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Materials, Volume 9, Issue 7 (July 2016) – 111 articles

Cover Story (view full-size image): Magnetism in Electronically Imbalanced Clathrate-like Compounds
The transition metals Fe, Co, and Ni substitute Cu in a clathrate-like compound Eu7Cu44As23 to modify its magnetic properties while keeping its crystal symmetry intact. Unlike typical clathrates, Eu7Cu44As23 is an electronically imbalanced compound allowing a wide range of heterovalent substitutions. Spins of the Eu2+ (4f7) cations that reside in oversized cages of the framework tend to order ferromagnetically; however, Ni-substituted compound shows an increase in TC to 25 K, whereas substitution of Fe for Cu suppresses ordering. View the paper
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2407 KiB  
Article
Change in Dielectric Properties in the Microwave Frequency Region of Polypyrrole–Coated Textiles during Aging
by Eva Hakansson, Akif Kaynak and Abbas Kouzani
Materials 2016, 9(7), 609; https://doi.org/10.3390/ma9070609 - 22 Jul 2016
Cited by 5 | Viewed by 5416
Abstract
Complex permittivity of conducting polypyrrole (PPy)-coated Nylon-Lycra textiles is measured using a free space transmission measurement technique over the frequency range of 1–18 GHz. The aging of microwave dielectric properties and reflection, transmission and absorption for a period of 18 months is demonstrated. [...] Read more.
Complex permittivity of conducting polypyrrole (PPy)-coated Nylon-Lycra textiles is measured using a free space transmission measurement technique over the frequency range of 1–18 GHz. The aging of microwave dielectric properties and reflection, transmission and absorption for a period of 18 months is demonstrated. PPy-coated fabrics are shown to be lossy over the full frequency range. The levels of absorption are shown to be higher than reflection in the tested samples. This is attributed to the relatively high resistivity of the PPy-coated fabrics. Both the dopant concentration and polymerisation time affect the total shielding effectiveness and microwave aging behaviour. Distinguishing either of these two factors as being exclusively the dominant mechanism of shielding effectiveness is shown to be difficult. It is observed that the PPy-coated Nylon-Lycra samples with a p-toluene sulfonic acid (pTSA) concentration of 0.015 M and polymerisation times of 60 min and 180 min have 37% and 26% decrease in total transmission loss, respectively, upon aging for 72 weeks at room temperature (20 °C, 65% Relative humidity (RH)). The concentration of the dopant also influences the microwave aging behaviour of the PPy-coated fabrics. The samples with a higher dopant concentration of 0.027 mol/L pTSA are shown to have a transmission loss of 32.6% and 16.5% for short and long polymerisation times, respectively, when aged for 72 weeks. The microwave properties exhibit better stability with high dopant concentration and/or longer polymerization times. High pTSA dopant concentrations and/or longer polymerisation times result in high microwave insertion loss and are more effective in reducing the transmission and also increasing the longevity of the electrical properties. Full article
(This article belongs to the Special Issue Electroactive Polymers)
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Figure 1

Figure 1
<p>The variation of the diameter of Nylon-Lycra fibre with polymerisation time. Dopant concentration 0.018 mol/L <span class="html-italic">p</span>TSA.</p>
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<p>Optical transmission microscopy image of microtome sections of sample fibres of PPy-<span class="html-italic">p</span>TSA coated Nylon-Lycra fabrics, coated for 120 min of polymerisation time.</p>
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<p>Schematic of free space transmission set-up.</p>
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<p>Surface resistivity (R<sub>S</sub>) for newly coated and aged (six months) conducting PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra as a function of polymerisation time. <span class="html-italic">p</span>TSA concentration: 0.018 mol/L.</p>
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<p>Surface resistivity (R<sub>S</sub>) for recently coated and aged (six months) conducting PPy-<span class="html-italic">p</span>TSA Nylon-Lycra as a function of dopant concentration. Polymerisation time: 180 min.</p>
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<p>(<b>a</b>) Real part of permittivity for PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra. Polymerisation time: 180 min, concentration: 0.018 mol/L; (<b>b</b>) Imaginary part of permittivity for PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra. Polymerisation time: 180 min, concentration: 0.018 mol/L.</p>
Full article ">Figure 6 Cont.
<p>(<b>a</b>) Real part of permittivity for PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra. Polymerisation time: 180 min, concentration: 0.018 mol/L; (<b>b</b>) Imaginary part of permittivity for PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra. Polymerisation time: 180 min, concentration: 0.018 mol/L.</p>
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<p>Averages of the real part of permittivity for PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra during degradation during aging for three different polymerisation times (60, 120 and 180 min). <span class="html-italic">p</span>TSA concentration: 0.018 mol/L.</p>
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<p>Averages of the imaginary part of permittivity for PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra during degradation during aging for three polymerisation times (60, 120 and 180 min). <span class="html-italic">p</span>TSA concentration: 0.018 mol/L.</p>
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<p>Reflection, transmission, absorption and total transmission loss for PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra. Polymerisation time: 60 min, <span class="html-italic">p</span>TSA concentration: 0.015 mol/L. Please make the explanations smaller and put them inside the piture like the <a href="#materials-09-00609-f005" class="html-fig">Figure 5</a>, <a href="#materials-09-00609-f006" class="html-fig">Figure 6</a>, <a href="#materials-09-00609-f007" class="html-fig">Figure 7</a>, <a href="#materials-09-00609-f008" class="html-fig">Figure 8</a> and <a href="#materials-09-00609-f009" class="html-fig">Figure 9</a>.</p>
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<p>Reflection, transmission, absorption and total transmission loss for PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra. Polymerisation time: 180 min, <span class="html-italic">p</span>TSA concentration: 0.015 mol/L.</p>
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<p>Reflection, transmission, absorption and total transmission loss for PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra. Polymerisation time: 60 min, <span class="html-italic">p</span>TSA concentration: 0.027 mol/L.</p>
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<p>Reflection, transmission, absorption and total transmission loss for PPy-<span class="html-italic">p</span>TSA–coated Nylon-Lycra. Polymerisation time: 180 min, <span class="html-italic">p</span>TSA concentration: 0.027 mol/L.</p>
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9084 KiB  
Article
Design and Fabrication of a Precision Template for Spine Surgery Using Selective Laser Melting (SLM)
by Di Wang, Yimeng Wang, Jianhua Wang, Changhui Song, Yongqiang Yang, Zimian Zhang, Hui Lin, Yongqiang Zhen and Suixiang Liao
Materials 2016, 9(7), 608; https://doi.org/10.3390/ma9070608 - 22 Jul 2016
Cited by 40 | Viewed by 11204
Abstract
In order to meet the clinical requirements of spine surgery, this paper proposes the fabrication of the customized template for spine surgery through computer-aided design. A 3D metal printing-selective laser melting (SLM) technique was employed to directly fabricate the 316L stainless steel template, [...] Read more.
In order to meet the clinical requirements of spine surgery, this paper proposes the fabrication of the customized template for spine surgery through computer-aided design. A 3D metal printing-selective laser melting (SLM) technique was employed to directly fabricate the 316L stainless steel template, and the metal template with tiny locating holes was used as an auxiliary tool to insert spinal screws inside the patient’s body. To guarantee accurate fabrication of the template for cervical vertebra operation, the contact face was placed upwards to improve the joint quality between the template and the cervical vertebra. The joint surface of the printed template had a roughness of Ra = 13 ± 2 μm. After abrasive blasting, the surface roughness was Ra = 7 ± 0.5 μm. The surgical metal template was bound with the 3D-printed Acrylonitrile Butadiene Styrene (ABS) plastic model. The micro-hardness values determined at the cross-sections of SLM-processed samples varied from HV0.3 250 to HV0.3 280, and the measured tensile strength was in the range of 450 MPa to 560 MPa, which showed that the template had requisite strength. Finally, the metal template was clinically used in the patient’s surgical operation, and the screws were inserted precisely as the result of using the auxiliary template. The geometrical parameters of the template hole (e.g., diameter and wall thickness) were optimized, and measures were taken to optimize the key geometrical units (e.g., hole units) in metal 3D printing. Compared to the traditional technology of screw insertion, the use of the surgical metal template enabled the screws to be inserted more easily and accurately during spinal surgery. However, the design of the high-quality template should fully take into account the clinical demands of surgeons, as well as the advice of the designing engineers and operating technicians. Full article
(This article belongs to the Special Issue 3D Printing for Biomedical Engineering)
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Graphical abstract

Graphical abstract
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<p>Key steps to design the spinal surgery template. (<b>a</b>) Atlas (up) and axis (down); (<b>b</b>) curved surface and cervical vertebra; (<b>c</b>) guider hole and locating hole; and (<b>d</b>) template with the handle and cervical vertebra.</p>
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<p>Principle of SLM manufacturing and the experimental DiMetal-100 equipment. (<b>a</b>) Principle of SLM manufacturing; and (<b>b</b>) DiMetal-100.</p>
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<p>The SEM image of 316L stainless steel powder having the size of 500 mesh.</p>
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<p>Microscopic analysis of surface morphology of stainless steel parts from SLM. (<b>a</b>) Surface morphology of the side part; and (<b>b</b>) surface morphology of the upper part.</p>
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<p>Location adjustment and addition of supports for the surgical template model.</p>
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<p>Spinal surgery template obtained from SLM. (<b>a</b>) Surgical template without removing the support; and (<b>b</b>) surgical template after abrasive blasting.</p>
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<p>Fitting of the metal template and the FDM-printed cervical vertebra model.</p>
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<p>Illustration of laser scanning the overhang.</p>
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<p>In vitro test of the metal templates. (<b>a</b>) Axis template; (<b>b</b>) atlas template.</p>
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<p>(<b>a</b>) Use of the atlas template; (<b>b</b>) insertion of screws into atlas using the template; (<b>c</b>) use of the axis template; (<b>d</b>) insertion of screws into the axis during the operation involving the insertion of high-precision screws with templates.</p>
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<p>The surgical results observed through the CT reverse engineering method. (<b>a</b>) Sagittal view; (<b>b</b>) transverse view; (<b>c</b>) 3D orientation 1; and (<b>d</b>) 3D orientation 2.</p>
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<p>Redundant parts of the atlas template (marked in red).</p>
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<p>Limitations of principles for fabricating two classes of round holes. (<b>a</b>) The contour error of round holes parallel to the Z axis; (<b>b</b>) the three stages in fabricating an overhang hole; and (<b>c</b>) an illustration of deep laser penetration.</p>
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<p>Small round holes fabrication experiments. (<b>a</b>) Fabricated round holes parallel to the Z axis; (<b>b</b>) Fabricated round holes vertical to the Z axis.</p>
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6396 KiB  
Article
Influence of Network Structure on Glass Transition Temperature of Elastomers
by Katarzyna Bandzierz, Louis Reuvekamp, Jerzy Dryzek, Wilma Dierkes, Anke Blume and Dariusz Bielinski
Materials 2016, 9(7), 607; https://doi.org/10.3390/ma9070607 - 22 Jul 2016
Cited by 93 | Viewed by 11927
Abstract
It is generally believed that only intermolecular, elastically-effective crosslinks influence elastomer properties. The role of the intramolecular modifications of the polymer chains is marginalized. The aim of our study was the characterization of the structural parameters of cured elastomers, and determination of their [...] Read more.
It is generally believed that only intermolecular, elastically-effective crosslinks influence elastomer properties. The role of the intramolecular modifications of the polymer chains is marginalized. The aim of our study was the characterization of the structural parameters of cured elastomers, and determination of their influence on the behavior of the polymer network. For this purpose, styrene-butadiene rubbers (SBR), cured with various curatives, such as DCP, TMTD, TBzTD, Vulcuren®, DPG/S8, CBS/S8, MBTS/S8 and ZDT/S8, were investigated. In every series of samples a broad range of crosslink density was obtained, in addition to diverse crosslink structures, as determined by equilibrium swelling and thiol-amine analysis. Differential scanning calorimetry (DSC) and dynamic mechanical analysis (DMA) were used to study the glass transition process, and positron annihilation lifetime spectroscopy (PALS) to investigate the size of the free volumes. For all samples, the values of the glass transition temperature (Tg) increased with a rise in crosslink density. At the same time, the free volume size proportionally decreased. The changes in Tg and free volume size show significant differences between the series crosslinked with various curatives. These variations are explained on the basis of the curatives’ structure effect. Furthermore, basic structure-property relationships are provided. They enable the prediction of the effect of curatives on the structural parameters of the network, and some of the resulting properties. It is proved that the applied techniques—DSC, DMA, and PALS—can serve to provide information about the modifications to the polymer chains. Moreover, on the basis of the obtained results and considering the diversified curatives available nowadays, the usability of “part per hundred rubber” (phr) unit is questioned. Full article
(This article belongs to the Special Issue Advances in Research on Elastomers)
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Figure 1
<p>Performance of an elastomer under loading force and after its removal: (<b>a</b>) plastic deformation of an uncrosslinked elastomer; and (<b>b</b>) elastic recovery of a crosslinked elastomer.</p>
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<p>Structures formed as a result of curing intermolecular crosslinks: (<b>a</b>) carbon-carbon crosslinks; (<b>b</b>) sulfidic crosslinks, intramolecular modifications of the polymer chains: (<b>c</b>) cyclic sulfur structures; and (<b>d</b>) pendant groups.</p>
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<p>Crosslink density and crosslink structures formed during the curing process with use of various curatives. The columns in each series correspond to the samples with an increasing amount of curatives, as listed in <a href="#materials-09-00607-t002" class="html-table">Table 2</a>.</p>
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<p>“Static” <span class="html-italic">T</span><sub>g</sub> as a function of crosslink density for the uncrosslinked reference and all cured series of samples.</p>
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<p>Tan delta as a function of temperature for the uncrosslinked reference and the DPG/S<sub>8</sub> cured series of samples.</p>
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<p>“Dynamic” <span class="html-italic">T</span><sub>g</sub>, determined by a maximum of the tan delta peak, as a function of the crosslink density for the uncrosslinked reference and all cured series of samples.</p>
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<p>“Dynamic” <span class="html-italic">T</span><sub>g</sub>, determined by a maximum of <span class="html-italic">E</span>’’, as a function of crosslink density for the uncrosslinked reference and all cured series of samples.</p>
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<p>Height of tan delta peak as a function of crosslink density for the uncrosslinked reference and all cured series of samples.</p>
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<p>Width of tan delta peak in the half of height, as a function of crosslink density for the uncrosslinked reference and all cured series of samples.</p>
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<p>Dependence between height of tan delta at 70 °C and the crosslink density for the uncrosslinked reference and all cured series of samples.</p>
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<p>Density of samples as a function of crosslink density for the uncrosslinked reference and all cured series of samples.</p>
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<p>Size of free volumes as a function of crosslink density for the uncrosslinked reference and all cured series of samples.</p>
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2747 KiB  
Article
Hydration of Hybrid Alkaline Cement Containing a Very Large Proportion of Fly Ash: A Descriptive Model
by Inés Garcia-Lodeiro, Shane Donatello, Ana Fernández-Jiménez and Ángel Palomo
Materials 2016, 9(7), 605; https://doi.org/10.3390/ma9070605 - 22 Jul 2016
Cited by 119 | Viewed by 10397
Abstract
In hybrid alkaline fly ash cements, a new generation of binders, hydration, is characterized by features found in both ordinary portland cement (OPC) hydration and the alkali activation of fly ash (AAFA). Hybrid alkaline fly ash cements typically have a high fly ash [...] Read more.
