dataesr/scientific-paragraphs-categorization huggingface dataset:
Finally, the largest one-step dilution reaches point B below MHC. The octanol is therefore at a negligible concentration in the water-rich phase. SANS data only show a BP signal in the oil-rich phase and essentially a flat background in the water-rich phase: neither pre-Ouzo aggregates nor progressive aggregates are detected in the water-rich phase, with 91% of the polar mass fraction. As measured by density, the octanol-rich phase still contains 10% water and 17% ethanol. This sample separates neatly and immediately with no need for further centrifugation. In such a situation, there is no delayed macroscopic phase separation: no Ouzo droplets nucleate and grow.
Synthetic alite can be made by solid state sintering of decarbonated calcium oxide and fine silica, with possible addition of impurities (alumina, magnesium, sulfates), depending on the polymorph to be reached  [23]. The elastic properties are typically determined by nanoindentation experiments and at the macroscale by resonance frequency measurements  [24, 25]. Nanoindentation experiments are most of the time performed on hydrated mortar or cement paste  [22, [26] [27] [28] , and more rarely on pure and doped clinker phases  [24]. Unhydrated clinker phases are known to exhibit stiffnesses by 3-5 times larger and hardnesses by one order of magnitude larger than hydrated phases  [22, 24, 29]. Two force fields (FF) introduced in the cemff database  [9]  were employed to describe atomic interactions in C 3 S: INTERFACE FF (IFF)  [13, 30]  and ClayFF  [31].
ClayFF does not account explicitly for covalent bonding in silicates, and larger charges are used for silicon atoms (2. 1e) when compared to IFF (1. 0e). The ionic nature of these bonds is thus overestimated in ClayFF, and impacts substantially computed surface tension  [13]. We also expect an influence of this assumption on the elastic behaviour  [30]. Results in better agreement with experimental measurements are expected with IFF, for which parameters were optimized especially for C 3 S  [13]. Every simulation in the present paper were performed with the LAMMPS simulation code  [32]. A 12 Å cutoff, and an Ewald summation with precision of 10 -5 were adopted for short-range and long-range interaction, respectively.
The simulations were performed in the NpT ensemble with the same MD parameters as previously. The systems were relaxed during 0. 5 ns, and the data were collected for 1 ns. Within the direct method, the specific heat c p was computed by linear fitting of the enthalpy with respect to the temperature at five points around the temperature of interest (e. g. , 280, 290, 300, 310 and 320 K to compute the specific heat at 300 K). The same method was employed to calculate the expansion coefficient, fitting the volume variation with respect to the temperature. To avoid the external influence of thermostating or barostating, the relaxed systems were equilibrated for 500 ps in the NVE ensemble, before running simulation of 100 ps, dumping the trajectory at each time step to be able to observe high vibrational frequencies.
Graphene has been used in a few studies as the prototypical ultra-sensitive 2D charge transport material to sense the SCO transition. 260, 545 In a first study, large-area CVD graphene was employed to sense the spin transition occurring in a thin layer of SCO nanoparticles. 260 In this case, the resistance of the graphene sheet was measured as a function of temperature and gate voltage in a four-probe van der Pauw configuration (Figure  33a ) before and after covering the device with a thin layers of SCO nanoparticles. Transfer curves were acquired at different temperatures, permitting to extract different representative parameters. A thermal hysteresis was observed in the resistance at the Dirac point and in the hole mobility, consistent with magnetometry data for the SCO nanoparticles in powder.
Multiresponsive transistors and memories The Internet of Everything will lead us to a scenario in which interactions between humans and devices will be critical to allow people to use, monitor or configure Internet of Things devices. Interactions in such applications are based on responsive devices, leading to the generation and transfer, i. e. communication, of a huge amount of data. The efficient processing of these data relies on transistors and memories as the basic electronic elements whose integration can lead to responsive devices. Since responsiveness can be exploited for precise sensing, near-sensor and insensor computing can be developed in which computation tasks are moved partly to the sensory terminals. 614 One representative example is the optical memory, which exploits one device to simultaneously respond to the light signal and store the input optical signal.
