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Materials, Volume 6, Issue 3 (March 2013) – 28 articles , Pages 713-1204

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262 KiB  
Article
Factors Affecting the Effectiveness of Inorganic Silicate Sealer Material through Multi-Quality Characteristics
by Si-Yu Zou, Ran Huang, Mao-Chieh Chi and Hui-Mi Hsu
Materials 2013, 6(3), 1191-1204; https://doi.org/10.3390/ma6031191 - 22 Mar 2013
Cited by 16 | Viewed by 4981
Abstract
This study investigates the effectiveness of concrete protection with two inorganic silicate sealer materials (ISSMs). The Taguchi method and grey relational analysis (GRA) have been used to identify the key factors influencing concrete protection provided by the surface treatment. Seven control factors with [...] Read more.
This study investigates the effectiveness of concrete protection with two inorganic silicate sealer materials (ISSMs). The Taguchi method and grey relational analysis (GRA) have been used to identify the key factors influencing concrete protection provided by the surface treatment. Seven control factors with two levels were selected. By using the orthogonal array L12 (27), 12 experiments are chosen and four tests—the compressive strength test, resistivity test, absorption test and permeability test—were performed. Results have shown that the major factors affecting the protection effectiveness of ISSM are the water-binder ratio of mortar substrate, age of substrate for sealer application, addition of pozzolanic material and sealer type. Full article
(This article belongs to the Section Advanced Materials Characterization)
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Figure 1

Figure 1
<p>Inorganic Silicate Sealer Material.</p>
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<p>S/N ratio response graph for compressive strength.</p>
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<p>S/N ratio response graph for Resistivity.</p>
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<p>S/N ratio response graph for water absorption.</p>
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<p>S/N ratio response graph for permeability.</p>
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<p>Grey relational grade responses graph for multi-quality factors.</p>
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6207 KiB  
Review
Polymeric Thin Films for Organic Electronics: Properties and Adaptive Structures
by Sebastiano Cataldo and Bruno Pignataro
Materials 2013, 6(3), 1159-1190; https://doi.org/10.3390/ma6031159 - 22 Mar 2013
Cited by 33 | Viewed by 9728
Abstract
This review deals with the correlation between morphology, structure and performance of organic electronic devices including thin film transistors and solar cells. In particular, we report on solution processed devices going into the role of the 3D supramolecular organization in determining their electronic [...] Read more.
This review deals with the correlation between morphology, structure and performance of organic electronic devices including thin film transistors and solar cells. In particular, we report on solution processed devices going into the role of the 3D supramolecular organization in determining their electronic properties. A selection of case studies from recent literature are reviewed, relying on solution methods for organic thin-film deposition which allow fine control of the supramolecular aggregation of polymers confined at surfaces in nanoscopic layers. A special focus is given to issues exploiting morphological structures stemming from the intrinsic polymeric dynamic adaptation under non-equilibrium conditions. Full article
(This article belongs to the Special Issue Conjugated Polymers 2012)
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Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>(<b>a</b>) Schematic depiction of charge transport in a edge-on packed polymer assembly. Yellow bricks indicate monomers along the polymer backbone. X, Y, Z denote the charge transport directions along the polymer chain, across the alkyl moieties of parallel chains and between face-to-face piled chains, respectively; (<b>b</b>) Schematic depiction of the π-stacking and chain-to-chain packing of polymers. In the inset, the reading-key shows the example of P(NDI2OD-T2) that is discussed below.</p>
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<p>Molecular structures of materials used in organic thin film field-effect transistors (OFETs) reported as examples in this review.</p>
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<p>(<b>a</b>) Scanning tunneling microscope image of chain folding for regioregular poly(3-dodecylthiophene); (<b>b</b>) Calculated model of chain folding (Reprinted with permission from reference [<a href="#B64-materials-06-01159" class="html-bibr">64</a>]. Copyright 2002 Wiley-VCH Verlag GmbH &amp; Co.).</p>
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<p>(<b>a,b</b>) AFM image of P3HT nanofibers across electrodes on SiO<sub>2</sub>/Si substrate; (<b>c</b>) cross section of the dashed line shown in (b). The fibre heights from top to bottom are 5.6, 6.3, 3.9, and 3.3 nm. (Reprinted with permission from Reference [<a href="#B67-materials-06-01159" class="html-bibr">67</a>]. Copyright (2003) by the Wiley-VCH Verlag GmbH &amp; Co.).</p>
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<p>(<b>a</b>) Superficial pressure <span class="html-italic">vs.</span> mean molecular area graph showing the rise in pressure as the polymer self-assembly proceeds toward the edge-on packing. (Reprinted with permission from Reference [<a href="#B69-materials-06-01159" class="html-bibr">69</a>]. Copyright (2012) by the Wiley-VCH Verlag GmbH &amp; Co.); (<b>b,c</b>) Descriptive depictions respectively of a mixed face-on/edge-on structure and of a strictly packed edge-on structure (Reprinted with permission from Reference [<a href="#B70-materials-06-01159" class="html-bibr">70</a>]. Copyright (2006) by the Nature Publishing Group).</p>
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<p>Graphical depiction showing the charge carrier paths available in (<b>a</b>) an edge-on; and in (<b>b</b>) a mixed edge-on/face-on ordered thin-film (tilted phases are missing in this scheme for simplicity). In the inset, the reading key is reported by using again the example of P(NDI2OD-T2).</p>
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<p>AFM image of spin-coated CDT–BTZ–C16 copolymer film showing ring-shaped structures (Reprinted with permission from Reference [<a href="#B78-materials-06-01159" class="html-bibr">78</a>]. Copyright (2012) by Wiley-VCH Verlag GmbH &amp; Co.).</p>
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<p>(<b>a</b>) Graphical depiction of the CDT-BTZ deposition by dip-coating showing the polymer backbones aligned parallel to the dipping direction; (<b>b</b>) AFM image showing the polymeric fibres (red arrow) aligned along the dipping direction (yellow arrow) (Reprinted with permission from reference [<a href="#B78-materials-06-01159" class="html-bibr">78</a>]. Copyright (2012) by Wiley-VCH Verlag GmbH &amp; Co.).</p>
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<p>(<b>a</b>) Schematic representation of the zone-casting deposition method; (<b>b</b>) TEM large-area microgragh of a linear pattern. (Reprinted with permission from Reference [<a href="#B79-materials-06-01159" class="html-bibr">79</a>]. Copyright (2005) Wiley-VCH Verlag GmbH &amp; Co.). (<b>c,d,e</b>) Optical micrographs of microcrystalline columnar patterns of DT-TTF deposited on glass by zone casting at different casting rates: (<b>c</b>) 6 µm/s; (<b>d</b>) 10 µm/s; (<b>e</b>) 16 µm/s. Arrows indicates the casting direction (Reprinted with permission from Reference [<a href="#B80-materials-06-01159" class="html-bibr">80</a>]. Copyright (2008) by Elsevier).</p>
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<p>Schematic depiction of the photovoltaic operation for a bulk heterojunction solar cell. (Reprinted with permission from Reference [<a href="#B107-materials-06-01159" class="html-bibr">107</a>]. Copyright (2008) by Materials Research Society).</p>
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<p>Some of the most used organic semiconductor materials in OSCs. (Reprinted with permission from Reference [<a href="#B110-materials-06-01159" class="html-bibr">110</a>]. Copyright (2010) by American Chemical Society).</p>
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<p>AFM surface morphology of MDMO-PPV/PCBM (1:4 wt%) BHJ thin-film spin coated with different solvents: (<b>a</b>) toluene; (<b>b</b>) chlorobenzene. The cross sections below the images are taken horizontally corresponding with the arrows. (Reprinted with permission from Reference [<a href="#B121-materials-06-01159" class="html-bibr">121</a>]. Copyright (2001) by American Institute of Physics).</p>
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<p>AFM height images of PF10TBT:PCBM BHJs spin-casted from chlorobenzene (see <a href="#materials-06-01159-f011" class="html-fig">Figure 11</a> for molecular structures) containing (<b>a</b>) 20; (<b>b</b>) 50; and (<b>c</b>) 80 wt% of PCBM. The horizontal scale bar is 200 nm; z-scale is 6 nm. (Reprinted with permission from Reference [<a href="#B133-materials-06-01159" class="html-bibr">133</a>]. Copyright (2008) by American Chemical Society).</p>
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<p>AFM topography (<b>a</b>) and phase-lag images; (<b>b,c</b>) of 50:50 wt% P3HT:PDB BHJ thin-film; (<b>d</b>) Size distribution of the phase-separated domains. (Reprinted with permission from Reference [<a href="#B120-materials-06-01159" class="html-bibr">120</a>]. Copyright (2010) by Wiley-VCH Verlag GmbH &amp; Co.).</p>
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<p>(<b>a</b>) AFM image of a solvent-annealed P3HT:PCBM BHJ thin-film. (Reprinted with permission from Reference [<a href="#B60-materials-06-01159" class="html-bibr">60</a>]. Copyright (2007) by Wiley-VCH Verlag GmbH &amp; Co.); (<b>b</b>) 3D electron tomography of P3HT nanofibres in a P3HT/PCBM BHJ displaying a bi-continuous percolating network. In the bottom-left corner, the 3D image is integrated in an artistic view on energy conversion by OSCs (Reprinted with permission from Reference [<a href="#B139-materials-06-01159" class="html-bibr">139</a>]. Copyright (2009) by American Chemical Society).</p>
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<p>Schematic depiction of a roll-to-roll process for the large scale fabrication of OSCs: (<b>a</b>) casting of the D:A blend solution (ITO is indium tin oxide); (<b>b</b>) dynamic layer formation by controlled solvent evaporation, the sketch describes the solution shear flow inducing chain alignment; (<b>c</b>) A picture of the roll-to-roll apparatus (in the inset, the flexible OSCs before contact deposition). (Reprinted with permission from Reference [<a href="#B145-materials-06-01159" class="html-bibr">145</a>]. Copyright (2010) by Wiley-VCH Verlag GmbH &amp; Co.).</p>
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2057 KiB  
Review
Applications of Carbon Nanotubes for Lithium Ion Battery Anodes
by Zhili Xiong, Young Soo Yun and Hyoung-Joon Jin
Materials 2013, 6(3), 1138-1158; https://doi.org/10.3390/ma6031138 - 21 Mar 2013
Cited by 163 | Viewed by 15020
Abstract
Carbon nanotubes (CNTs) have displayed great potential as anode materials for lithium ion batteries (LIBs) due to their unique structural, mechanical, and electrical properties. The measured reversible lithium ion capacities of CNT-based anodes are considerably improved compared to the conventional graphite-based anodes. Additionally, [...] Read more.
Carbon nanotubes (CNTs) have displayed great potential as anode materials for lithium ion batteries (LIBs) due to their unique structural, mechanical, and electrical properties. The measured reversible lithium ion capacities of CNT-based anodes are considerably improved compared to the conventional graphite-based anodes. Additionally, the opened structure and enriched chirality of CNTs can help to improve the capacity and electrical transport in CNT-based LIBs. Therefore, the modification of CNTs and design of CNT structure provide strategies for improving the performance of CNT-based anodes. CNTs could also be assembled into free-standing electrodes without any binder or current collector, which will lead to increased specific energy density for the overall battery design. In this review, we discuss the mechanism of lithium ion intercalation and diffusion in CNTs, and the influence of different structures and morphologies on their performance as anode materials for LIBs. Full article
(This article belongs to the Special Issue Carbon Nanotubes)
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Figure 1

Figure 1
<p>HF/4-31G Optimized structures of nanotubes with 8, 9, and 10-membered ring defects. (Reprinted with permission from [<a href="#B19-materials-06-01138" class="html-bibr">19</a>]. Copyright (2003) by the Elsevier).</p>
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<p>(<b>a</b>) Derivative of 1st cycle reversible capacity; and (<b>b</b>) reversible capacity of g-CNT (carbon nanotube) and l-CNT, divided into three potential areas of graphene layer deintercalation (0.01–0.6 V), inner core deinsertion (0.6–1.9 V) and extraction from functional groups (1.9–3.0 V); ~0.5 mg/cm<sup>2</sup>, 1 M LiPF<sub>6</sub> in 1:1 EC: DEC, 50 mAh/g. (Reprinted with permission from [<a href="#B57-materials-06-01138" class="html-bibr">57</a>]. Copyright (2012) by Elsevier).</p>
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<p>(<b>a</b>) C<sub>66</sub>H<sub>12</sub>; (<b>b</b>) C<sub>88</sub>H<sub>16</sub>; (<b>c</b>) C1<sub>10</sub>H<sub>20</sub>; and (<b>d</b>) C<sub>132</sub>H<sub>24</sub> cluster models used for the calculations of the pure (3,3), (4,4), (5,5) and (6,6) SWNTs; (<b>e</b>) Li<sub>3</sub>C<sub>66</sub>H<sub>12</sub>; (<b>f</b>) Li<sub>4</sub>C<sub>88</sub>H<sub>16</sub>; (<b>g</b>) Li<sub>5</sub>C<sub>110</sub>H<sub>20</sub>; and (<b>h</b>) Li<sub>6</sub>C<sub>132</sub>H<sub>24</sub> cluster models used for the calculations of the Li outside absorption; (<b>i</b>) LiC<sub>66</sub>H<sub>12</sub>; (<b>j</b>) Li<sub>4</sub>C<sub>88</sub>H<sub>16</sub>; (<b>k</b>) Li<sub>5</sub>C<sub>110</sub>H<sub>20</sub>; and (<b>l</b>) Li<sub>6</sub>C<sub>132</sub>H<sub>24</sub> cluster models used for the calculations of the Li inside absorption. The figures (a–l) are top views from the mouth of nanotubes. The figures m and n are side views of the pure and Li outside-absorbed (6, 6) nanotubes. Three kinds of carbon atoms, denoted by C<sub>1</sub>, C<sub>2</sub> and C<sub>3</sub>, are given in figures. (Reprinted with permission from [<a href="#B14-materials-06-01138" class="html-bibr">14</a>]. Copyright (2004) by Elsevier).</p>
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<p>The variation of Li/C ratio as a function of tube diameter. The equilibrium configurations SWNTs filled with Li atoms are shown in the insets of this figure. White and grey balls represent carbon and Li atoms, respectively. (Reprinted with permission from [<a href="#B13-materials-06-01138" class="html-bibr">13</a>]. Copyright (2005) by Elsevier).</p>
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<p>FESEM (Field emission scanning electron microscopy) images of the MWCNTs (multiwalled carbon nanotubes) with diameter range of (<b>a</b>) 10–20 nm; (<b>b</b>) 20–40 nm; (<b>c</b>) 40–60 nm; and (<b>d</b>) 60–100 nm. (Reprinted with permission from [<a href="#B58-materials-06-01138" class="html-bibr">58</a>]. Copyright (2012) by Elsevier).</p>
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<p>Transmission electron microscopy (TEM) and high-resolution TEM images of (<b>a,b</b>) very long; (<b>c,d</b>) long; and (<b>e,f</b>) short CNTs. (Reprinted with permission from [<a href="#B66-materials-06-01138" class="html-bibr">66</a>]. Copyright (2007) by Wiley).</p>
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<p>Variation of <span class="html-italic">C</span><sub>rev</sub> with number of cycles at a current density of 25 mAg<sup>–1</sup>. Note that the capacity becomes stable after 30 cycles. (Reprinted with permission from [<a href="#B66-materials-06-01138" class="html-bibr">66</a>]. Copyright (2007) by Wiley).</p>
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<p>Performances of different CNTs in Li-ion batteries. Discharge/charge curves of Li insertion/extraction into/from conventional (<b>a</b>) long; (<b>b</b>) short; and (<b>c</b>) cut CNTs for the first and second cycles at a current density of 25 mAg<sup>−1</sup>; and (<b>d</b>) charge capacities of long and short CNTs as a function of cycle number. (Reprinted with permission from [<a href="#B67-materials-06-01138" class="html-bibr">67</a>]. Copyright (2009) by Elsevier).</p>
Full article ">Figure 8 Cont.
