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At least 145 records · Page 8
All sourcesNASA NTRSDOE OSTI
DOE OSTI2020

Materials Data on Zn(InAu4)3 by Materials Project

Zn(Au4In)3 is beta Cu3Ti-derived structured and crystallizes in the orthorhombic Pmm2 space group. The structure is three-dimensional. there are seven inequivalent Au+0.75- sites. In the first Au+0.75- site, Au+0.75- is bonded in a distorted see-saw-like geometry to eight Au+0.75-, two equivalent Zn2+, and two equivalent In+2.33+ atoms. There are six shorter (2.95 Å) and two longer (3.10 Å) Au–Au bond lengths. Both Au–Zn bond lengths are 2.94 Å. Both Au–In bond lengths are 2.92 Å. In the second Au+0.75- site, Au+0.75- is bonded in a distorted see-saw-like geometry to eight Au+0.75- and four In+2.33+ atoms. There are four shorter (2.96 Å) and four longer (3.05 Å) Au–Au bond lengths. There are two shorter (2.95 Å) and two longer (2.97 Å) Au–In bond lengths. In the third Au+0.75- site, Au+0.75- is bonded in a distorted see-saw-like geometry to eight Au+0.75-, one Zn2+, and three In+2.33+ atoms. There are a spread of Au–Au bond distances ranging from 2.92–3.08 Å. The Au–Zn bond length is 2.86 Å. There are two shorter (2.97 Å) and one longer (3.00 Å) Au–In bond lengths. In the fourth Au+0.75- site, Au+0.75- is bonded to eight Au+0.75-, two equivalent Zn2+, and two equivalent In+2.33+ atoms to form distorted AuZn2In2Au8 cuboctahedra that share corners with four equivalent ZnAu12 cuboctahedra, corners with ten AuIn4Au8 cuboctahedra, edges with four AuZn2In2Au8 cuboctahedra, edges with six InAu12 cuboctahedra, faces with two equivalent ZnAu12 cuboctahedra, faces with two equivalent InAu12 cuboctahedra, and faces with six AuZn2In2Au8 cuboctahedra. There are a spread of Au–Au bond distances ranging from 2.88–2.98 Å. There are one shorter (3.02 Å) and one longer (3.05 Å) Au–Zn bond lengths. Both Au–In bond lengths are 2.95 Å. In the fifth Au+0.75- site, Au+0.75- is bonded to eight Au+0.75- and four In+2.33+ atoms to form distorted AuIn4Au8 cuboctahedra that share corners with four equivalent InAu12 cuboctahedra, corners with ten AuZn2In2Au8 cuboctahedra, edges with two equivalent ZnAu12 cuboctahedra, edges with four AuIn4Au8 cuboctahedra, edges with four equivalent InAu12 cuboctahedra, faces with four InAu12 cuboctahedra, and faces with ten AuZn2In2Au8 cuboctahedra. There are two shorter (2.96 Å) and one longer (2.98 Å) Au–Au bond lengths. There are a spread of Au–In bond distances ranging from 2.94–3.07 Å. In the sixth Au+0.75- site, Au+0.75- is bonded in a 12-coordinate geometry to eight Au+0.75-, two equivalent Zn2+, and two equivalent In+2.33+ atoms. There are one shorter (2.82 Å) and one longer (2.98 Å) Au–Au bond lengths. Both Au–Zn bond lengths are 2.90 Å. There are one shorter (3.05 Å) and one longer (3.08 Å) Au–In bond lengths. In the seventh Au+0.75- site, Au+0.75- is bonded to eight Au+0.75- and four In+2.33+ atoms to form distorted AuIn4Au8 cuboctahedra that share corners with four equivalent AuIn4Au8 cuboctahedra, corners with four equivalent InAu12 cuboctahedra, edges with two equivalent ZnAu12 cuboctahedra, edges with four InAu12 cuboctahedra, edges with six AuZn2In2Au8 cuboctahedra, faces with four InAu12 cuboctahedra, and faces with eleven AuZn2In2Au8 cuboctahedra. The Au–Au bond length is 2.95 Å. There are a spread of Au–In bond distances ranging from 2.94–3.06 Å. Zn2+ is bonded to twelve Au+0.75- atoms to form ZnAu12 cuboctahedra that share corners with two equivalent InAu12 cuboctahedra, corners with eight equivalent AuZn2In2Au8 cuboctahedra, edges with two equivalent ZnAu12 cuboctahedra, edges with four equivalent InAu12 cuboctahedra, edges with eight AuIn4Au8 cuboctahedra, faces with two equivalent ZnAu12 cuboctahedra, faces with four equivalent AuZn2In2Au8 cuboctahedra, and faces with four equivalent InAu12 cuboctahedra. There are two inequivalent In+2.33+ sites. In the first In+2.33+ site, In+2.33+ is bonded to twelve Au+0.75- atoms to form InAu12 cuboctahedra that share corners with two equivalent ZnAu12 cuboctahedra, corners with eight equivalent AuIn4Au8 cuboctahedra, edges with six InAu12 cuboctahedra, edges with eight AuZn2In2Au8 cuboctahedra, faces with six InAu12 cuboctahedra, and faces with eight AuIn4Au8 cuboctahedra. In the second In+2.33+ site, In+2.33+ is bonded to twelve Au+0.75- atoms to form InAu12 cuboctahedra that share corners with two equivalent InAu12 cuboctahedra, corners with four equivalent AuIn4Au8 cuboctahedra, edges with two equivalent ZnAu12 cuboctahedra, edges with four InAu12 cuboctahedra, edges with ten AuZn2In2Au8 cuboctahedra, faces with two equivalent ZnAu12 cuboctahedra, faces with four InAu12 cuboctahedra, and faces with six AuZn2In2Au8 cuboctahedra.

