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At least 523 records · Page 29

Surface Termination of CsPbBr 3 Perovskite Quantum Dots Determined by Solid-State NMR Spectroscopy

Cesium lead halide perovskite quantum dots (QDs) have gained significant attention as next-generation optoelectronic materials; however, their properties are highly dependent on their surface chemistry. The surfaces of cuboidal CsPbBr 3 QDs have been intensively studied by both theoretical and experimental techniques, but fundamental questions still remain about the atomic termination of the QDs. The surface binding sites and modes of ligands at the surface remain unproven. Herein, we demonstrate that solid-state NMR spectroscopy allows the unambiguous assignment of organic surface ligands via 1 H, 13 C, and 31 P NMR. Surface-selective 133 Cs solid-state NMR spectra show the presence of an additional 133 Cs NMR signal with a unique chemical shift that is attributed to Cs atoms terminating the surface of the particle and which are likely coordinated by carboxylate ligands. Dipolar dephasing curves that report on the distance between the surface ammonium ligands and Cs and Pb were recorded using double resonance 1 H{ 133 Cs} and 1 H{ 207 Pb} RESPDOR experiments. Model QD surface slabs with different possible surface terminations were generated from the CsPbBr 3 crystal structure and theoretical RESPDOR dipolar dephasing curves considering all possible 1 H- 133 Cs/ 207 Pb spin pairs were then calculated. Comparison of the calculated and experimental RESPDOR curves indicates the particles are CsBr terminated (not PbBr 2 terminated) with alkylammonium ligands substituting into some surface Cs sites, consistent with the surface-selective 133 Cs NMR experiments. Lastly, these results highlight the utility of high-resolution solid-state NMR spectroscopy for studying ligand binding and the surface structure of nanomaterials.

37 INORGANIC, ORGANIC, PHYSICAL, AND ANALYTICAL CH↗

Search for hidden-charm tetraquark with strangeness in e + e - → $K$ + $D^{*}_{s}$ - $D$ *0 + c.c.*

We report a search for a heavier partner of the recently observed Z cs (3985) - state, denoted as $Z^{'-}_{cs}$, in the process e + e - → $K$ + $D^{*}_{s}$ - $D$ *0 + c.c., based on e + e - collision data collected at the center-of-mass energies of $\sqrt{s}$ = 4.661, 4.682 and 4.699 GeV with the BESIII detector. The $Z^{'-}_{cs}$ is of interest as it is expected to be a candidate for a hidden-charm and open-strange tetraquark. A partial-reconstruction technique is used to isolate K + recoil-mass spectra, which are probed for a potential contribution from $Z^{'-}_{cs}$ → $D^{*}_{s}$ - $D$ *0 + (c.c.). We find an excess of $Z^{'-}_{cs}$ → $D^{*}_{s}$ - $D$ *0 + (c.c.) candidates with a significance of 2.1σ, after considering systematic uncertainties, at a mass of 4123.5 ± 0.7 stat. ± 4.7 syst. ) MeV/c 2 . As the data set is limited in size, the upper limits are evaluated at the 90% confidence level on the product of the Born cross sections (σ BORN ) and the branching fraction ($\mathcal{B}$) of $Z^{'-}_{cs}$ → $D^{*}_{s}$ - $D$ *0 , under different assumptions of the $Z^{'-}_{cs}$ mass from 4.120 to 4.140 MeV and of the width from 10 to 50 MeV at the three center-of-mass energies. The upper limits of σ BORN ∙ $\mathcal{B}$ are found to be at the level of $\mathcal{O}$(1) pb at each energy. Larger data samples are needed to confirm the $Z^{'-}_{cs}$ state and clarify its nature in the coming years.

73 NUCLEAR PHYSICS AND RADIATION PHYSICS↗

Uncoordinated Spectrum Sharing in Millimeter Wave Networks Using Carrier Sensing

Here, we propose using Carrier Sensing (CS) for distributed interference management in millimeter-wave (mmWave) cellular networks where spectrum is shared by multiple operators that do not coordinate among themselves. In addition, even the base station sites can be shared by the operators. We describe important challenges in using traditional CS in this setting and propose enhanced CS protocols to address these challenges. Using stochastic geometry, we develop a general framework for downlink coverage probability analysis of our shared mmWave network in the presence of CS and derive the downlink coverage probability expressions for several CS protocols. Our work is the first to investigate and analyze (using stochastic geometry) CS for mmWave networks with spectrum and BS sites shared among non-coordinating operators. We evaluate the downlink coverage probability of our shared mmWave network using simulations as well as numerical examples based on our analysis. Our evaluations show that our proposed approach leads to an improvement in coverage probability, compared to the coverage probability with no CS, for higher values of signal-to-interference and noise ratio (SINR). Interestingly, our evaluations also reveal that for lower values of SINR, not using any CS is the best strategy in terms of the downlink coverage probability.

