dataesr/scientific-paragraphs-categorization huggingface dataset:
Motor response evaluation Motor responses evoked by ultrasound stimulation with and without MBs were compared to investigate the enhanced neuromodulatory effect induced by the oscillation of MBs. The motor cortex of the mouse was selected as the simulation target. Electromyogram (EMG) signals evoked by ultrasound stimulation were recorded by the tungsten electrodes inserted into the triceps muscles of mouse forelimbs. EMG signals were amplified with a gain of 1000 and bandpass filtered between 300 Hz and 5 kHz using an amplifier (model 1700, A-M Systems, Inc. , Sequim, WA, USA), and acquired at a 10 kHz sampling frequency using a data acquisition card (1550A, Axon Instruments, San Jose, CA, USA). Twenty ultrasound stimulations as described above in 8 s intervals were performed for each condition.
The staining brain sections were cut at 40 μm in thickness using a cryotome. Then, the brain sections were incubated with the primary antibody against c-fos (1:500, ab214672, Abcam) at 4 ℃ for 12 h, and were washed and incubated with Invitrogen Alexa Fluor Plus 555 donkey anti-rabbit IgG secondary antibody (1:1000, A32794, Invitrogen) for 1 h at room temperature. Histological images were acquired using a fluorescence microscope, and analyzed with the ImageJ software (NIH).
We acknowledge  A. Hadj-Azzem  for his help in the compound synthesis,  J. Debray  for the orientation of the single crystals,  P. Lachkar  for his help with the PPMS, and  F. Museur  for discussions. V. Cathelin ,  P. C. W. Holdsworth ,  E. Lhotel  and  C. Paulsen  acknowledge financial support from  ANR, France , Grant No. ANR-15-CE30-0004. P. C. W. Holdsworth,  P. Lejay ,  E. Lhotel , and  P. C. W. Holdsworth  acknowledge financial support from  ANR, France , Grant No. ANR-19-CE30-0040. D. Prabhakaran  acknowledges financial support from  EP-SRC, UK , Grant No. EP/N034872/1.
Polarized optical microscopy (POM) Polarized optical microscopy is a fundamental tool to ensure the homogenous distribution of dopants in a LC matrix; therefore, polarized optical microscopic (POM) observations were performed on the ZEISS AXIO equipped with Infinity2 image capturing software. During the POM measurements, the temperature of materials was controlled with a Linkam TMS 94 hotstage. The pure 8CB and its GO nanoflakes composites were filled in 50 µm thick unaligned commercial sample cells (purchased from AWAT, Poland) to perform polarized optical microscopy.
RCC-M Approach Two proposals to modify the RCC-M code (or Requests for Modification (RM)) were submitted in late 2014 and were incorporated into the 2016 version of the RCC-M code  [11] , as Rules in Probationary Phase. This so-called RCC-M approach encompassed not only a proposal for a fatigue curve, but also a dedicated method to incorporate environmental effects. The mean air curve specified in this document is identical to the one in NUREG/CR-6909. This conclusion was reached  [23]  based on a statistical comparison of the air data available and the NUREG/CR-6909. The coefficients on life and strain amplitude were determined as the combination of international research and the results from French experimental campaigns  [24]. Concerning the factor on life, it is calculated as the statistical combination of aggravating parameters linked to the component effect, the loading effect, and data scatter.
These three categories recall the ones in NUREG/CR-6909 (surface roughness, loading history, size effect, and data scatter), but each one is intended to cover a much wider range of effects than NUREG/CR-6909. For instance, the component effect covers the surface roughness, the size effect, and the effect of a strain gradient through the thickness. The objective of covering a wider range of effects is to acknowledge interactions between effects  [24] , as well as to leave room for other effects that are unaccounted for. The final coefficients are given as ranges, which are combined through statistical methods, as in NUREG/CR-6909. This leads to a final coefficient of 10. Concerning the factor on strain amplitude, as in NUREG/CR -6909, it is recognised that the combination of the aggravating effect is not applicable and that the greatest aggravating effect is applicable.
The environmental effects are seemingly taken into account through the JNES proposal  [31] , which was determined based on experimental data. The Japanese proposal was one of the first proposals to account for EAF in fatigue calculations. The environmental factor (F en ) expressions were simply established through a study of the data trends, which was an approach that was subsequently followed in NUREG/CR-6909. The overall approach is summarized in Table  A1. As for NUREG/CR-6909, one main comment on the EAF methodology is that it does not include the possible interactions between aggravating parameters. This approach is still under discussion among the DCFS committee. The conclusion of the work is destined to be integrated into the JSME code.