ACKNOWLEDGMENT The activity in Strasbourg was supported by the EC through the ERC project SUPRA2DMAT (GA-833707) and the Graphene Flagship Core 3 project (GA-881603) as well as the Labex projects CSC (ANR-10LABX-0026 CSC) and NIE (ANR-11-LABX-0058 NIE) within the Investissement d'Avenir program ANR-10-IDEX-0002-02 the International Center for Frontier Research in Chemistry and the Institut Universitaire de France (IUF). The activity in San Sebastian was supported by the Spanish MICINN under the Maria de Maeztu Units of Excellence.
Acknowledgements L. D. C, S. P. and Y. Z. thank  USIAS  for financial support. E. P. acknowledges  Solvay  for the Ph. D fellowship. We thank  Pierre Picchetti  ( University of Strasbourg ) for the N 2 adsorption, SAXS and TEM analysis,  Dr. Laura Talamini  ( University of Strasbourg ) for the cytocompatibility experiments,  Dr. Victor Sebastian  ( University of Zaragoza ) for the cryo-SEM imaging and  Fabio Longo  for the technical support. Etienne Piantanida  and  Ivo Boskoski  contributed equally to this work.
Acknowledgements This work has received funding from the  Horizon 2020 program  of the  European Union  for research and innovation, under grant agreement no. 722176  ( INDEED ) and  SNSF  via project nr- 40B2-0_176680  and  BSCGI0-157705. AKS acknowledges the  Laboratoire des Matériaux Semiconducteurs, EPFL  for the kind hospitality during her secondment within the  INDEED  project. We thank  Vincenzo Grillo  ( CNR-Nano, Modena, Italy ) for very helpful discussions. WKM, AMB acknowledge  Spanish MINE-ICO  under project  ENE 2016-79282-C5-1-R (AEI/FEDER ,  UE ) and  Gobierno de Aragón (Grupo Reconocido DGA )  T03_17R  ( FEDER, UE  and  T03_20R ).
II. 3. c Mapping the reciprocal space using area detectors We pointed out above the interest in performing mapping (2D or 3D) of the scattered signal around diffraction peaks. With the principle detailed above, the sample is oriented with respect to the x-ray beam and the detector is positioned such as to access a particular point in the reciprocal space. Then these positions are adjusted such as to access the next point to measure. Chapter 18 -Artificial laminar oxide multiferroic magnetoelectric thin film structures regulation (~1 s) can be up to 10 -100 times higher than the data acquisition times (few 10 to 100 ms). When volumes in the reciprocal space are to be measured, the total acquisition time of a dataset can thus easily raise to hours or days. With the arrival on the market of reliable, fast, low noise and high dynamics detectors, approaches using them instead of the 'classical' point detector are appearing  [59, 60].
Indeed, each dataset is now containing a 2D slice (not necessarily along high symmetry directions) in reciprocal space. Measuring 3D volumes thus simply reduces, most of the time, to a simple line-scan of the position of the sample and / or detector. Since the data acquisition per point can be typically reduced well below 1 s (high photon flux), this acquisition is most of the time done in a continuous mode  [61] , during the angular movements. The result is a tremendous gain concerning not only the duration of the acquisition of large datasets, but very good resolution of the data (in reciprocal space). Mathematical algorithms  [59, 62]  are then needed in order to properly re-synchronize datasets and angular position, as well as to reconstruct the reciprocal space and access the particular points / directions / planes.
III. 2 Synchrotron based -characterization techniques All the samples reported in Table  1  were measured using the same systematical experimental approach. For the x-ray diffraction approach, once the sample is aligned with respect to the x-ray beam, the following datasets were acquired: (i) x-ray reflectivity, (ii) specular x-ray diffraction (00L direction) line-scans, (iii) in plane grazing incidence XRD line-scans (along 2 symmetry directions, [H00] and [HH0]), and (iv) Reciprocal Space Maps (RSMs) at particular positions (containing both an in plane and an out of plane component) in fixed grazing incidence geometry  [38, 39]. For the (ii) and (iii) situations, rocking scans at the positions of diffraction peaks characteristic to BTO and CFO (several diffraction orders) were also recorded.
