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Corrosion behavior of ferritic FeCrAl alloys in simulated BWR normal water chemistry

Ferritic iron-chromium-aluminum (FeCrAl) alloys with varying Cr content were subjected to in-situ irradiation-corrosion with energetic protons or electron beams in pure water with various oxygen concentrations. Oxide microstructure and composition were characterized to compare the corrosion under irradiation with the thermal corrosion in the same water conditions. The dominant effect seems to be the production of H 2 O 2 at the surface by the intense proton and electron beams. The corrosion potential of FeCrAl under BWR-NWC condition is somewhat above the Cr 2 O 3 /CrO 4 2- phase boundary, oxidizing the Cr(III) to Cr(VI) in the outer part of the film, but with some Cr(III) remaining in the interior of the oxide. The beam increases the corrosion potential, significantly reducing Cr(III) content throughout the oxide. Finally, the crystallites on the surface, which form by re-precipitation from solution, do not contain Cr because at low potential Cr(III) is not soluble, and at high potential Cr(VI) is quite soluble.

36 MATERIALS SCIENCE↗

Microstructural evolution of compositionally complex solid-solution alloys under in-situ dual-beam irradiation

Here, this work attempts to link the microstructural evolution of single-phase compositionally complex alloy (CCA) compositions under dual-beam irradiation to their Mn-content via the stacking-fault energy (SFE) and vacancy migration energies. Two alloys, Cr 18 Fe 27 Mn 27 Ni 28 and Cr 15 Fe 35 Mn 15 Ni 35 , along with less compositionally complex pure Ni and Fe 56 Ni 44 binary were irradiated at 500 and 600 °C under dual-beam 1 MeV Kr 2+ and 16 keV He + heavy-ions up to 7 displacements per atom (dpa) with a He/dpa ratio of 0.75 %/dpa using in situ transmission electron microscopy (TEM). Due to the bubble-stabilizing effect of implanted He, bubbles were observed in all irradiations, and populations of faulted interstitial loops were characterized in Cr 18 Fe 27 Mn 27 Ni 28 and Cr 15 Fe 35 Mn 15 Ni 35 . A reduction in swelling was observed in the two CCAs compared to pure Ni and Fe 56 Ni 44 . Although swelling increased from 500 to 600 °C in Fe 56 Ni 44 , Cr 15 Fe 35 Mn 15 Ni 35 and Cr 18 Fe 27 Mn 27 Ni 28 both swelled slightly more at 500 °C. This was attributed to the difference in vacancy mobility, stronger pinning effect of vacancies on He, and the sink strength of faulted dislocation loops. Faulted interstitial loops nucleated with a higher number density and dislocation line density in Cr 15 Fe 35 Mn 15 Ni 35 at both temperatures, and at 600 °C in both materials. The differences in faulted loop population and temperature effect on swelling are correlated to the Mn-content and the measured SFE (20.2 ± 6.7 mJ/m 2 for Cr 18 Fe 27 Mn 27 Ni 28 and 9.2 ± 3.4 mJ/m 2 for Cr 15 Fe 35 Mn 15 Ni 35 ).

36 MATERIALS SCIENCE↗

Chromium-doped uranium dioxide fuels: A review

UO 2 doped with parts per million CR 2 O 3 powder is considered a potential near term accident tolerant fuel candidate. Here, the results of decades of industry and academic research into Cr-doped UO 2 are analyzed and their shortcomings are critiqued. Focusing on the incorporation mechanisms of Cr into the fuel matrix, we explore a mechanistic understanding of the characteristic properties of Cr-doped UO 2 , notably, enhanced fission gas retention attributed to enlarged grain sizes following sintering, along with marginal improvements in the thermophysical properties. The findings of recent X-ray Adsorption Near Edge Spectroscopy studies were compared and put into conversation with historic data regarding the incorporation of Cr in UO 2 . On the basis of defect mechanisms, the case is made for the substitutional incorporation of Cr governing the lattice solubility but not the enhanced U diffusivity. Instead, Cr/CR 2 O 3 redox chemistry in a well-defined oxygen potential explains the differences in the U diffusivity and O/M ratio. The primary mechanism of doping enhanced grain growth is found to be liquid assisted sintering due to a CRO (1) eutectic phase at the grain boundaries. The role of inhomogeneities in Cr concentration in UO 2 at various length scales across the materials microstructure is highlighted and connected to promising experimental and modeling work to fill in the gaps in the current understanding of Cr-doped UO 2 . The review considers both the open scientific questions and engineering applications to illustrate the deep connections between the practice and theory in the design of accident tolerant nuclear fuels. In conclusion, the review ends with an outline of future works that combine meticulous irradiation studies and high resolution experiments with next generation modeling and simulations techniques empowered by machine learning advances to accelerate the fabrication and adoption of Cr-doped UO 2 light water reactors.

