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Materials, Volume 12, Issue 15 (August-1 2019) – 160 articles

Cover Story (view full-size image): The endodontic regeneration is very challenging because pulp and dentin formation, revascularization and reinnervation can be concomitantly required. Polymer scaffolds constitute keystone of the different endodontic regenerative strategies. Indeed, they provide a solid environment for adhesion, proliferation and differentiation of competent cells incorporated or attracted to the lesion by “cell homing”. Besides, they constitute adequate delivery system of active biomolecules for orchestrating the different steps of endodontic regeneration and the diverse cellular fonctions. Collagen, fibrin, polypeptide, PCL and chitosan are the main types of polymeric endodontic scaffolds. Recently, proposals to associate different polymers have emerged for adding crucial advantages. View this paper.
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15 pages, 2080 KiB  
Article
Improvement of Surface Roughness and Hydrophobicity in PETG Parts Manufactured via Fused Deposition Modeling (FDM): An Application in 3D Printed Self–Cleaning Parts
by Juan M. Barrios and Pablo E. Romero
Materials 2019, 12(15), 2499; https://doi.org/10.3390/ma12152499 - 6 Aug 2019
Cited by 55 | Viewed by 7677
Abstract
The fused deposition modeling (FDM) technique is used today by companies engaged in the fabrication of traffic signs for the manufacture of light-emitting diode LED spotlights. In this sector, the surface properties of the elements used (surface finish, hydrophobic features) are decisive because [...] Read more.
The fused deposition modeling (FDM) technique is used today by companies engaged in the fabrication of traffic signs for the manufacture of light-emitting diode LED spotlights. In this sector, the surface properties of the elements used (surface finish, hydrophobic features) are decisive because surfaces that retain little dirt and favor self–cleaning behavior are needed. A design of experiments (L27) with five factors and three levels has been carried out. The factors studied were: Layer height (LH), print temperature (T), print speed (PS), print acceleration (PA), and flow rate (F). Polyethylene terephthalate glycol (PETG) specimens of 25.0 × 25.0 × 2.4 mm have been printed and, in each of them, the surface roughness (Ra,0, Ra,90), sliding angle (SA0, SA90), and contact angle (CA0, CA90) in both perpendicular directions have been measured. Taguchi and ANOVA analysis shows that the most influential variables in this case are printing acceleration for Ra, 0 (p–value = 0.052) and for SA0 (p–value = 0.051) and flow rate for Ra, 90 (p–value = 0.001) and for SA90 (p–value = 0.012). Although the ANOVA results for the contact angle are not significant, specimen 8 (PA = 1500 mm/s2 and flow rate F = 110%) and specimen 10 (PA =1500 mm/s2 and F = 100%) have reached contact angle values above or near the limit value for hydrophobia, respectively. Full article
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Graphical abstract

Graphical abstract
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<p>3D printed LED spotlights for road signals.</p>
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<p>Fused deposition modeling (FDM) 3D printer parameters studied in the work.</p>
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<p>Graphical description of the methodology followed in the work: (<b>a</b>) Design of experiments and computer-aided design and computer-aided manufacturing CAD-CAM stage, (<b>b</b>) D printing of specimens, (<b>c</b>) surface roughness measurements, (<b>d</b>) sliding and contact angle measurements, (<b>e</b>) statistical data processing.</p>
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<p>Graphical explanation of the orientations in which the measurements have been carried out.</p>
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<p>Results obtained via the Taguchi method for <span class="html-italic">R<sub>a,0</sub></span>: Layer height (LH), printing temperature (T), printing speed (PS), printing acceleration (PA), and flow rate (F).</p>
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<p>Results obtained via the Taguchi method for <span class="html-italic">R<sub>a 90</sub></span>: Layer height (LH), printing temperature (T), printing speed (PS), printing acceleration (PA), and flow rate (F).</p>
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<p>Results obtained via the Taguchi method for SA<sub>0</sub> (°): Layer height (LH), printing temperature (T), printing speed (PS), printing acceleration (PA), and flow rate (F).</p>
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<p>Results obtained via the Taguchi method for SA<sub>90</sub> (°): Layer height (LH), printing temperature (T), printing speed (PS), printing acceleration (PA), and flow rate (F).</p>
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<p>Results obtained via the Taguchi method for CA<sub>0</sub> (°): Layer height (LH), printing temperature (T), printing speed (PS), printing acceleration (PA), and flow rate (F).</p>
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<p>Results obtained via the Taguchi method for CA<sub>90</sub> (°): Layer height (LH), printing temperature (T), printing speed (PS), printing acceleration (PA), and flow rate (F).</p>
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<p>Micrographs obtained via SEM (× 37): (<b>a</b>) Specimen 22, (<b>b</b>) specimen 1.</p>
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<p>(<b>a</b>) Specimen 8: Contact angle measured in direction perpendicular to extrusion direction (CA<sub>90</sub>), (<b>b</b>) specimen 10: Contact angle measured in direction parallel to extrusion direction (CA<sub>0</sub>).</p>
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<p>Headlight printed in polyethylene terephthalate glycol (PETG) for traffic sign.</p>
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<p>Drop sliding over different profiles: (<b>a</b>) Profile obtained by Lee et al. [<a href="#B19-materials-12-02499" class="html-bibr">19</a>] by dip-coating in a solution with nanoparticles, (<b>b</b>) profile obtained through an appropriate selection of PA and F (specimen 22), (<b>c</b>) profile obtained through an inappropriate selection of PA and F (specimen 1).</p>
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<p>Road dimensional errors at start, acceleration, deceleration, and stopping of a print head (elaborated from [<a href="#B25-materials-12-02499" class="html-bibr">25</a>]).</p>
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17 pages, 9280 KiB  
Article
Leaf Age-Dependent Effects of Foliar-Sprayed CuZn Nanoparticles on Photosynthetic Efficiency and ROS Generation in Arabidopsis thaliana
by Ilektra Sperdouli, Julietta Moustaka, Orestis Antonoglou, Ioannis-Dimosthenis S. Adamakis, Catherine Dendrinou-Samara and Michael Moustakas
Materials 2019, 12(15), 2498; https://doi.org/10.3390/ma12152498 - 6 Aug 2019
Cited by 33 | Viewed by 4047
Abstract
Young and mature leaves of Arabidopsis thaliana were exposed by foliar spray to 30 mg L−1 of CuZn nanoparticles (NPs). The NPs were synthesized by a microwave-assisted polyol process and characterized by dynamic light scattering (DLS), X-ray diffraction (XRD), and transmission electron [...] Read more.
Young and mature leaves of Arabidopsis thaliana were exposed by foliar spray to 30 mg L−1 of CuZn nanoparticles (NPs). The NPs were synthesized by a microwave-assisted polyol process and characterized by dynamic light scattering (DLS), X-ray diffraction (XRD), and transmission electron microscopy (TEM). CuZn NPs effects in Arabidopsis leaves were evaluated by chlorophyll fluorescence imaging analysis that revealed spatiotemporal heterogeneity of the quantum efficiency of PSII photochemistry (ΦPSΙΙ) and the redox state of the plastoquinone (PQ) pool (qp), measured 30 min, 90 min, 180 min, and 240 min after spraying. Photosystem II (PSII) function in young leaves was observed to be negatively influenced, especially 30 min after spraying, at which point increased H2O2 generation was correlated to the lower oxidized state of the PQ pool. Recovery of young leaves photosynthetic efficiency appeared only after 240 min of NPs spray when also the level of ROS accumulation was similar to control leaves. On the contrary, a beneficial effect on PSII function in mature leaves after 30 min of the CuZn NPs spray was observed, with increased ΦPSΙΙ, an increased electron transport rate (ETR), decreased singlet oxygen (1O2) formation, and H2O2 production at the same level of control leaves.An explanation for this differential response is suggested. Full article
(This article belongs to the Special Issue The Role of Metal Ions in Biology, Biochemistry and Medicine)
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Figure 1
<p>The X-ray diffraction (XRD) patterns of CuZn nanoparticles (NPs) (<b>a</b>), and the size distribution (diameter in nm) of the aqueous suspensions of CuZn NPs evaluated by dynamic light scattering (DLS) numbers measurements (<b>b</b>).</p>
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<p>Size and morphology of CuZn NPs determined by transmission electron microscopy.</p>
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<p>Changes in the quantum efficiency of photosystem II (PSII) photochemistry (Φ<span class="html-italic"><sub>PSΙΙ</sub></span>) (<b>a</b>), and the quantum yield of regulated non-photochemical energy loss in PSII (Φ<span class="html-italic"><sub>NPQ</sub></span>) (<b>b</b>); of <span class="html-italic">Arabidopsis thaliana</span> young and mature leaves measured (at 140 μmol photons m<sup>−</sup><sup>2</sup> s<sup>−</sup><sup>1</sup>) 30 min, 90 min, 180 min, and 240 min after the foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs or distilled water (control). Error bars on columns are standard deviations based on four to five leaves from different plants. Columns with different letters (lowercase for young leaves and capitals for mature) are statistically different (<span class="html-italic">p</span> &lt; 0.05). An asterisk (*) represents a significantly different mean of the same time treatment between young and mature leaves (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>Changes in the quantum yield of non-regulated energy dissipation in PSII (Φ<span class="html-italic"><sub>NO</sub></span>) of <span class="html-italic">Arabidopsis thaliana</span> young and mature leaves measured (at 140 μmol photons m<sup>−</sup><sup>2</sup> s<sup>−</sup><sup>1</sup>) 30 min, 90 min, 180 min, and 240 min after the foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs or distilled water (control). Error bars on columns are standard deviations based on four to five leaves from different plants. Columns with different letter (lower case for young leaves and capitals for mature) are statistically different (<span class="html-italic">p</span> &lt; 0.05). An asterisk (*) represents a significantly different mean of the same time treatment between young and mature leaves (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>Changes in the non-photochemical fluorescence quenching (NPQ) (<b>a</b>), and the relative PSII electron transport rate (ETR) (<b>b</b>); of <span class="html-italic">Arabidopsis thaliana</span> young and mature leaves measured (at 140 μmol photons m<sup>−</sup><sup>2</sup> s<sup>−</sup><sup>1</sup>) 30 min, 90 min, 180 min, and 240 min after the foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs or distilled water (control). Error bars on columns are standard deviations based on four to five leaves from different plants. Columns with different letter (lower case for young leaves and capitals for mature) are statistically different (<span class="html-italic">p</span> &lt; 0.05). An asterisk (*) represents a significantly different mean of the same time treatment between young and mature leaves (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>Changes in the photochemical fluorescence quenching, which is the relative reduction state of the plastoquinone (PQ) pool, reflecting the fraction of open PSII reaction centers (<span class="html-italic">q</span><sub>p</sub><span class="html-small-caps">) </span>of young and mature <span class="html-italic">Arabidopsis thaliana</span> leaves measured (at 140 μmol photons m<sup>−2</sup> s<sup>–1</sup>) 30 min, 90 min, 180 min, and 240 min after the foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs or distilled water (control). Error bars on columns are standard deviations based on four to five leaves from different plants. Columns with different letter (lower case for young leaves and capitals for mature) are statistically different (<span class="html-italic">p</span> &lt; 0.05). An asterisk (*) represents a significantly different mean of the same time treatment between young and mature leaves (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>Representative chlorophyll fluorescence images of the effective quantum yield of PSII photochemistry (Φ<span class="html-italic"><sub>PSΙΙ</sub></span>) of <span class="html-italic">Arabidopsis thaliana</span> young leaves after 5 min of illumination at 140 μmol photons m<sup>−</sup><sup>2</sup> s<sup>–1</sup>. Leaves were measured after the foliar spray with distilled water (control) (<b>a</b>), or 30 min (<b>b</b>), 90 min (<b>c</b>), 180 min (<b>d</b>) and 240 min (<b>e</b>) after the foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs. The color code depicted at the bottom of the images ranges from values 0.0 to 1.0. The areas of interest (AOI) are shown in each image. The average Φ<span class="html-italic"><sub>PSΙΙ</sub></span> value of all the AOI for the whole leaf is shown.</p>
Full article ">Figure 8
<p>Representative chlorophyll fluorescence images of the effective quantum yield of PSII photochemistry (Φ<span class="html-italic"><sub>PSΙΙ</sub></span>) of <span class="html-italic">Arabidopsis thaliana</span> mature leaves after 5 min of illumination at 140 μmol photons m<sup>−</sup><sup>2</sup> s<sup>–1</sup>. Leaves were measured after the foliar spray with distilled water (control) (<b>a</b>), or 30 min (<b>b</b>), 90 min (<b>c</b>), 180 min (<b>d</b>) and 240 min (<b>e</b>) after the foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs. The color code depicted at the bottom of the images ranges from values 0.0 to 1.0. The areas of interest (AOI) are shown in each image. The average Φ<span class="html-italic"><sub>PSΙΙ</sub></span> value of all the AOI for the whole leaf is shown.</p>
Full article ">Figure 9
<p>Representative chlorophyll fluorescence images of the relative reduction state of the plastoquinone (PQ) pool, that is, the photochemical fluorescence quenching, reflecting the fraction of open PSII reaction centers (<span class="html-italic">q</span><sub>p</sub><span class="html-small-caps">), </span>of <span class="html-italic">Arabidopsis thaliana</span> young leaves after 5 min of illumination at 140 μmol photons m<sup>−2</sup> s<sup>–1</sup>. Leaves were measured after the foliar spray with distilled water (control) (<b>a</b>), or 30 min (<b>b</b>), 90 min (<b>c</b>), 180 min (<b>d</b>), and 240 min (<b>e</b>) after the foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs. The color code depicted at the bottom of the images ranges from values 0.0 to 1.0. The areas of interest (AOI) are shown in each image. The average <span class="html-italic">q</span><sub>p</sub> value of all the AOI for the whole leaf is shown.</p>
Full article ">Figure 10
<p>Representative chlorophyll fluorescence images of the relative reduction state of the plastoquinone (PQ) pool—that is, the photochemical fluorescence quenching, reflecting the fraction of open PSII reaction centers (<span class="html-italic">q</span><sub>p</sub><span class="html-small-caps">) </span>of <span class="html-italic">Arabidopsis thaliana</span> mature leaves after 5 min of illumination at 140 μmol photons m<sup>−2</sup> s<sup>–1</sup>. Leaves were measured after the foliar spray with distilled water (control) (<b>a</b>), or 30 min (<b>b</b>), 90 min (<b>c</b>), 180 min (<b>d</b>) and 240 min (<b>e</b>) after the foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs. The color code depicted at the bottom of the images ranges from values 0.0 to 1.0. The areas of interest (AOI) are shown in each image. The average <span class="html-italic">q</span><sub>p</sub> value of all the AOI for the whole leaf is shown.</p>
Full article ">Figure 11
<p>Representative patterns of reactive oxygen species (ROS) (H<sub>2</sub>O<sub>2</sub>) production in <span class="html-italic">Arabidopsis thaliana</span> young (<b>a</b>–<b>e</b>) and mature (<b>f</b>–<b>j</b>) leaves, as indicated by the fluorescence of H<sub>2</sub>DCF-DA. The H<sub>2</sub>O<sub>2</sub> generation after the foliar spray with distilled water (control) in a young leaf (<b>a</b>) and mature leaf (<b>f</b>); or 30 min after foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs in a young leaf (<b>b</b>) and mature leaf (<b>g</b>); 90 min after foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs in a young leaf (<b>c</b>) and mature leaf (<b>h</b>); 180 min after foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs in a young leaf (<b>d</b>) and mature leaf (<b>i</b>); and 240 min after foliar spay with 30 mg L<sup>−1</sup> of CuZn NPs in a young leaf (<b>e</b>), and mature leaf (<b>j</b>). Scale bare: 200 µm. A higher H<sub>2</sub>O<sub>2</sub> content is indicated by the light green color.</p>
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13 pages, 20881 KiB  
Article
Fluorescent PCDTBT Nanoparticles with Tunable Size for Versatile Bioimaging
by Srujan Cheruku, Lien D’Olieslaeger, Nick Smisdom, Joeri Smits, Dirk Vanderzande, Wouter Maes, Marcel Ameloot and Anitha Ethirajan
Materials 2019, 12(15), 2497; https://doi.org/10.3390/ma12152497 - 6 Aug 2019
Cited by 8 | Viewed by 5039
Abstract
Conjugated polymer nanoparticles exhibit very interesting properties for use as bio-imaging agents. In this paper, we report the synthesis of PCDTBT (poly([9-(1’-octylnonyl)-9H-carbazole-2,7-diyl]-2,5-thiophenediyl-2,1,3-benzothiadiazole-4,7-diyl-2,5-thiophene-diyl)) nanoparticles of varying sizes using the mini-emulsion and emulsion/solvent evaporation approach. The effect of the size of the particles on the [...] Read more.