In hybrid alkaline fly ash cements, a new generation of binders, hydration, is characterized by features found in both ordinary portland cement (OPC) hydration and the alkali activation of fly ash (AAFA). Hybrid alkaline fly ash cements typically have a high fly ash (70 wt % to 80 wt %) and low clinker (20 wt % to 30 wt %) content. The clinker component favors curing at ambient temperature. A hydration mechanism is proposed based on the authors’ research on these hybrid binders over the last five years. The mechanisms for OPC hydration and FA alkaline activation are summarized by way of reference. In hybrid systems, fly ash activity is visible at very early ages, when two types of gel are formed: C–S–H from the OPC and N–A–S–H from the fly ash. In their mutual presence, these gels tend to evolve, respectively, into C–A–S–H and (N,C)–A–S–H. The use of activators with different degrees of alkalinity has a direct impact on reaction kinetics but does not modify the main final products, a mixture of C–A–S–H and (N,C)–A–S–H gels. The proportion of each gel in the mix does, however, depend on the alkalinity generated in the medium. Full article
(This article belongs to the Special Issue Advances in Geopolymers and Alkali-Activated Materials)
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Graphical abstract

Graphical abstract
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<p>Position of hybrid alkaline fly ash cements on the pure Portland cement (PC)-pure alkali activation of fly ash (AAFA) spectrum, relative to pozzolanic fly ash cements.</p>
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<p>Descriptive model for poly-phase OPC grain hydration and a typical calorimetric curve for OPC hydration (grain drawings adapted from Scrivener as quoted in Taylor (1997) [<a href="#B27-materials-09-00605" class="html-bibr">27</a>]).</p>
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<p>Conceptual model for AAFA cement hydration. (<b>a</b>) Starting material; (<b>b</b>) initial alkaline attack on the ashes and early N–A–S–H gel formation; (<b>c</b>) gel polymerisation and positioning on the inner and outer surfaces of the exposed fly ash; and (<b>d</b>) mature and heterogeneous AAFA cement paste microstructure (adapted from Fernández and Palomo [<a href="#B7-materials-09-00605" class="html-bibr">7</a>]).</p>
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<p><sup>29</sup>Si MAS NMR spectra: (<b>a</b>) initial raw mix (30% clinker + 70% fly ash); (<b>b</b>) 28-day water-hydrated material; (<b>c</b>) 28-day NaOH-hydrated material; (<b>d</b>) 28-day NaOH + WG (waterglass)-hydrated material (adapted from Palomo et al. [<a href="#B18-materials-09-00605" class="html-bibr">18</a>]).</p>
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<p>Changes in gel composition and microstructure of a hybrid alkaline cement with a very high fly ash content: (<b>a</b>) initial stage; (<b>b</b>) early age sample (min); (<b>c</b>) early age sample (h); (<b>d</b>) 7-day sample; (<b>e</b>) 28-day sample.</p>
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<p>Nano-structural mechanism for gel formation in hybrid alkaline cements; (<b>a</b>) dissolution of ionic species from the source of alumino-and calcium silicates; (<b>b</b>) precipitation of aluminum-high (type I) N–A–S–H gels and C–S–H gels; (<b>c</b>) silica uptake by both gels with an increase in C–S–H gel mean chain length and the generation of silica-high type 2 N–A–S–H gels; (<b>d</b>) diffusion of aluminum and calcium in the matrix and their uptake, respectively, in C–S–H and N–A–S–H gels to form (N,C)–A–S–H gels; (<b>e</b>) distortion of the (N,C)–A–S–H gel due to the polarizing effect of calcium, leading to its rupture, while the C–A–S–H gel continues to take up aluminum species in bridging positions, favoring chain cross-linking and hence a more polymerized structure (hydrogen bonds omitted in this final stage).</p>
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11275 KiB  
Article
Transformation and Precipitation Reactions by Metal Active Gas Pulsed Welded Joints from X2CrNiMoN22-5-3 Duplex Stainless Steels
by Ion-Dragos Utu, Ion Mitelea, Sorin Dumitru Urlan and Corneliu Marius Crăciunescu
Materials 2016, 9(7), 606; https://doi.org/10.3390/ma9070606 - 21 Jul 2016
Cited by 12 | Viewed by 6123
Abstract
The high alloying degree of Duplex stainless steels makes them susceptible to the formation of intermetallic phases during their exposure to high temperatures. Precipitation of these phases can lead to a decreasing of the corrosion resistance and sometimes of the toughness. Starting from [...] Read more.
The high alloying degree of Duplex stainless steels makes them susceptible to the formation of intermetallic phases during their exposure to high temperatures. Precipitation of these phases can lead to a decreasing of the corrosion resistance and sometimes of the toughness. Starting from the advantages of the synergic Metal Active Gas (MAG) pulsed welding process, this paper analyses the structure formation particularities of homogeneous welded joints from Duplex stainless steel. The effect of linear welding energy on the structure morphology of the welded joints was revealed by macro- and micrographic examinations, X-ray energy dispersion analyses, measurements of ferrite proportion and X-ray diffraction analysis. The results obtained showed that the transformation of ferrite into austenite is associated with the chromium, nickel, molybdenum and nitrogen distribution between these two phases and their redistribution degree is closely linked to the overall heat cycle of the welding process. The adequate control of the energy inserted in the welded components provides an optimal balance between the two microstructural constituents (Austenite and Ferrite) and avoids the formation of undesirable intermetallic phases. Full article
(This article belongs to the Section Advanced Materials Characterization)
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Figure 1
<p>The shape and dimensions of welding joint.</p>
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<p>Components and welding torch.</p>
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<p>Macroscopic images of the welded joints cross section: (<b>a</b>) E<sub>l</sub> welded joint = 6.9 kJ/cm, E<sub>l</sub> filling layers = 10 kJ/cm; (<b>b</b>) E<sub>l</sub> welded joint = 6.9 kJ/cm, E<sub>l</sub> filling layers = 15 kJ/cm; and (<b>c</b>) E<sub>l</sub> welded joint = 6.9 kJ/cm, E<sub>l</sub> filling layers = 20.7 kJ/cm. Chemical reactive: ferric chloride 10 cm<sup>3</sup>; hydrochloric acid 30 cm<sup>3</sup>; and ethylic alcohol 120 cm<sup>3</sup>.</p>
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<p>The phases pseudo binary Fe-Cr-Ni diagram for 68% Fe [<a href="#B23-materials-09-00606" class="html-bibr">23</a>,<a href="#B24-materials-09-00606" class="html-bibr">24</a>].</p>
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<p>Microstructure of the base metal.</p>
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<p>Microstructure of the root layer.</p>
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<p>Microstructure of the last deposited layer for achieving the welded joint with a linear energy E<sub>l</sub> = 15 kJ/cm: (<b>a</b>) magnification 50×; and (<b>b</b>) magnification 200×.</p>
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<p>Microstructure of the weld-HAZ interface for achieving the welded joint with a linear energy. E<sub>l</sub> = 15 kJ/cm: (<b>a</b>) magnification 50×; and (<b>b</b>) magnification 200×.</p>
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<p>Ferrite diagram index with construction for ferrite index calculation.</p>
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<p>Examination of the last layer deposition with E<sub>l</sub> = 15 kJ/cm: (<b>a</b>) SEM image; and (<b>b</b>) line scans showing the compositional variation for the region indicated in (<b>a</b>).</p>
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<p>Examination of the median zone in the deposited layer with E<sub>l</sub> = 15 kJ/cm; and (<b>a</b>) SEM image; (<b>b</b>) line scans showing the compositional variation for the region indicated in (<b>a</b>).</p>
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<p>XRD pattern of the welded joint root layer realized with E<sub>l</sub> = 6.9 kJ/cm.</p>
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<p>XRD pattern of the welded joint central zone E<sub>l</sub> = 15 kJ/cm.</p>
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<p>XRD pattern of the welded joint filling layer realized with E<sub>l</sub> = 15 kJ/cm.</p>
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<p>XRD pattern of the interface weld-HAZ for E<sub>l</sub> = 15 kJ/cm.</p>
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<p>XRD pattern of the base metal.</p>
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4004 KiB  
Article
Thermal Stability and Flammability of Styrene-Butadiene Rubber-Based (SBR) Ceramifiable Composites
by Rafał Anyszka, Dariusz M. Bieliński, Zbigniew Pędzich, Przemysław Rybiński, Mateusz Imiela, Mariusz Siciński, Magdalena Zarzecka-Napierała, Tomasz Gozdek and Paweł Rutkowski
Materials 2016, 9(7), 604; https://doi.org/10.3390/ma9070604 - 21 Jul 2016
Cited by 17 | Viewed by 9671
Abstract
Ceramifiable styrene-butadiene (SBR)-based composites containing low-softening-point-temperature glassy frit promoting ceramification, precipitated silica, one of four thermally stable refractory fillers (halloysite, calcined kaolin, mica or wollastonite) and a sulfur-based curing system were prepared. Kinetics of vulcanization and basic mechanical properties were analyzed and added [...] Read more.
Ceramifiable styrene-butadiene (SBR)-based composites containing low-softening-point-temperature glassy frit promoting ceramification, precipitated silica, one of four thermally stable refractory fillers (halloysite, calcined kaolin, mica or wollastonite) and a sulfur-based curing system were prepared. Kinetics of vulcanization and basic mechanical properties were analyzed and added as Supplementary Materials. Combustibility of the composites was measured by means of cone calorimetry. Their thermal properties were analyzed by means of thermogravimetry and specific heat capacity determination. Activation energy of thermal decomposition was calculated using the Flynn-Wall-Ozawa method. Finally, compression strength of the composites after ceramification was measured and their micromorphology was studied by scanning electron microscopy. The addition of a ceramification-facilitating system resulted in the lowering of combustibility and significant improvement of the thermal stability of the composites. Moreover, the compression strength of the mineral structure formed after ceramification is considerably high. The most promising refractory fillers for SBR-based ceramifiable composites are mica and halloysite. Full article
(This article belongs to the Special Issue Advances in Research on Elastomers)
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Figure 1
<p>Cone calorimetry analysis of the vulcanizates: heat release rate (<b>a</b>); total heat released (<b>b</b>); averaged heat release rate (<b>c</b>) and mass loss (<b>d</b>).</p>
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<p>Changes to specific heat capacity of the ceramifiable composites with the increase of temperature.</p>
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<p>Thermogravimetric characteristic of the samples at heating rate of 5 K/min (<b>a</b>) and plots exhibiting Flynn-Wall-Ozawa approach toward estimation of decomposition energy for: SBR_pris (<b>b</b>); SBR_hal (<b>c</b>); SBR_kao (<b>d</b>); SBR_mic (<b>e</b>) and SBR_wol (<b>f</b>) vulcanizates.</p>
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<p>Thermogravimetric characteristic of the samples at heating rate of 5 K/min (<b>a</b>) and plots exhibiting Flynn-Wall-Ozawa approach toward estimation of decomposition energy for: SBR_pris (<b>b</b>); SBR_hal (<b>c</b>); SBR_kao (<b>d</b>); SBR_mic (<b>e</b>) and SBR_wol (<b>f</b>) vulcanizates.</p>
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<p>SEM photographs of the ceramified composites’ cross-sections taken under different magnifications of 350× (<b>a1</b>, <b>b1</b>, <b>c1</b> and <b>d1</b>) and 1000× (<b>a2</b>, <b>b2</b>, <b>c2</b> and <b>d2</b>) for: SBR_hal (<b>a</b>); SBR_kao (<b>b</b>); SBR_mic (<b>c</b>) and SBR_wol (<b>d</b>).</p>
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<p>SEM photographs of the ceramified composites’ cross-sections taken under different magnifications of 350× (<b>a1</b>, <b>b1</b>, <b>c1</b> and <b>d1</b>) and 1000× (<b>a2</b>, <b>b2</b>, <b>c2</b> and <b>d2</b>) for: SBR_hal (<b>a</b>); SBR_kao (<b>b</b>); SBR_mic (<b>c</b>) and SBR_wol (<b>d</b>).</p>
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7872 KiB  
Article
Fiberglass Grids as Sustainable Reinforcement of Historic Masonry
by Luca Righetti, Vikki Edmondson, Marco Corradi and Antonio Borri
Materials 2016, 9(7), 603; https://doi.org/10.3390/ma9070603 - 21 Jul 2016
Cited by 16 | Viewed by 6366
Abstract
Fiber-reinforced composite (FRP) materials have gained an increasing success, mostly for strengthening, retrofitting and repair of existing historic masonry structures and may cause a significant enhancement of the mechanical properties of the reinforced members. This article summarizes the results of previous experimental activities [...] Read more.
Fiber-reinforced composite (FRP) materials have gained an increasing success, mostly for strengthening, retrofitting and repair of existing historic masonry structures and may cause a significant enhancement of the mechanical properties of the reinforced members. This article summarizes the results of previous experimental activities aimed at investigating the effectiveness of GFRP (Glass Fiber Reinforced Polymers) grids embedded into an inorganic mortar to reinforce historic masonry. The paper also presents innovative results on the relationship between the durability and the governing material properties of GFRP grids. Measurements of the tensile strength were made using specimens cut off from GFRP grids before and after ageing in aqueous solution. The tensile strength of a commercially available GFRP grid has been tested after up 450 days of storage in deionized water and NaCl solution. A degradation in tensile strength and Young’s modulus up to 30.2% and 13.2% was recorded, respectively. This degradation indicated that extended storage in a wet environment may cause a decrease in the mechanical properties. Full article
(This article belongs to the Section Advanced Composites)
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<p>(<b>a</b>) 66 × 66 mm<sup>2</sup> GFRP grid; (<b>b</b>) 33 × 33 mm<sup>2</sup> GFRP grid; (<b>c</b>) schematic layout.</p>
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<p>(<b>a</b>) Shear compression test; (<b>b</b>) diagonal compression test.</p>
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<p>(<b>a</b>) Reinforcement application; (<b>b</b>) test arrangement.</p>
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<p>Ring beams under loading: (<b>a</b>) grid arrangement for stonemasonry beams; (<b>b</b>) P5-G33-V.</p>
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<p>66 × 66 mm<sup>2</sup> GFRP grid: (<b>a</b>) weft direction (SR type); (<b>b</b>) warp direction (SC type).</p>
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<p>Specimens obtained from the 66 × 66 mm<sup>2</sup> GFRP grid.</p>
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<p>Detail of the epoxy tabs glued at both ends of the specimens.</p>
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<p>Load-extension curves for untreated specimens: (<b>a</b>) SR-series; (<b>b</b>) SC-series.</p>
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<p>Catastrophic collapse of the GFRP sample.</p>
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<p>Partial fiber-failure at the GFRP grids joint.</p>
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<p>Comparison between SR and SR_SW_3.</p>
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<p>Comparison between SR and SR_W_5.</p>
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<p>Tensile strength vs. treatment time for SR-series (<b>a</b>) NaCl solution; (<b>b</b>) deionized water.</p>
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<p>Tensile strength vs. treatment time for SC-series: (<b>a</b>) NaCl solution; (<b>b</b>) deionized water.</p>
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<p>Young’s modulus vs. treatment time for SR-series (<b>a</b>) NaCl solution; (<b>b</b>) deionized water.</p>
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<p>Young’s modulus vs. treatment time for SC-series: (<b>a</b>) NaCl solution; (<b>b</b>) deionized water.</p>
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<p>SEM micrograph of GFRP specimen aged in deionized water for 11 months: (<b>a</b>,<b>b</b>) section perpendicular to the fiber; (<b>c</b>,<b>d</b>) section parallel to the fiberglass filament.</p>
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6489 KiB  
Article
Guided Wave Based Crack Detection in the Rivet Hole Using Global Analytical with Local FEM Approach
by Md Yeasin Bhuiyan, Yanfeng Shen and Victor Giurgiutiu
Materials 2016, 9(7), 602; https://doi.org/10.3390/ma9070602 - 21 Jul 2016
Cited by 57 | Viewed by 6989
Abstract
In this article, ultrasonic guided wave propagation and interaction with the rivet hole cracks has been formulated using closed-form analytical solution while the local damage interaction, scattering, and mode conversion have been obtained from finite element analysis. The rivet hole cracks (damage) in [...] Read more.