42 ENGINEERING↗

Modification and analysis of context-specific genome-scale metabolic models: methane-utilizing microbial chassis as a case study

ABSTRACT Context-specific genome-scale model (CS-GSM) reconstruction is becoming an efficient strategy for integrating and cross-comparing experimental multi-scale data to explore the relationship between cellular genotypes, facilitating fundamental or applied research discoveries. However, the application of CS modeling for non-conventional microbes is still challenging. Here, we present a graphical user interface that integrates COBRApy, EscherPy, and RIPTiDe, Python-based tools within the BioUML platform, and streamlines the reconstruction and interrogation of the CS genome-scale metabolic frameworks via Jupyter Notebook. The approach was tested using -omics data collected for Methylotuvimicrobium alcaliphilum 20Z R , a prominent microbial chassis for methane capturing and valorization. We optimized the previously reconstructed whole genome-scale metabolic network by adjusting the flux distribution using gene expression data. The outputs of the automatically reconstructed CS metabolic network were comparable to manually optimized i IA409 models for Ca-growth conditions. However, the CS model questions the reversibility of the phosphoketolase pathway and suggests higher flux via primary oxidation pathways. The model also highlighted unresolved carbon partitioning between assimilatory and catabolic pathways at the formaldehyde-formate node. Only a very few genes and only one enzyme with a predicted function in C1 metabolism, a homolog of the formaldehyde oxidation enzyme ( fae1-2 ), showed a significant change in expression in La-growth conditions. The CS-GSM predictions agreed with the experimental measurements under the assumption that the Fae1-2 is a part of the tetrahydrofolate-linked pathway. The cellular roles of the tungsten (W)-dependent formate dehydrogenase ( fdhAB ) and fae homologs ( fae1-2 and fae3 ) were investigated via mutagenesis. The phenotype of the f dhAB mutant followed the model prediction. Furthermore, a more significant reduction of the biomass yield was observed during growth in La-supplemented media, confirming a higher flux through formate. M. alcaliphilum 20Z R mutants lacking fae1-2 did not display any significant defects in methane or methanol-dependent growth. However, contrary to fae1, the fae1-2 homolog failed to restore the formaldehyde-activating enzyme function in complementation tests. Overall, the presented data suggest that the developed computational workflow supports the reconstruction and validation of CS-GSM networks of non-model microbes. IMPORTANCE The interrogation of various types of data is a routine strategy to explore the relationship between genotype and phenotype. An efficient approach for integrating and cross-comparing experimental multi-scale data in the context of whole-genome-based metabolic network reconstruction becomes a powerful tool that facilitates fundamental and applied research discoveries. The present study describes the reconstruction of a context-specific (CS) model for the methane-utilizing bacterium, Methylotuvimicrobium alcaliphilum 20Z R . M. alcaliphilum 20Z R is becoming an attractive microbial platform for the production of biofuels, chemicals, pharmaceuticals, and bio-sorbents for capturing atmospheric methane. We demonstrate that this pipeline can help reconstruct metabolic models that are similar to manually curated networks. Furthermore, the model is able to highlight previously overlooked pathways, thus advancing fundamental knowledge of non-model microbial systems or promoting their development toward biotechnological or environmental implementations.

Kulyashov, M. A.↗

Small to Full Height Scale Comparisons of Cesium Ion Exchange Performance with Crystalline Silicotitanate

The U.S. Department of Energy’s (DOE) Hanford Site houses 56 million gallons of high-level radioactive waste generated from plutonium production from 1944 to 1988. The supernatant waste, currently stored in underground tanks, is intended to be vitrified following filtration and 137 Cs removal at the Hanford Waste Treatment and Immobilization Plant (WTP) Low-Activity Waste (LAW) Vitrification Facility. The WTP Pretreatment Facility will not be operational for several years. The Tank Side Cesium Removal (TSCR) system is a technology demonstration that will remove cesium from tank waste supernate to support directly feeding LAW to the vitrification facility. The 137 Cs removal is important to meet the WTP LAW contract specification and ultimately for creating a contact-handled waste form. The waste acceptance criteria (WAC) limit for the WTP LAW Facility is <3.18E-5 Ci 137 Cs per mole Na. The TSCR system is skid mounted and employs two key technologies: dead end filtration for solids removal and ion exchange (IX) for cesium removal. Filtration is necessary to protect the functionality of the IX columns. The IX process utilizes sodium form crystalline silicotitanate (CST) IX media produced by UOP Honeywell, LLC (Des Plaines, IL) under the product name IONSIV R9140-B, 18 x 50 mesh, in a lead-lag-polish column configuration. Each column contains a CST bed height of 92 inches and a volume of approximately 157 gallons of CST IX media. The full-scale TSCR operation will run at a residence time of 1.9 bed volumes (BV)/h, which results in a superficial velocity of 7.3 cm/min and a flowrate of ~5 gal/min. Column testing at small (2.5% of the full bed height), medium (12% of the full bed height), and full-height scales has been previously conducted to evaluate process variables and scale up performance of Cs exchange onto the CST. Cesium load performances from various sieve cuts at the small scale indicated that a 30-mesh sieve cut be tested to determine if it better reflects the 12% and full-height column performances at the small scale. Two process flowrates were tested in the small-column configuration with <30-mesh CST and simulant solutions. These tests were compared to full-height column tests at the same residence times to assess CST particle size effect on column scaling. Table S.1 summarizes the observed column performance determined for the two flowrates juxtaposed to the previous work with 5.6 M Na simulant at higher scales (used as benchmarks). The WAC breakthroughs between the small and full-height tests at 1.3 BV/h differed by ~59 BVs. The WAC breakthroughs for small, medium, and full-height tests at 1.8 BV/h were consistent at 240 BVs. The 50% Cs breakthroughs were nominally equivalent for all column tests. The common transition zones and onsets of Cs breakthrough at the 1.8 BV/h tests indicated that the Cs mass transfers were equivalent and thus the <30-mesh CST Cs load performance at the small scale successfully modeled that of the full-height system. It is recommended that the <30-mesh CST be used in subsequent 10-mL CST bed tests.

