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At least 145 records · Page 8

Air quality and health impacts of the 2020 wildfires in California

Abstract Background Wildfires in 2020 ravaged California to set the annual record of area burned to date. Clusters of wildfires in Northern California surrounded the Bay Area covering the skies with smoke and raising the air pollutant concentrations to hazardous levels. This study uses the Fire Inventory from the National Center for Atmospheric Research database and the Community Multiscale Air Quality model to estimate the effects of wildfire emissions on air quality during the period from August 16 to October 28 of 2020. In addition, low-cost sensor data for fine particulate matter (PM 2.5 ) from the PurpleAir network is used to enhance modeled PM 2.5 concentrations. The resulting impacts on ozone and PM 2.5 are used to quantify the health impacts caused by wildfires using the Benefits Mapping and Analysis Program – Community Edition. Results Wildfire activity significantly increased direct PM 2.5 emissions and emissions of PM 2.5 and ozone precursors. Direct PM 2.5 emissions surged up to 38 times compared to an average day. Modeling results indicated that wildfires alone led to a rise in ozone daily maximum 8-h average by up to 10 ppb and exceeded PM 2.5 air quality standards in numerous locations by up to 10 times. While modeled PM 2.5 concentrations were lower than measurements, correcting these with PurpleAir data improved the accuracy. The correction using PurpleAir data increased estimates of wildfire-induced mortality due to PM 2.5 exposure by up to 16%. Conclusions The increased hospital admissions and premature mortality attributed to wildfires were found to be comparable to the health impacts avoided by strategies aimed at meeting ozone and PM2.5 air quality standards. This suggests that widespread wildfire emissions can negate years of efforts dedicated to controlling air pollution. The integration of low-cost sensor data proved invaluable in refining the estimates of health impacts from PM2.5 resulting from wildfires.

54 ENVIRONMENTAL SCIENCES↗

Convergent Manufacturing of Large-Scale Components for Nuclear Applications, via Additive Manufacturing and Powder Metallurgy Hot Isostatic Pressing

Powder metallurgy (PM)–hot isostatic pressing (PM-HIP) has long been recognized as a powerful route for producing fully dense, near net shape metallic components. By consolidating powders under high temperature and pressure, HIP provides isotropic properties, uniform microstructures, and scalability to complex geometries that are vital for sectors such as aerospace, energy, and nuclear power. Yet despite these advantages, the technology has remained constrained by costly trial and error canister fabrication, limitations of conventional forging, and incomplete knowledge about how the canister design influences final part properties. Additive manufacturing (AM), by contrast, thrives on design freedom and geometric flexibility but struggles with speed, scalability, and cost when applied to very large structures. The research presented in this report investigated how a convergent manufacturing approach, combining AM with PM-HIP, can merge the strengths of both technologies, leveraging AM’s flexibility for canister design and HIP’s consolidation capability to deliver reliable, large, and complex parts. The work progressed through three case studies that built on one another in scale and complexity. Small cylindrical canisters fabricated by conventional methods, laser powder bed fusion, and directed energy deposition were filled with stainless steel powders and subjected to HIP. The resulting parts demonstrated near-full density and mechanical properties on par with wrought stainless steel, showing for the first time that AM canisters can be a direct substitute for conventional ones without sacrificing quality. The next step involved a medium-scale, noncentrosymmetric T-valve, which is an enclosed, multibranch geometry that tested the limits of AM + PM-HIP integration. The T-valve achieved predictable shrinkage and uniform densification, confirming feasibility for enclosed designs. However, this study also revealed oxide inclusions and interfacial challenges at the AM + HIP boundary, underscoring the critical importance of controlling interface chemistry and employing robust, in situ strategies, such as melt pool monitoring and thermal monitoring, coupled with nondestructive evaluation techniques such as x-ray computed tomography. Finally, the effort culminated in fabricating a large-scale impeller weighing nearly 2000 lb and spanning 5 ft in diameter. Produced via multirobot wire arc AM and hot isostatic pressed to near-full density, the impeller validated industrial-scale feasibility. Predictive models closely matched experimental shrinkage, tensile properties were spatially uniform across the component, and the AM + PM-HIP interface proved mechanically sound despite the presence of oxide-decorated prior particle boundaries. This large-scale demonstration is a major milestone, showing that hybrid AM + PM‑HIP can reliably deliver components at reactor-relevant scales. Collectively, these studies charted a logical pathway: small-scale work built scientific confidence, medium-scale work highlighted opportunities and challenges, and large-scale work proved industrial impact. The overarching conclusion of this report is that AM + PM-HIP should not be seen as a replacement for forging but as a complementary pathway that provides the US with flexibility, resilience, and new options for manufacturing nuclear-grade components. Looking ahead, several directions emerge as critical to sustaining progress. Predictive modeling must become faster, more accessible, and more accurate, with digital twins and machine learning reducing reliance on trial and error. Powders and alloys must be optimized for HIP, with improved cleanliness, reduced oxides, and tailored chemistries that enhance creep, fatigue, and irradiation resistance. Interfaces between AM and HIP regions must be better engineered through coatings, machining strategies, and surface treatments to mitigate oxide formation and ensure reliable bonding to explore opportunities for HIP of targeted compositional parts, as well as multimaterial HIP cladding applications. Monitoring and nondestructive evaluation need to expand, incorporating multimodal sensors, x-ray computed tomography, and real-time data integration through platforms such as Pelican. At the same time, the pathway to industrial adoption requires techno-economic analysis, machinability studies, and qualification frameworks aligned with industry and regulatory standards. Finally, workforce and academic engagement must be strengthened. Programs that train technicians and engineers for US Navy and US Department of Energy manufacturing challenges should be paired with academic partnerships to support fundamental research, with open sharing of non-export-controlled data to accelerate innovation and build the next generation of experts. In conclusion, this report demonstrates that hybrid AM + PM-HIP is scientifically viable and strategically important. By combining the design agility of AM with the consolidation strength of HIP and embedding modeling, monitoring, and workforce development, this approach provided a transformative new capability for US manufacturing. The path forward is clear: hybrid AM + PM-HIP is not just a promising research direction but is also potentially an industrially relevant pathway that can reshape how nuclear-grade components are designed, qualified, and deployed.