III. 2. a X-ray reflectivity (XRR) X-ray reflectivity (XRR) measurements were performed on several particular samples, with the aim of (i) confirming the relative thickness of the constituting layers, cf. the aimed thickness during the AO-MBE process, and (ii) confirming the relative low roughness (< 1 nm r. m. s. ) of the constituting films at the end of the growth process  [24]. The period of the oscillations (in q coordinates, measured directly on the dataset or extracted after a Fourier Transform [60 and references therein,79,80]) can be converted into thickness of the corresponding layer. A more quantitative approach involves modelling and fitting the whole dataset  [24, 50, 79]  Several reflectivity curves for increasing thickness of the bilayer are shown in Figure  9  along with an example of fitted dataset.
These measurements confirm the thickness of the layers (within 10% of the aimed value, and topped to about 0. 8 nm) and show that the manufacturing approach and conditions are granting well defined layers with very low roughness (~ 0. 2 -0. 3 nm r. m. s. for the buried interfaces and slightly increased to ~ 0. 4 nm r. m. s. for the topmost surface). Note also that there is a slight increase of the interfaces roughness with the increase of the thickness of the constituting layers. Although the presence of extra interfacial layers of thickness < 1 nm cannot be completely out-ruled from these datasets, if present, they are in very limited / low quantity. Thus, we can exclude a significant intermixing of the oxide layers.
III. 2. b X-ray diffraction (XRD) in specular geometry X-ray diffraction (XRD) measurements in specular geometry (aligned on the crystalline lattice) were performed for all samples. As an example, the datasets measured for the samples already shown in XRR are presented in Figure  10. The data are represented using reciprocal lattice units (r. l. u. ) of STO, i. e. the XRD peaks of the substrate will appear at integer coordinates. Due to the particular crystalline structure of the BTO and CFO (at room temperature slightly tetragonal with c/a ~ 1. 01% and cubic -inverse spinel respectively), as well as to the approximately double lattice parameter of the CFO (compared to BTO and STO), CFO XRD characteristic peaks appear only close to even L coordinates (r. l. u. of STO), while BTO characteristic peaks appear close to each integer L coordinate, as illustrated in Figure  10.
For the samples investigated here, typically (HHL) and (H0L) RSMs (H ~ 2, L ~ 2 r. l. u. of STO) were performed. Figure  12  schematically illustrates the signal distribution in the reciprocal space for a CFO / BTO / STO(001) system, as well as a 2D measurement around a particular region ((222)STO Bragg peak in this case, for the 15 nm CFO / 21 nm BTO / STO(001) sample), region in which both CFO and BTO will yield to significant scattered signal. The measured RSMs for all the available samples are reported in Figures  13  and 14. From such datasets, each of the characteristic XRD peaks (CFO and BTO) are fitted using a 2D Gaussian function (see e. g. Supplementary Material in ref. [24] ) and the corresponding parameters are extracted. The H and L positions for each peak are converted to lattice parameters.
01. We mentioned earlier that for diffraction peaks characteristic to each of the 2 layers, and for several orders of them, their azimuthal and radial widths were measured * Perovskites and other Framework Structure Crystalline Materials * p 538 Chapter 18 -Artificial laminar oxide multiferroic magnetoelectric thin film structures (either in separate line-scan measurements or from the RSMs datasets). The reciprocal space Bragg peak width is expected to be the result of the convolution of several contributing components: (i) a mosaic spread (angular mis-orientation between the crystallites constituting the epitaxial film) that is a constant angular azimuthal opening at any reciprocal momentum q value; (ii) a domain size that leads to a finite width q in reciprocal space for any peak, and (iii) a lattice parameter dispersion (micro strain) that will spread linearly with q.
The azimuthal peak width, in a direction parallel to the sample surface, is significantly large and corresponds to mosaicity. In the direction perpendicular to the surface, the small finite thickness of the layer is dominating and is considered as domain size. The azimuthal width will be dominated by the first two effects and the radial one by the last two. Knowing the experimental widths for at least two peaks at different momentum transfer values is thus a minimum in order to determine these three contributions. Even if in some cases only one XRD peak was measured, data can be extracted by assuming some of the contributions as dominant, and the other(s) being neglected. Mosaicity and crystalline domain size, values in the plane of the surface of the sample deduced from the XRD datasets (from  [72] ).
