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At least 667 records · Page 37

Rotational Energy Transfer Cross Sections in N2-N2 Collisions

Rotational inelastic transitions of N2 have been studied in the coupled state (CS, also called centrifugal sudden) and infinite-order-sudden (IOS) approximations, using the N2-N2 rigid-rotor potential of van der Avoird et al. For benchmarking purposes, close coupling (CC) calculations have also been carried out over a limited energy range and for even j - even j collisions only. Both the CC and CS cross sections have been obtained with and without exchange symmetry, whereas exchange is neglected in the IOS calculations. The CS results track the CC cross sections rather well. At total energies between 113 to 219 cm(exp -1) the average deviation is 14%. The deviation decrease with increasing energy, indicating that the CS approximation can be used as a substitute at higher energies when the CC calculations become impractical. Comparison between the CS and IOS cross sections at the high energy end of the CS calculation, 500 - 680 cm(exp-1), shows significant differences between the two. In addition, the IOS results exhibits sensitivity to the amount of inelasticity and the results for large DELTA J transitions are subjected to bigger errors. At total energy 113 cm(exp -1) and above, the average deviation between state-to-state cross sections calculated with even and odd exchange symmetries is 1.5%.

Huo, Winifred M.↗

Influence of exercise training on the oxidative capacity of rat abdominal muscles

Our purpose was to determine if endurance exercise training would increase the oxidative capacity of the abdominal expiratory muscles of the rat. Accordingly, 9 male rats were subjected to an endurance training protocol (1 h/day, 6 days/week, 9 weeks) and 9 litter-mates served as controls. Citrate synthase (CS) activity was used as an index of oxidative capacity, and was determined in the following muscles: soleus, plantaris, costal diaphragm, crural diaphragm, and in all four abdominal muscles: rectus abdominis, transversus abdominis, external oblique, and internal oblique. Compared to their non-trained litter-mates, the trained rats had higher peak whole body oxygen consumption rates (+ 16%) and CS activities in plantaris (+34%) and soleus (+36%) muscles. Thus, the training program caused substantial systemic and locomotor muscle adaptations. The CS activity of costal diaphragm was 20% greater in the trained animals, but no difference was observed in crural diaphragm. The CS activity in the abdominal muscles was less than one-half of that in locomotor and diaphragm muscles, and there were no significant changes with training except in the rectus abdominis where a 26% increase was observed. The increase in rectus abdominis CS activity may reflect its role in postural support and/or locomotion, as none of the primary expiratory pumping muscles adapted to the training protocol. The relatively low levels of CS activity in the abdominal muscles suggests that they are not recruited frequently at rest, and the lack of an increase with training indicates that these muscles do not contribute significantly to the increased ventilatory activity accompanying exercise in the rat.

Non-NASA Center↗

UAS Modeling of the Communication Links Study Results

There were many links calculated for this and the other scenarios. The rain was analyzed for 99.9% availability with rain rated of none, 20 mm/hr and 90 mm/hr at a height of 5 km out to 25 NM. This was done for each scenario for LOS and for BLOS links for Scenario 5 and 6. Scenario 1 was a LOS-only scenario. Use of two 3 dB Antennas on both ends. The CS2 was unable to maintain a control RF Link during the flight. The largest access gap periods between object top and bottom UA antennae were caused by terrain (ridges and hills). The CS Antenna was changed to High Gain Directional Antenna, all three CS maintained lock on vehicle. There were RF dropouts between the top and bottom UA antennae caused by aircraft obstructions (fuselage, wings, wheel assembles, etc.). Note that for this study antenna locations were placed on top and bottom center of the UA body. Future study should include actual UA antenna locations on the aircraft providing manufactures are willing to provide information. The importance of CS location(s) was demonstrated for primary or backup CS. With a second backup CS placed in a suitable location the UA was able to maintain an overall RF link. The actual location of both backup CSs required the antenna location to be place 150 ft above ground in order to establish a RF link between the UA and CS.