Conjugated polymer nanoparticles exhibit very interesting properties for use as bio-imaging agents. In this paper, we report the synthesis of PCDTBT (poly([9-(1’-octylnonyl)-9H-carbazole-2,7-diyl]-2,5-thiophenediyl-2,1,3-benzothiadiazole-4,7-diyl-2,5-thiophene-diyl)) nanoparticles of varying sizes using the mini-emulsion and emulsion/solvent evaporation approach. The effect of the size of the particles on the optical properties is investigated using UV-Vis absorption and fluorescence emission spectroscopy. It is shown that PCDTBT nanoparticles have a fluorescence emission maximum around 710 nm, within the biological near-infrared “optical window”. The photoluminescence quantum yield shows a characteristic trend as a function of size. The particles are not cytotoxic and are taken up successfully by human lung cancer carcinoma A549 cells. Irrespective of the size, all particles show excellent fluorescent brightness for bioimaging. The fidelity of the particles as fluorescent probes to study particle dynamics in situ is shown as a proof of concept by performing raster image correlation spectroscopy. Combined, these results show that PCDTBT is an excellent candidate to serve as a fluorescent probe for near-infrared bio-imaging. Full article
(This article belongs to the Special Issue Functional Conjugated Polymers for Bioimaging and Biosensing)
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Graphical abstract

Graphical abstract
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<p>(<b>top</b>) Schematic illustration of the PCDTBT NP synthesis. (<b>bottom</b>) Chemical structure of PCDTBT.</p>
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<p>TEM micrographs of the different sized nanoparticles: (<b>A</b>) NP1, (<b>B</b>) NP2, (<b>C</b>) NP3, (<b>D</b>) NP4, and (<b>E</b>) NP5. The inset shows the morphology of a single particle in an enlarged view.</p>
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<p>UV-Vis absorption (solid lines) and fluorescence (dashed lines) spectra of (<b>A</b>) PCDTBT in NP (NP1) and MD form, and (<b>B</b>) the differently sized PCDTBT NPs (NP1, NP2, NP3, NP4, NP5). The UV-Vis absorption spectrum of the NPs is hypsochromically shifted and fluorescence spectrum bathochromically shifted, compared to its MD form.</p>
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<p>Dose-dependent cytotoxicity of the different PCDTBT NPs after 24 h of exposure, as determined by the Alamar blue assay on A549 cells, showing no significant cytotoxicity. Error bars show the standard deviations of the measurements (n = 3).</p>
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<p>Two-photon microscopic images of A549 cells incubated for 18 h with 50 µg/mL of (<b>A</b>–<b>E</b>) NP1–NP5 respectively. The NPs are seen in green; they are superimposed on transmission images of the cells. All the NPs are internalized by the A549 cells. Scale bar: 25 µm.</p>
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<p>Diffusion coefficients of the different PCDTBT NP samples as measured by RICS. The diffusion coefficients increase as the hydrodynamic size (as measured by DLS) of the particles decreases.</p>
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15 pages, 5370 KiB  
Article
Microstructural Evolution and Refinement Mechanism of a Beta–Gamma TiAl-Based Alloy during Multidirectional Isothermal Forging
by Kai Zhu, Shoujiang Qu, Aihan Feng, Jingli Sun and Jun Shen
Materials 2019, 12(15), 2496; https://doi.org/10.3390/ma12152496 - 6 Aug 2019
Cited by 10 | Viewed by 3540
Abstract
Multidirectional isothermal forging (MDIF) was used on a Ti-44Al-4Nb-1.5Cr-0.5Mo-0.2B (at. %) alloy to obtain a crack-free pancake. The microstructural evolution, such as dynamic recovery and recrystallization behavior, were investigated using electron backscattered diffraction and transmission electron microscopy methods. The MDIF broke down the [...] Read more.
Multidirectional isothermal forging (MDIF) was used on a Ti-44Al-4Nb-1.5Cr-0.5Mo-0.2B (at. %) alloy to obtain a crack-free pancake. The microstructural evolution, such as dynamic recovery and recrystallization behavior, were investigated using electron backscattered diffraction and transmission electron microscopy methods. The MDIF broke down the initial near-lamellar microstructure and produced a refined and homogeneous duplex microstructure. γ grains were effectively refined from 3.6 μm to 1.6 μm after the second step of isothermal forging. The ultimate tensile strength at ambient temperature and the elongation at 800 °C increased significantly after isothermal forging. β/B2→α2 transition occurred during intermediate annealing, and α2 + γ→β/B2 transition occurred during the second step of isothermal forging. The refinement mechanism of the first-step isothermal forging process involved the conversion of the lamellar structure and discontinuous dynamic recrystallization (DDRX) of γ grains in the original mixture-phase region. The lamellar conversion included continuous dynamic recrystallization and DDRX of the γ laths and bugling of the γ phase. DDRX behavior of γ grains dominated the refinement mechanism of the second step of isothermal forging. Full article
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Figure 1

Figure 1
<p>(<b>a</b>) Schematic of MDIF (multidirectional isothermal forging); (<b>b</b>) sampling position for the first and second steps of isothermal forging; (<b>c</b>) parameters of MDIF and intermediate annealing, appearance of the first-step and the second-step isothermally forged pancakes.</p>
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<p>SEM (scanning electron microscopy) images of TiAlNbCrMo alloy: (<b>a</b>) after hot isostatic pressing (HIP); (<b>b</b>) 1200 °C/2 h/WQ. The γ phase appears as dark gray. The light gray contrast indicates α<sub>2</sub>/γ colonies, whereas the white ones correspond to the β/B2 phase.</p>
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<p>Phase distribution maps overlapped by GBs of TiAlNbCrMo alloy during MDIF: (<b>a</b>) first step of isothermal forging; (<b>b</b>) intermediate annealing at 1100 °C for 1 h; (<b>c</b>) second step of isothermal forging. The isothermal forging direction in all images is vertical. RL, KL, FG, and CG denote remnant lamellar, kinked lamellar, fine grain, and coarse grain, respectively.</p>
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<p>Distribution of the γ grain size of TiAlNbCrMo alloy: (<b>a</b>) after annealing at 1100 °C for 1 h; (<b>b</b>) after the second step of isothermal forging.</p>
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<p>RL area in the first-step isothermally forged microstructure of TiAlNbCrMo alloy: (<b>a</b>) inverse pole figure (IPF) map of γ grains; (<b>b</b>) IPF map and corresponding crystallographic orientations of L1 selected in (<b>a</b>); (<b>c</b>) line profiles of misorientation angles along arrow AB in (<b>b</b>). KL area in the first-step isothermally forged microstructure: (<b>d</b>) IPF map of γ grains; (<b>e</b>) IPF map and corresponding crystallographic orientations of L2 selected in (<b>d</b>); (<b>f</b>,<b>g</b>) line profiles of misorientation angle along the arrows AB and BC in (<b>e</b>).</p>
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<p>CG area in the first-step isothermally forged microstructure of TiAlNbCrMo alloy: (<b>a</b>) phase map; (<b>b</b>) IPF map of γ grains; (<b>c</b>) IPF map and corresponding crystallographic orientations of P1, P2, and P3 selected in (<b>b</b>). FG area in the first-step isothermally forged microstructure: (<b>d</b>) IPF map of γ grains; (<b>e</b>) distribution of GB misorientations.</p>
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<p>TEM (transmission electron microscopy) images of the first-step isothermally forged microstructure of TiAlNbCrMo alloy: (<b>a</b>) slightly deformed remnant lamellae; (<b>b</b>) remnant lamellae with γ twins and DRX γ grains. Selected area electron diffraction (SAED) pattern in the corner corresponding to the γ twins; (<b>c</b>) γ nucleation and dislocation tangle; (<b>d</b>) kinked lamellae; (<b>e</b>) dislocation wall within a γ grain; (<b>f</b>) refined grains.</p>
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<p>TEM images of the second-step isothermally forged microstructure of TiAlNbCrMo alloy: (<b>a</b>) growing DRX γ grains; (<b>b</b>) GB features of γ grains.</p>
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13 pages, 3179 KiB  
Article
Cold Isostatic Pressing to Improve the Mechanical Performance of Additively Manufactured Metallic Components
by Isidoro Iván Cuesta, Emilio Martínez-Pañeda, Andrés Díaz and Jesús Manuel Alegre
Materials 2019, 12(15), 2495; https://doi.org/10.3390/ma12152495 - 6 Aug 2019
Cited by 13 | Viewed by 5063
Abstract
Additive manufacturing is becoming a technique with great prospects for the production of components with new designs or shapes that are difficult to obtain by conventional manufacturing methods. One of the most promising techniques for printing metallic components is binder jetting, due to [...] Read more.
Additive manufacturing is becoming a technique with great prospects for the production of components with new designs or shapes that are difficult to obtain by conventional manufacturing methods. One of the most promising techniques for printing metallic components is binder jetting, due to its time efficiency and its ability to generate complex parts. In this process, a liquid binding agent is selectively deposited to adhere the powder particles of the printing material. Once the metallic piece is generated, it undergoes a subsequent process of curing and sintering to increase its density (hot isostatic pressing). In this work, we propose subjecting the manufactured component to an additional post-processing treatment involving the application of a high hydrostatic pressure (5000 bar) at room temperature. This post-processing technique, so-called cold isostatic pressing (CIP), is shown to increase the yield load and the maximum carrying capacity of an additively manufactured AISI 316L stainless steel. The mechanical properties, with and without CIP processing, are estimated by means of the small punch test, a suitable experimental technique to assess the mechanical response of small samples. In addition, we investigate the porosity and microstructure of the material according to the orientations of layer deposition during the manufacturing process. Our observations reveal a homogeneous distribution independent of these orientations, evidencing thus an isotropic behaviour of the material. Full article
(This article belongs to the Section Manufacturing Processes and Systems)
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Figure 1
<p>Porosity distribution in AISI 316L manufactured using binder jetting.</p>
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<p>Orientations and microstructure in AISI 316L manufactured using binder jetting.</p>
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<p>Schematic description of the device to carry out the high hydrostatic pressure post-processing at room temperature.</p>
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<p>Typical load–displacement curve and schematic description of the experimental setup involved in the small punch test (SPT).</p>
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<p>SPT load–displacement curves (TS orientation) for the AISI 316L with and without CIP.</p>
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<p>SPT load–displacement curves for specimens showing premature fracture in L direction: (<b>a</b>) B3 specimen and (<b>b</b>) E3 specimen.</p>
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<p>Aspect of premature fracture (ductile–intergranular) in the SPT specimen E3.</p>
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<p>Aspect of typical ductile fracture in SPT specimens.</p>
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11 pages, 1196 KiB  
Article
Influence of Solution Deposition Process on Modulating Majority Charge Carrier Type and Quality of Perovskite Thin Films for Solar Cells
by Chuangchuang Chang, Xiaoping Zou, Jin Cheng, Tao Ling, Yujun Yao and Dan Chen
Materials 2019, 12(15), 2494; https://doi.org/10.3390/ma12152494 - 6 Aug 2019
Cited by 11 | Viewed by 4411
Abstract
In the past ten years, extensive research has witnessed the rapid development of perovskite solar cells (PSCs) and diversified preparation processing craft. At present, the most widely used methods of preparing perovskite solar cells are the one-step method and the two-step method. The [...] Read more.
In the past ten years, extensive research has witnessed the rapid development of perovskite solar cells (PSCs) and diversified preparation processing craft. At present, the most widely used methods of preparing perovskite solar cells are the one-step method and the two-step method. The main work of this paper is to study the effect of the solution deposition process on the quality of perovskite thin films, as well as modulating majority charge carrier types. Perovskite film was prepared in air by designing different processes, which were then adequately analyzed with corresponding methods. It was demonstrated that the preparation process plays a crucial role in modulating the type of majority carrier and in achieving high-quality perovskite thin film. The one-step prepared perovskite layer is enriched in MA+, leading to a P type majority carrier type thin film. The two-step prepared perovskite layer is enriched in Pb2+, leading to a N type majority carrier type thin film. In addition, we found that the one-step method caused PbI2 residue due to component segregation, which seriously affects the interface and film quality of the perovskite layer. This work aims to modulate the majority carrier type of perovskite film through different preparation processes, which can lay the foundation for the study of homojunction perovskite solar cells to improve the device performance of PSCs. Full article
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<p>The structure of the device prepared by the one-step method (<b>a</b>) and two-step method (<b>b</b>) from top to bottom are fluorine-doped SnO<sub>2</sub> FTO (C/Au)/Spiro-OMeTAD/CH<sub>3</sub>NH<sub>3</sub>PbI<sub>3</sub>/mp-TiO<sub>2</sub>/bl-TiO<sub>2</sub>/FTO. The figure includes the direction of the built-in electric field, the direction of carrier migration and the majority carrier type of perovskite films.</p>
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<p>Flow chart of preparation of perovskite film by the one-step (<b>a</b>) method and the two-step (<b>b</b>) method.</p>
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<p>Top view and cross-sectional view of the SEM images for one-step (<b>a</b>,<b>b</b>) and two-step (<b>c</b>,<b>d</b>).</p>
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<p>XRD patterns of perovskite films with one-step and two-step. The blue circle is the peak of residual PbI<sub>2</sub>.</p>
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<p>UV-visible absorption spectra of perovskite films with the one-step and the two-step methods.</p>
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<p>Photoluminescence (PL) spectra of perovskite films with the one-step process method (<b>a</b>) and the two-step process method (<b>b</b>).</p>
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<p>Photoluminescence (PL) spectra of perovskite films with the one-step process method (<b>a</b>) and the two-step process method (<b>b</b>).</p>
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<p>Photocurrent voltage density reverse scan (RS) curve of One-step carbon, Two-step carbon and Two-step gold.</p>
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32 pages, 4954 KiB  
Review
Nanotechnology in Transportation Vehicles: An Overview of Its Applications, Environmental, Health and Safety Concerns
by Muhammad Shafique and Xiaowei Luo
Materials 2019, 12(15), 2493; https://doi.org/10.3390/ma12152493 - 6 Aug 2019
Cited by 74 | Viewed by 12005
Abstract
Nanotechnology has received increasing attention and is being applied in the transportation vehicle field. With their unique physical and chemical characteristics, nanomaterials can significantly enhance the safety and durability of transportation vehicles. This paper reviews the state-of-the-art of nanotechnology and how this technology [...] Read more.
Nanotechnology has received increasing attention and is being applied in the transportation vehicle field. With their unique physical and chemical characteristics, nanomaterials can significantly enhance the safety and durability of transportation vehicles. This paper reviews the state-of-the-art of nanotechnology and how this technology can be applied in improving the comfort, safety, and speed of transportation vehicles. Moreover, this paper systematically examines the recent developments and applications of nanotechnology in the transportation vehicle industry, including nano-coatings, nano filters, carbon black for tires, nanoparticles for engine performance enchantment and fuel consumption reduction. Also, it introduces the main challenges for broader applications, such as environmental, health and safety concerns. Since several nanomaterials have shown tremendous performance and have been theoretically researched, they can be potential candidates for applications in future environmental friendly transportation vehicles. This paper will contribute to further sustainable research and greater potential applications of environmentally friendly nanomaterials in healthier transportation vehicles to improve the transportation industry around the globe. Full article
(This article belongs to the Special Issue Advanced Materials for Transport Applications 2020)
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<p>The representation of nanomaterials’ length measured in nanosize [<a href="#B1-materials-12-02493" class="html-bibr">1</a>].</p>
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<p>Potential applications of nanotechnology in transportation and the associated environmental health and safety concerns.</p>
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<p>The flowchart diagram for screening articles for this study.</p>
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<p>Impact of and demands for nanotechnology applications in the transportation vehicle industry.</p>
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<p>Representation of resistance to erosive wear of various coatings against aging time [<a href="#B46-materials-12-02493" class="html-bibr">46</a>].</p>
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<p>Nanomaterial self-repairing mechanism for surface coatings [<a href="#B50-materials-12-02493" class="html-bibr">50</a>].</p>
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<p>Representing the surface properties on glass plates in (<b>a</b>) conventional mirror (untreated surfaces) and (<b>b</b>) modern antiglare mirror (hydrophobic) [<a href="#B38-materials-12-02493" class="html-bibr">38</a>].</p>
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<p>Illustration of the effect of various concentrations of Al<sub>2</sub>O<sub>3</sub> nanofluid on the heat exchange efficiency of heat recovery of an engine [<a href="#B66-materials-12-02493" class="html-bibr">66</a>].</p>
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<p>CFRP composite applications in various components of an Airbus 350 (source: Hexcel [<a href="#B93-materials-12-02493" class="html-bibr">93</a>]).</p>
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<p>Comparison of the thermal conductivity of a PCM incorporated with nano-architecture (0%, 2%, 5% of Al<sub>2</sub>O<sub>3</sub>) [<a href="#B107-materials-12-02493" class="html-bibr">107</a>].</p>
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<p>Variation of the water contact angle with temperature in the coatings (Polyvinylidene fluoride and multiwall carbon nanotube [<a href="#B109-materials-12-02493" class="html-bibr">109</a>].</p>
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<p>The variation of corrosion rate vs. time of three surfaces in a marine environment [<a href="#B117-materials-12-02493" class="html-bibr">117</a>].</p>
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<p>Ship’s hull showing a patch covered with silicon hydrogel (right side), whereas slime and algae are found on the hull with SPC coating paint (left side). Reprinted from [<a href="#B120-materials-12-02493" class="html-bibr">120</a>] with the permission of the American Chemical Society, copyright 2019.</p>
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<p>Nanotechnology environmental health and safety concerns.</p>
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<p>Nanomaterials versus likelihood of exposure [<a href="#B160-materials-12-02493" class="html-bibr">160</a>].</p>
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<p>Nano-safety framework for enhanced safety in the nano-industry. Adopted from [<a href="#B180-materials-12-02493" class="html-bibr">180</a>].</p>
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<p>Major four research gaps and future opportunities which need to be considered for the broad and sustainable application of nanotechnology in transportation vehicles.</p>
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12 pages, 4642 KiB  
Article
The Interface and Mechanical Properties of a CVD Single Crystal Diamond Produced by Multilayered Nitrogen Doping Epitaxial Growth
by Yun Zhao, Chengming Li, Jinlong Liu, Kang An, Xiongbo Yan, Lifu Hei, Liangxian Chen, Junjun Wei and Fanxiu Lu
Materials 2019, 12(15), 2492; https://doi.org/10.3390/ma12152492 - 6 Aug 2019
Cited by 11 | Viewed by 4400
Abstract
In the present investigation, a nitrogen-doped multilayer homoepitaxial single crystal diamond is synthesized on a high-pressure high temperature (HPHT) Ib-type diamond substrate using the microwave plasma chemical vapor deposition (MPCVD) method. When 0.15 sccm of nitrogen was added in the gas phase, the [...] Read more.
