dataesr/scientific-paragraphs-categorization huggingface dataset:
The input ports of the circuitry are connected to the five working electrodes (WEs) of the microfluidic cartridge via an inverting amplifier and an analog matrix switch. The input ports of the circuitry can be connected to any of the working electrodes individually or to all of them simultaneously. The DC voltage of the working electrodes is adjusted by a D/A convertor connected to the non-inverting input port of the amplifier. The impedance measurement unit was also used to measure the impedance of four pairs of fill sensors that are integrated within the microfluidic cartridge. The measurement is based on Nyquist plot followed by fitting of data with equivalent circuits where the Rct is in parallel with Cdl and all in series with Rs as the resistance of solution. The Warburg impedance is not observed since at high frequencies, the Warburg impedance is small given that the diffusing reactants are not required to move very far.
The results are compared with numerical integration computed with Scipy python library, using Gauss-Kronrod quadrature formula  (Kronrod, 1965). Numerical results, longer to assess (10 times longer than an unoptimized straightforward implementation of the presented method) and therefore not usable in optimization or finite element simulation codes, are considered accurate and used as a basis for comparison on Table  1  which provides the relative errors between the different methods. S R=1 S R=0. 5 S R=0. 01 Bazant (directions penalization) 1. 10 -6 % 4. 8% 7. 9% Bazant (weights penalization) 1. 10 -6 % 5. 2% 32% Proposed method (112 directions) 2. 10 -3 % 2. 10 -3 % 3. 10 -3 % Proposed method (422 directions) 2. 10 -4 % 3. 10 -4 % 3. 10 -4 % Table 1: Relative error for numerical integration over a sphere, an ellipsoid with an axis ratio of 0.
,   Gasser et al. , 2006). The model is parameterized using a set of micro-structural parameters derived from fibers distribution (A,θ) and a set of mechanical parameters related to macromolecules (C,N ). First, structural parameters are imposed in order to identify the material parameters on one experimental data set. In a second step, the structural parameters are identified using the precedent identified material parameters and compared to real parameters. The quality of the fittings are evaluated by computing the coefficient of determination R 2. In the present paper, from two different individuals, epigastric anterior rectus sheath were sampled  (Astruc et al. , 2018). From each sample, three specimens were retrieved very close to each others to asssume the fibers orientations are equivalent.
Identification of material parameters The first individual is used to obtain material parameters (C,N ). A classical multi-photon confocal image is given in Fig. 13-A   and modeled curves along the three directions, using a Truncated-Newton algorithm  (Dembo and Steihaug, 1983) , available in Python library Scipy  (Jones et al. , 2001). The material parameters, C and N , for collagen fibers are given in Table  2 :   (Astruc et al. , 2018) , the moduli ranged from 0. 39 MPa in small deformations to 15 MPa in large deformations. However, in this constitutive model, the C parameter does not correspond to the stiffness of the entire tissue, but to the stiffness of the unit element, the fiber. Sherman et al. (2015)  conducted a literature review on collagen tissues at different scales. The rigidity of the collagen molecule is in the GPa range while the whole tissue has a modulus in the MPa range, or even kPa.
Simulation of the Electromagnetic Field Distribution in Monomodal Cavities The commercial simulation software package, COMSOL 5. 1, was used to model the electromagnetic field, power absorption, and sample temperature in the T 111 and T 10× cavities. Three different physics were considered in the model: electromagnetic waves, heat transfer and fluid dynamics  [23]. For simplicity, the simulated sample consisted in an uncoated SiC monolith. A physics-controlled mesh size was adopted. The magnetic field contribution was neglected, the variation of the dielectric properties of each material with temperature was defined by the user and the 3D wave equation was only applied in the air domain inside the waveguide. In particular, the experimental dielectric values obtained for β-SiC were employed.
We have used the FEMM software to calculate the force between two spheres placed in a constant magnetic field H: F rFEM = 2πa 2 π 0 σ rr cos(θ ) -σ rθ sin(θ ) sin(θ )dθ (4) with σ rr = µ 0 (µ f H 2 r -0. 5H 2 ) σ rθ = µ 0 µ f H r H θ In our case the carrier liquid was non-magnetic and so µ f =1. The fields H r and H θ are the field normal and tangential to the internal surface of the particle, respectively. In Figure  S2 , we have compared the dependence of these three models on the amplitude of the magnetic field for a separation distance of 0. 01a and a radius of 1 mm. As shown in this figure, the multipolar force (Equation  1 ) and the FEM calculation (Equation  4 ) gave the same result at low field as expected but above H = 25 kA/m, the multipolar model overestimates the force. The analytical model (Equation  3 ) largely overestimates the force.
