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18 pages, 13375 KiB  
Article
Numerical Simulation of 50 mm 316L Steel Joint of EBW and Its Experimental Validation
by Xiaowei Xia, Jiefeng Wu, Zhihong Liu, Jianguo Ma, Haibiao Ji and Xiaodong Lin
Metals 2022, 12(5), 725; https://doi.org/10.3390/met12050725 - 24 Apr 2022
Cited by 5 | Viewed by 2503
Abstract
The 316L thick plate electron beam welding (EBW) has been widely used in fusion test reactor manufacturing. Therefore, the numerical simulation of the 50 mm 316L austenitic stainless steel by two heat sources and experimental on microstructure and residual stress have been studied [...] Read more.
The 316L thick plate electron beam welding (EBW) has been widely used in fusion test reactor manufacturing. Therefore, the numerical simulation of the 50 mm 316L austenitic stainless steel by two heat sources and experimental on microstructure and residual stress have been studied in this article. In the simulation study, the traditional heat source model (3D Gaussian heat source) and composite heat source (double ellipsoid heat source superimposed on the 3D Gaussian heat source) were proposed to simulate the welding of local joint. Weld cross-section, temperature curve, and residual stress after welding obtained by simulations were investigated. The experimental study involved residual stress tests and microstructure analysis. It turned out that the result of the composite heat source was closer to the actual joint. The residual stress distribution of simulation was validated and in accordance with experimental measurement. Moreover, the microstructures were studied by electro backscattered diffraction (EBSD) and compared with the temperature curve. The formation mechanism of microstructural heterogeneity was caused mainly by different thermal cycles at different positions of the thick plate. The top of the joint was more prone to stress concentration. Full article
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<p>Technology roadmap.</p>
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<p>Schematic diagram: the dimensions of test plate, EBW welding direction.</p>
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<p>Schematic diagram: sampling location of the EBSD samples (a, b, c), sample placement direction (TD, RD).</p>
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<p>Simulation framework of thermo–mechanical FE simulation. Reprinted from refs. [<a href="#B10-metals-12-00725" class="html-bibr">10</a>,<a href="#B11-metals-12-00725" class="html-bibr">11</a>].</p>
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<p>Finite element meshing for the local welded joint.</p>
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<p>Traditional heat source model: (<b>a</b>) double ellipsoid heat source, (<b>b</b>) 3D Gaussian heat source. Reproduced from [<a href="#B16-metals-12-00725" class="html-bibr">16</a>,<a href="#B18-metals-12-00725" class="html-bibr">18</a>], with permission from Ji-Jun Xin, 2022.</p>
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<p>Composite heat source (double ellipsoid heat source superimposed on 3D Gaussian heat source). Reproduced from [<a href="#B10-metals-12-00725" class="html-bibr">10</a>], with permission from Elsevier, 2019.</p>
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<p>The constraints for the simulation: (<b>a</b>) symmetric constraint settings for simulation of local welded joint, (<b>b</b>) clamping positions for free clamps and rigid clamps.</p>
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<p>The simulated transient temperature contours using 3D Gaussian heat source at different times: (<b>a</b>) 5 s, (<b>b</b>) 30 s, (<b>c</b>) 60 s, (<b>d</b>) 100 s.</p>
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<p>The simulated transient temperature contours using a composite heat source at different times: (<b>a</b>) 5 s, (<b>b</b>) 30 s, (<b>c</b>) 60 s, (<b>d</b>) 100 s.</p>
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<p>Comparison between simulation and experiment on weld cross-section using: (<b>a</b>) 3D Gaussian heat source, (<b>b</b>) composite heat source.</p>
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<p>Schematic diagram of path BC, B′C′, AD, BB′.</p>
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<p>The simulated thermal cycle curve (°C) using the 3D Gaussian heat source in different paths: (<b>a</b>) BC, (<b>b</b>) B′C′, (<b>c</b>) AD, (<b>d</b>) BB′.</p>
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<p>The simulated thermal cycle curve (°C) using the composite heat source in different paths: (<b>a</b>) BC, (<b>b</b>) B′C′, (<b>c</b>) AD, (<b>d</b>) BB′.</p>
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<p>The simulated stresses contour maps at a time of: (<b>a</b>) 60 s, (<b>b</b>) 600 s.</p>
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<p>The simulated distribution of residual stresses in BC direction: (<b>a</b>) transverse, (<b>b</b>) longitudinal.</p>
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<p>The simulated distribution of residual stresses in AD direction: (<b>a</b>) transverse, (<b>b</b>) longitudinal.</p>
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<p>Residual stresses measurement by blind hole method (σ is stress, R is the resistor).</p>
