[go: up one dir, main page]
More Web Proxy on the site http://driver.im/
Next Issue
Volume 17, July-2
Previous Issue
Volume 17, June-2
You seem to have javascript disabled. Please note that many of the page functionalities won't work as expected without javascript enabled.
 
 
materials-logo

Journal Browser

Journal Browser

Materials, Volume 17, Issue 13 (July-1 2024) – 334 articles

Cover Story (view full-size image): Zinc/magnesium ferrite nanoparticles prepared using sol-gel and solvothermal methods, and subsequently functionalized with silver, exhibit notable photodegradation activity using visible light. The best results were achieved with nanoparticles obtained with sol-gel and including an intermediate cleaning step before silver photodeposition. The rate constant for malachite green photodegradation using the optimized nanoparticles is significantly higher than those reported for other nanoparticulate systems. Dye adsorption on the nanoparticles accounts for a large amount of the dye removal process. Moreover, the silver-functionalized mixed ferrites have suitable properties for future industrial applications, also benefiting from the potential for photocatalyst magnetic recovery and reuse. View this paper
  • Issues are regarded as officially published after their release is announced to the table of contents alert mailing list.
  • You may sign up for e-mail alerts to receive table of contents of newly released issues.
  • PDF is the official format for papers published in both, html and pdf forms. To view the papers in pdf format, click on the "PDF Full-text" link, and use the free Adobe Reader to open them.
Order results
Result details
Section
Select all
Export citation of selected articles as:
17 pages, 1881 KiB  
Article
Bimodal Absorber Frequencies Shift Induced by the Coupling of Bright and Dark Modes
by Yun Chen, Jiangbo Hu, Shan Yin, Wentao Zhang and Wei Huang
Materials 2024, 17(13), 3379; https://doi.org/10.3390/ma17133379 - 8 Jul 2024
Viewed by 1064
Abstract
In this paper, we demonstrate that the absorption frequencies of the bimodal absorber shift with the coupling strength of the bright and dark modes. The coupling between the bright mode and the dark mode can acquire electromagnetically induced transparency, we obtain the analytical [...] Read more.
In this paper, we demonstrate that the absorption frequencies of the bimodal absorber shift with the coupling strength of the bright and dark modes. The coupling between the bright mode and the dark mode can acquire electromagnetically induced transparency, we obtain the analytical relationship between the absorbing frequencies, the resonant frequencies, losses of the bright mode and dark mode, and the coupling strength between two modes by combining the coupled mode theory with the interference theory. As the coupling strength between the bright mode and the dark mode decreases, the two absorption peaks gradually move closer to each other, inversely, they will move away from each other. The simulation employs three distinct metasurface structures with coupling of the bright and dark modes, thereby verifying the generality of the theoretical findings. Full article
(This article belongs to the Special Issue Terahertz Materials and Technologies in Materials Science)
Show Figures