Preparation of Materials The polymer PLA2002D was obtained from NatureWorks ® Ingeo™ (Minnetonka, MN, USA); its weight average molecular weight (MW) was about 120 kg•mol -1. Orotic acid (Figure  1 ) was from Sigma-Aldrich (St. Louis, MO, USA). It was in the form of fine powder, the grains were of uneven shape, where the majority of particle sizes was in the interval from 7 to 30 µm. The distribution of the particle cross-section arreas was evaluated with optical microscopy using ImageJ 1. 5 software (Wayne Rasband, National Institutes of Health, Bethesda, MD, USA) (Figure  S1  in Supplementary Materials). OA has melting point of about 345 • C so it was still solid at the processing temperature. First, PLA masterbatch with 5% (w/w) of OA was prepared by melting and mixing the components in the two-screw laboratory mini-extruder DSM Xplore 15 (Xplore Instruments BV, Sittard, The Netherlands) at 190 • C for 5 min.
Scanning Electron Microscopy (SEM) Particles of OA and PLA film materials were analyzed with the Phenom Pro (Thermo Fisher Scientific, Waltham, MA, USA) SEM. The samples were observed at the acceleration voltage of 10 kV in the backscattered electron mode. Measurements were carried out on samples without prior metallization using a special sample holder for Phenom Pro. Image analysis of the orotic acid particles was done with the ImageJ 1. 5 software (Wayne Rasband, National Institutes of Health, Bethesda, MD, USA). The size of individual particles was determined from threshold-adjusted SEM images.
Three parallel flasks were run for each sample, along with four blanks. The experimental data were used to derive basic parameters of the biodegradation curves with the help of a mathematical model adapted from  [35] : Cco 2 = Cco 2Max 1 + exp 2 + 4k Cco 2Max (C -t) - Cco 2Max 1 + exp 2 + 4k Cco 2Max C (5) where C CO 2Max is the maximal level of evolved CO 2 carbon expressed as the % of the maximal theoretical value; k represents the maximal rate of CO 2 production (days -1 ) and C is the length of the lag phase (days). The modeling was done in open source software Gnuplot (version 5. 2, Thomas Williams, Colin Kelley).
It could be seen that after 20 h of exposure, the OA peak was eliminated, providing an evidence of compound photodegradation. The photodegraded samples were further evaluated in melt rheology experiments using plateplate geometry. Data for the PLA materials with the increasing content of OA were displayed in the form of Cole-Cole plots (Figure  5 ) as typical semicircle traces in the complex plane. It is evident that the storage modulus decreases with the increasing content of OA for non-irradiated samples; hence, OA provides some level of lubrication in the PLA matrix. The intersections of the semicircles with "x" axis correspond to the zero-shear viscosity (η0), which is proprotional to MW of the polymer (Equation (  4 )). Comparing the traces for the increasing irradiation times, it is obvious that the photodegradation was accompanied by polymer chain scissions and resulted in a marked decrease in its MW.
3% OA content dropped to about 80 kg•mol -1 at the end of the period observed in Figure  5. In the later phase of the photodegradation, OA was probably degraded already, as could be assumed from UV-VIS spectra (Figure  4 ), and the zero shear viscosity for all materials with different contents of OA leveled at about 0. 3 Pa•s -1 (Figure  6 ). The photodegraded samples were further evaluated in melt rheology experiments using plate-plate geometry. Data for the PLA materials with the increasing content of OA were displayed in the form of Cole-Cole plots (Figure  5 ) as typical semicircle traces in the complex plane. It is evident that the storage modulus decreases with the increasing content of OA for non-irradiated samples; hence, OA provides some level of lubrication in the PLA matrix. The intersections of the semicircles with "x" axis correspond to the zero-shear viscosity (η 0 ), which is proprotional to MW of the polymer (Equation (  4 )).