<p>Performances of different CNTs in Li-ion batteries. Discharge/charge curves of Li insertion/extraction into/from conventional (<b>a</b>) long; (<b>b</b>) short; and (<b>c</b>) cut CNTs for the first and second cycles at a current density of 25 mAg<sup>−1</sup>; and (<b>d</b>) charge capacities of long and short CNTs as a function of cycle number. (Reprinted with permission from [<a href="#B67-materials-06-01138" class="html-bibr">67</a>]. Copyright (2009) by Elsevier).</p>
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<p>The electrochemical performance of the freestanding CNT films: (<b>a</b>) galvanostatic charge–discharge profiles in the 1st cycle; and (<b>b</b>) cycling behavior between 0.01 and 2.00 V <span class="html-italic">vs.</span> Li/Li<sup>+</sup> at a specific current of 25 mAg<sup>−1</sup>. (Reprinted with permission from [<a href="#B40-materials-06-01138" class="html-bibr">40</a>]. Copyright (2009) by Elsevier).</p>
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2487 KiB  
Article
Recent Advances in Creep Modelling of the Nickel Base Superalloy, Alloy 720Li
by William Harrison, Mark Whittaker and Steve Williams
Materials 2013, 6(3), 1118-1137; https://doi.org/10.3390/ma6031118 - 20 Mar 2013
Cited by 28 | Viewed by 8522
Abstract
Recent work in the creep field has indicated that the traditional methodologies involving power law equations are not sufficient to describe wide ranging creep behaviour. More recent approaches such as the Wilshire equations however, have shown promise in a wide range of materials, [...] Read more.
Recent work in the creep field has indicated that the traditional methodologies involving power law equations are not sufficient to describe wide ranging creep behaviour. More recent approaches such as the Wilshire equations however, have shown promise in a wide range of materials, particularly in extrapolation of short term results to long term predictions. In the aerospace industry however, long term creep behaviour is not critical and more focus is required on the prediction of times to specific creep strains. The current paper illustrates the capability of the Wilshire equations to recreate full creep curves in a modern nickel superalloy. Furthermore, a finite-element model based on this method has been shown to accurately predict stress relaxation behaviour allowing more accurate component lifing. Full article
(This article belongs to the Special Issue Superalloys)
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Figure 1

Figure 1
<p>Microstructure of Alloy 720Li.</p>
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<p>Relationship of minimum creep rate (<math display="inline"> <semantics> <mrow> <msub> <mover accent="true"> <mi>ε</mi> <mo>˙</mo> </mover> <mtext>m</mtext> </msub> </mrow> </semantics> </math>) with rupture time (<math display="inline"> <semantics> <mrow> <msub> <mi>t</mi> <mtext>f</mtext> </msub> </mrow> </semantics> </math>) for Alloy 720Li (550 °C to 750 °C).</p>
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<p>Power Law representation of Alloy 720Li (550 °C to 750 °C).</p>
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<p>Dependence of <math display="inline"> <semantics> <mrow> <mi>ln</mi> <mrow> <mo>(</mo> <mrow> <mo>−</mo> <mi>ln</mi> <mrow> <mo>(</mo> <mrow> <mrow> <mi>σ</mi> <mo>/</mo> <mrow> <msub> <mi>σ</mi> <mrow> <mtext>TS</mtext> </mrow> </msub> </mrow> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> </semantics> </math> on <math display="inline"> <semantics> <mrow> <mi>ln</mi> <mrow> <mo>(</mo> <mrow> <msub> <mi>t</mi> <mtext>f</mtext> </msub> <mi>exp</mi> <mrow> <mo>(</mo> <mrow> <mrow> <mrow> <mo>−</mo> <msub> <mi>Q</mi> <mi>c</mi> </msub> </mrow> <mo>/</mo> <mrow> <mi>R</mi> <mi>T</mi> </mrow> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> </semantics> </math> for Alloy 720Li, with <math display="inline"> <semantics> <mrow> <msubsup> <mi>Q</mi> <mi>c</mi> <mo>*</mo> </msubsup> </mrow> </semantics> </math> ≅ 330 kJ mol<sup>−1</sup>.</p>
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<p>Stress rupture plots for Alloy 720Li with stress normalised by <math display="inline"> <semantics> <mrow> <msub> <mi>σ</mi> <mrow> <mtext>TS</mtext> </mrow> </msub> </mrow> </semantics> </math> predicted using Equation (4) (550 °C to 750 °C).</p>
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<p>A comparison between experimental creep rupture lives for Alloy 720Li and those obtained using Equation (4) (550 °C to 750 °C). Dashed lines represent a deviation of a factor +/−2.</p>
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<p>Dependence of <math display="inline"> <semantics> <mrow> <mi>ln</mi> <mrow> <mo>(</mo> <mrow> <mo>−</mo> <mi>ln</mi> <mrow> <mo>(</mo> <mrow> <mrow> <mi>σ</mi> <mo>/</mo> <mrow> <msub> <mi>σ</mi> <mrow> <mtext>TS</mtext> </mrow> </msub> </mrow> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> </semantics> </math> on <math display="inline"> <semantics> <mrow> <mi>ln</mi> <mrow> <mo>(</mo> <mrow> <msub> <mover accent="true"> <mi>ε</mi> <mo>˙</mo> </mover> <mtext>m</mtext> </msub> <mi>exp</mi> <mrow> <mo>(</mo> <mrow> <mrow> <mrow> <mo>−</mo> <msub> <mi>Q</mi> <mi>c</mi> </msub> </mrow> <mo>/</mo> <mrow> <mi>R</mi> <mi>T</mi> </mrow> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> </semantics> </math> for Alloy 720Li, with <math display="inline"> <semantics> <mrow> <msubsup> <mi>Q</mi> <mi>c</mi> <mo>*</mo> </msubsup> </mrow> </semantics> </math> ≅ 330 kJ mol<sup>−1</sup>.</p>
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<p>Minimum creep rate plots for Alloy 720Li with stress normalised by <math display="inline"> <semantics> <mrow> <msub> <mi>σ</mi> <mrow> <mtext>TS</mtext> </mrow> </msub> </mrow> </semantics> </math>. Solid lines represent the fit obtained using Equation (5) (550 °C to 750 °C).</p>
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<p>A comparison between experimental minimum creep rates for Alloy 720Li and those obtained using Equation (5) (550 °C to 750 °C). Dashed lines represent a deviation of a factor +/−2.</p>
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<p>Schematic representation of different creep curves with equal values of <math display="inline"> <semantics> <mrow> <msub> <mover accent="true"> <mi>ε</mi> <mo>˙</mo> </mover> <mtext>m</mtext> </msub> </mrow> </semantics> </math>, <math display="inline"> <semantics> <mrow> <msub> <mi>ε</mi> <mtext>f</mtext> </msub> </mrow> </semantics> </math> and <math display="inline"> <semantics> <mrow> <msub> <mi>t</mi> <mtext>f</mtext> </msub> </mrow> </semantics> </math>.</p>
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<p>Normalised creep curves showing the variation in the proportion of primary to tertiary creep with test conditions.</p>
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<p>Dependence of strain to failure, <math display="inline"> <semantics> <mrow> <msub> <mi>ε</mi> <mtext>F</mtext> </msub> </mrow> </semantics> </math> against normalised stress for Alloy 720Li at 550 °C to 750 °C.</p>
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<p>Description of a creep curve using <math display="inline"> <semantics> <mrow> <msub> <mi>ε</mi> <mtext>P</mtext> </msub> </mrow> </semantics> </math>, <math display="inline"> <semantics> <mrow> <msub> <mover accent="true"> <mi>ε</mi> <mo>˙</mo> </mover> <mtext>m</mtext> </msub> </mrow> </semantics> </math>, <math display="inline"> <semantics> <mrow> <msub> <mi>t</mi> <mtext>f</mtext> </msub> </mrow> </semantics> </math> and <math display="inline"> <semantics> <mrow> <msub> <mi>ε</mi> <mtext>F</mtext> </msub> </mrow> </semantics> </math>.</p>
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<p>Dependence of primary creep strain, <math display="inline"> <semantics> <mrow> <msub> <mi>ε</mi> <mtext>P</mtext> </msub> </mrow> </semantics> </math> against normalised stress for Alloy 720Li at 550 °C to 750 °C.</p>
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<p>Dependence of total creep strain to failure, <math display="inline"> <semantics> <mrow> <msub> <mi>ε</mi> <mtext>F</mtext> </msub> </mrow> </semantics> </math> on tertiary creep strain for Alloy 720Li at 550 °C to 750 °C.</p>
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<p>Dependence of <math display="inline"> <semantics> <mrow> <mi>ln</mi> <mrow> <mo>(</mo> <mrow> <mi>ln</mi> <mrow> <mo>(</mo> <mrow> <mrow> <mi>σ</mi> <mo>/</mo> <mrow> <msub> <mi>σ</mi> <mrow> <mi>T</mi> <mi>S</mi> </mrow> </msub> </mrow> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> </semantics> </math> on <math display="inline"> <semantics> <mrow> <mi>ln</mi> <mrow> <mo>(</mo> <mrow> <msub> <mi>t</mi> <mrow> <mi>ε</mi> <mo>=</mo> <mn>1</mn> <mi>%</mi> </mrow> </msub> <mi>exp</mi> <mrow> <mo>(</mo> <mrow> <mrow> <mrow> <mo>−</mo> <msub> <mi>Q</mi> <mi>c</mi> </msub> </mrow> <mo>/</mo> <mrow> <mi>R</mi> <mi>T</mi> </mrow> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> <mo>)</mo> </mrow> </mrow> </semantics> </math> for Alloy 720Li, with <math display="inline"> <semantics> <mrow> <msubsup> <mi>Q</mi> <mi>c</mi> <mo>*</mo> </msubsup> </mrow> </semantics> </math> ≅ 330 kJ mol<sup>−1</sup>.</p>
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<p>Time to 1% creep strain, <span class="html-italic">t</span><sub>ε</sub> = 1%, for Alloy720Li predicted using Equations (15) and (16) (550 °C to 750 °C).</p>
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<p>A comparison between experimental times to 1% creep strain for Alloy 720Li and those obtained using Equation (9) (550 °C to 750 °C). Dashed lines represent a deviation of a factor +/−2.</p>
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<p>Dependence of creep strain, <math display="inline"> <semantics> <mrow> <msub> <mi>ε</mi> <mtext>c</mtext> </msub> </mrow> </semantics> </math>, on stress, <math display="inline"> <semantics> <mi>σ</mi> </semantics> </math>, and time for Alloy 720Li at 650 °C as predicted by the Wilshire creep curve method.</p>
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<p>Predicted and experimental creep curves for Alloy 720Li at 650 °C and 700 °C.</p>
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<p>Comparison of predicted and experimentally obtained stress relaxation data.</p>
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<p>Dependence of <math display="inline"> <semantics> <mrow> <mrow> <mrow> <msub> <mi>ε</mi> <mtext>F</mtext> </msub> </mrow> <mo>/</mo> <mrow> <msub> <mi>ε</mi> <mtext>P</mtext> </msub> </mrow> </mrow> </mrow> </semantics> </math> against normalised stress for Alloy 720Li at 550 °C to 750 °C.</p>
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122 KiB  
Article
Towards a Consensus View on Understanding Nanomaterials Hazards and Managing Exposure: Knowledge Gaps and Recommendations
by Geoffrey Hunt, Iseult Lynch, Flemming Cassee, Richard D. Handy, Teresa F. Fernandes, Markus Berges, Thomas A. J. Kuhlbusch, Maria Dusinska and Michael Riediker
Materials 2013, 6(3), 1090-1117; https://doi.org/10.3390/ma6031090 - 20 Mar 2013
Cited by 29 | Viewed by 8888
Abstract
The aim of this article is to present an overview of salient issues of exposure, characterisation and hazard assessment of nanomaterials as they emerged from the consensus-building of experts undertaken within the four year European Commission coordination project NanoImpactNet. The approach adopted is [...] Read more.
The aim of this article is to present an overview of salient issues of exposure, characterisation and hazard assessment of nanomaterials as they emerged from the consensus-building of experts undertaken within the four year European Commission coordination project NanoImpactNet. The approach adopted is to consolidate and condense the findings and problem-identification in such a way as to identify knowledge-gaps and generate a set of interim recommendations of use to industry, regulators, research bodies and funders. The categories of recommendation arising from the consensual view address: significant gaps in vital factual knowledge of exposure, characterisation and hazards; the development, dissemination and standardisation of appropriate laboratory protocols; address a wide range of technical issues in establishing an adequate risk assessment platform; the more efficient and coordinated gathering of basic data; greater inter-organisational cooperation; regulatory harmonization; the wider use of the life-cycle approaches; and the wider involvement of all stakeholders in the discussion and solution-finding efforts for nanosafety. Full article
(This article belongs to the Special Issue Nanotoxicology)
1782 KiB  
Article
Thermo-Mechanical Behavior of Textile Heating Fabric Based on Silver Coated Polymeric Yarn
by Syed Talha Ali Hamdani, Prasad Potluri and Anura Fernando
Materials 2013, 6(3), 1072-1089; https://doi.org/10.3390/ma6031072 - 20 Mar 2013
Cited by 69 | Viewed by 11498
Abstract
This paper presents a study conducted on the thermo-mechanical properties of knitted structures, the methods of manufacture, effect of contact pressure at the structural binding points, on the degree of heating. The test results also present the level of heating produced as a [...] Read more.