12 MANAGEMENT OF RADIOACTIVE AND NON-RADIOACTIVE W↗

Ion Exchange Processing of AP-105 Hanford Tank Waste through Crystalline Silicotitanate in a Staged 2- then 3-Column System (Rev.1)

The Tank Side Cesium Removal (TSCR) system, under development by Washington River Protection Solutions LLC (WRPS), will send initial low-activity Hanford waste tank supernate feeds to the Hanford Waste Treatment and Immobilization Plant (WTP) Low-Activity Waste (LAW) Facility. In addition to entrained solids removal from the supernate, the primary goal of TSCR is to remove cesium-137 ( 137 Cs) by ion exchange, allowing contact handling of the liquid effluent product at the WTP. Crystalline silicotitanate (CST) ion exchange media, manufactured by Honeywell UOP, LLC (product IONSIVTM R9140-B), was selected as the ion exchange media at TSCR. CST is a non-elutable inorganic material that has demonstrated robust chemical, physical, and radiation tolerance while maintaining functionality. However, exchange kinetics of Cs onto CST is slow, resulting in low utilization of the CST Cs load capacity before unacceptable Cs breakthrough. Two process flow designs have been tested, as follows. 1. Lead-lag column processing: The lead column was removed after the lag column effluent reached the waste acceptance criteria (WAC) limit, the lag column was moved into the lead position, and a new lag column was installed. This format used ~52% Cs load capacity on the lead column. 2. Lead-lag-polish column processing: The processing was stopped when the polish column effluent reached the WAC limit. This format resulted in 81% Cs load capacity on the lead column. Testing with diluted feed from Hanford tank AP-105 (AP-105DF) incorporated a nuanced change to the lead-lag-polish column system where the polish column was inserted when the lag column effluent reached WAC limit. A 10.9-L volume of AP-105DF (diluted to 5.6 M Na) was processed through the Direct Feed Test Platform system, established at Pacific Northwest National Laboratory to support small-scale waste qualification efforts. The columns consisted of 10-mL CST beds (CST Lot 2002009604, sieved to screen out >30-mesh particles) placed in 1.5-cm-inner-diameter columns. Feed was processed at 1.83 bed volumes (BV) per hour; the flowrate, in terms of contact time with the CST bed, matched the expected flowrate at TSCR. The <30-mesh CST sieve cut was expected to provide appropriate performance scaling to a full-height column. The installation of the polish column later in processing (after processing 523 BVs) did not appear to fundamentally change the utilization of the lead column for Cs exchange nor did it extend the total feed processing volume when compared to the previous test with AP-107 feed. Table ES.1 and Figure ES.1 summarize the measured AP-105DF Cs load performance.

12 MANAGEMENT OF RADIOACTIVE AND NON-RADIOACTIVE W↗

Community Solar and Community Solar+Storage: A Roadmap of Barriers and Solutions for Commercial Systems in NYC

Sustainable CUNY worked with decision makers and subject matter experts (SME's) to identify the barriers to and solutions for advancing commercial Community Solar (CS) and CS+Storage (CS+S) in urban areas. This roadmap captures the key challenges and solutions identified by New York City (NYC) stakeholders, including the Real Estate Board of New York (REBNY), through a collaborative process. Solar, as well as storage, are among the fastest growing energy segments in the United States, with CS, also known as Community Distributed Generation (CDG), gaining popularity with those who may not own or have access to a viable roof. Urban areas like NYC, which have a large population of renters, are particularly well suited for CS projects where credits from the power produced by a large remote installation are offered on a subscription basis to residents or businesses in the community. However, CS and CS+S projects have stalled at the doorstep of many cities. Host site owners, particularly those with large rooftops, have been slow to commit to installing CS due to competing rooftop usage and programs, limited knowledge about incentives, lack of economic data, and a complicated implementation process.