Figure 1

Figure 1
<p>(<b>a</b>) The schematic figure of THz bimodal absorber. (<b>b</b>) The schematic figure of the absorption spectrum. (<b>c</b>–<b>e</b>) are examples of the different unit cells of metamaterial devices with different structures of bright modes and dark modes. The geometrical parameters of (<b>c</b>) are <math display="inline"><semantics> <mrow> <msub> <mi>P</mi> <mi>x</mi> </msub> <mo>=</mo> <msub> <mi>P</mi> <mi>y</mi> </msub> <mo>=</mo> <mn>110</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>L</mi> <mo>=</mo> <mn>86</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>l</mi> <mo>=</mo> <mn>35</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>g</mi> <mo>=</mo> <mn>25</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>w</mi> <mo>=</mo> <mn>5</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m with vary distance <span class="html-italic">d</span> between CW and U-shape structure. The geometrical parameters of (<b>d</b>) are <math display="inline"><semantics> <mrow> <msub> <mi>P</mi> <mi>x</mi> </msub> <mo>=</mo> <msub> <mi>P</mi> <mi>y</mi> </msub> <mo>=</mo> <mn>120</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>L</mi> <mo>=</mo> <mn>88</mn> <mo> </mo> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>l</mi> <mo>=</mo> <mn>29</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>g</mi> <mo>=</mo> <mn>5</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>w</mi> <mo>=</mo> <mn>5</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m with vary distance between CW and double-SRRs structure. The geometrical parameters of (<b>e</b>) are <math display="inline"><semantics> <mrow> <msub> <mi>P</mi> <mi>x</mi> </msub> <mo>=</mo> <msub> <mi>P</mi> <mi>y</mi> </msub> <mo>=</mo> <mn>120</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>L</mi> <mo>=</mo> <mn>108</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>R</mi> <mo>=</mo> <mn>20</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>w</mi> <mo>=</mo> <mn>5</mn> <mo> </mo> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, <math display="inline"><semantics> <mrow> <mi>α</mi> <mo>=</mo> <msup> <mn>20</mn> <mo>∘</mo> </msup> </mrow> </semantics></math>, with vary distance <span class="html-italic">d</span> between CW and double-CSRRs structure.</p>
Full article ">Figure 2
<p>Transmission spectra of individual bright and dark modes structures and the whole structure. The black line represents the transmission spectrum of the single CW with <span class="html-italic">y</span> polarization (corresponding to the bright mode ➁). The blue and the red lines are the transmission spectra of the excited dark mode (single U-shape) with <span class="html-italic">x</span> polarization (➂) and unexcited dark mode with <span class="html-italic">y</span> polarization (➃), respectively. The green line represents the EIT transmission spectrum with the coupling of the bright and the dark modes (corresponding to the whole structure with <span class="html-italic">y</span> polarization ➀).</p>
Full article ">Figure 3
<p>Transmission spectra of individual bright and dark modes structures and the whole structure. (<b>a</b>) The black line shows the transmission spectrum of a single CW with <span class="html-italic">y</span> polarization (corresponding to the bright mode ➁). The blue and the red lines are transmission spectra of the excited dark mode (two SRRs-shape) with <span class="html-italic">x</span> polarization (➂) and unexcited dark mode with <span class="html-italic">y</span> polarization (➃), respectively. The green line represents the EIT transmission spectrum with the coupling of the bright and the dark modes (corresponding to the whole structure with <span class="html-italic">y</span> polarization (➀). (<b>b</b>) The black line shows the transmission spectrum of a single CW with <span class="html-italic">y</span> polarization (corresponding to the bright mode ➁). The blue and the red lines are the transmission spectra of the excited dark mode (two CSRRs-shape) with <span class="html-italic">x</span> polarization (➂) and unexcited dark mode with <span class="html-italic">y</span> polarization (➃), respectively. The green line represents the EIT transmission spectrum with the coupling of the bright and the dark modes (corresponding to the whole structure with <span class="html-italic">y</span> polarization (➀).</p>
Full article ">Figure 4
<p>(<b>a</b>,<b>c</b>,<b>e</b>) are three typical EIT metasurface structures with different geometrical parameters of bright and dark modes. (<b>b</b>,<b>d</b>,<b>f</b>) are the corresponding absorption spectra with different distances <span class="html-italic">d</span> between the bright modes (CWs) and the dark modes (U-shape, SRRs-shape, and CRRs-shape) structures.</p>
Full article ">Figure 5
<p>The absorption spectra of the whole structure (blue line) and the single bright mode (black line) and dark mode (red line) under <span class="html-italic">y</span> polarization with different structures (<b>a</b>) U-shape, and (<b>b</b>) CSRRs.</p>
Full article ">Figure 6
<p>The absorption spectra of the whole structure (blue line) and the single bright mode (black line) and dark modes (red line) under <span class="html-italic">y</span> polarization with different positions (<b>a</b>) <math display="inline"><semantics> <mrow> <mi>d</mi> <mi>y</mi> <mo>=</mo> <mo>−</mo> <mn>29.5</mn> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m, and (<b>b</b>) <math display="inline"><semantics> <mrow> <mi>d</mi> <mi>y</mi> <mo>=</mo> <mn>29.5</mn> <mspace width="0.166667em"/> <mi mathvariant="sans-serif">μ</mi> </mrow> </semantics></math>m.</p>
Full article ">Figure 7
<p>Simulation and theory spectra of three different structures, the transmission (<b>a</b>,<b>c</b>,<b>e</b>), and the absorption (<b>b</b>,<b>d</b>,<b>f</b>). The black dotted lines are the simulated results, and the red solid lines are the theoretical results.</p>
Full article ">Figure 8
<p>Simulation and theory spectra of the U-shape structure. The CST simulated result (black dotted line), the theoretical result obtained by our method (red solid line), the theoretical result by employing CMT without interference model (green solid line), and the theoretical result by interference model without CMT (blue solid line).</p>
Full article ">
13 pages, 3573 KiB  
Article
Deformation Behavior of AZ31 Magnesium Alloy with Pre-Twins under Biaxial Tension
by Hanshu Dai, Mengmeng Sun and Yao Cheng
Materials 2024, 17(13), 3377; https://doi.org/10.3390/ma17133377 - 8 Jul 2024
Cited by 1 | Viewed by 780
Abstract
In the present study, the mechanical response and deformation behavior of a Mg AZ31 plate with different types of pre-twins was systematically investigated under biaxial tension along the normal direction (ND) and transverse direction (TD) with different stress ratios. The results show that [...] Read more.
In the present study, the mechanical response and deformation behavior of a Mg AZ31 plate with different types of pre-twins was systematically investigated under biaxial tension along the normal direction (ND) and transverse direction (TD) with different stress ratios. The results show that significant hardening was observed under biaxial tension. The yield values in the direction of larger stress values were higher than those under uniaxial loading conditions, and the solute atom segregation at twin boundaries generates more obvious strengthening effect. Noting that, for TRH (with cross compression along the rolling direction (RD) and TD and annealing at 180 °C for about 0.5 h) sample, the strength effect of the RD yield stress σRD:σND = 2:1 was higher than that of the ND yield stress under stress ratio σRD:σND = 1:2. There is a complex competition between twinning and detwinning under biaxal tension along the ND and TD of the pre-twinned samples with the variation in the stress ratio along the TD and RD. The variation in the twin volume fractions for all samples under biaxial firstly decreases and then increases with a higher stress ratio along the ND. As for the TDH sample (precompression along the TD and annealing), the changes of the twin volume fraction were lower than that of the TR sample (cross compression along the TD and RD). However, the amplitude of variation in twin volume fraction of the TRH sample is higher than that of the TR sample. This is because the relative activity of detwinning decreases and that of twinning increases, as the ND stress mainly leads to the growth of pre-twins and the TD stress often promotes detwinning of primary twins. With a higher stress ratio along the ND, the activity of twinning deformation increases and that of detwinning decreases. Full article
(This article belongs to the Section Metals and Alloys)
Show Figures

