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At least 73 records · Page 4

Complete β-decay patterns of 142 Cs, 142 Ba, and 142 La determined using total absorption spectroscopy

Background: The β decays of fission products produced in nuclear fuel are important for nuclear energy applications and fundamental science of reactor antineutrinos. In particular, nuclear reactor safety is related to the decay modes of radioactive neutron-rich nuclei, primarily via the emission of γ rays, neutrons, and electrons. Additionally nuclear reactors are the most powerful man-made source of antineutrinos emitted during the β decay of fission products. These antineutrinos are used to inspect fundamental properties of leptons as well as informing reactor operation. However, the majority of data on complex decays of fission products collected in the evaluated nuclear data repositories like Evaluated Nuclear Structure Data File (ENSDF) and Evaluated Nuclear Data Files (ENDF) are based on low-efficiency and often incomplete measurements resulting in questionable reference reactor antineutrino flux predictions, see the analysis by [Nichols, J. Nucl. Sci. Technol. 52, 17 (2015)]. Various assessments like the one done under the auspices of the [Yoshida et al., Assessment of Fission Product Decay Data for Decay Heat Calculations: A report by the Working Party on International Evaluation Co-operation of the Nuclear Energy Agency Nuclear Science Committee (Nuclear Energy Agency, Organization for Economic Co-operation and Development, Paris, France, 2007), Vol. 25], as well as by [Sonzogni, Johnson, and McCutchan, Phys. Rev. C 91, 011301(R) (2015)] and [Dwyer and Langford, Phys. Rev. Lett. 114, 012502 (2015)], list the A = 142 isobars with high cumulative fission yield among the important nuclei where data for reactor decay heat and/or antineutrino production should be verified and/or improved. Purpose: Here, our goal is to improve the quality of β -decay measurements and evaluate the impact of modified decay schemes on reactor decay heat and antineutrino energy spectra, for fission products along the A = 142 isobaric chain. This work is an in depth follow-up on [Rasco et al., Phys. Rev. Lett. 117, 092501 (2016)]. which presented briefly the impact of the corrected decay scheme of 142 Cs . Here, we extend the data to full isobaric decay chain including the daughter nuclei, 142 Ba and 142 La, and present more details on the 142 Cs results. Method: The decays of neutron-rich isobars of mass A = 142 produced by means of proton-induced fission of 238 U were measured using the Modular Total Absorption Spectrometer (MTAS) array on-line at the mass separator and Tandem accelerator at Oak Ridge National Laboratory. Results: The β -decay schemes for 142 Cs and 142 La were modified with respect to the nuclear data repositories. A small β-delayed neutron branching ratio for 142 Cs emitter was remeasured as $0.10^{+5}_{–3}% %. Improved precision on the measured half-lives is reported. Small corrections to the low-energy decay of 142 Ba are made. The β-decay patterns for 142 La and 142 Cs are presented. The decay heat release and cross section for the detection of reactor antineutrinos are deduced and compared to earlier results. Conclusions: The β-feeding pattern for 142 Cs having decay energy value $Q_β$ of over 7 MeV was substantially modified with respect to the current ENSDF entry. Smaller changes were encountered for 142 La, but since this A = 142 isobar also has a large cumulative yield in fission, the changes influence both decay heat and the antineutrino spectra. The previously known β intensities for 142 Ba decay ($Q_β$ value of 2.2 MeV) were verified and slightly modified. Overall, increased decay heat values and lower flux of antineutrinos interacting with matter are presented.

73 NUCLEAR PHYSICS AND RADIATION PHYSICS↗

Crystal structure of dicaesium strontium hexacyanidoferrate(II), Cs 2 Sr[Fe(CN) 6 ], from laboratory X-ray powder data

Ferrocyanides with general formula A I x B II y [Fe(CN) 6 ], where A and B are cations, are thought to accept many substitutions on the A and B positions. In this communication, the synthesis and crystal structure of Cs 2 Sr[Fe(CN) 6 ] are reported. The latter was obtained from K 2 Ba[Fe(CN) 6 ] particles, put in contact with caesium and strontium ions. Hence, a simultaneous ion-exchange mechanism (Cs for K, Sr for Ba) occurs to yield Cs 2 Sr[Fe(CN) 6 ]. The synthesis protocol shows that K 2 BaFe(CN) 6 particles can be used for the simultaneous trapping of radioactive caesium and strontium nuclides in water streams. Cs 2 Sr[Fe(CN) 6 ] adopts the cryolite structure type and is isotypic with the known compound Cs 2 Na[Mn(CN) 6 ] [dicaesium sodium hexacyanidomanganate(III)]. The octahedrally coordinated Sr and Fe sites both are located on inversion centres, and the eightfold-coordinated Cs site on a general position.

