per newton) at T = 5 K, at frequencies to at least 1 megahertz. Furthermore, by tuning SrTiO 3 toward quantum criticality, we more than double the EO and piezo-electric effects, demonstrating a linear Pockels coefficient above 1000 pm/V. Furthermore, our results probe the link between quantum phase transitions, dielectric susceptibility, and nonlinearity, unlocking opportunities in cryogenic optical and mechanical systems and providing a framework for discovering new nonlinear materials.

Anderson, Christopher P. [Stanford University, CA ↗
DOE OSTI2020

Materials Data on HoTa7O19 by Materials Project

HoTa7O19 crystallizes in the hexagonal P-6c2 space group. The structure is three-dimensional. Ho3+ is bonded in a 8-coordinate geometry to eight O2- atoms. There are six shorter (2.40 Å) and two longer (2.63 Å) Ho–O bond lengths. There are two inequivalent Ta5+ sites. In the first Ta5+ site, Ta5+ is bonded in a 7-coordinate geometry to seven O2- atoms. There are a spread of Ta–O bond distances ranging from 1.93–2.46 Å. In the second Ta5+ site, Ta5+ is bonded in an octahedral geometry to six equivalent O2- atoms. All Ta–O bond lengths are 2.01 Å. There are five inequivalent O2- sites. In the first O2- site, O2- is bonded in a distorted trigonal planar geometry to one Ho3+ and two Ta5+ atoms. In the second O2- site, O2- is bonded in a trigonal planar geometry to three equivalent Ta5+ atoms. In the third O2- site, O2- is bonded in a distorted bent 150 degrees geometry to three equivalent Ta5+ atoms. In the fourth O2- site, O2- is bonded in a bent 150 degrees geometry to two equivalent Ta5+ atoms. In the fifth O2- site, O2- is bonded in a 3-coordinate geometry to one Ho3+ and three equivalent Ta5+ atoms.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Enhancing Enzyme-Mediated Hydrolysis of Mechanical Pulps by Deacetylation and Delignification

Alkaline induced deacetylation of the hemicellulose combined with subsequent mechanical refining enhanced the enzyme-mediated hydrolysis of pretreated corn stover. The addition of either NaOH (80 °C) or mild KOH (25 °C) to corn stover prior to mechanical refining led to greater than 80% deacetylation with the NaOH treatment also solubilizing low-molecular-weight lignin that was enriched in $β$-O-4 linkages with more than 25% and 13% of the total and surface lignin removed, respectively. Furthermore, the influence of deacetylation and delignification were further enhanced when NaOH was supplemented with 3% Na 2 SO 3 , resulting in 100% deacetylation, 34% delignification, and a >20% increase in the hydrolysis yield of the substrate xylan. A milder KOH treatment resulted in the retention of more than 95% of the lignin within the cellulose rich, water-insoluble fraction with no apparent change in the surface lignin. However, both methods resulted in enhanced xylan hydrolysis when treated with xylanases, suggesting that deacetylation had enhanced accessibility to the xylan present in the pretreated of corn stover. It was apparent that cellulose accessibility was also enhanced by partial delignification, as NaOH treatment resulted in a 65% and 43% increase in the Water Retention Value and Directed Orange dye adsorption, respectively.

37 INORGANIC, ORGANIC, PHYSICAL, AND ANALYTICAL CH↗
DOE OSTI2020

Materials Data on Ho2Cu(SiO3)4 by Materials Project

Ho2Cu(SiO3)4 crystallizes in the triclinic P-1 space group. The structure is three-dimensional. Ho3+ is bonded in a 7-coordinate geometry to seven O2- atoms. There are a spread of Ho–O bond distances ranging from 2.22–2.77 Å. Cu2+ is bonded in a distorted square co-planar geometry to four O2- atoms. There is two shorter (1.98 Å) and two longer (1.99 Å) Cu–O bond length. There are two inequivalent Si4+ sites. In the first Si4+ site, Si4+ is bonded to four O2- atoms to form corner-sharing SiO4 tetrahedra. There are a spread of Si–O bond distances ranging from 1.62–1.67 Å. In the second Si4+ site, Si4+ is bonded to four O2- atoms to form corner-sharing SiO4 tetrahedra. There are a spread of Si–O bond distances ranging from 1.63–1.67 Å. There are six inequivalent O2- sites. In the first O2- site, O2- is bonded in a distorted trigonal planar geometry to one Ho3+, one Cu2+, and one Si4+ atom. In the second O2- site, O2- is bonded in a distorted bent 120 degrees geometry to two Si4+ atoms. In the third O2- site, O2- is bonded in a 3-coordinate geometry to two equivalent Ho3+ and one Si4+ atom. In the fourth O2- site, O2- is bonded in a 3-coordinate geometry to one Ho3+, one Cu2+, and one Si4+ atom. In the fifth O2- site, O2- is bonded in a bent 150 degrees geometry to one Ho3+ and two Si4+ atoms. In the sixth O2- site, O2- is bonded in a 3-coordinate geometry to two equivalent Ho3+ and one Si4+ atom.