36 MATERIALS SCIENCE↗
DOE OSTI2022

Thermodynamic modeling of the Pd–Zn system with uncertainty quantification and its implication to tailor catalysts

Pd–Zn intermetallic catalysts show encouraging combinations of activity and selectivity on well-defined active site ensembles. Thermodynamic description of the Pd–Zn system, delineating phase boundaries and enumerating site occupancies within intermediate alloy phases, is essential to determining the ensembles of Pd–Zn atoms as a function of composition and temperature. Combining the present extensive first-principles calculations based on density functional theory (DFT) and available experimental data, the Pd–Zn system was remodeled using the CALculation of PHAse Diagrams (CALPHAD) approach. High throughput modeling tools with uncertainty quantification, i.e., ESPEI and PyCalphad, were incorporated in the phase analysis. Here, the site occupancies across the γ phase composition region were given special attention. A four-sublattice model was used for the γ phase owing to its four Wyckoff positions, i.e., the outer tetrahedral (OT) site 8c, the inner tetrahedral (IT) site 8c, the octahedral (OH) site 12e, and the cuboctahedral (CO) site 24g. The site fractions of Pd and Zn calculated from the present thermodynamic model show the occupancy preference of Pd in the OT and OH sublattices in agreement with experimental observations. The force constants obtained from DFT-based phonon calculations further supports the tendency of Pd occupying the OH sublattice compared with the IT and CO sublattice. The catalytic ensembles changing from Pd monomers (Pd 1 ) to trimers (Pd 3 ) on the surface of γ phase are attributed to the increase of Pd occupancy in the OH sublattice.