Cleveland, Mack Wesley [Massachusetts Inst. of Tec↗

Radiolytic Production of Radical Species in Gibbsite Doped with Iron and Chromium Ions

Gibbsite (aluminum hydroxide, Al(OH) 3 ) nanoparticles, synthesized from aluminum chloride or aluminum nitrate, were doped with metal ions, Cr(III) or Fe(III), and then irradiated with γ rays to determine the effect of the dopants on radiolytic hydrogen (H 2 ) production and radical generation. The addition of Cr(III) and Fe(III) ions at concentrations of 0.5% or 5% decreased the concentration of stable oxygen-centered radicals, with the strongest suppression in Cr(III) doped samples. A decrease in H 2 yields was observed with increasing Cr(III) or Fe(III) concentrations, with the greatest effect observed for the Fe(III)-doped samples. Reduction of the Cr(III) to Cr(II) and Fe(III) to Fe(II) was also observed, probably due to scavenging of radiolytically produced electrons. However, further processes differ for Fe(III)- and Cr(III)-doped systems. Both ions are reduced by the free electrons, leading to a decrease in H 2 production, but they react differently with the oxygen radicals. Cr(III) can be oxidized by oxygen radicals, whereas Fe(III) cannot. Fe(II) can interact with peroxides, possible products of intermediate oxygen oxidation, converting back to Fe(III) and leaving oxygen radicals behind. These oxidation reactions lead to a difference in the observed relative effects on H 2 yields and oxygen radical production between Cr(III)- and Fe(III)-doped gibbsite. In conclusion, the connection between electron scavenging and H 2 production indicates that radiolytically produced electrons are precursors to H 2 .

Anions↗

Modification of Ni-20Cr corrosion dealloying behavior in molten fluorides via cold work induced plastic deformation

The corrosion dealloying behavior of cold-worked (CW) Ni20Cr alloy (wt%) was studied in molten LiF-NaF-KF (or FLiNaK) salts at 600 °C, equal to a homologous temperature (TH) of 0.52. Alloys were cold-rolled to achieve reductions of thickness of 10%, 30%, and 50% introducing plastic deformation and a high density of dislocations. Potentiostatic holds (Eapplied) were applied in two different electrode potential regimes. At 1.75VK+/K$${\text{V}}_{{\text{K}}^{+}/{\text{K}}}$$, Cr dealloying to Cr(II) and Cr(III) is predominant, while at 1.90 VK+/K$${\text{V}}_{{\text{K}}^{+}/{\text{K}}}$$, both Ni and Cr are oxidized in molten FLiNaK at 600 °C. In these potential regimes, dealloyed Ni20Cr displayed bicontinuous porosity within the grain interior and at grain boundaries, driven by the high driving force for Cr dissolution and sustained by defect mediated outward solid state diffusion of Cr in parallel with surface diffusion of Ni. The bicontinuous porous structure developed was observed to undergo further coarsening and densification of the Ni-rich ligaments at a higher electrode potential. The main effect of CW observed is the introduction of plastic deformation and dislocation substructures that serve as short-circuit paths for Cr solid state diffusion to surfaces exposed to FLiNaK. This modified the evolution of the bicontinuous porous structure which increased with CW substantially. Kinetic analysis reveals that the Cr dealloying at +1.75 VK+/K$${\text{V}}_{{\text{K}}^{+}/{\text{K}}}$$ and 1.90 VK+/K$${\text{V}}_{{\text{K}}^{+}/{\text{K}}}$$ is initially charge transfer controlled, except for the 50% CW condition at 1.90 VK+/K$${\text{V}}_{{\text{K}}^{+}/{\text{K}}}$$, where the process becomes limited by slow Cr defect mediated bulk diffusion. The rate determining factors are explored and compared to experimental results.

