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Enhancement of Optical Efficiency of CSP Mirrors for Reducing O&M Cost via Near-Continuous Operation of Self-Cleaning Electrodynamic Screens (EDS). Final Report

Over the past decade, techno-economical advancements in solar energy systems, particularly the improvement in the conversion efficiency of PV modules made with mono-crystalline silicon solar cells from 12% to 20%, as well as the cost reduction in manufacturing by a factor of about 10%, have made it possible to achieve a levelized cost of electricity (LCOE) in PV plants that is comparable to, or less than, the cost of deriving electricity from fossil fuels. Operating PV plants in mid-latitude sun-belt regions, where the solar irradiance level is highest, provides a high annual energy-yield (kWh/kWp) due to two factors: (1) the availability of predictable high solar irradiance throughout the year with the fewest interruptions in solar flux from clouds and rain, and (2) the increased conversion efficiency of crystalline solar cells, as recombination loss has decreased with increased intensity of the sunlight that illuminates the silicon solar cells. Semi-arid and desert regions, however, are plagued by high atmospheric dust concentrations and frequent sand storms. The deposition of a layer of dust on the optical surfaces of solar collectors such as PV modules and concentrating mirrors reduces the transmission efficiency of sunlight that actually reaches the solar cells or receivers, resulting in high energy-yield soiling loss. There are two major cost components to operating a solar plant: (1) installation costs, and (2) operation-and-maintenance (O&M) costs. There is no fuel cost; hence operating a solar plant in a semi-arid or desert region provides high returns on investment if soiling losses are mitigated via efficient cleaning methods and optimized cleaning frequency. If solar collectors are not cleaned, the accumulation of dust layers on solar collectors may cause the operation of such plants in arid regions to become economically unviable. Washing solar collectors with water and detergent, as is most commonly done now, is an efficient method for cleaning. The conventional approach in utility-scale solar plants is to use a large truck with a water tank and pump system for spraying deionized water on the surface of the solar collectors. Robotic cleaning with brushes, used for many solar plants, requires lesser water for cleaning. The water consumed using semi-automated cleaning of PV modules in utility-scale solar plants is approximately 2 liters/m 2 per cleaning cycle. The total optical surface area of the solar collectors in 1 TW-scale solar installation will be more than 3 × 109 m 2 ; hence an enormous amount of water be needed for cleaning. There simply is not enough fresh water in the sun-belt areas of the world for predicted cleaning needs. In solar power plants, the estimated cost of cleaning solar collectors includes expenses related to the equipment used, labor, cost of transportation of water, the energy required for cleaning, plus ancillary costs whereas the cost of water is not considered. The water used is obtained from sources located close to plant sites, unmindful of the environmental and societal impact as the power plants are oftentimes located in regions that face severe drought. This practice is very similar to the cost calculations in deriving the levelized cost of electricity (LCOE) in conventional power plants based on burning fossil fuel such as coal and gas, while disregarding the cost of climate change and health effects. Unless a water-free or low-water cleaning method is established, the expansion of solar plants may lose public support in areas suffering long intervals of drought. The goal of this research project has been the development and application of the Electrodynamic Screen (EDS) as a means for a water-free, scalable cleaning process applicable to solar-power installations, including rooftop applications. We describe here the development of an EDS film-based cleaning process as an emerging method for use on PV modules, parabolic troughs, and heliostats. This report aims to show the feasibility of integrating or retrofitting EDS films onto the optical surfaces of solar collectors (both PV and CSP) while maintaining high transmission or reflection efficiency. The cleaning action provided by the EDS film is an active method to remove dust deposits by electrodynamic force. Current lab-scale prototype EDS films, retrofitted onto solar panels and mirrors, have shown to be capable of maintaining optical transmission or specular-reflection efficiencies higher than 90% of initial values under clean conditions. The optical surfaces of solar collectors laminated with EDS films can remove more than 90% of deposited dust when the EDS is activated for less than two minutes. As an electrodynamic dust removal process, the EDS film-based method is designed primarily for the removal of dust in solar installations located in semi-arid and desert areas, where the atmosphere is often dry and dusty and rainfall is infrequent. While EDS film application minimizes water consumption and facilitates cleaning as frequently as needed, it has limitations in removing contaminants such as soot, organic pollutants deposited as fine films on the surface, and bird droppings. The dust removal