14 SOLAR ENERGY↗

Coherent structures - Reality and myth

Large-scale coherent structures (CS) in turbulent shear flows are characterized, reviewing recent theoretical and experimental investigations. The use of computers as a research tool and the flow-visualization experimental technique are introduced, CS are defined, the history of their discovery is traced, and their main characteristics are listed. Topics discussed and illustrated include the initial condition of the free shear layer, triple and double decomposition, topological features of CS, detection and eduction of CS, phase alignment via cross correlation, induced versus natural structures, the bursting phenomenon, turbulent spot, streaks, bursting frequency, the axisymmetric mixing layer, vortex pairing in an axisymmetric jet, CS and jet noise, broadband noise amplification via pure-tone excitation, CS interaction in a plane-jet near field, the Taylor hypothesis applied to CS, negative production, and the validity of the Reynolds-number similarity hypothesis. It is found that the coherent Reynolds stress, vorticity, and production are not much greater than the time-averaged values for fully developed flows with significant incoherent turbulence, suggesting that the importance of CS may have been exaggerated in some recent studies.

Hussain, A. K. M. F.↗

Using Combustion Synthesis to Reinforce Berms and Other Regolith Structures

The Moonraker Excavator and other tools under development for use on the Moon, Mars, and asteroids will be employed to construct a number of civil engineering projects and to mine the soil. Mounds of loose soil will be subject to the local transport mechanisms plus artificial mechanisms such as blast effects from landers and erosion from surface vehicles. Some of these structures will require some permanence, with a minimum of maintenance and upkeep. Combustion Synthesis (CS) is a family of processes and techniques whereby chemistry is used to transform materials, often creating flame in a hard vacuum. CS can be used to stabilize civil engineering works such as berms, habitat shielding, ramps, pads, roadways, and the like. The method is to unroll thin sheets of CS fabric between layers of regolith and then fire the fabric, creating a continuous sheet of crusty material to be interposed among layers of loose regolith. The combination of low-energy processes, ISRU (in situ resource utilization) excavator, and CS fabrics, seems compelling as a general method for establishing structures of some permanence and utility, especially in the role of robotic missions as precursors to manned exploration and settlement. In robotic precursory missions, excavator/ mobility ensembles mine the Lunar surface, erect constructions of soil, and dispense sheets of CS fabrics that are covered with layers of soil, fired, and then again covered with layers of soil, iterating until the desired dimensions and forms are achieved. At the base of each berm, for example, is a shallow trench lined with CS fabric, fired and filled, mounded, and then covered and fired, iteratively to provide a footing against lateral shear. A larger trench is host to a habitat module, backfilled, covered with fabric, covered with soil, and fired. Covering the applied CS fabric with layers of soil before firing allows the resulting matrix to incorporate soil both above and below the fabric ply into the fused layer, developing a very irregular surface which, like sandpaper, can provide an anchor for loose soil. CS fabrics employ a coarse fiberglass weave that persists as reinforcement for the fired material. The fiberglass softens at a temperature that exceeds the combustion temperature by factors of two to three, and withstands the installation process. This type of structure should be more resistant to rocket blast effects from Lunar landers.

Rodriquez, Gary↗

Long Term Assessment of Radiocesium in Deer, Fish, Soil, and Vegetation at the Savannah River Site

Throughout the Savannah River Site's (SRS) operational history, many radionuclides have been released into the environment. However, due to fallout from weapons testing, the amount released from SRS, its persistence in the environment, and the seclusion of the Site, radiocesium (Cs-137) is one of the most critical radionuclides in the SRS environment. The Effective half-life (Te) is the time it takes for a radionuclide in the environment to decrease by 50% of its initial amount. There are three means of radionuclide removal: Physical: Radioactive decay, sedimentation, and washout; Chemical: Changes in pH, oxidation state or adsorption; Biological: Changes in the food web or translocation. Effective half-life (T{sub e}) = log{sub e}2/λ{sub e} Where λ{sub e} is estimated from the slopes of loge-transformed Cs-137 activity concentrations regressed on year. The objective of this work was to calculate the effective half-life of Cs-137 in various biota at SRS and to perform an assessment of the changes in the effective half life over time. Compared to 2013 data, there is a slight increase in the effective half-lives for fish at most sampling locations. This effective half-life increase is an indication that the rate of Cs-137 loss is starting to plateau. The effective half-life of Cs-137 in SRS fish ranges from 4-11 years. The effective half-life of Cs-137 in soil at the Creek plantation is about 15 years. The effective half-life of Cs-137 in grassy vegetation at the Creek Plantation is about 14 years. The effective half-life of deer hunted on the SRS is about 15.5 years. After termination of all reactor activity by 1980, the Cs-137 activity began to drop drastically.