Figure 1

Figure 1
<p>(<b>a</b>) ND inverse pole figure map and (<b>b</b>) pole figure of <math display="inline"><semantics> <mrow> <mfenced separators="|"> <mrow> <mn>0001</mn> </mrow> </mfenced> <mo> </mo> <mi>and</mi> <mo> </mo> <mfenced separators="|"> <mrow> <mn>10</mn> <mover accent="true"> <mrow> <mn>1</mn> </mrow> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </mfenced> </mrow> </semantics></math> for initial sample. (<b>c</b>) Schematic diagram of compression along TD (TD sample) and multi-directional compression along TD and RD (TR sample). (<b>d</b>) Cruciform specimen and IPBF-8000 (CARE Measurement &amp; Control Co., Ltd., Tianjing, China) biaxial tension testing system.</p>
Full article ">Figure 2
<p>True stress–strain curves of the TD sample (<b>a</b>), TR sample (<b>b</b>), TDH sample (<b>c</b>) and TRH sample (<b>d</b>) under uniaxial tension.</p>
Full article ">Figure 3
<p>True stress–strain curves of the TD sample under biaxial tension.</p>
Full article ">Figure 4
<p>True stress–strain curves of the TR sample under biaxial tension.</p>
Full article ">Figure 5
<p>True stress–strain curves of the TDH sample under biaxial tension.</p>
Full article ">Figure 6
<p>True stress–strain curves of the TRH sample under biaxial tension.</p>
Full article ">Figure 7
<p>Inverse pole figure and grain boundary of the TD sample (<b>a</b>,<b>b</b>), TR sample (<b>c</b>,<b>d</b>), TDH sample (<b>e</b>,<b>f</b>), and TRH sample (<b>g</b>,<b>h</b>).</p>
Full article ">Figure 8
<p>Inverse pole figure and grain boundary figure for TD sample under biaxial tension: (<b>a</b>,<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 2:1; (<b>b</b>,<b>e</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:1; (<b>c</b>,<b>f</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:2.</p>
Full article ">Figure 9
<p>Inverse pole figure and grain boundary figure for TR sample under biaxial tensioned: (<b>a</b>,<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 2:1; (<b>b</b>,<b>e</b>)<math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:1; (<b>c</b>,<b>f</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:2.</p>
Full article ">Figure 10
<p>Inverse pole figure and grain boundary figure for TDH sample under biaxial tension: (<b>a</b>,<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 2:1; (<b>b</b>,<b>e</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:1; (<b>c</b>,<b>f</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:2.</p>
Full article ">Figure 11
<p>Inverse pole figure and grain boundary figure for TRH sample under biaxial tension: (<b>a</b>,<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 2:1; (<b>b</b>,<b>e</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:1; (<b>c</b>,<b>f</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:2.</p>
Full article ">Figure 12
<p>Pole figure for undeformed TD sample and biaxial-tensioned samples: (<b>a</b>) undeformed sample; (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 2:1; (<b>c</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:1; (<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:2.</p>
Full article ">Figure 13
<p>Pole figure for undeformed TR sample and biaxial-tensioned samples: (<b>a</b>) undeformed sample; (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 2:1; (<b>c</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:1; (<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:2.</p>
Full article ">Figure 14
<p>Pole figure for undeformed TDH sample and biaxial-tensioned samples: (<b>a</b>) undeformed sample; (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 2:1; (<b>c</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:1; (<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>TD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:2.</p>
Full article ">Figure 15
<p>Pole figure for undeformed TRH sample and biaxial-tensioned samples: (<b>a</b>) undeformed sample; (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 2:1; (<b>c</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:1; (<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>RD</mi> </mrow> </msub> <mo>:</mo> <msub> <mrow> <mi mathvariant="sans-serif">σ</mi> </mrow> <mrow> <mi>ND</mi> </mrow> </msub> </mrow> </semantics></math> = 1:2.</p>
Full article ">Figure 16
<p>Changes in the twin volume fraction of TD and TR deformed samples compared with undeformed samples under different stress ratios.</p>
Full article ">Figure 17
<p>(<b>a</b>) Definition figure of TD and RD orientation and distribution of TD and RD orientation for TD (<b>b</b>) and TR (<b>c</b>) sample.</p>
Full article ">Figure 18
<p>Change in twin volume fraction for (<b>a</b>) TD and TDH samples and (<b>b</b>) TR and TRH sample.</p>
Full article ">Figure 19
<p>Distribution of TD and RD orientation for TRH sample.</p>
Full article ">
12 pages, 3138 KiB  
Article
Synthesis of Up-Conversion CaTiO3: Er3+ Films on Titanium by Anodization and Hydrothermal Method for Biomedical Applications
by Nguyen Thi Thanh Tuyen, Ta Quoc Tuan, Le Van Toan, Le Thi Tam and Vuong-Hung Pham
Materials 2024, 17(13), 3376; https://doi.org/10.3390/ma17133376 - 8 Jul 2024
Cited by 1 | Viewed by 909
Abstract
The present study investigates the effects of Er3+ doping content on the microstructure and up-conversion emission properties of CaTiO3: Er3+ phosphors as a potential material in biomedical applications. The CaTiO3: x%Er3+ (x = 0.5, [...] Read more.
The present study investigates the effects of Er3+ doping content on the microstructure and up-conversion emission properties of CaTiO3: Er3+ phosphors as a potential material in biomedical applications. The CaTiO3: x%Er3+ (x = 0.5, 1.0, 1.5, 2.0, 2.5, and 3.0%) films were synthesized on Ti substrates by a hydrothermal reaction at 200 °C for 24 h. The SEM image showed the formation of cubic nanorod CaTiO3: Er3+ films with a mean edge size value of (1–5) μm. When excited with 980 nm light, the CaTiO3: Er3+ films emitted a strong green band and a weak red band of Er3+ ions located at 543, 661, and 740 nm. The CaTiO3: Er3+ film exhibited excellent surface hydrophilicity with a contact angle of ~zero and good biocompatibility against baby hamster kidney (BHK) cells. CaTiO3: Er3+ films emerge as promising materials for different applications in the biomedical field. Full article
(This article belongs to the Section Thin Films and Interfaces)
Show Figures