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<p>Comparison of test and simulation residual stresses results in BC path.</p>
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<p>IPF maps of: (<b>a</b>) “a” sample, (<b>b</b>) “b” sample, (<b>c</b>) “c” sample, (<b>d</b>) base metal. See the sampling location of the EBSD samples in <a href="#metals-12-00725-f003" class="html-fig">Figure 3</a>.</p>
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<p>KAM maps of: (<b>a</b>) “a” sample, (<b>b</b>) “b” sample, (<b>c</b>) “c” sample.</p>
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<p>The grain diameter of the welded joint.</p>
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<p>Misorientation angle in the welded joint.</p>
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12 pages, 3367 KiB  
Article
Mechanical Properties of Tensile Cracking in Indium Tin Oxide Films on Polycarbonate Substrates
by Jiali Zhou, Xuan Zhang, Xiaofeng Zhang, Wenqiao Zhang, Jiuyong Li, Yuandong Chen, Hongyan Liu and Yue Yan
Coatings 2022, 12(4), 538; https://doi.org/10.3390/coatings12040538 - 17 Apr 2022
Cited by 19 | Viewed by 3671
Abstract
The electro-mechanical behaviors of transparent conductive oxide film on polymer substrate are of great concern because they would greatly affect the stability and lifespan of the corresponding devices. In this paper, indium tin oxide (ITO) films with different thicknesses were deposited on a [...] Read more.
The electro-mechanical behaviors of transparent conductive oxide film on polymer substrate are of great concern because they would greatly affect the stability and lifespan of the corresponding devices. In this paper, indium tin oxide (ITO) films with different thicknesses were deposited on a polycarbonate (PC) sheet; meanwhile, in situ electrical resistance, in situ scanning electron microscopy and profilometry were employed to record the electrical resistance, morphologies and residual stress in order to investigate the fracture behavior and electrical-mechanical properties of ITO films under uniaxial tension loading. The electrical resistance changes, crack initiation, crack propagation and crack density evolution of ITO films were systematically characterized by in situ tests. Three fracture stages of ITO films were summarized: Ⅰ crack initiation, Ⅱ crack propagation, Ⅲ crack saturation and delamination. The crack initiation and electrical failure in a thinner ITO film occurred at relatively higher applied tensile strain; namely, the ductility of the film decreased as the film thickness increased. Residual compressive stress was recorded in the ITO films deposited on PC at room temperature and increased as the film thickness increased. Intrinsic crack initiation strain (CIS*) showed an opposite thickness dependence to residual strain (εr); the increase in residual compressive strain was counteracted by the decrease of intrinsic cohesion, leading to an overall decrease in effective crack initiation strain (CIS) when the film thickness increased. In addition, integrated with a formulated mechanics model and the analysis of the three fracture stages under tension, the fracture toughness and interfacial shear strength were quantitatively determined. As the film thickness increased (in the range of 50~500 nm), the fracture toughness decreased and the films were more prone to crack, whereas the interfacial shear strength increased and the films were less likely to delaminate. Full article
(This article belongs to the Topic Inorganic Thin Film Materials)
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Graphical abstract
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<p>(<b>a</b>) Fractional change in resistance (ΔR/R<sub>0</sub>) of ITO with different thicknesses deposited on PC as a function of strain ε; (<b>b</b>) ΔR/R<sub>0</sub>~ε curve of ITO with 500 nm thickness deposited on PC under different strain rates. R<sub>0</sub> denoted the electrical resistance of the unloaded ITO thin film.</p>
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<p>Stress–strain curves of PC substrate and ITO film on PC. Illustrations are surface topography of 500 nm ITO film after unloading: (<b>a</b>) Stretched to 2.2% strain; (<b>b</b>) stretched to 5% strain.</p>
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<p>Three fracture stages of ITO film (50 nm) under uniaxial tension: Stage I, crack initiation; stage II, crack propagation; stage III, crack saturation and delamination.</p>
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<p>Typical process of crack initiation, propagation, saturation and delamination in 50 nm ITO film on PC. (<b>a</b>,<b>b</b>) were stage I, crack initiation; (<b>c</b>–<b>e</b>) were stage II, crack propagation; (<b>f</b>–<b>i</b>) were stage III, crack saturation and delamination.</p>
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<p>Buckling and fracture of 50 nm ITO film on PC. (<b>b</b>) was an enlarged drawing of (<b>a</b>).</p>
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<p>ITO films with different thicknesses on PC substrate: (<b>a</b>) CD; (<b>b</b>) CIS(t) and CD<sub>s</sub> (t).</p>