In this article, ultrasonic guided wave propagation and interaction with the rivet hole cracks has been formulated using closed-form analytical solution while the local damage interaction, scattering, and mode conversion have been obtained from finite element analysis. The rivet hole cracks (damage) in the plate structure gives rise to the non-axisymmetric scattering of Lamb wave, as well as shear horizontal (SH) wave, although the incident Lamb wave source (primary source) is axisymmetric. The damage in the plate acts as a non-axisymmetric secondary source of Lamb wave and SH wave. The scattering of Lamb and SH waves are captured using wave damage interaction coefficient (WDIC). The scatter cubes of complex-valued WDIC are formed that can describe the 3D interaction (frequency, incident direction, and azimuth direction) of Lamb waves with the damage. The scatter cubes are fed into the exact analytical framework to produce the time domain signal. This analysis enables us to obtain the optimum design parameters for better detection of the cracks in a multiple-rivet-hole problem. The optimum parameters provide the guideline of the design of the sensor installation to obtain the most noticeable signals that represent the presence of cracks in the rivet hole. Full article
(This article belongs to the Special Issue Advances in Structural Health Monitoring for Aerospace Structures)
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<p>Illustration of the multiple-rivet-hole lap joint.</p>
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<p>(<b>a</b>) Framework of the combined analytical and finite element approach (CAFA); (<b>b</b>) Representative model of the damage for FE analysis; (<b>c</b>) “Scatter cube” of wave damage interaction coefficient (WDIC).</p>
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<p>Illustration of local finite element method (FEM) modeling (<b>a</b>) Pristine model; (<b>b</b>) Local damage model with NRB; (<b>c</b>) 3D view of damage model; (<b>d</b>) Stress modeshapes; (<b>e</b>) FE Loading in the thickness direction.</p>
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<p>Comparison between analytical and FEM results (<b>a</b>) WDIC<sub>LW_LW</sub> (<b>b</b>) WDIC<sub>LW_SH</sub> in polar coordinates (pristine plate).</p>
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<p>Alteration of wave damage interaction coefficient (WDIC) profiles of scattered Lamb and shear horizontal (SH) waves with different damage conditions: (<b>a</b>) Pristine; (<b>b</b>) Hole; (<b>c</b>) Hole + Crack.</p>
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<p>Subtracted WDIC profiles of scattered Lamb and SH waves to account the damage effect only: (<b>a</b>) Hole only; (<b>b</b>) Crack only.</p>
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<p>Frequency domain variation of WDIC<sub>S0_S0</sub> at different azimuthal positions (<math display="inline"> <semantics> <mrow> <mi mathvariant="sans-serif">θ</mi> <mo>=</mo> <mn>9</mn> <mo>°</mo> </mrow> </semantics> </math>).</p>
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<p>Frequency domain variation of WDIC<sub>S0_S0</sub> for multiple incident directions.</p>
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<p>Azimuthal variation of (<b>a</b>) <math display="inline"> <semantics> <mrow> <msub> <mrow> <mtext>WDIC</mtext> </mrow> <mrow> <mi mathvariant="normal">S</mi> <mn>0</mn> <mo>_</mo> <mi mathvariant="normal">S</mi> <mn>0</mn> </mrow> </msub> </mrow> </semantics> </math>; (<b>b</b>) <math display="inline"> <semantics> <mrow> <msub> <mrow> <mtext>WDIC</mtext> </mrow> <mrow> <mi mathvariant="normal">A</mi> <mn>0</mn> <mo>_</mo> <mi mathvariant="normal">A</mi> <mn>0</mn> </mrow> </msub> </mrow> </semantics> </math> at different frequencies.</p>
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<p>The wave fields for (<b>a</b>) Hole; (<b>b</b>) Hole + Crack (<b>c</b>) Crack only (<math display="inline"> <semantics> <mrow> <mi>f</mi> <mo>=</mo> <mn>538</mn> <mo> </mo> <mtext>kHz</mtext> </mrow> </semantics> </math>, <math display="inline"> <semantics> <mrow> <mi mathvariant="sans-serif">θ</mi> <mo>=</mo> <mn>0</mn> <mo>°</mo> </mrow> </semantics> </math>).</p>
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<p>A simplified case of the multiple-rivet-hole problem.</p>
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<p>Sensing signals for different sets of frequency–location (<math display="inline"> <semantics> <mrow> <mi mathvariant="sans-serif">θ</mi> <mo>=</mo> <mn>27</mn> <mo>°</mo> </mrow> </semantics> </math>).</p>
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2611 KiB  
Article
Gas Diffusion Electrodes Manufactured by Casting Evaluation as Air Cathodes for Microbial Fuel Cells (MFC)
by Sandipam Srikanth, Deepak Pant, Xochitl Dominguez-Benetton, Inge Genné, Karolien Vanbroekhoven, Philippe Vermeiren and Yolanda Alvarez-Gallego
Materials 2016, 9(7), 601; https://doi.org/10.3390/ma9070601 - 21 Jul 2016
Cited by 23 | Viewed by 7548
Abstract
One of the most intriguing renewable energy production methods being explored currently is electrical power generation by microbial fuel cells (MFCs). However, to make MFC technology economically feasible, cost efficient electrode manufacturing processes need to be proposed and demonstrated. In this context, VITO [...] Read more.
One of the most intriguing renewable energy production methods being explored currently is electrical power generation by microbial fuel cells (MFCs). However, to make MFC technology economically feasible, cost efficient electrode manufacturing processes need to be proposed and demonstrated. In this context, VITO has developed an innovative electrode manufacturing process based on film casting and phase inversion. The screening and selection process of electrode compositions was done based on physicochemical properties of the active layer, which in turn maintained a close relation with their composition A dual hydrophilic-hydrophobic character in the active layer was achieved with values of εhydrophilic up to 10% while εTOTAL remained in the range 65 wt % to 75 wt %. Eventually, selected electrodes were tested as air cathodes for MFC in half cell and full cell modes. Reduction currents, up to −0.14 mA·cm2− at −100 mV (vs. Ag/AgCl) were reached in long term experiments in the cathode half-cell. In full MFC, a maximum power density of 380 mW·m−2 was observed at 100 Ω external load. Full article
(This article belongs to the Special Issue Advances in Renewable Energy Conversion Materials)
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<p>SEM image of the cross-section of a cast AL (<b>a</b>) and a cast HGDL (<b>b</b>).</p>
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<p>(<b>a</b>) Pore size distribution of a HGDL with composition FEP:PSf 75:25; (<b>b</b>) Pore size distribution of an AL/SS without HGDL (determined by Hg intrusion porometry); (<b>c</b>) Effect of MFC operation on pore size diameter.</p>
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<p>LSV traces for a VITO CaSE™ electrode (C:PSf 70:30), forward and backward scan (scan rate: 1 mV·s<sup>−1</sup>).</p>
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<p>Effect of the composition of the AL (C wt %) on the performance of the VITO CaSE™ electrode.</p>
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<p>Performance of a VITO CaSE™ electrode (C:PSf 70:30) as a function of time at constant voltage −100 mV vs. Ag/AgCl.</p>
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<p>(<b>a</b>) Cell potential and anodic, cathodic half-cell potentials against time during MFC operation with VITO CaSE™ electrode as cathode; (<b>b</b>) Comparative power density profiles against time during MFC operation with VITO CoRE™ and VITO CaSE™ cathodes.</p>
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<p>Comparative polarization profiles across varying external loads (10 kΩ–10 Ω) during MFC operation with VITO CoRE™ and VITO CaSE™ cathodes.</p>
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<p>Schematic representation of the cathode half-cell and cross section of the electrode (inset).</p>
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4254 KiB  
Article
Investigation of the Self-Healing Behaviors of Microcapsules/Bitumen Composites by a Repetitive Direct Tension Test
by Jun-Feng Su, Peng Yang, Ying-Yuan Wang, Shan Han, Ning-Xu Han and Wei Li
Materials 2016, 9(7), 600; https://doi.org/10.3390/ma9070600 - 21 Jul 2016
Cited by 33 | Viewed by 7734
Abstract
The aim of this work was to evaluate the self-healing behaviors of bitumen using microcapsules containing rejuvenator by a modified fracture healing–refracture method through a repetitive tension test. Microcapsules had mean size values of 10, 20 and 30 μm with a same core/shell [...] Read more.
The aim of this work was to evaluate the self-healing behaviors of bitumen using microcapsules containing rejuvenator by a modified fracture healing–refracture method through a repetitive tension test. Microcapsules had mean size values of 10, 20 and 30 μm with a same core/shell ratio of 1/1. Various microcapsules/bitumen samples were fabricated with microcapsule contents of 1.0, 3.0 and 5.0 wt. %, respectively. Tension strength values of microcapsules/bitumen samples were measured by a reparative fracture-healing process under different temperatures. It was found that these samples had tensile strength values larger than the data of pure bitumen samples under the same conditions after the four tensile fracture-healing cycles. Fracture morphology investigation and mechanism analysis indicated that the self-healing process was a process consisting of microcapsules being broken, penetrated and diffused. Moreover, the crack healing of bitumen can be considered as a viscosity driven process. The self-healing ability partly repaired the damage of bitumen during service life by comparing the properties of virgin and rejuvenated bitumen. Full article
(This article belongs to the Section Advanced Materials Characterization)
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<p>Illustration of the self-healing process of aged bitumen by microcapsules containing rejuvenator: (<b>a</b>) the structure of asphalt consisting of bitumen and aggregates; (<b>b</b>) microcrack generation and microcapsules broken; and (<b>c</b>) the self-healing of aged bitumen by leaked rejuvenator with the help of diffusion and capillarity actions.</p>
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<p>Illustration of tension test sample size.</p>
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<p>Illustration of the relationship between the time and fracture with a repetitive tension test.</p>
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<p>Morphologies of microcapsules/bitumen samples; (<b>a</b>) optical microscope morphology of microcapsules in emulsion; (<b>b</b>) SEM morphology of microcapsules and (<b>c</b>) microcapsules/bitumen composite sample.</p>
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<p>SEM cross-section morphology of a microcapsules/bitumen sample.</p>
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<p>Tension strength values of microcapsules/bitumen samples during a reparative fracture-healing process (four recycles) under temperature of 0 °C, microcapsules contents are 1.0, 3.0 and 5.0 wt. %; (<b>a</b>) tension strength values of pure bitumen (80/100) and bitumen (40/50), tension strength values of bitumen samples with microcapsules mean size of; (<b>b</b>) 10 μm; (<b>c</b>) 20 μm; and (<b>d</b>) 30 μm.</p>
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<p>Tension strength values of microcapsules/bitumen samples (microcapsules: 3.0 wt. %, 20 μm) during a reparative fracture-healing process (four recycles, each healing time: 24 h) under different temperatures.</p>
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<p>Tension strength values of microcapsules/bitumen samples (microcapsules sample-5, 3.0 wt. %, 20 μm) during a fracture-healing process under 10 °C with healing time of: 4 h, 8 h, 12 h, 16 h and 20 h.</p>
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<p>Self-healing capability of microcapsules/bitumen samples (microcapsules: 3.0 wt. %, 20 μm) calculated by properties values (penetration, softening point and viscosity) during a reparative fracture-healing process (four recycles) under 0 °C, each cycle healing time of 24 h.</p>
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<p>Morphologies of broken microcapsules on the surface of cracks under temperature of (<b>a</b>) 0 °C; (<b>b</b>) 10 °C; and (<b>c</b>) 20 °C.</p>
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<p>Fluorescence microscopy morphologies of microcapsules/bitumen sample (bitumen, 40/50; microcapsule, 20 μm, 3.0 wt. %) of (<b>a</b>) original; (<b>b</b>) after going through the healing cycle once and (<b>c</b>) going through the healing cycle twice.</p>
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<p>Tension fracture of microcapsules/bitumen samples: Images of bitumen samples broken process using a displacement speed of 100 mm·min<sup>−1</sup> at 0 °C, (<b>a</b>–<b>d</b>) the pure bitumen (40/50), (<b>a</b>’–<b>d</b>’) the re-fracture of the same sample of bitumen (40/50) mixing with microcapsules (20 μm, 3.0 wt. %): <b>A</b> and <b>B</b> are the strain-stress curves.</p>
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<p>Illustration of self-healing of bitumen during tension test; (<b>a</b>) tension test sample; (<b>b</b>–<b>e</b>) the first-cycle of tension fracture; (<b>f</b>) the broken microcapsules on the interface of crack; (<b>g</b>) the healing process of bitumen sample; and (<b>h</b>–<b>j</b>) the second-cycle of tension fracture, rejuvenator penetration into aged bitumen.</p>
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3243 KiB  
Review
Recent Developments in Antimicrobial Polymers: A Review
by Madson R. E. Santos, Ana C. Fonseca, Patrícia V. Mendonça, Rita Branco, Arménio C. Serra, Paula V. Morais and Jorge F. J. Coelho
Materials 2016, 9(7), 599; https://doi.org/10.3390/ma9070599 - 20 Jul 2016
Cited by 163 | Viewed by 12910
Abstract
Antimicrobial polymers represent a very promising class of therapeutics with unique characteristics for fighting microbial infections. As the classic antibiotics exhibit an increasingly low capacity to effectively act on microorganisms, new solutions must be developed. The importance of this class of materials emerged [...] Read more.
Antimicrobial polymers represent a very promising class of therapeutics with unique characteristics for fighting microbial infections. As the classic antibiotics exhibit an increasingly low capacity to effectively act on microorganisms, new solutions must be developed. The importance of this class of materials emerged from the uncontrolled use of antibiotics, which led to the advent of multidrug-resistant microbes, being nowadays one of the most serious public health problems. This review presents a critical discussion of the latest developments involving the use of different classes of antimicrobial polymers. The synthesis pathways used to afford macromolecules with antimicrobial properties, as well as the relationship between the structure and performance of these materials are discussed. Full article
(This article belongs to the Special Issue Self-Cleaning and Antimicrobial Surfaces)
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<p>Schematic representation of the different types of antimicrobial polymeric systems (adapted from [<a href="#B8-materials-09-00599" class="html-bibr">8</a>]).</p>
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<p>Structure of chitosan.</p>
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<p>Structure of ε-PL at pH &lt; pI.</p>
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<p>Chemical structure of the homopolymers PSSAmC<sub>16</sub>, PSSPhC<sub>16</sub>, PVBCHAM and the copolymers P(MMA-<span class="html-italic">co</span>-VBCHAM), P(SSNa-<span class="html-italic">co</span>-VBCHAM) and P(AA-<span class="html-italic">co</span>-VBCHAM) [<a href="#B129-materials-09-00599" class="html-bibr">129</a>].</p>
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<p>Mechanism of the transition between attack function (CB-ring, killing bacteria) and defense function (CB–OH resists and releases bacteria) (adapted from [<a href="#B135-materials-09-00599" class="html-bibr">135</a>]).</p>
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<p>Chemical structure of ammonium ethyl methacrylate homopolymer (AEMPs) [<a href="#B136-materials-09-00599" class="html-bibr">136</a>].</p>
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<p>Chemical structures for: (<b>a</b>) poly-(ethylene imine); (<b>b</b>) alkyl chains directly linked to cationic groups and (<b>c</b>) alkyl chains and cationic groups linked by a spacer [<a href="#B150-materials-09-00599" class="html-bibr">150</a>].</p>
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<p>Chemical structure of poly(vinyl amine) with cationic, azetidinium and alkyl groups on the side chain [<a href="#B151-materials-09-00599" class="html-bibr">151</a>].</p>
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<p>Structure of TMC.</p>
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<p>Structures of the sulfonamide-chitosan derivatives prepared by Dragostin et al. (adapted from [<a href="#B154-materials-09-00599" class="html-bibr">154</a>]).</p>
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<p>Structure of the chitosan derivatives bearing quaternary phosphonium salts used by Zhu et al. [<a href="#B155-materials-09-00599" class="html-bibr">155</a>].</p>
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<p>Structures of the <span class="html-italic">O</span>-quaternary ammonium salt chitosan derivatives.</p>
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<p>Structures of the prodrug methacrylated monomers: (<b>a</b>) prodrug with the aliphatic ester linkage; and (<b>b</b>) prodrug with the aromatic ester linkage. In red is represented the structure of ciprofloxacin.</p>
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<p>Synthesis route of the cationic random copolymer: (PTPB) (4-penten-1-yl) triphenylphosphonium bromide, (AM) acrylamide and (DADMAC) diallyl dimethyl ammonium chloride using 2,20-azobis(2-methylpropionamidine)dihydrochloride (AIBA) as initiator [<a href="#B127-materials-09-00599" class="html-bibr">127</a>].</p>
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<p>Mechanism for the synthesis of P(SSAmC<sub>16</sub>-<span class="html-italic">co</span>-VBCHAM<sub>x</sub>) copolymers [<a href="#B129-materials-09-00599" class="html-bibr">129</a>].</p>
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<p>Reaction scheme of the preparation of a synthetic polymer mimic AMPs based on a guanidinium salt [<a href="#B10-materials-09-00599" class="html-bibr">10</a>].</p>
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<p>Synthesis of random copolymers containing either amine or guanidine pendant groups [<a href="#B148-materials-09-00599" class="html-bibr">148</a>].</p>
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2979 KiB  
Article
Benefits of Sealed-Curing on Compressive Strength of Fly Ash-Based Geopolymers
by Sujeong Lee, Arie Van Riessen and Chul-Min Chon
Materials 2016, 9(7), 598; https://doi.org/10.3390/ma9070598 - 20 Jul 2016
Cited by 33 | Viewed by 5185
Abstract
There is no standardized procedure for producing geopolymers; therefore, many researchers develop their own procedures for mixing and curing to achieve good workability and strength development. The curing scheme adopted is important in achieving maximum performance of resultant geopolymers. In this study, we [...] Read more.