12 MANAGEMENT OF RADIOACTIVE AND NON-RADIOACTIVE W↗

High-efficiency perovskite photovoltaic modules achieved via cesium doping

Perovskite solar modules have been attracting increasing attention due to their market potential, yet publications concerned with theintrinsic scale-up potential of different perovskite compositions remain relatively scarce. On the other hand, while great success is being made towards improving the power conversion efficiency (PCE) of perovskite solar cells (PSCs) by cesium cation (Cs + ) doping of the perovskite, more attention is being paid to the perovskite phase stabilization effect of Cs + doping, and less to other properties that are critical to understand and futher improve the PSC's. In this work, moderately-Cs-doped MAPbI 3 was employed as a model perovskite material in order to exclude the phase stabilization effect. Our systematic study revealed the influence of Cs + in organic-inorganic hybrid perovskites on the crystal structure, crystallization process, trap state density, band structure and charge (i.e., ions or photo-carriers) transport. Markedly, it has been observed that Cs + doping can greatly increase the carrier diffusion length in the perovskite films, thus improving the potential to scale-up PSC's.The PCE of small area devices (0.09 cm 2 ) was increased to 21.72% from 19.73%, with decreased hysteresis behavior and increased operational stability (T85 = 1000 h) after Cs + doped, where T85 refers to the retention of 85% of the initial PCE. Moreover, a PCE of 21.08% was obtained for a Cs + -containing perovskite module with an active area > 30 cm 2 , which demonstrates a better "reproducibility" than the reference sample (MAPbI3-based perovskite modules, PCE = 18.26%).

14 SOLAR ENERGY↗

Materials Data on Cs2Ce10Os2I17 by Materials Project

Cs2Ce10Os2I17 crystallizes in the monoclinic C2/m space group. The structure is three-dimensional. Cs is bonded to twelve I atoms to form CsI12 cuboctahedra that share corners with fourteen CeOs2I4 octahedra, edges with two equivalent CsI12 cuboctahedra, a faceface with one CsI12 cuboctahedra, and faces with six CeOsI5 octahedra. The corner-sharing octahedra tilt angles range from 35–48°. There are a spread of Cs–I bond distances ranging from 4.15–4.48 Å. There are four inequivalent Ce sites. In the first Ce site, Ce is bonded to one Os and five I atoms to form distorted CeOsI5 octahedra that share corners with two equivalent CsI12 cuboctahedra, corners with five CeOs2I4 octahedra, edges with five CeOs2I4 octahedra, and faces with two equivalent CsI12 cuboctahedra. The corner-sharing octahedra tilt angles range from 5–10°. The Ce–Os bond length is 2.78 Å. There are a spread of Ce–I bond distances ranging from 3.22–3.41 Å. In the second Ce site, Ce is bonded to one Os and five I atoms to form distorted CeOsI5 octahedra that share corners with two equivalent CsI12 cuboctahedra, corners with four CeOs2I4 octahedra, edges with five CeOs2I4 octahedra, and faces with two equivalent CsI12 cuboctahedra. The corner-sharing octahedra tilt angles range from 0–10°. The Ce–Os bond length is 2.72 Å. There are a spread of Ce–I bond distances ranging from 3.20–3.40 Å. In the third Ce site, Ce is bonded to one Os and five I atoms to form distorted CeOsI5 octahedra that share corners with three equivalent CsI12 cuboctahedra, corners with two CeOsI5 octahedra, edges with six CeOs2I4 octahedra, and a faceface with one CsI12 cuboctahedra. The corner-sharing octahedra tilt angles range from 1–9°. The Ce–Os bond length is 2.79 Å. There are a spread of Ce–I bond distances ranging from 3.18–3.42 Å. In the fourth Ce site, Ce is bonded to two equivalent Os and four I atoms to form CeOs2I4 octahedra that share corners with four equivalent CsI12 cuboctahedra, corners with three CeOs2I4 octahedra, and edges with eight CeOs2I4 octahedra. The corner-sharing octahedra tilt angles range from 0–5°. There are one shorter (2.81 Å) and one longer (2.90 Å) Ce–Os bond lengths. There are a spread of Ce–I bond distances ranging from 3.29–3.46 Å. Os is bonded to six Ce atoms to form edge-sharing OsCe6 octahedra. There are six inequivalent I sites. In the first I site, I is bonded in a 5-coordinate geometry to two equivalent Cs and three Ce atoms. In the second I site, I is bonded in a 5-coordinate geometry to two equivalent Cs and three Ce atoms. In the third I site, I is bonded in a distorted square co-planar geometry to four Ce atoms. In the fourth I site, I is bonded in a distorted rectangular see-saw-like geometry to one Cs and three Ce atoms. In the fifth I site, I is bonded in a 4-coordinate geometry to two equivalent Cs and two Ce atoms. In the sixth I site, I is bonded in a 4-coordinate geometry to one Cs and three Ce atoms.