Chan, Ho Lun↗

Ethylene polymerization with a crystallographically well-defined metal–organic framework supported catalyst

The inherent crystallinity of metal–organic framework (MOF) catalysts offers the possibility to understand the structure of the active site at the molecular level. This property is often lacking in traditional amorphous supports. Cr-SIM-NU-1000, a MOF-supported Cr 3+ heterogeneous catalyst, is shown to be competent for ethylene polymerization after activation with AlEt 2 Cl (DEAC), producing crystalline linear polyethylene (PE). The polymer produced has a low polydispersity (D = 2.0), in marked contrast to the Phillips supported chromium catalyst, Cr@SiO 2 (D ~ 8–65). Cr-SIM-NU-1000 achieves a turnover frequency of 2.6 × 10 3 h –1 under 40 bar ethylene pressure at room temperature, with corresponding PE productivity of 1.3 × 10 5 g PE mol –1 Cr per h. Single crystal X-ray diffraction (SC-XRD) of the pre-catalyst was conducted by collecting a structure of alkyl aluminum (DEAC) co-catalyst treated Cr-SIM-NU-1000. This crystal structure provides insight into the interactions between DEAC co-catalyst and Cr active site, revealing a Cr–C bond after treatment with DEAC. Furthermore, DEAC is crystallographically resolved at the terminal oxy-ligands of the node and likely also exists within the window pores of the framework between nodes, based on electron density mapping. Cr-SIM-NU-1000 offers the opportunity to study a structurally well-defined olefin polymerization system, with atomically precise characterization of the pre-catalyst structure. Furthermore, this allows the proposal of a mechanism and feeds into future development of next-generation heterogeneous catalyst systems.

37 INORGANIC, ORGANIC, PHYSICAL, AND ANALYTICAL CH↗

Low temperature hot corrosion

The reaction of Co-Cr, Ni-Cr, Co-Cr-Al, and Ni-Cr-Al alloys with Na2SO4 in the presence of SO3 at temperatures between 700 and 750 C leads to the formation of liquid CoSO4-Na2SO4 or NiSO4-Na2SO4 deposits on the alloy surface. The formation of Cr2O3 and/or Al2O3 below this deposit results in a locally low P(O2) and a higher P(S2) and P(SO2). It is noted that these conditions can prevent protective oxide formation either by sulfide formation in the alloy, which localizes the Cr and/or Al in discrete particles, or by acid fluxing involving a reaction between Al2O3 or Cr2O3 and SO2 to form a salt-soluble species and subsequent reprecipitation as porous oxides in regions of higher P(O2). These processes may occur simultaneously, although a given alloy generally exhibits features of predominantly one type. Here, the Ni-Cr and Ni-Cr-Al alloys, and to some extent the Co-Cr alloys, exhibit features indicative of the sulfidation mechanism, whereas the morphology for the Co-Cr-Al alloy is more consistent with a predominant acid fluxing mechanism.