This paper presents a study conducted on the thermo-mechanical properties of knitted structures, the methods of manufacture, effect of contact pressure at the structural binding points, on the degree of heating. The test results also present the level of heating produced as a function of the separation between the supply terminals. The study further investigates the rate of heating and cooling of the knitted structures. The work also presents the decay of heating properties of the yarn due to overheating. Thermal images were taken to study the heat distribution over the surface of the knitted fabric. A tensile tester having constant rate of extension was used to stretch the fabric. The behavior of temperature profile of stretched fabric was observed. A comparison of heat generation by plain, rib and interlock structures was studied. It was observed from the series of experiments that there is a minimum threshold force of contact at binding points of a knitted structure is required to pass the electricity. Once this force is achieved, stretching the fabric does not affect the amount of heat produced. Full article
(This article belongs to the Special Issue Advances in Multifunctional Materials)
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<p>Sketch of the arrangement of the silver yarn and the elastomeric yarn in the plain knitted heating fabric.</p>
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<p>A binding point at the sinker loop of the knitted structure.</p>
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<p>Flowchart for MatLab program.</p>
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<p>Current<span class="html-italic"> vs.</span> conducting yarn length for the silver yarn at 9 V.</p>
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<p>Thermal images for (<b>a</b>) plain; (<b>b</b>) rib and (<b>c</b>) interlock structures at 3 V.</p>
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<p>Thermal images for (<b>a</b>) plain; (<b>b</b>) rib and (<b>c</b>) interlock structures at 3 V.</p>
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<p>Theoretical temperature profiles of plain knitted structure.</p>
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<p>Comparison of silver yarn plain, rib and interlock structures at 3 V and 80 mm terminal separation.</p>
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<p>Schematic diagrams of (<b>a</b>) plain; (<b>b</b>) 1 × 1 rib and (<b>c</b>) interlock knitted structure.</p>
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<p>Comparison of Silver yarn, plain, rib and interlock structures at 9 V Sample size: 40 mm.</p>
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<p>Change of temperature with respect to strain %.</p>
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<p>Yarn path notations for plain (<b>a</b>) technical front and (<b>b</b>) technical back.</p>
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<p>Knitted heating fabric with bus bars for electrical terminals.</p>
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300 KiB  
Article
Quinacridone-Diketopyrrolopyrrole-Based Polymers for Organic Field-Effect Transistors
by Masahiro Akita, Itaru Osaka and Kazuo Takimiya
Materials 2013, 6(3), 1061-1071; https://doi.org/10.3390/ma6031061 - 18 Mar 2013
Cited by 11 | Viewed by 8209
Abstract
Incorporation of pigment or dye molecules as building units is of great interest in the development of semiconducting polymers, due to their strong intermolecular interactions arising from the strong local dipoles in the unit structure, which would facilitate the charge transport property. In [...] Read more.
Incorporation of pigment or dye molecules as building units is of great interest in the development of semiconducting polymers, due to their strong intermolecular interactions arising from the strong local dipoles in the unit structure, which would facilitate the charge transport property. In this paper, semiconducting polymers based on well-known pigments, namely, quinacridone and diketopyrrolopyrrole, are synthesized and characterized. The π-stacking distances are found to be 3.5–3.8 Å, which is fairly narrow for semiconducting polymers, indicating that they possess strong intermolecular interactions. Interestingly, polymer orientation is influenced by the composition of alkyl side chains. While the edge-on orientation is observed when the linear alkyl groups are introduced for all the side chains, the face-on orientation is observed when the branched alkyl groups are introduced either in the quinacridone or diketopyrrolopyrrole unit. It is found that the electronic structure of the present polymers is mostly affected by that of the diketopyrrolopyrrole unit, as evidenced by the absorption spectra and computation. Although the field-effect mobility of the polymers is modest, i.e., in the order of 10−4–10−3 cm2/Vs, these findings could be important information for the development of semiconducting polymers. Full article
(This article belongs to the Special Issue Conjugated Polymers)
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<p>Chemical structure of quinacridone and a quinacridone-based semiconducting polymer.</p>
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<p>UV-Vis absorption spectra of the polymers in chlorobenzene solution (<b>a</b>) and in thin film (<b>b</b>).</p>
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<p>Computation (DFT at B3LYP/6-31(d) level) of the HOMO and LUMO geometry of quinacridone (QA, left), polymer repeat unit (QADPP, middle), and dithienyl diketopyrrolopyrrole (DPP2T), in which the methyl group is used as the substituents. HOMO (<span class="html-italic">E</span><sub>HOMO</sub>) and LUMO levels (<span class="html-italic">E</span><sub>LUMO</sub>) for each compound are also shown. <span class="html-italic">E</span><sub>HOMO</sub> and <span class="html-italic">E</span><sub>LUMO</sub> for QA and DPP2T were determined by electrochemistry. <span class="html-italic">E</span><sub>HOMO</sub> denoted as QADPP is that of the polymer (PQADPP-16DT) obtained by photoelectron spectroscopy in air (PESA), and <span class="html-italic">E</span><sub>LUMO</sub> is determined by the addition of optical bandgap to <span class="html-italic">E</span><sub>HOMO</sub>.</p>
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<p>Transfer characteristics of OFETs based on PQADPP-16, -16DT, and -DT16 (<b>a</b>) and output characteristics of OFETs based on PQADPP-16 (<b>b</b>); -16DT (<b>c</b>); and -DT16 (<b>d</b>).</p>
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<p>2D-GIXD patterns of the polymer films. GIXD: Grazing incidence X-ray diffraction.</p>
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<p>Synthesis and chemical structure of the polymers based on quinacridone (QA) and diketopyrrolopyrrole (DPP).</p>
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561 KiB  
Article
Photoluminescence Study of Gallium Nitride Thin Films Obtained by Infrared Close Space Vapor Transport
by Guillermo Santana, Osvaldo De Melo, Jorge Aguilar-Hernández, Rogelio Mendoza-Pérez, B. Marel Monroy, Adolfo Escamilla-Esquivel, Máximo López-López, Francisco De Moure, Luis A. Hernández and Gerardo Contreras-Puente
Materials 2013, 6(3), 1050-1060; https://doi.org/10.3390/ma6031050 - 15 Mar 2013
Cited by 44 | Viewed by 8961
Abstract
Photoluminescence (PL) studies in GaN thin films grown by infrared close space vapor transport (CSVT-IR) in vacuum are presented in this work. The growth of GaN thin films was done on a variety of substrates like silicon, sapphire and fused silica. Room temperature [...] Read more.
Photoluminescence (PL) studies in GaN thin films grown by infrared close space vapor transport (CSVT-IR) in vacuum are presented in this work. The growth of GaN thin films was done on a variety of substrates like silicon, sapphire and fused silica. Room temperature PL spectra of all the GaN films show near band-edge emission (NBE) and a broad blue and green luminescence (BL, GL), which can be seen with the naked eye in a bright room. The sample grown by infrared CSVT on the silicon substrate shows several emission peaks from 2.4 to 3.22 eV with a pronounced red shift with respect to the band gap energy. The sample grown on sapphire shows strong and broad ultraviolet emission peaks (UVL) centered at 3.19 eV and it exhibits a red shift of NBE. The PL spectrum of GaN films deposited on fused silica exhibited a unique and strong blue-green emission peak centered at 2.38 eV. The presence of yellow and green luminescence in all samples is related to native defects in the structure such as dislocations in GaN and/or the presence of amorphous phases. We analyze the material quality that can be obtained by CSVT-IR in vacuum, which is a high yield technique with simple equipment set-up, in terms of the PL results obtained in each case. Full article
(This article belongs to the Special Issue Luminescent Materials 2013)
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<p>Experimental set-up scheme and photograph of the graphite crucible used in the CSVT system.</p>
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<p>X-ray diffraction (XRD) pattern of a representative GaN sample grown on p-Si (111) substrate. The insert shows the diffractograms of samples grown on fused silica (<b>A</b>) and sapphire (<b>B</b>) and the GaN reference.</p>
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<p>Scanning electron microscope (SEM) micrograph and energy dispersive spectroscopy (EDS) spectrum of the polycrystalline GaN thin film grown on silicon substrate.</p>
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<p>Room temperature photoluminescence spectrum for a sample grown by infrared CSVT technique on silicon substrate.</p>
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<p>Room temperature photoluminescence spectrum for a sample grown by infrared CSVT technique on sapphire substrate.</p>
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<p>Room temperature photoluminescence spectrum for a sample grown by infrared CSVT technique on fused silica substrate.</p>
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1325 KiB  
Review
Advanced Electrodes for High Power Li-ion Batteries
by Karim Zaghib, Alain Mauger, Henri Groult, John B. Goodenough and Christian M. Julien
Materials 2013, 6(3), 1028-1049; https://doi.org/10.3390/ma6031028 - 15 Mar 2013
Cited by 118 | Viewed by 14196
Abstract
While little success has been obtained over the past few years in attempts to increase the capacity of Li-ion batteries, significant improvement in the power density has been achieved, opening the route to new applications, from hybrid electric vehicles to high-power electronics and [...] Read more.
While little success has been obtained over the past few years in attempts to increase the capacity of Li-ion batteries, significant improvement in the power density has been achieved, opening the route to new applications, from hybrid electric vehicles to high-power electronics and regulation of the intermittency problem of electric energy supply on smart grids. This success has been achieved not only by decreasing the size of the active particles of the electrodes to few tens of nanometers, but also by surface modification and the synthesis of new multi-composite particles. It is the aim of this work to review the different approaches that have been successful to obtain Li-ion batteries with improved high-rate performance and to discuss how these results prefigure further improvement in the near future. Full article
(This article belongs to the Special Issue Advanced Materials for Lithium Ion Batteries)
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<p>High resolution transmission electron microscopy (HRTEM) features of LiNi<sub>1/3</sub>Mn<sub>1/3</sub>Co<sub>1/3</sub>O<sub>2</sub> (LNMC) powders for as-grown (<b>a</b>) and heat treated sample with sucrose at 600 °C for 30 min in air (<b>b</b>). (Reprinted with permission from [<a href="#B57-materials-06-01028" class="html-bibr">57</a>]. Copyright 2011 Elsevier.)</p>
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<p>Discharge cell voltage <span class="html-italic">vs.</span> gravimetric capacity of the Li//LNMCO cells for various C-rate for (<b>a</b>) the as-grown cathode material and (<b>b</b>) heat treated sample with sucrose at 600 °C for 30 min in air. (Reprinted with permission from [<a href="#B57-materials-06-01028" class="html-bibr">57</a>]. Copyright 2011 Elsevier.)</p>
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<p>The modified Peukert plots of Li cells for the as-grown and the surface modified LNMC cathode material. (Reprinted with permission from [<a href="#B57-materials-06-01028" class="html-bibr">57</a>]. Copyright 2011 Elsevier.)</p>
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<p>(<b>a</b>) Energy Dispersive X-ray Detector (EDX) spectra at three spots show that both Mn and Fe in the analyzed areas with Mn peak intensity higher than Fe’s one. On average, the relative concentration Mn:Fe is 2/3:1/3. (Cu and Si are from the sample support); (<b>b</b>) Transmission Electron Microscope (TEM) image showing the continuous carbon coating deposited onto the LFP layer. (Reprinted with permission from [<a href="#B59-materials-06-01028" class="html-bibr">59</a>]. Copyright 2012 Elsevier.)</p>
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<p>Voltage as a function of time in charge/discharge conditions corresponding to theoretical rate C/24 for the composite C-LiFePO<sub>4</sub>-LiMnPO<sub>4</sub> and LiMn<sub>2/3</sub>Fe<sub>1/3</sub>PO<sub>4</sub> for comparison. (Reprinted with permission from [<a href="#B59-materials-06-01028" class="html-bibr">59</a>]. Copyright 2012 Elsevier.)</p>
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<p>Modified Peukert plot for the C-LiFePO<sub>4</sub>-LiMnPO<sub>4</sub> and LiMn<sub>2/3</sub>Fe<sub>1/3</sub>PO<sub>4</sub> samples for comparison. (Reprinted with permission from [<a href="#B59-materials-06-01028" class="html-bibr">59</a>]. Copyright 2012 Elsevier.)</p>
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<p>EDX maps of the P (<b>a</b>) and Fe (<b>b</b>) elements for the C-LiFePO<sub>4</sub> coated LiMn<sub>1.5</sub>Ni<sub>0.5</sub>O<sub>4</sub> multi-composite. (Reprinted with permission from [<a href="#B66-materials-06-01028" class="html-bibr">66</a>]. Copyright 2012 Elsevier.)</p>
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<p>Discharge profiles of the Li//C-LiFePO<sub>4</sub>-coated LiMn<sub>1.5</sub>Ni<sub>0.5</sub>O<sub>4</sub> cell at different C rates. (Reprinted with permission from [<a href="#B66-materials-06-01028" class="html-bibr">66</a>]. Copyright 2012 Elsevier.)</p>
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<p>Modified Peukert plot of the Li//C-LiFePO<sub>4</sub>-coated and uncoated LiMn<sub>1.5</sub>Ni<sub>0.5</sub>O<sub>4</sub> cells between 3.0 and 4.9 V. (Reprinted with permission from [<a href="#B66-materials-06-01028" class="html-bibr">66</a>]. Copyright 2012 Elsevier.)</p>
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<p>Cyclability of the Li/LiMn<sub>1.5</sub>Ni<sub>0.5</sub>O<sub>4</sub> and Li/LiFePO<sub>4</sub>-coated LiMn<sub>1.5</sub>Ni<sub>0.5</sub>O<sub>4</sub> cells at 1C between 3 and 4.9 V. (Reprinted with permission from [<a href="#B66-materials-06-01028" class="html-bibr">66</a>]. Copyright 2012 Elsevier.)</p>
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<p>Cycle life of a LiFePO<sub>4</sub>/EC-DEC-1<span class="html-italic">M</span> LiPF<sub>6</sub>/Li<sub>4</sub>Ti<sub>5</sub>O<sub>12</sub> 18650-cell. The cycle charge rate is 10C (6 min) at 100% state of charge, the discharge rate is 5C (12 min) at 100% depth of discharge during the test (Reprinted with permission from [<a href="#B68-materials-06-01028" class="html-bibr">68</a>]. Copyright 2011 Elsevier).</p>
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<p>Thermal infrared image of the LTO//LFP “18650”-type cell recorded during charge at rate 50C, at full charge 2.1 V (bottom), and total discharge at 1.0 V (top). The electrolyte is with 1 mol L<sup>−1</sup> LiPF<sub>6</sub> in EC-DEC (1:1). (Reprinted with permission from [<a href="#B68-materials-06-01028" class="html-bibr">68</a>]. Copyright 2011 Elsevier.)</p>
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1273 KiB  
Article
Graphene versus Multi-Walled Carbon Nanotubes for Electrochemical Glucose Biosensing
by Dan Zheng, Sandeep Kumar Vashist, Michal Marcin Dykas, Surajit Saha, Khalid Al-Rubeaan, Edmond Lam, John H.T. Luong and Fwu-Shan Sheu
Materials 2013, 6(3), 1011-1027; https://doi.org/10.3390/ma6031011 - 14 Mar 2013
Cited by 69 | Viewed by 11505
Abstract
: A simple procedure was developed for the fabrication of electrochemical glucose biosensors using glucose oxidase (GOx), with graphene or multi-walled carbon nanotubes (MWCNTs). Graphene and MWCNTs were dispersed in 0.25% 3-aminopropyltriethoxysilane (APTES) and drop cast on 1% KOH-pre-treated glassy carbon electrodes (GCEs). [...] Read more.