36 MATERIALS SCIENCE↗

Materials Data on Cs7NbIn3As5 by Materials Project

Cs7NbIn3As5 crystallizes in the triclinic P-1 space group. The structure is three-dimensional. there are seven inequivalent Cs1+ sites. In the first Cs1+ site, Cs1+ is bonded in a 3-coordinate geometry to three As3- atoms. There are a spread of Cs–As bond distances ranging from 3.61–4.23 Å. In the second Cs1+ site, Cs1+ is bonded in a 3-coordinate geometry to four As3- atoms. There are a spread of Cs–As bond distances ranging from 3.68–4.12 Å. In the third Cs1+ site, Cs1+ is bonded in a 3-coordinate geometry to three As3- atoms. There are a spread of Cs–As bond distances ranging from 3.73–3.87 Å. In the fourth Cs1+ site, Cs1+ is bonded in a 5-coordinate geometry to five As3- atoms. There are a spread of Cs–As bond distances ranging from 3.56–4.05 Å. In the fifth Cs1+ site, Cs1+ is bonded in a 1-coordinate geometry to five As3- atoms. There are a spread of Cs–As bond distances ranging from 3.60–4.00 Å. In the sixth Cs1+ site, Cs1+ is bonded in a 4-coordinate geometry to four As3- atoms. There are a spread of Cs–As bond distances ranging from 3.63–4.12 Å. In the seventh Cs1+ site, Cs1+ is bonded in a 4-coordinate geometry to four As3- atoms. There are a spread of Cs–As bond distances ranging from 3.81–3.97 Å. Nb5+ is bonded in a tetrahedral geometry to four As3- atoms. There are a spread of Nb–As bond distances ranging from 2.43–2.56 Å. There are three inequivalent In1+ sites. In the first In1+ site, In1+ is bonded in a distorted T-shaped geometry to three As3- atoms. There are a spread of In–As bond distances ranging from 2.83–2.95 Å. In the second In1+ site, In1+ is bonded in a distorted T-shaped geometry to three As3- atoms. There are a spread of In–As bond distances ranging from 2.87–2.91 Å. In the third In1+ site, In1+ is bonded in a distorted T-shaped geometry to three As3- atoms. There are a spread of In–As bond distances ranging from 2.83–2.97 Å. There are five inequivalent As3- sites. In the first As3- site, As3- is bonded in a 1-coordinate geometry to six Cs1+, one Nb5+, and two In1+ atoms. In the second As3- site, As3- is bonded in a 1-coordinate geometry to five Cs1+, one Nb5+, and two In1+ atoms. In the third As3- site, As3- is bonded in a 1-coordinate geometry to four Cs1+, one Nb5+, and two In1+ atoms. In the fourth As3- site, As3- is bonded in a 9-coordinate geometry to six Cs1+ and three In1+ atoms. In the fifth As3- site, As3- is bonded in a 1-coordinate geometry to seven Cs1+ and one Nb5+ atom.