Figure 1

Figure 1
<p>(<b>a</b>) XRD patterns of CaTiO<sub>3</sub>: <span class="html-italic">x</span>Er<sup>3+</sup> films (<span class="html-italic">x</span> = 0.5, 1.0, 1.5, 2.0, 2.5, and 3.0 mol%); (<b>b</b>) Raman spectra of CaTiO<sub>3</sub>: Er<sup>3+</sup> films.</p>
Full article ">Figure 2
<p>EDS spectra of (<b>a</b>) CaTiO<sub>3</sub>: 0.5%Er<sup>3+</sup>, (<b>b</b>) CaTiO<sub>3</sub>: 2%Er<sup>3+</sup>, and (<b>c</b>) CaTiO<sub>3</sub>: 3%Er<sup>3+</sup> samples.</p>
Full article ">Figure 3
<p>FESEM images of the CaTiO<sub>3</sub>: Er<sup>3+</sup> films with divergent Er<sup>3+</sup> concentration; (<b>a</b>) 0.5% Er<sup>3+</sup> films; (<b>b</b>) 1%Er<sup>3+</sup>; (<b>c</b>) 1.5% Er<sup>3+</sup>; and (<b>d</b>) 2%Er<sup>3+</sup>.</p>
Full article ">Figure 4
<p>(<b>a</b>) UC emission spectra of CaTiO<sub>3</sub>:x% Er<sup>3+</sup> films (x = 0.5, 1.0, 1.5, 2.0, 2.5, and 3.0 mol%). (<b>b</b>) The intensity of green (<sup>2</sup>H<sub>11/2</sub>, <sup>4</sup>S<sub>3/2</sub>–<sup>4</sup>I<sub>15/2</sub>) and red (<sup>4</sup>F<sub>9/2</sub>–<sup>4</sup>I<sub>15/2</sub>) in UC emission as a function of Er<sup>3+</sup> doping concentrations under excitation at 980 nm.</p>
Full article ">Figure 5
<p>(<b>a</b>) PLE excitation spectra of CaTiO<sub>3</sub>: 2% Er<sup>3+</sup> films under emission at 550 nm. (<b>b</b>) PL emission spectra of CaTiO<sub>3</sub>: x% Er<sup>3+</sup> (x = 0.5, 1.0, 1.5, 2.0, 2.5 and 3.0 mol%), under excitation at 980 nm.</p>
Full article ">Figure 6
<p>(<b>a</b>) UC emission spectra of the 2% Er<sup>3+</sup> sample with different power density. (<b>b</b>) The log–log plots of red and green emission intensity as a function of the excitation laser power.</p>
Full article ">Figure 7
<p>Energy level diagram of CaTiO<sub>3</sub>: Er<sup>3+</sup> under excitation at 980 nm.</p>
Full article ">Figure 8
<p>Contact angles of Ti substrate, CaTiO<sub>3</sub>, and CaTiO<sub>3</sub>: Er<sup>3+</sup> films.</p>
Full article ">Figure 9
<p>CLMS images of the BHK cell on (<b>a</b>) Ti; (<b>b</b>) CaTiO<sub>3</sub>: Er<sup>3+</sup> films; and (<b>c</b>) proliferation of the BHK cell on Ti and CaTiO<sub>3</sub>: Er<sup>3+</sup> films after 72 h of culturing. The red indicates the cytoskeleton structure of the cells and the green indicates the cell nuclei.</p>
Full article ">
16 pages, 2344 KiB  
Article
Effect of Carbon on Void Nucleation in Iron
by Lin Shao
Materials 2024, 17(13), 3375; https://doi.org/10.3390/ma17133375 - 8 Jul 2024
Viewed by 863
Abstract
The study reports the significance of carbon presence in affecting void nucleation in Fe. Without carbon, void nucleation rates decrease gradually at high temperatures but remain significantly high and almost saturated at low temperatures. With carbon present, even at 1 atomic parts per [...] Read more.
The study reports the significance of carbon presence in affecting void nucleation in Fe. Without carbon, void nucleation rates decrease gradually at high temperatures but remain significantly high and almost saturated at low temperatures. With carbon present, even at 1 atomic parts per million, void nucleation rates show a low-temperature cutoff. With higher carbon levels, the nucleation temperature window becomes narrower, the maximum nucleation rate becomes lower, and the temperature of maximum void nucleation shifts to a higher temperature. Fundamentally, this is caused by the change in effective vacancy diffusivity due to the formation of carbon-vacancy complexes. The high sensitivity of void nucleation to carbon comes from the high sensitivity of void nucleation to the vacancy arrival rate in a void. The void nucleation is calculated by first obtaining the effective vacancy diffusivity considering the carbon effect, then calculating the defect concentration and defect flux change considering both carbon effects and pre-existing dislocations, and finally calculating the void nucleation rate based on the recently corrected homogeneous void nucleation theory. The study is important not only in the fundamental understanding of impurity effects in ion/neutron irradiation but also in alloy engineering for judiciously introducing impurities to increase swelling resistance, as well as in the development of simulation and modeling methodologies applicable to other metals. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Void density <math display="inline"><semantics> <mrow> <mi>n</mi> <mfenced separators="|"> <mrow> <mi>x</mi> </mrow> </mfenced> <mo> </mo> </mrow> </semantics></math> as a function of void size (number of vacancies contained in a void) under various conditions in α-iron: (<b>a</b>) different temperatures, (<b>b</b>) different <span class="html-italic">S</span> values, and (<b>c</b>) different <math display="inline"><semantics> <mrow> <mrow> <mrow> <msub> <mrow> <mi>β</mi> </mrow> <mrow> <mi>i</mi> </mrow> </msub> </mrow> <mo>/</mo> <mrow> <msub> <mrow> <mi>β</mi> </mrow> <mrow> <mi>v</mi> </mrow> </msub> </mrow> </mrow> </mrow> </semantics></math> ratios.</p>
Full article ">Figure 2
<p>Void nucleation rates as a function of S at different temperatures (700, 800 K, 900 K) and <math display="inline"><semantics> <mrow> <mrow> <mrow> <msub> <mrow> <mi>β</mi> </mrow> <mrow> <mi>i</mi> </mrow> </msub> </mrow> <mo>/</mo> <mrow> <msub> <mrow> <mi>β</mi> </mrow> <mrow> <mi>v</mi> </mrow> </msub> </mrow> </mrow> </mrow> </semantics></math> ratios (0, 0.6, 0.9, and 0.99).</p>
Full article ">Figure 3
<p>Vacancy concentration (atomic fraction, on a logarithmic scale) at different temperatures for various steady-state void nucleation rates (color contour) and under different dpa rates (square lines) in α-iron. The point of intersection between a square line and a colored contour line gives the nucleation rate at a specific temperature and dpa rate.</p>
Full article ">Figure 4
<p>Effective vacancy diffusivity as a function of temperatures and C concentrations in α-iron.</p>
Full article ">Figure 5
<p>The map of void nucleation rates as a function of C concentrations and temperatures in α-iron.</p>
Full article ">Figure 6
<p>The plot of void nucleation rates as a function of temperature for C concentrations ranging from 0 to 1000 appm in α-iron.</p>
Full article ">
12 pages, 26650 KiB  
Article
Mechanical and Physicochemical Characteristics of a Novel Premixed Calcium Silicate Sealer
by Naji Kharouf, Filippo Cardinali, Raya Al-Rayesse, Ammar Eid, Ziad Moujaes, Mathilda Nafash, Hamdi Jmal, Frédéric Addiego and Youssef Haikel
Materials 2024, 17(13), 3374; https://doi.org/10.3390/ma17133374 - 8 Jul 2024
Viewed by 1200
Abstract
The aim of the present in vitro study was to evaluate specific mechanical and physicochemical properties of three calcium silicate-based sealers, BioRoot™ Flow (BRF), CeraSeal (CRS) and TotalFill® (TF). Samples were prepared to evaluate different physicochemical and mechanical properties of the tested [...] Read more.
The aim of the present in vitro study was to evaluate specific mechanical and physicochemical properties of three calcium silicate-based sealers, BioRoot™ Flow (BRF), CeraSeal (CRS) and TotalFill® (TF). Samples were prepared to evaluate different physicochemical and mechanical properties of the tested sealers. These evaluations were accomplished by investigating the pH changes over time, porosity, roughness, flow properties, compressive strength and wettability. The results were statistically evaluated using one-way analysis of variance. All three sealers demonstrated an alkaline pH from 1 h of immersion in water to 168 h. A higher porosity and hydrophily were detected in BRF samples compared to CRS and TF. No significant difference was found between the tested materials in the flow properties. Lower compressive strength values were observed for BRF compared to TF and CRS. Differently shaped structures were detected on the three materials after 7 days of immersion in PBS. The three materials demonstrated a higher solubility than 3% after 24 h of immersion in water (CRS < BRF < TF). The novel premixed calcium silicate sealer (BRF) had comparable physicochemical properties to the existing sealers. The lower compressive strength values could facilitate the removal of these materials during retreatment procedures. Further studies should investigate the biological effects of the novel sealer. Full article
Show Figures