: A simple procedure was developed for the fabrication of electrochemical glucose biosensors using glucose oxidase (GOx), with graphene or multi-walled carbon nanotubes (MWCNTs). Graphene and MWCNTs were dispersed in 0.25% 3-aminopropyltriethoxysilane (APTES) and drop cast on 1% KOH-pre-treated glassy carbon electrodes (GCEs). The EDC (1-ethyl-(3-dimethylaminopropyl) carbodiimide)-activated GOx was then bound covalently on the graphene- or MWCNT-modified GCE. Both the graphene- and MWCNT-based biosensors detected the entire pathophysiological range of blood glucose in humans, 1.4–27.9 mM. However, the direct electron transfer (DET) between GOx and the modified GCE’s surface was only observed for the MWCNT-based biosensor. The MWCNT-based glucose biosensor also provided over a four-fold higher current signal than its graphene counterpart. Several interfering substances, including drug metabolites, provoked negligible interference at pathological levels for both the MWCNT- and graphene-based biosensors. However, the former was more prone to interfering substances and drug metabolites at extremely pathological concentrations than its graphene counterpart. Full article
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Graphical abstract

Graphical abstract
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<p>High resolution images of (<b>a</b>) grapheme-glucose oxidase (GOx); (<b>b</b>) Nafion/graphene-GOx; (<b>c</b>) MWCNT-GOx and (<b>d</b>) Nafion/MWCNT-GOx modified glassy carbon substrates using a helium ion microscope from Carl Zeiss, Germany. The scale bars for (<b>a</b>)/(<b>b</b>) and (<b>c</b>)/(<b>d</b>) are 10 μm and 200 nm, respectively.</p>
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<p>(<b>a</b>) CVs of Nafion/GOx/glassy carbon electrodes (GCE) (blue), Nafion/graphene/GCE (yellow), Nafion/MWCNT/GCE (red), Nafion/graphene-GOx/GCE (green) and Nafion/MWCNT-GOx/GCE (black) in N<sub>2</sub>-saturated PBS at 100 mV s<sup>−1</sup>; (<b>b</b>) The effect of scan rate (20, 50, 100, 150 and 200 mV s<sup>−1</sup>) on the DET of GOx on Nafion/MWCNT-GOx/GCE in N<sub>2</sub>-saturated PBS. Inlet: the linear relation between <span class="html-italic">i</span><sub>pc</sub> (or <span class="html-italic">i</span><sub>pa</sub>) and <span class="html-italic">v</span>; (<b>c</b>) The relation between the formal potential (observed on Nafion/MWCNT-GOx/GCE) and different pH values: 5.65, 6.36, 7.2, 7.72, 8.29. Scan rate = 100 mV s<sup>−</sup><sup>1</sup>; (<b>d</b>) Plot of <span class="html-italic">E</span><sub>p</sub> (of the Nafion/MWCNT-GO<span class="html-italic">x</span>/GCE) <span class="html-italic">vs.</span> log <span class="html-italic">v</span>, <span class="html-italic">v</span> = 0.1, 0.2, 0.3, 0.4, 0.5, 0.7, 0.9, 1.1, 1.3, 1.5, 1.7, 1.9 V s<sup>−</sup><sup>1</sup>. Inlet: the relation between <span class="html-italic">E</span><sub>pa</sub> (or <span class="html-italic">E</span><sub>pc</sub>) and log <span class="html-italic">v</span>.</p>
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<p>CVs of (<b>a</b>,<b>c</b>) Nafion/graphene-GOx/GCE and (<b>b</b>,<b>d</b>) Nafion/MWCNT-GOx/GCE in (<b>a</b>,<b>b</b>) nitrogen and (<b>c</b>,<b>d</b>) air-saturated PBS containing (i) 0 mM; (ii) 1 mM and (iii) 8 mM glucose. Scan rate: 100 mV s<sup>−1</sup>.</p>
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<p>(<b>a</b>) The amperometric response of Nafion/MWCNT-GOx/GCE for the detection of 0.5 to 32 mM glucose at −0.45 V in the presence of O<sub>2</sub>; (<b>b</b>) Assay curves for the detection of commercial glucose by the graphene- and MWCNT-based electrodes. The error bars represent standard deviation (SD); (<b>c</b>) Assay curves for the detection of Sugar-Chex whole blood glucose linearity standards by both electrodes. The error bars represent the SD; (<b>d</b>) The effect of interfering substances on the electrochemical detection of 6.8 mM blood glucose standard by both electrodes.</p>
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<p>The preparation of graphene- and multi-walled carbon nanotube (MWCNT)-based glucose biosensors.</p>
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632 KiB  
Article
Cosmetic Analysis Using Matrix-Assisted Laser Desorption/Ionization Mass Spectrometry Imaging (MALDI-MSI)
by Diogo Noin De Oliveira, Sabrina De Bona Sartor, Mônica Siqueira Ferreira and Rodrigo Ramos Catharino
Materials 2013, 6(3), 1000-1010; https://doi.org/10.3390/ma6031000 - 13 Mar 2013
Cited by 24 | Viewed by 8192
Abstract
A new “omic” platform—Cosmetomics—that proves to be extremely simple and effective in terms of sample preparation and readiness for data acquisition/interpretation is presented. This novel approach employing Matrix-Assisted Laser Desorption/Ionization Mass Spectrometry Imaging (MALDI-MSI) for cosmetic analysis has proven to readily identify and [...] Read more.
A new “omic” platform—Cosmetomics—that proves to be extremely simple and effective in terms of sample preparation and readiness for data acquisition/interpretation is presented. This novel approach employing Matrix-Assisted Laser Desorption/Ionization Mass Spectrometry Imaging (MALDI-MSI) for cosmetic analysis has proven to readily identify and quantify compounds of interest. It also allows full control of all the production phases, as well as of the final product, by integration of both analytical and statistical data. This work has focused on products of daily use, namely nail polish, lipsticks and eyeliners of multiple brands sold in the worldwide market. Full article
(This article belongs to the Special Issue Advances in Cosmetics)
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<p>Principal Component Analysis (PCA) score plots showing the different clusters of samples. The three classes (new, in use and expired) are stated.</p>
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<p>Correlation loadings plot for the principal components in lipstick samples: <span class="html-italic">m/z</span> range of 520–560 (diacylglicerols (DAGs)) for the expired product, <span class="html-italic">m/z</span> range of 890–1000 (higher triacylglycerols (TAGs)) for the “in-use” products and <span class="html-italic">m/z</span> range of 1100–1210 (ceramides) for the new products. The marked ions were the ones chosen as biomarkers for each degradation phase.</p>
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<p>Score plots of the eyeliner sample groups. The groups are represented as “exp” for expired samples, “new” for new samples and “in-use” for used samples.</p>
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<p>Correlation loadings for the principal components of the eyeliner samples: It is noted there is a very good correlation for both the new and “in-use” groups, as they presented ions in the <span class="html-italic">m/z</span> range of 700–800 (lower TAGs). It is possible to observe several ions on the <span class="html-italic">m/z</span> 900 and higher. The marked ions were the ones chosen as biomarkers for each degradation phase.</p>
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<p>Mass Spectrometry Imaging (MSI) of the samples analyzed on ImageJ software for the semi-quantification. The intensity on the grayscale indicates more (darker) or less (lighter) concentration of the desired analyte. This figure also illustrates that all samples were assigned the same area for further quantitative comparison.</p>
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<p>Semi-quantification results. The graph presents a comparison between all the nine samples as to the content of Sudan III (<span class="html-italic">m/</span>z 351, [M − H]<sup>−</sup>). It is noticeable that sample CCR has the greatest relative quantity when compared to all the others. The values stated on the top refer to the mean found of the calculations in triplicate. The values are expressed in arbitrary units.</p>
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<p>MS/MS spectrum of ion on <span class="html-italic">m/z</span> 351—[M − H]<sup>−</sup> identified as Sudan III.</p>
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2664 KiB  
Article
Grafting of Amines on Ethanol-Extracted SBA-15 for CO2 Adsorption
by Yong Li, Nannan Sun, Lei Li, Ning Zhao, Fukui Xiao, Wei Wei, Yuhan Sun and Wei Huang
Materials 2013, 6(3), 981-999; https://doi.org/10.3390/ma6030981 - 12 Mar 2013
Cited by 62 | Viewed by 9812
Abstract
SBA-15 prepared via ethanol extraction for template removing was grafted with three kinds of amine precursors (mono-, di-, tri-aminosilanes) to synthesis new CO2 adsorbents. The SBA-15 support and the obtained adsorbents were characterized by X-ray diffraction (XRD), small-angle X-ray scattering (SAXS), N [...] Read more.
SBA-15 prepared via ethanol extraction for template removing was grafted with three kinds of amine precursors (mono-, di-, tri-aminosilanes) to synthesis new CO2 adsorbents. The SBA-15 support and the obtained adsorbents were characterized by X-ray diffraction (XRD), small-angle X-ray scattering (SAXS), N2 adsorption/desorption, thermogravimetry (TG), elemental analysis, Fourier transform infrared (FTIR) spectrometry, scanning electron microscopy (SEM) and transmission electron microscopy (TEM). It was found that, except higher silanol density, the ethanol-extracted SBA-15 support possessed a more regular mesophase and thicker walls than traditionally calcined samples, leading to a good stability of the adsorbent under steam treatment. The adsorption capacity of different amine-grafted samples was found to be influenced by not only the surface amine density, but also their physiochemical properties. These observations provide important support for further studies of applying amine-grafted adsorbents in practical CO2 capture process. Full article
(This article belongs to the Special Issue Advances in Mesoporous Materials)
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<p>(<b>A</b>) X-ray diffraction (XRD); and (<b>B</b>) small-angle X-ray scattering (SAXS). Patterns of SBA-15-c and SBA-15-ex. a: SBA-15-c; b: SBA-15-ex.</p>
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<p>N<sub>2</sub> adsorption–desorption isotherms and pore distribution curves of SBA-15. a: SBA-15-c; b: SBA-15-ex.</p>
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<p>Scanning electron microscopy (SEM) and transmission electron microscopy (TEM) images of SBA-15-ex.</p>
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<p>Thermogravimetric analysis (TGA) curves of a: SBA-15-c; b and SBA-15-ex.</p>
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<p>Diffuse reflectance infrared Fourier transform spectroscopy (DRIFTS) spectra of SBA-15-ex and amine-grafted SBA-15-ex. a: SBA-15-ex; b: APTMS-SBA-15-ex; c: AEAPS-SBA-15-ex; d: TA-SBA-15-ex.</p>
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<p>(<b>A</b>) XRD; and (<b>B</b>) SAXS patterns of amine-grafted SBA-15-ex. a: APTMS-SBA-15-ex; b: AEAPS-SBA-15-ex; c: TA-SBA-15-ex.</p>
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<p>SEM images of SBA-15-ex and amine-grafted SBA-15-ex. (<b>A</b>) SBA-15-ex; (<b>B</b>) APTMS-SBA-15-ex; (<b>C</b>) AEAPS-SBA-15-ex; (<b>D</b>) TA-SBA-15-ex.</p>
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<p>SEM images of SBA-15-ex and amine-grafted SBA-15-ex. (<b>A</b>) SBA-15-ex; (<b>B</b>) APTMS-SBA-15-ex; (<b>C</b>) AEAPS-SBA-15-ex; (<b>D</b>) TA-SBA-15-ex.</p>
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<p>Breakthrough curves of CO<sub>2</sub> adsorption at 25 °C. a: APTMS-SBA-15-ex; b: AEAPS-SBA-15-ex; c: TA-SBA-15-ex; d: APTMS-SBA-15-c; e: SBA-15-ex.</p>
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<p><span class="html-italic">In situ</span> DRIFTS spectra of amine-grafted SBA-15-ex. a: APTMS-SBA-15-ex; b: AEAPS-SBA-15-ex; c: TA-SBA-15-ex.</p>
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<p>Comparison of (<b>A</b>) adsorption capacity; (<b>B</b>) Brunauer–Emmett–Teller (BET) surface area; (<b>C</b>) total pore volume; and (<b>D</b>) N contents of amine-grafted SBA-15 before and after steam treatment. a: APTMS-SBA-15-c; b: APTMS-SBA-15-ex; c: AEAPS-SBA-15-ex; d: TA-SBA-15-ex.</p>
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<p>Comparison of (<b>A</b>) adsorption capacity; (<b>B</b>) Brunauer–Emmett–Teller (BET) surface area; (<b>C</b>) total pore volume; and (<b>D</b>) N contents of amine-grafted SBA-15 before and after steam treatment. a: APTMS-SBA-15-c; b: APTMS-SBA-15-ex; c: AEAPS-SBA-15-ex; d: TA-SBA-15-ex.</p>
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<p>The molecular structures of the aminosilanes.</p>
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<p>Possible CO<sub>2</sub> adsorption species on different amine-grafted SBA-15. (<b>a</b>) APTMS-SBA-15-ex; (<b>b</b>) AEAPS-SBA-15-ex; (<b>c</b>) TA-SBA-15-ex.</p>
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501 KiB  
Article
Preparation of Amidoxime Polyacrylonitrile Chelating Nanofibers and Their Application for Adsorption of Metal Ions
by Fenglin Huang, Yunfei Xu, Shiqin Liao, Dawei Yang, You-Lo Hsieh and Qufu Wei
Materials 2013, 6(3), 969-980; https://doi.org/10.3390/ma6030969 - 11 Mar 2013
Cited by 141 | Viewed by 9445
Abstract
Polyacrylonitrile (PAN) nanofibers were prepared by electrospinning and they were modified with hydroxylamine to synthesize amidoxime polyacrylonitrile (AOPAN) chelating nanofibers, which were applied to adsorb copper and iron ions. The conversion of the nitrile group in PAN was calculated by the gravimetric method. [...] Read more.
Polyacrylonitrile (PAN) nanofibers were prepared by electrospinning and they were modified with hydroxylamine to synthesize amidoxime polyacrylonitrile (AOPAN) chelating nanofibers, which were applied to adsorb copper and iron ions. The conversion of the nitrile group in PAN was calculated by the gravimetric method. The structure and surface morphology of the AOPAN nanofiber were characterized by a Fourier transform infrared spectrometer (FT-IR) and a scanning electron microscope (SEM), respectively. The adsorption abilities of Cu2+ and Fe3+ ions onto the AOPAN nanofiber mats were evaluated. FT-IR spectra showed nitrile groups in the PAN were partly converted into amidoxime groups. SEM examination demonstrated that there were no serious cracks or sign of degradation on the surface of the PAN nanofibers after chemical modification. The adsorption capacities of both copper and iron ions onto the AOPAN nanofiber mats were higher than those into the raw PAN nanofiber mats. The adsorption data of Cu2+ and Fe3+ ions fitted particularly well with the Langmuir isotherm. The maximal adsorption capacities of Cu2+ and Fe3+ ions were 215.18 and 221.37 mg/g, respectively. Full article
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<p>Fourier transform infrared spectrometer (FT-IR) spectra of raw polyacrylonitrile (PAN) and amidoxime polyacrylonitrile (AOPAN) nanofiber mats (<b>a</b>) Raw PAN; (<b>b</b>) Modified PAN.</p>
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<p>Scanning electron microscope (SEM) photos of (<b>a</b>) PAN nanofibers; (<b>b</b>) AOPAN nanofibers (53% conversion).</p>
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<p>Adsorption capacities of copper and iron ions onto the PAN and AOPAN nanofibers.</p>
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<p>Adsorption of Cu<sup>2+</sup> and Fe<sup>3+</sup> ions on the AOPAN (43.6% conversion) nanofiber mat, in a 500 ppm solution as a function of time.</p>
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<p>Adsorption isotherms of iron ions on the (<b>a</b>) AOPAN (31.4% conversion) fitting models; (<b>b</b>) Langmuir model at 303 K and adsorption isotherms of copper ions on the (<b>c</b>) AOPAN (36% conversion) fitting models; (<b>d</b>) Langmuir model at 303 K.</p>
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<p>Adsorption isotherms of iron ions on the (<b>a</b>) AOPAN (31.4% conversion) fitting models; (<b>b</b>) Langmuir model at 303 K and adsorption isotherms of copper ions on the (<b>c</b>) AOPAN (36% conversion) fitting models; (<b>d</b>) Langmuir model at 303 K.</p>
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<p>The reaction between hydroxylamine and nitrile group.</p>
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1741 KiB  
Review
A Special Material or a New State of Matter: A Review and Reconsideration of the Aerogel
by Ai Du, Bin Zhou, Zhihua Zhang and Jun Shen
Materials 2013, 6(3), 941-968; https://doi.org/10.3390/ma6030941 - 8 Mar 2013
Cited by 422 | Viewed by 28536
Abstract
The ultrahighly nanoporous aerogel is recognized as a state of matter rather than as a functional material, because of its qualitative differences in bulk properties, transitional density and enthalpy between liquid and gas, and diverse chemical compositions. In this review, the characteristics, classification, [...] Read more.