36 MATERIALS SCIENCE↗
DOE OSTI2024

Suppressing metal corrosion through identification of optimal crystallographic plane for Zn batteries

Direct use of metals as battery anodes could significantly boost the energy density, but suffers from limited cycling. To make the batteries more sustainable, one strategy is mitigating the propensity for metals to form random morphology during plating through orientation regulation, e.g., hexagonal Zn platelets locked horizontally by epitaxial electrodeposition or vertically aligned through Zn/electrolyte interface modulation. Current strategies center around obtaining (002) faceted deposition due to its minimum surface energy. Here, benefiting from the capability of preparing a library of faceted monocrystalline Zn anodes and controlling the orientation of Zn platelet deposits, we challenge this conventional belief. We show that while monocrystalline (002) faceted Zn electrode with horizontal epitaxy indeed promises the highest critical current density, the (100) faceted electrode with vertically aligned deposits is the most important one in suppressing Zn metal corrosion and promising the best reversibility. Such uniqueness results from the lowest electrochemical surface area of (100) faceted electrode, which intrinsically builds upon the surface atom diffusion barrier and the orientation of the pallets. These new findings based on monocrystalline anodes advance the fundamental understanding of electrodeposition process for sustainable metal batteries and provide a paradigm to explore the processing–structure–property relationships of metal electrodes.

25 ENERGY STORAGE↗
DOE OSTI2020

Materials Data on Zn by Materials Project

Zn is Magnesium structured and crystallizes in the hexagonal P6_3/mmc space group. The structure is three-dimensional. Zn is bonded to twelve equivalent Zn atoms to form a mixture of edge, face, and corner-sharing ZnZn12 cuboctahedra. There are six shorter (2.63 Å) and six longer (3.01 Å) Zn–Zn bond lengths.

36 MATERIALS SCIENCE↗
DOE OSTI2024

Effect of Zn Addition on Phase Evolution in AlCrFeCoNiZn High–Entropy Alloy

The addition of Zn to AlCrFeCoNi high-entropy alloy (HEA) poses intriguing questions as to how it would affect phase evolution. Herein, the phase evolution in AlCrFeCoNiZn is studied using a combination of experimental techniques (X-ray diffraction, scanning electron microscopy, energy-dispersive spectroscopy, and differential scanning calorimetry) and computational (density-functional theory [DFT], calculation of phase diagrams, and machine-learning) methods. Mechanically alloyed and spark-plasma-sintered AlCrFeCoNiZn assumes a metastable single-phase, body-centered-cubic (BCC) structure that undergoes diffusion-controlled phase separation upon subsequent heat treatment to form separate (Al, Cr)-rich, (Fe, Co)-rich, and (Zn, Ni)-rich phases. The formation of (Al, Cr)-rich phase, not reported previously in AlCrFeCoNi-based HEAs, is attributed to strong clustering tendency of Cr–Zn and Cr–Ni pairs, combined with the strong ordering of Zn–Ni pair, driving out Cr that in turn combines with Al to form a (Al, Cr)-rich phase. In the DFT results, the formation of thermodynamically stable L1 2 phase is shown wherein Cr–Fe–Zn [Al–Ni-Co] preferably occupy1a (000) [3c (0 ½ ½)] positions. Furthermore, the sluggish diffusional transformation to L1 2 phase from BCC precursors is attributed to the small stacking-fault energy of AlCrFeCoNiZn. The equilibrated HEA exhibits a high microhardness of 8.24 GPa with an elastic modulus of 184 GPa.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Reversible (De)Intercalation of Hydrated Zn 2+ in Mg 2+ -Stabilized V 2 O 5 Nanobelts with High Areal Capacity

The rechargeable aqueous zinc ion battery (ZIB) is regarded as one of the most promising candidates for large-scale energy storage applications due to its low-cost and eco-friendly properties. However, the development of a suitable cathode operating with high areal capacity and uncovering the relevant reaction mechanisms remain challenging. Herein, the application of Mg 0.26 V 2 O 5 ∙0.73H 2 O (MVO) nanobelts as a ZIB cathode is demonstrated. In situ FT-IR reveals the shift of OH stretching from 3350 cm -1 to 3200 cm -1 , corresponding to the hydration shell of Zn 2+ , while in situ Raman suggests the interlayer charges creening effect, which would boost the intercalation of hydrated Zn 2+ . Density function theory reveals that the hydrated Zn 2+ can lower the Coulombic repulsion at the electrode-electrolyte interface and circumvents the desolvation penalty of hydrated Zn 2+ during the (de)intercalation process. Additionally, excellent structure stability and large interlayer spacing guarantee the highly reversible (de)intercalation of hydrated Zn 2+ . Therefore, the MVO nanobelts exhibit a high areal capacity of 2.12 mAh cm -2 at 0.05 A g -1 , outstanding cycling stability of 2500 cycles at 10 A g -1 with a mass loading of 5 mg cm -2 . Finally, it is believed that the use of hydrated intercalation charge carriers will boost further studies in other multivalent rechargeable batteries.