In the present investigation, a nitrogen-doped multilayer homoepitaxial single crystal diamond is synthesized on a high-pressure high temperature (HPHT) Ib-type diamond substrate using the microwave plasma chemical vapor deposition (MPCVD) method. When 0.15 sccm of nitrogen was added in the gas phase, the growth rate of the doped layer was about 1.7 times that of the buffer layer, and large conical and pyramidal features are formed on the surface of the sample. Raman mapping and photoluminescence imaging of the polished cross sectional slice shows a broadband emission, with a characteristic zero phonon line (ZPL) at 575 nm in the doped layers, and large compressive stress was formed in the nitrogen-doped layers. X-ray topography shows that the defects at the interface can induce dislocation. The pyramid feature is formed at the defect, and more nitrogen-related defects are formed in the pyramid region. Thin nitrogen-doped multilayers were successfully prepared, and the thickness of the nitrogen-doped and buffer layers was about 650 nm each. The indentation measurements reveal that the thin nitrogen-doped multilayers are ultra-tough (at least ~22 MPa m1/2), compared to the Ib-type HPHT seed substrate (~8 MPa m1/2) and the unintentionally doped chemical vapor deposition (CVD) single crystal diamond (~14 MPa m1/2). Full article
(This article belongs to the Special Issue Functional Surface Structures and Thin Solid Films)
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<p>Schematic of the chemical vapor deposition (CVD) layers of sample 1 with various amounts of added N<sub>2</sub>. The white and light gray layers correspond to the buffer and the nitrogen-doped layers, respectively. The yellow part corresponds to the Ib-type high-pressure high temperature (HPHT) seed substrate.</p>
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<p>(<b>a</b>) Schematic of laser cutting of the nitrogen-doped multilayers grown on the HPHT seed substrate. The two cutting planes perpendicular to the surface are shown in light green. (<b>b</b>) Optical image of the 400-μm-thick cross section slice obtained after laser-cutting and polishing of the lateral faces.</p>
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<p>(<b>a</b>) Laser-scanning Raman images show the Raman mapping of the diamond peak shift (left inset) and the fluorescence intensity of the NV<sup>0</sup> defect of the cross section slice (white dotted line area). Correspondingly, the diamond peak shift (1332.6–1335.5 cm<sup>−1</sup>) and the fluorescence intensity of NV<sup>0</sup> (0–3200 counts) are shown in the same color bar on the top. (<b>b</b>) Raman spectra recorded at room temperature for the 0.12 sccm nitrogen-doped layer and the buffer layer, respectively. (<b>c</b>) UV-excited photoluminescence image of the polished cross sectional slice of the nitrogen-doped multilayer CVD diamond grown on the Ib-type HPHT substrate.</p>
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<p>Optical microscope image of the surface morphology of sample 1 prepared with intentional addition of N<sub>2</sub>. The blue dotted lines mark the conical and pyramidal features on the surface.</p>
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<p>(<b>a</b>,<b>b</b>) Optical images showing the surface morphology and the cross section of the pyramidal feature, respectively. (<b>c</b>) Raman image of the defect formed at the interface was recorded by measuring the signal intensity at 1420 cm<sup>−1</sup> (corresponding to the emission from the NV<sup>0</sup> defect).</p>
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<p>(<b>a</b>,<b>b</b>) Optical images showing the surface morphology and the cross section of the pyramidal feature, respectively. (<b>c</b>) Raman image of the defect formed at the interface was recorded by measuring the signal intensity at 1420 cm<sup>−1</sup> (corresponding to the emission from the NV<sup>0</sup> defect).</p>
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<p>(<b>a</b>) XRT image of the (100)-cut slice of the sample 1 showing the interface between the HPHT seed substrate and the CVD layer, which is indicated by the green arrow. (<b>b</b>) Magnified XRT image of the pyramidal feature. The image shows that a number of dislocations are formed at the defect, and some of the dislocations are bent along the direction of the step flow. (<b>c</b>) Optical microscope image of surface morphology of the HPHT seed substrate after plasma etching.</p>
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<p>(<b>a</b>) XRT image of the (100)-cut slice of the sample 1 showing the interface between the HPHT seed substrate and the CVD layer, which is indicated by the green arrow. (<b>b</b>) Magnified XRT image of the pyramidal feature. The image shows that a number of dislocations are formed at the defect, and some of the dislocations are bent along the direction of the step flow. (<b>c</b>) Optical microscope image of surface morphology of the HPHT seed substrate after plasma etching.</p>
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<p>(<b>a</b>) Surface morphology of sample 2. (<b>b</b>) Raman scan of the cross section of sample 2 showing the presence of alternating thin nitrogen-doped and buffer layers. The inset shows the Raman spectra of the first-order phonon peak of diamond in different positions.</p>
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<p>(<b>a</b>) Surface morphology of sample 2. (<b>b</b>) Raman scan of the cross section of sample 2 showing the presence of alternating thin nitrogen-doped and buffer layers. The inset shows the Raman spectra of the first-order phonon peak of diamond in different positions.</p>
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<p>Secondary ion mass spectroscopy (SIMS) profile of the thin nitrogen-doped multilayers of sample 2.</p>
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<p>The indented surfaces of the samples viewed via SEM, in which the parameters a<sub>1</sub>, a<sub>2</sub>, b<sub>1</sub>, and b<sub>2</sub> used to determine the Vickers hardness and fracture toughness are indicated. (<b>a</b>) The indented surface of the Ib-type HPHT seed substrate. (<b>b</b>,<b>c</b>) The indented surfaces of the samples 3 and 2, respectively.</p>
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16 pages, 16419 KiB  
Article
3D Printing of Conductive Tissue Engineering Scaffolds Containing Polypyrrole Nanoparticles with Different Morphologies and Concentrations
by Chunyang Ma, Le Jiang, Yingjin Wang, Fangli Gang, Nan Xu, Ting Li, Zhongqun Liu, Yongjie Chi, Xiumei Wang, Lingyun Zhao, Qingling Feng and Xiaodan Sun
Materials 2019, 12(15), 2491; https://doi.org/10.3390/ma12152491 - 6 Aug 2019
Cited by 38 | Viewed by 6281
Abstract
Inspired by electrically active tissues, conductive materials have been extensively developed for electrically active tissue engineering scaffolds. In addition to excellent conductivity, nanocomposite conductive materials can also provide nanoscale structure similar to the natural extracellular microenvironment. Recently, the combination of three-dimensional (3D) printing [...] Read more.
Inspired by electrically active tissues, conductive materials have been extensively developed for electrically active tissue engineering scaffolds. In addition to excellent conductivity, nanocomposite conductive materials can also provide nanoscale structure similar to the natural extracellular microenvironment. Recently, the combination of three-dimensional (3D) printing and nanotechnology has opened up a new era of conductive tissue engineering scaffolds exhibiting optimized properties and multifunctionality. Furthermore, in the case of two-dimensional (2D) conductive film scaffolds such as periosteum, nerve membrane, skin repair, etc., the traditional preparation process, such as solvent casting, produces 2D films with defects of unequal bubbles and thickness frequently. In this study, poly-l-lactide (PLLA) conductive scaffolds incorporated with polypyrrole (PPy) nanoparticles, which have multiscale structure similar to natural tissue, were prepared by combining extrusion-based low-temperature deposition 3D printing with freeze-drying. Furthermore, we creatively integrated the advantages of 3D printing and solvent casting and successfully developed a 2D conductive film scaffold with no bubbles, uniform thickness, and good structural stability. Subsequently, the effects of concentration and morphology of PPy nanoparticles on electrical properties and mechanical properties of 3D conductive scaffolds and 2D conductive films scaffolds have been studied, which provided a new idea for the design of both 2D and 3D electroactive tissue engineering scaffolds. Full article
(This article belongs to the Special Issue Electro-Active Scaffolds for Tissue Engineering)
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<p>SEM images (<b>a</b>) and TEM images (<b>b</b>) of tubular PPy nanoparticles (T-PPy), SEM images (<b>c</b>) and TEM images (<b>d</b>) of spherical PPy nanoparticles (S-PPy). Scar bar is 200 nm.</p>
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<p>Viscosity curve of 3D printing ink containing polypyrrole (PPy) nanoparticles with different concentration and morphology in the speed range of 0.1–100 rad/s.</p>
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<p>Optical and SEM images of 3D conductive scaffolds containing 10 wt% T-PPy or S-PPy prepared by combining 3D printing and freeze-drying. (<b>a</b>–<b>c</b>) Optical images of 3D conductive scaffolds (pure, tubular, and spherical in turn), (<b>d</b>–<b>f</b>) SEM images of the scaffolds at the magnification of 26, scar bar is 200 μm, (pure, tubular, and spherical in turn), (<b>g</b>–<b>i</b>) SEM images of the scaffolds at the magnification of 1000, scar bar is 10 μm, (<b>j</b>–<b>l</b>) SEM images of the scaffolds at the magnification of 10,000, scar bar is 1 μm.</p>
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<p>Conductivity of 3D conductive scaffolds.</p>
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<p>Compressive strength of 3D conductive scaffolds.</p>
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<p>SEM images of pure poly-l-lactide (PLLA) film and films containing 10 wt% T-PPy and S-PPy, (<b>a</b>–<b>c</b>) physical images of three films, scar bar is 1 cm (pure, T-PPy, and S-PPy, in turn)), (<b>d</b>–<b>f</b>) SEM images of three films at 104 magnification, scar bar is 200 μm (10 wt% PPy, T-PPy, and S-PPy, in turn), (<b>g</b>–<b>i</b>) SEM images of three films at 10,000 magnification, and scar bar is 1 μm (10 wt% PPy, T-PPy, and S-PPy, in turn).</p>
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<p>Conductivity of 2D conductive films.</p>
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<p>Tensile strength of 2D conductive films.</p>
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<p>Viability of L929 cells cultured on pure PLLA films and films containing spherical or tubular PPy nanoparticles, compared with blank control group.</p>
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<p>Schematic illustration of the overall experimental design.</p>
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9 pages, 3427 KiB  
Article
Bending Strain and Bending Fatigue Lifetime of Flexible Metal Electrodes on Polymer Substrates
by Tae-Wook Kim, Jong-Sung Lee, Young-Cheon Kim, Young-Chang Joo and Byoung-Joon Kim
Materials 2019, 12(15), 2490; https://doi.org/10.3390/ma12152490 - 6 Aug 2019
Cited by 59 | Viewed by 10765
Abstract
As the technology of flexible electronics has remarkably advanced, the long-term reliability of flexible devices has attracted much attention, as it is an important factor for such devices in reaching real commercial viability. To guarantee the bending fatigue lifetime, the exact evaluation of [...] Read more.
As the technology of flexible electronics has remarkably advanced, the long-term reliability of flexible devices has attracted much attention, as it is an important factor for such devices in reaching real commercial viability. To guarantee the bending fatigue lifetime, the exact evaluation of bending strain and the change in electrical resistance is required. In this study, we investigated the bending strains of Cu thin films on flexible polyimide substrates with different thicknesses using monolayer and bilayer bending models and monitored the electrical resistance of the metal electrode during a bending fatigue test. For a thin metal electrode, the bending strain and fatigue lifetime were similar regardless of substrate thickness, but for a thick metal film, the fatigue lifetime was changed by different bending strains in the metal electrode according to substrate thickness. To obtain the exact bending strain distribution, we conducted a finite-element simulation and compared the bending strains of thin and thick metal structures. For thick metal electrodes, the real bending strain obtained from a bilayer model or simulation showed values much different from those from a simple monolayer model. This study can provide useful guidelines for developing highly reliable flexible electronics. Full article
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<p>(<b>a</b>) Schematic illustrations and equations for calculating bending strain using monolayer and bilayer models. (<b>b</b>) Schematic and image of a bending fatigue test and an electrical resistance monitoring system.</p>
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<p>(<b>a</b>) Normalized electrical resistance changes of 100 nm thick Cu film on 50, 75, and 125 µm thick polyimide (PI) as a function of the number of bending cycles under bending strain amplitudes of 0.7%, 1%, and 1.5%. (<b>b</b>) SEM images of 100 nm thick Cu film after the bending fatigue test.</p>
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<p>(<b>a</b>) Normalized electrical resistance changes of 1 μm thick Cu film on 50, 75, and 125 μm thick PI as a function of the number of bending cycles under bending strain amplitudes of 0.7%, 1%, and 1.5%. (<b>b</b>) SEM images of 1 μm thick Cu film after the bending fatigue test.</p>
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<p>Calculated bending strains of (<b>a</b>) 100 nm thick Cu film and (<b>b</b>) 1 μm thick Cu film using monolayer and bilayer models.</p>
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<p>Finite-element method (FEM) modeling and strain distributions: (<b>a</b>) 100 nm thick Cu on 50 μm thick PI, (<b>b</b>) 100 nm thick Cu on 125 μm, (<b>c</b>) 1 μm thick Cu on 50 μm thick PI, and (<b>d</b>) 1 μm thick Cu on 125 μm thick PI.</p>
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21 pages, 12152 KiB  
Article
Efficacy of Bacterial Cellulose as a Carrier of BMP-2 for Bone Regeneration in a Rabbit Frontal Sinus Model
by Takashi Koike, Jingjing Sha, Yunpeng Bai, Yuhei Matsuda, Katsumi Hideshima, Takaya Yamada and Takahiro Kanno
Materials 2019, 12(15), 2489; https://doi.org/10.3390/ma12152489 - 6 Aug 2019
Cited by 21 | Viewed by 4172
Abstract
If the alveolar bone height of patients requiring dental implants in the maxillary molar region is inadequate, it is difficult to achieve satisfactory outcomes using existing bone graft materials. We previously reported the possible utility of bacterial cellulose (BC) as a new dental [...] Read more.