The ultrahighly nanoporous aerogel is recognized as a state of matter rather than as a functional material, because of its qualitative differences in bulk properties, transitional density and enthalpy between liquid and gas, and diverse chemical compositions. In this review, the characteristics, classification, history and preparation of the aerogel were introduced. More attention was paid to the sol-gel method for preparing different kinds of aerogels, given its important role on bridging the synthetic parameters with the properties. At last, preparation of a novel single-component aerogel, design of a composite aerogel and industrial application of the aerogel were regarded as the research tendency of the aerogel state in the near future. Full article
(This article belongs to the Special Issue Advances in Sol-gel Derived Materials)
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<p>The distribution and transition of different states of matter in “density” <span class="html-italic">vs</span>. “enthalpy of the system” diagram.</p>
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<p>The classification of the aerogels.</p>
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<p>The number of papers published every year.</p>
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<p>Basic research scheme for the aerogel.</p>
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<p>General scheme of traditional sol-gel method.</p>
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<p>The scheme of the preparation of a carbonized RF (CRF) aerogel, activated CRF aerogel and diamond aerogel.</p>
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284 KiB  
Article
Effects of Hydrolysed Whey Proteins on the Techno-Functional Characteristics of Whey Protein-Based Films
by Markus Schmid, Lesley-Virgina Hinz, Florian Wild and Klaus Noller
Materials 2013, 6(3), 927-940; https://doi.org/10.3390/ma6030927 - 7 Mar 2013
Cited by 45 | Viewed by 7247
Abstract
Pure whey protein isolate (WPI)-based cast films are very brittle due to its strong formation of protein cross-linking of disulphide bonding, hydrogen bonding as well as hydrophobic and electrostatic interactions. However, this strong cross-linking is the reason for its final barrier performance. To [...] Read more.
Pure whey protein isolate (WPI)-based cast films are very brittle due to its strong formation of protein cross-linking of disulphide bonding, hydrogen bonding as well as hydrophobic and electrostatic interactions. However, this strong cross-linking is the reason for its final barrier performance. To overcome film brittleness of whey protein layers, plasticisers like glycerol are used. It reduces intermolecular interactions, increases the mobility of polymer chains and thus film flexibility can be achieved. The objective of this study was to investigate the influence of hydrolysed whey protein isolate (WPI) in whey protein isolate-based cast films on their techno-functional properties. Due to the fact, that the addition of glycerol is necessary but at the same time increases the free volume in the film leading to higher oxygen and water vapour permeability, the glycerol concentration was kept constant. Cast films with different ratios of hydrolysed and not hydrolysed WPI were produced. They were characterised in order to determine the influence of the lower molecular weight caused by the addition of hydrolysed WPI on the techno-functional properties. This study showed that increasing hydrolysed WPI concentrations significantly change the mechanical properties while maintaining the oxygen and water vapour permeability. The tensile and elastic film properties decreased significantly by reducing the average molecular weight whereas the yellowish coloration and the surface tension considerably increased. This study provided new data which put researchers and material developers in a position to tailor the characteristics of whey protein based films according to their intended application and further processing. Full article
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<p>Influence of hydrolysed whey protein isolate (WPI) content and film component ratio in denatured WPI-based films on Water Vapour Permeability.</p>
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<p>Influence of hydrolysed WPI content and film component ratio in denatured WPI-based films on Oxygen Permeability.</p>
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<p>Influence of hydrolysed WPI content and film component ratio in denatured WPI-based films on Tensile strength.</p>
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<p>Influence of hydrolysed WPI content and film component ratio in denatured WPI-based films on Young’s Modulus.</p>
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<p>Influence of hydrolysed WPI content and film component ratio in denatured WPI-based films on disperse part of surface energy.</p>
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<p>Influence of hydrolysed WPI content and film component ratio in denatured WPI-based films on polar part of surface energy.</p>
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<p>Influence of hydrolysed WPI content and film component ratio in denatured WPI-based films on yellow colouration.</p>
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1210 KiB  
Article
Covalently Bonded Chitosan on Graphene Oxide via Redox Reaction
by Karina Bustos-Ramírez, Ana L. Martínez-Hernández, Gonzalo Martínez-Barrera, Miguel De Icaza, Víctor M. Castaño and Carlos Velasco-Santos
Materials 2013, 6(3), 911-926; https://doi.org/10.3390/ma6030911 - 7 Mar 2013
Cited by 94 | Viewed by 11013
Abstract
Carbon nanostructures have played an important role in creating a new field of materials based on carbon. Chemical modification of carbon nanostructures through grafting has been a successful step to improve dispersion and compatibility in solvents, with biomolecules and polymers to form nanocomposites. [...] Read more.
Carbon nanostructures have played an important role in creating a new field of materials based on carbon. Chemical modification of carbon nanostructures through grafting has been a successful step to improve dispersion and compatibility in solvents, with biomolecules and polymers to form nanocomposites. In this sense carbohydrates such as chitosan are extremely valuable because their functional groups play an important role in diversifying the applications of carbon nanomaterials. This paper reports the covalent attachment of chitosan onto graphene oxide, taking advantage of this carbohydrate at the nanometric level. Grafting is an innovative route to modify properties of graphene, a two-dimensional nanometric arrangement, which is one of the most novel and promising nanostructures. Chitosan grafting was achieved by redox reaction using different temperature conditions that impact on the morphology and features of graphene oxide sheets. Transmission Electron Microscopy, Fourier Transform Infrared, Raman and Energy Dispersive spectroscopies were used to study the surface of chitosan-grafted-graphene oxide. Results show a successful modification indicated by the functional groups found in the grafted material. Dispersions of chitosan-grafted-graphene oxide samples in water and hexane revealed different behavior due to the chemical groups attached to the graphene oxide sheet. Full article
(This article belongs to the Special Issue Advances in Multifunctional Materials)
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<p>Transmission electron microscope (TEM) images of: (<b>a</b>) GEO, (<b>b</b>) CGEO1, (<b>c</b>) CGEO2 and (<b>d</b>) CGEO3 (see <a href="#materials-06-00911-t001" class="html-table">Table 1</a>).</p>
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<p>(<b>a</b>) Atomic force microscopy (AFM) image of chitosan acquired as is; (<b>b</b>) topography of chitosan; (<b>c</b>) AFM image of GEO; (<b>d</b>) topography of GEO; (<b>e</b>) AFM image of chitosan-grafted graphene oxide sheet and (<b>f</b>) topography of chitosan grafted graphene oxide sheet.</p>
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<p>Fourier transform infrared spectroscopy (FTIR) spectra of: (<b>a</b>) graphite; (<b>b</b>) GO; (<b>c</b>) GEO; (<b>d</b>–<b>f</b>) chitosan-grafted graphene oxide at different temperatures of treatment: (<b>d</b>) CGEO1; (<b>e</b>) CGEO2; (<b>f</b>) CGEO3 and (<b>g</b>) chitosan.</p>
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<p>Raman spectra of: (<b>a</b>) graphite; (<b>b</b>) GO; (<b>c</b>) GEO; (<b>d</b>–<b>f</b>) chitosan-grafted graphene oxide at different temperatures: (<b>d</b>) CGEO1; (<b>e</b>) CGEO2; (<b>f</b>) CGEO3.</p>
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<p>Dispersion study of: (<b>A</b>) water after sonication; (<b>B</b>) hexane after sonication; (<b>C</b>) water after sonication and 24 h kept at rest; (<b>D</b>) hexane after sonication and 24 h kept at rest; (<b>E</b>) UV-Vis spectra of samples dispersed in water after sonication; (<b>F</b>) UV-Vis spectra of samples dispersed in water after sonication and 24 h kept at rest: (<b>a</b>) graphite; (<b>b</b>) GO; (<b>c</b>) GEO; (<b>d</b>–<b>f</b>) chitosan-grafted graphene oxide at: (<b>d</b>) CGEO1; (<b>e</b>) CGEO2; (<b>f</b>) CGEO3.</p>
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<p>Reaction scheme of chitosan grafting onto graphene oxide.</p>
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289 KiB  
Article
Ultrafast Transient Spectroscopy of Polymer/Fullerene Blends for Organic Photovoltaic Applications
by Sanjeev Singh and Zeev Valy Vardeny
Materials 2013, 6(3), 897-910; https://doi.org/10.3390/ma6030897 - 6 Mar 2013
Cited by 18 | Viewed by 6622
Abstract
We measured the picoseconds (ps) transient dynamics of photoexcitations in blends of regio-regular poly(3-hexyl-thiophene) (RR-P3HT) (donors-D) and fullerene (PCBM) (acceptor-A) in an unprecedented broad spectral range of 0.25 to 2.5 eV. In D-A blends with maximum domain separation, such as RR-P3HT/PCBM, with (1.2:1) [...] Read more.
We measured the picoseconds (ps) transient dynamics of photoexcitations in blends of regio-regular poly(3-hexyl-thiophene) (RR-P3HT) (donors-D) and fullerene (PCBM) (acceptor-A) in an unprecedented broad spectral range of 0.25 to 2.5 eV. In D-A blends with maximum domain separation, such as RR-P3HT/PCBM, with (1.2:1) weight ratio having solar cell power conversion efficiency of ~4%, we found that although the intrachain excitons in the polymer domains decay within ~10 ps, no charge polarons are generated at their expense up to ~1 ns. Instead, there is a build-up of charge-transfer (CT) excitons at the D-A interfaces having the same kinetics as the exciton decay. The CT excitons dissociate into separate polarons in the D and A domains at a later time (>1 ns). This “two-step” charge photogeneration process may be typical in organic bulk heterojunction cells. We also report the effect of adding spin 1/2 radicals, Galvinoxyl on the ultrafast photoexcitation dynamics in annealed films of RR-P3HT/PCBM blend. The addition of Galvinoxyl radicals to the blend reduces the geminate recombination rate of photogenerated CT excitons. In addition, the photoexcitation dynamics in a new D-A blend of RR-P3HT/Indene C60 trisadduct (ICTA) has been studied and compared with the dynamics in RR-P3HT/PCBM. Full article
(This article belongs to the Special Issue Photovoltaic Materials)
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<p>(color on line) (<b>a</b>) Schematic diagram of nano-domains of polymer (donor) and fullerene (acceptor) depicted in bulk heterojunction organic photovoltaic blend; (<b>b</b>) Schematic molecular structures of the Regio Regular (RR)-P3HT polymer, 6,6-phenyl-C<sub>61</sub>-butyric acid methyl ester (PCBM), Indene C60 trisadduct (ICTA) and Galvinoxyl radical.</p>
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<p>(color on line) (<b>a</b>) The transient photomodulation spectrum of pristine RR-P3HT film at <span class="html-italic">t</span> = 150 fs and <span class="html-italic">t</span> = 100 ps, respectively. The exciton bands PA<sub>1</sub>, SE and PB are indicated; (<b>b</b>) The transient decay of PA<sub>1</sub> and PB bands up to t = 180 ps.</p>
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<p>(color on line) (<b>a</b>) The transient photomodulation spectrum of RR-P3HT/PCBM blend film at <span class="html-italic">t</span> = 0 and <span class="html-italic">t</span> = 300 ps, respectively; the exciton band PA<sub>1</sub>, and CT exciton bands CT<sub>1</sub> and CT<sub>2</sub> are indicated. The blue circles and line represent the background (BG) PA spectrum measured at <span class="html-italic">t</span> = −5 ps; (<b>b</b>) The transient decay of PA<sub>1</sub>, build-up dynamics of CT<sub>2</sub>, and the PB decay up to 180 ps. The line through the data points is a fit using the Förester resonant energy transfer (FRET) mechanism (see text); the same function also fits the CT<sub>2</sub> build-up dynamics.</p>
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<p>(color on line) (<b>a</b>) The transient photomodulation spectrum of RR-P3HT/PCBM blend film at <span class="html-italic">t</span> = 30 ps excited at 3.1 eV, normalized and subtracted from the spectrum at <span class="html-italic">t</span> = 0, that shows the two newly formed CT<sub>1</sub> and CT<sub>2</sub> bands; (<b>b</b>) Same as in (<b>a</b>) but at <span class="html-italic">t</span> = 0 and excited at 1.55 eV, which is below the gap of both polymer and fullerene constituents. The green circles and line represent the background (BG) PA spectrum measured at t = −5 ps.</p>
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<p>(color on line) The transient decays in RR-P3HT/PCBM (1.2:1) films mixed with 0%, 3% and 10% of Galvinoxyl impurities measured at: (<b>a</b>) 2.26 eV (PB) and (<b>b</b>) 1.3 eV (CT<sub>2</sub>).</p>
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<p>(color on line) (<b>a</b>) The transient photomodulation spectrum of RR-P3HT/ICTA blend at <span class="html-italic">t</span> = 1 ps and <span class="html-italic">t</span> = 200 ps, respectively excited at 3.1 eV; the PA bands PB, PA<sub>1</sub> and CT<sub>2</sub> are assigned; (<b>b</b>) The transient decay of PB (2.26 eV) and the decay of CT<sub>2</sub> (1.3 eV).</p>
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448 KiB  
Article
Electronic Two-Transition-Induced Enhancement of Emission Efficiency in Polymer Light-Emitting Diodes
by Ren-Ai Chen, Cong Wang, Sheng Li and Thomas F. George
Materials 2013, 6(3), 886-896; https://doi.org/10.3390/ma6030886 - 6 Mar 2013
Viewed by 5172
Abstract
With the development of experimental techniques, effective injection and transportation of electrons is proven as a way to obtain polymer light-emitting diodes (PLEDs) with high quantum efficiency. This paper reveals a valid mechanism for the enhancement of quantum efficiency in PLEDs. When an [...] Read more.