Chiang, K. T.↗

Processing and Mechanical Properties of NiAl-Based In-Situ Composites

In-situ composites based on the NiAl-Cr eutectic system were successfully produced by containerless processing and evaluated. The NiAl-Cr alloys had a fibrous microstructure while the NiAl-(Cr,Mo) alloys containing 1 at. percent or more molybdenum exhibited a lamellar structure. The NiAl-28Cr-6Mo eutectic displays promising high temperature strength while still maintaining a reasonable room temperature fracture toughness when compared to other NiAl-based materials. The Laves phase NiAlTa was used to strengthen NiAl and very promising creep strengths were found for the directionally solidified NiAl-NiAlTa eutectic. The eutectic composition was found to be near NiAl-15.5Ta (at. percent) and well aligned microstructures were produced at this composition. An off-eutectic composition of NiAl-14.5Ta was also processed, consisting of NiAl dendrites surrounded by aligned eutectic regions. The room temperature toughness of these two phase alloys was similar to that of polycrystalline NiAl even with the presence of the brittle Laves phase NiAlTa. Polyphase in-situ composites were generated by directional solidification of ternary eutectics. The systems investigated were the Ni-Al-Ta-X (X=Cr, Mo, or V) alloys. Ternary eutectics were found in each of these systems and both the eutectic composition and temperature were determined. Of these ternary eutectics, the one in the NiAl-Ta-Cr system was found to be the most promising. The fracture toughness of the NiAl-(Cr,Al)NiTa-Cr eutectic was intermediate between those of the NiAl-NiAlTa eutectic and the NiAl-Cr eutectic. The creep strength of this ternary eutectic was similar to or greater than that of the NiAl-Cr eutectic.

Johnson, David Ray↗

Removing cosmic-ray hits from multiorbit HST Wide Field Camera images

We present an optimized algorithm that removes cosmic rays ('CRs') from multiorbit Hubble Space Telescope (HST) Wide Field/Planetary Camera ('WF/PC') images. It computes the image noise in every iteration from the WF/PC CCD equation. This includes all known sources of random and systematic calibration errors. We test this algorithm on WF/PC stacks of 2-12 orbits as a function of the number of available orbits and the formal Poissonian sigma-clipping level. We find that the algorithm needs greater than or equal 4 WF/PC exposures to locate the minimal sky signal (which is noticeably affected by CRs), with an optimal clipping level at 2-2.5 x sigma(sub Poisson). We analyze the CR flux detected on multiorbit 'CR stacks,' which are constructed by subtracting the best CR filtered images from the unfiltered 8-12 orbit average. We use an automated object finder to determine the surface density of CRS as a function of the apparent magnitude (or ADU flux) they would have generated in the images had they not been removed. The power law slope of the CR 'counts' (gamma approximately = 0.6 for N(m) m(exp gamma)) is steeper than that of the faint galaxy counts down to V approximately = 28 mag. The CR counts show a drop off between 28 less than or approximately V less than or approximately 30 mag (the latter is our formal 2 sigma point source sensitivity without spherical aberration). This prevents the CR sky integral from diverging, and is likely due to a real cutoff in the CR energy distribution below approximately 11 ADU per orbit. The integral CR surface density is less than or approximately 10(exp 8)/sq. deg, and their sky signal is V approximately = 25.5-27.0 mag/sq. arcsec, or 3%-13% of our NEP sky background (V = 23.3 mag/sq. arcsec), and well above the EBL integral of the deepest galaxy counts (B(sub J) approximately = 28.0 mag/sq. arcsec). We conclude that faint CRs will always contribute to the sky signal in the deepest WF/PC images. Since WFPC2 has approximately 2.7x lower read noise and a thicker CCD, this will result in more CR detections than in WF/PC, potentially affecting approximately 10%-20% of the pixels in multiorbit WFPC2 data cubes.

Windhorst, Rogier A.↗

Mitigating fatigue on the flight deck: how is controlled rest used in practice?