There is no standardized procedure for producing geopolymers; therefore, many researchers develop their own procedures for mixing and curing to achieve good workability and strength development. The curing scheme adopted is important in achieving maximum performance of resultant geopolymers. In this study, we evaluated the impact of sealed and unsealed curing on mechanical strength of geopolymers. Fly ash-based geopolymers cured in sealed and unsealed moulds clearly revealed that retention of water during curing resulted in superior strength development. The average compressive strength of sealed-cured geopolymers measured after 1 day of curing was a modest 50 MPa, while after 7 day curing the average compressive strength increased to 120~135 MPa. In the unsealed specimens the average compressive strength of geopolymers was lower; ranging from 60 to 90 MPa with a slight increase as the curing period increased. Microcracking caused by dehydration is postulated to cause the strength decrease in the unsealed cured samples. These results show that water is a crucial component for the evolution of high strength three-dimensional cross-linked networks in geopolymers. Full article
(This article belongs to the Special Issue Advances in Geopolymers and Alkali-Activated Materials)
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<p>Particle size distribution for as-received ash and milled ash analysed by means of a laser diffractometer. Top cut (D97) particle size was reduced from 156.2 to 20.5 μm.</p>
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<p>Percentage weight loss with temperatures ranging from room temperature to 900 °C.</p>
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<p>Thermogravimetric curves for the sealed “A” and the unsealed “B” series geopolymer specimens. The sealed “A” series specimens lost relatively more moisture at low temperatures and the weight loss at high temperatures was reversed.</p>
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<p>Compressive strength of geopolymers of the sealed “A” series specimens and the unsealed “B” series specimens. “A” series specimens in sealed moulds presented higher compressive strength at testing periods. Numbers in the bars are the apparent density (g/cm<sup>3</sup>).</p>
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<p>BET surface area (♦) and BJH desorption average pore diameter (◦) of geopolymers. The sealed specimens presented higher BET surface area with smaller pore diameter compared with the unsealed specimens.</p>
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<p>X-ray diffraction patterns of geopolymers described in <a href="#materials-09-00598-t001" class="html-table">Table 1</a>. XRD patterns do not show any differences that could explain the substantial strength difference between the “A” and “B” series specimens.</p>
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<p>NMR spectra of samples A1, A7 and B7.</p>
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7222 KiB  
Article
A Numerical Study on the Effect of Debris Layer on Fretting Wear
by Tongyan Yue and Magd Abdel Wahab
Materials 2016, 9(7), 597; https://doi.org/10.3390/ma9070597 - 20 Jul 2016
Cited by 77 | Viewed by 7701
Abstract
Fretting wear is the material damage of two contact surfaces caused by micro relative displacement. Its characteristic is that debris is trapped on the contact surfaces. Depending on the material properties, the shapes of the debris, and the dominant wear mechanisms, debris can [...] Read more.
Fretting wear is the material damage of two contact surfaces caused by micro relative displacement. Its characteristic is that debris is trapped on the contact surfaces. Depending on the material properties, the shapes of the debris, and the dominant wear mechanisms, debris can play different roles that either protect or harm interfaces. Due to the micro scale of the debris, it is difficult to obtain instantaneous information and investigate debris behavior in experiments. The Finite Element Method (FEM) has been used to model the process of fretting wear and calculate contact variables, such as contact stress and relative slip during the fretting wear process. In this research, a 2D fretting wear model with a debris layer was developed to investigate the influence of debris on fretting wear. Effects of different factors such as thickness of the debris layer, Young’s modulus of the debris layer, and the time of importing the layer into the FE model were considered in this study. Based on FE results, here we report that: (a) the effect of Young’s modulus of the debris layer on the contact pressure is not significant; (b) the contact pressure between the debris layer and the flat specimen decreases with increasing thickness of the layer and (c) by importing the debris layer in different fretting wear cycles, the debris layer shows different roles in the wear process. At the beginning of the wear cycle, the debris layer protects the contact surfaces of the first bodies (cylindrical pad and flat specimen). However, in the final cycle, the wear volumes of the debris layers exhibit slightly higher damage compared to the model without the debris layer in all considered cases. Full article
(This article belongs to the Special Issue Numerical Analysis of Tribology Behavior of Materials)
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<p>The fretting wear model with debris layer: (<b>a</b>) global scale with dimensions and (<b>b</b>) local configuration at the contact zone.</p>
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<p>Wear scars of the specimen after different fretting wear cycles; <span class="html-italic">P</span> = 185 N and <span class="html-italic">D</span> = 25 µm.</p>
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<p>Contact interaction of the debris layer model.</p>
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<p>The flowchart of the fretting wear simulation with the debris layer.</p>
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<p>Contact pressure distributions of the top and bottom interfaces for different <span class="html-italic">E</span>s of the debris layer; <span class="html-italic">t</span> = 5 µm.</p>
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<p>Contact pressure distributions of the top interface for different thicknesses of the debris layer; <span class="html-italic">E</span> = 360 GPa.</p>
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<p>Contact pressure distributions of the bottom interface for different thicknesses of the debris layer, <span class="html-italic">E</span> = 360 GPa.</p>
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<p>Contact pressure distribution for different layer thicknesses and number of cycles: layer thickness = 5 µm, 10 µm, 20 µm and without layer after 500 cycles.</p>
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<p>Contact pressure distribution for different layer thicknesses and number of cycles: layer thickness = 5 µm, 10 µm, 20 µm and without layer after 1500 cycles.</p>
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<p>Contact pressure distribution for different layer thicknesses and number of cycles: layer thickness = 5 µm, 10 µm, 20 µm and without layer, after 2500 cycles.</p>
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<p>Wear scars after 1000 cycles: importing time= 500 cycles and layer thickness = 5 µm, 10 µm, 20 µm.</p>
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<p>Wear scars after 2000 cycles and 3000 cycles: importing time = 1500, 2500 cycles and layer thickness = 5 µm, 10 µm, 20 µm.</p>
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<p>Wear scar after 3000 cycles of the debris layer model: importing time = 500 cycles and layer thickness = 5 µm, 10 µm, 20 µm.</p>
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<p>Wear scar after 3000 cycles of the debris layer model: importing time = 1500 cycles and layer thickness = 5 µm, 10 µm, 20 µm.</p>
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<p>Wear scar after 3000 cycles of the debris layer model: importing time = 2500 cycles and layer thickness = 5 µm, 10 µm, 20 µm.</p>
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<p>Wear scar after 18,000 cycles based on debris layer model: importing time = 500, 1500, 2500 cycles and layer thickness = 5 µm, 10 µm, 20 µm.</p>
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<p>Difference of wear damage compared to the case of basic model, after 1000 cycles, 2000 cycles and 3000 cycles.</p>
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<p>Difference of wear damage compared to the case of basic model, after 3000 cycles.</p>
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<p>Difference of wear damage compared to the case of basic model, after 18,000 cycles.</p>
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9456 KiB  
Article
Microstructures and Mechanical Properties of Co-Cr Dental Alloys Fabricated by Three CAD/CAM-Based Processing Techniques
by Hae Ri Kim, Seong-Ho Jang, Young Kyung Kim, Jun Sik Son, Bong Ki Min, Kyo-Han Kim and Tae-Yub Kwon
Materials 2016, 9(7), 596; https://doi.org/10.3390/ma9070596 - 20 Jul 2016
Cited by 116 | Viewed by 8484
Abstract
The microstructures and mechanical properties of cobalt-chromium (Co-Cr) alloys produced by three CAD/CAM-based processing techniques were investigated in comparison with those produced by the traditional casting technique. Four groups of disc- (microstructures) or dumbbell- (mechanical properties) specimens made of Co-Cr alloys were prepared [...] Read more.
The microstructures and mechanical properties of cobalt-chromium (Co-Cr) alloys produced by three CAD/CAM-based processing techniques were investigated in comparison with those produced by the traditional casting technique. Four groups of disc- (microstructures) or dumbbell- (mechanical properties) specimens made of Co-Cr alloys were prepared using casting (CS), milling (ML), selective laser melting (SLM), and milling/post-sintering (ML/PS). For each technique, the corresponding commercial alloy material was used. The microstructures of the specimens were evaluated via X-ray diffractometry, optical and scanning electron microscopy with energy-dispersive X-ray spectroscopy, and electron backscattered diffraction pattern analysis. The mechanical properties were evaluated using a tensile test according to ISO 22674 (n = 6). The microstructure of the alloys was strongly influenced by the manufacturing processes. Overall, the SLM group showed superior mechanical properties, the ML/PS group being nearly comparable. The mechanical properties of the ML group were inferior to those of the CS group. The microstructures and mechanical properties of Co-Cr alloys were greatly dependent on the manufacturing technique as well as the chemical composition. The SLM and ML/PS techniques may be considered promising alternatives to the Co-Cr alloy casting process. Full article
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<p>XRD patterns of the Co-Cr alloys tested. The black arrow in the ML group indicates a shift of the (111) plane. The SLM group showed only the presence of the Co-based <span class="html-italic">γ</span> (fcc) phase. The carbide (M<sub>23</sub>C<sub>6</sub>) formation was identified only in the ML/PS group.</p>
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<p>Optical microscopy images of the Co-Cr alloys tested. (<b>a</b>) CS; (<b>b</b>) ML; (<b>c</b>) SLM; and (<b>d</b>) ML/PS (200×, scale bar = 100 μm). The red rounded squares in the small box in C indicate laser scan traces (small box in C: 100×, scale bar = 100 μm).</p>
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<p>BSE images of the Co-Cr alloys tested. (<b>a</b>) CS; (<b>b</b>) ML; (<b>c</b>) SLM; and (<b>d</b>) ML/PS (500×, scale bar = 30 μm). The secondary phases were observed in the CS and ML specimens, but such phases were absent in the SLM specimen.</p>
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<p>BSE and corresponding EDS mapping images for each group. (<b>a</b>) CS; (<b>b</b>) ML; (<b>c</b>) SLM; and (<b>d</b>) ML/PS (500×, scale bar = 50 μm).</p>
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<p>BSE images of the Co-Cr alloys for EDS point analysis. (<b>a</b>) CS; (<b>b</b>) ML; (<b>c</b>) SLM; and (<b>d</b>) ML/PS (10,000×, scale bar = 1 μm). In each figure, the numbers indicate the points subjected to the EDS analysis.</p>
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<p>BSE image (band contrast map) for each group and corresponding phase and inverse pole figure (IPF) maps. (<b>a</b>) CS; (<b>b</b>) ML; (<b>c</b>) SLM; and (<b>d</b>) ML/PS (500×, scale bar = 50 μm).</p>
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<p>Comparison of mechanical properties of the four Co-Cr alloys tested (<span class="html-italic">n</span> = 6). For each figure, means with different letters indicate statistical differences between groups (<span class="html-italic">p</span> &lt; 0.05). The green and blue horizontal lines indicate the type 4 and 5 criteria (minimum value), respectively, in ISO 22674. The type 4 and 5 criteria are the same for percent elongation (black horizontal line).</p>
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<p>SEM images of the fractured surfaces after tensile test. (<b>a</b>) CS; (<b>b</b>) ML; (<b>c</b>) SLM; and (<b>d</b>) ML/PS (500×, scale bar = 30 μm).</p>
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9507 KiB  
Review
Optimization of Layered Cathode Materials for Lithium-Ion Batteries
by Christian Julien, Alain Mauger, Karim Zaghib and Henri Groult
Materials 2016, 9(7), 595; https://doi.org/10.3390/ma9070595 - 19 Jul 2016
Cited by 93 | Viewed by 14300
Abstract
This review presents a survey of the literature on recent progress in lithium-ion batteries, with the active sub-micron-sized particles of the positive electrode chosen in the family of lamellar compounds LiMO2, where M stands for a mixture of Ni, [...] Read more.
This review presents a survey of the literature on recent progress in lithium-ion batteries, with the active sub-micron-sized particles of the positive electrode chosen in the family of lamellar compounds LiMO2, where M stands for a mixture of Ni, Mn, Co elements, and in the family of yLi2MnO3•(1 − y)LiNi½Mn½O2 layered-layered integrated materials. The structural, physical, and chemical properties of these cathode elements are reported and discussed as a function of all the synthesis parameters, which include the choice of the precursors and of the chelating agent, and as a function of the relative concentrations of the M cations and composition y. Their electrochemical properties are also reported and discussed to determine the optimum compositions in order to obtain the best electrochemical performance while maintaining the structural integrity of the electrode lattice during cycling. Full article
(This article belongs to the Special Issue Advances in Renewable Energy Conversion Materials)
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<p>Schematic figure of a Li-ion battery. LiCoO<sub>2</sub> is used as a cathode and graphite as an anode.</p>
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<p>Schematic representation of the energy diagram vs. density of states for Li<sub>x</sub>Ni<sub>1/3</sub>Mn<sub>1/3</sub>Co<sub>1/3</sub>O<sub>2</sub> at different charge states. The Fermi level of the cathode material is represented for three state of charge. (<b>a</b>) Full discharge; (<b>b</b>) half discharge; (<b>c</b>) full charge.</p>
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<p>Ternary phase diagram of the mixed transition-metal oxides LiNi<sub>w</sub>Mn<sub>y</sub>Co<sub>z</sub>O<sub>2</sub> (<span class="html-italic">w</span> + <span class="html-italic">y</span> + <span class="html-italic">z</span> = 1) formed by the LiCoO<sub>2</sub>-LiNiO<sub>2</sub>-LiMnO<sub>2</sub> solid solutions. The compounds studied in this work are marked in red. The samples are noted (<span class="html-italic">w’y’z’</span>) where <span class="html-italic">w</span><span class="html-italic">’</span> = 10<span class="html-italic">w</span>, <span class="html-italic">y’ =</span> 10<span class="html-italic">y</span> and <span class="html-italic">z’ =</span> 10<span class="html-italic">z</span>.</p>
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<p>HRTEM images of LiNi<sub>0.55</sub>Co<sub>0.45</sub>O<sub>2</sub> layered powders with different particle sizes: ca. 100–150 nm (<b>a</b>) and 1.5–2.0 µm (<b>b</b>) and discharge profiles as a function of C-rate for Li//LiNi<sub>0.55</sub>Co<sub>0.45</sub>O<sub>2</sub> coin-type cells with two cathode materials of 100 nm and 2 µm particle size. The good crystallinity of powders is shown by the electron diffraction diagram (inset); (<b>c</b>) discharge curves for 100–150 nm; (<b>d</b>) discharge curves for 1.5–2.0 µm.</p>