Birr, Richard↗

Precision Oxygen Isotope Measurements of Two C-Rich Hydrated Interplanetary Dust Particles

Introduction: Chondritic-smooth IDPs (Interplanetary Dust Particles) are low porosity objects whose mineralogy is dominated by aqueous alteration products such as Mg-rich phyllosilicates (smectite and serpentine group) and Mg-Fe carbonate minerals. Their hydrated mineralogy combined with low atmospheric entry velocities have been used to infer an origin largely from asteroidal sources. Spectroscopic studies show that the types and abundance of organic matter in CS IDPs is similar to that in CP IDPs. Although CS IDPs show broad similarities to primitive carbonaceous chondrites, only a few particles have been directly linked to specific meteorite groups such as CM and CI chondrites based on the presence of diagnostic minerals. Many CS IDPs however, have carbon contents that greatly exceed that of known meteorite groups suggesting that they either may derive from comets or represent samples of more primitive parent bodies than do meteorites. It is now recognized that many large, dark primitive asteroids in the outer main belt, as well as some trans-Neptunian objects, show spectroscopic evidence for aqueous alteration products on their surfaces. Some CS IDPs exhibit large bulk D enrichments similar to those observed in the cometary CP IDPs. While hydrated minerals in comets have not been unambiguously identified to date, the presence of the smectite group mineral nontronite has been inferred from infrared spectra obtained from the ejecta from comet 9P/Tempel 1 during the Deep Impact mission. Recent observations of low temperature sulfide minerals in Stardust mission samples suggest that limited aqueous activity occurred on comet Wild-2. All of these observations, taken together, suggest that the high-carbon hydrated IDPs are abundant and important samples of primitive solar system objects not represented in meteorite collections. Oxygen isotopic compositions of chondrites reflect mixing between a 16O-rich reservoir and a 17O,18O-rich reservoir produced via mass-independent fractionation. The composition of the 16O-rich reservoir is well constrained but material representing the 17O,18O-rich end-member is rare. Self-shielding models predict that cometary water, presumed to represent this reservoir, should be enriched in 17O and 18O by greater than 200 per mille. The high-carbon hydrated IDPs may be among the best materials available to search for preserved "cometary" H2O signatures. In order to better understand the origin and evolution of these particles, we have obtained 10 hydrated interplanetary dust particles for coordinated mineralogical, isotopic and organic analyses. We have previously reported the results of mineralogical and O isotopic measurements of two hydrated IDPs; here we present results of O isotopic measurements of three additional IDPs. Samples and Methods: Three interplanetary dust particles (L2079C35, L2083D46 and L2083E46) were embedded in S and partially ultramicrotomed into approximately 70 nanometer sections for analysis via transmission electron microscopy (TEM). The remainders of the unsliced particles were removed from S and pressed into high purity Au foil that was cleaned with HF acid and annealed at 800 degrees Centigrade. The pressed IDPs were analyzed via electron microprobe analysis (EPMA) for quantitative bulk chemical analysis. After EPMA analysis, the IDPs were subjected to precision O isotope analysis with the UCLA Cameca IMS-1270 ion probe. A 20 kiloelectronvolt, 0.5 nanoangstrom Cs+ primary beam of approximately 15 micrometers diameter was used for each measurement. Small particles of San Carlos olivine and Burma spinel were pressed into the Au foil for use as standards to correct for instrumental mass fractionation. The detection system was configured for multicollection, with 16O measured on a Faraday cup, and 17O and 18O measured on electron multipliers (EMs). Individual analyses consisted of 15 cycles of 10 seconds per cycle. Additionally, two microtome thin sections were measured for H isotopic compositions with the JSC NanoSIMS 50L ion probe. An 8 picoangstrom, 16 kiloelectronvolt Cs plus primary beam was used. Measurements consisted of H, C, 12C, 16O, and 18O collected with EMs in multicollection. Terrestrial biotite and kerogen were used for isotopic standards. A significant challenge in O isotope measurement of hydrated minerals is the interference from 16OH at mass 17O. We ensured that the 17O and 16OH peaks were fully resolved by using a mass resolution of greater than 7000 and by careful analyses of San Carlos olivine, Burma spinel and chlorite hydrated mineral standards. The hydride was further suppressed with a cold finger attached to an LN2 dewar to trap volatiles in the sample chamber. All sputtered ions were counted (i.e. presputtering was not used); after applying background, yield and deadtime corrections, we performed a change-point analysis on our data via R in order to determine when the sample reached sputtering equilibrium; data points collected prior to the change point were excluded. Change-point analysis was also used to determine whether the IDP had completely sputtered. Results: Mineralogy. IDPs C35 and E46 exhibited hydrated mineralogies, Fe-Ni sulfide grains, nanoglobules and occasional enstatite grains distributed throughout a fine-grained Mg-Fe saponite matrix. C35 also contained breunnerite (Mg,Fe)CO3; solar flare tracks were observed in enstatite, indicating minimal atmospheric entry heating. The mineralogy of D46 is dominated by a large FeS grain with a minor component of adhering silicate material. D46 was strongly heated during atmorpheric entry as evidenced by a well-developed magnetite rim. EPMA analyses show that both C35 and E46 have high carbon contents of 20 weight percentage (approximately 6X CI). D46 contains approximately 6 wt.weight percentage C. A significant amount of the carbon is present as carbon nanoglobules. Results: Hydrogen isotopes: Although the bulk delta D values of both sections of L2079C35 were within error of SMOW (minus 33 plus or minus 19 per mille, 1 plus or minus 14 per mille 1 sigma), several delta D-rich hotspots were also identified, reaching 2000 per mille. As shown in Fig. 1, these hotspots are clearly associated with discrete carbonaceous inclusions that are akin to nanoglobules found in many meteorites and other IDPs. Oxygen Isotopes. Results of the oxygen isotope measurements are shown in Figure 1. The oxygen isotope composition for L2079C35 was delta 18O equals plus11.6 plus or minus 1.9per mille, delta 17O equals plus 7.9 plus or minus 1.9per mille (2 standard errors). The oxygen isotope composition for L2083D46 was delta 18O equals minus 8.1 plus or minus 1.9 per mille, delta 17O equals minus 6.4 plus or minus 3.1 per mille (2 standard errors). The oxygen isotope composition for L2083E46 was delta 18O equals plus 12.0 plus or minus 1.9 per mille, delta 17O equals plus 9.2 plus or minus 2.0 per mille (2 standard errors). Discussion: Despite mineralogical similarities to highly aqueously altered carbonaceous chondrites, the hydrated IDPs we analyzed have oxygen isotopic compositions that are distinct from matrix materials in the CI, CM, and CR chondrites. The IDPs plot along the Young-Russell line, with delta 17O values for C35 and E46 suggestive of interaction with a 16O-poor reservoir. However, we have thus far not observed evidence of extreme 16O-poor reservoirs expected from self-shielding models and observed in Acfer 094 simplectite. The high carbon contents of the IDPs also set them apart from known meteoritic samples. The lack of atmospheric entry heating effects are consistent with low encounter velocities and suggest either an asteroidal source, or a low inclination, low eccentricity cometary origin. Conclusions: The unusual oxygen isotopic compositions, high carbon contents, and the abundance of Drich nanoglobules, together, suggest that the high-carbon, hydrated IDPs are derived from a primitive source that is not yet represented in meteorite collections.