Controlled Rest (CR) refers to a short, voluntary nap opportunity taken by pilots on the flight deck as a countermeasure to unanticipated sleepiness in flight. This study explores the profile of CR use in a long-haul commercial airline. Forty-four pilots wore actiwatches and filled in an application-based sleep/work diary for approximately 2 weeks resulting in complete records from 239 flights. Timing of sleep periods and flight schedules were analyzed relative to home-base time. Pearson correlations were used to assess the influence of pilot demographics on CR use. A mixed-effects logistic regression was used to analyze the impact of schedule factors on CR. CR was taken on 46% (n=110) of flights, with 80% (n=106/133) of all CR attempts estimated by actigraphy to have successfully achieved sleep. Average sleep duration during successful rest periods was estimated as 31.7 ± 12.2 minutes. CR was more frequent on return (60%, n=71) vs. outbound flights (33%, n=39); 2-pilot (69%, n=83) vs. >2-pilot flights (23%, n=27); <10h (63%, n=80) vs. >10h duration flights (27%, n=30); and night (55%, n=76) vs. day flights (34%, n=34) (all p≤0.001). There was no significant difference for direction of travel (eastbound: 51%, n= 57; westbound: 40%, n= 44; p=0.059). Of note, 22% (n=26) of augmented flights contained both CR and bunk rest. Data from this airline show that CR is most commonly used as a countermeasure to sleepiness on flights <10h duration (2-pilot crews) and home-base nighttime flights. Future studies are required to determine the generalizability of these results to other airlines.

sleepiness↗

Characterizing Radiation-Induced Chromium Redox Chemistry

The redox behavior of Cr(III) and Cr(VI) in nuclear environments were studied by analyzing aqueous irradiated chromium ions using UV-Visible spectroscopy. The formation of different chromium oxidation states can occur through gamma radiolysis of chromium solutions. Characterization of radiation-induced chromium is not well understood, and yet important as chromium can make its way into the primary coolant of reactors because of the corrosion of stainless steel reactor components. Furthermore, Cr(VI) is toxic and not suitable for environmental release, therefore Cr speciation is important. Fricke dosimetry was performed to collect doses rates, specific extinction coefficients were obtained from various analytical methods for the two oxidation states of chromium. Chromium samples--conditioned at various pH's and concentration to understand the effects--were then irradiated using a Coblat-60 gamma irradiator. Three optical spectroscopy analytical methods were used , including direct oxidation state measurements and complexation by either EDTA or DPC. Complexation by EDTA was found to not be a reliable method. Radiolytic oxidation of Cr(III) to Cr(VI), and reduction of Cr(VI) to Cr(III) were clearly seen, except for Cr(III) samples were a pH less than or equal to 2, where no change occurred.

38 RADIATION CHEMISTRY, RADIOCHEMISTRY, AND NUCLEA↗

Materials Data on CrCoGe by Materials Project

CoCrGe crystallizes in the hexagonal P6_3/mmc space group. The structure is three-dimensional. Cr is bonded in a 12-coordinate geometry to two equivalent Cr, six equivalent Co, and six equivalent Ge atoms. Both Cr–Cr bond lengths are 2.55 Å. All Cr–Co bond lengths are 2.69 Å. All Cr–Ge bond lengths are 2.69 Å. Co is bonded in a 11-coordinate geometry to six equivalent Cr and five equivalent Ge atoms. There are three shorter (2.37 Å) and two longer (2.55 Å) Co–Ge bond lengths. Ge is bonded in a 11-coordinate geometry to six equivalent Cr and five equivalent Co atoms.

36 MATERIALS SCIENCE↗

Materials Data on Cr2As by Materials Project

Cr2As crystallizes in the tetragonal P4/nmm space group. The structure is three-dimensional. there are two inequivalent Cr sites. In the first Cr site, Cr is bonded to five equivalent As atoms to form a mixture of distorted edge and corner-sharing CrAs5 square pyramids. There are one shorter (2.44 Å) and four longer (2.54 Å) Cr–As bond lengths. In the second Cr site, Cr is bonded in a 12-coordinate geometry to four equivalent As atoms. All Cr–As bond lengths are 2.51 Å. As is bonded in a 9-coordinate geometry to nine Cr atoms.

36 MATERIALS SCIENCE↗

Materials Data on Be2Cr by Materials Project

Be2Cr is Hexagonal Laves structured and crystallizes in the hexagonal P6_3/mmc space group. The structure is three-dimensional. there are two inequivalent Be sites. In the first Be site, Be is bonded to six Be and six equivalent Cr atoms to form a mixture of edge, face, and corner-sharing BeBe6Cr6 cuboctahedra. There are a spread of Be–Be bond distances ranging from 2.06–2.14 Å. There are two shorter (2.45 Å) and four longer (2.47 Å) Be–Cr bond lengths. In the second Be site, Be is bonded to six equivalent Be and six equivalent Cr atoms to form a mixture of edge, face, and corner-sharing BeBe6Cr6 cuboctahedra. All Be–Cr bond lengths are 2.46 Å. Cr is bonded in a 12-coordinate geometry to twelve Be and four equivalent Cr atoms. There are three shorter (2.56 Å) and one longer (2.62 Å) Cr–Cr bond lengths.