36 MATERIALS SCIENCE↗

Using Low-Cost Measurement Systems to Investigate Air Quality: A Case Study in Palapye, Botswana

Exposure to particulate air pollution is a major cause of mortality and morbidity worldwide. In developing countries, the combustion of solid fuels is widely used as a source of energy, and this process can produce exposure to harmful levels of particulate matter with diameters smaller than 2.5 microns (PM 2.5 ). However, as countries develop, solid fuel may be replaced by centralized coal combustion, and vehicles burning diesel and gasoline may become common, changing the concentration and composition of PM 2.5 , which ultimately changes the population health effects. Therefore, there is a continuous need for in-situ monitoring of air pollution in developing nations, both to estimate human exposure and to monitor changes in air quality. In this study, we present measurements from a 5-week field experiment in Palapye, Botswana. We used a low-cost, highly portable instrument package to measure surface-based aerosol optical depth (AOD), real-time surface PM 2.5 concentrations using a third-party optical sensor, and time-integrated PM 2.5 concentration and composition by collecting PM 2.5 onto Teflon filters. Furthermore, we employed other low-cost measurements of real-time black carbon and time-integrated ammonia to help interpret the observed PM 2.5 composition and concentration information during the field experiment. We found that the average PM 2.5 concentration (9.5 μg∙m –3 ) was below the World Health Organization (WHO) annual limit, and this concentration closely agrees with estimates from the Global Burden of Disease (GBD) report estimates for this region. Sulfate aerosol and carbonaceous aerosol, likely from coal combustion and biomass burning, respectively, were the main contributors to PM 2.5 by mass (33% and 27% of total PM 2.5 mass, respectively). While these observed concentrations were on average below WHO guidelines, we found that the measurement site experienced higher concentrations of aerosol during first half our measurement period (14.5 μg∙m –3 ), which is classified as "moderately unhealthy" according to the WHO standard.