25 ENERGY STORAGE↗
DOE OSTI2024

The distinct conditions of atmospheric and underground nuclear tests revealed by Zn isotopic compositions of nuclear debris samples

We analyzed the Zn isotopic compositions of nuclear debris samples from atmospheric and underground nuclear tests. Samples from the site of atmospheric tests exhibit a range of Zn isotopic fractionation (δ 66 Zn JMC-Lyon = 0.23–0.86 ‰) while samples from underground tests exhibit Zn isotopic compositions with minimal variation among samples and from terrestrial igneous rock standards (δ 66 ZnJMC-Lyon = 0.28–0.39 ‰). In conclusion, the larger range of δ 66 Zn JMC-Lyon observed in atmospheric test samples relative to underground test samples is likely the result of the open system characteristics of atmospheric nuclear tests and the closed system characteristics of underground nuclear tests.

38 RADIATION CHEMISTRY, RADIOCHEMISTRY, AND NUCLEA↗
DOE OSTI2021

The subsurface structure of abraded Al–Zn–Mg–Cu alloy

Surface abrasion has been shown to introduce heavy shear stress and produce a few hundred nanometers thick altered surface layer (ASL) on Al alloys. Such ASLs exhibit microstructural changes at room temperature and different corrosion resistance than the underlying substrate. Here, we report how sample dimensions and temperature affect the deformed subsurface microstructure evolution on an abraded Al–Zn–Mg–Cu alloy using transmission electron microscopy (TEM) and atom probe tomography. The ASL microstructure evolves differently in the bulk sample than in the thin TEM specimen. In the freshly abraded ASL, the original η'/η precipitates and grain boundaries were deformed toward the abrasion direction. After 7-day natural aging of the freshly abraded bulk sample, well-defined subgrains formed locally in the ASL, and unusual Al 2 Cu (θ) and Mg x Zn y phases precipitated at the subgrain boundaries. However, during natural aging of this TEM specimen taken from the abraded and aged bulk samples, much faster changes occurred, including the continued formation of subgrains and θ particles in the entire ASL, and the diffusion of Zn atoms out of Mg x Zn y particles to form a Zn particle. On the other hand, no obvious microstructural changes occurred in the ASL during 3-month natural aging of the TEM specimen immediately taken from the freshly abraded sample. Finally, this work advances the understanding of how Al alloy microstructures respond during and following any shear deformation, and complex and unexpected effects of sample dimensions on the behavior.

36 MATERIALS SCIENCE↗
DOE OSTI2023

Precision measurement of 65 Zn electron-capture decays with the KDK coincidence setup

65 Zn is a common calibration source, moreover used as a radioactive tracer in medical and biological studies. In many cases, γ-spectroscopy is a preferred method of 65 Zn standardization, which relies directly on the branching ratio of Jπ( 65 Zn) = 5/2- → Jπ( 65 Cu) = 5/2 - via electron capture (EC*). We measure the relative intensity of this branch to that proceeding directly to the ground state (EC 0 ) using a novel coincidence technique, finding I EC 0/IEC* = 0.9684 ± 0.0018. Re-evaluating the decay scheme of 65 Zn by adopting the commonly evaluated branching ratio of I β+ = 1.4271(7)% we obtain IEC* = (50.08 ± 0.06)%, and I EC 0 = (48.50 ± 0.06)%. The associated 1115 keV gamma intensity agrees with the previously reported NNDC value, and is now accessible with a factor of ~2 increase in precision. Our re-evaluation removes reliance on the deduction of this gamma intensity from numerous measurements, some of which disagree and depend directly on total activity determination. The KDK experimental technique provides a new avenue for verification or updates to the decay scheme of 65 Zn, and is applicable to other isotopes.