36 MATERIALS SCIENCE↗

Materials Data on Cr4P9O32 by Materials Project

Cr4P9O32 crystallizes in the tetragonal P-42_1c space group. The structure is three-dimensional. Cr+4.75+ is bonded to six O2- atoms to form CrO6 octahedra that share corners with six PO4 tetrahedra. There are a spread of Cr–O bond distances ranging from 1.92–1.96 Å. There are three inequivalent P5+ sites. In the first P5+ site, P5+ is bonded to four O2- atoms to form PO4 tetrahedra that share corners with two equivalent CrO6 octahedra and a cornercorner with one PO4 tetrahedra. The corner-sharing octahedra tilt angles range from 43–44°. There are a spread of P–O bond distances ranging from 1.51–1.61 Å. In the second P5+ site, P5+ is bonded to four O2- atoms to form PO4 tetrahedra that share corners with three equivalent CrO6 octahedra and a cornercorner with one PO4 tetrahedra. The corner-sharing octahedra tilt angles range from 28–48°. There are a spread of P–O bond distances ranging from 1.52–1.60 Å. In the third P5+ site, P5+ is bonded to four equivalent O2- atoms to form PO4 tetrahedra that share corners with four equivalent CrO6 octahedra. The corner-sharing octahedral tilt angles are 41°. All P–O bond lengths are 1.55 Å. There are eight inequivalent O2- sites. In the first O2- site, O2- is bonded in a bent 150 degrees geometry to one Cr+4.75+ and one P5+ atom. In the second O2- site, O2- is bonded in a distorted bent 120 degrees geometry to one Cr+4.75+ and one P5+ atom. In the third O2- site, O2- is bonded in a bent 150 degrees geometry to one Cr+4.75+ and one P5+ atom. In the fourth O2- site, O2- is bonded in a distorted bent 150 degrees geometry to one Cr+4.75+ and one P5+ atom. In the fifth O2- site, O2- is bonded in a distorted bent 150 degrees geometry to one Cr+4.75+ and one P5+ atom. In the sixth O2- site, O2- is bonded in a distorted bent 120 degrees geometry to two P5+ atoms. In the seventh O2- site, O2- is bonded in a distorted bent 150 degrees geometry to one Cr+4.75+ and one P5+ atom. In the eighth O2- site, O2- is bonded in a single-bond geometry to one P5+ atom.