Figure 1

Figure 1
<p>Graphical image demonstrates the various Teflon molds used for porosity, solubility, pH, compressive strength, scanning electron microscope, roughness, flow and contact angle analyses.</p>
Full article ">Figure 2
<p>pH evolution with time (1, 24, 72 and 168 h) of distilled water at 37 °C in contact with BRF (BioRoot™ Flow), CRS (CeraSeal) and TF (TotalFill<sup>®</sup>). * <span class="html-italic">p</span> &lt; 0.05.</p>
Full article ">Figure 3
<p>Water drop profiles on BRF (BioRoot™ Flow), CRS (CeraSeal) and TF (TotalFill<sup>®</sup>) surfaces after 10 s of water drop deposition. Digital micrographs of the different surfaces using KEYENCE 7000 VHX showing the roughness of each material.</p>
Full article ">Figure 4
<p>Scanning electron microscope images (2000× and 8000× magnification) demonstrating the mineral depositions on BRF (BioRoot™ Flow), CRS (CeraSeal) and TF (TotalFill<sup>®</sup>) surfaces after 7 days of immersion in PBS. EDX analysis demonstrates the chemical compositions of the different surfaces.</p>
Full article ">Figure 5
<p>Volume rendering of segmented pores (blue color) with a scale bar of 500 µm, and equivalent pore diameter–frequency curves obtained by X-ray tomography analysis in BRF (BioRoot™ Flow), CRS (CeraSeal) and TF (TotalFill<sup>®</sup>).</p>
Full article ">Figure 6
<p>Means and standard deviations of compressive strength values for BRF (BioRoot™ Flow), CRS (CeraSeal) and TF (TotalFill<sup>®</sup>). * <span class="html-italic">p</span> &lt; 0.05.</p>
Full article ">Figure 7
<p>Digital images of the material expansion of BRF (BioRoot™ Flow), CRS (CeraSeal) and TF (TotalFill<sup>®</sup>) after 72 h of incubation at 37 °C. Red circle showed the expansion of BRF sealer.</p>
Full article ">
15 pages, 4551 KiB  
Article
The Impact of Microwave Annealing on MoS2 Devices Assisted by Neural Network-Based Big Data Analysis
by Xing Su, Siwei Cui, Yifei Zhang, Hui Yang and Dongping Wu
Materials 2024, 17(13), 3373; https://doi.org/10.3390/ma17133373 - 8 Jul 2024
Viewed by 790
Abstract
Microwave annealing, an emerging annealing method known for its efficiency and low thermal budget, has established a foundational research base in the annealing of molybdenum disulfide (MoS2) devices. Typically, to obtain high-quality MoS2 devices, mechanical exfoliation is commonly employed. This [...] Read more.
Microwave annealing, an emerging annealing method known for its efficiency and low thermal budget, has established a foundational research base in the annealing of molybdenum disulfide (MoS2) devices. Typically, to obtain high-quality MoS2 devices, mechanical exfoliation is commonly employed. This method’s challenge lies in achieving uniform film thickness, which limits the use of extensive data for studying the effects of microwave annealing on the MoS2 devices. In this experiment, we utilized a neural network approach based on the HSV (hue, saturation, value) color space to assist in distinguishing film thickness for the fabrication of numerous MoS2 devices with enhanced uniformity and consistency. This method allowed us to precisely assess the impact of microwave annealing on device performance. We discovered a relationship between the device’s electrical performance and the annealing power. By analyzing the statistical data of these electrical parameters, we identified the optimal annealing power for MoS2 devices as 700 W, providing insights and guidance for the microwave annealing process of two-dimensional materials. Full article
(This article belongs to the Section Energy Materials)
Show Figures

Figure 1

Figure 1
<p>The classification of four typical MoS<sub>2</sub> thicknesses.</p>
Full article ">Figure 2
<p>Box-and-whisker plots representing the distribution of RGB values across four distinct categories of film thickness: (<b>a</b>) Category 1; (<b>b</b>) Category 2; (<b>c</b>) Category 3; (<b>d</b>) Category 4.</p>
Full article ">Figure 3
<p>Box-and-whisker plots representing the distribution of HSV values across four distinct categories of film thickness: (<b>a</b>) Category 1; (<b>b</b>) Category 2; (<b>c</b>) Category 3; (<b>d</b>) Category 4.</p>
Full article ">Figure 4
<p>Neural network structure for discriminating membrane thickness.</p>
Full article ">Figure 5
<p>Showcased the training process and results of the neural network: (<b>a</b>) A graph depicting the change in validation loss over epochs. (<b>b</b>) The confusion matrix of prediction results; 1, 2, 3, and 4 indicate Category 1, Category 2, Category 3, and Category 4.</p>
Full article ">Figure 6
<p>(<b>a</b>) Optical photograph of a typical MoS<sub>2</sub> device, accompanied by precise values measured via AFM before (in black) and after (in red). The scale bar in the figure is 20 μm. (<b>b</b>) Raman spectroscopy profiles before (in black) and after (in red) 700 W MWA power.</p>
Full article ">Figure 7
<p>(<b>a</b>,<b>b</b>), respectively, depict the transfer characteristic curve and the logarithmic form of the representative MoS<sub>2</sub> FET following exposure to 210 W MWA power in an N<sub>2</sub> atmosphere. (<b>c</b>,<b>d</b>), respectively, depict the transfer characteristic curve and the logarithmic form of the representative MoS<sub>2</sub> FET following exposure to 490 W MWA power in an N<sub>2</sub> atmosphere. (<b>e</b>,<b>f</b>), respectively, depict the transfer characteristic curve and the logarithmic form of the representative MoS<sub>2</sub> FET following exposure to 700 W MWA power in an N<sub>2</sub> atmosphere. (<b>g</b>,<b>h</b>), respectively, depict the transfer characteristic curve and the logarithmic form of the representative MoS<sub>2</sub> FET following exposure to 980 W MWA power in an N<sub>2</sub> atmosphere.</p>
Full article ">Figure 8
<p>The curve before annealing is represented by a dotted line, and the curve after annealing is represented by a solid line. (<b>a</b>) The output curve of the representative MoS<sub>2</sub> FET after the 210 W MWA powers in the N<sub>2</sub> atmosphere. (<b>b</b>) The output curve of the representative MoS<sub>2</sub> FET after the 490 W MWA powers in the N<sub>2</sub> atmosphere. (<b>c</b>) The output curve of the representative MoS<sub>2</sub> FET after the 700 W MWA powers in the N<sub>2</sub> atmosphere. (<b>d</b>) The output curve of the representative MoS<sub>2</sub> FET after the 980 W MWA powers in the N<sub>2</sub> atmosphere.</p>
Full article ">Figure 9
<p>(<b>a</b>) Statistical data on the on-state current. (<b>b</b>) Statistical data on the subthreshold slope. (<b>c</b>) Statistical data on the field-effect mobility. (<b>d</b>) Statistical data on the intrinsic mobility. (<b>e</b>) Statistical data on the contact resistance. (<b>f</b>) Statistical data on the trap density.</p>
Full article ">Figure 10
<p>(<b>a</b>) AFM characterization of SiO<sub>2</sub> dielectric without MWA. (<b>b</b>) AFM characterization of SiO<sub>2</sub> dielectric after MWA at 700 W.</p>
Full article ">
12 pages, 2716 KiB  
Article
Naphthenic Acid Corrosion Mitigation: The Role of Niobium in Low-Carbon Steel
by Nurliyana Mohamad Arifin, Kesahvanveraragu Saravanan and Ervina Efzan Mhd Noor
Materials 2024, 17(13), 3372; https://doi.org/10.3390/ma17133372 - 8 Jul 2024
Viewed by 830
Abstract
Naphthenic acid corrosion is a well-recognized factor contributing to corrosion in the construction of offshore industry pipelines. To mitigate the corrosive effects, minor quantities of alloying elements are introduced into the steel. This research specifically explores the corrosion effects arising from immersing low-carbon [...] Read more.
Naphthenic acid corrosion is a well-recognized factor contributing to corrosion in the construction of offshore industry pipelines. To mitigate the corrosive effects, minor quantities of alloying elements are introduced into the steel. This research specifically explores the corrosion effects arising from immersing low-carbon steel, specifically A333 Grade 6, in a naphthenic acid solution. Various weight percentages of niobium were incorporated, and the resulting properties were observed. It was noted that the addition of 2% niobium in low-carbon steel exhibited the least mass loss and a lower corrosion rate after a 12 h immersion in naphthenic acid. Microstructural analysis using scanning electron microscopy (SEM) revealed small white particles, indicating the presence of oil sediment residue, along with corrosion pits. Following the addition of 2% niobium, the occurrence of corrosion pits markedly decreased, and only minor voids were observed. Additionally, the chemical composition analysis using energy-dispersive X-Ray analysis (EDX) showed that the black spot exhibited the highest percentage of carbon, resembling high corrosion attack. Meanwhile, the whitish regions with low carbon content indicated the lowest corrosion attack. The results demonstrated that the addition of 2% niobium yielded optimal properties for justifying corrosion effects. Therefore, low-carbon steel with a 2% niobium addition can be regarded as a superior corrosion-resistant material for offshore platform pipeline applications. Full article
(This article belongs to the Section Corrosion)
Show Figures