54 ENVIRONMENTAL SCIENCES↗

Materials Data on Pm3I by Materials Project

Pm3I is Uranium Silicide-like structured and crystallizes in the tetragonal I4/mmm space group. The structure is three-dimensional. there are two inequivalent Pm sites. In the first Pm site, Pm is bonded to four equivalent I atoms to form a mixture of distorted corner and edge-sharing PmI4 cuboctahedra. All Pm–I bond lengths are 3.65 Å. In the second Pm site, Pm is bonded in a square co-planar geometry to four equivalent I atoms. All Pm–I bond lengths are 3.46 Å. I is bonded to twelve Pm atoms to form a mixture of corner, edge, and face-sharing IPm12 cuboctahedra.

36 MATERIALS SCIENCE↗

Materials Data on PmMg2 by Materials Project

Mg2Pm is Cubic Laves structured and crystallizes in the trigonal R32 space group. The structure is three-dimensional. there are two inequivalent Mg sites. In the first Mg site, Mg is bonded to six equivalent Mg and six equivalent Pm atoms to form a mixture of edge, face, and corner-sharing MgPm6Mg6 cuboctahedra. All Mg–Mg bond lengths are 3.05 Å. All Mg–Pm bond lengths are 3.58 Å. In the second Mg site, Mg is bonded to six Mg and six equivalent Pm atoms to form a mixture of edge, face, and corner-sharing MgPm6Mg6 cuboctahedra. All Mg–Mg bond lengths are 3.06 Å. There are four shorter (3.58 Å) and two longer (3.59 Å) Mg–Pm bond lengths. Pm is bonded in a 12-coordinate geometry to twelve Mg and four equivalent Pm atoms. All Pm–Pm bond lengths are 3.74 Å.

36 MATERIALS SCIENCE↗

An Initial Evaluation of the Elevated-Temperature Cyclic Properties of Optimized 316H Stainless Steel Fabricated by Powder Metallurgy Hot Isostatic Pressing

Powder metallurgy hot isostatic pressing (PM-HIP) is a mature advanced manufacturing technology, which can consolidate metallic powder under high temperature and pressure to generate near-net shape components. This process can lower production costs and reduce component lead times for nuclear reactor construction and can be readily deployed in the near term for microreactor components because of their smaller size. The purpose of this work is to continue the evaluation of elevated-temperature cyclic material properties for PM-HIP 316H stainless steel. Prior scoping results have shown that the commercially procured PM-HIP stainless-steel materials have reduced creep-fatigue performance compared to wrought 316 stainless steels. To better understand how PM-HIP processed material properties compare to traditional manufacturing methods, additional billets of PM-HIP 316H stainless steel were procured and tested. This testing is necessary to understand how elevated-temperature properties are influenced by the PM-HIP process and what data are needed for incorporating PM HIP 316H into the American Society of Mechanical Engineers Boiler Pressure Vessel Code, Section III, Division 5 for high temperature reactor construction. Specifically, an additional PM-HIP 316H stainless steel billet with lower oxygen and nitrogen concentrations was fabricated by the Nuclear Advanced Manufacturing Research Centre of the United Kingdom and tested to understand if elevated-temperature cyclic properties can be improved. The creep-fatigue resistance of the material from this new billet did not show appreciable improvement compared to prior testing.

11 NUCLEAR FUEL CYCLE AND FUEL MATERIALS↗

A comparison of wrought and powder metallurgical FeCrAl claddings under simulated LWR accident transients

Iron-chromium-aluminum (FeCrAl) alloys are potential accident tolerant fuel (ATF) cladding candidates for light-water reactors but are difficult to fabricate as thin-walled tubes via conventional cast-and-wrought routes. Powder metallurgy (PM) offers a manufacturing alternative with improved compositional control, but its transient accident performance has not been directly benchmarked against wrought variants. This study evaluates the burst behavior of commercially developed PM-processed FeCrAl alloys, PM-C26M (Fe-12Cr-6Al-2Mo) and the high precipitate density FA-SMT (Fe-22Cr-5Al-3Mo), under simulated light-water reactor accident transient conditions. Burst testing was conducted using the Severe Accident Test Station with heating rates of 5 °C/s and 50 °C/s and internal pressures ranging from 25 MPa to 100 MPa. PM-C26M reproduced wrought C26M burst behavior within 7–37 °C across the stress range, indicating that PM processing does not compromise transient strength. FA-SMT exhibited markedly higher burst temperatures and reduced heating-rate sensitivity, consistent with its engineered precipitate strengthening. FA-SMT rupture exhibited axial "unzipping" rather than the lateral tearing characteristic of PM- and wrought C26M. Post-test EBSD and fractography indicate that this behavior is strongly correlated with strain-gated intergranular void nucleation associated with the dense precipitate architecture of FA-SMT, a response absent in the comparatively clean PM-C26M matrix and consistent with rupture morphologies reported for oxide-dispersion strengthened (ODS) FeCrAl of similar base-matrix chemistry to PM-C26M. These findings highlight the potential of powder metallurgy as a viable fabrication route for ATF claddings from an accident performance standpoint.