73 NUCLEAR PHYSICS AND RADIATION PHYSICS↗
DOE OSTI2023

Tuning the Radius Ratio to Enhance Thermoelectric Properties in the Zintl Compounds AM 2 Sb 2 (A = Ba, Sr; M = Zn, Cd)

Five novel Zintl phase solid solutions in the Ba 1–x Sr x Zn 2–y Cd y Sb 2 (0 ≤ x ≤ 0.13(1); 0 ≤ y ≤ 0.32(2)) system were successfully synthesized by the molten Pb metal-flux method, and the powder X-ray diffraction and single-crystal X-ray diffraction analyses proved that all five title compounds adopted the BaCu 2 S 2 -type phase having the orthorhombic Pnma space group (Z = 4, Pearson code oP20) with five crystallographically independent atomic sites. The previously studied BaCu 2 S 2 -type antimonides demonstrated a limited tolerance for doping in contrast to the CaAl 2 Si 2 -type antimonides. To understand the relatively narrower phase width and limited dopability of the title BaCu 2 S 2 -type phase than the CaAl 2 Si 2 -type phase in the overall Ba 1–x Sr x Zn 2–y Cd y Sb 2 system, the radius ratio of cations and anionic elements r + /r – for two structure types were thoroughly investigated. For the first time, the r + /r – ratio was identified as a critical factor for the phase selectivity: (1) r + /r – > 1 favored the BaCu 2 S 2 -type phase, and (2) r + /r – < 1 favored the CaAl 2 Si 2 -type phase. Further, we also revealed the structural transformation mechanism from the more widely observed CaAl 2 Si 2 -type phase to the title BaCu 2 S 2 -type phase as the relatively larger cationic elements were introduced to the system. A series of DFT calculations using the three hypothetical models indicated that a resonance peak near EF in the density of states curves was descended from the relatively flat band structure at several special symmetry points rationalizing the enhanced Seebeck coefficients of Ba 0.94(1) Sr 0.06 Zn 1.86(3) Cd 0.14 Sb 2 and Ba 0.96(1) Sr 0.04 Zn 1.68(2) Cd 0.32 Sb 2 . Electron localization function analysis rationalized the correlation between the polarity change of anionic Zn/Cd–Sb bonds and the charge carrier mobility on the anionic frameworks. Temperature-dependent thermoelectric properties were studied for the four title compounds, and the results proved that the Sr and Cd doping in the title Ba 1–x Sr x Zn 2–y Cd y Sb 2 system successfully enhanced the ZT values through the increased Seebeck coefficients and the reduced total thermal conductivities.

36 MATERIALS SCIENCE↗
DOE OSTI2025

Semiconducting Zn x Mo 3 S 13 -GO Chalcocarbogel: A High-Capacity and Stable Sulfur-Equivalent Conversion-Based Electrode for Lithium-Ion Batteries