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<p>(<b>a</b>) The crack density and the variation of electrical resistance of ITO films with different thicknesses deposited on PC substrates as a function of the applied strain; (<b>b</b>) A model showing the conductive layer between ITO fragments.</p>
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<p>Film thickness dependence of internal stress measured crack initiation strain, and intrinsic crack initiation strain of ITO films. The thick continuous lines are power-law fits (with exponent equal to −0.76) to CIS*.</p>
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21 pages, 13257 KiB  
Article
The Effect of Laser Beam Processing on the Properties of WC-Co Coatings Deposited on Steel
by Norbert Radek, Janusz Konstanty, Jacek Pietraszek, Łukasz J. Orman, Marcin Szczepaniak and Damian Przestacki
Materials 2021, 14(3), 538; https://doi.org/10.3390/ma14030538 - 23 Jan 2021
Cited by 37 | Viewed by 2682
Abstract
The main objective of the present work is to determine the effects of laser processing on properties of WC-Co electro-spark deposited (ESD) coatings on steel substrates. Tungsten carbide coatings have been applied to steel substrates using a manual electrode feeder, model EIL-8A. The [...] Read more.
The main objective of the present work is to determine the effects of laser processing on properties of WC-Co electro-spark deposited (ESD) coatings on steel substrates. Tungsten carbide coatings have been applied to steel substrates using a manual electrode feeder, model EIL-8A. The laser beam processing (LBP) of electro-spark coatings was performed using an Nd:YAG fiber laser. The microstructure and properties of laser treated/melted coatings were evaluated by means of scanning electron microscopy (SEM), X-ray diffraction (XRD), surface geometric structure (SGS) and roughness measurements and adhesion, microhardness, residual stresses, corrosion resistance and application tests. The obtained experimental data were subjected to statistical analysis and multidimensional numerical and visual exploratory techniques. It has been shown conclusively that the laser-treated ESD WC-Co coatings are characterized by lower microhardness, higher resistance to corrosion, increased roughness and better adhesion to the substrate. LBP homogenizes the chemical composition, refines the microstructure and heals microcracks and pores of ESD coatings. The laser treated ESD WC-Co coatings can be used in frictional sliding nodes (e.g., on the front seal rings used in pumps) and as protective layers. Full article
(This article belongs to the Special Issue Laser Treatment for Surface Layers)
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<p>Particle morphology of submicron-grained powders: (<b>a</b>) cobalt and (<b>b</b>) tungsten carbide.</p>
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<p>Pulse-plasma sintering (PPS) sintering facility.</p>
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<p>Fabrication of an electrode by PPS.</p>
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<p>As-deposited microstructure of the WC-Co coating.</p>
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<p>Distribution of elements on the WC-Co coating surface.</p>
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<p>Microstructure of the WC-Co coating within the WC-Co coating after laser beam processing (LBP).</p>
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<p>Distribution of elements on the WC-Co coating surface after LBP.</p>
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<p>EDS analysis of the electro-spark deposited (ESD) WC-Co coatings: (<b>a</b>) as-deposited and (<b>b</b>) after LBP.</p>
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<p>XRD patterns of the WC-Co coatings: (<b>a</b>) before LBP and (<b>b</b>) after LBP.</p>
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<p>Topography of coatings: (<b>a</b>) before LBP and (<b>b</b>) after LBP.</p>
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<p>Distribution of ordinates and specimen bearing curves: (<b>a</b>) before LBP and (<b>b</b>) after LBP.</p>
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<p>Isotropy of samples. (<b>a</b>) Before LBP and (<b>b</b>) after LBP.</p>
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<p>Examples of surface profiles of WC-Co coatings: (<b>a</b>) before LBM and (<b>b</b>) after LBM (perpendicular).</p>
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<p>Three dimensional images of scratches made on the WC-Co coatings: (<b>a</b>) before LBP and (<b>b</b>) after LBP.</p>
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<p>Raw data obtained from adhesion tests.</p>
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<p>Microhardness measurement results.</p>
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<p>Comparison of the microhardness at particular locations before and after LBP.</p>
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<p>Comparison of microhardness at particular locations before and after LBP.</p>
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<p>Scree plot for the microhardnesses dataset.</p>
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<p>PCA1 vs. PCA2 plot revealing clustering of the microhardnesses dataset.</p>