Bell, Sam [ORNL] (ORCID:0000000251905657)↗

Stellar populations and merger rates of brightest cluster galaxies a billion years ago: SDSS MaNGA IFU spectroscopy

ABSTRACT We investigate the spectroscopic properties of 85 brightest cluster galaxies (BCGs) and their companions observed with the SDSS MaNGA integral field unit. Galaxy redshifts are between 0.08 < z < 0.15, allowing for a field-of-view up to 80 × 80 kpc. For the main galaxies: the average age of the BCG cores is 7.66$\, \pm \,$1.36 Gyr with no significant gradient out to $2\, R_ {e}$; the average metallicity of the BCG cores is $[Z/H]=0.23\, \pm \, 0.03$ with a negative gradient of Δ[Z/H]/Δ(R/Re) = –0.14$\, \pm \, 0.09$ which flattens beyond $1.2\, R_ {e}$. Velocity dispersion gradients are mostly flat, but a few positive slopes are seen in the most massive galaxies. Emission lines are present in 12 of the BCGs, most often confined to the central $\sim 2\,$ kpc with emission line ratios well-described by a LINER or AGN excitation source. There are 78 companion galaxies identified and 9 have nebular emission lines that indicate recent star formation. The companions with flux ratios of 4:1 and 20:1 within 30 kpc of their BCG’s core are studied. The companion galaxies have a median age of 7.65$\, \pm \,$1.55 Gyr and are high-metallicity systems, with a median [Z/H] = 0.17 ± 0.07. Close spectroscopic companions with higher merging probabilities have an average merging time of 0.5 ± 0.2 Gyr. The average merger rate is 0.08$\, \pm \, 0.12 \,$ Gyr−1 for 4:1 companions and 0.26$\, \pm \, 0.22 \,$ Gyr−1 for 20:1 companions, allowing for an increase in mass of 2.3$\, \pm \,$3.4 per cent Gyr−1 and 3.5$\, \pm \,$3.2 per cent Gyr−1, respectively.

Edwards, Louise O. V. (ORCID:000000029135997X)↗

Precision measurement of the B0 meson lifetime using B0→J/ψK∗0 decays with the ATLAS detector

A measurement of the B0$$B^{0}$$ meson lifetime using B0→J/ψK∗0$$ B^{0} \rightarrow J/\psi K^{*0} $$ decays in data from 13 TeV$$\text {TeV}$$ proton–proton collisions with an integrated luminosity of 140fb-1$$ 140~\mathrm {fb^{-1}} $$ recorded by the ATLAS detector at the LHC is presented. The measured effective lifetime is τ=1.5053±0.0012(stat.)±0.0035(syst.)ps.$$ \tau = 1.5053\pm 0.0012~\mathrm {(stat.)} \pm 0.0035~\mathrm {(syst.)~ps}. $$The average decay width extracted from the effective lifetime, using parameters from external sources, is Γd=0.6639±0.0005(stat.)±0.0016(syst.)±0.0038(ext.)ps-1,$$\begin{aligned} \Gamma _d = 0.6639\pm 0.0005~\mathrm {(stat.)} \pm 0.0016~\mathrm {(syst.)}\\ \pm 0.0038~\text {(ext.)} \text {~ps}^{-1}, \end{aligned}$$where the uncertainties are statistical, systematic and from external sources. The earlier ATLAS measurement of Γs$$\Gamma _s$$ in the Bs0→J/ψϕ$$B^{0}_{s} \rightarrow J/\psi \phi $$ decay was used to derive a value for the ratio of the average decay widths Γd$$\Gamma _d$$ and Γs$$\Gamma _s$$ for B0$$B^{0} $$ and Bs0$$B^{0}_{s} $$ mesons respectively, of ΓdΓs=0.9905±0.0022(stat.)±0.0036(syst.)±0.0057(ext.).$$ \frac{\Gamma _d }{\Gamma _s } = 0.9905\pm 0.0022~\text {(stat.)} \pm 0.0036~\text {(syst.)} \pm 0.0057~\text {(ext.)}. $$The measured lifetime, average decay width and decay width ratio are in agreement with theoretical predictions and with measurements by other experiments. This measurement provides the most precise result of the effective lifetime of the B0$$B^{0}$$ meson to date.