Lithium–sulfur batteries with a sulfur electrode offer a theoretical capacity of ∼1672 mAh g –1 , but rapid capacity loss mainly constrains their practical application. This work introduces a semiconducting and amorphous Zn x Mo 3 S 13 -GO (x = 0.5) chalcocarbogel sulfur-equivalent electrode with superior capacity and stability for lithium-ion batteries (LIBs). The Zn x Mo 3 S 13 -GO is synthesized in solution under ambient conditions, and its local structure contains S–S, M-Q (M = Mo, Zn; Q = S, O), C–S, and Mo–Mo bonding motifs with Mo coordination environment closely related to Mo 3 S 13 anions, as determined by X-ray photoelectron spectroscopy, synchrotron X-ray scattering, X-ray absorption spectroscopy, and ab initio molecular dynamics simulations. The Li/Zn x Mo 3 S 13 -GO cell offers an initial discharge capacity of 1019 mAh g –1 at a rate of C/3. After the activation cycles, the Li/Zn x Mo 3 S 13 -GO cell demonstrates good cycling stability, retaining a discharge capacity of 519.4 mAh g –1 after 250 cycles with ∼99.98% Coulombic efficiency and excellent rate capabilities. Moreover, it provides an initial discharge capacity of ∼574 mAh g –1 and maintains a retention capacity of 279 mAh g –1 at 1C after 625 cycles. The Lewis acidic Zn 2+ ion enhances the Lewis basic polysulfide anchoring ability and reduces the dissolution of polysulfides produced during the redox process through Zn–S covalent interaction, while the semiconducting and amorphous structure of the chalcocarbogel increases the electrical and ionic conductivity. Furthermore, this work highlights chalcocarbogels’ potential for developing high-capacity and stable electrodes for LIBs.

25 ENERGY STORAGE↗
DOE OSTI2025

Determination of Site Occupancy in the M–Pd–Zn (M = Cu, Ag, and Au) γ-Brass Phase by CALculation of PHAse Diagrams Modeling and Rietveld Refinement

The Pd–Zn γ-brass phase provides exciting opportunities for synthesizing site-isolated catalysts with precisely controlled Pd active site ensembles. Introducing a third metallic element into the γ-brass lattice further perturbs the catalytic active site ensembles. Here, in this work, we introduce coinage metallic elements M (M = Cu, Ag, and Au) into the Pd–Zn γ-brass phase and investigate the site occupation factors of each element in the γ-brass lattice. The CALculation of PHAse Diagrams (CALPHAD) modeling approach supported by energetics predicted by the density functional theory and X-ray and neutron diffraction with Rietveld refinement were used to identify the SOF on each Wyckoff site for various M amounts alloyed into the Pd–Zn γ-brass phase. The present analysis unveils the strong preference for Pd occupying the outer tetrahedral (OT) site in the γ-brass lattice, while the coinage metallic elements tend to substitute for Zn on the octahedral (OH) site. The determination of site occupancy in the bulk M–Pd–Zn γ-brass phase provides opportunities to investigate and tailor potential catalytically active site ensembles in the γ-brass phase materials.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Sputtered p-Type Cu x Zn 1– x S Back Contact to CdTe Solar Cells

As thin-film cadmium telluride (CdTe) solar cells gain prominence, one particular challenge is optimizing contacts and their interfaces to transfer charge without losses in efficiency. Back contact recombination is still significant and will prevent CdTe solar technology from reaching its full potential in device efficiency, and transparent back contacts have not been developed for bifacial solar technology or multijunction solar cells. To address these challenges, here we investigate sputtered Cu x Zn 1– x S as a p-type semi-transparent back contact material to thin-film polycrystalline CdTe solar cells at Cu concentrations x = 0.30, 0.45, and 0.60. This material is selected for its high hole conductivity (160–2120 S cm –1 ), wide optical band gap (2.25–2.75 eV), and variable ionization potential (approximately 6–7 eV) that can be aligned to that of CdTe. We report that without device optimization, CdTe solar cells with these Cu x Zn 1– x S back contacts perform as well as control cells with standard ZnTe:Cu back contacts. We observe no reduction in external quantum efficiency, low contact barrier heights of approximately 0.3 eV, and carrier lifetimes on par with those of baseline CdTe. These cells are relatively stable over one year in air, with V OC and efficiency of the x = 0.30 cell decreasing by only 1 and 3%, respectively. Using scanning electron microscopy and scanning transmission electron microscopy to investigate the Cu x Zn 1– x S/CdTe interface, we demonstrate that the Cu x Zn 1– x S layer segregates into a bilayer of Cu-Te-S and Zn-Cd-S, and thermodynamic reaction calculations support these findings. Despite its bilayer formation, the back contact still functions well. This investigation explains some of the physical mechanisms governing the device stack, inspires future work to understand interfacial chemistry and charge transfer, and elicits optimization to achieve higher-efficiency CdTe cells.