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<p>SEM images of NMC samples: (<b>a</b>) 333; (<b>b</b>) 442; and (<b>c</b>) 532 compounds prepared by solid-state reaction at 850 °C in air.</p>
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<p>Rietveld refinement patterns of NMC samples: (<b>a</b>) 333; (<b>b</b>) 442; (<b>c</b>) 532 synthesized by solid-state reaction. The cross marks show observed XRD intensities and the solid line (red) represents calculated intensities. The curve at the bottom (blue) is the difference between the calculated and observed intensities on the same scale.</p>
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<p>Typical discharge profiles of different Li//NMC cells with cathodes synthesized by the solid-state reaction route at 850 °C. The electrochemical test were carried out at discharge rate C/5 in the voltage window 2.8–4.6 V vs. Li<sup>0</sup>/Li<sup>+</sup>.</p>
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<p>Discharge profiles vs. specific capacity of the Li//LiNi<sub>0.4</sub>Mn<sub>0.4</sub>Co<sub>0.2</sub>O<sub>2</sub> cells between 2.5 and 4.4 V at various C-rates. The inset shows the rate capability of the 442 compound.</p>
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<p>SEM (<b>a</b>) and HRTEM (<b>b</b>) images of Li<sub>1.04</sub>Ni<sub>0.32</sub>Mn<sub>0.32</sub>Co<sub>0.32</sub>O<sub>2</sub> powders synthesized the co-precipitation method from hydroxide precursor assisted by ammonium and sodium hydroxides.</p>
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<p>Electrochemical performance of Li<sub>1+x</sub>(NMC)<sub>1-x</sub>O<sub>2</sub> electrode materials as a function of synthetic parameters. The specific capacity of the Li cells is plotted for different C-rates.</p>
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<p>(<b>a</b>) TG/DTA profile for the precursor of NMC synthesized by the co-precipitation technique using metal acetates as raw materials and succinic acid as a polymeric agent with a chelate to metal ion molar ratio <span class="html-italic">R</span> = 0.5 (<b>a</b>) and <span class="html-italic">R</span> = 2 (<b>b</b>). With <span class="html-italic">R</span> = 2, the combustion temperature is lowered to 342 °C.</p>
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<p>(<b>a</b>) Rietveld refinement patterns of NMC synthesized at <span class="html-italic">R</span> = 2 via wet chemical method (<span class="html-italic">R</span><sub>p</sub> = 9.8%). The plus marks show observed X-ray diffraction intensities and the solid line (in red on the web version) represents calculated intensities. The curve at the bottom (in blue on the web version) is the difference between the calculated and observed intensities on the same scale; (<b>b</b>) The concentration of Ni(3<span class="html-italic">b</span>) defects (site-exchange rate of the Li<sup>+</sup>/Ni<sup>2+</sup> cation mixing) as a function of the <span class="html-italic">R</span> parameter for the symmetric NMC compounds.</p>
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<p>(<b>a</b>,<b>b</b>) SEM images of NMC synthesized at <span class="html-italic">R</span> = 2 via wet chemical method at different magnifications; (<b>c</b>) HRTEM image showing the fringe system corresponding to the spacing between (003) lattice planes in the <math display="inline"> <semantics> <mrow> <mi>R</mi> <mover accent="true"> <mn>3</mn> <mo stretchy="true">¯</mo> </mover> <mi>m</mi> </mrow> </semantics> </math> space group.</p>
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<p>Initial discharge profiles of synthesized NMC sample sintered at 900 °C for 15 h, synthesized with chelate to metal ion ratio at 0.5 ≤ <span class="html-italic">R</span> ≤ 3.0.</p>
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<p>Peukert plots showing the difference in the electrochemical performance of LiNi<sub>1/3</sub>Mn<sub>1/3</sub>Co<sub>1/3</sub>O<sub>2</sub> electrodes synthesized using wet-chemical method assisted by oxalic and tartaric acid.</p>
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<p>Initial capacity loss of LiNi<sub>1/3</sub>Mn<sub>1/3</sub>Co<sub>1/3</sub>O<sub>2</sub> electrodes cycled at C/20 as a function of the annealing temperature.</p>
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<p>(<b>a</b>–<b>c</b>) TEM images of individual LiNi<sub>0.33+<span class="html-italic">δ</span></sub>Mn<sub>0.33+<span class="html-italic">δ</span></sub>Co<sub>0.33-2<span class="html-italic">δ</span></sub>O<sub>2</sub> nanoparticles with <span class="html-italic">δ</span> = 0.025, 0.05, and 0.075, respectively; (<b>d</b>) HRTEM image of a nanoparticle (<span class="html-italic">δ</span> = 0.025) showing lattice fringes consistent with the interspacing of the (003) planes of the <math display="inline"> <semantics> <mrow> <mi>R</mi> <mover accent="true"> <mn>3</mn> <mo stretchy="true">¯</mo> </mover> <mi>m</mi> </mrow> </semantics> </math> layered structure.</p>
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<p>Evolution of the strain (&lt;<span class="html-italic">e</span><sup>2</sup>&gt;)<sup>1/2</sup> with the deviation from stoichiometry <span class="html-italic">δ</span> in LiNi<sub>0.33+<span class="html-italic">δ</span></sub>Mn<sub>0.33+<span class="html-italic">δ</span></sub>Co<sub>0.33-2<span class="html-italic">δ</span></sub>O<sub>2</sub> samples synthesized by the sol-gel method.</p>
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<p>Peukert plots for Li//LiNi<sub>0.33+<span class="html-italic">δ</span></sub>Mn<sub>0.33+<span class="html-italic">δ</span></sub>Co<sub>0.33-2<span class="html-italic">δ</span></sub>O<sub>2</sub> cells.</p>
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<p>HRTEM images of Li-rich cathode materials <span class="html-italic">y</span>Li<sub>2</sub>MnO<sub>3</sub>•(1 − <span class="html-italic">y</span>)(LiNi<sub>0.5</sub>Mn<sub>0.5</sub>O<sub>2</sub>). (<b>a</b>) <span class="html-italic">y</span> = 0.0 (LiNi<sub>0.5</sub>Mn<sub>0.5</sub>O<sub>2</sub>); (<b>b</b>) <span class="html-italic">y</span> = 0.3 (Li<sub>1.134</sub>Ni<sub>0.3</sub>Mn<sub>0.566</sub>O<sub>2</sub>); (<b>c</b>) <span class="html-italic">y</span> = 0.5 (Li<sub>1.2</sub>Ni<sub>0.2</sub>Mn<sub>0.6</sub>O<sub>2</sub>); (<b>d</b>) image magnification for Li<sub>1.2</sub>Ni<sub>0.2</sub>Mn<sub>0.6</sub>O<sub>2</sub> showing the hexagonal shape of nanoparticles.</p>
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<p>Charge–discharge profiles of Li//Li(Ni<sub>x</sub>Li<sub>(1/3-2x/3)</sub>Mn<sub>(2/3-x/3)</sub>)O<sub>2</sub> coin cells: (<b>a</b>) LiNi<sub>0.5</sub>Mn<sub>0.5</sub>O<sub>2</sub>; (<b>b</b>) Li<sub>1.134</sub>Ni<sub>0.3</sub>Mn<sub>0.556</sub>O<sub>2</sub>; and (<b>c</b>) Li<sub>1.2</sub>Ni<sub>0.2</sub>Mn<sub>0.6</sub>O<sub>2</sub>. Cycles were carried out at C/10 rate (30 mA·g<sup>−1</sup>) in the potential range 2.0–4.8 V vs. Li<sup>0</sup>/Li<sup>+</sup>.</p>
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<p>The first charge–discharge profile of a Li//Li<sub>1.2</sub>Ni<sub>0.2</sub>Mn<sub>0.6</sub>O<sub>2</sub> cell cycled at C/10, showing the mechanism of the activation of Li<sub>2</sub>MnO<sub>3</sub> and LiNi<sub>0.5</sub>Mn<sub>0.5</sub>O<sub>2</sub> components.</p>
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<p>Cyclic performance of Li//Li(Ni<sub>x</sub>Li<sub>(1/3-2x/3)</sub>Mn<sub>(2/3-x/3)</sub>)O<sub>2</sub> electrodes at C/10.</p>
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1305 KiB  
Article
Spectroscopic Study of Plasma Polymerized a-C:H Films Deposited by a Dielectric Barrier Discharge
by Thejaswini Halethimmanahally Chandrashekaraiah, Robert Bogdanowicz, Eckart Rühl, Vladimir Danilov, Jürgen Meichsner, Steffen Thierbach and Rainer Hippler
Materials 2016, 9(7), 594; https://doi.org/10.3390/ma9070594 - 19 Jul 2016
Cited by 10 | Viewed by 6049
Abstract
Plasma polymerized a-C:H thin films have been deposited on Si (100) and aluminum coated glass substrates by a dielectric barrier discharge (DBD) operated at medium pressure using C2Hm/Ar (m = 2, 4, 6) gas mixtures. The deposited films [...] Read more.
Plasma polymerized a-C:H thin films have been deposited on Si (100) and aluminum coated glass substrates by a dielectric barrier discharge (DBD) operated at medium pressure using C2Hm/Ar (m = 2, 4, 6) gas mixtures. The deposited films were characterized by Fourier transform infrared reflection absorption spectroscopy (FT-IRRAS), Raman spectroscopy, and ellipsometry. FT-IRRAS revealed the presence of sp3 and sp2 C–H stretching and C–H bending vibrations of bonds in the films. The presence of D and G bands was confirmed by Raman spectroscopy. Thin films obtained from C2H4/Ar and C2H6/Ar gas mixtures have ID/IG ratios of 0.45 and 0.3, respectively. The refractive indices were 2.8 and 3.1 for C2H4/Ar and C2H6/Ar films, respectively, at a photon energy of 2 eV. Full article
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<p>Photographs of a-C:H films deposited on glass substrates in a dielectric barrier discharge (DBD) with different precursor gases C<sub>2</sub>H<span class="html-italic"><sub>m</sub></span>/Ar (<span class="html-italic">m</span> = 2, 4, 6).</p>
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<p>(<b>a</b>) FTIR spectra of a-C:H films obtained from C<sub>2</sub>H<span class="html-italic"><sub>m</sub></span>/Ar (<span class="html-italic">m</span> = 2, 4, 6) gas mixture, (gas pressure = 300 mbar, gas ratio = 1:2, power = 4 W). To ease comparison, the data obtained with C<sub>2</sub>H<sub>6</sub>/Ar and C<sub>2</sub>H<sub>4</sub>/Ar are shifted upwards by 0.2 and 0.3, respectively; (<b>b</b>) Magnification of the FTIR region 3030–2820 cm<sup>−1</sup>. For comparison, the data obtained with C<sub>2</sub>H<sub>6</sub>/Ar and C<sub>2</sub>H<sub>4</sub>/Ar are shifted upwards.</p>
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<p>Raman spectra of a-C:H films obtained from C<sub>2</sub>H<span class="html-italic"><sub>m</sub></span>/Ar (<span class="html-italic">m</span> = 4, 6) gas mixtures, (gas pressure <span class="html-italic">p</span> = 300 mbar, gas ratio 1:2, power <span class="html-italic">p</span> = 4 W).</p>
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<p>Wavelength-dependence of the optical constants <span class="html-italic">n</span>(λ) and <span class="html-italic">k</span>(λ) for the films prepared with C<sub>2</sub>H<sub>4</sub>/Ar and C<sub>2</sub>H<sub>6</sub>/Ar gas mixtures.</p>
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<p>Absorption coefficients for the films prepared with C<sub>2</sub>H<sub>4</sub>/Ar and C<sub>2</sub>H<sub>6</sub>/Ar gas mixtures obtained from spectroscopic ellipsometry.</p>
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3359 KiB  
Article
Binary Alkali-Metal Silicon Clathrates by Spark Plasma Sintering: Preparation and Characterization
by Igor Veremchuk, Matt Beekman, Iryna Antonyshyn, Walter Schnelle, Michael Baitinger, George S. Nolas and Yuri Grin
Materials 2016, 9(7), 593; https://doi.org/10.3390/ma9070593 - 19 Jul 2016
Cited by 9 | Viewed by 5454
Abstract
The binary intermetallic clathrates K8-xSi46 (x = 0.4; 1.2), Rb6.2Si46, Rb11.5Si136 and Cs7.8Si136 were prepared from M4Si4 (M = K, Rb, Cs) precursors by [...] Read more.
The binary intermetallic clathrates K8-xSi46 (x = 0.4; 1.2), Rb6.2Si46, Rb11.5Si136 and Cs7.8Si136 were prepared from M4Si4 (M = K, Rb, Cs) precursors by spark-plasma route (SPS) and structurally characterized by Rietveld refinement of PXRD data. The clathrate-II phase Rb11.5Si136 was synthesized for the first time. Partial crystallographic site occupancy of the alkali metals, particularly for the smaller Si20 dodecahedra, was found in all compounds. SPS preparation of Na24Si136 with different SPS current polarities and tooling were performed in order to investigate the role of the electric field on clathrate formation. The electrical and thermal transport properties of K7.6Si46 and K6.8Si46 in the temperature range 4–700 K were investigated. Our findings demonstrate that SPS is a novel tool for the synthesis of intermetallic clathrate phases that are not easily accessible by conventional synthesis techniques. Full article
(This article belongs to the Special Issue Inorganic Clathrate Materials)
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<p>Crystal structures of (<b>a</b>) Na<sub>4</sub>Si<sub>4</sub>; (<b>b</b>) <span class="html-italic">M</span><sub>4</sub>Si<sub>4</sub> (<span class="html-italic">M</span> = K, Rb, or Cs); (<b>c</b>) <span class="html-italic">M</span><sub>8-<span class="html-italic">x</span></sub>Si<sub>46</sub>; and (<b>d</b>) <span class="html-italic">M</span><sub>24-<span class="html-italic">x</span></sub>Si<sub>136</sub>.</p>
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<p>(<b>a</b>) SPS setup for the preparation of clathrates; (<b>b</b>–<b>e</b>) Location and relative amounts of the reaction products for different polarities and different die and punch materials; (<b>f</b>–<b>h</b>) Optical micrographs of the cross-sections from fractured post-reaction pellets illustrating the directional growth of clathrates at the anode.</p>
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<p>Powder X-ray diffraction (PXRD) patterns of the SPS-prepared clathrates-I K<sub>7.6</sub>Si<sub>46</sub> (550 °C) and K<sub>6.8</sub>Si<sub>46</sub> (600 °C). Red asterisks mark the reflections of <span class="html-italic">α</span>-Si (&lt;0.2 mass % in K<sub>7.6</sub>Si<sub>46</sub> and 1.5 mass % in K<sub>6.8</sub>Si<sub>46</sub>). The experimental intensities are shown as a solid line. The difference between the experimental and calculated intensities is shown below the experimental data; the tick marks represent the positions of the diffraction reflections of the clathrate-I phase.</p>
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<p>Powder X-ray diffraction (PXRD) patterns of the Rb<sub>6.2</sub>Si<sub>46</sub> and Rb<sub>11.1</sub>Si<sub>136</sub> mixed product and clathrate-II Cs<sub>7.8</sub>Si<sub>136</sub>. The experimental intensities are shown as a solid line. The differences between the experimental and calculated intensities are shown below the experimental data. The tick marks represent the positions of the diffraction reflections. Red asterisks mark the reflections from <span class="html-italic">α</span>-Si (&lt;0.2 mass % in Rb<sub>6.2</sub>Si<sub>46</sub> and Rb<sub>11.1</sub>Si<sub>136</sub> and 2.5 mass % in Cs<sub>7.8</sub>Si<sub>136</sub>).</p>
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<p>Lattice parameters versus <span class="html-italic">M</span> content, <span class="html-italic">x</span> for clathrate-I Na<span class="html-italic"><sub>x</sub></span>Si<sub>136</sub> (0 &lt; <span class="html-italic">x</span> &lt; 24) [<a href="#B28-materials-09-00593" class="html-bibr">28</a>], Na<sub>24</sub>Si<sub>136</sub> [<a href="#B16-materials-09-00593" class="html-bibr">16</a>], K<sub>17.2</sub>Si<sub>136</sub> [<a href="#B19-materials-09-00593" class="html-bibr">19</a>], Rb<sub>11.5</sub>Si<sub>136</sub> (this work), and Cs<sub>7.8</sub>Si<sub>136</sub> (this work), as well as ternary Rb<sub>8</sub>Na<sub>16</sub>Si<sub>136</sub> and Cs<sub>8</sub>Na<sub>16</sub>Si<sub>136</sub> [<a href="#B27-materials-09-00593" class="html-bibr">27</a>].</p>
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<p>Transport properties of polycrystalline K<sub>7.6</sub>Si<sub>46</sub> and K<sub>6.8</sub>Si<sub>46</sub>. The low temperature, 2 to 300 K, and high temperature, 300 to 700 K, are described in the text. (<b>Top</b>) electrical resistivity <span class="html-italic">ρ</span>; (<b>Middle</b>) Seebeck coefficient <span class="html-italic">S</span>; (<b>Bottom</b>) thermal conductivity <span class="html-italic">κ</span>.</p>
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<p>Transport properties of polycrystalline K<sub>7.6</sub>Si<sub>46</sub> and K<sub>6.8</sub>Si<sub>46</sub>. The low temperature, 2 to 300 K, and high temperature, 300 to 700 K, are described in the text. (<b>Top</b>) electrical resistivity <span class="html-italic">ρ</span>; (<b>Middle</b>) Seebeck coefficient <span class="html-italic">S</span>; (<b>Bottom</b>) thermal conductivity <span class="html-italic">κ</span>.</p>
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7624 KiB  
Article
Acoustic Performance of Resilient Materials Using Acrylic Polymer Emulsion Resin
by Haseog Kim, Sangki Park and Seahyun Lee
Materials 2016, 9(7), 592; https://doi.org/10.3390/ma9070592 - 19 Jul 2016
Cited by 4 | Viewed by 6189
Abstract
There have been frequent cases of civil complaints and disputes in relation to floor impact noises over the years. To solve these issues, a substantial amount of sound resilient material is installed between the concrete slab and the foamed concrete during construction. A [...] Read more.