With the development of experimental techniques, effective injection and transportation of electrons is proven as a way to obtain polymer light-emitting diodes (PLEDs) with high quantum efficiency. This paper reveals a valid mechanism for the enhancement of quantum efficiency in PLEDs. When an external electric field is applied, the interaction between a negative polaron and triplet exciton leads to an electronic two-transition process, which induces the exciton to emit light and thus improve the emission efficiency of PLEDs. Full article
(This article belongs to the Special Issue Conjugated Polymers 2012)
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<p>Lattice configuration of the triplet exciton (<b>a</b>) and negative polaron (<b>b</b>), where the unit of the vertical axis is Angstroms; and schematic graphic (<b>c</b>) of the collision of the negative polaron (P) and triplet exciton (T) inside the conjugated polymer layer. Initially, the triplet exciton stays in the middle of the polymer chain, and the polaron starts from the right side of the chain.</p>
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<p>Evolution of the lattice configuration during the process of the interaction between the negative polaron and triplet exciton under an external electric field.</p>
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<p>Schematic diagram of the electron population during the electronic two-transition process.</p>
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<p>Three dimensional (3D) column chart of the evolution of the electron population of four energy levels of the negative polaron and triplet exciton for the time points of 0, 200, 500 and 900 ps.</p>
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<p>Time evolution of the fluorescence spectra after normalization. The red round points (685 nm) represent light emitted by the transformation of the triplet exciton, while the blue triangular points (538 nm) represent the light emitted by the decay of the singlet exciton.</p>
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<p>Net charge variation of the triplet exciton within the first 100 ps (the unit on the vertical axis is +|e|).</p>
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<p>Evolution of the electroluminescent internal quantum efficiency, including the decay of the singlet exciton and emission from the two-transition process of the triplet exciton.</p>
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1867 KiB  
Article
An Efficient Local Molecular Dynamics Polymerization Simulation Combined with an Ab Initio MO Method
by Peng Xie, Yuuichi Orimoto and Yuriko Aoki
Materials 2013, 6(3), 870-885; https://doi.org/10.3390/ma6030870 - 6 Mar 2013
Cited by 7 | Viewed by 7549
Abstract
A new local ab initio molecular dynamics method, namely elongation molecular dynamics (ELG-MD) is proposed for highly efficient simulations of aperiodic polymer systems. ELG-MD combines the elongation method (ELG) with the Gear predictor corrector (GPC) algorithm of molecular dynamics simulation. In this method, [...] Read more.
A new local ab initio molecular dynamics method, namely elongation molecular dynamics (ELG-MD) is proposed for highly efficient simulations of aperiodic polymer systems. ELG-MD combines the elongation method (ELG) with the Gear predictor corrector (GPC) algorithm of molecular dynamics simulation. In this method, the local gradients acting on the atom’s nucleus in the active region are calculated by the ELG method while the equations of the nucleus’s motion are solved by the GPC algorithm. In this work, the first application of this ELG-MD method is described to investigate the stable conformation of polyglycine with surrounding water molecules. The water effects on the structure of polyglycine are examined. The ELG-MD simulations show that the formation of the polyglycine helix is strongly induced by the hydrogen bonds observed in two types of H-bond rings. Full article
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<p>Flowchart of the elongation method illustrated using polyglycine with water molecules. The canonical molecular orbital (CMO) and region localized molecular orbital (RLMO) indicate canonical and regional localized molecular orbitals, respectively.</p>
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<p>The flowchart of the elongation molecular dynamics (ELG-MD) method. The “Energy and Density (B + M)” means that the energy and density of the B + M region are obtained with the contribution from the A region.</p>
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<p>Polyglycine (Gly)<sub>14</sub> in β-strand conformation with 14 water molecules. (Gly)<sub>14</sub> are divided into A, B, M<sub>1</sub>, M<sub>2</sub> and M<sub>3</sub> regions for the ELG-MD procedures. The notations A and B do not correspond to those in <a href="#materials-06-00870-f002" class="html-fig">Figure 2</a>.</p>
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<p>(<b>a</b>) The structure of the A, B, M<sub>1</sub> and M<sub>2</sub> regions of (Gly)<sub>14</sub> in a quasi-α-helix conformation as the initial structure for ELG-MD simulation. Panels (<b>b</b>) and (<b>c</b>) show two types of H-bond ring. The dotted lines in the panels denote hydrogen bonds.</p>
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<p>The initial structure of the M<sub>1</sub>, M<sub>2</sub> and M<sub>3</sub> regions (atoms from 62 to 143). C60 and O61 belong to the B region.</p>
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<p>Fluctuations of the Hartree-Fock energy of (Gly)<sub>14</sub> with 14 water molecules in the simulation at 298.15 K: (<b>a</b>) ELG-MD simulation; (<b>b</b>) conventional <span class="html-italic">ab initio</span> MD simulation.</p>
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<p>(<b>a</b>) Root-mean-square deviation (RMSD) of the molecular structure between ELG-MD and conventional <span class="html-italic">ab initio</span> MD with fixing of the same atoms; (<b>b</b>) Superimposed structures at 500 fs. (Red: conventional AIMD. Blue: ELG-MD).</p>
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<p>Fluctuations of the H-bond distances between peptide and water molecules in the interacting space (5 ps ELG-MD simulation). The numbering of the atoms is shown in <a href="#materials-06-00870-f005" class="html-fig">Figure 5</a>. M<sub>1</sub>, M<sub>2</sub> and M<sub>3</sub> denote the M<sub>1</sub> region, M<sub>2</sub> region and M<sub>3</sub> region shown in <a href="#materials-06-00870-f005" class="html-fig">Figure 5</a> respectively. More details of the H-bond distances in Panel b and h are shown in <a href="#materials-06-00870-f009" class="html-fig">Figure 9</a> and <a href="#materials-06-00870-f010" class="html-fig">Figure 10</a>, respectively.</p>
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<p>Snapshot of H-bond rings in the M<sub>1</sub> region at (<b>a</b>) 3330 fs and (<b>b</b>) 4300 fs.</p>
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<p>Snapshot at 5000fs of (<b>a</b>) entire peptide (Gly)<sub>14</sub>. Atoms from 1 to 61 belong to the frozen region; atoms from 62 to 143 belong to the active region; (<b>b</b>) Interacting space (M<sub>1</sub>, M<sub>2</sub> and M<sub>3</sub>); and (<b>c</b>) H-bond.</p>
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937 KiB  
Article
From Powders to Dense Metal Parts: Characterization of a Commercial AlSiMg Alloy Processed through Direct Metal Laser Sintering
by Diego Manfredi, Flaviana Calignano, Manickavasagam Krishnan, Riccardo Canali, Elisa Paola Ambrosio and Eleonora Atzeni
Materials 2013, 6(3), 856-869; https://doi.org/10.3390/ma6030856 - 6 Mar 2013
Cited by 286 | Viewed by 16876
Abstract
In this paper, a characterization of an AlSiMg alloy processed by direct metal laser sintering (DMLS) is presented, from the analysis of the starting powders, in terms of size, morphology and chemical composition, through to the evaluation of mechanical and microstructural properties of [...] Read more.
In this paper, a characterization of an AlSiMg alloy processed by direct metal laser sintering (DMLS) is presented, from the analysis of the starting powders, in terms of size, morphology and chemical composition, through to the evaluation of mechanical and microstructural properties of specimens built along different orientations parallel and perpendicular to the powder deposition plane. With respect to a similar aluminum alloy as-fabricated, a higher yield strength of about 40% due to the very fine microstructure, closely related to the mechanisms involved in this additive process is observed. Full article
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Graphical abstract

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<p>The scanning strategy employed in this work: (<b>a</b>) the parameters considered with different power and scanning speed; (<b>b</b>) the non-contour area of each layer is rotated of 67° in comparison to the previous one.</p>
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<p>The four different orientations considered for producing DMLS aluminum alloy specimens.</p>
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<p>The as-received aluminum alloy powder observed by field emission scanning electron microscope (FESEM).</p>
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<p>Particle size distribution of as-received aluminum alloy powder.</p>
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<p>(<b>a</b>) Typical stress-strain curves for aluminum alloy DMLS specimens built along four different orientations; (<b>b</b>) yield strength and Young’s modulus evaluation for the representative curve of a specimen along <span class="html-italic">z</span> axis.</p>
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<p>Optical microscope images of an aluminum alloy DMLS sample after etching with Weck’s reagent: (<b>a</b>) a section along the build direction (<span class="html-italic">z</span> axis); (<b>b</b>) a section parallel to the powder deposition plane (<span class="html-italic">xy</span>-plane).</p>
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<p>Optical microscope images after Weck’s etching showing: (<b>a</b>) the presence of pores and at a higher magnification; (<b>b</b>) the shape of a melt pool with its contour<b>.</b></p>
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<p>FESEM images of an aluminum alloy DMLS sample after etching with Weck’s reagent, sectioned along the <span class="html-italic">z</span> axis: (<b>a</b>) mp<sub>1</sub> and mp<sub>2</sub> are areas of two adjacent melt pools, while the region delimited by the white lines correspond to the melt pool contour (mpc); (<b>b</b>–<b>d</b>) the three regions at higher magnifications. In the inset, it possible to observe the nanometric grain size.</p>
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<p>FESEM images of an aluminum alloy DMLS fracture surface at increasing magnifications: (<b>a</b>–<b>d</b>) it is covered by sub-micrometric voids and dimples with a nanometric thickness.</p>
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2290 KiB  
Article
Multifunctional Cement Composites Strain and Damage Sensors Applied on Reinforced Concrete (RC) Structural Elements
by Francisco Javier Baeza, Oscar Galao, Emilio Zornoza and Pedro Garcés
Materials 2013, 6(3), 841-855; https://doi.org/10.3390/ma6030841 - 6 Mar 2013
Cited by 148 | Viewed by 9100
Abstract
In this research, strain-sensing and damage-sensing functional properties of cement composites have been studied on a conventional reinforced concrete (RC) beam. Carbon nanofiber (CNFCC) and fiber (CFCC) cement composites were used as sensors on a 4 m long RC beam. Different casting conditions [...] Read more.
In this research, strain-sensing and damage-sensing functional properties of cement composites have been studied on a conventional reinforced concrete (RC) beam. Carbon nanofiber (CNFCC) and fiber (CFCC) cement composites were used as sensors on a 4 m long RC beam. Different casting conditions (in situ or attached), service location (under tension or compression) and electrical contacts (embedded or superficial) were compared. Both CNFCC and CFCC were suitable as strain sensors in reversible (elastic) sensing condition testing. CNFCC showed higher sensitivities (gage factor up to 191.8), while CFCC only reached gage factors values of 178.9 (tension) or 49.5 (compression). Furthermore, damage-sensing tests were run, increasing the applied load progressively up to the RC beam failure. In these conditions, CNFCC sensors were also strain sensitive, but no damage sensing mechanism was detected for the strain levels achieved during the tests. Hence, these cement composites could act as strain sensors, even for severe damaged structures near to their collapse. Full article
(This article belongs to the Special Issue Advances in Multifunctional Materials)
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<p>(<b>a</b>) Three dimensional (3D) view of the sensors’ distribution; also, loading and support conditions are represented; (<b>b</b>) Cross section dimensions and steel rebar’s arrangement; (<b>c</b>) Sensors’ location and nomenclature (NF = carbon nanofiber; CF = carbon fiber; G = strain gage).</p>
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<p>Electrical contacts: 1 and 2 are for current input; 3 and 4 for voltage measure.</p>
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<p>Loading configuration during: (<b>a</b>) strain-sensing tests; (<b>b</b>) damage-sensing tests.</p>
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<p>Electrical resistance and bending moment in the middle cross section <span class="html-italic">versus</span> time for sensors located on the compression side of the RC beam and with different conductive admixtures: (<b>a</b>) 1% CF10; (<b>b</b>) 2% CNF.</p>
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<p>Electrical resistance <span class="html-italic">versus</span> longitudinal strain for sensors located on the compression side of the RC beam and with 1% CF10 or 2% CNF additions, respectively.</p>
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<p>Comparison of fractional resistance-strain curves of 1% CF10 sensors under different strain conditions: compression (left curve) or tension (right curve).</p>
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<p>Class of sensor according to its dimensions: (<b>a</b>) 2 × 2 × 8 cm³; (<b>b</b>) 0.7 × 20 × 8 cm³.</p>
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<p>Comparison of 2% CNF (addition by cement mass) sensors: dimensions influence 2 × 2 × 8 cm³ <span class="html-italic">vs.</span> 0.7 × 20 × 8 cm³. (<b>a</b>) Electrical resistance and bending moment in the middle cross section <span class="html-italic">vs.</span> time for the 0.7 × 20 × 8 cm³ sensor; (<b>b</b>) resistance fractional change <span class="html-italic">vs.</span> longitudinal strain curves comparison between sensors NF2 and NF4.</p>
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<p>Comparison of 1% CF10 sensors with different thicknesses (0.5 mm and 2 mm).</p>
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<p>Damage sensing test for sensors NF2 (<b>a</b>) and NF4 (<b>b</b>), Resistance fractional change and longitudinal strain at sensor’s location are represented, both <span class="html-italic">vs.</span> time.</p>
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<p>Resistance fractional change <span class="html-italic">vs.</span> strain for sensor NF2 damage sensing test.</p>
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304 KiB  
Review
Dye Sensitizers for Photodynamic Therapy
by Alexandra B. Ormond and Harold S. Freeman
Materials 2013, 6(3), 817-840; https://doi.org/10.3390/ma6030817 - 6 Mar 2013
Cited by 710 | Viewed by 23999
Abstract
Photofrin® was first approved in the 1990s as a sensitizer for use in treating cancer via photodynamic therapy (PDT). Since then a wide variety of dye sensitizers have been developed and a few have been approved for PDT treatment of skin and [...] Read more.
Photofrin® was first approved in the 1990s as a sensitizer for use in treating cancer via photodynamic therapy (PDT). Since then a wide variety of dye sensitizers have been developed and a few have been approved for PDT treatment of skin and organ cancers and skin diseases such as acne vulgaris. Porphyrinoid derivatives and precursors have been the most successful in producing requisite singlet oxygen, with Photofrin® still remaining the most efficient sensitizer (quantum yield = 0.89) and having broad food and drug administration (FDA) approval for treatment of multiple cancer types. Other porphyrinoid compounds that have received approval from US FDA and regulatory authorities in other countries include benzoporphyrin derivative monoacid ring A (BPD-MA), meta-tetra(hydroxyphenyl)chlorin (m-THPC), N-aspartyl chlorin e6 (NPe6), and precursors to endogenous protoporphyrin IX (PpIX): 1,5-aminolevulinic acid (ALA), methyl aminolevulinate (MAL), hexaminolevulinate (HAL). Although no non-porphyrin sensitizer has been approved for PDT applications, a small number of anthraquinone, phenothiazine, xanthene, cyanine, and curcuminoid sensitizers are under consideration and some are being evaluated in clinical trials. This review focuses on the nature of PDT, dye sensitizers that have been approved for use in PDT, and compounds that have entered or completed clinical trials as PDT sensitizers. Full article
(This article belongs to the Special Issue Advances in Colorants)
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<p>Examples of psoralen photosensitizers.</p>
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<p>Basic structures of porphyrinoid photosensitizers.</p>
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<p>Modified Jablonski diagram showing Type II sensitization process.</p>
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<p>Schematic representation of photodynamic therapy (PDT) treatment of a malignant tumor [<a href="#B7-materials-06-00817" class="html-bibr">7</a>].</p>
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<p>Triplet (<sup>3</sup>O<sub>2</sub>) and singlet (<sup>1</sup>O<sub>2</sub>) states of oxygen.</p>
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<p>Synthesis of hematoporphyrin derivative (HpD) from heme.</p>
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<p>Molecular structures of some second generation porphyrins.</p>
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<p>Pathway for heme biosynthesis.</p>
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<p>Molecular structures of methyl aminolevulinate (MAL) and Hexaminolevulinate (HAL).</p>
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<p>Examples of chlorins evaluated for PDT use.</p>
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<p>Formation of <span class="html-italic">meta</span>-tetra(hydroxyphenyl)chlorin (m-THPC) by tosylhydrazine reduction of <span class="html-italic">meta</span>-tetra(hydroxyphenyl)porphyrin (<span class="html-italic">m</span>-THPP).</p>
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<p>Molecular structure of 2-(1-hexyloxyethyl)-2-devinyl pyropheophorbide (HPPH).</p>
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<p>Examples of pheophorbide sensitizers for PDT use.</p>
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<p>Molecular structure of a texaphyrin sensitizer.</p>
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<p>Examples of phthalocyanine PDT sensitizers.</p>
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<p>Example of an anthraquinone PDT sensitizer.</p>
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<p>Examples of phenothiazine PDT sensitizers.</p>
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<p>Examples of xanthene PDT sensitizers.</p>
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<p>Example of a merocyanine PDT sensitizer.</p>
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<p>Example of a curcuminoid PDT sensitizer.</p>
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757 KiB  
Article
Characterization and Stability of Tanshinone IIA Solid Dispersions with Hydroxyapatite
by Xiaopan Wang, Li Li, Wei Huo, Lulu Hou, Zhiying Zhao and Weiguang Li
Materials 2013, 6(3), 805-816; https://doi.org/10.3390/ma6030805 - 6 Mar 2013
Cited by 21 | Viewed by 5878
Abstract
Solid dispersions of tanshinone IIA (TanIIA) using hydroxyapatite (HAp) as the dispersing carrier (TanIIA-HAp SDs) were prepared by the solvent evaporation method. The formed solid dispersions were characterized by scanning electron microscopy (SEM), differential scanning calorimetry analysis (DSC), X-ray powder diffraction (XRPD) and [...] Read more.