If the alveolar bone height of patients requiring dental implants in the maxillary molar region is inadequate, it is difficult to achieve satisfactory outcomes using existing bone graft materials. We previously reported the possible utility of bacterial cellulose (BC) as a new dental treatment material. BC has a high absorptive capacity, good mechanical strength, and good volume retention. BC loaded with bone morphogenetic protein-2 (BMP-2) might allow effective alveolar bone augmentation. We created critical frontal bone defect models in 12 male Japanese white rabbits and divided them into four groups: sham; BC (BC grafting only); BMP-2 (treated with BMP-2 solution only); and BC+BMP-2 (grafted with BC loaded with BMP-2). Newly formed bone volume was calculated via hematoxylin-eosin staining evaluation. The proliferating cell nuclear antigen and osteocalcin levels were determined by the immunohistochemical staining analysis. All measured indices of the BC+BMP-2 group were significantly superior to those of the other groups (all p < 0.05). BC maintained the graft space and released BMP-2 in a sustained manner, promoting optimal bone formation. The BC+BMP-2 combination enhanced bone regeneration and shows promise as a useful means of clinical pre-dental implant bone augmentation in the maxillary sinus. Full article
(This article belongs to the Special Issue Micro and Nanotechnologies in Biomedicines)
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<p>SEM micrographs of surface and cross-section of BC. (<b>A</b>) The surface of BC observed under 10.0 kx magnification. (<b>B</b>) The surface of BC observed under 50.0 kx magnification. (<b>C</b>) The cross-section of BC observed under 5000× magnification.</p>
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<p>The schematics shows the experimental animal procedure of a rabbit frontal sinus model in the frontal view. Experimental animal procedure: (<b>A</b>). Incision line in the rabbit frontal sinus area; (<b>B</b>) Excision of 7 × 5 mm windows in the bilateral frontal bone; (<b>C</b>). Movement of the bone wall and reflection of the sinus membrane using a mucosal elevator to form sufficient grafting space; (<b>D</b>). The left side was used as a sham control (no graft) and the right side received the graft in the BC, BMP-2, and BC+BMP-2 groups.</p>
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<p>H&amp;E staining in the (<b>a</b>): sham (n = 3), (<b>b</b>): BC (n = 3), (<b>c</b>): BMP-2 (n = 3), and (<b>d</b>): BC+BMP-2 (n = 3) groups at four and eight weeks. Blue arrows indicate connective tissue, black arrows indicate newly formed bone, and yellow arrows indicate cartilage tissue. HBS, host bone side; SMS, sinus membrane side; BC, bacterial cellulose. White scale bars (500 μm) indicate slices at 4× magnification; black scale bars (100 μm) indicate slices at 20× magnification.</p>
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<p>H&amp;E staining in the (<b>a</b>): sham (n = 3), (<b>b</b>): BC (n = 3), (<b>c</b>): BMP-2 (n = 3), and (<b>d</b>): BC+BMP-2 (n = 3) groups at four and eight weeks. Blue arrows indicate connective tissue, black arrows indicate newly formed bone, and yellow arrows indicate cartilage tissue. HBS, host bone side; SMS, sinus membrane side; BC, bacterial cellulose. White scale bars (500 μm) indicate slices at 4× magnification; black scale bars (100 μm) indicate slices at 20× magnification.</p>
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<p>H&amp;E staining analysis of newly formed bone values: (<b>A</b>) Comparison of newly formed bone values between different groups, analyzed by One-way analysis of variance and LSD-<span class="html-italic">t</span> test. * <span class="html-italic">p</span> &lt; 0.05; NS: no significance. Error bars indicate standard deviations. (<b>B</b>) Comparison of newly formed bone values between four and eight weeks, analyzed by independent-samples <span class="html-italic">t</span>-test; * <span class="html-italic">p</span> &lt; 0.05; NS: no significance. Error bars indicate standard deviations.</p>
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<p>Immunohistochemical staining of PCNA expression in the (<b>a</b>): sham (n = 3), (<b>b</b>): BC (n = 3), (<b>c</b>): BMP-2 (n = 3), and (<b>d</b>): BC+BMP-2 (n = 3) groups at four and eight weeks. Blue arrows indicate connective tissue, black arrows indicate newly formed bone, and yellow arrows indicate cartilage tissue. HBS, host bone side; SMS, sinus membrane side; BC, bacterial cellulose. White scale bars (500 μm) indicate slices at 4× magnification; black scale bars (100 μm) indicate slices at 20× magnification.</p>
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<p>Immunohistochemical staining of PCNA expression in the (<b>a</b>): sham (n = 3), (<b>b</b>): BC (n = 3), (<b>c</b>): BMP-2 (n = 3), and (<b>d</b>): BC+BMP-2 (n = 3) groups at four and eight weeks. Blue arrows indicate connective tissue, black arrows indicate newly formed bone, and yellow arrows indicate cartilage tissue. HBS, host bone side; SMS, sinus membrane side; BC, bacterial cellulose. White scale bars (500 μm) indicate slices at 4× magnification; black scale bars (100 μm) indicate slices at 20× magnification.</p>
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<p>Immunohistochemical staining of PCNA expression in the (<b>a</b>): sham (n = 3), (<b>b</b>): BC (n = 3), (<b>c</b>): BMP-2 (n = 3), and (<b>d</b>): BC+BMP-2 (n = 3) groups at four and eight weeks. Blue arrows indicate connective tissue, black arrows indicate newly formed bone, and yellow arrows indicate cartilage tissue. HBS, host bone side; SMS, sinus membrane side; BC, bacterial cellulose. White scale bars (500 μm) indicate slices at 4× magnification; black scale bars (100 μm) indicate slices at 20× magnification.</p>
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<p>Immunohistochemical staining analysis of PCNA-positive cell ratios: (<b>A</b>) Comparison of the PCNA-positive cell ratios between groups, analyzed by one-way analysis of variance and LSD-<span class="html-italic">t</span> test. * <span class="html-italic">p</span> &lt; 0.05; NS: no significance. Error bars indicate standard deviations. (<b>B</b>) Comparison of PCNA-positive cell ratios between time points, analyzed by independent-samples <span class="html-italic">t</span>-test. * <span class="html-italic">p</span> &lt; 0.05; NS: no significance. Error bars indicate standard deviations.</p>
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<p>Immunohistochemical staining analysis of PCNA-positive cell ratios: (<b>A</b>) Comparison of the PCNA-positive cell ratios between groups, analyzed by one-way analysis of variance and LSD-<span class="html-italic">t</span> test. * <span class="html-italic">p</span> &lt; 0.05; NS: no significance. Error bars indicate standard deviations. (<b>B</b>) Comparison of PCNA-positive cell ratios between time points, analyzed by independent-samples <span class="html-italic">t</span>-test. * <span class="html-italic">p</span> &lt; 0.05; NS: no significance. Error bars indicate standard deviations.</p>
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<p>Immunohistochemical staining of OC expression in the (<b>a</b>): sham (n = 3), (<b>b</b>): BC (n = 3), (<b>c</b>): BMP-2 (n = 3), and (<b>d</b>): BC+BMP-2 (n = 3) groups at four and eight weeks. Blue arrows indicate connective tissue, black arrows indicate newly formed bone, and yellow arrows indicate cartilage tissue. HBS, host bone side; SMS, sinus membrane side; BC, bacterial cellulose. White scale bars (500 μm) indicate slices at 4× magnification; black scale bars (100 μm) indicate slices at 20× magnification.</p>
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<p>Immunohistochemical staining of OC expression in the (<b>a</b>): sham (n = 3), (<b>b</b>): BC (n = 3), (<b>c</b>): BMP-2 (n = 3), and (<b>d</b>): BC+BMP-2 (n = 3) groups at four and eight weeks. Blue arrows indicate connective tissue, black arrows indicate newly formed bone, and yellow arrows indicate cartilage tissue. HBS, host bone side; SMS, sinus membrane side; BC, bacterial cellulose. White scale bars (500 μm) indicate slices at 4× magnification; black scale bars (100 μm) indicate slices at 20× magnification.</p>
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<p>Immunohistochemical staining analysis of OC-stained area ratios: (<b>A</b>) Comparison of OC-stained area ratios between groups, analyzed by one-way analysis of variance and LSD-<span class="html-italic">t</span> test. * <span class="html-italic">p</span> &lt; 0.05; NS: no significance. Error bars indicate standard deviations. (<b>B</b>) Comparison of OC-stained area ratios between time points, analyzed by independent-samples <span class="html-italic">t</span>-test. * <span class="html-italic">p</span> &lt; 0.05; NS: no significance. Error bars indicate standard deviations.</p>
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20 pages, 8095 KiB  
Article
Isothermal Crystallization Kinetics of Poly(4-hydroxybutyrate) Biopolymer
by Ina Keridou, Luis J. del Valle, Lutz Funk, Pau Turon, Ibraheem Yousef, Lourdes Franco and Jordi Puiggalí
Materials 2019, 12(15), 2488; https://doi.org/10.3390/ma12152488 - 6 Aug 2019
Cited by 13 | Viewed by 4168
Abstract
Thermal properties and crystallization kinetics of poly(4-hydroxybutyrate) (P4HB) have been studied. The polymer shows the typical complex melting behavior associated to different lamellar populations. Annealing processes had great repercussions on properties and the morphology of constitutive lamellae as verified by X-ray scattering data. [...] Read more.
Thermal properties and crystallization kinetics of poly(4-hydroxybutyrate) (P4HB) have been studied. The polymer shows the typical complex melting behavior associated to different lamellar populations. Annealing processes had great repercussions on properties and the morphology of constitutive lamellae as verified by X-ray scattering data. Kinetics of isothermal crystallization was evaluated by both polarizing optical microscopy (POM) and calorimetric (DSC) measurements, which indicated a single crystallization regime. P4HB rendered banded spherulites with a negative birefringence when crystallized from the melt. Infrared microspectroscopy was applied to determine differences on the molecular orientation inside a specific ring according to the spherulite sectorization or between different rings along a determined spherulitic radius. Primary nucleation was increased during crystallization and when temperature decreased. Similar crystallization parameters were deduced from DSC and POM analyses (e.g., secondary nucleation parameters of 1.69 × 105 K2 and 1.58 × 105 K2, respectively). The effect of a sporadic nucleation was therefore minimized in the experimental crystallization temperature range and a good proportionality between overall crystallization rate (k) and crystal growth rate (G) was inferred. Similar bell-shaped curves were postulated to express the temperature dependence of both k and G rates, corresponding to the maximum of these curves close to a crystallization temperature of 14–15 °C. Full article
(This article belongs to the Special Issue Biomedical Applications of Polyesters and Related Polymers)
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Graphical abstract

Graphical abstract
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<p>Sequence of calorimetric and heating runs performed with the initial commercial suture of poly(4-hydroxybutyrate (P4HB): (<b>a</b>) First heating run performed at 10 °C/min; (<b>b</b>) Cooling run at 10 °C/min after keeping the sample in the melt state for one min; (<b>c</b>) Heating run at 10 °C/min of the above melt crystallized samples and (<b>d</b>) Heating run at 10 °C/min of a sample quenched from the melt at the maximum rate allowed by the equipment.</p>
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<p>Calorimetric (DSC) heating runs performed at the indicated rates with the commercial P4HB (Poly(4-hydroxybutyrate)) suture.</p>
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<p>Wide angle X-ray diffraction (WAXD) profiles (<b>a</b>); Small angle X-ray scattering (SAXS) profiles (<b>b</b>) and correlation functions (<b>c</b>) of the initial commercial P4HB suture (red line) and a P4HB melt crystallized sample (blue line). Deconvoluted WAXD peaks are only indicated for the melt crystallized sample.</p>
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<p>DSC heating runs of P4HB previously crystallized at the indicated temperatures.</p>
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<p>Hoffman-Weeks plot for P4HB considering the temperatures of its first melting peak.</p>
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<p>Exothermic DSC peaks corresponding to the isothermal crystallization from the melt state performed between 24 °C and 38 °C (<b>a</b>) and the cold crystallization performed between −26 °C and −20 °C (<b>b</b>).</p>
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<p>Evolution of the relative crystallinity over time for isothermal crystallizations of P4HB at the indicated temperatures. (<b>a</b>) Samples coming from the melt state; (<b>b</b>) Glassy sample obtained from a fast cooling from the melt.</p>
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<p>Avrami plots obtained from isothermal melt (<b>a</b>) and cold (<b>b</b>) crystallizations.</p>
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<p>(<b>a</b>) Experimental (<b>×</b>) and simulated (<b>●</b>) temperature dependence of the overall crystallization rate of P4HB for isothermal melt crystallization. For the sake of completeness experimental cold crystallization data are also plotted (×); (<b>b</b>) Temperature dependence of the overall crystallization rates (<b>◊</b>, ◊) and the reciprocal crystallization half-times (о, о) of P4HB for melt and cold crystallizations.</p>
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<p>Optical micrographs showing P4HB spherulites crystallized at 36 °C (<b>a</b>) and 47 °C (<b>b</b>). The inset of (<b>b</b>) corresponds to a micrograph taken with a red tint plate.to determine the spherulite sign.</p>
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<p>Temperature dependence of the primary nucleation density for crystallization performed from the melt state.</p>
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<p>Optical micrographs showing P4HB spherulites crystallized at 47 °C for (<b>a</b>) 100 min, (<b>b</b>) 150 min, (<b>c</b>) 180 min, (<b>d</b>) 250 min, (<b>e</b>) 350 min and (<b>f</b>) 350 min. In the case of (<b>f</b>), the micrograph has been taken with a red tint plate. Comparison of micrographs taken after 47 min (<b>g</b>) and 80 min (<b>h</b>) for the crystallization performed at 46 °C. The dashed red circle points out the region where the apparition of a new spherulite is clear.</p>
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<p>Variation of the spherulitic radius with crystallization time for temperatures between 37 °C and 42 °C (<b>a</b>) and 43 °C and 49 °C (<b>b</b>).</p>
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<p>(<b>a</b>) FTIR spectra of THE P4HB suture with labelling of main bands; (<b>b</b>) Optical polarized micrographs showing spherulites developed in a solvent casting film. Insets show the chemical image obtained from C=O and CH<sub>2</sub> (shoulder) bands; (<b>c</b>) Micrographs showing a representative banded spherulite and the specific microdomains were FTIR spectra were recorded; (<b>d</b>) Microinfrared spectra taken from the indicated microdomains (keeping the colour code). Different magnifications and wavenumber regions are showed.</p>
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<p>Lauritzen-Hoffman plots for the crystal growth rate (<b>a</b>) and the overall crystallization rate (<b>b</b>) for the isothermal crystallization of P4HB.</p>
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<p>Temperature dependence of the crystal growth (●, <b>◊</b>) and overall crystallization (●, <b>◊</b>) rate. Simulated data is represented by circles and experimental data by rhombus.</p>
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10 pages, 2343 KiB  
Article
Annealing-Induced Changes in the Nature of Point Defects in Sublimation-Grown Cubic Silicon Carbide
by Michael Schöler, Clemens Brecht and Peter J. Wellmann
Materials 2019, 12(15), 2487; https://doi.org/10.3390/ma12152487 - 6 Aug 2019
Cited by 3 | Viewed by 3867
Abstract
In recent years, cubic silicon carbide (3C-SiC) has gained increasing interest as semiconductor material for energy saving and optoelectronic applications, such as intermediate-band solar cells, photoelectrochemical water splitting, and quantum key distribution, just to name a few. All these applications critically depend on [...] Read more.
In recent years, cubic silicon carbide (3C-SiC) has gained increasing interest as semiconductor material for energy saving and optoelectronic applications, such as intermediate-band solar cells, photoelectrochemical water splitting, and quantum key distribution, just to name a few. All these applications critically depend on further understanding of defect behavior at the atomic level and the possibility to actively control distinct defects. In this work, dopants as well as intrinsic defects were introduced into the 3C-SiC material in situ during sublimation growth. A series of isochronal temperature treatments were performed in order to investigate the temperature-dependent annealing behavior of point defects. The material was analyzed by temperature-dependent photoluminescence (PL) measurements. In our study, we found a variation in the overall PL intensity which can be considered as an indication of annealing-induced changes in structure, composition or concentration of point defects. Moreover, a number of dopant-related as well as intrinsic defects were identified. Among these defects, there were strong indications for the presence of the negatively charged nitrogen vacancy complex (NC–VSi), which is considered a promising candidate for spin qubits. Full article
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<p>As-grown bulk cubic silicon carbide (3C-SiC) sample and typical temperature dependent photoluminescence (PL) spectra of the sample: (<b>a</b>) backlight image of the as-grown bulk 3C-SiC sample prepared by epitaxial sublimation growth. The inhomogeneities of the coloring originate from carbon inclusions, protrusions, and, primarily, residuals from the seed mounting on the back side of the layer; (<b>b</b>) typical temperature-dependent PL-spectra of the as-grown 3C-SiC. The spectra were acquired with a 405 nm laser. Three sections were classified and labeled as second-order-diffraction (SOD), near-infrared (NIR), and visible (VIS) luminescence.</p>
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<p>Identification of peak positions in the second-order-diffraction (SOD) and visible (VIS) regimes: (<b>a</b>) Within the SOD regime, four distinct peaks can be identified. Two of them were assigned to SOD of VIS and two originated from point defects. The spectra were acquired with the 405 nm laser and the InGaAs detector. (<b>b</b>) Within the VIS regime, four distinct peaks can be identified. Two of them were assigned to donor–acceptor pairs (DAP) and two of them were assigned to defect centers originating from point defects. The spectra were acquired with the 405 nm laser and the charge-coupled device (CCD) detector after the annealing step at 100 °C.</p>
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<p>Behavior of (<b>a</b>) SOD and (<b>b</b>) VIS during temperature treatments. For improved clarity, only distinct temperatures of “as-grown” (without T-treatment), 700 °C, 850 °C, and 1300 °C are shown. The arrows indicate the shift of PL spectra after annealing. All spectra in both diagrams were acquired at a PL temperature of 50 K after temperature treatment. For excitation, the 405 nm laser was used in combination with the InGaAs detector. The shaded areas describe the variance of the reproducible reaching of the measuring position.</p>
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<p>Integrated intensities of the VIS regime (1.5–2.15 eV) and SOD regime (0.73–1.08 eV) as a function of annealing temperature. Mechanisms explaining the curve characteristics are indicated in the diagram. The spectra were acquired with the 405 nm laser and the InGaAs detector at a measuring temperature of 50 K.</p>
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16 pages, 4027 KiB  
Article
Biosorption of Methylene Blue Dye Using Natural Biosorbents Made from Weeds
by Francisco Silva, Lorena Nascimento, Matheus Brito, Kleber da Silva, Waldomiro Paschoal and Roberto Fujiyama
Materials 2019, 12(15), 2486; https://doi.org/10.3390/ma12152486 - 5 Aug 2019
Cited by 74 | Viewed by 4980
Abstract
The purpose of this work is to make use of vegetables that, although widely found in nature, there are few applications. The weeds used here, Cyanthilium cinereum (L.) H. Rob (CCLHR) and Paspalum maritimum (PMT) found in the Amazon region of Belém state [...] Read more.