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<p>Polarization curves of the tested samples.</p>
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<p>Experimental setup for measuring residual stresses using the Waisman–Phillips method.</p>
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<p>Distribution of residual stresses in the WC-Co coating in the as-coated and laser treated condition.</p>
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<p>The flange of a gas cylinder with a permanent mark.</p>
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<p>Worn marker intended for regeneration.</p>
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<p>Marker with WC-Co ESD coating (without LBP).</p>
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<p>Lathe turning of 40H steel bars with an HS6-5-2 HSS indexable insert: cutting speed v<sub>c</sub> = 57 m/min, workpiece rotation n = 450 rpm and feed <span class="html-italic">p</span> = 250 mm/min.</p>
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<p>Computerised Numerical Control CNC lathe with a feeder.</p>
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<p>Joint with an inner thread.</p>
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17 pages, 11672 KiB  
Article
The Analysis of Micro-Scale Deformation and Fracture of Carbonized Elastomer-Based Composites by In Situ SEM
by Eugene S. Statnik, Semen D. Ignatyev, Andrey A. Stepashkin, Alexey I. Salimon, Dilyus Chukov, Sergey D. Kaloshkin and Alexander M. Korsunsky
Molecules 2021, 26(3), 587; https://doi.org/10.3390/molecules26030587 - 22 Jan 2021
Cited by 10 | Viewed by 3271
Abstract
Carbonized elastomer-based composites (CECs) possess a number of attractive features in terms of thermomechanical and electromechanical performance, durability in aggressive media and facile net-shape formability, but their relatively low ductility and strength limit their suitability for structural engineering applications. Prospective applications such as [...] Read more.
Carbonized elastomer-based composites (CECs) possess a number of attractive features in terms of thermomechanical and electromechanical performance, durability in aggressive media and facile net-shape formability, but their relatively low ductility and strength limit their suitability for structural engineering applications. Prospective applications such as structural elements of micro-electro-mechanical systems MEMS can be envisaged since smaller principal dimensions reduce the susceptibility of components to residual stress accumulation during carbonization and to brittle fracture in general. We report the results of in situ in-SEM study of microdeformation and fracture behavior of CECs based on nitrile butadiene rubber (NBR) elastomeric matrices filled with carbon and silicon carbide. Nanostructured carbon composite materials were manufactured via compounding of elastomeric substance with carbon and SiC fillers using mixing rolling mill, vulcanization, and low-temperature carbonization. Double-edge notched tensile (DENT) specimens of vulcanized and carbonized elastomeric composites were subjected to in situ tensile testing in the chamber of the scanning electron microscope (SEM) Tescan Vega 3 using a Deben microtest 1 kN tensile stage. The series of acquired SEM images were analyzed by means of digital image correlation (DIC) using Ncorr open-source software to map the spatial distribution of strain. These maps were correlated with finite element modeling (FEM) simulations to refine the values of elastic moduli. Moreover, the elastic moduli were derived from unloading curve nanoindentation hardness measurements carried out using a NanoScan-4D tester and interpreted using the Oliver–Pharr method. Carbonization causes a significant increase of elastic moduli from 0.86 ± 0.07 GPa to 14.12 ± 1.20 GPa for the composite with graphite and carbon black fillers. Nanoindentation measurements yield somewhat lower values, namely, 0.25 ± 0.02 GPa and 9.83 ± 1.10 GPa before and after carbonization, respectively. The analysis of fractography images suggests that crack initiation, growth and propagation may occur both at the notch stress concentrator or relatively far from the notch. Possible causes of such response are discussed, namely, (1) residual stresses introduced by processing; (2) shape and size of fillers; and (3) the emanation and accumulation of gases in composites during carbonization. Full article
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<p>Experimental stress–strain curves with indicated 95% confidence interval for (<b>a</b>) vulcanized and (<b>b</b>) carbonized specimens that were tested at a constant crosshead speed of 0.2 mm/min. The appearance of broken samples is shown in the lower row of images.</p>
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<p>Experimental characteristics obtained for carbonized specimens filled with SiC and tested for 0.5, 1.0, 1.5, and 2.0 mm/min traverse speeds.</p>
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<p>The example of the macro view for different specimens in various perspectives: (<b>a</b>) fractography and (<b>b</b>) cracks propagation.</p>
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<p>The microscopic appearance of sample fracture surfaces.</p>