Snead, C. J.↗

Evaluation of Observed and Modelled Aerosol Lifetimes Using Radioactive Tracers of Opportunity and an Ensemble of 19 Global Models

Aerosols have important impacts on air quality and climate, but the processes affecting their removal from the atmosphere are not fully understood and are poorly constrained by observations. This makes modelled aerosol lifetimes uncertain. In this study, we make use of an observational constraint on aerosol lifetimes provided by radionuclide measurements and investigate the causes of differences within a set of global models. During the Fukushima Dai-Ichi nuclear power plant accident of March 2011, the radioactive isotopes cesium-137 (Cs-137) and xenon-133 (Xe-133) were released in large quantities. Cesium attached to particles in the ambient air, approximately according to their available aerosol surface area. Cs-137 size distribution measurements taken close to the power plant suggested that accumulation mode (AM) sulfate aerosols were the main carriers of cesium. Hence, Cs-137 can be used as a proxy tracer for the AM sulfate aerosol's fate in the atmosphere. In contrast, the noble gas Xe-133 behaves almost like a passive transport tracer. Global surface measurements of the two radioactive isotopes taken over several months after the release allow the derivation of a lifetime of the carrier aerosol. We compare this to the lifetimes simulated by 19 different atmospheric transport models initialized with identical emissions of Cs-137that were assigned to an aerosol tracer with each model's default properties of AM sulfate, and Xe-133 emissions that were assigned to a passive tracer. We investigate to what extent the modelled sulfate tracer can reproduce the measurements, especially with respect to the observed loss of aerosol mass with time. Modelled Cs-137and Xe-133 concentrations sampled at the same location and times as station measurements allow a direct comparison between measured and modelled aerosol lifetime. The e-folding lifetime e, calculated from station measurement data taken between 2 and 9 weeks after the start of the emissions, is 14.3 days (95% confidence interval 13.1-15.7 days). The equivalent modelled e lifetimes have a large spread, varying between 4.8 and 26.7 days with a model median of 9.42.3 days, indicating too fast a removal in most models. Because sufficient measurement data were only available from about 2 weeks after the release, the estimated lifetimes apply to aerosols that have undergone long-range transport, i.e. not for freshly emitted aerosol. However, modelled instantaneous lifetimes show that the initial removal in the first 2 weeks was quicker (lifetimes between 1 and 5 days) due to the emissions occurring at low altitudes and co-location of the fresh plume with strong precipitation. Deviations between measured and modelled aerosol lifetimes are largest for the northernmost stations and at later time periods, suggesting that models do not transport enough of the aerosol towards the Arctic. The models underestimate passive tracer (Xe-133) concentrations in the Arctic as well but to a smaller extent than for the aerosol (Cs-137) tracer. This indicates that in addition to too fast an aerosol removal in the models, errors in simulated atmospheric transport towards the Arctic in most models also contribute to the underestimation of the Arctic aerosol concentrations.