The purpose of this work is to make use of vegetables that, although widely found in nature, there are few applications. The weeds used here, Cyanthilium cinereum (L.) H. Rob (CCLHR) and Paspalum maritimum (PMT) found in the Amazon region of Belém state of Pará-Brazil, contribute to the problem of water contamination by the removal of the methylene blue dye through the biosorption process, taking advantage of other materials for economic viability and processing. The influences of parameters such as, biosorbent dose, contact time, and initial concentration of dye were examined. The characterizations were realized using SEM to verify the morphology of the material and spectroscopy in the FTIR region. As for the adsorption mechanism, the physical adsorption mechanism prevailed. The time required for the system to reach equilibrium for both biosorbents was from 50 min, following a kinetics described by the pseudo-second order model. The adsorption isotherm data for PMT were better adjusted to the Langmuir model and the biosorption capacity ( q m a x ) value was (56.1798 mg/g). CCLHR was better adjusted to the Freundlich model and its maximum biosorption capacity was 76.3359 mg/g. Thus, these weed species are promising for the biosorption of methylene blue dye in effluents. Full article
(This article belongs to the Special Issue Porous Materials for Environmental Applications)
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<p>Infrared spectrum of <span class="html-italic">Paspalum maritimum</span> (PMT) (<b>a</b>) and CCLHR (<b>b</b>) samples, in the range of 400–4000 cm<sup>−1</sup>.</p>
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<p>Scanning electron microscope (SEM) image of (<b>a</b>) PMT with magnification of 2190× and (<b>b</b>) CCLHR with magnification of 1720×.</p>
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<p>Biosorbent dose vs. biosorption capacity vs. percentage of removal: (<b>a</b>) PMT and (<b>b</b>) CCLHR.</p>
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<p>Initial concentration vs. percentage of removal vs. biosorption capacity: (<b>a</b>) PMT and (<b>b</b>) CCLHR.</p>
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<p>Adsorption isotherm of MB: (<b>a</b>) PMT, (<b>b</b>) CCLHR.</p>
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<p>Freundlich isothermal adsorption equation fitting of methylene blue: (<b>a</b>) PMT, (<b>b</b>) CCLHR.</p>
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<p>Langmuir isothermal adsorption equation fitting of methylene blue: (<b>a</b>) PMT, (<b>b</b>) CCLHR.</p>
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<p>Adsorption isotherms with the Langmuir and Freundlich models: (<b>a</b>) PMT, (<b>b</b>) CCLHR.</p>
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<p>Curve of R<sub>L</sub> by the initial concentration for PMT and CCLHR.</p>
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<p>Contact time vs. percentage of removal vs. biosorption capacity: (<b>a</b>) PMT and (<b>b</b>) CCLHR.</p>
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<p>Plots of pseudo-first-order kinetic model for the biosorption: (<b>a</b>) PMT and (<b>b</b>) CCLHR.</p>
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<p>Plots of pseudo-second-order kinetic model for the biosorption: (<b>a</b>) PMT and (<b>b</b>) CCLHR.</p>
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24 pages, 19652 KiB  
Article
GFRP Bars Anchorage Resistance in a GFRP-Reinforced Concrete Bridge Barrier
by Michael Rostami, Khaled Sennah and Saman Hedjazi
Materials 2019, 12(15), 2485; https://doi.org/10.3390/ma12152485 - 5 Aug 2019
Cited by 4 | Viewed by 5502
Abstract
In the present paper, experimental and numerical investigations were conducted on concrete bridge barriers utilizing glass fiber reinforced polymer (GFRP) bars with a hook at their ends. Implementation of these hooked bars instead of the bent bars or headed-end bars in the bridge [...] Read more.
In the present paper, experimental and numerical investigations were conducted on concrete bridge barriers utilizing glass fiber reinforced polymer (GFRP) bars with a hook at their ends. Implementation of these hooked bars instead of the bent bars or headed-end bars in the bridge barriers presented in the Canadian Highway Bridge Design Code (CHBDC) was investigated on American Association for State Highway and Transportation Officials (AASHTO) test level 5 (TL-5) concrete bridge barriers. This research aimed to reach a cost effective and safe anchorage method for GFRP bars at the barrier–deck junction, compared to the conventional bend bars or headed-end bars. Therefore, an experimental program was developed and performed to qualify the use of the recently-developed, small radius hooked bars at the barrier–deck junction. The experimental findings were compared with the design factored applied transverse load specified in CHBDC for the design of the barrier–deck junction as well as factored applied bending moment obtained at the barrier–deck junction using a recently-conducted finite-element modeling. Satisfactory behavior for the developed hooked GFRP bars as well as their anchorage resistance was established and a reasonable factor of safety in design of barrier–deck joint was achieved. Full article
(This article belongs to the Special Issue Polymer in/on Concrete)
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<p>Reinforcement details of AASHTO test level 5 (TL-5) barrier reinforced with glass fiber reinforced polymer (GFRP) bars with headed ends and 180° hooks. (<b>a</b>) Barrier with headed GFRP bars; (<b>b</b>) Barrier with 180° hooked GFRP bars.</p>
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<p>Views of the developed GFRP bar with 180° hook. (<b>a</b>) length of the hook; (<b>b</b>) radius of the hook.</p>
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<p>Specimen # 1: Interior location of barrier connected to a cantilever slab (hooks facing the roadway).</p>
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<p>Specimen # 2: Interior location of barrier connected to a thin cantilever slab (hooks not facing roadway).</p>
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<p>Specimen # 3: End location of barrier connected to a cantilever slab.</p>
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<p>Specimen # 4: Interior location of barrier connected to a non-deformable slab.</p>
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<p>Specimen # 5: Interior location of the barrier connected to a non-deformable slab using post-installed bars.</p>
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<p>Views of the formwork and reinforcement details. (<b>a</b>) Specimen # 1; (<b>b</b>) Specimen # 2; (<b>c</b>) Specimen # 3; (<b>d</b>) Specimen # 5.</p>
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<p>Test setup. (<b>a</b>) Tie-down system and loading system; (<b>b</b>) locations of potentiometers (POTs).</p>
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<p>Specimen # 1 before and after testing. (<b>a</b>) Test setup; (<b>b</b>) crack pattern at failure.</p>
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<p>Specimen # 1: Load vs. displacement history.</p>
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<p>Specimen # 1: Load vs. bar strain history.</p>
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<p>Specimen # 1: Load vs. concrete strain history.</p>
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<p>Specimen # 2 crack pattern. (<b>a</b>) Side view; (<b>b</b>) front view.</p>
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<p>Specimen # 2: Load vs. displacement history.</p>
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<p>Specimen # 2: Load vs. bar strain history.</p>
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<p>Specimen # 2: Load vs. concrete strain history.</p>
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<p>Specimen # 3: crack pattern. (<b>a</b>) Side view; (<b>b</b>) front view.</p>
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<p>Specimen # 3: Load vs. displacement history.</p>
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<p>Specimen # 3: Load vs. bar strain history.</p>
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<p>Specimen # 3: Load vs. concrete strain history.</p>
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<p>Specimen # 4 before and after testing. (<b>a</b>) Test setup; (<b>b</b>) crack pattern.</p>
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<p>Specimen # 4: Load vs. displacement history.</p>
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<p>Specimen # 4: Load vs. GFRP bar strain history.</p>
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<p>Specimen # 4: Load vs. concrete strain history.</p>
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<p>Specimen # 5: crack pattern. (<b>a</b>) Right side view; (<b>b</b>) left side view.</p>
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<p>Specimen # 5: Load vs. displacement history.</p>
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<p>Specimen # 5: Load vs. GFRP bar strain history.</p>
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<p>Specimen # 5: Load vs. concrete strain history.</p>
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<p>Finite element model and applied transverse loading. (<b>a</b>)Transverse load distribution on interior location (<b>left</b>) and end location (<b>right</b>). (<b>b</b>) Typical finite element model and notations used for the parametric study [<a href="#B18-materials-12-02485" class="html-bibr">18</a>].</p>
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<p>Finite element model and applied transverse loading. (<b>a</b>)Transverse load distribution on interior location (<b>left</b>) and end location (<b>right</b>). (<b>b</b>) Typical finite element model and notations used for the parametric study [<a href="#B18-materials-12-02485" class="html-bibr">18</a>].</p>
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<p>Design factors of safety for TL-5 barrier in <a href="#materials-12-02485-f001" class="html-fig">Figure 1</a>b at an interior location.</p>
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<p>Design factors of safety for TL-5 barrier in <a href="#materials-12-02485-f001" class="html-fig">Figure 1</a>b at end location.</p>
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10 pages, 3737 KiB  
Article
A New Reversible Phase Transformation of Intermetallic Ti3Sn
by Minshu Du, Lishan Cui and Feng Liu
Materials 2019, 12(15), 2484; https://doi.org/10.3390/ma12152484 - 5 Aug 2019
Cited by 10 | Viewed by 3893
Abstract
Ti3Sn has received increasing attention as a high damping metallic material and as an anode material for rechargeable lithium-ion batteries. However, a heated dispute concerning the existence of solid state phase transformation of stoichiometric Ti3Sn impedes its development. Here, [...] Read more.
Ti3Sn has received increasing attention as a high damping metallic material and as an anode material for rechargeable lithium-ion batteries. However, a heated dispute concerning the existence of solid state phase transformation of stoichiometric Ti3Sn impedes its development. Here, thermal-induced reversible phase transformation of Ti3Sn is demonstrated to happen at around 300 K by the means of in-situ variable-temperature X-ray diffraction (XRD) of Ti3Sn powder, which is also visible for bulk Ti3Sn on the thermal expansion curve by a turning at 330 K. The new phase’s crystal structure of Ti3Sn is determined to be orthorhombic with a space group of Cmcm and the lattice parameters of a = 5.87 Å, b = 10.37 Å, c = 4.76 Å respectively, according to selected area electron diffraction patterns in transmission electron microscope (TEM) and XRD profiles. The hexagonal → orthorhombic phase transformation is calculated to be reasonable and consistent with thermodynamics theory. This work contributes to a growing knowledge of intermetallic Ti3Sn, which may provide fundamental insights into its damping mechanism. Full article
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<p>Phase transformation characterization of intermetallic Ti<sub>3</sub>Sn. (<b>a</b>) DSC result. (<b>b</b>) Thermal expansion test result.</p>
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<p>Comparison of conventional X-ray diffraction (XRD) patterns between (<b>a</b>) bulk Ti<sub>3</sub>Sn sample and (<b>b</b>) Ti<sub>3</sub>Sn powder during the cooling process. (<b>a</b>) XRD peaks of bulk Ti<sub>3</sub>Sn near hexagonal D0<sub>19</sub> phase (002), (201) and (203) crystal faces. (<b>b</b>) XRD peaks of Ti<sub>3</sub>Sn powder near hexagonal D0<sub>19</sub> phase (002), (201) and (203) crystal faces, respectively.</p>
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<p>Overlapping twins in bulk Ti<sub>3</sub>Sn sample. (<b>a</b>) Extensively distributed twins; (<b>b</b>) lamellar nano-twins; (<b>c</b>) multiple twins distributed with 120° crossover; (<b>d</b>) stepped twins and inner lamellar twins.</p>
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<p>Lattice d-spacing variations of Ti<sub>3</sub>Sn powder during in-situ cooling and heating process. (<b>a</b>) D-spacing change of D0<sub>19</sub>-(110) plane; (<b>b</b>) d-spacing change of D0<sub>19</sub>-(200) plane; (<b>c</b>) d-spacing change of D0<sub>19</sub>-(201) plane in a temperature range of 93–320 K, respectively. The D0<sub>19</sub> (201) peak still existed after phase transformation to the lowest temperature of 93 K.</p>
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<p>A set of selected area electron diffraction (SAED) patterns of Ti<sub>3</sub>Sn at the room temperature. The crystal zone axis and experimental tilting angle between the neighboring SAED patterns are indicated in the figure.</p>
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<p>Rietveld refinement result of XRD profile of Ti<sub>3</sub>Sn powder at 93 K, in which the hexagonal phase and the orthorhombic phase positions were indicated by green bars and red bars, respectively. The phase contents were also shown by the pie sub-figure as inserted.</p>
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<p>Temperature dependence of lattice parameters a, b and c of orthorhombic Ti<sub>3</sub>Sn during cooling and heating processes, in which the schematic unit cell is also showed.</p>
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<p>Comparison of the projection drawings of the hexagonal structure (drawn in black) and the orthorhombic structure (drawn in pink) of Ti<sub>3</sub>Sn from c axis, in which a, b axes of the hexagonal structure and a’, b’ axes of the orthorhombic structure were also indicated.</p>
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12 pages, 4402 KiB  
Article
Effect of Eggshell Powder on the Hydration of Cement Paste
by Natnael Shiferaw, Lulit Habte, Thriveni Thenepalli and Ji Whan Ahn
Materials 2019, 12(15), 2483; https://doi.org/10.3390/ma12152483 - 5 Aug 2019
Cited by 60 | Viewed by 9679
Abstract
Eggshells are one of the solid wastes in the world and are considered hazardous according to European Commission regulations. The utilization of solid wastes, like eggshells, will help create a sustainable environment by minimizing the solid wastes that are disposed into the environment. [...] Read more.
Eggshells are one of the solid wastes in the world and are considered hazardous according to European Commission regulations. The utilization of solid wastes, like eggshells, will help create a sustainable environment by minimizing the solid wastes that are disposed into the environment. The utilization of eggshell powder in cement also helps to reduce the carbon dioxide emissions from cement factories by reducing clinker production. In this study, the effect of eggshell powder on the hydration of cement products was investigated using X-ray diffraction (XRD), thermogravimetric analysis (TGA), Fourier-transform infrared spectroscopy (FT-IR), and scanning electron microscopy (SEM). Pastes were made with 10% and 20% eggshell powder and examined for 1, 14, and 28 days of hydration. The addition of eggshell powder transformed ettringite to monosulfoaluminate and to monocarboaluminate. In 20% eggshell powder, the formation of monocarboaluminate was detected in the early stages and accelerated the hydration reaction. The CaCO3 from the eggshells reacted with the C3A and changed the hydration products of the pastes. The addition of eggshell powder provided nucleation sites in the hydration products and accelerated cement hydration. Full article
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<p>Waste eggshell landfill.</p>
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<p>Raw eggshells and eggshell powder.</p>
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<p>XRD analysis of eggshell powder (ESP).</p>
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<p>Activity test of ESP.</p>
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<p>XRD analysis of 1-day cement paste.</p>
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<p>XRD analysis of 14-day cement paste.</p>
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<p>XRD analysis of 28-day cement paste.</p>
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<p>(<b>a</b>) TGA result of 1-day cement paste; (<b>b</b>) DTA result of 1-day cement paste.</p>
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<p>(<b>a</b>) TGA result of 28-day cement paste; (<b>b</b>) DTA result of 28-day cement paste.</p>
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<p>Degree of hydration.</p>
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<p>FT-IR results of cement pastes.</p>
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<p>SEM image of (<b>a</b>) ordinary Portland cement (OPC) and (<b>b</b>) samples containing ESP.</p>
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12 pages, 4397 KiB  
Article
Biocompatibility and Mineralization Activity of Three Calcium Silicate-Based Root Canal Sealers Compared to Conventional Resin-Based Sealer in Human Dental Pulp Stem Cells
by Deog-Gyu Seo, Donghee Lee, Yong-Min Kim, Dani Song and Sin-Young Kim
Materials 2019, 12(15), 2482; https://doi.org/10.3390/ma12152482 - 5 Aug 2019
Cited by 54 | Viewed by 5916
Abstract
The purpose of this study was to compare the cytotoxic effects and mineralization activity of three calcium silicate-based root canal sealers to those of a conventional resin-based sealer. Experiments were performed using human dental pulp stem cells grown in a monolayer culture. The [...] Read more.