36 MATERIALS SCIENCE↗

Materials Data on CsMg14SiO16 by Materials Project

CsMg14SiO16 is Caswellsilverite-derived structured and crystallizes in the tetragonal P4/mmm space group. The structure is three-dimensional. Cs is bonded to six O atoms to form CsO6 octahedra that share corners with two equivalent CsO6 octahedra, corners with four equivalent MgO6 octahedra, and edges with twelve MgO6 octahedra. The corner-sharing octahedral tilt angles are 0°. There are two shorter (2.23 Å) and four longer (2.52 Å) Cs–O bond lengths. There are five inequivalent Mg sites. In the first Mg site, Mg is bonded to six O atoms to form MgO6 octahedra that share corners with two equivalent CsO6 octahedra, corners with two equivalent MgO6 octahedra, corners with two equivalent SiO6 octahedra, and edges with twelve MgO6 octahedra. The corner-sharing octahedral tilt angles are 0°. There are a spread of Mg–O bond distances ranging from 1.87–2.32 Å. In the second Mg site, Mg is bonded to six O atoms to form MgO6 octahedra that share corners with six MgO6 octahedra, edges with two equivalent SiO6 octahedra, and edges with ten MgO6 octahedra. The corner-sharing octahedra tilt angles range from 0–7°. There are a spread of Mg–O bond distances ranging from 2.19–2.24 Å. In the third Mg site, Mg is bonded to six O atoms to form MgO6 octahedra that share corners with six MgO6 octahedra, edges with two equivalent CsO6 octahedra, and edges with ten MgO6 octahedra. The corner-sharing octahedra tilt angles range from 0–11°. There are a spread of Mg–O bond distances ranging from 2.09–2.30 Å. In the fourth Mg site, Mg is bonded to six O atoms to form MgO6 octahedra that share corners with six MgO6 octahedra, edges with two equivalent CsO6 octahedra, and edges with ten MgO6 octahedra. The corner-sharing octahedra tilt angles range from 0–11°. There are a spread of Mg–O bond distances ranging from 2.09–2.30 Å. In the fifth Mg site, Mg is bonded to six O atoms to form MgO6 octahedra that share corners with six equivalent MgO6 octahedra, an edgeedge with one CsO6 octahedra, an edgeedge with one SiO6 octahedra, and edges with ten MgO6 octahedra. The corner-sharing octahedra tilt angles range from 1–16°. There are a spread of Mg–O bond distances ranging from 2.18–2.24 Å. Si is bonded to six O atoms to form SiO6 octahedra that share corners with two equivalent SiO6 octahedra, corners with four equivalent MgO6 octahedra, and edges with twelve MgO6 octahedra. The corner-sharing octahedral tilt angles are 0°. There are four shorter (2.07 Å) and two longer (2.23 Å) Si–O bond lengths. There are nine inequivalent O sites. In the first O site, O is bonded to five Mg and one Si atom to form a mixture of edge and corner-sharing OMg5Si octahedra. The corner-sharing octahedra tilt angles range from 0–11°. In the second O site, O is bonded to one Cs and five Mg atoms to form a mixture of distorted edge and corner-sharing OCsMg5 octahedra. The corner-sharing octahedra tilt angles range from 0–11°. Both O–Mg bond lengths are 2.24 Å. In the third O site, O is bonded to one Cs and five Mg atoms to form a mixture of distorted edge and corner-sharing OCsMg5 octahedra. The corner-sharing octahedra tilt angles range from 0–11°. All O–Mg bond lengths are 2.24 Å. In the fourth O site, O is bonded to six Mg atoms to form OMg6 octahedra that share corners with six equivalent OMg6 octahedra and edges with twelve OMg5Si octahedra. The corner-sharing octahedra tilt angles range from 1–5°. In the fifth O site, O is bonded to four equivalent Mg and two equivalent Si atoms to form OMg4Si2 octahedra that share corners with six OMg4Si2 octahedra and edges with twelve OMg5Si octahedra. The corner-sharing octahedral tilt angles are 0°. In the sixth O site, O is bonded to six Mg atoms to form OMg6 octahedra that share corners with six OMg4Si2 octahedra and edges with twelve OMg5Si octahedra. The corner-sharing octahedral tilt angles are 0°. In the seventh O site, O is bonded to two equivalent Cs and four Mg atoms to form OCs2Mg4 octahedra that share corners with six OMg6 octahedra and edges with twelve OCsMg5 octahedra. The corner-sharing octahedral tilt angles are 0°. In the eighth O site, O is bonded to one Cs and five Mg atoms to form a mixture of distorted edge and corner-sharing OCsMg5 octahedra. The corner-sharing octahedra tilt angles range from 0–11°. The O–Mg bond length is 1.87 Å. In the ninth O site, O is bonded to one Cs and five Mg atoms to form a mixture of distorted edge and corner-sharing OCsMg5 octahedra. The corner-sharing octahedra tilt angles range from 0–11°. There are one shorter (1.87 Å) and two longer (2.24 Å) O–Mg bond lengths.

36 MATERIALS SCIENCE↗

Materials Data on Cs2LaN5O17 by Materials Project

Cs2LaN5O17 crystallizes in the monoclinic C2/c space group. The structure is three-dimensional. Cs is bonded to eight O atoms to form distorted CsO8 hexagonal bipyramids that share corners with two equivalent LaO12 cuboctahedra, corners with four equivalent CsO8 hexagonal bipyramids, an edgeedge with one LaO12 cuboctahedra, and an edgeedge with one CsO8 hexagonal bipyramid. There are a spread of Cs–O bond distances ranging from 3.06–3.38 Å. La is bonded to twelve O atoms to form LaO12 cuboctahedra that share corners with four equivalent CsO8 hexagonal bipyramids and edges with two equivalent CsO8 hexagonal bipyramids. There are a spread of La–O bond distances ranging from 2.60–2.77 Å. There are three inequivalent N sites. In the first N site, N is bonded in a trigonal planar geometry to three O atoms. There are a spread of N–O bond distances ranging from 1.25–1.28 Å. In the second N site, N is bonded in a trigonal planar geometry to three O atoms. There are a spread of N–O bond distances ranging from 1.25–1.28 Å. In the third N site, N is bonded in a trigonal planar geometry to three O atoms. There is one shorter (1.24 Å) and two longer (1.28 Å) N–O bond length. There are nine inequivalent O sites. In the first O site, O is bonded in a distorted single-bond geometry to one Cs, one La, and one N atom. In the second O site, O is bonded in a distorted single-bond geometry to two equivalent Cs and one N atom. In the third O site, O is bonded in a distorted single-bond geometry to two equivalent Cs, one La, and one N atom. In the fourth O site, O is bonded in a distorted single-bond geometry to one La and one N atom. In the fifth O site, O is bonded in a distorted single-bond geometry to one Cs, one La, and one N atom. In the sixth O site, O is bonded in a distorted single-bond geometry to two equivalent Cs and one N atom. In the seventh O site, O is bonded in a distorted single-bond geometry to one La and one N atom. In the eighth O site, O is bonded in a single-bond geometry to one N atom. In the ninth O site, O is bonded in a single-bond geometry to one La atom.