Massoni, Nicolas↗

Involvement of DNA-PK(sub cs) in DSB Repair Following Fe-56 Ion Irradiation

When cells are exposed to radiation, cellular lesions are induced in the DNA including double strand breaks (DSBs), single strand breaks and clustered DNA damage, which if not repaired with high fidelity may lead to detrimental biological consequences. Complex DSBs are induced by ionizing radiation and characterized by the presence of base lesions close to the break termini. They are believed to be one of the major causes of the biological effects of IR. The complexity of DSBs increases with the ionization density of the radiation and these complex DSBs are distinct from the damage induced by sparsely ionizing gamma-radiation. It has been hypothesized that complex DSBs produced by heavy ions in space pose problems to the DNA repair machinery. We have used imm uno-cyto-chemical staining of phosphorylated histone H2AX (gamma-H2AX) foci, as a marker of DSBs. We have investigated the formation and loss of gamma-H2AX foci and RAD51 foci (a protein involved in the homologous recombination pathway) in mammalian cells induced by low fluences of low-LET gamma-radiation and high-LET Fe-56 ions (1GeV/n, 151 keV/micron LET). M059J and M059K cells, which are deficient and proficient in DNA-PK(sub cs) activity respectively, were used to examine the role of DNA-PK(sub cs), a key protein in the non-homologous end joining (NHEJ) pathway of DSB repair, along with HF19 human fibroblasts. Followi ng irradiation with Fe-56 ions the rate of repair was slower in M059J cells compared with that in M059K, indicating a role for DNA-PK(sub cs) in the repair of DSB induced by Fe-56 ions. However a small percentage of DSBs induced are rejoined within 5 h although many DSBs still persist up to 24 h. When RAD51 was examined in M059J/K cells, RAD51 foci are visible 24 hours after irradiation in approximately 40% of M059J cells compared with <5% of M059K cells indicating that persistent DSBs or those formed at stalled replication forks recruit RAD51 in DNA-PK(sub cs) deficient cells. Following 1 Gy gamma-radiation the induction of gamma-H2AX foci is similar in M059J and M059K cells. However, the repair rate of DSBs is slower in M059J cells than in M059K as shown previously but faster than seen with DSB induced by 56Fe ions. Vanillin, an inhibitor of DNA-PK(sub cs), reduces significantly the rate of DSB repair in HF19 cells following 1 Gy gamma-radiation but at 0.25 Gy gamma-irradiation the rate of DSB repair is similar in the presence or absence vanillin, thus suggesting the repair of a sub-set of DSBs induced by low dose, low-LET radiation does not require DNA-PK(sub cs). This sub-set of DSBs is formed in lower yield with high LET radiation. T he complexity of DNA DSBs induced by HZE radiation will be discussed in terms of reduced repair efficiency and provide scope to model different sub-classes of DSBs as precursors that may lead to the detrimental health effects of HZE radiation.

O'Neill, Peter↗

The Influence of Alkalinity on the Uptake of Cs{sup +} and Sr{sup 2+} by Cation-substituted Natisites in Sodium-bearing Conditions - 20336

The titanosilicate natisite (Na{sub 2}TiSiO{sub 5}) is a kinetic phase of the mineral sitinakite (Na{sub 2}Ti{sub 2}O{sub 3}SiO{sub 4}.2H{sub 2}O), which is a reference material in the removal of Cs and Sr from radioactive high-level waste. Natisite is disregarded in the literature as a candidate sorbent for Cs and Sr, despite being more thermally stable than sitinakite, which is a critical property for this application. Replacing portion of the Ti in natisite by other metals is believed to enhance natisite sorption properties. In nuclear waste remediation, Cs and Sr are contained in high-salinity liquid wastes that can either be highly acidic or alkaline. In the present study, Al-, Sn-, and Zr-natisites were synthesized, and compared to pure natisite and sitinakite in batch experiments. Five concentrations of NaOH and NaNO{sub 3} (i.e. source of Na{sup +}) mimicking conditions of high alkalinity, and competing Na{sup +} ions, respectively, were evaluated. Sorption results demonstrate that sitinakite is generally more effective than all four natisites in removing Cs and Sr. However, sitinakite uptake mechanism seems to deteriorate at increasing concentrations of base and Na{sup +}. Although less selective than sitinakite, all natisite sorbents provided a less dramatic decline in Cs and Sr uptake through increasing molarities. Overall, there was an improvement in the sorption of Cs and Sr by the metal-substituted materials over natisite and, in neither of the testing solutions, natisite outperformed its substituted variants. In highly alkaline solutions, Sn- and Zr-Natisite provided for exceptional removal for Sr, removing more than twice the amount sorbed by sitinakite at 0.1 M NaOH. The results obtained for Sr uptake by all four natisite materials in alkaline solutions are promising, especially considering the highly alkaline nature of wastes from the nuclear industry. Future studies should investigate the sorption mechanisms responsible for natisite selectivity for Sr at high pH. (authors)