Radioactive isotopes↗

Wash Penalty Factors: Insight into the Effects of Water Wash Down of Building Materials for Radionuclide/Nuclear (Rn) Decontamination - 20153

The release of radiological material to the urban environment can have a devastating socio-economic impact. In an urban release scenario, areas around the dispersal epicenter and any areas contaminated via atmospheric deposition may require extensive decontamination. Most recently, our group reported the decontamination efficacy of pressurized water washing of common porous building materials, and compared the penetration depth of the contaminations before and after exposure to pressurized tap water. Here, we continue evaluation of the decontamination efficacy of wash solutions based on potassium (K{sup +}) salt for cesium (Cs), strontium (Sr), and europium (Eu) contaminations on common building surfaces. The surfaces included: the cement used in concrete, the aggregate used in concrete, intact concrete, roadway asphalt, asphalt shingles, and latex paint. We deposited solutions of {sup 137}Cs, {sup 85}Sr, and {sup 152}Eu onto numerous common building materials and exposed these materials to a static bath or low-pressure flow of tap water, 0.1 M potassium chloride (KCl), and 0.5 M KCl. The decontamination efficacy and the depth profile for residual contamination were measured to determine the conditions under which applying a wash solution has benefit compared to physically removing the surface material. To aid in these analyses, we introduced a 'wash penalty factor' to quantify the degree to which contamination migrated into the bulk material by the action of the wash method. On asphalt, 70-80% of the radionuclides were found to be within 0.02 mm of the surface. Cs{sup +} bonded to negative charge sites on the surface of the mineral aggregate (used in concrete) so decontamination was improved by ion exchange with K{sup +}. Sr{sup 2+} is soluble and removed by water, while not bonding to aggregate or demonstrating solubility in the liquid asphalt. Eu{sup 3+} is precipitated and not removed in gentle wash but displays mobility within the pore space that suggests its presence as a colloid. Concrete is more porous than asphalt, and 80% of the radionuclides were within 0.2 mm of the surface for {sup 137}Cs and {sup 152}Eu and 50- 80% for {sup 85}Sr. On concrete, Cs{sup +} bonds similarly to asphalt. Sr{sup 2+} bonds to the cement or precipitates from the alkaline pore water. Eu{sup 3+} sorbs to the cement and then precipitates. In brick, the results for Cs{sup +} and Sr{sup 2+} suggested that diffusion of ions from deeper in the coupon was important. Eu{sup 3+} is removed poorly due to precipitation. We will explain and report example wash penalty factors that vary from 0 to > 1 for the various methods and the implications for deciding when to implement wash down methods. (authors)

12 MANAGEMENT OF RADIOACTIVE AND NON-RADIOACTIVE W↗

GeoMelt{sup R} In-Container Vitrification (ICV){sup TM} for Fukushima Daiichi Water Treatment Secondary Wastes - 20212