36 MATERIALS SCIENCE↗

Materials Data on Dy(CrS2)3 by Materials Project

Dy(CrS2)3 crystallizes in the orthorhombic Pmn2_1 space group. The structure is three-dimensional. there are three inequivalent Dy3+ sites. In the first Dy3+ site, Dy3+ is bonded in a 8-coordinate geometry to eight S2- atoms. There are a spread of Dy–S bond distances ranging from 2.80–3.07 Å. In the second Dy3+ site, Dy3+ is bonded in a 8-coordinate geometry to eight S2- atoms. There are a spread of Dy–S bond distances ranging from 2.78–3.03 Å. In the third Dy3+ site, Dy3+ is bonded in a 8-coordinate geometry to eight S2- atoms. There are a spread of Dy–S bond distances ranging from 2.79–2.87 Å. There are eight inequivalent Cr3+ sites. In the first Cr3+ site, Cr3+ is bonded to six S2- atoms to form a mixture of edge and corner-sharing CrS6 octahedra. The corner-sharing octahedra tilt angles range from 51–56°. There are a spread of Cr–S bond distances ranging from 2.36–2.56 Å. In the second Cr3+ site, Cr3+ is bonded to six S2- atoms to form a mixture of edge and corner-sharing CrS6 octahedra. The corner-sharing octahedra tilt angles range from 49–60°. There are a spread of Cr–S bond distances ranging from 2.32–2.48 Å. In the third Cr3+ site, Cr3+ is bonded to six S2- atoms to form a mixture of edge and corner-sharing CrS6 octahedra. The corner-sharing octahedra tilt angles range from 47–59°. There are a spread of Cr–S bond distances ranging from 2.37–2.48 Å. In the fourth Cr3+ site, Cr3+ is bonded to six S2- atoms to form a mixture of edge and corner-sharing CrS6 octahedra. The corner-sharing octahedra tilt angles range from 50–59°. There are a spread of Cr–S bond distances ranging from 2.40–2.43 Å. In the fifth Cr3+ site, Cr3+ is bonded to six S2- atoms to form a mixture of edge and corner-sharing CrS6 octahedra. The corner-sharing octahedra tilt angles range from 49–59°. There are a spread of Cr–S bond distances ranging from 2.36–2.49 Å. In the sixth Cr3+ site, Cr3+ is bonded to six S2- atoms to form a mixture of edge and corner-sharing CrS6 octahedra. The corner-sharing octahedra tilt angles range from 50–60°. There are a spread of Cr–S bond distances ranging from 2.36–2.53 Å. In the seventh Cr3+ site, Cr3+ is bonded to six S2- atoms to form a mixture of edge and corner-sharing CrS6 octahedra. The corner-sharing octahedra tilt angles range from 48–58°. There are a spread of Cr–S bond distances ranging from 2.34–2.58 Å. In the eighth Cr3+ site, Cr3+ is bonded to six S2- atoms to form a mixture of edge and corner-sharing CrS6 octahedra. The corner-sharing octahedra tilt angles range from 47–60°. There are a spread of Cr–S bond distances ranging from 2.37–2.44 Å. There are sixteen inequivalent S2- sites. In the first S2- site, S2- is bonded in a 5-coordinate geometry to two Dy3+ and three Cr3+ atoms. In the second S2- site, S2- is bonded in a 3-coordinate geometry to three Cr3+ atoms. In the third S2- site, S2- is bonded in a distorted trigonal planar geometry to three Cr3+ atoms. In the fourth S2- site, S2- is bonded in a 5-coordinate geometry to two Dy3+ and three Cr3+ atoms. In the fifth S2- site, S2- is bonded in a 5-coordinate geometry to two equivalent Dy3+ and three Cr3+ atoms. In the sixth S2- site, S2- is bonded in a 5-coordinate geometry to two equivalent Dy3+ and three Cr3+ atoms. In the seventh S2- site, S2- is bonded in a 3-coordinate geometry to three Cr3+ atoms. In the eighth S2- site, S2- is bonded to two equivalent Dy3+ and three Cr3+ atoms to form distorted SDy2Cr3 square pyramids that share corners with six SDy2Cr3 trigonal bipyramids, corners with four equivalent SDyCr3 trigonal pyramids, edges with two equivalent SDy2Cr3 trigonal bipyramids, and edges with four SDyCr3 trigonal pyramids. In the ninth S2- site, S2- is bonded to one Dy3+ and three Cr3+ atoms to form distorted SDyCr3 trigonal pyramids that share a cornercorner with one SDy2Cr3 trigonal bipyramid, corners with seven SDyCr3 trigonal pyramids, an edgeedge with one SDy2Cr3 square pyramid, an edgeedge with one SDy2Cr3 trigonal bipyramid, and edges with two SDyCr3 trigonal pyramids. In the tenth S2- site, S2- is bonded to one Dy3+ and three Cr3+ atoms to form distorted SDyCr3 trigonal pyramids that share corners with two equivalent SDy2Cr3 square pyramids, corners with two equivalent SDy2Cr3 trigonal bipyramids, corners with five SDyCr3 trigonal pyramids, and edges with three SDy2Cr3 trigonal bipyramids. In the eleventh S2- site, S2- is bonded to one Dy3+ and three Cr3+ atoms to form distorted SDyCr3 trigonal pyramids that share a cornercorner with one SDy2Cr3 trigonal bipyramid, corners with seven SDyCr3 trigonal pyramids, edges with two SDy2Cr3 trigonal bipyramids, and an edgeedge with one SDyCr3 trigonal pyramid. In the twelfth S2- site, S2- is bonded to one Dy3+ and three Cr3+ atoms to form distorted SDyCr3 trigonal pyramids that share corners with two equivalent SDy2Cr3 trigonal bipyramids, corners with five SDyCr3 trigonal pyramids, an edgeedge with one SDy2Cr3 square pyramid, edges with two SDy2Cr3 trigonal bipyramids, and an edgeedge with one SDyCr3 trigonal pyramid. In the thirteenth S2- site, S2- is bonded to one Dy3+ and three Cr3+ atoms to form distorted SDyCr3 trigonal pyramids that share corners with two SDy2Cr3 trigonal bipyramids, corners with eight SDyCr3 trigonal pyramids, an edgeedge with one SDy2Cr3 trigonal bipyramid, and an edgeedge with one SDyCr3 trigonal pyramid. In the fourteenth S2- site, S2- is bonded to two Dy3+ and three Cr3+ atoms to form distorted SDy2Cr3 trigonal bipyramids that share corners with three SDy2Cr3 trigonal bipyramids, corners with three SDyCr3 trigonal pyramids, an edgeedge with one SDy2Cr3 square pyramid, edges with three SDy2Cr3 trigonal bipyramids, and edges with three SDyCr3 trigonal pyramids. In the fifteenth S2- site, S2- is bonded to two Dy3+ and three Cr3+ atoms to form distorted SDy2Cr3 trigonal bipyramids that share a cornercorner with one SDy2Cr3 square pyramid, corners with three SDy2Cr3 trigonal bipyramids, corners with three SDyCr3 trigonal pyramids, edges with three SDy2Cr3 trigonal bipyramids, and edges with three SDyCr3 trigonal pyramids. In the sixteenth S2- site, S2- is bonded to two Dy3+ and three Cr3+ atoms to form distorted SDy2Cr3 trigonal bipyramids that share corners with two equivalent SDy2Cr3 square pyramids, corners with four SDy2Cr3 trigonal bipyramids, corners with two SDyCr3 trigonal pyramids, edges with three SDy2Cr3 trigonal bipyramids, and edges with three SDyCr3 trigonal pyramids.