Aad, G↗

Ducted Fuel Injection And Cooled Spray Technologies For Particulate Control In Heavy-duty Diesel Engines (Final Report)

Cooled Spray (CS) and Ducted Fuel Injection (DFI) are in-cylinder technologies for diesel engines that can reduce particulate matter and soot emissions and data has been published showing that these technologies can reduce soot emissions by 75-100% for some engines at some operating conditions. However, little is known about scaling the devices for engine size. Additionally, the performance of either technology over the engine duty cycle has not been explored. This project addresses both of these points through single-cylinder engine investigations. The objectives of this project are to provide details about dimensional scaling of these devices and to demonstrate 75% PM reduction over a range of operating conditions on a single-cylinder engine. Two engines were used for this project: a 125mm bore optically accessible engine at Sandia National Laboratories and a 168mm bore metal engine at Southwest Research Institute. The optical engine was used to study the performance of DFI and CS inserts for a large injector orifice diameter injector that is characteristic of a locomotive engine and to perform scaling studies for DFI. The metal engine was used to perform scaling and alignment studies for CS and to evaluate the technology for both EGR and non-EGR engines over the engine operating map. Modifications were required for both engines to accept the prototype inserts being tested. The optical engine required a new fuel injector, cylinder head and piston so that tests could be run at the pressures and engine speeds required. Additionally, a novel rotating stage was designed for the optical engine to simplify alignment of the modules. The metal engine required a modified cylinder head to accept CS inserts and a modified piston to provide additional space around the fuel injector for the CS inserts. Tests on the optical engine showed that DFI reduces PM emissions for both small injector orifices (0.170mm diameter) and large injector orifices (0.290mm). For high load testing, the DFI modules were not as effective as at low load testing, but it was acknowledged that minimal geometric optimization was performed and more improvements may be possible. Comparing DFI to CS and conventional diesel combustion (CDC), DFI performed better than CS or CDC. The CS geometries used in these studies may not be ideal for that engine and additional modifications likely would improve performance. Tests on the metal engine showed PM reductions as high has 80% at some operating conditions with duty-cycle PM reductions of ~50% for EGR and non-EGR configurations. The CS testing on the metal engine showed that chamfering of the fuel passage inlet either through hydro-erosion or mechanical grinding provided significant improvements in the PM reduction capabilities of the insert. Additionally, alignment sensitivities were explored and the data show that the tolerance to misalignment is approximately 0.05 to 0.1mm for the inserts that were studied here. Air-fuel ratio was shown to be important in the effectiveness of the CS inserts. In several tests, it was shown that the CS inserts are more effective at reducing the PM for high-AFR operating conditions compared to low AFR conditions. In summary, multiple designs were evaluated on both engines. It was found that for the conditions and configurations studied here, a fuel passage diameter of ~2.5mm performed best overall. Significant duty-cycle PM reductions are possible using these technologies and sensitivities to AFR, alignment fuel passage diameter and inlet fuel passage shaping were explored and are reported here. More PM reduction may be possible with improved geometric design and attention to alignment practices.