The Japanese government is supporting development work implemented jointly by Veolia subsidiaries Kurion Japan, K.K., Veolia Nuclear Solutions (VNS), Inc., and Veolia Nuclear Solutions Federal Services, LLC for treating radioactive waste generated from Fukushima Daiichi Nuclear Power Station (NPS) water treatment using the GeoMelt{sup TM} In-Container Vitrification (ICV){sup TM} technology. The initial work consisted of glass formulation and engineering-scale testing which was completed in 2018, in the frame of an IRID (International Research Institute for Nuclear Decommissioning) program as part of a project subsidized by Japan's Ministry of Economy, Trade and Industry (METI). The Fukushima Daiichi NPS Mid- and Long-Term Road-map requires investigation of methods to stabilize solid wastes (and to immobilize radioisotopes in the wastes) generated as a result of emergency response and decommissioning activities. Cooling water treatment has resulted in a significant amount of solid and slurry secondary wastes (mostly adsorbents and ion-exchange materials) which will require processing at some point. GeoMelt{sup R} ICV{sup TM} is a joule-heated melter technology which uses a refractory-lined single-use container combining the melter and disposal container. There is no pouring required nor concerns with refractory corrosion which allows the process to accommodate a wide range of waste chemistries and high waste loadings. The testing described here consisted of three engineering-scale melts, each processing between 212 kg and 240 kg of waste simulants, glass formers, and non-radioactive cesium (Cs) and strontium (Sr) tracers. Continuous isokinetic stack sampling of off-gas emissions was performed for each test in order to calculate Cs and Sr retention in the glass wasteform. Single-pass retention of Cs in the final glass wasteform ranged from 91.46 to 99.30%, and single-pass retention of Sr ranged from 99.76 to 100%. Planned particulate recycle will increase these retention levels. Melt 1 processed a mixture of KUR-EH (a zeolite-based ion-exchange material), simulated Advanced Liquid Processing System (ALPS) Carbonate and Iron Slurries, and glass additives. Melt 2 processed a mixture of KUR-EH, KUR-TSG (a titanate-based adsorbent), and glass additives. Melt 3 processed a mixture of KUR-EH, simulated barium sulfate/iron ferrocyanide sludge (AREVA sludge), and glass additives. Waste loadings for these melts ranged from 70 weight percent (wt%) to 82 wt%. Vitrification produces a waste form much denser than the stored water treatment secondary waste wastes, resulting in significant volume reduction. Volume reductions for the three tests ranged from 74 to 79 vol%. Vitrification produces a chemically durable wasteform. Pacific Northwest National Laboratory (PNNL) tested three glass samples from each engineering-scale melt) by the Materials Characterization Center 1 (MCC-1) test, an international standard leach test of the chemical durability of nuclear waste glasses. PNNL also obtained one U.S. reference glass (EA Glass) and two Japan reference glasses P0798) and tested these under the same MCC-1 conditions (90 deg. C, 10 m-1, DIW, and 7, 14, 28-day) as the GeoMelt{sup R} ICV{sup TM} glasses. The GeoMelt{sup R} ICV{sup TM} glasses exhibited lower total normalized releases and 14- to 28-day normalized release rates than the three reference glasses. These results suggest that the GeoMelt{sup R} ICV{sup TM} glasses have durabilities on par with high-level waste glasses under standard test conditions. Post-melt process sampling and analysis indicated no Cs migration into the melter refractory materials and very little deposition of Cs or Sr onto the melter hood or off-gas piping internals. The results of the testing indicated good Cs retention in the glass, high volume reduction and waste loadings, and excellent chemical durability. These factors are important to minimize treatment costs and to protect workers and the environment. (authors)

12 MANAGEMENT OF RADIOACTIVE AND NON-RADIOACTIVE W↗

Modeling Cost of Offshore Carbon Storage in Saline Reservoirs

Poster presentation to the AAPG-SEG-SPE CCUS 2024 Conference. Offshore saline reservoirs provide a significant and accessible resource for geologic carbon storage (CS). The offshore environment requires distinct approaches to site selection, operations, monitoring, and risk that affect the technoeconomic assessment of offshore CS projects. The National Energy Technology Laboratory (NETL) has developed a CS cost model for offshore saline reservoirs known as CO2_S_COM_Offshore. Based on NETL’s widely used CO2_S_COM cost model for onshore saline CS, CO2_S_COM_Offshore enables technoeconomic analysis of CS in offshore areas. This model comprehensively incorporates multiple facets of offshore CS projects, from regional evaluation and site selection to permitting, transport, operations, monitoring, site closure, and decommissioning. Developed to model cost for offshore United States (US) Exclusive Economic Zones, aspects of this model can be adapted to international projects. Presented at the SPE/AAPG/SEG Carbon Capture Utilization and Storage Conference in Houston, TX, March 11-13, 2024.