efficiency of the EDS is maximum at relative humidity RH is 40 to 50% and decreases at when RH > 65%. Many solar plant sites undergo diurnal and seasonal cycles of high ambient, early afternoon temperatures and an RH that reaches the dew point early in the morning. These variations in atmospheric conditions do not limit the operation of the EDS film. This report presents a brief review of the progress and the potential of EDS film technology for mitigating the impact of dust on solar collectors via water-free cleaning, as well as current technical challenges regarding efficiency and durability. Our experimental data on the performance of EDS films show that: (1) the dust-removal efficiency (DRE) can reach levels higher than 90%, (2) the specular reflectivity (SR) of EDS film-laminated second-surface mirrors reach levels in excess of 90%, (3) the specular reflectivity restoration (SRR) can exceed 90%, (4) the output-power restoration (OPR) of PV modules can exceed 95%, and (5) the optical transmission efficiency (TE) of the EDS films can be greater than 90%. Working with Sandia National Laboratories (NM), Corning Research and Development Corporation (NY), Eastman Kodak (NY), Tomark-Worthen Industries (NH), and EDS Chile SPA (Chile), we have produced EDS film-laminated PV modules and demonstrated their self-cleaning functions without requiring water. We have demonstrated that the operational range of EDS films will cover the expected ambient temperature of solar fields at RH cycling varying from 20 to 95% as long as the EDS films are activated in the RH range 20 to 50%. (Typical solar-field climates in deserts and semi-arid lands often reach near dew point in coastal areas.) Our experiments on the application of hydrophobic-fluorinated nanoparticle coatings on EDS film surfaces show that the EDS operational range can be extended to higher RH levels that approach the dew point. At Eastman Kodak, as one of our industrial partners, we were able to establish a process for manufacturing EDS films using flexographic printing of the electrodes onto transparent polymer films. This process utilizes an existing manufacturing line at Eastman Kodak that allows fabrication of medium-scale EDS films (26 cm × 30 cm). The manufacturing process has the capacity to produce EDS films at high production speeds. The medium-scale EDS films that have been printed at Kodak were evaluated in the lab at Boston University. The EDS films produced at Kodak were laminated at Tomark-Worthen using an industrial scale vacuum laminator to produce EDS film stacks, which can be affixed onto the optical surfaces of PV modules or concentrating mirrors. The EDS film stack consists of the EDS films that have Willow® Glass (WG) which has a thickness of 100 μm as the front surface. The WG sheets obtained from Corning Research and Development Corporation are customized in size and shape to cover the active area of the EDS films. The back surface of the EDS film stack is integrated onto the optical surface of the solar panel or mirror using optically clear adhesive (OCA) films or silicone adhesives. The OCA films (thickness 25 μm) are produced by 3M. The EDS film stacks have the architecture: WG/OCA/EDS Film/OCA/ over PV module or solar mirror. The power-supply units needed for activating the electrodes of the EDS film were designed and produced at Boston University. These power supply units provide three-phase, 1.2 kV voltage pulses at a very low current (micro-ampere) level and at a low frequency (≈ 5 Hz). The voltage pulses are applied to the electrodes in a sequence such that the train of pulses resembles a unidirectional traveling wave of electrical field on the surface of the EDS film. The dust particles on the surface become charged electrostatically and are levitated by the Coulomb force. The lateral sweeping action of the traveling electric field created by the three-phase voltages pulses then sweeps the dust off the surface. The energy consumed by the EDS electrodes is less than 0.2 Wh/m 2 /cleaning cycle, enabling energy-efficient restoration of output power (OPR) of PV module or specular reflectivity restoration (SRR) for solar mirrors. The EDS system consists of (1) an EDS film stack laminated onto the solar collectors, (2) connection of the EDS film to its power supply unit and (3) Interconnection of the power supply to PV modules or solar mirrors. Design, construction and assessment of field-testing units that have EDS stack laminated PV modules for evaluating the performance of the EDS films in solar fields is being carried out at BU. Our progress under this project, aimed at the advancement of EDS film technology, has reached DOE Technology Readiness Level (TRL) 6. Based on the extensive laboratory evaluations and limited field trials, as well as contacts with potential users, we believe that the technology has reached its commercial stage. We are conducting a cost analysis using the National Renewable Energy Laboratory (NREL) System Advisory Model (SAM) and are preparing for field trials of EDS films in different solar fields in the US, Chile, India and in the Middle East. A brief description of EDS film performance, construction and testing of the field-test unit, autonomous operation of the field-test unit for evaluating EDS performance in increasing energy yield, associated revenue savings, and water conservation is presented.