12 MANAGEMENT OF RADIOACTIVE AND NON-RADIOACTIVE W↗

Materials Data on Cs(TeO3)2 by Materials Project

Cs(TeO3)2 crystallizes in the trigonal R-3m space group. The structure is three-dimensional. Cs is bonded to six O atoms to form CsO6 octahedra that share corners with twelve TeO6 octahedra. The corner-sharing octahedra tilt angles range from 64–72°. There are three shorter (3.22 Å) and three longer (3.24 Å) Cs–O bond lengths. There are two inequivalent Te sites. In the first Te site, Te is bonded to six O atoms to form TeO6 octahedra that share corners with six equivalent CsO6 octahedra and corners with six TeO6 octahedra. The corner-sharing octahedra tilt angles range from 42–69°. There is two shorter (1.94 Å) and four longer (1.99 Å) Te–O bond length. In the second Te site, Te is bonded to six equivalent O atoms to form TeO6 octahedra that share corners with six equivalent CsO6 octahedra and corners with six equivalent TeO6 octahedra. The corner-sharing octahedra tilt angles range from 44–72°. All Te–O bond lengths are 2.11 Å. There are two inequivalent O sites. In the first O site, O is bonded in a 2-coordinate geometry to one Cs and two equivalent Te atoms. In the second O site, O is bonded in a 2-coordinate geometry to one Cs and two Te atoms.

36 MATERIALS SCIENCE↗

Materials Data on Cs(MoS)9 by Materials Project

Cs(MoS)9 crystallizes in the hexagonal P6_3/m space group. The structure is three-dimensional. Cs is bonded in a 9-coordinate geometry to nine S atoms. There are three shorter (3.65 Å) and six longer (3.68 Å) Cs–S bond lengths. There are two inequivalent Mo sites. In the first Mo site, Mo is bonded in a distorted see-saw-like geometry to four S atoms. There are a spread of Mo–S bond distances ranging from 2.50–2.55 Å. In the second Mo site, Mo is bonded in a distorted see-saw-like geometry to four S atoms. There are two shorter (2.50 Å) and two longer (2.54 Å) Mo–S bond lengths. There are two inequivalent S sites. In the first S site, S is bonded in a 5-coordinate geometry to one Cs and four Mo atoms. In the second S site, S is bonded in a distorted pentagonal planar geometry to one Cs and four Mo atoms.

36 MATERIALS SCIENCE↗

Materials Data on Cs by Materials Project

Cs is Tungsten structured and crystallizes in the trigonal R-3m space group. The structure is three-dimensional. Cs is bonded in a body-centered cubic geometry to eight equivalent Cs atoms. There are six shorter (5.28 Å) and two longer (5.32 Å) Cs–Cs bond lengths.

36 MATERIALS SCIENCE↗

Materials Data on Cs by Materials Project

Cs is Magnesium structured and crystallizes in the hexagonal P6_3/mmc space group. The structure is three-dimensional. Cs is bonded to twelve equivalent Cs atoms to form a mixture of edge, face, and corner-sharing CsCs12 cuboctahedra. There are six shorter (5.47 Å) and six longer (5.51 Å) Cs–Cs bond lengths.

36 MATERIALS SCIENCE↗

Materials Data on Cs by Materials Project

Cs is Hg_xSn-like structured and crystallizes in the tetragonal I4_1/amd space group. The structure is three-dimensional. Cs is bonded to eight equivalent Cs atoms to form a mixture of edge and corner-sharing CsCs8 hexagonal bipyramids. There are four shorter (5.14 Å) and four longer (5.32 Å) Cs–Cs bond lengths.

36 MATERIALS SCIENCE↗

Materials Data on Cs by Materials Project

Cs is High Pressure (4-7GPa) Tellurium-like structured and crystallizes in the tetragonal P4_2/mbc space group. The structure is three-dimensional. Cs is bonded in a 6-coordinate geometry to six equivalent Cs atoms. There are a spread of Cs–Cs bond distances ranging from 5.15–5.47 Å.

36 MATERIALS SCIENCE↗

Materials Data on Cs by Materials Project

Cs is Protactinium-like structured and crystallizes in the orthorhombic Pnma space group. The structure is three-dimensional. Cs is bonded in a distorted q6 geometry to ten equivalent Cs atoms. There are a spread of Cs–Cs bond distances ranging from 5.24–5.51 Å.

36 MATERIALS SCIENCE↗

Materials Data on Cs by Materials Project

Cs is beta Np structured and crystallizes in the orthorhombic Pbcm space group. The structure is three-dimensional. Cs is bonded in a 4-coordinate geometry to six equivalent Cs atoms. There are a spread of Cs–Cs bond distances ranging from 5.20–5.48 Å.