Solid dispersions of tanshinone IIA (TanIIA) using hydroxyapatite (HAp) as the dispersing carrier (TanIIA-HAp SDs) were prepared by the solvent evaporation method. The formed solid dispersions were characterized by scanning electron microscopy (SEM), differential scanning calorimetry analysis (DSC), X-ray powder diffraction (XRPD) and Fourier transforms infrared (FTIR) spectroscopy. The in vitro dissolution rate and the stability of TanIIA-HAp SDs were also evaluated. DSC and XRPD showed that TanIIA was changed from a crystalline to an amorphous form. FTIR suggested the presence of interactions between TanIIA and HAp in solid dispersions. The result of an in vitro dissolution study showed that the dissolution rate of TanIIA-HAp SDs was nearly 7.11-folds faster than free TanIIA. Data from stability studies for over one year of TanIIA-HAp SDs performed under room temperature revealed no significant differences in drug content and dissolution behavior. All these results indicated that HAp may be a promising carrier for improving the oral absorption of TanIIA. Full article
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<p>The dissolution profiles of tanshinone IIA (TanIIA) and solid dispersions (SDs) at different TanIIA/HAp (hydroxyapatite) ratios of 1:3, 1:5, 1:7, 1:9 and the 1:9 physical mixtures. Each point represents the mean ± SD (<span class="html-italic">n</span> = 3).</p>
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<p>Scanning electron microscopy (SEM) photomicrographs of TanIIA (<b>A</b>) and 1:9 (w/w) SDs (<b>B</b>).</p>
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<p>Differential scanning calorimetry (DSC) curves of TanIIA (<b>A</b>); hydroxyapatite (HAp) (<b>B</b>); 1:9 (w/w) physical mixtures (<b>C</b>) and 1:9 (w/w) SDs (<b>D</b>).</p>
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<p>The X-ray powder diffractograms: TanIIA (<b>A</b>); HAp (<b>B</b>); 1:9 (w/w) physical mixtures (<b>C</b>) and 1:9 (w/w) SDs (<b>D</b>).</p>
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<p>Fourier transform infrared (FTIR) spectra of TanIIA (<b>A</b>); HAp (<b>B</b>); 1:9 physical mixtures (<b>C</b>) and 1:9 SDs (<b>D</b>).</p>
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<p>The dissolution rate of TanIIA in 1 h from different samples.</p>
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432 KiB  
Article
Influence of N2 Partial Pressure on Structure and Mechanical Properties of TiAlN/Al2O3 Multilayers
by Jingyue Yan, Lei Dong, Chongkuan Gao, Ning Wang and Dejun Li
Materials 2013, 6(3), 795-804; https://doi.org/10.3390/ma6030795 - 28 Feb 2013
Cited by 5 | Viewed by 5719
Abstract
TiAlN/Al2O3 multilayers with different Ar/N2 ratios were deposited on Si substrates in different N2 partial pressure by magnetron sputtering. The crystalline and multilayer structures of the multilayers were determined by a glancing angle X-ray diffractometer (XRD). A nanoindenter [...] Read more.
TiAlN/Al2O3 multilayers with different Ar/N2 ratios were deposited on Si substrates in different N2 partial pressure by magnetron sputtering. The crystalline and multilayer structures of the multilayers were determined by a glancing angle X-ray diffractometer (XRD). A nanoindenter was used to evaluate the hardness, the elastic modulus and scratch scan of the multilayers. The chemical bonding was investigated by a X-ray Photoelectron Spectroscopy (XPS). The maximum hardness (36.3 GPa) and elastic modulus (466 GPa) of the multilayers was obtained when Ar/N2 ratio was 18:1. The TiAlN/Al2O3 multilayers were crystallized with orientation in the (111) and (311) crystallographic planes. The multilayers displayed stably plastic recovery in different Ar/N2 ratios. The scratch scan and post scan surface profiles of TiAlN/Al2O3 multilayers showed the highest critical fracture load (Lc) of 53 mN for the multilayer of Ar/N2 = 18:1. It indicated that the multilayer had better practical adhesion strength and fracture resistance. Full article
(This article belongs to the Special Issue Advances in Multifunctional Materials)
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<p>High resolution X-ray reflectivity (XRR) curve of TiAlN/Al<sub>2</sub>O<sub>3</sub> multilayer (<span class="html-italic">Λ</span> = 10 nm).</p>
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<p>X-ray diffractometer (XRD) patterns of TiAlN/Al<sub>2</sub>O<sub>3 </sub>multilayers at different Ar/N<sub>2</sub> ratios.</p>
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<p>High resolution X-ray Photoelectron Spectroscopy (XPS) spectra of Ti<sub>2p</sub>, N<sub>1s</sub>, Al<sub>2p</sub>, O<sub>1s</sub> electrons for the TiAlN/Al<sub>2</sub>O<sub>3</sub> multilayer.</p>
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<p>Hardness and elastic modulus of TiAlN/Al<sub>2</sub>O<sub>3 </sub>multilayers at different Ar/N<sub>2</sub> ratios.</p>
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<p>Residual stresses of TiAlN/Al<sub>2</sub>O<sub>3 </sub>multilayers at different Ar/N<sub>2</sub> ratios.</p>
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<p>Typical load <span class="html-italic">vs</span>. nano-indenter displacement curve of TiAlN/Al<sub>2</sub>O<sub>3</sub> multilayers with different Ar/N<sub>2</sub> ratios</p>
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<p>Surface profiles of the scratch-scan on TiAlN/Al<sub>2</sub>O<sub>3</sub> multilayers with different Ar/N<sub>2</sub> ratios.</p>
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1026 KiB  
Article
Biosynthesis and Characterization of Nanocellulose-Gelatin Films
by Siriporn Taokaew, Sutasinee Seetabhawang, Pongpun Siripong and Muenduen Phisalaphong
Materials 2013, 6(3), 782-794; https://doi.org/10.3390/ma6030782 - 28 Feb 2013
Cited by 97 | Viewed by 10786
Abstract
A nanocellulose-gelatin (bacterial cellulose gelatin (BCG)) film was developed by a supplement of gelatin, at a concentration of 1%–10% w/v, in a coconut-water medium under the static cultivation of Acetobacter xylinum. The two polymers exhibited a certain degree of miscibility. The BCG [...] Read more.
A nanocellulose-gelatin (bacterial cellulose gelatin (BCG)) film was developed by a supplement of gelatin, at a concentration of 1%–10% w/v, in a coconut-water medium under the static cultivation of Acetobacter xylinum. The two polymers exhibited a certain degree of miscibility. The BCG film displayed dense and uniform homogeneous structures. The Fourier transform infrared spectroscopy (FTIR) results demonstrated interactions between the cellulose and gelatin. Incorporation of gelatin into a cellulose nanofiber network resulted in significantly improved optical transparency and water absorption capacity of the films. A significant drop in the mechanical strengths and a decrease in the porosity of the film were observed when the supplement of gelatin was more than 3% (w/v). The BCG films showed no cytotoxicity against Vero cells. Full article
(This article belongs to the Special Issue Advances in Cellulosic Materials)
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<p>The overview (top) and high magnification (bottom) photomicrographs of the bacterial cellulose (BC) and bacterial cellulose gelatin (BCG) films: (<b>a</b>) BC; (<b>b</b>) BCG-3 and (<b>c</b>) BCG-10.</p>
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<p>Optical photographs of the BC, BCG and gelatin films: (<b>a</b>) BC; (<b>b</b>) BCG-1; (<b>c</b>) BCG-3; (<b>d</b>) BCG-5; (<b>e</b>) BCG-7; (<b>f</b>) BCG-10 and (<b>g</b>) gelatin.</p>
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<p>The Fourier transform infrared spectroscopy (FTIR) spectra of the BC, BCG and gelatin films: (<b>a</b>) BC; (<b>b</b>) BCG-1; (<b>c</b>) BCG-3; (<b>d</b>) BCG-5; (<b>e</b>) BCG-7; (<b>f</b>) BCG-10 and <b>(g)</b> gelatin powder.</p>
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<p>The X-ray diffractometer (XRD) patterns and crystallinity (%) of the BC and BCG films: (<b>a</b>) BC; (<b>b</b>) BCG-3; (<b>c</b>) BCG-5 and (<b>d</b>) BCG-7.</p>
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<p>The tensile strength (<b>a</b>) and the elongation at break (<b>b</b>) of the BC and BCG films as a function of gelatin concentration in culture medium: dried film (●); reswollen film (■).</p>
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<p>The water absorption capacity of the BC and BCG films as a function of gelatin concentration in culture medium.</p>
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2725 KiB  
Review
“Smart” Materials Based on Cellulose: A Review of the Preparations, Properties, and Applications
by Xiaoyun Qiu and Shuwen Hu
Materials 2013, 6(3), 738-781; https://doi.org/10.3390/ma6030738 - 28 Feb 2013
Cited by 427 | Viewed by 28276
Abstract
Cellulose is the most abundant biomass material in nature, and possesses some promising properties, such as mechanical robustness, hydrophilicity, biocompatibility, and biodegradability. Thus, cellulose has been widely applied in many fields. “Smart” materials based on cellulose have great advantages—especially their intelligent behaviors in [...] Read more.
Cellulose is the most abundant biomass material in nature, and possesses some promising properties, such as mechanical robustness, hydrophilicity, biocompatibility, and biodegradability. Thus, cellulose has been widely applied in many fields. “Smart” materials based on cellulose have great advantages—especially their intelligent behaviors in reaction to environmental stimuli—and they can be applied to many circumstances, especially as biomaterials. This review aims to present the developments of “smart” materials based on cellulose in the last decade, including the preparations, properties, and applications of these materials. The preparations of “smart” materials based on cellulose by chemical modifications and physical incorporating/blending were reviewed. The responsiveness to pH, temperature, light, electricity, magnetic fields, and mechanical forces, etc. of these “smart” materials in their different forms such as copolymers, nanoparticles, gels, and membranes were also reviewed, and the applications as drug delivery systems, hydrogels, electronic active papers, sensors, shape memory materials and smart membranes, etc. were also described in this review. Full article
(This article belongs to the Special Issue Advances in Cellulosic Materials)
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<p>Molecular structure of cellulose.</p>
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<p>Examples of “smart” materials based on cellulose and their possible applications.</p>
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<p>Preparation strategies of “smart” materials based on cellulose.</p>
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<p>Cylindrical-shaped PNIPAm-CMC full interpenetrating networks (IPN) hydrogels were prepared by the simultaneous radical crosslinking of CMC and PNIPAm polymer chains. The CMC/PNIPAm weight ratio was 5.0/95.0 and the hydrogels were prepared at 18 °C. PNIPAm: Poly(<span class="html-italic">N</span>-isopropylacrylamide); CMC: carboxymethyl cellulose. Reprinted with permission from [<a href="#B30-materials-06-00738" class="html-bibr">30</a>]. Copyright 2010 Springer.</p>
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<p>General mechanism for radical crosslinking of Na-Alg/CMC mixture in the presence of <span class="html-italic">N</span>,<span class="html-italic">N</span>′-methylene-<span class="html-italic">bis</span>-acrylamide (MBA). Reprinted with permission from [<a href="#B46-materials-06-00738" class="html-bibr">46</a>]. Copyright 2006 Elsevier.</p>
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<p>Synthesis route of microgels prepared from hydroxypropyl cellulose (HPC) [<a href="#B33-materials-06-00738" class="html-bibr">33</a>].</p>
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<p>Synthesis route of the poly(<span class="html-italic">N</span>,<span class="html-italic">N</span>-dimethyl aminoethyl methacrylate) (PDMAEMA) and poly(4-vinyl pyridine) (P4VP) grafted HPC via atom transfer radical polymerization (ATRP) [<a href="#B53-materials-06-00738" class="html-bibr">53</a>,<a href="#B54-materials-06-00738" class="html-bibr">54</a>].</p>
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<p>Schematic diagram illustrating the processes for the preparation of the PNIPAm-<span class="html-italic">g</span>-HPC copolymers via ATRP of NIPAm from the alkyl bromide-functionalized HPC macroinitiator and the formation of stimuli-responsive hydrogels via crosslinking. Reprinted with permission from [<a href="#B55-materials-06-00738" class="html-bibr">55</a>]. Copyright 2010 American Chemical Society.</p>
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<p>Synthesis route of the thiolated HPC derivatives. Reprinted with permission from [<a href="#B58-materials-06-00738" class="html-bibr">58</a>]. Copyright 2010 Royal Society of Chemistry.</p>
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<p>Synthesis route of temperature-responsive hydrogels based on HEC. Reprinted with permission from [<a href="#B60-materials-06-00738" class="html-bibr">60</a>]. Copyright 2010 Taylor &amp; Francis.</p>
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<p>Synthesis route of cellulose 2-[(4-methyl-2-oxo-2H-chromen-7-yl) oxy] acetates (3a-d) and cellulose 2-[(4-methyl-2-oxo-2H-chromen-7-yl) oxy] acetate [4-(<span class="html-italic">N</span>,<span class="html-italic">N</span>,<span class="html-italic">N</span>-trimethylamonium) chloride] butyrates (5a-d) via <span class="html-italic">in situ</span> activation of 2-[(4-methyl-2-oxo-2H-chromen-7-yl) oxy] acetic acid (2) and (3-carboxypropyl) trimethylammonium chloride (4) with <span class="html-italic">N</span>,<span class="html-italic">N</span>-carbonyldiimidazole (CDI) in DMAc/LiCl. Reprinted with permission from [<a href="#B67-materials-06-00738" class="html-bibr">67</a>]. Copyright 2012 Springer.</p>
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<p>Synthesis route of pH-responsive CNCs (carboxylated CNCs and amine-functionalized CNCs). Reprinted with permission from [<a href="#B72-materials-06-00738" class="html-bibr">72</a>]. Copyright 2012 American Chemical Society.</p>
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<p>Synthesis route of nanoparticles with photocleavable PS grafts. Reprinted with permission from [<a href="#B73-materials-06-00738" class="html-bibr">73</a>]. Copyright 2012 Royal Society of Chemistry.</p>
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<p>(<b>a</b>) Schematic of cellulose-PPy nanocomposite fabrication process; (<b>b</b>) Fabricated flexible humidity and temperature sensor. Reprinted with permission from [<a href="#B92-materials-06-00738" class="html-bibr">92</a>]. Copyright 2010 Elsevier.</p>