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<p>Displacement (<b>top</b>) and stain (<b>below</b>) distribution along X-axis at nominal macro strain values of 0, 0.007, 0.015 and 0.022, respectively.</p>
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<p>Correlation of modeled (<b>left</b>) and experimental (<b>right</b>) strain fields.</p>
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<p>The roughness profile for vulcanized (<b>left</b>) and carbonized (<b>right</b>) specimens of EC-FC-1 composition.</p>
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<p>The Young’s modulus distribution of vulcanized (purple) and carbonized (blue) specimens of EC-FC-1 composite.</p>
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<p>The workflow of preparation composite materials based on the carbonized polymer matrix.</p>
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<p>The shape and dimensions of double-edge notched tensile (DENT) specimens.</p>
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<p>The view of the experimental setup—the chamber of the SEM Tescan Vega 3.</p>
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<p>The typical load–displacement curves and fracture appearance for a CEC after vulcanization (<b>1</b>) and carbonization (<b>2</b>).</p>
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<p>The pattern quality of the captured SEM images.</p>
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<p>The workflow of the digital image correlation (DIC) analysis.</p>
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<p>The schematic for finite element analysis (FEA) simulation.</p>
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<p>An example of fractography analysis in carbonized elastomer-based composites (CEC) specimens.</p>
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<p>Typical load–displacement curve at nanoindentation.</p>
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<p>The microstructure of prepared samples with different compositions.</p>
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15 pages, 863 KiB  
Article
The Proposition of a Mathematical Model for the Location of Electrical and Electronic Waste Collection Points
by Ítalo Ruan Barbosa de Aquino, Josenildo Ferreira da Silva Junior, Patricia Guarnieri and Lucio Camara e Silva
Sustainability 2021, 13(1), 224; https://doi.org/10.3390/su13010224 - 29 Dec 2020
Cited by 13 | Viewed by 2898
Abstract
Given the environmental impacts produced by the growing increase in waste electrical and electronic equipment (WEEE) and their current inadequate management, this article proposes a mathematical model to define the best location for installing WEEE collection points. The objective is to minimize the [...] Read more.
Given the environmental impacts produced by the growing increase in waste electrical and electronic equipment (WEEE) and their current inadequate management, this article proposes a mathematical model to define the best location for installing WEEE collection points. The objective is to minimize the cost of the reverse logistics system concerning transportation, installation, opportunity cost, and distance between points and demand. We used a heuristic created from the greedy randomized adaptive search procedure and genetic algorithm meta-heuristics to solve the model, with part of the model variables being defined by another heuristic or by the JuMP v.0.21.2 and CLP Solver v.0.7.1 packages, to guarantee an optimal response to a subproblem of these variables. The model and its solver were written in the Julia Programming Language and executed in two test scenarios. In the first, three vehicles with small loads must collect at five points. In the second, a vehicle with greater available capacity must collect at five points. The results obtained show that the mathematical model and the heuristic are adequate to solve the problem. Thus, we understood that the proposed method contributes to the literature, given the criticality of the current scenario concerning the management of WEEE, and it can assist managers and public policymakers when providing inputs for decision-making related to the choice of the best location for installing collection points. Full article
(This article belongs to the Section Sustainable Management)
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<p>District Maurício de Nassau, Caruaru, Pernambuco. Source: adapted from Google Maps (2019).</p>
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<p>Route to be travelled by the vehicle. Source: adapted from Google Maps (2019).</p>
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1421 KiB  
Review
Recent Advances on Electro-Oxidation of Ethanol on Pt- and Pd-Based Catalysts: From Reaction Mechanisms to Catalytic Materials
by Ye Wang, Shouzhong Zou and Wen-Bin Cai
Catalysts 2015, 5(3), 1507-1534; https://doi.org/10.3390/catal5031507 - 2 Sep 2015
Cited by 411 | Viewed by 28295
Abstract
The ethanol oxidation reaction (EOR) has drawn increasing interest in electrocatalysis and fuel cells by considering that ethanol as a biomass fuel has advantages of low toxicity, renewability, and a high theoretical energy density compared to methanol. Since EOR is a complex multiple-electron [...] Read more.