36 MATERIALS SCIENCE↗

Materials Data on Cs by Materials Project

Cs is Copper structured and crystallizes in the cubic Fm-3m space group. The structure is three-dimensional. Cs is bonded to twelve equivalent Cs atoms to form a mixture of edge, corner, and face-sharing CsCs12 cuboctahedra. All Cs–Cs bond lengths are 5.46 Å.

36 MATERIALS SCIENCE↗

Materials Data on Cs by Materials Project

Cs is Tungsten structured and crystallizes in the monoclinic C2/m space group. The structure is three-dimensional. Cs is bonded in a 8-coordinate geometry to six equivalent Cs atoms. There are a spread of Cs–Cs bond distances ranging from 5.09–5.31 Å.

36 MATERIALS SCIENCE↗

Materials Data on Cs by Materials Project

Cs is Copper structured and crystallizes in the tetragonal I4/mmm space group. The structure is three-dimensional. Cs is bonded to twelve equivalent Cs atoms to form a mixture of corner, edge, and face-sharing CsCs12 cuboctahedra. There are four shorter (5.37 Å) and eight longer (5.53 Å) Cs–Cs bond lengths.

36 MATERIALS SCIENCE↗

The Carbon Storage Technical Viability Approach (CS TVA)

The Carbon Storage Technical Viability Approach (CS TVA) StoryMap provides an in-depth overview of the products created during the CS TVA research effort. In detail, the StoryMap addresses the CS TVA Matrix, Database Version 2.0, Database Catalog, Workflow, and Data Availability Result Database, discussing how each was developed and implemented. Information on how the matrix, database, and database catalog are interconnected, and their usage is also explained. The workflow section provides information on the CS TVA product development from the data-gathering stage to the final data availability results. A section on an expansion of the CS TVA workflow that utilizes Natural Language processing (NLP) section was included. Finally, the Data Availability Results Database is discussed. These results provide data science-informed insights into potential data gaps when assessing the viability of carbon storage in a given area or region.

Carbon Storage↗

First ITER CS module test results

The ITER Central Solenoid (CS) is under fabrication by the US ITER organization and its subcontractors. US ITER will supply seven modules to ITER IO, six of which will be assembled in a stack that forms the ITER Central Solenoid, with one as a spare. The first module fabrication has been completed by General Atomics (GA) at their facility and has begun testing including high voltage testing, Paschen testing in the vacuum and then testing at 4.5 K and up to 40 kA in order to demonstrate compliance of the coil to ITER requirements. In the paper we present the Test Plan and results of the CS Module performance tests, especially at 40 kA current. Herein, AC losses, joint resistances and hydraulic characteristics of the coil are all measured. Displacements of the coil height and hoop strain of the CS Module are also measured to verify structural and mechanical characteristics of the coil along with cooldown shrinkage of the coil. This information is used for verification of the stack behavior of CS in ITER operation. The test results and preliminary analyses results are presented, compared to expectations, and discussed. All measured parameters suggest that the CS module will perform well in ITER machine.

70 PLASMA PHYSICS AND FUSION TECHNOLOGY↗

Heat capacity and thermodynamic functions of partially dehydrated cation-exchanged (Na + , Cs + , Cd 2+ , Li + , and NH 4 + ) $\mathrm{RHO}$ zeolites

Synthetic zeolites have a myriad of applications in industry due to their porous frameworks, potential to exhibit flexibility, and specific interactions with guest molecules. One topology of zeolites, RHO, is known to be flexible and have strong interactions with both H 2 O and CO 2 . Here we have performed heat capacity measurements on three partially dehydrated zeolite RHO samples containing extra-framework cations Na + and Cs + , Cd 2+ and Cs + , and Li + and NH 4 + to understand the energetics of these materials. Based on fits of the heat capacity data, we report smooth thermodynamic functions of C p,m , Δ T 0 S m °, Δ T 0 H m °, and Φ m ° for these samples. The standard S m ° at 298.15 K are 76.3 ± 0.8, 72.1 ± 0.8, and 68.8 ± 0.7 J∙K -1 ∙mol -1 for the Na,Cs RHO, Cd,Cs RHO, and Li,NH 4 RHO samples, respectively, and the standard H m ° at 298.15 K are 12.1 ± 0.1, 11.4 ± 0.1, and 11.4 ± 0.1 kJ∙mol -1 . Our measurements also show a transition in the heat capacity of Na,Cs RHO, the sample with the highest water content, between 180 and 300 K that is not clearly observed in the other two samples. We attribute this transition to labile water and cations in the framework. This movement could also be coupled with a temperature-induced lattice expansion. Future work will include heat capacity measurements on fully dehydrated and fully hydrated zeolite RHO in order to separate these two possible phenomena.

37 INORGANIC, ORGANIC, PHYSICAL, AND ANALYTICAL CH↗