There have been frequent cases of civil complaints and disputes in relation to floor impact noises over the years. To solve these issues, a substantial amount of sound resilient material is installed between the concrete slab and the foamed concrete during construction. A new place-type resilient material is made from cement, silica powder, sodium sulfate, expanded-polystyrene, anhydrite, fly ash, and acrylic polymer emulsion resin. Its physical characteristics such as density, compressive strength, dynamic stiffness, and remanent strain are analyzed to assess the acoustic performance of the material. The experimental results showed the density and the dynamic stiffness of the proposed resilient material is increased with proportional to the use of cement and silica powder due to the high contents of the raw materials. The remanent strain, related to the serviceability of a structure, is found to be inversely proportional to the density and strength. The amount of reduction in the heavyweight impact noise is significant in a material with high density, high strength, and low remanent strain. Finally, specimen no. R4, having the reduction level of 3 dB for impact ball and 1 dB for bang machine in the single number quantity level, respectively, is the best product to obtain overall acoustic performance. Full article
(This article belongs to the Section Advanced Composites)
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<p>A mold for specimen of a place-type resilient material.</p>
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<p>Schematic diagram of the place-type resilient material.</p>
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<p>Experiment process of the place-type resilient material.</p>
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<p>Test method for dynamic stiffness by pulse shaker.</p>
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<p>Measuring thickness according to time and weight for remanent strain.</p>
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<p>The proposed place-type resilient material.</p>
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<p>Variations of density according to mixing conditions.</p>
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<p>Variations of compressive strength according to mixing conditions.</p>
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<p>Variations of dynamic stiffness according to mixing conditions.</p>
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<p>Variations of remanent strain according to mixing conditions.</p>
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<p>Schematic overview of floor system with resilient materials installation: (<b>a</b>) typical floor system; and (<b>b</b>) proposed floor system.</p>
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<p>Construction process for floor system using resilient materials.</p>
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<p>Overview and floor plan of the test building: (<b>a</b>) ISO view of the test building; and (<b>b</b>) floor plan of the test building.</p>
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<p>Two floor impact sources.</p>
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<p>Floor impact sound level with the proposed materials in 1/3 Octave bands—Impact ball.</p>
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<p>Floor impact sound level with the proposed materials in 1/1 Octave bands—Impact ball.</p>
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<p>Floor impact sound level with the proposed materials in 1/3 Octave bands—Bang machine.</p>
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<p>Floor impact sound level with the proposed materials in 1/1 Octave bands—Bang machine.</p>
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5460 KiB  
Article
Stereocomplexation in Copolymer Networks Incorporating Enantiomeric Glycerol-Based 3-Armed Lactide Oligomers and a 2-Armed ɛ-Caprolactone Oligomer
by Ayaka Shibita, Seina Kawasaki, Toshiaki Shimasaki, Naozumi Teramoto and Mitsuhiro Shibata
Materials 2016, 9(7), 591; https://doi.org/10.3390/ma9070591 - 19 Jul 2016
Cited by 5 | Viewed by 4930
Abstract
The reactions of enantiomeric glycerol-based 3-armed lactide oligomers (H3DLAO and H3LLAO) and a diethylene glycol-based 2-armed ɛ-caprolactone oligomer (H2CLO) with hexamethylene diisocyanate (HDI) produced polyesterurethane copolymer networks (PEU-3scLAO/2CLOs 100/0, 75/25, 50/50, 25/75 and 0/100) with different feed ratios of stereocomplex (sc) lactide oligomer [...] Read more.
The reactions of enantiomeric glycerol-based 3-armed lactide oligomers (H3DLAO and H3LLAO) and a diethylene glycol-based 2-armed ɛ-caprolactone oligomer (H2CLO) with hexamethylene diisocyanate (HDI) produced polyesterurethane copolymer networks (PEU-3scLAO/2CLOs 100/0, 75/25, 50/50, 25/75 and 0/100) with different feed ratios of stereocomplex (sc) lactide oligomer (H3scLAO = H3DLAO + H3LLAO, H3DLAO/H3LLAO = 1/1) and H2CLO. Thermal and mechanical properties of the copolymer networks were compared with those of a simple homochiral (hc) network (PEU-3DLAO) produced by the reaction of H3DLAO and HDI. X-ray diffraction and differential scanning calorimetric analyses revealed that sc crystallites are formed without any hc crystallization for PEU-3scLAO/2CLOs, and that PEU-3DLAO is amorphous. The melting temperatures of sc crystallites for PEU-3scLAO/2CLOs were much higher than that of hc crystallites of H3DLAO. The polarized optical microscopic analysis revealed that the nucleation efficiency is enhanced with increasing feed of H3scLAO fraction, whereas the spherulite growth rate is accelerated with increasing feed H2CLO fraction over 100/0-50/50 networks. PEU-3scLAO/2CLO 100/0 (i.e., PEU-3scLAO) exhibited a higher tensile strength and modulus than PEU-3DLAO. The elongation at break and tensile toughness for PEU-3scLAO/2CLOs increased with an increasing feed amount of H2CLO. Full article
(This article belongs to the Section Biomaterials)
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<p><sup>1</sup>H-NMR spectrum of H3LLAO in CDCl<sub>3</sub>.</p>
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<p>FT-IR spectra of H3LLAO, H3DLAO, PEU-3scLAO/2CLOs (100/0, 75/25, 50/50, 25/75 and 0/100) and HDI. For PEU-3scLAO/2CLOs, longitudinally enlarged spectra at the wavelength region from 3100 to 3600 cm<sup>−1</sup> are also shown in the figure.</p>
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<p>Degree of swelling for PEU-3scLAO/2CLOs (100/0, 75/25, 50/50, 25/75 and 0/100) in chloroform, DMF or ethanol.</p>
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<p>XRD profiles of H3LLAO, H3DLAO, PEU-3DLAO and PEU-3scLAO/2CLOs (100/0, 75/25, 50/50, 25/75 and 0/100).</p>
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<p>FE-SEM images of the fractured surfaces of PEU-3scLAO/2CLOs (100/0, 75/25, 50/50, 25/75 and 0/100).</p>
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<p>Polarized optical microscope images of the PEU-3scLAO/2CLOs (100/0, 75/25, 50/50, 25/75 and 0/100) held at a specified temperature for 10 or 50 min after melted at 220 °C.</p>
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<p>DMA curves of PEU-3scLAO/2CLOs (100/0, 75/25, 50/50, 25/75 and 0/100).</p>
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<p>TGA curves of H3LLAO, H3DLAO, H2CLO, PEU-3DLAO and PEU-3scLAO/2CLOs (100/0, 75/25, 50/50, 25/75 and 0/100).</p>
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<p>Stress-strain curves of PEU-3scLAO/2CLOs (100/0, 75/25, 50/50, 25/75 and 0/100).</p>
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<p>Synthesis route of PEU-3scLAO/2CLOs.</p>
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8626 KiB  
Article
Microscale Simulation on Mechanical Properties of Al/PTFE Composite Based on Real Microstructures
by Chao Ge, Yongxiang Dong and Wubuliaisan Maimaitituersun
Materials 2016, 9(7), 590; https://doi.org/10.3390/ma9070590 - 19 Jul 2016
Cited by 48 | Viewed by 7465
Abstract
A novel numerical method at the microscale for studying the mechanical behavior of an aluminum-particle-reinforced polytetrafluoroethylene (Al/PTFE) composite is proposed and validated experimentally in this paper. Two types of 2D representative volume elements (RVEs), real microstructure-based and simulated microstructures, are established by following [...] Read more.
A novel numerical method at the microscale for studying the mechanical behavior of an aluminum-particle-reinforced polytetrafluoroethylene (Al/PTFE) composite is proposed and validated experimentally in this paper. Two types of 2D representative volume elements (RVEs), real microstructure-based and simulated microstructures, are established by following a series of image processing procedures and on a statistical basis considering the geometry and the distribution of particles and microvoids, respectively. Moreover, 3D finite element modelling based on the same statistical information as the 2D simulated microstructure models is conducted to show the efficiency and effectiveness of the 2D models. The results of all simulations and experiments indicate that real microstructure-based models and simulated microstructure models are efficient methods to predict elastic and plastic constants of particle-reinforced composites. Full article
(This article belongs to the Section Advanced Materials Characterization)
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<p>(<b>a</b>) Prepared Al/PTFE (polytetrafluoroethylene) samples and (<b>b</b>) true stress–strain curves of samples under quasi-static compression.</p>
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<p>Distribution of aluminum particle diameters.</p>
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<p>Distribution and geometry of microvoids extracted from SEM images. (<b>a</b>) From 1-R; and (<b>b</b>) from 2-R microstructure in <a href="#materials-09-00590-t001" class="html-table">Table 1</a>.</p>
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<p>(<b>a</b>) Circularity <span class="html-italic">C</span>; and (<b>b</b>) shape factor <span class="html-italic">S</span> of the microvoids extracted from the microstructures.</p>
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<p>Equivalent diameter distribution of microvoids.</p>
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<p>Flowchart of the reproduction process of the simulated microstructure of Al/PTFE.</p>
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<p>Deformation and contour of von Mises stress and plastic strain: (<b>a</b>) von Mises stress distribution of 4-R model; (<b>b</b>) von Mises stress distribution of 4-S model; (<b>c</b>) deformation of microvoid over time; (<b>d</b>) plastic strain distribution of 4-S model. Red circles indicate maximum shear stress points, and the red rectangle indicates the positions of microvoids in (<b>c</b>); red elliptical circle indicates the 45° shear bands in (<b>d</b>).</p>
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<p>Comparison between simulated stress–strain curves and experimental results.</p>
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<p>Contour plot at the final moment and stress–strain curves: (<b>a</b>) contour plot of matrix; (<b>b</b>) contour plot of particles; (<b>c</b>) comparison between stress–strain curves of 3D models and experimental results.</p>
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3153 KiB  
Article
In Situ Thermal Generation of Silver Nanoparticles in 3D Printed Polymeric Structures
by Erika Fantino, Annalisa Chiappone, Flaviana Calignano, Marco Fontana, Fabrizio Pirri and Ignazio Roppolo
Materials 2016, 9(7), 589; https://doi.org/10.3390/ma9070589 - 19 Jul 2016
Cited by 80 | Viewed by 10467
Abstract
Polymer nanocomposites have always attracted the interest of researchers and industry because of their potential combination of properties from both the nanofillers and the hosting matrix. Gathering nanomaterials and 3D printing could offer clear advantages and numerous new opportunities in several application fields. [...] Read more.
Polymer nanocomposites have always attracted the interest of researchers and industry because of their potential combination of properties from both the nanofillers and the hosting matrix. Gathering nanomaterials and 3D printing could offer clear advantages and numerous new opportunities in several application fields. Embedding nanofillers in a polymeric matrix could improve the final material properties but usually the printing process gets more difficult. Considering this drawback, in this paper we propose a method to obtain polymer nanocomposites by in situ generation of nanoparticles after the printing process. 3D structures were fabricated through a Digital Light Processing (DLP) system by disolving metal salts in the starting liquid formulation. The 3D fabrication is followed by a thermal treatment in order to induce in situ generation of metal nanoparticles (NPs) in the polymer matrix. Comprehensive studies were systematically performed on the thermo-mechanical characteristics, morphology and electrical properties of the 3D printed nanocomposites. Full article
(This article belongs to the Special Issue Materials for Photolithography and 3D Printing)
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<p>Sketch of Digital Light Processing (DLP) setup that projects dynamic digital masks on the photocurable formulation featuring the formation of the polyethylene glycol diacrylate structure. Subsequent Thermal treatment, with the formation of the silver nanoparticles by reduction of the metal precursors.</p>
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<p>3D objects produced by DLP technique from the formulation containing polyethylene glycol diacrylate (PEGDA) and 15 phr of silver nitrate. (<b>a</b>) Honeycomb structure as printed; (<b>b</b>,<b>c</b>) samples after the thermal treatments; the metallic aspect induced by the presence of the silver nanoparticles is clearly visible.</p>
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<p>(<b>a</b>) Isothermal treatments performed in air at different temperature (100 °C, 150 °C and 200 °C); (<b>b</b>) thermogravimetric analysis (TGA) plot of the sample PEGDA_15 phr AgNO<sub>3</sub> heated in nitrogen at a rate of 10 °C/min.</p>
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<p>UV-Vis plots of samples treated at (<b>a</b>) 100 °C; (<b>b</b>) 150 °C; (<b>c</b>) 200 °C in air and (<b>d</b>) 200 °C in vacuum obtained after different heating times.</p>
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<p>(<b>a</b>) Cross section of a sample treated 1 h at 150 °C in air; (<b>b</b>) Cross section of a sample treated 1 h at 150 °C in vacuum; (<b>c</b>) Cross section of the core of a sample treated 1 h at 150 °C in vacuum.</p>
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<p>(<b>a</b>) Cross section of a sample treated 1 h at 150 °C in air; (<b>b</b>) Cross section of a sample treated 1 h at 150 °C in vacuum; (<b>c</b>) Cross section of the core of a sample treated 1 h at 150 °C in vacuum.</p>
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<p>(<b>a</b>) Relationship between resistance and heating temperatures measured on flat printed specimens; (<b>b</b>) Conductivity and resistance values measured on flat samples treated at different temperatures for different times.</p>
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<p>I–V plot obtained by contating an honeycomb structure treated at 200 °C in vacuum. Inset: the current flowing trough the structure was sufficient to achieve the illumination of a led.</p>
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5291 KiB  
Article
Novel Mg-Doped SrMoO3 Perovskites Designed as Anode Materials for Solid Oxide Fuel Cells
by Vanessa Cascos, José Antonio Alonso and María Teresa Fernández-Díaz
Materials 2016, 9(7), 588; https://doi.org/10.3390/ma9070588 - 19 Jul 2016
Cited by 18 | Viewed by 6336
Abstract
SrMo1−xMxO3−δ (M = Fe and Cr, x = 0.1 and 0.2) oxides have been recently described as excellent anode materials for solid oxide fuel cells at intermediate temperatures (IT-SOFC) with LSGM as the electrolyte. In this work, we [...] Read more.
SrMo1−xMxO3−δ (M = Fe and Cr, x = 0.1 and 0.2) oxides have been recently described as excellent anode materials for solid oxide fuel cells at intermediate temperatures (IT-SOFC) with LSGM as the electrolyte. In this work, we have improved their properties by doping with aliovalent Mg ions at the B-site of the parent SrMoO3 perovskite. SrMo1−xMgxO3−δ (x = 0.1, 0.2) oxides have been prepared, characterized and tested as anode materials in single solid-oxide fuel cells, yielding output powers near 900 mW/cm−2 at 850 °C using pure H2 as fuel. We have studied its crystal structure with an “in situ” neutron power diffraction (NPD) experiment at temperatures as high as 800 °C, emulating the working conditions of an SOFC. Adequately high oxygen deficiencies, observed by NPD, together with elevated disk-shaped anisotropic displacement factors suggest a high ionic conductivity at the working temperatures. Furthermore, thermal expansion measurements, chemical compatibility with the LSGM electrolyte, electronic conductivity and reversibility upon cycling in oxidizing-reducing atmospheres have been carried out to find out the correlation between the excellent performance as an anode and the structural features. Full article
(This article belongs to the Special Issue Recent Advances in Materials for Solid Oxide Cells)
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<p>XRD patterns with CuK<sub>α</sub> radiation for SrMoO<sub>3</sub> and SrMo<sub>1</sub><sub>−</sub><sub>x</sub>Mg<sub>x</sub>O<sub>3−δ</sub> (x = 0.1 and 0.2), indexed in a simple cubic perovskite unit cell with a<sub>0</sub> ≈ 3.95 Å.</p>
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<p>Observed (crosses), calculated (full line) and difference (at the bottom) NPD profiles for SrMo<sub>0.9</sub>Mg<sub>0.1</sub>O<sub>3</sub><sub>−δ</sub> and SrMo<sub>0.8</sub>Mg<sub>0.2</sub>O<sub>3</sub><sub>−δ</sub> at 25 °C in air, refined in the cubic <span class="html-italic">Pm-3m</span> space group. The vertical markers correspond to the allowed Bragg reflections.</p>
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<p>Thermal evolution of the NPD patterns for SrMo<sub>0.9</sub>Mg<sub>0.1</sub>O<sub>3−δ</sub> between RT and 800 °C.</p>
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<p>Observed (crosses), calculated (full line) and difference (at the bottom) NPD profiles for SrMo<sub>0.9</sub>Mg<sub>0.1</sub>O<sub>3</sub><sub>−δ</sub> at (<b>a</b>) 400 and (<b>b</b>) 800 °C in vacuum (PO<sub>2</sub> = 10<sup>−</sup><sup>6</sup> Torr), refined in the cubic <span class="html-italic">Pm-3m</span> space group. The vertical markers correspond to the allowed Bragg reflections.</p>
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<p>Thermal variation of (<b>a</b>) the unit-cell parameter and (<b>b</b>) the equivalent isotropic displacement factor for O atoms (left axis) and the oxygen occupancy factor (right axis), from in situ NPD data.</p>
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<p>View of the crystal structure of the SrMo<sub>1−x</sub>Mg<sub>x</sub>O<sub>3−δ</sub> oxides, defined in a simple-cubic, primitive unit cell, showing the evolution of the thermal ellipsoids for oxygen atoms between (<b>a</b>) 200 °C and (<b>b</b>) 800 °C.</p>
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<p>Thermal analysis in O<sub>2</sub> flow (TG curve) of SrMo<sub>0.9</sub>Mg<sub>0.1</sub>O<sub>3</sub><sub>−δ</sub> and SrMo<sub>0.8</sub>Mg<sub>0.2</sub>O<sub>3</sub><sub>−δ</sub> perovskites, showing an oxidation step to a scheelite phase.</p>
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<p>(<b>a</b>) Rietveld plot after the structural refinement from XRD data of the oxidation product for SrMo<sub>0.9</sub>Mg<sub>0.1</sub>O<sub>3.67</sub> scheelite; (<b>b</b>) view of the scheelite crystal structure.</p>
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<p>Thermal expansion determined by dilatometry of the SrMo<sub>1</sub><sub>−</sub><sub>x</sub>Mg<sub>x</sub>O<sub>3−δ</sub> and SrMo<sub>1</sub><sub>−</sub><sub>x</sub>Mg<sub>x</sub>O<sub>4</sub><sub>−δ</sub> series.</p>
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<p>Dc-conductivity as a function of temperature for SrMo<sub>1</sub><sub>−</sub><sub>x</sub>Mg<sub>x</sub>O<sub>3</sub><sub>−δ</sub> (x = 0.1 and 0.2).</p>
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<p>Rietveld-refined XRD profiles of a mixture of LSGM and SrMo<sub>0.9</sub>Mg<sub>0.1</sub>O<sub>3</sub><sub>−δ</sub> after a thermal treatment at 900 °C in H<sub>2</sub>(5%)/N<sub>2</sub>, showing no reaction products between both phases other than the initial reactants. The first and second series of Bragg positions correspond to LSGM and SrMo<sub>0.9</sub>Mg<sub>0.1</sub>O<sub>3</sub><sub>−δ</sub>, respectively.</p>
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<p>Cell voltage (left axis) and power density (right axis) as a function of the current density for the test cell with the configuration SMMO (x = 0.1)/LDC/LSGM/SCFO in pure H<sub>2</sub> measured at T = 800 and 850 °C.</p>
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<p>Cell voltage (left axis) and power density (right axis) as a function of the current density for the test cell with the configuration SMMO (x = 0.2)/lanthanum-dope ceria (LDC)/LSGM/SCFO in pure H<sub>2</sub> measured at T = 800 and 850 °C. The inset shows a view of the cathodic side of the single cell.</p>
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4304 KiB  
Article
Effect of Transition Metal Substitution on the Structure and Properties of a Clathrate-Like Compound Eu7Cu44As23
by Igor V. Plokhikh, Dmitri O. Charkin, Valeriy Yu. Verchenko, Ivan A. Ignatyev, Sergey M. Kazakov, Alexey V. Sobolev, Igor A. Presniakov, Alexander A. Tsirlin and Andrei V. Shevelkov
Materials 2016, 9(7), 587; https://doi.org/10.3390/ma9070587 - 19 Jul 2016
Cited by 2 | Viewed by 5113
Abstract
A series of substitutional solid solutions—Eu7Cu44−xTxAs23 (T = Fe, Co, Ni)—based on a recently discovered clathrate-like compound (Eu7Cu44As23) were synthesized from the elements at 800 °C. Almost up to [...] Read more.