The following gradient was used to separate the 5 fungicides: (solvent A water, solvent B acetonitrile) 50% of B from 0 to 2 min, 70% of B from 2 to 8 min, 90% of B from 8 to 10 min, 50% of B from 10 to 12 min. Finally, a 2 min reconditioning step was applied at the initial conditions. A calibration curve was constructed over the range 0. 1-500 µmol⋅L -1 of each fungicide. Eight standards were prepared in (90/10, v/v, water/ethanol) solutions. The calibration curve equations and the correlation coefficients were y = 18648x + 18401 (R 2 = 0. 9991) for iprodione; y = 10682x + 8412 (R 2 = 0. 9993) for procymidone; y = 7428x -2736 (R 2 = 0. 9996) for pyrimethanil; y = 30934x + 7228 (R 2 = 0. 9994) for azoxystrobin and y = 7217x -3109 (R 2 = 0. 9996) for iprovalicarb. Statistical analysis (ANOVA with Tukey's post hoc analysis) was done using (XLSTAT, Addinsoft) software.
Acknowledgements This work was supported by the  Regional Council of Burgundy  and the  European Union  via  FEDER  ( Fonds Européen de Développement Régional ) funding. We are grateful to  AgroSup Dijon  for cofunding this research program. The authors thank  Fleur-Anne RIO  and  Camille DETANG  for their contribution to the experimental work. They thank  Anne-Sophie VIAUX  for the Laser diffraction analysis and Laurence DUJOURDY for helpful discussion about the design of experiment.
Preparation of the NiOx/CeO2-ZrO2 samples A series of nanostructural CeO2-ZrO2 supports of various compositions (CeO2 content from 100 to 0 %) has been prepared by a supercritical fluid technique starting from aqueous or water-ethanol solutions of ammonium cerium(IV) and zirconium(IV) nitrates (Sigma-Aldrich) as precursors. The solutions of such precursors have been contacted at the mixing point between two injection lines at temperature of 150 °C prior to enter them into a homemade continuous-flow reactor in which temperature was fixed at 400 °C and pressure at 25 MPa. Temperature and pressure have been selected to exceed the critical parameters of the water-ethanol mixture with a 29:71 molar ratio (Tc = 283. 55 °C, pc = 11. 69 MPa, NIST Standard Reference Database). Processes of forced hydrolysis, nucleation and growth of the CeO2-ZrO2 nanoparticles occurred thus under supercritical conditions.
Scanning electron microscopy (SEM) micrographs were recorded on a JEOL FEG 6700F microscope working at 9 kV accelerating voltage. The diffuse reflectance ultraviolet/visible (UV/Vis-DR) spectra of the investigated samples were recorded using a Perkin-Elmer Lambda 650 UV/Vis spectrophotometer with Praying Mantis (Harrick). The measurements were performed in the range of 200-900 nm with a resolution of 1 nm. The spectra were recorded under ambient conditions and the data transformed according to the Kubelka-Munk equation. Deconvolution of spectra was carried out using PeakFit4 software. The X-ray photoelectron spectroscopy (XPS) analyses were carried out in a PHI VersaProbeII Scanning XPS system using monochromatic Al Kα (1486. 6 eV) X-rays focused to a 100 µm spot and scanned over the sample area of 400 µm x 400 µm.
The photoelectron take-off angle was 45° and the pass energy in the analyzer was set to 23. 50 eV to obtain high energy resolution spectra for the C 1s, O 1s, Zr 3d, Ce 3d and Ni 2p regions. A dual beam charge compensation with 7 eV Ar + ions and 1 eV electrons were used to maintain a constant sample surface potential regardless of the sample conductivity. All XPS spectra were charge referenced to the unfunctionalized, saturated carbon C1s peak at 284. 8 eV. The operating pressure in the analytical chamber was below 4•10 -9 mbar. Deconvolution of spectra was carried out using PHI MultiPak software (v. 9. 7. 0. 1). Spectrum background was subtracted using the Shirley method.
min -1. After thermal treatments, relative density of samples was determined using Archimedes method in ethanol. Before microstructural observations, sintered samples were previously polished with SiC grinding paper and 0. 1 µm alumina suspension and thermally etched under air atmosphere during 30 minutes at temperatures lower than sintering temperature by 100°C. Conventional SEM (IT300 JEOL, Japan) was used to observe samples microstructure. The grain size was determined by the intercept method using ImageJ software (« Image Processing and Analysis in Java », National Institutes of Health, Etats-Unis).
The Schmidt number of the passive scalar is set to S c ¼ 1. This DNS is henceforth called the Inert Spatially Evolving case and additional information is given in Table  1. To identify the effects of the spatially evolving nature of the previously outlined cases on the scalar fields, DNS data of a temporally evolving non-reacting jet, referred to as the Inert Temporally Evolving case, are included in this investigation. The non-dimensional DNS features a comparable Jet Reynolds number to the High Re Flame of Re jet ¼ 9; 850. The flow and the scalar fields are statistically homogeneous in the stream-wise direction x and spanwise direction y. The non-dimensional size of the domain is L x ¼ 6π, L y ¼ 6π, and L z ¼ 12:5, discretized by 2560 × 2560 × 1312 grid points. The initial mean velocity profile was initialized as two mirrored hyperbolic-tangent profiles.