Conclusions When performing environmental fatigue assessments (EFAs) of nuclear components, it is (technically) possible to use a wide range of technical documents or standards. Moreover, load inputs may be derived from design transients or from real data captured by monitoring systems. This paper has provided an overview of the different EFA procedures, providing a comprehensive scheme on their different hypotheses, assumptions, and ways of dealing with environmental effects. The paper has also provided an explanation of the benefits of considering real data derived from real transients instead of design data derived from design transients. It finally includes a case study in which an environmental fatigue assessment is performed for two sequences of transients in a particular location (inner radius) of a nuclear structural component (charging nozzle).
This work was partly supported by the  JSPS  core to core program, A. Advanced Research Networks. We acknowledge financial support from the  European Commission  through the  H2020 Future and Emerging Technologies Graphene Flagship  (Grant Nos. 881603  and  785219 ) and Skytop (Grant No. 824123 ). This research was supported by a public grant overseen by the  French National Research Agency (ANR)  through  FLAG-ERA   SographMEM  Project  Grant  No. ANR-19-GRFI-0001-07  and as part of the  "Investissements d'Avenir" program  ( Labex NanoSaclay, Reference :  ANR-10-LABX-0035 ). This study was supported by the  JST Program on Open Innovation Platform with Enterprises, Research Institute  and  Academia (OPERA) ,  KAKENHI  (No. 15H03548 ),  Center for Spintronics Integrated Systems  (No. J190001511 ) foundation, and The  Murata Science Foundation  ( 072 ).
According to our diffraction geometry, with the sample and area detector at fixed diffraction angles, and for a convergent x-ray beam we use f ≈ 2  [43, 44] , η(t ) = -f ϑ (t ) cot(ω). (1) First, we investigated the transient strain of Bi:YIG as a function of the excitation fluence for NUV illumination to determine the response to an above-band-gap excitation. The results for Bi 2 Y 1 Fe 5 O 12 are shown in Fig. 2 (a) and yield the typical linear scaling of the strain amplitude with the fluence in accordance with other studies on semiconductors and insulators  [12, 45]. This dependence is analyzed by the blue linear fit in Fig. 3(a) , where the average strain η in FIG. 3. Averaged lattice strain η in Bi:YIG between 75 ps and 1 ns evaluated from the data set in Bi:YIG from 75 ps to 1 ns is displayed as a function of the NUV fluence.
The analysis of surface morphological and microstructural modification in the laser impact area was carried out using a scanning electron microscope (SEM, of Zeiss Supra55 FEG-SEM), equipped with a HKL-Oxford Instruments Electron BackScatter Diffraction (EBSD) system composed of a Nordlys II camera and Channel 5 software suit. EBSD acquisitions were performed at a fixed working distance of 15 mm and sample tilt of 70 • with respect to horizontal. For EBSD interrogation, the accelerating voltage of primary electron beam was set in the range of 7-30 kV, allowing the penetration depth of diffracted backscattered electrons to vary from 5 to 35 nm, approximately  [35]. A FEI Helios multisource system with combined functionalities, such as SEM, scanning transmission electron microscopy (STEM), energy dispersive x-ray spectroscopy (EDX), and focused ion beam (FIB) was used for various visualization, analysis, and STEM lamella preparation.
167 J/cm 2 , respectively. The transient reflectivity changes were measured by two photodiode detectors in imaging geometries with respect to the surface. The changes in reflectivity R/R with pump-probe delay are plotted for the two chosen intensities and the two probe angles as insets on Fig. 2 , where expected reflectivity R as a function of the excited free-electron density is also shown. To guide the eyes, the experimental data are fitted by the convolution of the Gaussian envelope of the laser pulse with a linear combination of several exponential functions as the measured signal is a convolution between the pulse duration and the carrier dynamics. To access the evolution of optical indices, we focus on the measured maximum values of the transient reflectivity changes as they represent uniquely determined pairs Re(ε), Im(ε) which are extracted by inverting Fresnel formulas at the given angles  [46, 47]  = 0.
A. Estimation of the transient electron density from TDDFT calculations The density of laser-excited electrons in silicon is calculated using TDDFT  [48, 49]  as implemented in OCTOPUS code  [50]. In this real-time TDDFT, the laser-induced electronexcitation process is described by time-dependent Kohn-Sham equations, i h ∂ ∂t ψ i (r, t ) = H KS (r, t )ψ i (r, t ), (2) where ψ i (r, t ) is a wave function of a single-electron state, i denotes the state index and runs over all initially occupied states. The Kohn-Sham Hamiltonian H KS (r, t ) is given by H KS (r, t ) = 1 2m -i∇ + e c A(t ) 2 + v ion (r) + v H (r, t ) + v xc (r, t ). (3) It includes ionic potential v ion (r), Hartree potential v H (r, t ) and exchange-correlation potential v xc (r, t ). A metageneralized-gradient approximation of Tran and Blaha is employed for the exchange-correlation potential  [51].