The ethanol oxidation reaction (EOR) has drawn increasing interest in electrocatalysis and fuel cells by considering that ethanol as a biomass fuel has advantages of low toxicity, renewability, and a high theoretical energy density compared to methanol. Since EOR is a complex multiple-electron process involving various intermediates and products, the mechanistic investigation as well as the rational design of electrocatalysts are challenging yet essential for the desired complete oxidation to CO2. This mini review is aimed at presenting an overview of the advances in the study of reaction mechanisms and electrocatalytic materials for EOR over the past two decades with a focus on Pt- and Pd-based catalysts. We start with discussion on the mechanistic understanding of EOR on Pt and Pd surfaces using selected publications as examples. Consensuses from the mechanistic studies are that sufficient active surface sites to facilitate the cleavage of the C–C bond and the adsorption of water or its residue are critical for obtaining a higher electro-oxidation activity. We then show how this understanding has been applied to achieve improved performance on various Pt- and Pd-based catalysts through optimizing electronic and bifunctional effects, as well as by tuning their surface composition and structure. Finally we point out the remaining key problems in the development of anode electrocatalysts for EOR. Full article
(This article belongs to the Special Issue Electrocatalysis in Fuel Cells)
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Graphical abstract
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<p>Schematic representation of the parallel pathways for ethanol oxidation on Pt electrodes in acidic media.</p>
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<p>Proposed reaction mechanism for electro-oxidation of ethanol on Pt electrodes. Solid arrows denote the mechanism at low electrolyte pH, while dashed arrows denote the mechanism at high electrolyte pH. Adapted from Reference [<a href="#B18-catalysts-05-01507" class="html-bibr">18</a>].</p>
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<p>The mechanism of ethanol oxidation at polycrystalline Pt in alkaline solutions proposed by Christensen. Reproduced with permission from Reference [<a href="#B20-catalysts-05-01507" class="html-bibr">20</a>] Copyright 2012, American Chemical Society.</p>
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<p>Reaction pathways for interfacial CH<sub>3</sub>CH<sub>2</sub>OH at Pd electrodes in alkaline media. Reproduced with permission from Reference [<a href="#B23-catalysts-05-01507" class="html-bibr">23</a>]. Copyright 2014, American Chemical Society.</p>
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<p>Reaction network calculated for ethanol electro-oxidation to CO<sub>2</sub>, methane, and acetate. Reproduced with permission from Reference [<a href="#B45-catalysts-05-01507" class="html-bibr">45</a>]. Copyright 2015, the Electrochemical Society.</p>
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<p>General scheme describing the ethanol oxidation reaction on Pd electrodes in the presence of an electrical double layer proposed by first principle calculations. Reproduced with permission from Reference [<a href="#B39-catalysts-05-01507" class="html-bibr">39</a>]. Copyright 2014, American Chemical Society.</p>
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<p>Calculated reaction network and reaction barriers (units, eV) for ethanol oxidation (<b>A</b>) on Pt (111) and acetyl oxidation (<b>B</b>) on Pt (211) (data on the left) and Pt (100) (data on the right). Reprinted and adapted with permission from Ref. [<a href="#B43-catalysts-05-01507" class="html-bibr">43</a>]. Copyright 2008, American Chemical Society.</p>