A series of substitutional solid solutions—Eu7Cu44−xTxAs23 (T = Fe, Co, Ni)—based on a recently discovered clathrate-like compound (Eu7Cu44As23) were synthesized from the elements at 800 °C. Almost up to 50% of Cu can be substituted by Ni, resulting in a linear decrease of the cubic unit cell parameter from a = 16.6707(1) Å for the ternary compound to a = 16.3719(1) Å for the sample with the nominal composition Eu7Cu24Ni20As23. In contrast, Co and Fe can only substitute less than 20% of Cu. Crystal structures of six samples of different composition were refined from powder diffraction data. Despite very small differences in scattering powers of Cu, Ni, Co, and Fe, we were able to propose a reasonable model of dopant distribution over copper sites based on the trends in interatomic distances as well as on Mössbauer spectra for the iron-substituted compound Eu7Cu36Fe8As23. Ni doping increases the Curie temperature to 25 K with respect to the parent compound, which is ferromagnetically ordered below 17.5 K, whereas Fe doping suppresses the ferromagnetic ordering in the Eu sublattice. Full article
(This article belongs to the Special Issue Inorganic Clathrate Materials)
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<p>Projection of the Eu<sub>7</sub>Cu<sub>44</sub>As<sub>23</sub> crystal structure onto the (001) plane.</p>
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<p>Cubic unit cell parameters vs. <span class="html-italic">x</span> in solid solutions Eu<sub>7</sub>Cu<sub>44−<span class="html-italic">x</span></sub>Ni<span class="html-italic"><sub>x</sub></span>As<sub>23</sub>. Markers cover standard deviations.</p>
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<p>(<b>a</b>–<b>d</b>) Coordination polyhedra of Eu1, Cu1, Cu2, and Cu3, respectively, in the crystal structure of Eu<sub>7</sub>Cu<sub>44</sub>As<sub>23</sub>.</p>
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<p><sup>57</sup>Fe Mössbauer spectrum of Eu<sub>7</sub>Cu<sub>36</sub>Fe<sub>8</sub>As<sub>23</sub> recorder at 15 K.</p>
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<p>The (<b>a</b>) Cu/Ni–As; and (<b>b</b>) Cu/Ni–Cu/Ni distances in the structure of Eu<sub>7</sub>Cu<sub>44−<span class="html-italic">x</span></sub>Ni<span class="html-italic"><sub>x</sub></span>As<sub>23</sub> for different <span class="html-italic">x</span>. Cu/Ni denotes mixed sites of Cu and Ni. The standard deviations are below the sizes of experimental datapoints. The lines are drawn to guide the eye.</p>
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<p>Magnetic susceptibility vs. temperature for (<b>a</b>) Eu<sub>7</sub>Cu<sub>36</sub>Fe<sub>8</sub>As<sub>23</sub> and (<b>b</b>) Eu<sub>7</sub>Cu<sub>42</sub>Ni<sub>2</sub>As<sub>2</sub>; inverse magnetic susceptibility vs. temperature for (<b>c</b>) Eu<sub>7</sub>Cu<sub>36</sub>Fe<sub>8</sub>As<sub>23</sub> and (<b>d</b>) Eu<sub>7</sub>Cu<sub>42</sub>Ni<sub>2</sub>As<sub>2</sub>; (<b>e</b>) magnetization vs. field for Eu<sub>7</sub>Cu<sub>36</sub>Fe<sub>8</sub>As<sub>23</sub>.</p>
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<p>The Rietveld refinement plot for Eu<sub>7</sub>Cu<sub>36</sub>Ni<sub>8</sub>As<sub>23</sub>. Experimental profile, green; peak positions, black; differential profile, red.</p>
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1702 KiB  
Article
Solvent-Induced Polymorphism of Iron(II) Spin Crossover Complexes
by Ivan Šalitroš, Olaf Fuhr and Mario Ruben
Materials 2016, 9(7), 585; https://doi.org/10.3390/ma9070585 - 19 Jul 2016
Cited by 22 | Viewed by 5905
Abstract
Two new mononuclear iron(II) compounds (1) and (2) of the general formula [Fe(L)2](BF4)2·nCH3CN (L = 4-(2-bromoethyn-1-yl)-2,6-bis(pyrazol-1-yl)pyridine, n = 1 for (1) and n = 2 for [...] Read more.
Two new mononuclear iron(II) compounds (1) and (2) of the general formula [Fe(L)2](BF4)2·nCH3CN (L = 4-(2-bromoethyn-1-yl)-2,6-bis(pyrazol-1-yl)pyridine, n = 1 for (1) and n = 2 for compound (2)), were synthesized. The room temperature crystallization afforded concomitant formation of two different solvent analogues: compound (1) exhibiting triclinic P-1 and compound (2) monoclinic C2/c symmetry. Single-crystal X-ray studies confirmed the presence of the LS (low-spin) state for both compounds at 180 K and of the HS (high-spin) state for compound (2) at 293 K, in full agreement with the magnetic investigations for both solvent polymorphs. Compound (1) exhibits spin transition above 293 K followed by subsequent solvent liberation, while the spin transition of (2) takes already place at 237 K. After complete solvent removal from the crystal lattice, compound (1d) (the desolvated polymorph derived from (1)) exhibits spin transition centered at 342 K accompanied by a thermal hysteresis loop, while the analogous compound (2d) (the desolvated derivate of compound (2)) remains blocked in the HS state over all the investigated temperature range. Full article
(This article belongs to the Special Issue Advances in Molecular Magnets and related Phenomena)
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<p>Thermogram of mixture sample of compounds (<b>1</b>) and (<b>2</b>).</p>
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<p>Asymmetric unit of solvated analogues (<b>a</b>) (<b>1</b>) and (<b>b</b>) (<b>2</b>).</p>
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<p>(Color on-line) Representation of the thermochromism of compound <b>2</b>.</p>
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<p>(<b>a</b>) Temperature-dependent magnetic properties of solvated (red circles) and desolvated (blue circles) mixture of compounds (<b>1</b>) [Fe(<b>L</b>)<sub>2</sub>](BF<sub>4</sub>)<sub>2</sub>·CH<sub>3</sub>CN and (<b>2</b>) [Fe(<b>L</b>)<sub>2</sub>](BF<sub>4</sub>)<sub>2</sub>·2CH<sub>3</sub>CN; (<b>b</b>) Field-dependent mole magnetization of desolvated sample at 1.9 K (mixture of (<b>1d</b>) and (<b>2d</b>)).</p>
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3885 KiB  
Article
Superplasticizer Addition to Carbon Fly Ash Geopolymers Activated at Room Temperature
by Lorenza Carabba, Stefania Manzi and Maria Chiara Bignozzi
Materials 2016, 9(7), 586; https://doi.org/10.3390/ma9070586 - 18 Jul 2016
Cited by 31 | Viewed by 8766
Abstract
Present concerns about global warming due to the greenhouse emissions in the atmosphere have pushed the cement industry to research alternatives to ordinary Portland cement (OPC). Geopolymer binder may constitute a possible breakthrough in the development of sustainable materials: understanding the effectiveness and [...] Read more.
Present concerns about global warming due to the greenhouse emissions in the atmosphere have pushed the cement industry to research alternatives to ordinary Portland cement (OPC). Geopolymer binder may constitute a possible breakthrough in the development of sustainable materials: understanding the effectiveness and the influences of superplasticizers on geopolymer systems is one of the essential requirements for its large-scale implementation. This study aims to investigate the possibility of using commercially available chemical admixtures designed for OPC concrete, to improve fresh properties of fly ash-based geopolymers and mortars. A special emphasis is laid upon evaluating their influence on mechanical and microstructural characteristics of the hardened material realized under room-temperature curing conditions. Results indicate that the addition of a polycarboxylic ether-based superplasticizer, in the amount of 1.0 wt. % by mass of fly ash, promotes an improvement in workability without compromising the final strength of the hardened material. Moreover, the addition of the polycarboxylic ether- and acrylic-based superplasticizers induces a refinement in the pore structure of hardened mortar leading to a longer water saturation time. Full article
(This article belongs to the Special Issue Advances in Geopolymers and Alkali-Activated Materials)
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<p>Workability of geopolymer expressed as relative spread (increase or decrease in %) of the geopolymer mixtures immediately (<b>a</b>) after mixing; (<b>b</b>) after 5 min; (<b>c</b>) 15 min; and (<b>d</b>) 30 min.</p>
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<p>Consistency of geopolymer mortars as function of time (average of four measurements). Standard deviation (δ) is not reported in the plot for clarity’s sake however it is in the range of ±5.</p>
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<p>FT-IR spectra for (<b>a</b>) ACRa; and (<b>b</b>) PCE superplasticizers dried in a vacuum dryer and after mixing with an 8 M NaOH solution.</p>
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<p>Mechanical properties of hardened geopolymer mortars after 28 days of curing at room temperature (values are reported as average of three measurements).</p>
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<p>Optical images of geopolymer mortars after 28 days of curing: (<b>a</b>) PCE_1; (<b>b</b>) ACRa_06; and (<b>c</b>) GP. (Magnification 8×).</p>
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<p>Pore distribution obtained via image analysis of two sections of hardened mortar (investigated area = 145 mm<sup>2</sup>).</p>
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<p>(<b>a</b>) Pore size distributions curves of the investigated geopolymer mortar samples; (<b>b</b>) content % of pores arranged per ranges of pore radius (<span class="html-italic">r</span>) within the range of 0.1 ≤ <span class="html-italic">r</span> &lt; 1 μm.</p>
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<p>(<b>a</b>) Pore size distributions curves of the investigated geopolymer mortar samples; (<b>b</b>) content % of pores arranged per ranges of pore radius (<span class="html-italic">r</span>) within the range of 0.1 ≤ <span class="html-italic">r</span> &lt; 1 μm.</p>
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<p>Capillary water absorption test results for GP, PCE_1, and ACRa_06 samples. The time of saturation for each sample is indicated with a vertical line.</p>
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1196 KiB  
Communication
Anomalous Halo Formation in an Arc-Melted ScNi-Sc2Ni Off-Eutectic Binary Alloy
by Kai Wang, Ming Wei and Lijun Zhang
Materials 2016, 9(7), 584; https://doi.org/10.3390/ma9070584 - 18 Jul 2016
Cited by 7 | Viewed by 4512
Abstract
Diverse non-equilibrium eutectic structures have attracted numerous experimental and theoretical studies. One special type is the formation of a halo of one phase around a primary dendrite of another phase. In our experiments, it was occasionally observed that ScNi halos grow as dendritic [...] Read more.
Diverse non-equilibrium eutectic structures have attracted numerous experimental and theoretical studies. One special type is the formation of a halo of one phase around a primary dendrite of another phase. In our experiments, it was occasionally observed that ScNi halos grow as dendritic morphology around the primary Sc 2 Ni dendrites in an arc-melted ScNi-Sc 2 Ni off-eutectic binary alloy. The formation of this anomalous halo structure was then well reproduced by employing quantitative phase-field simulations. Based on the phase-field simulation, It was found that (i) the large undercooling and growth velocity of the ScNi phase during solidification causes the formation of halos; and (ii) the released latent heat induces the recalescence phenomenon, and changes the solidification sequence largely, resulting in the anomalous halo structure in the Sc-34 at % Ni alloy. Full article
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<p>(<b>a</b>) Experimental microstructure of as-cast Sc-34 at % Ni binary alloy; (<b>b</b>) Enlarged view of the rectangular section in (<b>a</b>).</p>
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<p>(<b>a</b>) Linearized phase diagram of Sc-Ni binary alloy from 52.27 at % Sc to 72 at % Sc constructed according to the recent thermodynamic assessment by Cao et al. [<a href="#B25-materials-09-00584" class="html-bibr">25</a>]; (<b>b</b>) Temporal temperature curve (solid-line) and the volume fraction profile (dash-line) during simulation; (<b>c</b>) Ni concentration evolution near the Sc<math display="inline"> <semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics> </math>Ni grain.</p>
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<p>Phase-field simulated microstructure of the Sc-34 at % Ni binary alloy during solidification at different time slides: (<b>a</b>) 2.16 s; (<b>b</b>) 2.17 s; (<b>c</b>) 2.19 s; (<b>d</b>) 2.25 s; (<b>e</b>) 2.46 s; (<b>f</b>) 2.85 s.</p>
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2107 KiB  
Article
UV-Assisted 3D Printing of Glass and Carbon Fiber-Reinforced Dual-Cure Polymer Composites
by Marta Invernizzi, Gabriele Natale, Marinella Levi, Stefano Turri and Gianmarco Griffini
Materials 2016, 9(7), 583; https://doi.org/10.3390/ma9070583 - 16 Jul 2016
Cited by 133 | Viewed by 18888
Abstract
Glass (GFR) and carbon fiber-reinforced (CFR) dual-cure polymer composites fabricated by UV-assisted three-dimensional (UV-3D) printing are presented. The resin material combines an acrylic-based photocurable resin with a low temperature (140 °C) thermally-curable resin system based on bisphenol A diglycidyl ether as base component, [...] Read more.