36 MATERIALS SCIENCE↗

Materials Data on CsMg6Zn by Materials Project

CsMg6Zn crystallizes in the monoclinic Cm space group. The structure is three-dimensional. Cs is bonded in a 8-coordinate geometry to eight Mg and two equivalent Zn atoms. There are a spread of Cs–Mg bond distances ranging from 3.73–4.19 Å. There are one shorter (3.72 Å) and one longer (3.73 Å) Cs–Zn bond lengths. There are four inequivalent Mg sites. In the first Mg site, Mg is bonded in a 1-coordinate geometry to two equivalent Cs, five Mg, and one Zn atom. There are a spread of Mg–Mg bond distances ranging from 2.97–3.23 Å. The Mg–Zn bond length is 2.80 Å. In the second Mg site, Mg is bonded in a distorted body-centered cubic geometry to two equivalent Cs and six Mg atoms. There are a spread of Mg–Mg bond distances ranging from 3.21–3.28 Å. In the third Mg site, Mg is bonded in a 2-coordinate geometry to one Cs, four Mg, and two equivalent Zn atoms. Both Mg–Zn bond lengths are 2.82 Å. In the fourth Mg site, Mg is bonded in a 6-coordinate geometry to six Mg atoms. Zn is bonded in a 8-coordinate geometry to two equivalent Cs and six Mg atoms.

36 MATERIALS SCIENCE↗

Materials Data on CsMg6Cu by Materials Project

CsMg6Cu crystallizes in the orthorhombic Amm2 space group. The structure is three-dimensional. Cs is bonded to ten Mg and two equivalent Cu atoms to form a mixture of corner and face-sharing CsMg10Cu2 cuboctahedra. There are a spread of Cs–Mg bond distances ranging from 3.29–3.62 Å. Both Cs–Cu bond lengths are 3.41 Å. There are four inequivalent Mg sites. In the first Mg site, Mg is bonded in a distorted single-bond geometry to two equivalent Cs, five Mg, and one Cu atom. There are a spread of Mg–Mg bond distances ranging from 3.02–3.29 Å. The Mg–Cu bond length is 2.61 Å. In the second Mg site, Mg is bonded in a 8-coordinate geometry to eight Mg atoms. There are two shorter (3.30 Å) and four longer (3.32 Å) Mg–Mg bond lengths. In the third Mg site, Mg is bonded in a 9-coordinate geometry to two equivalent Cs, five Mg, and two equivalent Cu atoms. The Mg–Mg bond length is 3.25 Å. Both Mg–Cu bond lengths are 3.19 Å. In the fourth Mg site, Mg is bonded in a 12-coordinate geometry to two equivalent Cs and eight Mg atoms. Cu is bonded in a 8-coordinate geometry to two equivalent Cs and six Mg atoms.

36 MATERIALS SCIENCE↗

Materials Data on CsFe3P3O14 by Materials Project

CsFe3P3O14 crystallizes in the monoclinic C2/c space group. The structure is three-dimensional. Cs is bonded in a 10-coordinate geometry to ten O atoms. There are a spread of Cs–O bond distances ranging from 3.26–3.49 Å. There are two inequivalent Fe sites. In the first Fe site, Fe is bonded to six O atoms to form FeO6 octahedra that share corners with two equivalent PO4 tetrahedra, corners with two equivalent FeO5 trigonal bipyramids, and an edgeedge with one PO4 tetrahedra. There are a spread of Fe–O bond distances ranging from 1.97–2.14 Å. In the second Fe site, Fe is bonded to five O atoms to form FeO5 trigonal bipyramids that share a cornercorner with one FeO6 octahedra and corners with five PO4 tetrahedra. The corner-sharing octahedral tilt angles are 48°. There are a spread of Fe–O bond distances ranging from 1.90–2.11 Å. There are two inequivalent P sites. In the first P site, P is bonded to four O atoms to form PO4 tetrahedra that share corners with four equivalent FeO5 trigonal bipyramids and an edgeedge with one FeO6 octahedra. There is two shorter (1.54 Å) and two longer (1.57 Å) P–O bond length. In the second P site, P is bonded to four O atoms to form PO4 tetrahedra that share a cornercorner with one FeO6 octahedra and corners with three equivalent FeO5 trigonal bipyramids. The corner-sharing octahedral tilt angles are 46°. There are a spread of P–O bond distances ranging from 1.54–1.56 Å. There are seven inequivalent O sites. In the first O site, O is bonded in a distorted bent 120 degrees geometry to one Cs, one Fe, and one P atom. In the second O site, O is bonded in a distorted bent 150 degrees geometry to one Cs, one Fe, and one P atom. In the third O site, O is bonded in a distorted single-bond geometry to one Cs and one Fe atom. In the fourth O site, O is bonded in a distorted bent 150 degrees geometry to one Cs, one Fe, and one P atom. In the fifth O site, O is bonded in a 3-coordinate geometry to two Fe and one P atom. In the sixth O site, O is bonded in a 2-coordinate geometry to one Cs, one Fe, and one P atom. In the seventh O site, O is bonded in a bent 150 degrees geometry to one Fe and one P atom.

36 MATERIALS SCIENCE↗