36 MATERIALS SCIENCE↗

Materials Data on Cr2B by Materials Project

Cr2B is Khatyrkite-like structured and crystallizes in the orthorhombic Fddd space group. The structure is three-dimensional. there are two inequivalent Cr sites. In the first Cr site, Cr is bonded in a 4-coordinate geometry to four equivalent B atoms. There are two shorter (2.19 Å) and two longer (2.20 Å) Cr–B bond lengths. In the second Cr site, Cr is bonded in a 4-coordinate geometry to four equivalent B atoms. There are two shorter (2.19 Å) and two longer (2.20 Å) Cr–B bond lengths. B is bonded in a 10-coordinate geometry to eight Cr and two equivalent B atoms. Both B–B bond lengths are 2.11 Å.

36 MATERIALS SCIENCE↗

Materials Data on Cr2SbTe by Materials Project

Cr2SbTe crystallizes in the hexagonal P-6m2 space group. The structure is three-dimensional. Cr+2.50+ is bonded in a distorted body-centered cubic geometry to two equivalent Cr+2.50+, three equivalent Sb3-, and three equivalent Te2- atoms. There are one shorter (2.30 Å) and one longer (2.55 Å) Cr–Cr bond lengths. All Cr–Sb bond lengths are 2.70 Å. All Cr–Te bond lengths are 2.76 Å. Sb3- is bonded in a 6-coordinate geometry to six equivalent Cr+2.50+ atoms. Te2- is bonded in a 6-coordinate geometry to six equivalent Cr+2.50+ atoms.

36 MATERIALS SCIENCE↗