Mark-Moser, Mackenzie K.↗

Materials Data on CsI3 by Materials Project

CsI3 crystallizes in the orthorhombic Pnma space group. The structure is three-dimensional. Cs is bonded in a 10-coordinate geometry to ten I atoms. There are a spread of Cs–I bond distances ranging from 3.95–4.55 Å. There are three inequivalent I sites. In the first I site, I is bonded in a distorted rectangular see-saw-like geometry to two equivalent Cs and two I atoms. There are one shorter (2.90 Å) and one longer (3.02 Å) I–I bond lengths. In the second I site, I is bonded in a 5-coordinate geometry to four equivalent Cs and one I atom. In the third I site, I is bonded in a 3-coordinate geometry to four equivalent Cs and one I atom.

36 MATERIALS SCIENCE↗

Materials Data on CsBrF by Materials Project

CsBrF crystallizes in the tetragonal I4/mmm space group. The structure is three-dimensional. Cs is bonded to four equivalent Br and five equivalent F atoms to form distorted CsBr4F5 square pyramids that share corners with four equivalent FCs5Br octahedra, edges with eight equivalent CsBr4F5 square pyramids, and faces with four equivalent CsBr4F5 square pyramids. The corner-sharing octahedral tilt angles are 125°. All Cs–Br bond lengths are 3.81 Å. There are one shorter (2.97 Å) and four longer (3.12 Å) Cs–F bond lengths. Br is bonded in a 1-coordinate geometry to four equivalent Cs, one Br, and one F atom. The Br–Br bond length is 2.41 Å. The Br–F bond length is 2.49 Å. F is bonded to five equivalent Cs and one Br atom to form FCs5Br octahedra that share corners with four equivalent FCs5Br octahedra, corners with four equivalent CsBr4F5 square pyramids, and edges with eight equivalent FCs5Br octahedra. The corner-sharing octahedral tilt angles are 10°.

36 MATERIALS SCIENCE↗

Materials Data on CsIO4 by Materials Project

CsIO4 crystallizes in the orthorhombic Pnma space group. The structure is three-dimensional. Cs is bonded in a 8-coordinate geometry to eight O atoms. There are a spread of Cs–O bond distances ranging from 3.16–3.40 Å. There are three inequivalent O sites. In the first O site, O is bonded in a distorted single-bond geometry to two equivalent Cs and one I atom. The O–I bond length is 1.80 Å. In the second O site, O is bonded in a distorted single-bond geometry to three equivalent Cs and one I atom. The O–I bond length is 1.80 Å. In the third O site, O is bonded in a distorted linear geometry to one Cs and one I atom. The O–I bond length is 1.80 Å. I is bonded in a tetrahedral geometry to four O atoms.

36 MATERIALS SCIENCE↗

Materials Data on CsH18RuN6(ClO2)4 by Materials Project

Cs(O2Cl)4Ru(NH3)6 crystallizes in the trigonal R-3 space group. The structure is two-dimensional and consists of three Ru(NH3)6 clusters and three Cs(O2Cl)4 sheets oriented in the (0, 0, 1) direction. In each Ru(NH3)6 cluster, Ru5+ is bonded in an octahedral geometry to six equivalent N+0.67- atoms. All Ru–N bond lengths are 2.13 Å. N+0.67- is bonded in a distorted trigonal non-coplanar geometry to one Ru5+ and three H1+ atoms. All N–H bond lengths are 1.03 Å. There are three inequivalent H1+ sites. In the first H1+ site, H1+ is bonded in a single-bond geometry to one N+0.67- atom. In the second H1+ site, H1+ is bonded in a single-bond geometry to one N+0.67- atom. In the third H1+ site, H1+ is bonded in a single-bond geometry to one N+0.67- atom. In each Cs(O2Cl)4 sheet, Cs1+ is bonded in a distorted body-centered cubic geometry to six equivalent O2- and two equivalent Cl1- atoms. All Cs–O bond lengths are 3.16 Å. Both Cs–Cl bond lengths are 3.69 Å. There are two inequivalent O2- sites. In the first O2- site, O2- is bonded in a distorted single-bond geometry to one Cs1+ and one Cl1- atom. The O–Cl bond length is 1.46 Å. In the second O2- site, O2- is bonded in a single-bond geometry to one Cl1- atom. The O–Cl bond length is 1.47 Å. There are two inequivalent Cl1- sites. In the first Cl1- site, Cl1- is bonded in a tetrahedral geometry to four O2- atoms. In the second Cl1- site, Cl1- is bonded in a distorted single-bond geometry to one Cs1+ atom.