The purpose of this study was to compare the cytotoxic effects and mineralization activity of three calcium silicate-based root canal sealers to those of a conventional resin-based sealer. Experiments were performed using human dental pulp stem cells grown in a monolayer culture. The root canal sealers tested in this study were EndoSequence BC Sealer (Brasseler), BioRoot RCS (Septodont), Endoseal MTA (Maruchi), and AH Plus (Dentsply DeTrey). Experimental disks 6 mm in diameter and 3 mm in height were made and stored in a 100% humidity chamber at 37 °C for 72 h to achieve setting. The cytotoxicity of various root canal sealers was evaluated using a methyl-thiazoldiphenyl-tetrazolium (MTT) assay. To evaluate cell migration ability, a scratch wound healing method was used, and images of the scratch area were taken using a phase-contrast microscope. Cell morphology was evaluated by a scanning electron microscope after direct exposure for 72 h to each sealer disk. In the cell viability assay, there were no significant differences between the EndoSequence BC, BioRoot RCS, Endoseal MTA, and control groups in any experimental period (p > 0.05). In the cell migration assay, there were no significant differences between the EndoSequence BC, Endoseal MTA, and control groups in any experimental period (p > 0.05). BioRoot RCS exhibited slower cell migration relative to EndoSequence BC and Endoseal MTA for up to 72 h (p < 0.05). Conversely, it showed a similar wound healing percentage at 96 h (p > 0.05). In an evaluation of cell morphology, cells in direct contact with EndoSequence BC, BioRoot RCS, and Endoseal MTA disks showed superior spreading compared to those in contact with the AH Plus disk. In an Alizarin red staining assay, EndoSequence BC, BioRoot RCS, and Endoseal MTA showed a significant increase in mineralized nodule formation compared to the AH Plus group (p < 0.05). In conclusion, all calcium silicate-based root canal sealers tested in this study showed good biological properties and mineralization activity compared to conventional resin-based sealer. Full article
(This article belongs to the Special Issue Contemporary Endodontic Materials)
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<p>Experimental procedure of biocompatibility tests of each experimental sealer disk.</p>
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<p>Relative cell viability rate based on a methyl-thiazoldiphenyl-tetrazolium (MTT) assay. Asterisks indicate statistically significant differences between the control group and experimental groups.</p>
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<p>Relative wound healing rate based on the cell migration assay. Asterisks indicate statistically significant differences between the control group and experimental groups.</p>
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<p>Representative image of wound healing percentage based on the cell migration assay. (<b>a</b>) Control group, (<b>b</b>) AH Plus group, (<b>c</b>) EndoSequence BC Sealer group, (<b>d</b>) BioRoot RCS group, (<b>e</b>) Endoseal MTA group.</p>
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<p>Scanning electron microscope (SEM) results of direct contact of human dental pulp stem cells (hDPSCs) with each experimental sealer. (<b>a</b>) Control group, (<b>b,c</b>) cells with control disk, (<b>d</b>) AH Plus disk, (<b>e,f</b>) cells with AH Plus disk, (<b>g</b>) EndoSequence BC Sealer disk, (<b>h,i</b>) cells with EndoSequence BC Sealer disk, (<b>j</b>) BioRoot RCS disk, (<b>k,l</b>) cells with BioRoot RCS disk, (<b>m</b>) Endoseal MTA disk, (<b>n,o</b>) cells with Endoseal MTA disk.</p>
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<p>Relative mineralized nodule formation rate based on Alizarin red staining assay. Asterisk indicates a statistically significant difference between the control group and experimental groups. Different superscript letters indicate statistically significant differences.</p>
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20 pages, 6141 KiB  
Article
Effects of Transverse Crack on Chloride Ions Diffusion and Steel Bars Corrosion Behavior in Concrete under Electric Acceleration
by Fengyin Du, Zuquan Jin, Chuansheng Xiong, Yong Yu and Junfeng Fan
Materials 2019, 12(15), 2481; https://doi.org/10.3390/ma12152481 - 5 Aug 2019
Cited by 13 | Viewed by 4071
Abstract
Cracks greatly impact the durability of concrete structures due to their influence on the migration of chloride ions and the corrosion process of steel bars. This study investigates the effects of transverse cracks on chloride diffusion and the corrosion behavior of two types [...] Read more.
Cracks greatly impact the durability of concrete structures due to their influence on the migration of chloride ions and the corrosion process of steel bars. This study investigates the effects of transverse cracks on chloride diffusion and the corrosion behavior of two types of steel bars (low carbon steel and corrosion resistant steel) in fly ash concrete with 1 kg/m3 solution-polymerized super absorbent polymer. Electrochemical impedance spectroscopy was used to monitor the chloride-induced corrosion behavior of steel bars in concrete. The chloride profile around cracks was tested via chemical titration. The corrosion products diffusion area was photographed and measured to evaluate the influences of cracks on the corrosion degree of steel bars. Transverse cracks greatly influence the chloride ion transport. When their width is less than 0.15 mm, cracks exert little influence on both chloride diffusion and steel corrosion. When the crack width exceeds 0.15 mm, the chloride ion transmission coefficient is significantly improved and steel corrosion is accelerated. However, when the crack width exceeds 0.20 mm, this effect is gradually weakened. Based on the experimental data, a quantitative relationship between the crack width and the chloride ion transmission coefficient in electric acceleration was established. Full article
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<p>Diagram of potentiostatic accelerated corrosion of reinforced concrete.</p>
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<p>Sampling areas used for the chemical titration of chloride ions (mm).</p>
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<p>Chloride ion content distribution after electric acceleration. (<b>a</b>) Crack width (LC) = 0.10 mm; (<b>b</b>) Crack width (LC) = 0.15 mm; (<b>c</b>) Crack width (LC) = 0.20 mm; (<b>d</b>) Crack width (LC) = 0.30 mm; (<b>e</b>) Crack width (CR) = 0.10 mm; (<b>f</b>) Crack width (CR) = 0.15 mm; (<b>g</b>) Crack width (CR) = 0.20 mm; (<b>h</b>) Crack width (CR) = 0.30 mm.</p>
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<p>Anisotropic (1-D) cracks in concrete.</p>
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<p>Relationship between diffusion coefficients and distance from crack. (<b>a</b>) Concrete with LC; (<b>b</b>) Concrete with CR.</p>
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<p>Evolutions of Nyquist plots and bode diagrams for reinforcement low carbon (LC) concrete with different crack widths. (<b>a</b>,<b>b</b>) Crack width = 0.10 mm; (<b>c</b>,<b>d</b>) Crack width = 0.15 mm; (<b>e</b>,<b>f</b>) Crack width = 0.20 mm; (<b>g</b>,<b>h</b>) Crack width = 0.30 mm.</p>
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<p>Equivalent circuit applied to simulate the electrochemical impedance spectroscopy results for reinforcement steel.</p>
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<p>(<b>a</b>) Polarization resistance and (<b>b</b>) corrosion current density for concrete reinforced with low carbon steel with different crack widths.</p>
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<p>Evolutions of Nyquist plots for reinforced corrosion resistant concrete with different transverse crack widths. (<b>a</b>,<b>b</b>) Crack width = 0.10 mm; (<b>c</b>,<b>d</b>) Crack width = 0.15 mm; (<b>e</b>,<b>f</b>) Crack width = 0.20 mm; (<b>g</b>,<b>h</b>) Crack width = 0.30 mm.</p>
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<p>Evolutions of Nyquist plots for reinforced corrosion resistant concrete with different transverse crack widths. (<b>a</b>,<b>b</b>) Crack width = 0.10 mm; (<b>c</b>,<b>d</b>) Crack width = 0.15 mm; (<b>e</b>,<b>f</b>) Crack width = 0.20 mm; (<b>g</b>,<b>h</b>) Crack width = 0.30 mm.</p>
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<p>(<b>a</b>) Polarization resistance and (<b>b</b>) corrosion current density for reinforced corrosion resistant concrete with different transverse crack widths.</p>
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<p>Corrosion analysis of corroded reinforced concrete. (<b>a</b>) Actual rust spot distribution; (<b>b</b>) Captured rust spots.</p>
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<p>Pictures of concrete samples (LC) with transverse crack widths. (<b>a</b>) Crack width (LC) = 0.10 mm; (<b>b</b>) Crack width (LC) = 0.15 mm; (<b>c</b>) Crack width (LC) = 0.20 mm; (<b>d</b>) Crack width (LC) = 0.30 mm.</p>
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<p>Corrosion production distribution area of concretes with CR steels. (<b>a</b>) Crack width (LC) = 0.10 mm; (<b>b</b>) Crack width (LC) = 0.15 mm; (<b>c</b>) Crack width (LC) = 0.20 mm; (<b>d</b>) Crack width (LC) = 0.30 mm.</p>
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<p>Fitting results of crack width and corrosion production distribution area.</p>
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10 pages, 3979 KiB  
Article
Damping Enhancement Using Axially Functionally Graded Porous Structure Based on Acoustic Black Hole Effect
by Weiguang Zheng, Shiming He, Rongjiang Tang and Shuilong He
Materials 2019, 12(15), 2480; https://doi.org/10.3390/ma12152480 - 4 Aug 2019
Cited by 13 | Viewed by 3641
Abstract
The acoustic black hole (ABH) effect for damping flexural waves using axially functionally graded porous (FGP) structure is investigated. With proposed power-law porosity of FGP structure, ABH can be achieved and damping effect is enhanced. The physics are explained from divergent conditions of [...] Read more.
The acoustic black hole (ABH) effect for damping flexural waves using axially functionally graded porous (FGP) structure is investigated. With proposed power-law porosity of FGP structure, ABH can be achieved and damping effect is enhanced. The physics are explained from divergent conditions of the integrated wave phase at composite ends. Numerical results show the damping effect is increased with power law index. The phenomenon is expounded by the characteristics of reflection coefficient and impedance. It indicates that increasing power law index leads to smaller wavelength along to the end, then the wave needs more oscillation cycles to travel, which leads to more energy absorption. Transient analysis for 2D FGP structure also shows the focalization and ABH effect of the flexural waves. Full article
(This article belongs to the Collection Damping Materials)
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<p>A uniform beam with functionally graded porous (FGP) end.</p>
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<p>Frequency responses of the beams with FGP ends for different power law index (Euler-Bernoulli beam).</p>
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<p>Frequency responses of the beams with FGP ends for different power law index (Timoshenko beam).</p>
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<p>Real parts of the flexural wavelength along the <span class="html-italic">x</span>-axis at 8 and 20 kHz.</p>
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<p>Reflection coefficients for FGP ends with different power law index <span class="html-italic">N</span>.</p>
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<p>Scalar impedance <span class="html-italic">Z</span><sub>1</sub> along <span class="html-italic">x</span>-axis.</p>
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<p>Finite element model for the 2D application.</p>
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<p>Frequency responses of 2D plate with different power law index.</p>
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<p>Transient analysis of 2D FGP structure.</p>
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9 pages, 3741 KiB  
Article
In Situ Macroscopic Tensile Testing in SEM and Electron Channeling Contrast Imaging: Pencil Glide Evidenced in a Bulk β-Ti21S Polycrystal
by Meriem Ben Haj Slama, Nabila Maloufi, Julien Guyon, Slim Bahi, Laurent Weiss and Antoine Guitton
Materials 2019, 12(15), 2479; https://doi.org/10.3390/ma12152479 - 4 Aug 2019
Cited by 12 | Viewed by 4478
Abstract
In this paper, we report the successful combination of macroscopic uniaxial tensile testing of bulk specimen combined with In situ dislocation-scale observations of the evolution of deformation microstructures during loading at several stress states. The dislocation-scale observations were performed by Accurate Electron Channeling [...] Read more.
In this paper, we report the successful combination of macroscopic uniaxial tensile testing of bulk specimen combined with In situ dislocation-scale observations of the evolution of deformation microstructures during loading at several stress states. The dislocation-scale observations were performed by Accurate Electron Channeling Contrast Imaging in order to follow the defects evolution and their interactions with grain boundaries for several regions of interest during macroscopic loading. With this novel in situ procedure, the slip systems governing the deformation in polycrystalline bulk β-Ti21S are tracked during the macroscopic uniaxial tensile test. For instance, curved slip lines that are associated with “pencil glide” phenomenon and tangled dislocation networks are evidenced. Full article
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<p>(<b>a</b>) Tensile sample geometry and sizes (mm); (<b>b</b>) Elastic deformation simulation on COMSOL.</p>
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<p>Assembly of the tensile machine/sample inside the Scanning Electron Microscope (SEM); when SEM chamber is opened (left image) and inside the closed SEM chamber with the BackScattered Electrons (BSE) detector inserted (right images).</p>
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<p>In situ obtained stress-strain curve of the β-Ti21S showing the positions where observations/Accurate Electron Channeling Contrast Imaging (A-ECCI) were made: before loading (1), during elastic deformation (2: no defect formation was observed), at the beginning of the plastic domain (3), and for six intermediate states of the second tensile cycle before unloading (four to 10). The dashed vertical lines correspond to the relaxation after plastic deformation.</p>
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<p>Observed area of 600 × 450 µm<sup>2</sup> with the seven zones of interest in white dashed frames.</p>
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<p>(<b>a</b>) BSE micrographs in channeling condition (with <b>g</b> = (1–10) in the grain of interest) presenting the evolution of the defect structure corresponding to each deformation step of the tensile curve. The letter refers to the zone (E) and the number refers to the load state from the curve. Black arrows indicate slip lines, orange arrows indicate dislocations and yellow crosses indicate an increase in dislocation length; (<b>b</b>) Example of SE vs BSE images from zone (E8).</p>
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<p>(<b>a</b>) Local section reduction to create high-strained zones (<b>b</b>) BSE micrographs in channeling condition <span class="html-italic">post mortem</span> test showing dislocation networks and slip lines forming and evolving during plastic deformation.</p>
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<p>(<b>a</b>) Secondary Electron (SE) micrographs showing curved slip lines resulting from pencil glide phenomenon and (<b>b</b>) a corresponding schematic representation.</p>
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18 pages, 9531 KiB  
Article
Revealing the Nuclei Formation in Carbon-Inoculated Mg-3%Al Alloys Containing Trace Fe
by Chengbo Li, Shuqing Yang, Gan Luo, Hengbin Liao and Jun Du
Materials 2019, 12(15), 2478; https://doi.org/10.3390/ma12152478 - 4 Aug 2019
Cited by 5 | Viewed by 2888
Abstract
In this study, Fe-bearing Mg-3%Al alloys were inoculated by combining carbon with or without Ca. Both processes can significantly refine the grain size of Mg-3%Al alloys. The highest refining efficiency can be obtained by carbon combined with Ca. The synergistic grain refining efficiency [...] Read more.
In this study, Fe-bearing Mg-3%Al alloys were inoculated by combining carbon with or without Ca. Both processes can significantly refine the grain size of Mg-3%Al alloys. The highest refining efficiency can be obtained by carbon combined with Ca. The synergistic grain refining efficiency can be attributed to the constitutional undercooling produced by the addition of Ca. Two kinds of carbon-containing nuclei with duplex-phase particles and cluster particles were observed in the carbon-inoculated alloys. A thermodynamic model was established to disclose the formation mechanisms of the duplex-phase particles and Al4C3 cluster particles. This thermodynamic model is based on the change of Gibbs free energy for the formation of these two kinds of particles. The calculated results show that these two particles can form spontaneously, since the change of Gibbs free energy is negative. However, the Gibbs free change of the duplex-phase particle is more negative than the Al4C3 cluster particle. This indicates that the adsorption process is more spontaneous than the cluster process, and tiny Al4C3 particles are preferred to form duplex-phase particle, rather than gathering to form an Al4C3 cluster particle. In addition, the addition of Ca can reduce the interfacial energy between the Al4C3 phase and the Al–Fe phase and promote the formation of duplex-phase particles. Full article
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<p>Grain morphologies of (<b>a</b>) the original Mg-3%Al alloy, (<b>b</b>) the Mg-3%Al alloy containing 0.05%Fe, (<b>c</b>) the Mg-3%Al alloy containing 0.05%Fe refined by carbon inoculation, and (<b>d</b>) the Mg-3%Al alloy containing 0.05%Fe refined by carbon inoculation, combined with 0.2%Ca.</p>
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<p>Electron probe microanalyzer (EPMA)-back-scattered electron (BSE) micrographs of the 0.05%Fe containing Mg-3%Al alloy refined by carbon inoculation (<b>a</b>) and carbon inoculation combined with the addition of 0.2%Ca (<b>b</b>).</p>
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<p>EPMA analyses of two typical particles: (<b>a</b>) point analysis of the single particle; (<b>b</b>) line analysis of the duplex-phase particle.</p>
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<p>The totally constitutional undercooling <math display="inline"><semantics> <mrow> <mo>Δ</mo> <msub> <mi>T</mi> <mrow> <mi>c</mi> <mi>s</mi> </mrow> </msub> </mrow> </semantics></math> produced at the solid–liquid interface during the solidification.</p>
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<p>Schematic diagrams of the formation process of the duplex-phase and Al<sub>4</sub>C<sub>3</sub> cluster particles.</p>
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<p>The TEM microstructure of the Al<sub>4</sub>C<sub>3</sub> cluster from several tiny particles.</p>
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<p>Electron probe microanalyzer with a wavelength dispersion spectrometer (EPMA-WDS) map analysis of Mg-3%Al-0.05%Fe refined by carbon combining with Ca inoculation, with a holding time of 80 min. (<b>a</b>) The region of EPMA-WDS map analysis; (<b>b</b>–<b>f</b>) the distribution of the Fe, C, O, Ca, and Al elements, respectively.</p>
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<p>Electron probe microanalyzer with a wavelength dispersion spectrometer (EPMA-WDS) map analysis of Mg-3%Al-0.05%Fe refined by carbon combining with Ca inoculation, with a holding time of 80 min. (<b>a</b>) The region of EPMA-WDS map analysis; (<b>b</b>–<b>f</b>) the distribution of the Fe, C, O, Ca, and Al elements, respectively.</p>
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<p>Calculation model of the duplex and single structure particle.</p>
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<p>The Gibbs free energy of the duplex phase particle with different adsorption layers. (<b>a</b>) n = 1, (<b>b</b>) n = 100, (<b>c</b>) n = 1000, (<b>d</b>) the contour map of the n = 1000.</p>
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<p>The Gibbs free energy of the Al<sub>4</sub>C<sub>3</sub> cluster particles with different number tiny Al<sub>4</sub>C<sub>3</sub> particles. The number of tiny Al<sub>4</sub>C<sub>3</sub> particles is calculated by Equation (6). (<b>a</b>) n = 1, (<b>b</b>) n = 100, (<b>c</b>) n = 1000, (<b>d</b>) the contour map of n = 1000.</p>
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<p>The Gibbs free energy of the Al<sub>4</sub>C<sub>3</sub> cluster particles with different number tiny Al<sub>4</sub>C<sub>3</sub> particles. The number of tiny Al<sub>4</sub>C<sub>3</sub> particles is calculated by Equation (6). (<b>a</b>) n = 1, (<b>b</b>) n = 100, (<b>c</b>) n = 1000, (<b>d</b>) the contour map of n = 1000.</p>
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<p>The Gibbs free energy of the competitive trend with different layers. (<b>a</b>,<b>b</b>): n = 1, (<b>c</b>,<b>d</b>): n = 100, (<b>e</b>,<b>f</b>): n = 1000.</p>
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<p>The change of Gibbs free energy after Ca addition. The number of adsorption layers is 10, 100, and 1000, respectively.</p>
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20 pages, 8180 KiB  
Article
Influence of Pore Networking and Electric Current Density on the Crack Pattern in Reinforced Concrete Test Due to Pressure Rust Layer at Early Ages of an Accelerated Corrosion Test
by Ángela M. Bazán, Encarnación Reyes and Jaime C. Gálvez
Materials 2019, 12(15), 2477; https://doi.org/10.3390/ma12152477 - 4 Aug 2019
Cited by 4 | Viewed by 4384
Abstract
Research on early stages of corrosion of steel bars caused by chloride penetration is relevant in improving the durability of reinforced concrete structures. Similarly, the formation and development of cracks induced in the surrounding concrete is also of great importance. This paper uses [...] Read more.