Figure 1

Figure 1
<p>Melting profile of temperature for low-carbon steel type A333 Grade 6.</p>
Full article ">Figure 2
<p>Physical assessment of Fe-C after immersion.</p>
Full article ">Figure 3
<p>(<b>a</b>) Mass loss and (<b>b</b>) corrosion rate of Fe-C and Fe-C-Nb with different percentages of Nb addition.</p>
Full article ">Figure 3 Cont.
<p>(<b>a</b>) Mass loss and (<b>b</b>) corrosion rate of Fe-C and Fe-C-Nb with different percentages of Nb addition.</p>
Full article ">Figure 4
<p>Top-view images of (<b>a</b>,<b>b</b>) Fe-C and Fe-C-Nb with (<b>c</b>,<b>d</b>) 2%, (<b>e</b>,<b>f</b>) 4%, and (<b>g</b>,<b>h</b>) 6% of Nb addition at magnifications of 1000× and 3000×, respectively.</p>
Full article ">Figure 5
<p>Backscattered images of (<b>a</b>) Fe-C and Fe-C-Nb with (<b>b</b>) 2%, (<b>c</b>) 4%, and (<b>d</b>) 6% percentages of Nb addition.</p>
Full article ">
15 pages, 10448 KiB  
Article
Identifying Optimal Processing Variables and Investigating Mechanisms of Grain Alignment in Hot-Deformed NdFeB Magnets through Design of Experiments
by Jongbin Ahn, Jung-Goo Lee and Wooyoung Lee
Materials 2024, 17(13), 3371; https://doi.org/10.3390/ma17133371 - 8 Jul 2024
Viewed by 915
Abstract
This study introduces a novel approach for investigating hot-deformed NdFeB magnets by combining the minimal stress deformation process (MSDP) with the design of experiment (DoE) methodology. This study focused on enhancing the crystallographic alignment, particularly the c-axis alignment of the Nd2Fe [...] Read more.
This study introduces a novel approach for investigating hot-deformed NdFeB magnets by combining the minimal stress deformation process (MSDP) with the design of experiment (DoE) methodology. This study focused on enhancing the crystallographic alignment, particularly the c-axis alignment of the Nd2Fe14B grains, to optimize the magnetic properties. By utilizing the Box-Behnken design matrix and response surface regression, critical processes and variables were identified, determining that a hot-pressing temperature of 700 °C is crucial for achieving optimal grain alignment. Changing the strain rate to 0.019 mm/s under a stress of 110 MPa led to significant enhancements in the alignment, yielding magnets with a remanence of approximately 13.4 kG and a coercivity of 21 kOe. These findings highlight the effectiveness of combining the MSDP and DoE for predicting and achieving improved magnetic properties. Despite the challenges associated with understanding the complexity of crystal alignment mechanisms, this integrated approach successfully improved magnetic characteristics. The methodology represents a significant advancement in the fabrication of high-performance hot-deformed NdFeB magnets, marking a notable contribution to the field. Full article
Show Figures