36 MATERIALS SCIENCE↗

Materials Data on CsBr3 by Materials Project

CsBr3 crystallizes in the orthorhombic Pnma space group. The structure is three-dimensional. Cs is bonded in a 10-coordinate geometry to ten Br atoms. There are a spread of Cs–Br bond distances ranging from 3.69–4.29 Å. There are three inequivalent Br sites. In the first Br site, Br is bonded in a 5-coordinate geometry to four equivalent Cs and one Br atom. The Br–Br bond length is 2.66 Å. In the second Br site, Br is bonded to four equivalent Cs and one Br atom to form distorted BrCs4Br trigonal bipyramids that share corners with six equivalent BrCs2Br2 tetrahedra, corners with eight equivalent BrCs4Br trigonal bipyramids, an edgeedge with one BrCs2Br2 tetrahedra, and edges with two equivalent BrCs4Br trigonal bipyramids. The Br–Br bond length is 2.52 Å. In the third Br site, Br is bonded to two equivalent Cs and two Br atoms to form distorted BrCs2Br2 tetrahedra that share corners with two equivalent BrCs2Br2 tetrahedra, corners with six equivalent BrCs4Br trigonal bipyramids, and an edgeedge with one BrCs4Br trigonal bipyramid.

36 MATERIALS SCIENCE↗

Materials Data on CsXeF7 by Materials Project

XeCsF7 crystallizes in the cubic P2_13 space group. The structure is three-dimensional. Xe is bonded in a 7-coordinate geometry to seven F atoms. There are a spread of Xe–F bond distances ranging from 2.06–2.14 Å. Cs is bonded in a 9-coordinate geometry to fifteen F atoms. There are a spread of Cs–F bond distances ranging from 3.19–3.59 Å. There are three inequivalent F sites. In the first F site, F is bonded in a distorted single-bond geometry to one Xe and two equivalent Cs atoms. In the second F site, F is bonded in a distorted single-bond geometry to one Xe and two equivalent Cs atoms. In the third F site, F is bonded in a distorted single-bond geometry to one Xe and three equivalent Cs atoms.

36 MATERIALS SCIENCE↗

Materials Data on CsClO4 by Materials Project

CsClO4 crystallizes in the orthorhombic Pnma space group. The structure is three-dimensional. Cs is bonded in a 12-coordinate geometry to twelve O atoms. There are a spread of Cs–O bond distances ranging from 3.24–3.69 Å. There are three inequivalent O sites. In the first O site, O is bonded in a distorted single-bond geometry to three equivalent Cs and one Cl atom. The O–Cl bond length is 1.46 Å. In the second O site, O is bonded in a distorted single-bond geometry to three equivalent Cs and one Cl atom. The O–Cl bond length is 1.47 Å. In the third O site, O is bonded in a distorted single-bond geometry to three equivalent Cs and one Cl atom. The O–Cl bond length is 1.46 Å. Cl is bonded in a tetrahedral geometry to four O atoms.

36 MATERIALS SCIENCE↗

Materials Data on CsGa7 by Materials Project

CsGa7 crystallizes in the trigonal R-3m space group. The structure is three-dimensional. Cs is bonded in a 12-coordinate geometry to fifteen Ga atoms. There are a spread of Cs–Ga bond distances ranging from 3.85–3.94 Å. There are three inequivalent Ga sites. In the first Ga site, Ga is bonded in a 7-coordinate geometry to three equivalent Cs and four Ga atoms. There are one shorter (2.62 Å) and three longer (2.64 Å) Ga–Ga bond lengths. In the second Ga site, Ga is bonded in a 8-coordinate geometry to one Cs and seven Ga atoms. There are a spread of Ga–Ga bond distances ranging from 2.57–2.83 Å. In the third Ga site, Ga is bonded in a 9-coordinate geometry to three equivalent Cs and six Ga atoms. Both Ga–Ga bond lengths are 2.83 Å.