36 MATERIALS SCIENCE↗
DOE OSTI2024

Improving tubular protonic ceramic fuel cell performance by compensating Ba evaporation via a Ba-excess optimized proton conducting electrolyte synthesis strategy

Protonic ceramic fuel cells (PCFCs) are emerging as a promising technology for reduced temperature ceramic energy conversion devices. The BaCe 0.4 Zr 0.4 Y 0.1 Yb 0.1 O 3–δ (BCZYYb4411) electrolyte is notable for its high proton conductivity. However, the tendency of barium to volatilize in BCZYYb4411 during high-temperature sintering compromises its chemical stability and performance. This study investigates the effects of intentionally incorporating excess barium into BCZYYb4411, formulated as Ba 1+x Ce 0.4 Zr 0.4 Y0.1Yb 0.1 O 3–δ (where x = 0, 0.1, 0.2, and 0.3), with the aim of compensating barium evaporation and enhancing the physical and chemical properties. We find that excess barium results in a greater shrinkage rate, facilitating a denser electrolyte structure. This barium-enriched electrolyte demonstrates improved electrochemical performance by effectively counteracting the deleterious effects of barium evaporation. Applying this strategy to tubular PCFCs, we achieved a peak power density of 480 mW•cm –2 at 600 °C. This unique approach provides a simple, tunable, and easy-to-implement processing modification to achieve high-performance tubular PCFC.

25 ENERGY STORAGE↗
DOE OSTI2021

Magnetic structure of magnetoelectric multiferroic HoFeWO 6

The polar magnetic oxide, HoFeWO6, is synthesized, and its crystal structure, magnetic structure, and thermodynamic properties are investigated. HoFeWO 6 forms the polar crystal structure (space group Pna2 1 (#33)) due to the cation ordering of W 6+ and Fe 3+ . An antiferromagnetic transition at T N = 17 K is accompanied by a significant change in magnetic entropy with a value of ≈ 5 J kg -1 K-1 in a 70 kOe applied field. Temperature dependent neutron diffraction and magnetization data indicate that the Fe sublattice orders in a strongly non-collinear and non-coplanar arrangement below T N . The Fe ordering initially leads to induced ordering of the Ho spins such that the Ho spins also show behavior of long-range ordering that is evident from the neutron diffraction measurements. Below T ≈ 4 K, the Ho spins order independently and pull the Fe spins toward the direction of Ho spins. A comparison with the magnetic structures and corresponding ferroelectric properties of other members of RMWO 6 (R = Y, Sm-Tm, M = Cr, Fe, V) family indicate that the spontaneous polarization is due to the magnetic structure specific to the Fe sublattice through magnetoelectric coupling whereas the polarization is independent of the Ho sublattice.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Resonant x-ray absorption of strong-field-ionized CF 3 Br

We report on an experimental and theoretical study of strong-field laser ionization of CF 3 Br followed by resonant x-ray absorption at the Br K-edge. Distinct 1s -> 4p, 5p Rydberg transitions of Br q+ (q = 1-4) atomic ions are observed and identified with Hartree-Fock-Slater and relativistic configuration interaction calculations. Time-dependent density functional theory and ab initio molecular dynamics calculations were performed to simulate the dissociative ionization process and the molecular orbitals for the q = 1-4 charge states. Measurements were made with both parallel and perpendicular linear polarizations of the laser and x-rays, but dichroism was not observed, indicating negligible alignment by the laser ionization process. This result is explained by calculations on atomic Br and the molecular simulation.

74 ATOMIC AND MOLECULAR PHYSICS↗
DOE OSTI2020

Deficiencies in compression and yield in x-ray-driven implosions

This paper analyzes x-ray–driven implosions that are designed to be less sensitive to 2-D and 3-D effects in hohlraum and capsule physics. Key performance metrics including the burn-averaged ion temperature, hot-spot areal density, and fusion yield are found to agree with simulations where the design adiabat (internal pressure) is multiplied by a factor of 1.4. Furthermore, these results motivate the development of a simple model for interpreting experimental data, which is then used to quantify how improvements in compression could help achieve ignition.