ACKNOWLEDGMENTS This work was supported by the  ANR  project  DYLIPSS  ( ANR-12-IS04-0002-01 ) and by the  LABEX MANUTECH-SISE  ( ANR-10-LABX-0075 ) of the  Université de Lyon , within the  program Investissements d'Avenir  ( ANR-11-IDEX-0007 ) operated by the  French National Research Agency (ANR). Numerical calculations have been performed using HPC resources from  GENCI-TGCC  and  CINES , project  gen7041. This work was also supported by the  IMOTEP  project within the program Investissements d'Avenir operated by ADEME.
TGA Data Thermal stability analysis of both modified and unmodified PHBH/AVF biocomposites was performed by TGA and the results compared to those of neat PHBH. Table  3  shows the temperature values of T10 and T50 corresponding to 10% and 50% mass loss, respectively, and Tmdr is the temperature relative to the maximum decomposition rate. TGA data indicate that the presence of AVF in PHBH slightly decreases the thermal stability of the biocomposite materials independently of the chemical modification. Indeed, the main degradation temperatures, i. e. , T10, T50, and Tmdr, exhibit lower values. Further, the PHBH/A-AVF biocomposite presents the lowest thermal stability.
More generally, data is also needed for a better understanding of Pu-U oxide solid solutions chemistry in water. For these purposes, a fresh homogeneous MOx (i. e. before irradiation in a nuclear reactor) with 24 wt. % of Pu was leached in carbonated water under anoxic conditions over one year in order to simulate the behaviour of the Pu-rich agglomerates of MIMAS MOx fuels and to get kinetic data to model the radiolytic dissolution. The uranium, plutonium and hydrogen peroxide concentrations were measured over time, as well as the Eh and pH parameters. The mass balance between aqueous, colloidal and precipitated/sorbed fractions was quantitatively determined at the end of the experiment. Surface characterization, involving SEM-WDS and Raman spectroscopy, was achieved on the homogeneous MOx pellets before and after leaching.
2 database (Table  2 ) with an uncertainty of 0. 1%. The α, β and γ heat powers related to this isotopic composition were 1. 94×10 -3 , 1. 54×10 -5 and 5. 08×10 -6 W/gMOX, respectively. The α-activity of a pellet was 2. 2×10 9 Bq. g -1 MOx, which corresponds to an α-dose rate received by the solution of 9730 Gy. h -1 based on the Sunder calculation method  [12]. The β and γ dose rates were calculated at different distances from the pellet surface using the Vaskin © 3. 1. 0 and the Mercurad © 1. 04 codes respectively. The β dose rate was 0. 52 mGy. h -1 at 100 µm from the surface and mainly due to traces of 234m Pa. This dose rate was too low and therefore not considered. The γ dose rate, mainly produced by the 241 Am, quickly dropped, i. e. 110 mGy. h -1 at 100 µm, 4 mGy. h -  at 1 cm, and only 0.
SOLUBILITY DIAGRAMS AND MODELLING The CHESS software  [17]  and the ThermoChimie thermodynamic database  [18]  were used to calculate the solubility diagrams of U and Pu applicable to the long-term leaching of the MOx pellet. UO2 (crystallized), β-UO2(OH)2, and PuO2 (crystallized) have been discarded, as they are not expected to precipitate in such conditions. The MOx dissolution was modelled using kinetic reactions, which will be described later in the article.
[19]. The position is in line with the data of Elorrieta and confirms the homogeneous nature of the solid solution at the micron scale as already revealed by EPMA. Moreover, no traces of oxidized phases were observed by Raman spectroscopy. The intense 2LO band (around 1160 cm -1 ) and the absence of a signal around 630 cm -1 indicate the absence of M4O9 type phase. After the surface characterization, which confirmed the homogeneity of the pellets, the pellets were submitted to 10 pre-leaching cycles in carbonated water (see section 2. 2). Fig. 2  shows that the uranium concentration was under 10 µg. L -1 and no initial release peak was observed which demonstrates the absence of an oxidized layer  [20].