Glass (GFR) and carbon fiber-reinforced (CFR) dual-cure polymer composites fabricated by UV-assisted three-dimensional (UV-3D) printing are presented. The resin material combines an acrylic-based photocurable resin with a low temperature (140 °C) thermally-curable resin system based on bisphenol A diglycidyl ether as base component, an aliphatic anhydride (hexahydro-4-methylphthalic anhydride) as hardener and (2,4,6,-tris(dimethylaminomethyl)phenol) as catalyst. A thorough rheological characterization of these formulations allowed us to define their 3D printability window. UV-3D printed macrostructures were successfully demonstrated, giving a clear indication of their potential use in real-life structural applications. Differential scanning calorimetry and dynamic mechanical analysis highlighted the good thermal stability and mechanical properties of the printed parts. In addition, uniaxial tensile tests were used to assess the fiber reinforcing effect on the UV-3D printed objects. Finally, an initial study was conducted on the use of a sizing treatment on carbon fibers to improve the fiber/matrix interfacial adhesion, giving preliminary indications on the potential of this approach to improve the mechanical properties of the 3D printed CFR components. Full article
(This article belongs to the Special Issue Materials for Photolithography and 3D Printing)
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<p>Viscosity curves of B33 formulations (dual-cure blend containing 33 wt. % of photocurable acrylic component) at increasing SiO<sub>2</sub> content.</p>
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<p>Viscosity curves of SiO<sub>2</sub>-containing B33, B50 and carbon fiber-reinforced (CFR) (B50C5) composite formulations. For comparison, CFR and glass fiber-reinforced (GFR) composite formulations without the addition of SiO<sub>2</sub> are also presented (B50C5-noSiO<sub>2</sub> and B33G5-noSiO<sub>2</sub>, respectively).</p>
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<p>Representative stress–strain curves of UV-3D printed blend (B50) and composites incorporating untreated (B50C5) and sized (B50C5-S) carbon fibers.</p>
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<p>SEM micrographs (2500× magnification) of (<b>a</b>) virgin untreated; and (<b>b</b>) sized carbon fibers; fracture surface of tensile CFR polymer composites incorporating (<b>c</b>) virgin untreated; and (<b>d</b>) sized carbon fibers.</p>
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<p>Axonometric projection of the airfoil (<b>a</b>) and the propeller (<b>b</b>) 3D models used to demonstrate the printability of the GFR and CFR composite formulations developed in this work. UV-3D printed reproduction of the airfoil (<b>c</b>–<b>f</b>) and the propeller (<b>g</b>–<b>j</b>) 3D models based on the GFR (<b>c</b>,<b>d</b>,<b>g</b>,<b>h</b>) and CFR (<b>e</b>,<b>f</b>,<b>i</b>,<b>j</b>) polymer composite formulations developed in this work.</p>
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6715 KiB  
Article
Adsorption of Heavy Metals by Graphene Oxide/Cellulose Hydrogel Prepared from NaOH/Urea Aqueous Solution
by Xiong Chen, Sukun Zhou, Liming Zhang, Tingting You and Feng Xu
Materials 2016, 9(7), 582; https://doi.org/10.3390/ma9070582 - 16 Jul 2016
Cited by 127 | Viewed by 12009
Abstract
By taking advantage of cellulose, graphene oxide (GO), and the process for crosslinking using epichlorohydrin (ECH), we propose a simple and novel method to prepare GO/cellulose hydrogel with good potential to adsorb metal ions. GO nanosheets containing carboxyl and hydroxyl groups were introduced [...] Read more.
By taking advantage of cellulose, graphene oxide (GO), and the process for crosslinking using epichlorohydrin (ECH), we propose a simple and novel method to prepare GO/cellulose hydrogel with good potential to adsorb metal ions. GO nanosheets containing carboxyl and hydroxyl groups were introduced into the surface of the cellulose hydrogel with retention of the gel structure and its nanoporous property. Due to the introduction of GO, the GO/cellulose composite hydrogels exhibited good compressive strength. Adsorption capacity of Cu2+ significantly increases with an increase in the GO/cellulose ratio and GO/cellulose hydrogel showed high adsorption rates. The calculated adsorption capacities at equilibrium ( q e cal ) for GO/cellulose hydrogel (GO:cellulose = 20:100 in weight) was up to 94.34 mg·g−1, which was much higher than that of the pristine cellulose hydrogels. Furthermore, GO/cellulose hydrogel exhibited high efficient regeneration and metal ion recovery, and high adsorption capacity for Zn2+, Fe3+, and Pb2+. Full article
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<p>FTIR spectra of GO, GO/cellulose hydrogel, cellulose hydrogel, and Cu(II)-loaded GO/cellulose hydrogel.</p>
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<p>XRD patterns of GO, cellulose hydrogel, and GO(20)/cellulose(100) hydrogel.</p>
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<p>Proposed mechanism for cross-linking reaction of ECH with GO and cellulose.</p>
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<p>SEM images of GO(<span class="html-italic">x</span>)/cellulose(100) dry hydrogels with <span class="html-italic">x</span> = 2.5, 5, 10, 20, and 30, respectively. Cross-section images were taken inside the gel. Surface images were taken on the surface of the hydrogels.</p>
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<p>Point of zero charge of GO(20)/cellulose(100) hydrogel.</p>
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<p>Effects of GO to cellulose ratios on Cu<sup>2+</sup> ion adsorption on the hydrogel. The error bars represent standard deviations based on three measurements.</p>
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<p>Effect of pH on the adsorption capacity. The error bars represent standard deviations based on three measurements.</p>
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<p>Effects of adsorbent dose on Cu<sup>2+</sup> adsorption by the GO(20)/cellulose(100) hydrogel. The error bars represent standard deviations based on three measurements.</p>
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<p>Adsorption of Cu<sup>2+</sup> on the GO(20)/cellulose(100) hydrogel as a function of contact time. The error bars represent standard deviations based on three measurements.</p>
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<p>Adsorption of Cu<sup>2+</sup> on the GO(20)/cellulose(100) hydrogel as a function of Cu<sup>2+</sup> concentration. The error bars represent standard deviations based on three measurements.</p>
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<p>Effect of recycling bioadsorbents on Cu<sup>2+</sup> adsorption (initial concentration 200 mg·L<sup>−1</sup>; initial pH of solution 5.3, temperature, 298 K; contact time, 120 min). The error bars represent standard deviations based on three measurements.</p>
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<p>Adsorption amount of various metals on GO(20)/cellulose(100) hydrogels. The error bars represent standard deviations based on three measurements.</p>
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5971 KiB  
Article
Mechanical Behavior of Dowel-Type Joints Made of Wood Scrimber Composite
by Minjuan He, Duo Tao, Zheng Li and Maolin Li
Materials 2016, 9(7), 581; https://doi.org/10.3390/ma9070581 - 15 Jul 2016
Cited by 16 | Viewed by 8551
Abstract
As a renewable building material with low embodied energy characteristics, wood has gained more and more attention in the green and sustainable building industry. In terms of material resource and physical properties, scrimber composite not only makes full use of fast-growing wood species, [...] Read more.
As a renewable building material with low embodied energy characteristics, wood has gained more and more attention in the green and sustainable building industry. In terms of material resource and physical properties, scrimber composite not only makes full use of fast-growing wood species, but also has better mechanical performance and less inherent variability than natural wood material. In this study, the mechanical behavior of bolted beam-to-column joints built with a kind of scrimber composite was investigated both experimentally and numerically. Two groups of specimens were tested under monotonic and low frequency cyclic loading protocols. The experimental results showed that the bolted joints built with scrimber composite performed well in initial stiffness, ductility, and energy dissipation. A three-dimensional (3D) non-linear finite element model (FEM) for the bolted beam-to-column joints was then developed and validated by experimental results. The validated model was further used to investigate the failure mechanism of the bolted joints through stress analysis. This study can contribute to the application of the proposed scrimber composite in structural engineering, and the developed FEM can serve as a useful tool to evaluate the mechanical behavior of such bolted beam-to-column joints with different configurations in future research. Full article
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<p>Production and cross section of the scrimber composite.</p>
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<p>Specimen configuration (all dimensions are in mm).</p>
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<p>Test design: (<b>a</b>) test layout (all dimensions are in mm); (<b>b</b>) test set-up in the laboratory.</p>
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<p>Calculation of relative rotation.</p>
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<p>Consortium of Universities for Research in Earthquake Engineering (CUREE) protocol for the low frequency cyclic tests.</p>
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<p>Local crushing between beam and column.</p>
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<p>Failure modes: (<b>a</b>) external observation from monotonic test; (<b>b</b>) internal observation from monotonic test; (<b>c</b>) external observation from cyclic test; (<b>d</b>) internal observation from cyclic test.</p>
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<p>Moment-rotation (<span class="html-italic">M-θ</span>) curves and the average <span class="html-italic">M-θ</span> curve of monotonic tests.</p>
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<p>Analyses of cyclic tests: (<b>a</b>) typical hysteresis loop; (<b>b</b>) backbone curve.</p>
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<p>Comparison of average stiffness degradation between scrimber joint and glulam.</p>
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<p>Calculation of equivalent viscous damping ratio (EVDR): (<b>a</b>) mathematical meaning of <span class="html-italic">E<sub>d</sub></span> and <span class="html-italic">E<sub>p</sub></span>; (<b>b</b>) comparison between scrimber joint and glulam joint.</p>
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<p>Stress-strain properties of scrimber composite: (<b>a</b>) parallel-to-grain; (<b>b</b>) perpendicular-to-grain.</p>
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<p>The 3D finite element model (FEM).</p>
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<p>Numerical failure modes: (<b>a</b>) cracking of beam component; (<b>b</b>) yielding of bolts (all numbers in the figure are in MPa).</p>
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<p>Comparison of experimental and numerical <span class="html-italic">M-θ</span> curves.</p>
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<p>Stress distribution when initial splitting appears: (<b>a</b>) perpendicular-to-grain stress; (<b>b</b>) shear stress (all numbers in the figure are in MPa).</p>
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<p>Parametric analyses: (<b>a</b>) various yielding strength of bolts; (<b>b</b>) various strength factor of scrimber composite.</p>
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7966 KiB  
Article
Optimizing and Characterizing Geopolymers from Ternary Blend of Philippine Coal Fly Ash, Coal Bottom Ash and Rice Hull Ash
by Martin Ernesto Kalaw, Alvin Culaba, Hirofumi Hinode, Winarto Kurniawan, Susan Gallardo and Michael Angelo Promentilla
Materials 2016, 9(7), 580; https://doi.org/10.3390/ma9070580 - 15 Jul 2016
Cited by 41 | Viewed by 10905
Abstract
Geopolymers are inorganic polymers formed from the alkaline activation of amorphous alumino-silicate materials resulting in a three-dimensional polymeric network. As a class of materials, it is seen to have the potential of replacing ordinary Portland cement (OPC), which for more than a hundred [...] Read more.
Geopolymers are inorganic polymers formed from the alkaline activation of amorphous alumino-silicate materials resulting in a three-dimensional polymeric network. As a class of materials, it is seen to have the potential of replacing ordinary Portland cement (OPC), which for more than a hundred years has been the binder of choice for structural and building applications. Geopolymers have emerged as a sustainable option vis-à-vis OPC for three reasons: (1) their technical properties are comparable if not better; (2) they can be produced from industrial wastes; and (3) within reasonable constraints, their production requires less energy and emits significantly less CO2. In the Philippines, the use of coal ash, as the alumina- and silica- rich geopolymer precursor, is being considered as one of the options for sustainable management of coal ash generation from coal-fired power plants. However, most geopolymer mixes (and the prevalent blended OPC) use only coal fly ash. The coal bottom ash, having very few applications, remains relegated to dumpsites. Rice hull ash, from biomass-fired plants, is another silica-rich geopolymer precursor material from another significantly produced waste in the country with only minimal utilization. In this study, geopolymer samples were formed from the mixture of coal ash, using both coal fly ash (CFA) and coal bottom ash (CBA), and rice hull ash (RHA). The raw materials used for the geopolymerization process were characterized using X-ray fluorescence spectroscopy (XRF) for elemental and X-ray diffraction (XRD) for mineralogical composition. The raw materials’ thermal stability and loss on ignition (LOI) were determined using thermogravimetric analysis (TGA) and reactivity via dissolution tests and inductively-coupled plasma mass spectrometry (ICP) analysis. The mechanical, thermal and microstructural properties of the geopolymers formed were analyzed using compression tests, Fourier transform infra-red spectroscopy (FTIR), scanning electron microscopy (SEM) and thermogravimetric analysis (TGA). Using a Scheffé-based mixture design, targeting applications with low thermal conductivity, light weight and moderate strength and allowing for a maximum of five percent by mass of rice hull ash in consideration of the waste utilization of all three components, it has been determined that an 85-10-5 by weight ratio of CFA-CBA-RHA activated with 80-20 by mass ratio of 12 M NaOH and sodium silicate (55% H2O, modulus = 3) produced geopolymers with a compressive strength of 18.5 MPa, a volumetric weight of 1660 kg/m3 and a thermal conductivity of 0.457 W/m-°C at 28-day curing when pre-cured at 80 °C for 24 h. For this study, the estimates of embodied energy and CO2 were all below 1.7 MJ/kg and 0.12 kg CO2/kg, respectively. Full article
(This article belongs to the Special Issue Advances in Geopolymers and Alkali-Activated Materials)
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<p>Mix proportions used.</p>
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<p>XRD patterns of the raw materials. C, cristobalite-SiO<sub>2</sub>; Q, quartz-SiO<sub>2</sub>; H, hematite; M, magnetite.</p>
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<p>FTIR spectrograph of the raw materials.</p>
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<p>Thermograph of RHA.</p>
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<p>Thermograph of CFA.</p>
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<p>Thermograph of CBA.</p>
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<p>SEM micrograph of CFA ×1000.</p>
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<p>SEM micrograph of CBA (ground and sieved at 250 µm) ×1000.</p>
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<p>SEM micrograph of RHA ×1000.</p>
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<p>Response surface plots of the compressive strength of the geopolymer specimens and their projections onto the ternary diagram.</p>
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<p>Response surface plots of the thermal conductivity of the geopolymer specimens and their projections onto the ternary diagram.</p>
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<p>Response surface plots of the volumetric weight of the geopolymer specimens and their projections onto the ternary diagram.</p>
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<p>Overlay plots: (<b>a</b>) thermal conductivity &lt;0.43 W/m-°C, compressive strength &gt;11.7 MPa; (<b>b</b>) thermal conductivity &lt;0.46 W/m-°C, compressive strength &gt;11.7 MPa; (<b>c</b>) thermal conductivity &lt;0.46 W/m-°C, compressive strength &gt;10 MPa.</p>
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<p>Overlay plots: (<b>a</b>) thermal conductivity &lt;0.43 W/m-°C, compressive strength &gt;11.7 MPa; (<b>b</b>) thermal conductivity &lt;0.46 W/m-°C, compressive strength &gt;11.7 MPa; (<b>c</b>) thermal conductivity &lt;0.46 W/m-°C, compressive strength &gt;10 MPa.</p>
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<p>Ramp plot for Mix 1 of <a href="#materials-09-00580-t007" class="html-table">Table 7</a>.</p>
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<p>Ramp plot for Mix 2 of <a href="#materials-09-00580-t007" class="html-table">Table 7</a>.</p>
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<p>Ramp plot for Mix 3 of <a href="#materials-09-00580-t007" class="html-table">Table 7</a>.</p>
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<p>Trace plot for volumetric weight of Mix 1.</p>
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<p>Trace plot for thermal conductivity of Mix 1.</p>
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<p>Trace plot for compressive strength of Mix 1.</p>
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<p>Trace plot for volumetric weight of Mix 2.</p>
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<p>Trace plot for thermal conductivity of Mix 2.</p>
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<p>Trace plot for compressive strength of Mix 2.</p>
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<p>Trace plot for volumetric weight of Mix 3.</p>
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<p>Trace plot for thermal conductivity of Mix 3.</p>
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<p>Trace plot for compressive strength of Mix 3.</p>
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<p>Spectrograph comparison of CFA, CBA raw materials and 85-15 CFA-CBA geopolymer.</p>
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<p>Comparison between the spectrographs of the CFA, CBA and RHA raw materials and the 85-10-5 FA-CBA-RHA geopolymer.</p>
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<p>Spectrograph comparison of RHA raw material, 50-50 CFA-RHA geopolymer, and 1/3-1/3-1/3 CFA-CBA-RHA geopolymer.</p>
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<p>SEM micrograph of 95-5 CFA-RHA geopolymer ×1000.</p>
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<p>SEM micrograph of 85-15 CFA-CBA geopolymer ×1000.</p>
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<p>SEM micrograph of 85-10-5 CFA-CBA-RHA geopolymer ×1000.</p>
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<p>Thermograph of the 50-50 CFA-RHA geopolymer.</p>
Full article ">Figure 33
<p>Thermograph of the 50-50 CFA-CBA geopolymer.</p>
Full article ">Figure 34
<p>Compressive strength of the optimum mixes selected vs. 24-h pre-curing temperature.</p>
Full article ">Figure 35
<p>Volumetric weight of the optimum mixes selected vs. 24-h pre-curing temperature.</p>
Full article ">Figure 36
<p>Thermal conductivity of the optimum mixes vs. 24-h pre-curing temperature.</p>
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