14 SOLAR ENERGY↗

Review and Summary of Corrosion Behavior for Aluminum-Clad Spent Nuclear Fuel in Dry Storage

A description of the corrosion behavior of aluminum alloys used for cladding on aluminum-based, aluminum-clad nuclear fuel used in research reactors under potential dry storage conditions has been compiled. An evaluation is made of potential additional corrosion with water postulated to not be removed during drying. The relative humidity (RH) produced by typical dryness criteria for industrial spent nuclear fuel drying is expected to be low, particularly at high temperatures (17% RH at 20°C and lower at higher temperatures). Existing corrosion data suggests that negligible vapor-phase corrosion of aluminum is expected at such low humidity, even for nominally bare aluminum surfaces. That is, the predicted relative humidity from free water (e.g., 17% RH) is below the “critical” relative humidity (~40% RH at room temperature), below which no significant corrosion is observed for bare aluminum. Furthermore, reported room-temperature corrosion rates are very low even under saturated (100% RH) water vapor. Existing results showing significant vapor-phase corrosion corresponded specifically to conditions of high temper ed with high relative humidity. A relatively large reservoir of (chemically bound) water exists in the aluminum (oxy)hydroxide films on the SNF cladding surface. The estimated total could saturate the gas even at relatively high temperature if fully released; however, its release as molecular water is expected to only be plausible if the temperature during storage exceeds both the drying temperature and the threshold for thermal decomposition of the trihydroxides (~220°C). Therefore, the combination of high temperature and high relative humidity that could drive significant corrosion is considered implausible during sealed dry storage following an appropriate drying process, to include >220°C drying for canisters that may approach or exceed this temperature during storage. Vapor-phase testing of aluminum samples with an adherent (oxy)hydroxide layer, prepared in liquid water to resemble those on actual aluminum-clad spent nuclear fuel (ASNF), did not observe evidence of additional corrosion even at combined high-temperature (up to 180°C) and high-humidity (up to 100% RH) conditions. Instead, small net mass losses were observed for most specimens and attributed to dehydration of the samples, which had been air-dried only prior to testing. ASNF being moved to dry storage is expected to have an existing (oxy)hydroxide film, suggesting that the cladding will be less prone to additional corrosion than bare aluminum metal. If significant corrosion did occur during sealed storage, the overall extent and impact is expected to be small. Corrosion post-closure of a canister would not alter the total amount of hydrogen in the canister, so it would have no effect on the maximum H 2 release already assessed in existing bounding calculations. In addition, the total amount of water in a 25-µm dense bayerite film would consume a only ~8 µm additional aluminum metal on average, if fully consumed by oxidizing aluminum metal to Al 2 O 3 . These conclusions are consistent with ASNF-in-canister simulations to date, which included a reaction pathway for corrosion using kinetics from previous literature and believed to be conservative and predicted very low rates of corrosion.

11 NUCLEAR FUEL CYCLE AND FUEL MATERIALS↗

Materials Data on H12RhC8NO6 by Materials Project

Rh(C2O3)2N(CH3)4 crystallizes in the orthorhombic Pnma space group. The structure is zero-dimensional and consists of four tetramethylammonium molecules and four Rh(C2O3)2 clusters. In each Rh(C2O3)2 cluster, Rh3+ is bonded in a rectangular see-saw-like geometry to two C and two O2- atoms. Both Rh–C bond lengths are 1.85 Å. Both Rh–O bond lengths are 2.08 Å. There are four inequivalent C sites. In the first C site, C is bonded in a distorted bent 120 degrees geometry to two O2- atoms. There is one shorter (1.24 Å) and one longer (1.31 Å) C–O bond length. In the second C site, C is bonded in a distorted bent 120 degrees geometry to two O2- atoms. There is one shorter (1.24 Å) and one longer (1.30 Å) C–O bond length. In the third C site, C is bonded in a linear geometry to one Rh3+ and one O2- atom. The C–O bond length is 1.16 Å. In the fourth C site, C is bonded in a distorted linear geometry to one Rh3+ and one O2- atom. The C–O bond length is 1.16 Å. There are six inequivalent O2- sites. In the first O2- site, O2- is bonded in a distorted bent 120 degrees geometry to one Rh3+ and one C atom. In the second O2- site, O2- is bonded in a single-bond geometry to one C atom. In the third O2- site, O2- is bonded in a distorted bent 120 degrees geometry to one Rh3+ and one C atom. In the fourth O2- site, O2- is bonded in a single-bond geometry to one C atom. In the fifth O2- site, O2- is bonded in a single-bond geometry to one C atom. In the sixth O2- site, O2- is bonded in a single-bond geometry to one C atom.