70 PLASMA PHYSICS AND FUSION TECHNOLOGY↗
DOE OSTI2024

What next: Further implosion space exploration on the path to NIF extended yield capability

We present quantitative motivations and assessments of various proposed and ongoing directions to further improving yields and target gain of igniting indirect-drive implosions at the National Ignition Facility (NIF). These include increasing compression and confinement time, improving hohlraum and ablator efficiency, and further increasing peak power and laser energy. 1D hydroscaled simulations, augmented by analytic 1D theory, have been used to project yield improvements for each of these implosion optimization tracks, normalized to the best current performing 4 MJ shot. At current NIF capabilities of 2.2 MJ, 450 TW, we project several paths could reach 15 MJ yield levels. We also expect several key implosion physics questions will be addressed in attempting to reach this yield level. These include demonstrating to what extent lower adiabat designs leading to higher compression will increase gain and efficiency, and whether we can reduce residual kinetic energy and ablator-fuel mix that is probably limiting the current burn-up fraction. For an envisaged NIF upgrade to EL = 3 MJ at fixed 450 TW peak power, scaling capsule size and fuel thicknesses faster than pure hydroscaling should allow for yields that could reach up to 60–80 MJ, depending on the efficiency gains realized in increasing deuterium-tritium fuel thickness, reducing hohlraum losses, and switching to lower Z ablators. The laser-plasma instability and beam transmission scaling in these larger hohlraums is shown to be favorable if the spot size is increased with hohlraum scale.