However, in this case, the formation of the amorphous Pu(OH)4 layer has probably a stabilizing role and a H2O2 disproportion role. The deposition of amorphous hydroxide layers such as Pu(OH)4 is quite consistent with the observation made on other actinides, such as Th, U and Np, although no passivating role was mentioned  [22]. Nevertheless, the mechanism of formation of this amorphous layer remains unknown. A local reorganisation of the hydrated and depleted fluorite structure could be considered, or a dissolution/precipitation mechanism. The overall consistency of the kinetic rate constants (Table  4 ) obtained for the long-term leaching of Eq. 3 is illustrated in Fig. 9. The model A was performed with CHESS software by introducing the constants determined previously for H2O2 production and disproportionation and MOx oxidation.
Three fabrics with different weaving diagrams were produced, i. e. plain weave (H1), satin 6 weft effect (H2) and twill 6 weft effect, see Figure  1. On schematic views, made with WiseTex software, warp yarns are represented in blue color and weft yarns in red color. They have the same warp density of 6 yarns/cm and different weft densities, namely 5 yarns/cm for H1 and 9. 5 yarns/cm for H2 and H3. Warp and weft densities have been measured according to the standard NF ISO 4602  [46]. Composites plates were manufactured by hot pressing with the produced hemp fabrics and an epoxy resin, the GreenPoxy 56 from Sicomin Company. Their dimensions are 200 x 300 mm². The fabrics were conditioned at a temperature of 23°C and a relative humidity of 50% during at least 24 h prior to the composite manufacturing.
Composite properties The microstructure of the manufactured composites was characterized using X-ray nanotomography. Image acquisition was realized on an Easytom micro-nano tomograph (RX Solutions, France). The system is equipped with an X-ray source Hamamatsu Open Type Microfocus L10711 having maximum voltage 160 keV. The images reported herein were collected using X-rays of voltage 40 keV and a current of 22 µA. The X-ray transmission images were acquired using a Fluoroscopic High Speed imaging subsystem PaxScan 2520DX. The entire volume is reconstructed at a full resolution with a voxel size of 5. 77 µm, using filtered back-projection. The data were processed using VG Studio software. Tensile specimens were cut in the manufactured composite plates using a Trotec laser cutter. The mechanical characterization was conducted according the standard ASTM D3039-00  [55] , on a MTS Criterion 45 universal machine, with a crosshead displacement rate of 1 mm/min, a specimen width of 15 mm and a gauge length of 150 mm.
Methods Materials and physical measurements. All starting materials were of reagent grade quality and were obtained from commercial sources without further puri cation. Powder X-ray diffraction (PXRD) data were recorded on a Bruker D8 ADVANCE X-ray powder diffractometer (Cu-K a ) at room temperature. Infrared spectra were measured as KBr pellets on a Bruker Tensor 27 spectrometer in the range of 400 -4000 cm -1. Thermogravimetric analyses (TGA) were performed under a ow of nitrogen in the temperature range 25 -600 °C at a heating rate of 5 °C / min using a METTLER TOLEDO TGA/DSC 1 instrument. Elemental analyses for C, H and N were obtained with a Perkin Elmer 240C elemental analyser. Atom force microscope (AFM) measurements were carried out on VEECO Inc Multimode V. Scan electron microscopy (SEM) was performed on SHIMADZU SSX-550.
The magnetic data were obtained on polycrystalline and powder samples using a Quantum Design SQUID VSM system. The diamagnetic contributions of the samples were estimated from Pascal's constants. 45 nthesis   S26 ). Thermal analysis reveals that the water molecule can be completely removed below 140 °C, corresponding to the release of nine (25 -80 °C) and two (80 -140 °C) water molecules (Figure  S27 ). The total weight loss is 9. 87 %, in agreement with the removal of six lattice and ve coordinated water molecules (calcd. 9. 10 %). According to this result, the elemental analysis sample may have lost three water before tested, and the results are consistent with formula C 87 H 69 N 9 Co 3 Ir 2 O 20 (calcd. (%) C, 49. 24; H, 3. 28; N, 5. 94). Exfoliation into sheets. For all the exfoliation experiments the following was adopted.
Thus, we can use UV/Vis/NIR spectroscopy to directly measure the HOMO-LUMO gap. The UV/Vis/NIR data can now be correlated analogously to the CV data with the DFT calculations (B3LYP/def2-TZVP). As shown in Figure  8 , the maximumo ft he LL'CT correlates almost perfectly with the theoretical calculations andt he electrochemical data. These correlationsi nde-pendently validate the trend for the donor strength that we have already concluded from the CV measurements in order of decreasing donor strength: [ Q tBu 2À < Q NO 2À < Q Cl 2À < Q To l 2À < Q Ms 2À ]. Rearrangements in complexes 3and 4 Complex 3 showed ap articularb ehavior during the UV/Vis/NIR spectroelectrochemicali nvestigation. Upon oxidation of 3,a broad and very intenseb and at 950 nm emerged with a shoulder at around 750 nm (see Figure  9a ).