Acknowledgments The authors acknowledge funding from of the  European Research Council (ERC)  under the European Union's  Horizon 2020 research and innovation program  under grant agreement No  695747. In addition, the authors gratefully acknowledge the computing time provided by the  JARA High Performance Computing Partition  ( JHPC09  and  JHPC22 ) on the supercomputers JUQUEEN and JURECA at the  Jülich Supercomputing Centre.
Predictive Capabilities for New Experimental Results In this section we use the aforementioned GENERIC regression to predict the experimental results for an indentation velocity ż = 2 µm/s, while not being present in the training database. For that aim, we will use the GENERIC formalism matrices A, M and B obtained at ż = 0. 5 µm/s and ż = 8 µm/s. Using these results, we predict the matrices at ż = 2 µm/s using a linear interpolation approach. For instance: A @2µm/s = A @0. 5µm/s × 6. 5 + A @8µm/s × 1. 5 8. (14) Using the linear interpolation approach, we predict the GENERIC formalism matrices. Eventually, using a more accurate interpolation scheme is an option for interested users (Kriging for example). The prediction results are illustrated in Figures  8 9 10. The results show good predictions bounded between the two fitted quantities of interest at ż = 0.
6 nm, a little bit smaller than the 5. 1 nm NiAl2O4 crystallites reported earlier by Fan X. et al. in a study of a mesoporous nickelalumina material with 5 wt% Ni  [21]. At this point, it can be added that such sizes keep rather small for species that contain both nickel and aluminum atoms, explaining why the Ni-based nanospecies could not be detected by TEM in the calcined materials, neither in Ni5wt%-Al2O3-MOF nor in Ni5wt%-Al2O3-EISA. Nevertheless, the presence of nickel and its homogeneous distribution throughout the alumina matrices were totally confirmed by local TEM/EDS analyses in both calcined samples (data not detailed). The presence of nickel and its content were also validated by temperature programed reduction (TPR) experiments during which oxidized nickel (Ni 2+ ions or NiO) was transformed to Ni 0 (the active state for DRM).
The mean particle size of the crystalline NiAl 2 O 4 domains estimated by Scherer equation in this MOF-based sample is around 4. 6 nm, a little bit smaller than the 5. 1 nm NiAl 2 O 4 crystallites reported earlier by Fan X. et al. in a study of a mesoporous nickel-alumina material with 5 wt% Ni  [21]. At this point, it can be added that such sizes keep rather small for species that contain both nickel and aluminum atoms, explaining why the Ni-based nanospecies could not be detected by TEM in the calcined materials, neither in Ni 5wt% -Al 2 O 3-MOF nor in Ni 5wt% -Al 2 O 3-EISA. Nevertheless, the presence of nickel and its homogeneous distribution throughout the alumina matrices were totally confirmed by local TEM/EDS analyses in both calcined samples (data not detailed). The presence of nickel and its content were also validated by temperature programed reduction (TPR) experiments during which oxidized nickel (Ni 2+ ions or NiO) was transformed to Ni 0 (the active state for DRM).
With these settings, the corresponding convergence semiangle was 12 mrad, and the inner and outer collection semiangles on the STEM-HAADF detector were 90 and 390 mrad, respectively. Average sizes of nickel particles, when visible, were estimated using the ImageJ software and taking at least 500 particles into consideration. Powder X-ray diffraction (XRD) measurements were performed in the 2θ range 20-90 • on a PANalytical XPert3 diffractometer using a CuKα radiation (λ = 1. 5405 nm), a voltage of 30 Kv, a current of 10 mA and a time step of 2 s. Known ICDD powder XRD files were used to identify crystalline phases and mean sizes of crystalline domains (nanoparticles) were calculated using the Scherer's equation Dhkl = Kλ/βcosθ, where K is the shape factor of the average spherical crystalline, λ is the wavelength (1.