70 PLASMA PHYSICS AND FUSION TECHNOLOGY↗
DOE OSTI2020

Materials Data on Ho11Te16ClO48 by Materials Project

Ho11Te16O48Cl crystallizes in the triclinic P-1 space group. The structure is three-dimensional. there are six inequivalent Ho3+ sites. In the first Ho3+ site, Ho3+ is bonded in a 7-coordinate geometry to seven O2- atoms. There are a spread of Ho–O bond distances ranging from 2.23–2.54 Å. In the second Ho3+ site, Ho3+ is bonded in a 7-coordinate geometry to seven O2- atoms. There are a spread of Ho–O bond distances ranging from 2.22–2.75 Å. In the third Ho3+ site, Ho3+ is bonded in a 8-coordinate geometry to eight O2- atoms. There are a spread of Ho–O bond distances ranging from 2.25–2.57 Å. In the fourth Ho3+ site, Ho3+ is bonded in a 8-coordinate geometry to eight O2- atoms. There are a spread of Ho–O bond distances ranging from 2.25–2.54 Å. In the fifth Ho3+ site, Ho3+ is bonded in an octahedral geometry to six O2- atoms. There are a spread of Ho–O bond distances ranging from 2.22–2.37 Å. In the sixth Ho3+ site, Ho3+ is bonded in a distorted pentagonal bipyramidal geometry to seven O2- atoms. There are a spread of Ho–O bond distances ranging from 2.24–2.45 Å. There are eight inequivalent Te4+ sites. In the first Te4+ site, Te4+ is bonded in a 3-coordinate geometry to three O2- atoms. There are a spread of Te–O bond distances ranging from 1.90–1.97 Å. In the second Te4+ site, Te4+ is bonded in a distorted T-shaped geometry to three O2- atoms. There are a spread of Te–O bond distances ranging from 1.88–1.95 Å. In the third Te4+ site, Te4+ is bonded in a 4-coordinate geometry to four O2- atoms. There are a spread of Te–O bond distances ranging from 1.89–2.62 Å. In the fourth Te4+ site, Te4+ is bonded in a 5-coordinate geometry to four O2- and one Cl1- atom. There are a spread of Te–O bond distances ranging from 1.92–2.37 Å. The Te–Cl bond length is 2.89 Å. In the fifth Te4+ site, Te4+ is bonded in a 3-coordinate geometry to three O2- atoms. All Te–O bond lengths are 1.91 Å. In the sixth Te4+ site, Te4+ is bonded in a 3-coordinate geometry to three O2- atoms. There is two shorter (1.91 Å) and one longer (1.93 Å) Te–O bond length. In the seventh Te4+ site, Te4+ is bonded in a 3-coordinate geometry to three O2- atoms. There are a spread of Te–O bond distances ranging from 1.90–1.93 Å. In the eighth Te4+ site, Te4+ is bonded in a see-saw-like geometry to four O2- atoms. There are a spread of Te–O bond distances ranging from 1.89–2.18 Å. There are twenty-four inequivalent O2- sites. In the first O2- site, O2- is bonded in a distorted trigonal planar geometry to one Ho3+ and two Te4+ atoms. In the second O2- site, O2- is bonded in a bent 150 degrees geometry to one Ho3+ and one Te4+ atom. In the third O2- site, O2- is bonded in a distorted trigonal non-coplanar geometry to two Ho3+ and one Te4+ atom. In the fourth O2- site, O2- is bonded in a distorted trigonal non-coplanar geometry to two Ho3+ and one Te4+ atom. In the fifth O2- site, O2- is bonded in a trigonal planar geometry to two Ho3+ and one Te4+ atom. In the sixth O2- site, O2- is bonded in a distorted trigonal non-coplanar geometry to two Ho3+ and one Te4+ atom. In the seventh O2- site, O2- is bonded in a trigonal planar geometry to two Ho3+ and one Te4+ atom. In the eighth O2- site, O2- is bonded in a 4-coordinate geometry to two Ho3+ and two Te4+ atoms. In the ninth O2- site, O2- is bonded in a 3-coordinate geometry to two Ho3+ and one Te4+ atom. In the tenth O2- site, O2- is bonded in a 2-coordinate geometry to two Ho3+ and one Te4+ atom. In the eleventh O2- site, O2- is bonded in a 1-coordinate geometry to two Ho3+ and one Te4+ atom. In the twelfth O2- site, O2- is bonded in a distorted water-like geometry to two Te4+ atoms. In the thirteenth O2- site, O2- is bonded in a 3-coordinate geometry to two equivalent Ho3+ and one Te4+ atom. In the fourteenth O2- site, O2- is bonded in a 3-coordinate geometry to two Ho3+ and one Te4+ atom. In the fifteenth O2- site, O2- is bonded in a bent 150 degrees geometry to one Ho3+ and one Te4+ atom. In the sixteenth O2- site, O2- is bonded in a distorted trigonal non-coplanar geometry to two Ho3+ and one Te4+ atom. In the seventeenth O2- site, O2- is bonded in a distorted bent 150 degrees geometry to one Ho3+ and one Te4+ atom. In the eighteenth O2- site, O2- is bonded in a distorted bent 150 degrees geometry to one Ho3+ and one Te4+ atom. In the nineteenth O2- site, O2- is bonded in a 3-coordinate geometry to two Ho3+ and one Te4+ atom. In the twentieth O2- site, O2- is bonded in a 3-coordinate geometry to two Ho3+ and one Te4+ atom. In the twenty-first O2- site, O2- is bonded in a 2-coordinate geometry to two equivalent Ho3+ and one Te4+ atom. In the twenty-second O2- site, O2- is bonded in a 3-coordinate geometry to two Ho3+ and one Te4+ atom. In the twenty-third O2- site, O2- is bonded in a 2-coordinate geometry to one Ho3+ and one Te4+ atom. In the twenty-fourth O2- site, O2- is bonded in a 3-coordinate geometry to two Ho3+ and one Te4+ atom. Cl1- is bonded in a linear geometry to two equivalent Te4+ atoms.

36 MATERIALS SCIENCE↗
DOE OSTI2023

Reaching a burning plasma and ignition using smaller capsules/ Hohlraums , higher radiation temperatures, and thicker ablator/ice on the national ignition facility

In indirect-drive implosions, the final core hot spot energy and pressure and, hence, neutron yield attainable in 1D increase with increasing laser peak power and, hence, radiation drive temperature at the fixed capsule and Hohlraum size. Here we present simple analytic scalings validated by 1D simulations that quantify the improvement in performance and use this to explain existing data and simulation trends. Extrapolating to the 500 TW National Ignition Facility peak power limit in a low gas-fill 5.4 mm diameter Hohlraum based on existing high adiabat implosion data at 400 TW, 1.3 MJ and 1 × 10 16 yield, we find that a 2–3 × 10 17 yield (0.5–0.7 MJ) is plausible using only 1.8 MJ of laser energy. Based on existing data varying deuterium–tritium (DT) fuel thickness and dopant areal density, further improvements should be possible by increasing DT fuel areal density, and hence confinement time and yield amplification.

70 PLASMA PHYSICS AND FUSION TECHNOLOGY↗