36 MATERIALS SCIENCE↗

Materials Data on NbSiRh by Materials Project

NbRhSi crystallizes in the orthorhombic Pnma space group. The structure is three-dimensional. Nb is bonded in a 11-coordinate geometry to six equivalent Rh and five equivalent Si atoms. There are a spread of Nb–Rh bond distances ranging from 2.93–3.01 Å. There are three shorter (2.70 Å) and two longer (2.75 Å) Nb–Si bond lengths. Rh is bonded in a 4-coordinate geometry to six equivalent Nb and four equivalent Si atoms. There are a spread of Rh–Si bond distances ranging from 2.40–2.47 Å. Si is bonded in a 9-coordinate geometry to five equivalent Nb and four equivalent Rh atoms.

36 MATERIALS SCIENCE↗

Materials Data on CeAsRh by Materials Project

CeRhAs crystallizes in the orthorhombic Pnma space group. The structure is three-dimensional. Ce is bonded to six equivalent Rh and six equivalent As atoms to form a mixture of distorted face and edge-sharing CeAs6Rh6 cuboctahedra. There are a spread of Ce–Rh bond distances ranging from 2.85–3.22 Å. There are a spread of Ce–As bond distances ranging from 3.08–3.21 Å. Rh is bonded in a 9-coordinate geometry to six equivalent Ce and three equivalent As atoms. There are two shorter (2.50 Å) and one longer (2.51 Å) Rh–As bond lengths. As is bonded in a 9-coordinate geometry to six equivalent Ce and three equivalent Rh atoms.

36 MATERIALS SCIENCE↗

Materials Data on ThSbRh by Materials Project

ThRhSb is half-Heusler structured and crystallizes in the cubic F-43m space group. The structure is three-dimensional. Th is bonded to four equivalent Rh and six equivalent Sb atoms to form a mixture of distorted corner and face-sharing ThSb6Rh4 tetrahedra. All Th–Rh bond lengths are 2.91 Å. All Th–Sb bond lengths are 3.36 Å. Rh is bonded in a body-centered cubic geometry to four equivalent Th and four equivalent Sb atoms. All Rh–Sb bond lengths are 2.91 Å. Sb is bonded in a 10-coordinate geometry to six equivalent Th and four equivalent Rh atoms.

36 MATERIALS SCIENCE↗

Materials Data on USbRh by Materials Project

URhSb is half-Heusler structured and crystallizes in the cubic F-43m space group. The structure is three-dimensional. U is bonded to four equivalent Rh and six equivalent Sb atoms to form a mixture of distorted face and corner-sharing USb6Rh4 tetrahedra. All U–Rh bond lengths are 2.83 Å. All U–Sb bond lengths are 3.27 Å. Rh is bonded in a body-centered cubic geometry to four equivalent U and four equivalent Sb atoms. All Rh–Sb bond lengths are 2.83 Å. Sb is bonded in a 10-coordinate geometry to six equivalent U and four equivalent Rh atoms.

36 MATERIALS SCIENCE↗

Materials Data on Sr(GeRh)2 by Materials Project

Sr(RhGe)2 crystallizes in the tetragonal I4/mmm space group. The structure is three-dimensional. Sr is bonded in a 8-coordinate geometry to eight equivalent Rh and eight equivalent Ge atoms. All Sr–Rh bond lengths are 3.46 Å. All Sr–Ge bond lengths are 3.32 Å. Rh is bonded to four equivalent Sr and four equivalent Ge atoms to form a mixture of distorted corner, edge, and face-sharing RhSr4Ge4 tetrahedra. All Rh–Ge bond lengths are 2.48 Å. Ge is bonded in a 9-coordinate geometry to four equivalent Sr, four equivalent Rh, and one Ge atom. The Ge–Ge bond length is 2.90 Å.