Figure 1

Figure 1
<p>Backscattered electron-scanning electron microscope (BSE SEM) image of hot-pressed samples; (<b>a</b>) HP675, (<b>b</b>) HP700, and (<b>c</b>) HP725 samples.</p>
Full article ">Figure 2
<p>Nominal stress–true strain hot compression test at a deformation rate of 0.019 mm/s and compression test temperatures of (<b>a</b>) 775, (<b>b</b>) 800, and (<b>c</b>) 825 °C.</p>
Full article ">Figure 3
<p>X-ray diffraction (XRD) patterns of hot deformed magnets procued by (<b>a</b>) HP675 + HD785~HD815 with DR0.019, DR0.029, and DR0.039 and (<b>b</b>) HP700 + HD785 with DR 0.019 and DR0.039.</p>
Full article ">Figure 4
<p>Half Gaussian fitted curves of orientation deviation δ (°) of hot-deformed samples produced by HP700 + HD785 with DR 0.019 and DR0.039.</p>
Full article ">Figure 5
<p>Contour plots for showing the remanence (Br) for (<b>a</b>) HP × HD at DR 0.019 mm/s, (<b>b</b>) HP × DR at HD 800 °C, and (<b>c</b>) HD × DR at HP 700 °C; HP represents the hot-pressing temperature, HD represents the hot-deforming temperature, and DR indicates the deformation rate.</p>
Full article ">Figure 6
<p>Microstructural features of the hot-deformed magnet processed under the conditions of HP700 + HD785 + DR0.019: (<b>a</b>,<b>b</b>) are BSE-SEM images, and (<b>c</b>) is a transmission electron microscope (TEM) image.</p>
Full article ">Figure 7
<p>High-angle annular dark-field (HAADF) scanning transmission electron microscopy (HAADF-STEM) images and energy-dispersive X-ray spectroscopy (EDS) elemental maps for Dy, Pr, Nd, Ga, Co, and Fe in the hot-deformed magnet processed under the conditions of HP700 + HD785 + DR0.019.</p>
Full article ">Figure 8
<p>Logarithmic true strain rate versus logarithmic true stress curve, along with the stress exponent n in the BBD matrix for conditions (a):HP675 HD800, (b):HP700 HD785, (c):HP700 HD815, and (d):HP725 HD800.</p>
Full article ">Figure 9
<p>Demagnetization curves of hot-deformed magnets for (<b>a</b>) the raw magnetic powder, (<b>b</b>) after the hot-pressing process at 700 °C, and (<b>c</b>) after the hot-deformation process at 785 °C, with a deformation rate of 0.019 mm/s.</p>
Full article ">
14 pages, 18667 KiB  
Article
Mechanical Properties of Silicon Carbide Composites Reinforced with Reduced Graphene Oxide
by Kamil Broniszewski, Jarosław Woźniak, Tomasz Cygan, Dorota Moszczyńska and Andrzej Olszyna
Materials 2024, 17(13), 3370; https://doi.org/10.3390/ma17133370 - 8 Jul 2024
Viewed by 789
Abstract
This article presents research on the influence of reduced graphene oxide on the mechanical properties of silicon carbide matrix composites sintered with the use of the Spark Plasma Sintering method. The produced sinters were subjected to a three-point bending test. An increase in [...] Read more.
This article presents research on the influence of reduced graphene oxide on the mechanical properties of silicon carbide matrix composites sintered with the use of the Spark Plasma Sintering method. The produced sinters were subjected to a three-point bending test. An increase in flexural strength was observed, which reaches a maximum value of 503.8 MPa for SiC–2 wt.% rGO composite in comparison to 323 MPa for the reference SiC sample. The hardness of composites decreases with the increase in rGO content down to 1475 HV10, which is correlated with density results. Measured fracture toughness values are burdened with a high standard deviation due to the presence of rGO agglomerates. The KIC reaches values in the range of 3.22–3.82 MPa*m1/2. Three main mechanisms responsible for the increase in the fracture toughness of composites were identified: bridging, deflecting, and branching of cracks. Obtained results show that reduced graphene oxide can be used as a reinforcing phase to the SiC matrix, with an especially visible impact on flexural strength. Full article
Show Figures

Figure 1

Figure 1
<p>Relative density results for produced SiC–rGO composites.</p>
Full article ">Figure 2
<p>SPS sintering curves for SiC−2 wt.% rGO composite.</p>
Full article ">Figure 3
<p>SEM image of surface fracture of SiC–2 wt.% rGO: (<b>a</b>) Visible elongated grains of silicon carbide; (<b>b</b>) Reduced graphene oxide agglomerate and the interface between SiC matrix and rGO particles.</p>
Full article ">Figure 4
<p>Exemplary phase analysis of composite containing 2 wt.% rGO. Three phases were detected: the matrix phase–SiC (6H polytype), the reinforcement phase–rGO, and a trace amount of SiO<sub>2</sub>.</p>
Full article ">Figure 5
<p>The Raman spectra of pure rGO powder and the representative SiC−2 wt.% rGO composite. Vertical lines were placed in the peaks for the rGO powder substrate to help the observation of a slight shift towards higher values for the sinter.</p>
Full article ">Figure 6
<p>Measured values of Young modulus for sintered composites.</p>
Full article ">Figure 7
<p>Vickers hardness test results for SiC matrix composites reinforced with rGO.</p>
Full article ">Figure 8
<p>Results of fracture toughness of silicon carbide matrix composites reinforced with reduced graphene oxide.</p>
Full article ">Figure 9
<p>Main mechanisms of increasing the fracture toughness identified in produced SiC–rGO composites. (<b>a</b>) Crack deflecting; (<b>b</b>) Crack ending; (<b>c</b>–<b>e</b>) Crack bridging (<b>f</b>) Crack branching.</p>
Full article ">Figure 10
<p>Flexural strength results for produced composites.</p>
Full article ">Figure 11
<p>SEM images of fractures of beams after 3–point bending test. The compression curl area is located in the upper part of the samples. The blue circle indicates a possible fracture origin. (<b>a</b>,<b>b</b>) SiC–0.75 wt.% rGO composite; (<b>c</b>,<b>d</b>) SiC–2 wt.% rGO composite with marked rGO particles.</p>
Full article ">
8 pages, 1329 KiB  
Communication
Unified Solid Solution Product of [Nb][C] in Nb-Microalloyed Steels with Various Carbon Contents
by Yongming Yan, Yanjun Xue, Ke Liu, Wenchao Yu, Jie Shi and Maoqiu Wang
Materials 2024, 17(13), 3369; https://doi.org/10.3390/ma17133369 - 8 Jul 2024
Cited by 1 | Viewed by 670
Abstract
In this work, the solid solution product of [Nb][C] in the Nb-microalloyed steels with various carbon contents in the range of 0.20~1.80 wt.% was investigated by means of the extraction phase analysis method. The results showed that the Nb content in austenite tended [...] Read more.
In this work, the solid solution product of [Nb][C] in the Nb-microalloyed steels with various carbon contents in the range of 0.20~1.80 wt.% was investigated by means of the extraction phase analysis method. The results showed that the Nb content in austenite tended to first decrease and then increase with the increase of carbon content in the steels. A unified solid solution product of [Nb][C] in austenite at different temperatures was obtained according to the results of the experimental steels. The Nb content in austenite of the experimental steels with high carbon contents was lower than that calculated by Ohtani’s equation. The existence of NbC precipitates in the case and the core of the specimens carburized at 930 °C and 980 °C were verified by transmission electron microscopy (TEM) observations. The pinning effect of NbC precipitates on austenite grain growth was calculated according to the size and amount of NbC precipitates in the carburized case and the core of the carburized specimens. The calculated results of prior austenite grain sizes were in good agreement with the experimental results, which indicated that the unified solid solution product of [Nb][C] in Nb-microalloyed steels with various carbon contents was applicable for the low-pressure carburizing process. Full article
(This article belongs to the Section Metals and Alloys)
Show Figures