02 PETROLEUM↗

Materials Data on PmHo3 by Materials Project

Ho3Pm is beta Cu3Ti-like structured and crystallizes in the hexagonal P6_3/mmc space group. The structure is three-dimensional. there are three inequivalent Ho sites. In the first Ho site, Ho is bonded to eight Ho and four equivalent Pm atoms to form HoPm4Ho8 cuboctahedra that share corners with four equivalent PmHo12 cuboctahedra, corners with fourteen HoPm4Ho8 cuboctahedra, edges with six equivalent PmHo12 cuboctahedra, edges with twelve HoPm4Ho8 cuboctahedra, faces with four equivalent PmHo12 cuboctahedra, and faces with sixteen HoPm4Ho8 cuboctahedra. There are a spread of Ho–Ho bond distances ranging from 3.53–3.66 Å. There are two shorter (3.54 Å) and two longer (3.63 Å) Ho–Pm bond lengths. In the second Ho site, Ho is bonded to eight Ho and four equivalent Pm atoms to form HoPm4Ho8 cuboctahedra that share corners with four equivalent PmHo12 cuboctahedra, corners with fourteen HoPm4Ho8 cuboctahedra, edges with six equivalent PmHo12 cuboctahedra, edges with twelve HoPm4Ho8 cuboctahedra, faces with four equivalent PmHo12 cuboctahedra, and faces with sixteen HoPm4Ho8 cuboctahedra. There are a spread of Ho–Ho bond distances ranging from 3.53–3.66 Å. There are two shorter (3.54 Å) and two longer (3.63 Å) Ho–Pm bond lengths. In the third Ho site, Ho is bonded to eight Ho and four equivalent Pm atoms to form HoPm4Ho8 cuboctahedra that share corners with four equivalent PmHo12 cuboctahedra, corners with fourteen HoPm4Ho8 cuboctahedra, edges with six equivalent PmHo12 cuboctahedra, edges with twelve HoPm4Ho8 cuboctahedra, faces with four equivalent PmHo12 cuboctahedra, and faces with sixteen HoPm4Ho8 cuboctahedra. There are two shorter (3.54 Å) and two longer (3.63 Å) Ho–Pm bond lengths. Pm is bonded to twelve Ho atoms to form PmHo12 cuboctahedra that share corners with six equivalent PmHo12 cuboctahedra, corners with twelve HoPm4Ho8 cuboctahedra, edges with eighteen HoPm4Ho8 cuboctahedra, faces with eight equivalent PmHo12 cuboctahedra, and faces with twelve HoPm4Ho8 cuboctahedra.

36 MATERIALS SCIENCE↗

Materials Data on Pm3Si by Materials Project

Pm3Si is Uranium Silicide structured and crystallizes in the cubic Pm-3m space group. The structure is three-dimensional. Pm is bonded to eight equivalent Pm and four equivalent Si atoms to form distorted PmPm8Si4 cuboctahedra that share corners with twelve equivalent PmPm8Si4 cuboctahedra, edges with eight equivalent SiPm12 cuboctahedra, edges with sixteen equivalent PmPm8Si4 cuboctahedra, faces with four equivalent SiPm12 cuboctahedra, and faces with fourteen equivalent PmPm8Si4 cuboctahedra. All Pm–Pm bond lengths are 3.36 Å. All Pm–Si bond lengths are 3.36 Å. Si is bonded to twelve equivalent Pm atoms to form SiPm12 cuboctahedra that share corners with twelve equivalent SiPm12 cuboctahedra, edges with twenty-four equivalent PmPm8Si4 cuboctahedra, faces with six equivalent SiPm12 cuboctahedra, and faces with twelve equivalent PmPm8Si4 cuboctahedra.

36 MATERIALS SCIENCE↗

Materials Data on Pm3Tl by Materials Project

Pm3Tl is Uranium Silicide structured and crystallizes in the cubic Pm-3m space group. The structure is three-dimensional. Pm is bonded to eight equivalent Pm and four equivalent Tl atoms to form distorted PmPm8Tl4 cuboctahedra that share corners with twelve equivalent PmPm8Tl4 cuboctahedra, edges with eight equivalent TlPm12 cuboctahedra, edges with sixteen equivalent PmPm8Tl4 cuboctahedra, faces with four equivalent TlPm12 cuboctahedra, and faces with fourteen equivalent PmPm8Tl4 cuboctahedra. All Pm–Pm bond lengths are 3.51 Å. All Pm–Tl bond lengths are 3.51 Å. Tl is bonded to twelve equivalent Pm atoms to form TlPm12 cuboctahedra that share corners with twelve equivalent TlPm12 cuboctahedra, edges with twenty-four equivalent PmPm8Tl4 cuboctahedra, faces with six equivalent TlPm12 cuboctahedra, and faces with twelve equivalent PmPm8Tl4 cuboctahedra.