Topographic Characterization The morphologies were observed with a scanning electron microscope (MIRA3 Tescan). These observations were carried out with a secondary electron detector to reveal the topographic contrast. The various patterns constituting the topography of the surfaces are thus described. The in-plane contributions of the patterns (width and periodicity) can be measured precisely. The characterization of the morphology by SEM was completed using a quantitative analysis based on optical inteferometric measurements. These measurements were carried out in VSI mode (Vertical Scanning Interferometry), with green light (515 nm wavelength). The analyses of interferometric measurements were performed with the MountainsMap software (DigitalSurf) using the ISO-25178 roughness standard  [44].
Tungsten trioxide thin films were deposited on silicon substrates by non-reactive RF sputtering from a WO 3 target at room temperature. The WO 3 films were post-annealed at two different temperatures, 400 • C and 500 • C. The morphological and microstructural properties of these films were analyzed by using atomic force microscopy and X-ray diffraction. X-ray diffraction patterns only show WO 3 oxide phases. The AFM images show different morphologies with smaller grains for the film annealed at 400 • C. WO 3 sensing films and W heating elements were embedded in commercial cases for the fabrication of cost-effective gas sensors. The sensitivity and dynamic response of the sensors were analyzed under various concentrations of H 2 S, from 20 to 100 ppm, at SIMTRONICS SAS (3M Company, Saint Paul, MN, USA).
In the present study, the microstructure, electrical properties, and exposure to H 2 S of WO 3 thin films were investigated. RF non-reactive sputtering was used to deposit thin films on silicon substrates. Then, these films were annealed at two different temperatures, here 400 • C and 500 • C. WO 3 sensing elements associated to a tungsten-based heater were embedded in commercial cases for the fabrication of gas sensors. The electrical response and sensitivity of the cost-effective gas sensors were measured at different operating temperatures and under various concentrations of H 2 S at SIMTRONICS SAS (3M Company). Additionally, an original study is proposed. Indeed, the sensitivity evolution is explained by a model, and the experimental data are fitted by using equations related to this model.
Measurements under H 2 S The sensitivity of semiconductor gas sensors is highly dependent on the operating temperature. In order to determine the optimum operating temperature for the detection of H 2 S, the sensors were exposed to 100 ppm of H 2 S at various temperatures. The sensor responses were monitored by using the SIMTRONICS's measurement system and software. The electrical resistance values of the sensors were extracted from the collected data. An operating temperature ranging from 330 to 450 • C has been chosen for several reasons: (i) in previous tests, our sensors exposed to 100 ppm of H 2 S have given no significant response at temperatures below 250 • C; (ii) as seen in Section 3. 3, the WO 3 films present a huge variation of the conductance from 250 to 330 • C; (iii) the maximum operating temperature of our tungsten heater is 500 • C  [5].
Conclusions Tungsten trioxide thin films were elaborated by non-reactive RF magnetron sputtering and annealed at two different temperatures, 400 and 500 • C. The morphology and crystalline structure were studied. The DRX and AFM results suggest that an increase in the annealing temperature mainly affects the morphology of the film. Two sensors, composed of a W heating element, a WO 3 sensing element, and W electrodes embedded in a commercial case, were tested under different conditions at SIMTRONICS SAS (3M Company). Sensor-400 has given a higher sensitivity to H 2 S than sensor-500. This behavior can be linked to the presence of smaller grains in the film annealed at 400 • C. A model of the sensitivity evolution has revealed that the operating conduction mechanism is governed by a Schottky barrier-controlled conduction associated with the Freundlich adsorption isotherm for the adsorption of gases at the sensor surface.
Model and simulation setup First, a discharge plasma was reconstructed with edge plasma code package SOLPS-ITER  [14] [15] [16]  based on the H-mode high power on the EAST device (shot No. 70601). Then, the B powder was real-timely introduced vertically by gravity into plasma from a location at top of the private flux region of the upper divertor (R = 1. 50 m, close to the experiment setup), as shown in Fig. 1. The transport of B particles and its effects on the background plasma were simulated by the SOLPS-ITER. In comparison, another two simulation cases were carried out: one was a pure D discharge (corresponding to shot No. 70601), the other was a D discharge but with injecting Li powder instead of B powder. The parameters of background D plasma in all three cases were chosen the same. In the powder injection cases, the injection fluxes for both Li and B powders were 4.