Research on early stages of corrosion of steel bars caused by chloride penetration is relevant in improving the durability of reinforced concrete structures. Similarly, the formation and development of cracks induced in the surrounding concrete is also of great importance. This paper uses integration of the analytical models examined in the published literature, combined with experimental research in corrosion induced at the concrete/steel interface, in estimating the time-to-crack initiation of reinforced concrete subjected to corrosion. This work studies the influence of the porous network and electric current density on the cracking process at early ages. The experimental program was performed by using an accelerated corrosion test. Two types of concrete were performed: A conventional concrete (CC) and a concrete with silica fume (SFC). A current density of 50 μA/cm2 and 100 μA/cm2 was applied to specimens of both concretes. Examination performed by scanning electron microscopy (SEM) and energy-dispersive X-ray spectroscopy (EDS) provided both qualitative and quantitative information on the penetration of the rust layer in the surrounding concrete porous network. Strain gauges were used to measure corrosion-induced deformations between steel and concrete matrices, as well as the formation of corrosion-induced cracks. A good correlation between the rate of penetration of the rust products in the surrounding pores and the delay of the cracking pressure in concrete was observed from the experimental results. This phenomenon is incorporated into the analytical model by using a reduction factor, which mainly depends on the pore size of the concrete. The crack width obtained exhibited a significant dependency on electric current density at the beginning of the test, depending mainly on the pore size of the concrete later. Full article
(This article belongs to the Special Issue Corrosion of Reinforcing Steel in Reinforced Concrete)
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<p>Corrosion cracking process: The three-stage-model.</p>
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<p>Bars in the moulds before casting: (<b>a</b>) photo of the moulds, (<b>b</b>) sketch of the specimen with the bar. (Dimensions in mm). Adapted from [<a href="#B14-materials-12-02477" class="html-bibr">14</a>], with permission from © 2018 Elsevier.</p>
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<p>Bonding of the strain gauges before the accelerated corrosion testing.</p>
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<p>(<b>a</b>) Scheme of accelerated corrosion test. (<b>b</b>) Sketch of the cutting procedure of the specimen for SEM observation.</p>
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<p>Pore size distribution for each concrete (SFC, silica fume concrete and CC, conventional concrete).</p>
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<p>Circumferential strain around the rebar versus time for each concrete type and current density.</p>
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<p>BSE image at the steel/concrete interface (C, concrete; CL + CAR, Mill scale; S, Steel) and analytical lines across the interface of CC at (<b>a</b>) 8 days, (<b>b</b>) 14 days and (<b>c</b>) 35 days with a density current of 50 μA/cm<sup>2</sup>. Upper curves of each age: Fe and O; bottom curves of each age: Si and Ca. Adapted from [<a href="#B14-materials-12-02477" class="html-bibr">14</a>], with permission from © 2018 Elsevier</p>
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<p>BSE image at the steel (purple)/concrete (black) interface at 14 days for each concrete (SFC, silica fume concrete and CC, conventional concrete) at at 100 µA/cm<sup>2</sup> and 50 µA/cm<sup>2</sup>.</p>
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<p>Evolution of the circumferential strain as a function of the electric charge for each specimen at 50 and 100 μA/cm<sup>2</sup>.</p>
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<p>Evolution of the circumferential strain as a function of the electric charge measured by the four gauges for SFC 100.</p>
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<p>Evolution of the circumferential strain as a function of the rust layer thickness for both concretes at 50 and 100 μA/cm<sup>2</sup>.</p>
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<p>Geometrical considerations of the corrosion process in the reinforcement bar. Redrawn based on [<a href="#B14-materials-12-02477" class="html-bibr">14</a>], with permission from © 2018 Elsevier.</p>
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<p>Evolution of the crack width as a function of the electric charge for each specimen at 50 and 100 μA/cm<sup>2</sup>.</p>
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<p>Crack mapping of CC50, CC100, SFC50 and SFC 100 at 2, 5, 8, 14 26 and 35 days of testing age.</p>
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23 pages, 3438 KiB  
Review
Cross-Linking Strategies for Electrospun Gelatin Scaffolds
by Chiara Emma Campiglio, Nicola Contessi Negrini, Silvia Farè and Lorenza Draghi
Materials 2019, 12(15), 2476; https://doi.org/10.3390/ma12152476 - 4 Aug 2019
Cited by 196 | Viewed by 14919
Abstract
Electrospinning is an exceptional technology to fabricate sub-micrometric fiber scaffolds for regenerative medicine applications and to mimic the morphology and the chemistry of the natural extracellular matrix (ECM). Although most synthetic and natural polymers can be electrospun, gelatin frequently represents a material of [...] Read more.
Electrospinning is an exceptional technology to fabricate sub-micrometric fiber scaffolds for regenerative medicine applications and to mimic the morphology and the chemistry of the natural extracellular matrix (ECM). Although most synthetic and natural polymers can be electrospun, gelatin frequently represents a material of choice due to the presence of cell-interactive motifs, its wide availability, low cost, easy processability, and biodegradability. However, cross-linking is required to stabilize the structure of the electrospun matrices and avoid gelatin dissolution at body temperature. Different physical and chemical cross-linking protocols have been described to improve electrospun gelatin stability and to preserve the morphological fibrous arrangement of the electrospun gelatin scaffolds. Here, we review the main current strategies. For each method, the cross-linking mechanism and its efficiency, the influence of electrospinning parameters, and the resulting fiber morphology are considered. The main drawbacks as well as the open challenges are also discussed. Full article
(This article belongs to the Special Issue Polymer-based Instructive Scaffolds for Regenerative Medicine)
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Graphical abstract
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<p>Processing of collagen for gelatin extraction. Collagen, characterized by a triple-helix structure and insolubility, is processed either by acid (gelatin A) or alkaline (gelatin B) pre-treatment. After extraction, purification, and recovery, gelatin, a soluble product, is obtained. When dissolved in water, gelatin undergoes a reversible sol-gel transition by heat–cool process.</p>
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<p>Schematic illustration of representative cross-linking methods used to fabricate gelatin hydrogels.</p>
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<p>Schematic representation of cross-linking strategies used for the stabilization of electrospun gelatin matrices. Physical cross-linking can be performed by high energy electron beam, plasma treatment, or dehydrothermal treatment. Chemical cross-linking can be performed by immersion in a cross-linking solution, by using vapors of the cross-linker, or by chemically modifying gelatin to subsequently cross-link it by UV irradiation.</p>
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<p>Morphology of electrospun gelatin nanofibers cross-linked with different strategies: (<b>a</b>) Plasma treatment (scale bar: 5 μm; reprinted from [<a href="#B71-materials-12-02476" class="html-bibr">71</a>]), (<b>b</b>) dehydrothermal treatment (scale bar: 10 μm; reprinted from [<a href="#B54-materials-12-02476" class="html-bibr">54</a>] with permission of Elsevier), (<b>c</b>) EDC/NHS (scale bar = 10 μm; reprinted from [<a href="#B72-materials-12-02476" class="html-bibr">72</a>] with permission of John Wiley and Sons), (<b>d</b>) genipin (scale bar: 1 μm; reprinted from [<a href="#B78-materials-12-02476" class="html-bibr">78</a>] with permission of Elsevier), (<b>e</b>) glutaraldehyde vapor (scale bar: 10 μm; reprinted from [<a href="#B54-materials-12-02476" class="html-bibr">54</a>] with permission of Elsevier), (<b>f</b>) glutaraldehyde solution (scale bar: 5 μm; reprinted from [<a href="#B90-materials-12-02476" class="html-bibr">90</a>] with permission of John Wiley and Sons), (<b>g</b>) glyceraldehyde (scale bar: 1 μm reprinted from [<a href="#B70-materials-12-02476" class="html-bibr">70</a>] with permission of ACS Publications), and (<b>h</b>) Irgacure 2959 with UV treatment (scale bar: 5 μm reprinted from [<a href="#B98-materials-12-02476" class="html-bibr">98</a>] with permission of Elsevier).</p>
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<p>Tissue engineering applications of electrospun cross-linked gelatin matrices. (<b>a</b>) Cell infiltration inside electrospun gelatin vs. GelMA scaffolds (phalloidin staining, Alexa Fluor 488; scale bar: 50 μm) and (<b>b</b>) in vivo assessment of electrospun gelatin and GelMA scaffold skin regenerative potential by histological analysis (scale bar: 200 and 100 μm); reprinted from [<a href="#B100-materials-12-02476" class="html-bibr">100</a>] with permission of Elsevier. (<b>c</b>) Confocal images of primary Schwann cells cultured on random and aligned electrospun gelatin matrices (vs. tissue culture plastic as control; scale bar: 40 μm) [<a href="#B97-materials-12-02476" class="html-bibr">97</a>]. (<b>d</b>) SEM micrographs of human umbilical vein smooth muscle cells cultured on electrospun gelatin matrices for smooth muscle regeneration in vascular tissue engineering; reprinted from [<a href="#B83-materials-12-02476" class="html-bibr">83</a>] with permission of John Wiley and Sons.</p>
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<p>Future perspectives and open challenges in the fabrication of electrospun gelatin scaffolds.</p>
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9 pages, 5168 KiB  
Article
Electrochemistry and Rapid Electrochromism Control of MoO3/V2O5 Hybrid Nanobilayers
by Chung-Chieh Chang, Po-Wei Chi, Prem Chandan and Chung-Kwei Lin
Materials 2019, 12(15), 2475; https://doi.org/10.3390/ma12152475 - 3 Aug 2019
Cited by 27 | Viewed by 4171
Abstract
MoO3/V2O5 hybrid nanobilayers are successfully prepared by the sol–gel method with a spin- coating technique followed by heat -treatment at 350 °C in order to achieve a good crystallinity. The composition, morphology, and microstructure of the nanobilayers are [...] Read more.
MoO3/V2O5 hybrid nanobilayers are successfully prepared by the sol–gel method with a spin- coating technique followed by heat -treatment at 350 °C in order to achieve a good crystallinity. The composition, morphology, and microstructure of the nanobilayers are characterized by a scanning electron microscope (SEM) and X-ray diffractometer (XRD) that revealed the a grain size of around 20–30 nm, and belonging to the monoclinic phase. The samples show good reversibility in the cyclic voltammetry studies and exhibit an excellent response to the visible transmittance. The electrochromic (EC) window displayed an optical transmittance changes (ΔT) of 22.65% and 31.4% at 550 and 700 nm, respectively, with the rapid response time of about 8.2 s for coloration and 6.3 s for bleaching. The advantages, such as large optical transmittance changes, rapid electrochromism control speed, and excellent cycle durability, demonstrated in the electrochromic cell proves the potential application of MoO3/V2O5 hybrid nanobilayers in electrochromic devices. Full article
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<p>The schematic diagram of the preparation procedures for single-layered MoO<sub>3</sub>, V<sub>2</sub>O<sub>5</sub>, and MoO<sub>3</sub>/V<sub>2</sub>O<sub>5</sub> hybrid nanobilayers.</p>
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<p>X-ray diffraction patterns of MoO<sub>3</sub>/V<sub>2</sub>O<sub>5</sub> hybrid nanobilayers heated at 350 °C for 2 h in air.</p>
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<p>Field emission scanning electron microscope (FE-SEM) images of MoO<sub>3</sub>/V<sub>2</sub>O<sub>5</sub> hybrid nanobilayers heated at 350 °C for 2 h in air. (<b>a</b>) M350, (<b>b</b>) MV350, (<b>c</b>) VM350, (<b>d</b>) V350. The inset of (<b>b</b>) and (<b>c</b>) are the cross-section images of the samples MV350 and VM350.</p>
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<p>3-D cyclic voltammograms of MoO<sub>3</sub>/V<sub>2</sub>O<sub>5</sub> hybrid nanobilayers heated at 350 °C for 2 h in air.</p>
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<p>Transmittances of MoO<sub>3</sub>/V<sub>2</sub>O<sub>5</sub> hybrid nanobilayers heated at 350 °C for 2 h in air. (<b>a</b>) M350, (<b>b</b>) MV350, (<b>c</b>) VM350, (<b>d</b>) V350.</p>
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<p>Transmittances of MoO<sub>3</sub>/V<sub>2</sub>O<sub>5</sub> hybrid nanobilayers heated at 350 °C for 2 h in air. (<b>a</b>) M350, (<b>b</b>) MV350, (<b>c</b>) VM350, (<b>d</b>) V350.</p>
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<p>Transmittance changes (Δ<span class="html-italic">T</span>) of MoO<sub>3</sub>/V<sub>2</sub>O<sub>5</sub> hybrid nanobilayers heated at 350 °C for 2 h in air.</p>
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<p>(<b>a</b>) Current density response of MoO<sub>3</sub>/V<sub>2</sub>O<sub>5</sub> hybrid nanobilayers heated at 350 °C for 2 h in air. (<b>b</b>) Current density response in the colored state and (<b>c</b>) current density response in the bleached state of MoO<sub>3</sub>/V<sub>2</sub>O<sub>5</sub> hybrid nanobilayers.</p>
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22 pages, 4970 KiB  
Article
Internal Cracks and Non-Metallic Inclusions as Root Causes of Casting Failure in Sugar Mill Roller Shafts
by Muhammad Jamil, Aqib Mashood Khan, Hussien Hegab, Shoaib Sarfraz, Neeraj Sharma, Mozammel Mia, Munish Kumar Gupta, GuLong Zhao, H. Moustabchir and Catalin I. Pruncu
Materials 2019, 12(15), 2474; https://doi.org/10.3390/ma12152474 - 3 Aug 2019
Cited by 18 | Viewed by 7545
Abstract
The sugar mill roller shaft is one of the critical parts of the sugar industry. It requires careful manufacturing and testing in order to meet the stringent specification when it is used for applications under continuous fatigue and wear environments. For heavy industry, [...] Read more.
The sugar mill roller shaft is one of the critical parts of the sugar industry. It requires careful manufacturing and testing in order to meet the stringent specification when it is used for applications under continuous fatigue and wear environments. For heavy industry, the manufacturing of such heavy parts (>600 mm diameter) is a challenge, owing to ease of occurrence of surface/subsurface cracks and inclusions that lead to the rejection of the final product. Therefore, the identification and continuous reduction of defects are inevitable tasks. If the defect activity is controlled, this offers the possibility to extend the component (sugar mill roller) life cycle and resistance to failure. The current study aims to explore the benefits of using ultrasonic testing (UT) to avoid the rejection of the shaft in heavy industry. This study performed a rigorous evaluation of defects through destructive and nondestructive quality checks in order to detect the causes and effects of rejection. The results gathered in this study depict macro-surface cracks and sub-surface microcracks. The results also found alumina and oxide type non-metallic inclusions, which led to surface/subsurface cracks and ultimately the rejection of the mill roller shaft. A root cause analysis (RCA) approach highlighted the refractory lining, the hot-top of the furnace and the ladle as significant causes of inclusions. The low-quality flux and refractory lining material of the furnace and the hot-top, which were possible causes of rejection, were replaced by standard materials with better quality, applied by their standardized procedure, to prevent this problem in future production. The feedback statistics, evaluated over more than one year, indicated that the rejection rate was reduced for defective production by up to 7.6%. Full article
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<p>Sugar mill roller shaft with final groove ready for shipment.</p>
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<p>Possible sources contributing to the rejection of the roller shaft.</p>
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<p>Flow chart depicting critical processes in the manufacturing of the sugar mill roller shaft.</p>
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<p>(<b>a</b>) Schematic diagram depicting the application of cleaner, penetrant, and developer; (<b>b</b>) Sugar mill roller shaft after penetrant testing (PT)<b>.</b></p>
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<p>Schematic diagram of the ultrasonic testing (UT) set-up, depicting the test screen and compression probe.</p>
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<p>(<b>a</b>) Prepared sample for magnetic particle testing (MT); (<b>b</b>) MT yoke system to detect cracks.</p>
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<p>(<b>a</b>) A rough machined shaft that was rejected after UT inspection; (<b>b</b>) UT report locating internal cracks and foreign particle inclusions under duplicate measurements.</p>
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<p>Surface cracks after performing magnetic particle testing.</p>
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<p>(<b>a</b>) As-cast structure of ferrite within the fine pearlite matrix and at prior austenite grain boundaries, at a magnification of ×350; (<b>b</b>) Not-etched micro alumina-type inclusions are observed as per ASTM E-45, at a magnification of x350; (<b>c</b>) A fine matrix structure of ferrite within the fine pearlite matrix and at prior austenite grain boundaries, at a magnification of x400; (<b>d</b>) Not-etched micro oxide-type inclusions, at a magnification of ×400.</p>
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<p>(<b>a</b>,<b>b</b>) Microstructure of sample indicating alumina-type inclusions, as per ASTM E-45, (<b>c</b>,<b>d</b>) Microstructure of sample indicating oxide-type inclusions, as per ASTM E-45.</p>
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<p>(<b>a</b>) Micro-inclusions, oxide and alumina-type inclusions, observed as per ASTM E-45 (<b>b</b>) The specimen was hotly etched in HCl (1:1), as inclusions were observed and randomly distributed as per ASTM E-381. The random condition is R-5.</p>
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<p>Cause and effect diagram highlighting the causes of shaft rejection.</p>
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13 pages, 2148 KiB  
Article
Adhesive Cements That Bond Soft Tissue Ex Vivo
by Xiuwen Li, Michael Pujari-Palmer, David Wenner, Philip Procter, Gerard Insley and Håkan Engqvist
Materials 2019, 12(15), 2473; https://doi.org/10.3390/ma12152473 - 3 Aug 2019
Cited by 17 | Viewed by 7007
Abstract
The aim of the present study was to evaluate the soft tissue bond strength of a newly developed, monomeric, biomimetic, tissue adhesive called phosphoserine modified cement (PMC). Two types of PMCs were evaluated using lap shear strength (LSS) testing, on porcine skin: a [...] Read more.