36 MATERIALS SCIENCE↗

Materials Data on Pm3Y by Materials Project

Pm3Y is Uranium Silicide structured and crystallizes in the cubic Pm-3m space group. The structure is three-dimensional. Pm is bonded to eight equivalent Pm and four equivalent Y atoms to form PmPm8Y4 cuboctahedra that share corners with twelve equivalent PmPm8Y4 cuboctahedra, edges with eight equivalent YPm12 cuboctahedra, edges with sixteen equivalent PmPm8Y4 cuboctahedra, faces with four equivalent YPm12 cuboctahedra, and faces with fourteen equivalent PmPm8Y4 cuboctahedra. All Pm–Pm bond lengths are 3.63 Å. All Pm–Y bond lengths are 3.63 Å. Y is bonded to twelve equivalent Pm atoms to form YPm12 cuboctahedra that share corners with twelve equivalent YPm12 cuboctahedra, edges with twenty-four equivalent PmPm8Y4 cuboctahedra, faces with six equivalent YPm12 cuboctahedra, and faces with twelve equivalent PmPm8Y4 cuboctahedra.

36 MATERIALS SCIENCE↗

Materials Data on PmPu3 by Materials Project

Pu3Pm is beta Cu3Ti-like structured and crystallizes in the hexagonal P6_3/mmc space group. The structure is three-dimensional. there are three inequivalent Pu sites. In the first Pu site, Pu is bonded to eight Pu and four equivalent Pm atoms to form PuPm4Pu8 cuboctahedra that share corners with four equivalent PmPu12 cuboctahedra, corners with fourteen PuPm4Pu8 cuboctahedra, edges with six equivalent PmPu12 cuboctahedra, edges with twelve PuPm4Pu8 cuboctahedra, faces with four equivalent PmPu12 cuboctahedra, and faces with sixteen PuPm4Pu8 cuboctahedra. There are a spread of Pu–Pu bond distances ranging from 3.39–3.57 Å. There are two shorter (3.46 Å) and two longer (3.48 Å) Pu–Pm bond lengths. In the second Pu site, Pu is bonded to eight Pu and four equivalent Pm atoms to form PuPm4Pu8 cuboctahedra that share corners with four equivalent PmPu12 cuboctahedra, corners with fourteen PuPm4Pu8 cuboctahedra, edges with six equivalent PmPu12 cuboctahedra, edges with twelve PuPm4Pu8 cuboctahedra, faces with four equivalent PmPu12 cuboctahedra, and faces with sixteen PuPm4Pu8 cuboctahedra. All Pu–Pu bond lengths are 3.40 Å. There are two shorter (3.46 Å) and two longer (3.48 Å) Pu–Pm bond lengths. In the third Pu site, Pu is bonded to eight Pu and four equivalent Pm atoms to form PuPm4Pu8 cuboctahedra that share corners with four equivalent PmPu12 cuboctahedra, corners with fourteen PuPm4Pu8 cuboctahedra, edges with six equivalent PmPu12 cuboctahedra, edges with twelve PuPm4Pu8 cuboctahedra, faces with four equivalent PmPu12 cuboctahedra, and faces with sixteen PuPm4Pu8 cuboctahedra. There are two shorter (3.46 Å) and two longer (3.48 Å) Pu–Pm bond lengths. Pm is bonded to twelve Pu atoms to form PmPu12 cuboctahedra that share corners with six equivalent PmPu12 cuboctahedra, corners with twelve PuPm4Pu8 cuboctahedra, edges with eighteen PuPm4Pu8 cuboctahedra, faces with eight equivalent PmPu12 cuboctahedra, and faces with twelve PuPm4Pu8 cuboctahedra.

36 MATERIALS SCIENCE↗

Materials Data on Pm3Er by Materials Project

ErPm3 is Uranium Silicide structured and crystallizes in the cubic Pm-3m space group. The structure is three-dimensional. Er is bonded to twelve equivalent Pm atoms to form ErPm12 cuboctahedra that share corners with twelve equivalent ErPm12 cuboctahedra, edges with twenty-four equivalent PmPm8Er4 cuboctahedra, faces with six equivalent ErPm12 cuboctahedra, and faces with twelve equivalent PmPm8Er4 cuboctahedra. All Er–Pm bond lengths are 3.62 Å. Pm is bonded to four equivalent Er and eight equivalent Pm atoms to form PmPm8Er4 cuboctahedra that share corners with twelve equivalent PmPm8Er4 cuboctahedra, edges with eight equivalent ErPm12 cuboctahedra, edges with sixteen equivalent PmPm8Er4 cuboctahedra, faces with four equivalent ErPm12 cuboctahedra, and faces with fourteen equivalent PmPm8Er4 cuboctahedra. All Pm–Pm bond lengths are 3.62 Å.