Acknowledgements The High-PerformanceC omputing resources of the Zentraleinrichtungf ürD atenverarbeitung (ZEDAT) of  Freie Universität Berlin  are acknowledged. The authorsa re grateful to the  DFG PriorityP rogramS PP 2102 , " Light-controlled reactivity of metal complexes "( SA 1840/7-1 ) for financial support.
18 Diffraction data were collected using a Bruker Apex II diffractometer equipped with Mo Kα radiation (0. 71073 Å) and a CCD detector. The dehydration process was investigated from 50 to 300 °C in steps of 25 °C and from 300 to 350 °C in steps of 50 °C, using the same experimental apparatus described in ref 17. Each data collection lasted for ca. 7 h. The crystal was equilibrated at the set temperature for at least 40 min before starting a new data collection. Such experimental conditions can be regarded as dry and quasiequilibrium conditions. Data were integrated and corrected for absorption by using the software package APEX3 v2019. 1-0. 19 Two methods were employed to solve the structures: (i) direct methods, using ShelXTL  20  after determining the space group by Xprep,  19  and (ii) intrinsic phasing, using ShelxT.
21 The first approach indicated R3̅ m space group for datasets up to 100 °C. From 125 °C on, the suggested space group, based on R sym and figure of merit, was R3̅. The results obtained by the intrinsic phasing method mainly suggested R3m, R3̅ m, and R32 for all datasets. However, the correct space group could not be unequivocally assigned because of the close values of the indicators R weak , α, and x (initial Flack's parameter determined for noncentrosymmetric space groups). 21 Thus, we performed a series of structural refinements in the centric (R3̅ m, R3̅ ) and noncentric (R3, R3m, R32) solutions. Finally, the acentric space group R3m was chosen for all datasets from 125 to 300 °C, based on the R 1 values and weighting scheme of the structural refinements. The centrosymmetric space groups R3̅ m and R3̅ (and the acentric R32) were excluded based on the arrangement of the extraframework (EF) occupants and subsequent change of the framework observed at high temperatures (see the Section 3).
Structural refinements were carried out by SHELXL-2014 22 using neutral atomic scattering factors. Atom labels and coordinates of framework atoms were those used by Cametti and Churakov, 2020. 18 Extraframework species were located by difference Fourier maps. Atomic sites related by a pseudocenter of symmetry in R3m were labeled by doubling the number of digits of the corresponding site in R3̅ m. For instance, in R3̅ m, two independent tetrahedral sites T1 and T2 constitute the framework. In R3m, the two independent tetrahedral sites equivalent to T1 were labeled as T1 and T11. Reverse-obverse twinning [1̅ 00 01̅ 0 001] was observed for all structures in the investigated temperature range. The dataset collected at 200 °C was affected by high R int values, and a reasonable structure solution and refinement was not possible.
With the increase of temperature, the intensity of the reflections significantly decreased. At 275 and 300 °C the maximum theta value was 45. 39°(resolution = 0. 94 Å) and ACS Omega 40. 16°(resolution = 1. 0 Å), respectively. Thus, for these two datasets, structure refinements, although with a poor data/ parameter ratio (Table  1 ), were possible. At 350 °C, only cell parameters were extracted. Crystal data, data collection, and refinement details are reported in Table  1. All visualizations of crystal structures were produced by VESTA. 23 Cif files are available in the Supporting Information. 2. 3. X-ray Absorption Fine Structure Spectroscopy (XAFS). XAFS experiments were performed at the European Synchrotron Radiation Facility (ESRF) in Grenoble, France. The data were collected at the Spanish CRG beamline (SPLINE, BM25) equipped with a Rh-coated collimating mirror, a sagitally focusing Si(111) double-crystal monochromator, and a Rh-coated vertically focusing mirror.
The sample was gently ground, and the resulting powder was inserted in a 0. 7 mm glass capillary. Spectra were collected at the Ag K-edge (25 514 eV) in transmission mode using gasfilled ionization chambers. The high temperature (HT) measurements were performed in situ by using a N 2 blower (FMB Oxford). Data were recorded from 25 to 650 °C at the following temperatures: 25, 75, 175, 275, 350, 425, 550, and 650 °C. The equilibration time between each data collection was 10 min. Each scan was recorded up to k = 12. 0 Å -1 with a typical acquisition time of 30 min. To improve the signal-to-noise ratio, five scans were averaged at each temperature. XAFS data were reduced using WinXAS software. 24 For each spectrum, the background was subtracted, and the absorption edge jump was normalized to unity.