36 MATERIALS SCIENCE↗

Materials Data on Cs4Pr6C2I13 by Materials Project

Cs4Pr6C2I13 crystallizes in the tetragonal I4_1/amd space group. The structure is three-dimensional. Cs is bonded in a 7-coordinate geometry to seven I atoms. There are a spread of Cs–I bond distances ranging from 3.98–4.27 Å. There are two inequivalent Pr sites. In the first Pr site, Pr is bonded to one C and five I atoms to form distorted PrCI5 octahedra that share a cornercorner with one PrCI5 octahedra, corners with two equivalent PrC2I5 pentagonal bipyramids, and edges with four equivalent PrC2I5 pentagonal bipyramids. The corner-sharing octahedral tilt angles are 0°. The Pr–C bond length is 2.31 Å. There are a spread of Pr–I bond distances ranging from 3.18–3.42 Å. In the second Pr site, Pr is bonded to two equivalent C and five I atoms to form distorted PrC2I5 pentagonal bipyramids that share a cornercorner with one PrCI5 octahedra, edges with two equivalent PrCI5 octahedra, edges with two equivalent PrC2I5 pentagonal bipyramids, and faces with two equivalent PrC2I5 pentagonal bipyramids. The corner-sharing octahedral tilt angles are 7°. There are one shorter (2.63 Å) and one longer (2.64 Å) Pr–C bond lengths. There are a spread of Pr–I bond distances ranging from 3.20–3.46 Å. C is bonded in a 6-coordinate geometry to five Pr and one C atom. The C–C bond length is 1.39 Å. There are four inequivalent I sites. In the first I site, I is bonded to two equivalent Cs and three Pr atoms to form distorted ICs2Pr3 trigonal bipyramids that share corners with three equivalent ICs2Pr3 trigonal bipyramids, an edgeedge with one ICs2Pr3 trigonal bipyramid, and a faceface with one ICs4Pr2 octahedra. In the second I site, I is bonded to four equivalent Cs and two equivalent Pr atoms to form face-sharing ICs4Pr2 octahedra. In the third I site, I is bonded in a 5-coordinate geometry to two equivalent Pr atoms. In the fourth I site, I is bonded in a 6-coordinate geometry to four equivalent Cs and two Pr atoms.

36 MATERIALS SCIENCE↗

Materials Data on Cs5Si3AgO9 by Materials Project

Cs5AgSi3O9 crystallizes in the monoclinic P2_1/m space group. The structure is three-dimensional. there are five inequivalent Cs1+ sites. In the first Cs1+ site, Cs1+ is bonded in a 8-coordinate geometry to eight O2- atoms. There are a spread of Cs–O bond distances ranging from 3.03–3.57 Å. In the second Cs1+ site, Cs1+ is bonded in a 9-coordinate geometry to nine O2- atoms. There are a spread of Cs–O bond distances ranging from 3.18–3.60 Å. In the third Cs1+ site, Cs1+ is bonded in a 2-coordinate geometry to two equivalent O2- atoms. Both Cs–O bond lengths are 2.86 Å. In the fourth Cs1+ site, Cs1+ is bonded in a 2-coordinate geometry to two equivalent O2- atoms. Both Cs–O bond lengths are 2.80 Å. In the fifth Cs1+ site, Cs1+ is bonded in a 9-coordinate geometry to nine O2- atoms. There are a spread of Cs–O bond distances ranging from 3.12–3.48 Å. Ag1+ is bonded in a linear geometry to two equivalent O2- atoms. Both Ag–O bond lengths are 2.07 Å. There are three 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 1.64–1.67 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 1.62–1.72 Å. In the third 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 1.62–1.71 Å. There are six inequivalent O2- sites. In the first O2- site, O2- is bonded in a distorted single-bond geometry to five Cs1+ and one Si4+ atom. In the second O2- site, O2- is bonded in a 2-coordinate geometry to two Cs1+, one Ag1+, and one Si4+ atom. In the third O2- site, O2- is bonded in a distorted single-bond geometry to four Cs1+ and one Si4+ atom. In the fourth O2- site, O2- is bonded in a distorted bent 120 degrees geometry to two equivalent Cs1+ and two Si4+ atoms. In the fifth O2- site, O2- is bonded in a distorted bent 120 degrees geometry to three equivalent Cs1+ and two Si4+ atoms. In the sixth O2- site, O2- is bonded in a distorted bent 150 degrees geometry to three equivalent Cs1+ and two Si4+ atoms.

36 MATERIALS SCIENCE↗