36 MATERIALS SCIENCE↗

Materials Data on LiPm3 by Materials Project

LiPm3 is Uranium Silicide structured and crystallizes in the cubic Pm-3m space group. The structure is three-dimensional. Li is bonded to twelve equivalent Pm atoms to form LiPm12 cuboctahedra that share corners with twelve equivalent LiPm12 cuboctahedra, edges with twenty-four equivalent PmLi4Pm8 cuboctahedra, faces with six equivalent LiPm12 cuboctahedra, and faces with twelve equivalent PmLi4Pm8 cuboctahedra. All Li–Pm bond lengths are 3.53 Å. Pm is bonded to four equivalent Li and eight equivalent Pm atoms to form PmLi4Pm8 cuboctahedra that share corners with twelve equivalent PmLi4Pm8 cuboctahedra, edges with eight equivalent LiPm12 cuboctahedra, edges with sixteen equivalent PmLi4Pm8 cuboctahedra, faces with four equivalent LiPm12 cuboctahedra, and faces with fourteen equivalent PmLi4Pm8 cuboctahedra. All Pm–Pm bond lengths are 3.53 Å.

36 MATERIALS SCIENCE↗

Materials Data on PmTm3 by Materials Project

Tm3Pm is beta Cu3Ti-like structured and crystallizes in the hexagonal P6_3/mmc space group. The structure is three-dimensional. there are three inequivalent Tm sites. In the first Tm site, Tm is bonded to eight Tm and four equivalent Pm atoms to form TmPm4Tm8 cuboctahedra that share corners with four equivalent PmTm12 cuboctahedra, corners with fourteen TmPm4Tm8 cuboctahedra, edges with six equivalent PmTm12 cuboctahedra, edges with twelve TmPm4Tm8 cuboctahedra, faces with four equivalent PmTm12 cuboctahedra, and faces with sixteen TmPm4Tm8 cuboctahedra. There are a spread of Tm–Tm bond distances ranging from 3.49–3.64 Å. There are two shorter (3.52 Å) and two longer (3.59 Å) Tm–Pm bond lengths. In the second Tm site, Tm is bonded to eight Tm and four equivalent Pm atoms to form TmPm4Tm8 cuboctahedra that share corners with four equivalent PmTm12 cuboctahedra, corners with fourteen TmPm4Tm8 cuboctahedra, edges with six equivalent PmTm12 cuboctahedra, edges with twelve TmPm4Tm8 cuboctahedra, faces with four equivalent PmTm12 cuboctahedra, and faces with sixteen TmPm4Tm8 cuboctahedra. There are a spread of Tm–Tm bond distances ranging from 3.49–3.64 Å. There are two shorter (3.52 Å) and two longer (3.59 Å) Tm–Pm bond lengths. In the third Tm site, Tm is bonded to eight Tm and four equivalent Pm atoms to form TmPm4Tm8 cuboctahedra that share corners with four equivalent PmTm12 cuboctahedra, corners with fourteen TmPm4Tm8 cuboctahedra, edges with six equivalent PmTm12 cuboctahedra, edges with twelve TmPm4Tm8 cuboctahedra, faces with four equivalent PmTm12 cuboctahedra, and faces with sixteen TmPm4Tm8 cuboctahedra. There are two shorter (3.52 Å) and two longer (3.59 Å) Tm–Pm bond lengths. Pm is bonded to twelve Tm atoms to form PmTm12 cuboctahedra that share corners with six equivalent PmTm12 cuboctahedra, corners with twelve equivalent TmPm4Tm8 cuboctahedra, edges with eighteen TmPm4Tm8 cuboctahedra, faces with eight equivalent PmTm12 cuboctahedra, and faces with twelve TmPm4Tm8 cuboctahedra.

36 MATERIALS SCIENCE↗