36 MATERIALS SCIENCE↗

Materials Data on Ba(GeRh)2 by Materials Project

Ba(RhGe)2 crystallizes in the tetragonal I4/mmm space group. The structure is three-dimensional. Ba is bonded in a 8-coordinate geometry to eight equivalent Rh and eight equivalent Ge atoms. All Ba–Rh bond lengths are 3.72 Å. All Ba–Ge bond lengths are 3.49 Å. Rh is bonded to four equivalent Ba and four equivalent Ge atoms to form a mixture of distorted corner, edge, and face-sharing RhBa4Ge4 tetrahedra. All Rh–Ge bond lengths are 2.46 Å. Ge is bonded in a 8-coordinate geometry to four equivalent Ba and four equivalent Rh atoms.

36 MATERIALS SCIENCE↗

Materials Data on LuRh3C by Materials Project

LuRh3C is (Cubic) Perovskite structured and crystallizes in the cubic Pm-3m space group. The structure is three-dimensional. Lu is bonded to twelve equivalent Rh atoms to form LuRh12 cuboctahedra that share corners with twelve equivalent LuRh12 cuboctahedra, faces with six equivalent LuRh12 cuboctahedra, and faces with eight equivalent CRh6 octahedra. All Lu–Rh bond lengths are 2.94 Å. Rh is bonded to four equivalent Lu and two equivalent C atoms to form a mixture of distorted face, edge, and corner-sharing RhLu4C2 octahedra. The corner-sharing octahedra tilt angles range from 0–60°. Both Rh–C bond lengths are 2.08 Å. C is bonded to six equivalent Rh atoms to form CRh6 octahedra that share corners with six equivalent CRh6 octahedra and faces with eight equivalent LuRh12 cuboctahedra. The corner-sharing octahedral tilt angles are 0°.

36 MATERIALS SCIENCE↗

Materials Data on PrRh3C by Materials Project

PrRh3C is (Cubic) Perovskite structured and crystallizes in the cubic Pm-3m space group. The structure is three-dimensional. Pr is bonded to twelve equivalent Rh atoms to form PrRh12 cuboctahedra that share corners with twelve equivalent PrRh12 cuboctahedra, faces with six equivalent PrRh12 cuboctahedra, and faces with eight equivalent CRh6 octahedra. All Pr–Rh bond lengths are 3.01 Å. Rh is bonded to four equivalent Pr and two equivalent C atoms to form a mixture of distorted face, edge, and corner-sharing RhPr4C2 octahedra. The corner-sharing octahedra tilt angles range from 0–60°. Both Rh–C bond lengths are 2.13 Å. C is bonded to six equivalent Rh atoms to form CRh6 octahedra that share corners with six equivalent CRh6 octahedra and faces with eight equivalent PrRh12 cuboctahedra. The corner-sharing octahedral tilt angles are 0°.

36 MATERIALS SCIENCE↗

Materials Data on ScRh3C by Materials Project

ScRh3C is (Cubic) Perovskite structured and crystallizes in the cubic Pm-3m space group. The structure is three-dimensional. Sc is bonded to twelve equivalent Rh atoms to form ScRh12 cuboctahedra that share corners with twelve equivalent ScRh12 cuboctahedra, faces with six equivalent ScRh12 cuboctahedra, and faces with eight equivalent CRh6 octahedra. All Sc–Rh bond lengths are 2.90 Å. Rh is bonded to four equivalent Sc and two equivalent C atoms to form a mixture of distorted edge, face, and corner-sharing RhSc4C2 octahedra. The corner-sharing octahedra tilt angles range from 0–60°. Both Rh–C bond lengths are 2.05 Å. C is bonded to six equivalent Rh atoms to form CRh6 octahedra that share corners with six equivalent CRh6 octahedra and faces with eight equivalent ScRh12 cuboctahedra. The corner-sharing octahedral tilt angles are 0°.

36 MATERIALS SCIENCE↗

Materials Data on TmRh3C by Materials Project

TmRh3C is (Cubic) Perovskite structured and crystallizes in the cubic Pm-3m space group. The structure is three-dimensional. Tm is bonded to twelve equivalent Rh atoms to form TmRh12 cuboctahedra that share corners with twelve equivalent TmRh12 cuboctahedra, faces with six equivalent TmRh12 cuboctahedra, and faces with eight equivalent CRh6 octahedra. All Tm–Rh bond lengths are 2.94 Å. Rh is bonded to four equivalent Tm and two equivalent C atoms to form a mixture of distorted edge, face, and corner-sharing RhTm4C2 octahedra. The corner-sharing octahedra tilt angles range from 0–60°. Both Rh–C bond lengths are 2.08 Å. C is bonded to six equivalent Rh atoms to form CRh6 octahedra that share corners with six equivalent CRh6 octahedra and faces with eight equivalent TmRh12 cuboctahedra. The corner-sharing octahedral tilt angles are 0°.