The sample was evacuated under a vacuum of less than 10 -10 mbar, then a monochromatic X-ray (Al Kα) irradiated the sample and excited the electrons. Surface compositions were determined by attributing the observed energy peaks to a specific element and quantifying their area using the Casa XPS software. Stability tests during dry methane reforming reaction were conducted in a fixed bed reactor after in situ reduction of the calcined material at 800 • C for 2 h (heating rate 5 • C•min -1 ) under 30 mL•min -1 of 5 vol% H 2 /Ar. The tests were carried out at 650 • C and atmospheric pressure for 10 h under a flowing reactant gas composed of an equimolar amount of CH 4 and CO 2 diluted in Ar (atomic ratio 5/5/90). The hourly space velocity (GHSV) was chosen equal to 72 L•g -1 •h -1 from previous measurements  [17, 20].
Computational A molecular modelling study of the reactions that could explain the formation of detected products from glycerol transformation was carried out. All calculations (energies, optimizations, and frequencies) were performed at B3LYP density functional theory level (DFT), using the 6-311++G(d,p) basis set implemented in Gaussian 09 software  [25]. This basis set was selected based on a previous work published by  Chelli et al. [3]  who calculated the structural and vibrational properties of glycerol with high level of accuracy and computational efficiency using a similar basis set. Calculations of transition states for each elementary reaction were done to obtain thermodynamic and kinetic information (using the transition state theory) that fits the experimental results. All structures were optimized in their electronic ground state, which correspond to the multiplicity with the lowest energy.
In order to avoid any condensation of the fuel, the tube, the tanks and the manifold are heated up to 80 °C to allow the partial pressure of the 3-pentanol be at least three times lower than its vapor pressure. The data acquisition system has a frequency of 1 MHz and includes a NI Compact RIO which records the pressure signals from four individual piezoelectric pressure transducers PCB 113B22 in order to calculate the shock velocity and from a Kistler piezoelectric pressure transducer (603B1) located at the end-wall to calculate the ignition delay time and determine post-shock pressure, P5. It is defined as the time interval between the rebound of the shock wave at the end-wall and the onset of combustion, commonly defined by a sudden change in pressure (inflection point), see Figure  1. Postshock temperature, T5, is calculated from the shock wave velocity and the initial conditions based on the 1-D shock relations and the species thermodynamics using the chemical equilibrium software Gaseq  [16]  with an accuracy of ±1% which corresponds to ±10-15K according to the uncertainty calculation proposed by Petersen et al.
Shock tube experiments Mixtures of 1% 3-pentanol in O2/Ar are tested in a high-pressure shock tube at 20 and 40 bar of pressure and equivalence ratios of 0. 5, 1 and 2 between 1000 and 1460 K. No pressure rise was recorded after the reflected shock wave prior to the main ignition event. Kinetic model and experiment comparisons are presented in figure  10. The influence of the experimental conditions (temperature, pressure and equivalence ratio) on ignition delay times is observed to be as expected: the ignition delay times decrease with increasing pressure and temperature as well as increasing oxygen concentration. The effect of equivalence ratio is more apparent at 20 bar than at 40 bar, experimentally. Kinetic model agrees very well with the data for the mixtures ϕ = 0. 5 and 1, however predicts longer ignition delay times regardless of the pressure as far as the ϕ = 2 mixtures are concerned, although the global activation energy is correct.
Conclusion High pressure oxidation of 3-pentanol is investigated experimentally in a JSR and in a shock tube, for the first time. Mole fraction profiles of the reactants, final products, and stable intermediates are identified and measured by gas chromatography, mass spectrometry, and Fourier transform infrared spectrometry after sonic probe sampling at five equivalence ratios. Ignition delay times are measured for 1% fuel in O2/Ar mixtures at 20 and 40 bar for 3 equivalence ratios. Under the investigated conditions, 3-pentanol did not show any cool flame behavior and is found to produce various aldehydes and ketones as well as the olefin 2-pentene as one of its C5 intermediates. A submechanism for 3-pentanol was developed in order to represent the data with globally good performance, however some discrepancies were observed in species profiles, which suggest further work.
To test these two propositions, the solid-state magnetism was measured. The temperature-dependent magnetic data were recorded and χ and χT were plotted versus T and are represented in Figure  3. The χT value decreased gradually with decreasing temperature until the value approached zero, with two inflection points around 65 and 170 K. The near-zero value at low temperature indicates a singlet ground state while the value of 2. 3 emu•K•mol -1 is close to the theoretical value obtained by the sum of a 2 F state (f 13 ) and a 2 S state (bipym• -). The χ value versus the temperature is more indicative of the magnetic behavior of 2: a maximum was obtained at 170 K while the low-temperature data was low and independent of the temperature (temperature-independent paramagnetism (TIP) or Van Vleck paramagnetism)  [42, 43].