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<p>TEM images of dried dispersion of cellulose nanocrystals derived from (<b>a</b>) tunicate; (<b>b</b>) bacterial; (<b>c</b>) ramie; (<b>d</b>) sisal. Reprinted with permission from [<a href="#B69-materials-06-00738" class="html-bibr">69</a>]. Copyright 2010 American Chemical Society.</p>
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<p>Temperature dependence of <sup>1</sup>H NMR spectra of HPC-<span class="html-italic">g</span>-PDMAEMA solutions in D<sub>2</sub>O at pH (<b>a</b>) 3.0; (<b>b</b>) 8.1; and (<b>c</b>) 12.3. Reprinted with permission from [<a href="#B53-materials-06-00738" class="html-bibr">53</a>]. Copyright 2010 American Chemical Society.</p>
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<p>Left: SEM images of freeze-dried gels; Right: (<b>A</b>) Equilibrium swelling degree (SWeq) <span class="html-italic">vs.</span> temperature; (<b>B</b>) Temperature of the volume phase transition <span class="html-italic">T</span><sub>v</sub> for HPC/PNIPAm-IPN having different composition. (<b>a</b>) PNIPAm; (<b>b</b>) HPC/PNIPAm interpenetrated network (composition of 53.7/46.3 wt/wt); (<b>c</b>) HPC. Reprinted with permission from [<a href="#B56-materials-06-00738" class="html-bibr">56</a>]. Copyright 2004 Elsevier.</p>
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<p>Schematic diagram showing ideal particle structure of drug carriers with temperature- and pH-responsive shells [<a href="#B108-materials-06-00738" class="html-bibr">108</a>].</p>
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<p>Partition coefficient of vitamin B12 into a composite membrane with 30 wt % of 1:0.4 particles (<b>A</b>) In 0.1 mM KCl at varied temperature; (<b>B</b>) In 0.15 M PBS with varied pH values at 28 °C; (<b>C</b>) Schematic illustration of the permeation model for a composite membrane containing temperature- and pH-responsive nanoparticles. Reprinted with permission from [<a href="#B84-materials-06-00738" class="html-bibr">84</a>]. Copyright 2003 Elsevier.</p>
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<p>Profiles of insulin delivery across a membrane in response to glucose steps (50 to 200 to 400 to 50 mg/dL) in pH 7.4 PBS (10 mM/0.15 M NaCl) at 37 °C. The membrane consisted of 1.5 mg of GOD/0.43 mg of catalase and 35 wt % of the nanoparticles with a NIPAm:MAA molar ratio of 1:1. Reprinted with permission from [<a href="#B85-materials-06-00738" class="html-bibr">85</a>]. Copyright 2002 Elsevier.</p>
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<p>(<b>A</b>) Effects of pH on the swelling behaviors of QC/CMC hydrogels in buffer solutions; (<b>B</b>) Swelling ratio of hydrogels in different salt solutions (0.01 M): NaCl, CaCl<sub>2</sub>, and FeCl<sub>3</sub>; and (<b>C</b>) Schematic illustrations of the structures of QC/CMC hydrogels: (<b>a</b>) Gel31; (<b>b</b>) Gel32; and (<b>c</b>) Gel13. Reprinted with permission from [<a href="#B44-materials-06-00738" class="html-bibr">44</a>]. Copyright 2011 American Chemical Society.</p>
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<p>Proposed rapidly switchable water-sensitive shape-memory mechanism for the cellulose nanowhiskers/PUs comprising a cellulose nanowhiskers percolation network in an elastomeric matrix. Reprinted with permission from [<a href="#B117-materials-06-00738" class="html-bibr">117</a>]. Copyright 2012 Royal Society of Chemistry.</p>
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<p>Deflection and back–forth swing images at 303 K under various applied voltages of the gel: (<b>a</b>) E = 0 V/mm; (<b>b</b>) E = 500 V/mm; (<b>c</b>) E = 525 V/mm; and (<b>d</b>) E = 550 V/mm. Note: The polarity of the electrode on the left and right hand sides are always GND and positive, respectively. Size of the gel sample: 16.5 mm of length, 1 mm of thickness, 3 mm of width, and 0.0309 g of weight. Reprinted with permission from [<a href="#B100-materials-06-00738" class="html-bibr">100</a>]. Copyright 2012 Elsevier.</p>
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<p>(<b>A</b>) Temperature-sensing characteristics at 70% RH; (<b>B</b>) Humidity sensing characteristics of cellulose-PPy nanocomposite; (<b>C</b>) Capacitance of cellulose-PPy nanocomposite sensor as a function of temperature and humidity. Reprinted with permission from [<a href="#B92-materials-06-00738" class="html-bibr">92</a>]. Copyright 2010 Elsevier.</p>
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<p>Various characteristic conformational states of PSBMA polymer chains in (<b>a</b>) DI water; and (<b>b</b>) NaCl solution; (<b>c</b>) Reversible electrolyte-responsive behavior of RC-g-PSBMA; (<b>d</b>) Dependence of rejection rates of BSA and NPs upon the concentration of NaCl solutions. Reprinted with permission from [<a href="#B161-materials-06-00738" class="html-bibr">161</a>]. Copyright 2009 American Chemical Society.</p>
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264 KiB  
Article
Behavior of Elastoplastic Auxetic Microstructural Arrays
by Rivka Gilat and Jacob Aboudi
Materials 2013, 6(3), 726-737; https://doi.org/10.3390/ma6030726 - 28 Feb 2013
Cited by 14 | Viewed by 5573
Abstract
A continuum-based micromechanical model is employed for the prediction of the elasto-plastic behavior of periodic microstructural arrays that can generate negative values of Poisson’s ratios. The combined effects of the negative Poisson’s ratio generated by the array microstructure and the elastoplastic behavior of [...] Read more.
A continuum-based micromechanical model is employed for the prediction of the elasto-plastic behavior of periodic microstructural arrays that can generate negative values of Poisson’s ratios. The combined effects of the negative Poisson’s ratio generated by the array microstructure and the elastoplastic behavior of the constituents are studied. A design methodology for the determination of the constituents’ properties of two-phase arrays that generate required values of negative Poisson’s ratio is considered. Full article
(This article belongs to the Special Issue Auxetic Materials)
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Figure 1

Figure 1
<p>A multiphase composite with a periodic microstructure in the global system <math display="inline"> <mrow> <msub> <mi>x</mi> <mn>2</mn> </msub> <mspace width="3.33333pt"/> <mo>−</mo> <mspace width="3.33333pt"/> <msub> <mi>x</mi> <mn>3</mn> </msub> </mrow> </math>, characterized by a repeating unit cell (highlighted). The repeating unit cell is given with respect to the local coordinate system <math display="inline"> <mrow> <msub> <mi>y</mi> <mn>2</mn> </msub> <mo>−</mo> <msub> <mi>y</mi> <mn>3</mn> </msub> </mrow> </math>.</p>
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<p>Repeating re-entrant unit cell with angle <span class="html-italic">θ</span>. The shaded and white regions are labeled by 1 and 2, respectively.</p>
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<p>Variation of the effective Poisson ratios <math display="inline"> <msubsup> <mi>ν</mi> <mn>23</mn> <mo>*</mo> </msubsup> </math> and <math display="inline"> <msubsup> <mi>ν</mi> <mn>32</mn> <mo>*</mo> </msubsup> </math> with <span class="html-italic">θ</span> for a material with voids (<math display="inline"> <mrow> <msub> <mi>v</mi> <mi>f</mi> </msub> <mo>=</mo> <mn>0.28</mn> </mrow> </math>).</p>
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<p>Variation of the effective Poisson’s ratio <math display="inline"> <msubsup> <mi>ν</mi> <mn>23</mn> <mo>*</mo> </msubsup> </math> with volume ratio <math display="inline"> <msub> <mi>v</mi> <mi>f</mi> </msub> </math> of the material with voids (<math display="inline"> <mrow> <mi>θ</mi> <mo>=</mo> <msup> <mn>45</mn> <mo>∘</mo> </msup> </mrow> </math>).</p>
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<p>A repeating unit cell is shown for an array that generates negative effective Poisson’s ratios.</p>
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<p>Re-entrant array (<math display="inline"> <mrow> <mi>θ</mi> <mo>=</mo> <msup> <mn>45</mn> <mo>∘</mo> </msup> </mrow> </math>) with two distinct materials. Variation of the effective Poisson’s ratio <math display="inline"> <msubsup> <mi>ν</mi> <mn>23</mn> <mo>*</mo> </msubsup> </math> with the Young’s modulus of material 2 while keeping its Poisson’s ratio constant.</p>
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<p>Re-entrant array (<math display="inline"> <mrow> <mi>θ</mi> <mo>=</mo> <msup> <mn>45</mn> <mo>∘</mo> </msup> </mrow> </math>) with two distinct materials. Variation of the effective Poisson’s ratio <math display="inline"> <msubsup> <mi>ν</mi> <mn>23</mn> <mo>*</mo> </msubsup> </math> with the Poisson’s ratio of material 2 while keeping its Young’s modulus constant.</p>
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<p>The elastoplastic response of aluminum with voids in the re-entrant array with <math display="inline"> <mrow> <mi>θ</mi> <mo>=</mo> <msup> <mn>75</mn> <mo>∘</mo> </msup> </mrow> </math> that generates a negative effective elastic Poisson’s ratio. (<b>a</b>) Average transverse stresses and (<b>b</b>) transverse plastic strains.</p>
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<p>Plastic and apparent Poisson ratio of aluminum with voids in the re-entrant array with <math display="inline"> <mrow> <mi>θ</mi> <mo>=</mo> <msup> <mn>75</mn> <mo>∘</mo> </msup> </mrow> </math>, under uniaxial stress in the <math display="inline"> <msub> <mi>y</mi> <mn>2</mn> </msub> </math> direction.</p>
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<p>The von Misses stress distribution over the re-entrant repeating unit cell of aluminum with voids with <math display="inline"> <mrow> <mi>θ</mi> <mo>=</mo> <msup> <mn>75</mn> <mo>∘</mo> </msup> </mrow> </math>.</p>
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<p>The elastoplastic response of aluminum and elastic material in the re-entrant array with <math display="inline"> <mrow> <mi>θ</mi> <mo>=</mo> <msup> <mn>75</mn> <mo>∘</mo> </msup> </mrow> </math> that generates a positive effective elastic Poisson’s ratio. (<b>a</b>) Average transverse stresses and (<b>b</b>) transverse plastic strains.</p>
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<p>The elastoplastic response of aluminum with voids in the array with <math display="inline"> <mrow> <mi>θ</mi> <mo>=</mo> <msup> <mn>90</mn> <mo>∘</mo> </msup> </mrow> </math> that generates a positive effective elastic Poisson’s ratio. (<b>a</b>) Average transverse stress and (<b>b</b>) transverse plastic strains.</p>
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443 KiB  
Article
Structural and Luminescence Properties of Lu2O3:Eu3+ F127 Tri-Block Copolymer Modified Thin Films Prepared by Sol-Gel Method
by Angel De Jesus Morales Ramírez, Margarita García Hernández, Antonieta García Murillo, Felipe De Jesús Carrillo Romo, Joel Moreno Palmerin, Dulce Yolotzin Medina Velazquez and María Luz Carrera Jota
Materials 2013, 6(3), 713-725; https://doi.org/10.3390/ma6030713 - 26 Feb 2013
Cited by 6 | Viewed by 6798
Abstract
Lu2O3:Eu3+ transparent, high density, and optical quality thin films were prepared using the sol-gel dip-coating technique, starting with lutetium and europium nitrates as precursors and followed by hydrolysis in an ethanol-ethylene glycol solution. Acetic acid and acetylacetonate were [...] Read more.
Lu2O3:Eu3+ transparent, high density, and optical quality thin films were prepared using the sol-gel dip-coating technique, starting with lutetium and europium nitrates as precursors and followed by hydrolysis in an ethanol-ethylene glycol solution. Acetic acid and acetylacetonate were incorporated in order to adjust pH and as a sol stabilizer. In order to increment the thickness of the films and orient the structure, F127 Pluronic acid was incorporated during the sol formation. Structural, morphological, and optical properties of the films were investigated for different F127/Lu molar ratios (0–5) in order to obtain high optical quality films with enhanced thickness compared with the traditional method. X-ray diffraction (XRD) shows that the films present a highly oriented cubic structure <111> beyond 1073 K for a 3-layer film, on silica glass substrates. The thickness, density, porosity, and refractive index evolution of the films were investigated by means of m-lines microscopy along with the morphology by scanning electron microscope (SEM) and luminescent properties. Full article
(This article belongs to the Special Issue Advances in Sol-gel Derived Materials)
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<p>Fourier transform infrared (FTIR) spectra of Chemical evolution at Lu<sub>2</sub>O<sub>3</sub>:Eu<sup>3+</sup> F127 modified system, F127/Lu = 2.0.</p>
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<p>Structural evolution of Lu<sub>2</sub>O<sub>3</sub>:Eu<sup>3+</sup> F127 modified thin films. (<b>a</b>) F127/Lu=1.0; (<b>b</b>) F127/Lu = 2.0.</p>
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<p>Photograph of transparent Lu<sub>2</sub>O<sub>3</sub>:Eu<sup>3+</sup> F127 modified thin films.</p>
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<p>Scanning electron microscope (SEM) micrograph of Lu<sub>2</sub>O<sub>3</sub>:Eu<sup>3+</sup> F127 modified thin films annealed at 1073 K. (<b>a</b>) F127/Lu = 1.0; (<b>b</b>) F127/Lu = 2.0.</p>
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<p>SEM micrograph of the pore content at Lu<sub>2</sub>O<sub>3</sub>:Eu<sup>3+</sup> F127 modified thin films. (<b>a</b>) F127/Lu = 1.0; (<b>b</b>) F127/Lu = 2.0.</p>
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<p>Evolution of thickness of Lu<sub>2</sub>O<sub>3</sub>:Eu<sup>3+</sup> F127 modified thin films as a function of annealing temperature and F127/Lu molar ratio.</p>
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<p>Evolution of refractive index at 633 nm of Lu<sub>2</sub>O<sub>3</sub>:Eu<sup>3+</sup> F127 modified thin films as a function of annealing temperature and F127/Lu molar ratio.</p>
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<p>Excitation spectra (λ<sub>em</sub> = 612 nm) of Lu<sub>2</sub>O<sub>3</sub>:Eu<sup>3+</sup> F127 modified thin films as a function of F127/Lu molar ratio at annealing temperature of 1073 K.</p>
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<p>Emission spectra (λ<sub>exc</sub> = 254 nm) of Lu<sub>2</sub>O<sub>3</sub>:Eu<sup>3+</sup> F127 modified thin films as a function of F127/Lu molar ratio at annealing temperature of 1073 K.</p>
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<p>Emission spectra (λ<sub>exc</sub> = 254 nm) of Lu<sub>2</sub>O<sub>3</sub>:Eu<sup>3+</sup> F127, with a fixed F127/Lu = 1.0 level as function of annealing temperature.</p>
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