36 MATERIALS SCIENCE↗

Materials Data on YbRh3C by Materials Project

YbRh3C is (Cubic) Perovskite structured and crystallizes in the cubic Pm-3m space group. The structure is three-dimensional. Yb is bonded to twelve equivalent Rh atoms to form YbRh12 cuboctahedra that share corners with twelve equivalent YbRh12 cuboctahedra, faces with six equivalent YbRh12 cuboctahedra, and faces with eight equivalent CRh6 octahedra. All Yb–Rh bond lengths are 2.92 Å. Rh is bonded to four equivalent Yb and two equivalent C atoms to form a mixture of distorted corner, edge, and face-sharing RhYb4C2 octahedra. The corner-sharing octahedra tilt angles range from 0–60°. Both Rh–C bond lengths are 2.07 Å. C is bonded to six equivalent Rh atoms to form CRh6 octahedra that share corners with six equivalent CRh6 octahedra and faces with eight equivalent YbRh12 cuboctahedra. The corner-sharing octahedral tilt angles are 0°.

36 MATERIALS SCIENCE↗

Materials Data on MnAlRh2 by Materials Project

Rh2MnAl is Heusler structured and crystallizes in the cubic Fm-3m space group. The structure is three-dimensional. Mn is bonded in a body-centered cubic geometry to eight equivalent Rh atoms. All Mn–Rh bond lengths are 2.62 Å. Rh is bonded in a body-centered cubic geometry to four equivalent Mn and four equivalent Al atoms. All Rh–Al bond lengths are 2.62 Å. Al is bonded in a body-centered cubic geometry to eight equivalent Rh atoms.

36 MATERIALS SCIENCE↗

Materials Data on LaAsRh by Materials Project

LaRhAs is hexagonal omega structure-derived structured and crystallizes in the tetragonal I4_1md space group. The structure is three-dimensional. La is bonded to six equivalent Rh and six equivalent As atoms to form a mixture of face and edge-sharing LaAs6Rh6 cuboctahedra. There are four shorter (3.25 Å) and two longer (3.26 Å) La–Rh bond lengths. There are four shorter (3.22 Å) and two longer (3.32 Å) La–As bond lengths. Rh is bonded in a 9-coordinate geometry to six equivalent La and three equivalent As atoms. There are two shorter (2.47 Å) and one longer (2.49 Å) Rh–As bond lengths. As is bonded in a 9-coordinate geometry to six equivalent La and three equivalent Rh atoms.

36 MATERIALS SCIENCE↗

Materials Data on Ti3In3Rh2 by Materials Project

Ti3Rh2In3 crystallizes in the hexagonal P-62m space group. The structure is three-dimensional. Ti is bonded in a 12-coordinate geometry to four equivalent Rh and six equivalent In atoms. All Ti–Rh bond lengths are 2.69 Å. There are two shorter (2.97 Å) and four longer (3.08 Å) Ti–In bond lengths. Rh is bonded in a 9-coordinate geometry to six equivalent Ti and three equivalent In atoms. All Rh–In bond lengths are 2.87 Å. In is bonded to six equivalent Ti, two equivalent Rh, and four equivalent In atoms to form a mixture of distorted face and corner-sharing InTi6In4Rh2 cuboctahedra. There are two shorter (3.02 Å) and two longer (3.08 Å) In–In bond lengths.

36 MATERIALS SCIENCE↗

Materials Data on BaIn2Rh by Materials Project

BaRhIn2 crystallizes in the orthorhombic Cmcm space group. The structure is three-dimensional. Ba is bonded in a 1-coordinate geometry to three equivalent Rh and ten equivalent In atoms. There are one shorter (3.17 Å) and two longer (3.52 Å) Ba–Rh bond lengths. There are a spread of Ba–In bond distances ranging from 3.62–3.76 Å. Rh is bonded in a 9-coordinate geometry to three equivalent Ba and six equivalent In atoms. There are four shorter (2.82 Å) and two longer (2.84 Å) Rh–In bond lengths. In is bonded in a 3-coordinate geometry to five equivalent Ba and three equivalent Rh atoms.

36 MATERIALS SCIENCE↗