The aim of the present study was to evaluate the soft tissue bond strength of a newly developed, monomeric, biomimetic, tissue adhesive called phosphoserine modified cement (PMC). Two types of PMCs were evaluated using lap shear strength (LSS) testing, on porcine skin: a calcium metasilicate (CS1), and alpha tricalcium phosphate (αTCP) PMC. CS1 PCM bonded strongly to skin, reaching a peak LSS of 84, 132, and 154 KPa after curing for 0.5, 1.5, and 4 h, respectively. Cyanoacrylate and fibrin glues reached an LSS of 207 kPa and 33 kPa, respectively. αTCP PMCs reached a final LSS of ≈110 kPa. In soft tissues, stronger bond strengths were obtained with αTCP PMCs containing large amounts of amino acid (70–90 mol%), in contrast to prior studies in calcified tissues (30–50 mol%). When αTCP particle size was reduced by wet milling, and for CS1 PMCs, the strongest bonding was obtained with mole ratios of 30–50% phosphoserine. While PM-CPCs behave like stiff ceramics after setting, they bond to soft tissues, and warrant further investigation as tissue adhesives, particularly at the interface between hard and soft tissues. Full article
(This article belongs to the Special Issue Mineral Bone Cements: Current Status and Future Prospects)
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Graphical abstract

Graphical abstract
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<p>(<b>A</b>) Overview of the testing procedure and obtained data. Skin was removed from an entire ear, as a single piece, and subsequently sectioned into smaller strips 1 cm × 2 cm. (<b>B</b>) To ensure reproducible and comparable conditions each sample was held together during the curing stage using universal grips. (<b>C</b>) The lap shear testing setup. (<b>D</b>) Representative force/displacement curves for calcium metasilicate PMC (CS1), and the peak force per area was calculated for each sample. (<b>E</b>) Adhesive PMCs were applied to the skin surface as a viscous, tacky paste, with the failure surface.</p>
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<p>Particle size distribution of PMC precursors. The particle size limit of each PMC precursor (calcium salt) below which, based upon number, surface, and volume average calculations, (<b>A</b>) 50% (D0.5) or (<b>B</b>) 90% (D0.9) of all measured particles fall. (<b>C</b>) A distribution plot of all PMCs using surface average calculations. The surface area of each PMC precursor (<b>D</b>), determined by BET (white bars) or laser diffraction (black bars). Each αTCP (i.e., αTCP2.1) refers to the average particle size (D0.5, surface, in micrometers) of the calcium salt portion of PMC.</p>
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<p>Secondary electron SEM images of precursor calcium salts: (<b>A</b>) αTCP2.1, (<b>B</b>) αTCP1.9, (<b>C</b>) αTCP1.5, and (<b>D</b>) CS1 particles are shown at 1000× magnification. Inset images in the upper right corner reveal the surface topography and fine structure of respective particles at approximately 25,000× magnification. Each number following the precursor name (i.e., αTCP2.1) refers to the average particle size (D0.5, surface, in micrometers) of the calcium salt portion of PMC. Scale bars represent a 10 µm distance, while inset scale bars represent a 1 µm distance.</p>
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<p>X-ray diffraction of calcium salt precursors used to make PMCs.</p>
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<p>Lap shear strength of PMCs under varied testing conditions. (<b>A</b>) The bond strength of αTCP2.1 PMCs applied to porcine skin obtained from either the rostral (front) or caudal (back) portion of the ear. (<b>B</b>) Bond strength of αTCP2.1 PMCs tested at a crosshead speed of 1, 10, or 30 mm per minute. (<b>C</b>) Bond strength of αTCP2.1 PMCs applied to porcine skin of different sizes (overlap area). (<b>D</b>) The effect of using universal grips (black bars), compared to samples that were appositioned without grips (white bars) on the observed bond strength for each material. All samples contained 60 mol% of phosphoserine, unless otherwise indicated, and were cured for 90 min. Each αTCP, i.e., αTCP2.1, refers to the average particle size (D0.5, surface, in micrometers) of the calcium salt portion of PMC. * and ** indicate <span class="html-italic">p</span> &lt; 0.05, and <span class="html-italic">p</span> &lt; 0.01, respectively, in comparison to samples with a 1 cm<sup>2</sup> contact area (<b>C</b>), or between grip and no grip samples (<b>D</b>). Each data point and group represents a sample size of three (<span class="html-italic">n</span> = 3), except in <a href="#materials-12-02473-f005" class="html-fig">Figure 5</a>A, which contained six samples per group (<span class="html-italic">n</span> = 6).</p>
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<p>Lap shear strength of PMCs. (<b>A</b>) The optimal bond strength of PMCs, with varied ratio of calcium salt to phosphoserine, after curing for 90 min. (<b>B</b>) The optimal bond strength of αTCP PMCs of differing particle size, with varied ratios of calcium salt to phosphoserine after curing for 90 min. To ensure that the comparisons in (<b>A</b>) and (<b>B</b>) represented the true final cure strength, the cure kinetics of each PMC was compared at the optimal mole ratio for (<b>C</b>) CS1 PMC (53%) and (<b>D</b>) αTCP PMC (87%) after curing for 30, 90, or 240 min. αTCP1.5, αTCP1.9, and αTCP 2.1 refer to the average particle sizes (D0.5, surface, in micrometers) of the calcium salt portion of PMC. * and ** indicate <span class="html-italic">p</span> &lt; 0.05 and <span class="html-italic">p</span> &lt; 0.01, respectively, with all comparisons made against αTCP 2.1 PMC with respect to each time point or mole ratio. Each data point and group represents a sample size of six (<span class="html-italic">n</span> = 6) in <a href="#materials-12-02473-f006" class="html-fig">Figure 6</a>A–D.</p>
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7 pages, 1921 KiB  
Article
Effect of the Iron Reduction Index on the Mechanical and Chemical Properties of Continuous Basalt Fiber
by Lida Luo, Qichang Zhang, Qingwei Wang, Jiwen Xiao, Jin Liu, Linfeng Ding and Weizhong Jiang
Materials 2019, 12(15), 2472; https://doi.org/10.3390/ma12152472 - 3 Aug 2019
Cited by 8 | Viewed by 2923
Abstract
Basalt glass belongs to the iron-rich aluminosilicate glass system; thus, the iron content and the iron redox index (IRI=Fe2+/Fetotal) influence the viscosity, density, mechanical and chemical properties of basalt fiber (BF). In this work, continuous BFs with IRIs ranging [...] Read more.
Basalt glass belongs to the iron-rich aluminosilicate glass system; thus, the iron content and the iron redox index (IRI=Fe2+/Fetotal) influence the viscosity, density, mechanical and chemical properties of basalt fiber (BF). In this work, continuous BFs with IRIs ranging from 0.21–0.87 were prepared by adding a different amount of redox agents. An economical and easily accessible testing method—the spectral photometric method with 1,10-phenanthroline—is applied to measure the IRI with convinced accuracy, which has been approved by Mössbauer spectra and X-ray fluorescence analysis. The tensile strength of the BF samples increases approximately linearly with increasing IRI as a function of σ = 227.9 IRI + 780.0 . The FT-IR results indicate that, with increasing IRI, the ferric ions are replaced by the much stronger network formers (Al3+ and Si4+), hence the increased the tensile strength. The X-ray diffraction results show an amorphous nature of BF samples. Moreover, the tensile strength is significantly decreased after the alkali corrosion, which is partly attributed to the severe surface damaging according to the SEM results. This work proved the feasibility of mechanical property improvement in BF production by controlling the iron redox index. Full article
(This article belongs to the Section Materials Chemistry)
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<p><sup>57</sup>Fe resonant absorption Mössbauer spectra of IRI5 basalt fiber sample (iron redox index = 0.64).</p>
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<p>(<b>a</b>) Tensile strength of basalt fiber samples; (<b>b</b>) FT-IR absorption spectra of basalt fiber samples.</p>
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<p>XRD patterns of basalt fiber samples.</p>
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<p>(<b>a</b>) Tensile strength retention of basalt fiber samples after alkali corrosion; (<b>b</b>) mass retention of basalt fiber samples after acid corrosion.</p>
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<p>(<b>a</b>) SEM image of basalt fiber IRI3 sample; (<b>b</b>) SEM image of basalt fiber IRI3 sample after 0.5 mol/L NaOH corrosion.</p>
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13 pages, 3870 KiB  
Article
Impact of Electrocautery on Fatigue Life of Spinal Fusion Constructs—An In Vitro Biomechanical Study
by Haidara Almansour, Robert Sonntag, Wojciech Pepke, Thomas Bruckner, Jan Philippe Kretzer and Michael Akbar
Materials 2019, 12(15), 2471; https://doi.org/10.3390/ma12152471 - 3 Aug 2019
Cited by 7 | Viewed by 4104
Abstract
Instrumentation failure in the context of spine surgery is attributed to cyclic loading leading to formation of fatigue cracks, which later propagate and result in rod fracture. A biomechanical analysis of the potential impact of electrocautery on the fatigue life of spinal implants [...] Read more.
Instrumentation failure in the context of spine surgery is attributed to cyclic loading leading to formation of fatigue cracks, which later propagate and result in rod fracture. A biomechanical analysis of the potential impact of electrocautery on the fatigue life of spinal implants has not been previously performed. The aim of this study was to assess the fatigue life of titanium (Ti) and cobalt-chrome (CoCr) rod-screw constructs after being treated with electrocautery. Twelve spinal constructs with CoCr and Ti rods were examined. Specimens were divided into four groups by rod material (Ti and CoCr) and application of monopolar electrocautery on the rods’ surface (control-group and electrocautery-group). Electrocautery was applied on each rod at three locations, then constructs were cyclically tested. Outcome measures were load-to-failure, total number of cycles-to-failure, and location of rod failure. Ti-rods treated with electrocautery demonstrated a significantly decreased fatigue life compared to non-treated Ti-rods. Intergroup comparison of cycles-to-failure revealed a significant mean decrease of almost 9 × 105 cycles (p = 0.03). No CoCr-rods failed in this experiment. Electrocautery application on the surface of Ti-rods significantly reduces their fatigue life. Surgeons should exercise caution when using electrocautery in the vicinity of Ti-rods to mitigate the risk of rod failure. Full article
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<p>Electrocautery application. (<b>a</b>) Electric light arc, (<b>b</b>) sites, and (<b>c</b>) magnified view of the surface impact post electrocautery application. The first site was approximately 5 mm from the cephalic pedicle screw (#1). (#2 was at the center and #3 was analogous to #1 on the other side).</p>
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<p>Frontal view of the fatigue testing setup.</p>
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<p>Sites of rod fracture of titanium control group (Ti-CG) post biomechanical testing and fatigue fractures of the rods at the rod-screw junction.</p>
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<p>Sites of rod fracture of titanium electrocautery group (Ti-EG) post biomechanical testing.</p>
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<p>Boxplot representing the mean and 25% and 75% interquartile range of the total number of cycles to failure among the four tested groups.</p>
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<p>Microscopic analysis of fractured titanium rod after electrocautery (VHX-5000, Keyence, Osaka, Japan). (<b>a</b>) Post-fracture situation at the electrocautery mark. (<b>b</b>) Fracture surface with typical signs of fatigue fracture (beach lines and forced fracture area). The circle shows the location of crack initiation at the electrocautery mark.</p>
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<p>Sites of the titanium screw fracture of CoCr control group (CoCr-CG) post biomechanical testing.</p>
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<p>Magnified frontal (<b>a</b>) and lateral (<b>b</b>) views of the titanium screw fracture of one of CoCr electrocautery group constructs (CoCr-EG 3).</p>
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<p>Magnified lateral view of Ti-CG post biomechanical testing: fatigue fracture of the rod at the rod-screw junction, illustrating surface marks of the tightened screws on the rod.</p>
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17 pages, 5797 KiB  
Article
Mechanical Properties of High-Performance Steel-Fibre-Reinforced Concrete and Its Application in Underground Mine Engineering
by Xiang Li, Weipei Xue, Cao Fu, Zhishu Yao and Xiaohu Liu
Materials 2019, 12(15), 2470; https://doi.org/10.3390/ma12152470 - 3 Aug 2019
Cited by 18 | Viewed by 3651
Abstract
In order to economically and reasonably solve the problem of mineshaft support in complex geological conditions, the mechanical properties of high-performance steel-fiber-reinforced concrete (HPSFRC) and its application in mineshaft lining structures were investigated in this study. Firstly, the mix proportion of HPSFRC for [...] Read more.
In order to economically and reasonably solve the problem of mineshaft support in complex geological conditions, the mechanical properties of high-performance steel-fiber-reinforced concrete (HPSFRC) and its application in mineshaft lining structures were investigated in this study. Firstly, the mix proportion of HPSFRC for the mineshaft lining structure was obtained through raw material selection and preparation testing. Then, a series of mechanical property tests were conducted. The test results showed that the compressive, flexural, and tensile strengths of HPSFRC were 9%, 71%, and 53% higher than that of ordinary concrete, respectively. The fracture toughness of HPSFRC was 75% higher than that of the ordinary concrete and the fracture energy of HPSFRC was 16 times that of the ordinary concrete. Finally, the model test results of the HPSFRC shaft lining structure showed that the crack resistance, toughness, and bearing capacity of the shaft lining structure had been significantly improved under a non-uniform confining load because of the replacement of ordinary concrete with HPSFRC. HPSFRC was proved to be an ideal material for mineshaft support structures under complex geological conditions. Full article
(This article belongs to the Special Issue New and Emerging Construction Materials)
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<p>Aggregate gradation.</p>
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<p>RC65/60BN Dramix steel fiber.</p>
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<p>Dimensions and shapes of specimens: (<b>a</b>) compressive strength test; (<b>b</b>) flexural strength test; (<b>c</b>) split tensile strength test; (<b>d</b>) bending test; (<b>e</b>) wedge splitting test.</p>
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<p>Loading manner of the wedge splitting test: (<b>a</b>) wedge loading fixture; (<b>b</b>) roller bearing; (<b>c</b>) notch; (<b>d</b>) hinge roller.</p>
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<p>Templates for pouring shaft lining structure model.</p>
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<p>Shaft lining structure model with completed pouring.</p>
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<p>Load manner of shaft lining structure model.</p>
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<p>Placement of strain gauge and displacement meter.</p>
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<p>Specimens destroyed by split tensile strength test: (<b>a</b>) ordinary concrete specimen, (<b>b</b>) HPSFRC.</p>
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<p>Relationship between vertical load and deflection.</p>
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<p>Relationship between vertical load and <span class="html-italic">CMOD</span> (Crack Mouth Opened Deflection).</p>
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<p>Specimens destroyed by the wedge splitting test: (<b>a</b>) ordinary concrete specimen, (<b>b</b>) HPSFRC.</p>
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<p>Relationship between strain and load of the S4 model: (<b>a</b>) large load direction; (<b>b</b>) small load direction.</p>
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<p>Failure form of model S1.</p>
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<p>Failure form of model S3.</p>
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<p>Relationship between stress and load of S4 model: (<b>a</b>) large load direction; (<b>b</b>) small load direction.</p>
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<p>Relationship between strain and time of the HPSFRC shaft lining structure at a 940 m depth.</p>
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