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<p>(<b>A</b>) Positive voltammetric scans for Pt(111) and Pt<sub>ML</sub> supported on five different substrates in 0.1 M HClO<sub>4</sub> containing 0.5 M ethanol; (<b>B</b>) <span class="html-italic">In situ</span> infrared reflection-absorption spectroscopy (IRRAS) spectra recorded during EOR on the Pt<sub>ML</sub>/Au(111) electrode in 0.1 M HClO<sub>4</sub> containing 0.5 M ethanol. Inserted are models of pseudomorphic monolayers of Pt on two different substrates of Au(111) and Pd(111). Reprinted and adapted with permission from Reference [<a href="#B105-catalysts-05-01507" class="html-bibr">105</a>]. Copyright 2012, American Chemical Society.</p>
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<p>Integrated band intensities of CO<sub>2</sub>, CH<sub>3</sub>CHO and CH<sub>3</sub>COOH in IRRAS spectra from (<b>a</b>). Pt–SnO<sub>2</sub>/C with the atomic ratio Pt:Sn = 3:4; (<b>b</b>). Pt–Rh–SnO<sub>2</sub>/C with the atomic ratio Pt:Rh:Sn = 3:1:4; (<b>c</b>) The charge ratio of the total oxidation pathway (<span class="html-italic">C</span><sub>CO<sub>2</sub></sub>) over the partial oxidation pathway (<span class="html-italic">C</span><sub>CH<sub>3</sub>COOH</sub> + <span class="html-italic">C</span><sub>CH<sub>3</sub>CHO</sub>) as a function of electrode potential for both electrocatalysts in 0.1 M HClO<sub>4</sub> and 0.1 M ethanol. Reprinted and adapted with permission from Reference [<a href="#B9-catalysts-05-01507" class="html-bibr">9</a>]. Copyright 2010, Elsevier.</p>
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<p>Combinatorial array and screening results by fluorescence imaging of PtSnM electrode arrays in 6.0 M ethanol and quinine fluorescent indicator. Active compositions for ethanol electro-oxidation are shown as bright spots: fluorescence image at (<b>A</b>) lower overpotential (~0.27V <span class="html-italic">vs.</span> RHE); (<b>B</b>) intermediate overpotential (~0.46 V <span class="html-italic">vs.</span> RHE) and (<b>C</b>) high overpotential (~0.93 V <span class="html-italic">vs.</span> RHE); (<b>D</b>) Fluorescence onset potential for ethanol electro-oxidation on PtM and PtSnM library. Reproduced with permission from Reference [<a href="#B101-catalysts-05-01507" class="html-bibr">101</a>]. Copyright 2015, Elsevier.</p>
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<p>Surface cluster models of (<b>a</b>) Pd–Sn<sub>1</sub> and (<b>b</b>) Pd–Sn<sub>5</sub> used for modeling ethanol dehydrogenation, and reaction energies for H removal from ethanol over (<b>c</b>) Pd (111); (<b>d</b>) Pd–Sn<sub>1</sub>, (<b>e</b>) Pd–Sn<sub>5</sub> surfaces. Reproduced with permission from Reference [<a href="#B80-catalysts-05-01507" class="html-bibr">80</a>]. Copyright 2012, American Chemical Society.</p>
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<p>(<b>A</b>) XRD patterns of the Pd–P/C (curve a), Pd–Ni–P/C (curve b), Pd–Ni/C (curve c) and Pd/C (curve d). (<b>B</b>) Cyclic voltammograms for Pd-based catalysts in 0.5 M NaOH and 1 M C<sub>2</sub>H<sub>5</sub>OH at 50 mV·s<sup>−1</sup>; (<b>C</b>) Scheme of Pd–Ni–P atomic arrangement. The asterisks at 33.5° and 59.2° mark the peaks from Ni(OH)<sub>2</sub> (100) and (110) facets. Reprinted and adapted with permission from Reference [<a href="#B117-catalysts-05-01507" class="html-bibr">117</a>]. Copyright 2013, Elsevier.</p>
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<p>Potentiodynamic ATR-SEIRAS spectra on the as-deposited Pd–Ni–P film (<b>A</b>) and the de-alloyed film (<b>C</b>) in 0.1 M NaOH + 0.5 M ethanol; Potential-dependent band intensities for ν(CO<sub>ad</sub>) (blue) and ν<sub>s(OCO)</sub> of adsorbed acetate (green) with corresponding CVs recorded at 5 mV·s<sup>−1</sup> on the as-deposited Pd–Ni–P film (<b>B</b>) and the de-alloyed film (<b>D</b>) in 0.1 M NaOH + 0.5 M ethanol. Reproduced with permission from Reference [<a href="#B24-catalysts-05-01507" class="html-bibr">24</a>]. Copyright 2014, Elsevier.</p>
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