From Figs. 3  and 4 , we know that all types of B ions but B 5+ exist dominantly in the narrow region just outside the separatrix. This special distribution pattern leads to a great reduction of heat flux to the divertor -divertor detachment. The reason why impurity B has such a particular distribution but impurity Li must be related to the difference in inelastic collision cross-sections and the thresholds for these inelastic collision events. Please refer to ADAS datasets for details. The magnetic field does not affect the movement of neutrals, while the magnetic field confines their movement on certain magnetic flux surfaces when the neutrals are  ionized. Impurity ions leave their magnetic flux surface only by collisions. Thus, we can expect that the ionization collisions play a major role in determining in what magnetic flux tubes B ions stay.
Acknowledgements This work is supported by the  National Key R&D Program of China  under Grant Nos. 2017YFE0301100  and  2019YFE03030004 , and  Users with Excellence Program of Hefei Science Center CAS ( 2020HSC-UE010 ). The authors also thank  Supercomputing Center of Dalian University of Technology  for providing part of computation resources. The views and opinions expressed herein do not necessarily reflect those of the  ITER Organization.
0. 63) (Thermo Fisher Scientific, Bremen, Germany). Full survey scans were performed at a 120,000 resolution, and a top speed precursor selection strategy was applied to maximize the acquisition of peptide tandem mass spectrometry (MS/MS) with a maximum cycle time of 3 s. Higher-energy collisional dissociation (HCD) fragmentation mode was used at a normalized collision energy of 32%, with a precursor isolation window of 1. 6 m/z, and MS/MS was acquired in the ion trap. Peptides selected for MS/MS were excluded from further fragmentation during 60 s. The data collected by the MS were processed for protein identification and quantification using the MaxQuant version  1. 5. 3. 30 (Computational Systems Biochemistry Research Group, Max  Planck Institute of Biochemistry, Martinsried, Munich, Germany), using the Andromeda search engine set to search the UniProt database restricted to the E.
coli (strain K12) proteome (UniProt proteome ID: UP000000625, number of sequences: 4,306). Trypsin (cleavage after K,R) was used as the enzyme definition, allowing two missed cleavages. Carbamidomethylation of cysteine was specified as a fixed modification, whereas N-terminal acetylation of protein and oxidation of methionine were specified as variable modifications. The MS proteomics data have been deposited to the ProteomeXchange Consortium via the PRIDE  (Vizcaino et al. , 2016)  partner repository (EMBL-EBI, Cambridge, United Kingdom), and can be accessed at http://www. proteomexchange. org with the dataset identifier PXD010014. All data postprocessing and statistical analyses were performed using the custom MATLAB scripts. Intensity-based absolute quantification (iBAQ) and label-free quantification (LFQ) data were used as the basis for quantification.
C T. I i k I k M k. An additional normalization was then performed to correlate protein abundances in insoluble fractions to those in the total protein fractions. A list of 281 bona fide membrane proteins was obtained from the Uniprot database. These known, fully insoluble proteins should therefore have the same mass fractions in the total and pellet mass fractions. For this equality to hold, log-log scatter plots of pellet vs. total mass fractions (Figure  2A ) were used to perform curve fitting procedures (separately for each E. coli strain) of the form Log P = αLog T + β, where P and T correspond to pellet and total mass fractions, respectively. The obtained normalization coefficients α and β were then applied to the pellet mass factions of all identified proteins. Statistical analyses using our five biological replicates were then performed, first to determine which proteins were significantly quantified (i.
[36] o well-known bulk glasses were used as references in this zone: silica (Infrasil)  [8]  and a bulk borophosphate niobium (Bulk-BPN) glass. [16] Both of them were poled using a homogeneous electrode. Their Maker fringe analysis (data not presented here because similar results were published in our previous works)  [8, 29]  confirmed for both of them the electrooptic origin of the SHG signal. The values of the second-order susceptibilities estimated by this technique as well as the fitting parameters are shown in Table  2. Note that the thickness of the SHG-active layer for these reference samples was evaluated by other means (following the methodology described in our previous work). [16] he only unknown parameter in these fits was the magnitude of the χ  (2)  , thus making this technique robust.