14 SOLAR ENERGY↗
DOE OSTI2020

Potentiodynamics of the Zinc and Proton Storage in Disordered Sodium Vanadate for Aqueous Zn-Ion Batteries

A rechargeable Zn-ion battery is a promising aqueous system, where coinsertion of Zn 2+ and H + could address the obstacles of the sluggish ionic transport in cathode materials imposed by multivalent battery chemistry. However, there is a lack of fundamental understanding of this dual-ion transport, especially the potentiodynamics of the storage process. Here, a quantitative analysis of Zn 2+ and H + transport in a disordered sodium vanadate (NaV 3 O 8 ) cathode material has been reported. Collectively, synchrotron X-ray analysis shows that both Zn 2+ and H + storages follow an intercalation storage mechanism in NaV 3 O 8 and proceed in a sequential manner, where intercalations of 0.26 Zn 2+ followed by 0.24 H + per vanadium atom occur during discharging, while reverse dynamics happens during charging. We find that such a unique and synergistic dual-ion sequential storage favors a high capacity (265 mA h g –1 ) and an energy density (221 W h kg –1 ) based on the NaV 3 O 8 cathode and a great cycling life (a capacity retention of 78% after 2000 cycles) in Zn/NaV 3 O 8 full cells.

36 MATERIALS SCIENCE↗
DOE OSTI2024

A Comparison of CdS and Zn(O,S) Buffer Layers in (Ag,Cu)(In,Ga)Se2 Solar Cells

Cu(In,Ga)Se 2 -based solar cells typically use a C dS buffer layer, even though its relatively low bandgap causes parasitic absorption. While alternatives to CdS have been explored in other studies, limited results have been shown for Ag-alloyed CIGS (ACIGS). In this study, ACIGS solar cells with both CdS and Zn(O,S) buffer layers were fabricated and compared for solar cell performance. The Zn(O,S) buffer slightly improved J sc through reduced absorption, although surface optimization is necessary. The Zn(O,S) ACIGS also had improved FF through reduced series resistance and ideality factor, which could be improved further through optimization. However, the Voc in the Zn(O,S) samples was reduced, likely due to increased bulk and front interface recombination. This study shows the promise of Zn(O,S) as a buffer layer in ACIGS solar cells and suggests pathways for further improvement.

absorption↗
DOE OSTI2020

Materials Data on Zn(BIr)2 by Materials Project

Zn(IrB)2 crystallizes in the tetragonal I4/mmm space group. The structure is three-dimensional. Ir is bonded in a 8-coordinate geometry to four equivalent Zn and four equivalent B atoms. All Ir–Zn bond lengths are 2.67 Å. All Ir–B bond lengths are 2.16 Å. Zn is bonded in a body-centered cubic geometry to eight equivalent Ir atoms. B is bonded in a 8-coordinate geometry to four equivalent Ir and four equivalent B atoms. All B–B bond lengths are 2.12 Å.

36 MATERIALS SCIENCE↗
DOE OSTI2020

Materials Data on Zn(CN)2 by Materials Project

Zn(CN)2 is Tungsten structured and crystallizes in the cubic P-43m space group. The structure is zero-dimensional and consists of one Zn(CN)4 cluster and one zinc molecule. In the Zn(CN)4 cluster, Zn2+ is bonded in a tetrahedral geometry to four equivalent N3- atoms. All Zn–N bond lengths are 1.97 Å. C2+ is bonded in a single-bond geometry to one N3- atom. The C–N bond length is 1.17 Å. N3- is bonded in a linear geometry to one Zn2+ and one C2+ atom.

36 MATERIALS SCIENCE↗