Figure 1

Figure 1
<p>Schematic diagrams showing the low-pressure carburizing process.</p>
Full article ">Figure 2
<p>Variation of the solid solubility of Nb in austenite with carbon content at 980 °C.</p>
Full article ">Figure 3
<p>Optical micrographs showing prior austenite grains: (<b>a</b>) the case and (<b>b</b>) the core of the 930 °C carburized specimen.</p>
Full article ">Figure 4
<p>TEM micrographs showing NbC precipitates in (<b>a</b>) the case and (<b>b</b>) the core of the specimens carburized at 930 °C, and (<b>c</b>) the case and (<b>d</b>) core of the specimens carburized at 980 °C.</p>
Full article ">
14 pages, 8459 KiB  
Article
Performance and Morphology of Waterborne Polyurethane Asphalt in the Vicinity of Phase Inversion
by Chengwei Wu, Haocheng Yang, Xinpeng Cui, Yachun Chen, Zhonghua Xi, Jun Cai, Junsheng Zhang and Hongfeng Xie
Materials 2024, 17(13), 3368; https://doi.org/10.3390/ma17133368 - 8 Jul 2024
Cited by 1 | Viewed by 976
Abstract
Waterborne polyurethane asphalt emulsion (WPUA) is an environmentally friendly bituminous material, whose performance is highly dependent on the phase structure of the continuous phase. In this paper, WPUAs in the vicinity of phase inversion were prepared using waterborne polyurethane (WPU) and asphalt emulsion. [...] Read more.
Waterborne polyurethane asphalt emulsion (WPUA) is an environmentally friendly bituminous material, whose performance is highly dependent on the phase structure of the continuous phase. In this paper, WPUAs in the vicinity of phase inversion were prepared using waterborne polyurethane (WPU) and asphalt emulsion. The chemical structures, thermal stability, dynamic mechanical properties, phase-separated morphology and mechanical performance of WPUAs were studied. Fourier-transform infrared (FTIR) spectra revealed that there are no –NCO bonds in either the pure WPU or WPUAs. Moreover, the preparation of WPUA is a physical process. The addition of WPU weakens the thermal stability of asphalt emulsion. WPU improves the storage modulus of asphalt emulsion at lower and higher temperatures. The glass transition temperatures of the WPUA films are higher than that of the pure WPU film. When the WPU concentration increases from 30 wt% to 40 wt%, phase inversion occurs; that is, the continuous phase shifts from asphalt to WPU. The WPUA films have lower tensile strength and toughness than the pure WPU film. However, the elongations at break of the WPUA films are higher than that of the pure WPU film. Both the tensile strength and toughness of the WPUA films increase with the WPU concentration. Due to the occurrence of phase inversion, the elongation at break, tensile strength and toughness of the WPUA film containing 30 wt% WPU are increased by 29%, 250% and 369%, respectively, compared to the film with 40 wt% WPU. Full article
Show Figures

Figure 1

Figure 1
<p>Synthesis procedure of WPU.</p>
Full article ">Figure 2
<p>Schematic presentation of WPUA film preparation.</p>
Full article ">Figure 3
<p>FTIR spectra of asphalt emulsion, WPU and WPUA films.</p>
Full article ">Figure 4
<p>TGA (<b>a</b>) and DTG (<b>b</b>) curves of asphalt emulsion, WPU and WPUA films.</p>
Full article ">Figure 5
<p>Storage modulus as a function of temperature for WPU and WPUA films.</p>
Full article ">Figure 6
<p>Loss modulus as a function of temperature for WPU and WPUA films.</p>
Full article ">Figure 7
<p>Confocal microscopy photographs of WPUAs with different WPU concentrations: 30 wt% (<b>a</b>), 40 wt% (<b>b</b>) and 50 wt% (<b>c</b>).</p>
Full article ">Figure 8
<p>Mechanical properties of the WPU and WPUA films: tensile strength (<b>a</b>) and elongation at break (<b>b</b>).</p>
Full article ">Figure 9
<p>Toughness of the WPU and WPUA films.</p>
Full article ">
15 pages, 5814 KiB  
Article
Verification of the Laser Powder Bed Fusion Performance of 2024 Aluminum Alloys Modified Using Nano-LaB6
by Zeyu Yao and Ziwen Xie
Materials 2024, 17(13), 3367; https://doi.org/10.3390/ma17133367 - 8 Jul 2024
Viewed by 1176
Abstract
The application of 2024 aluminum alloy (comprising aluminum, copper, and magnesium) in the aerospace industry is extensive, particularly in the manufacture of seats. However, this alloy faces challenges during laser powder bed fusion (PBF-LB/M) processing, which often leads to solidification and cracking issues. [...] Read more.
The application of 2024 aluminum alloy (comprising aluminum, copper, and magnesium) in the aerospace industry is extensive, particularly in the manufacture of seats. However, this alloy faces challenges during laser powder bed fusion (PBF-LB/M) processing, which often leads to solidification and cracking issues. To address these challenges, LaB6 nanoparticles have been investigated as potential grain refiners. This study systematically examined the impact of adding different amounts of LaB6 nanoparticles (ranging from 0.0 to 1.0 wt.%) on the microstructure, phase composition, grain size, and mechanical properties of the composite material. The results demonstrate that the addition of 0.5 wt.% LaB6 significantly reduces the average grain size from 10.3 μm to 9 μm, leading to a significant grain refinement effect. Furthermore, the tensile strength and fracture strain of the LaB6-modified A2024 alloy reach 251 ± 2 MPa and 1.58 ± 0.12%, respectively. These findings indicate that the addition of appropriate amounts of LaB6 nanoparticles can effectively refine the grains of 2024 aluminum alloy, thereby enhancing its mechanical properties. This discovery provides important support for the broader application of 2024 aluminum alloy in the aerospace industry and other high-performance fields. Full article
(This article belongs to the Section Metals and Alloys)
Show Figures

Figure 1

Figure 1
<p>The morphology of feedstock powder: (<b>a</b>) the micrograph of A2024 powder, (<b>b</b>) the micrograph of LaB<sub>6</sub> powder, (<b>c</b>) the micrograph of LaB<sub>6</sub>/A2024 mixed powder, and (<b>d</b>) the corresponding EDS maps of (<b>c</b>).</p>
Full article ">Figure 2
<p>Particle size distribution histogram (μm).</p>
Full article ">Figure 3
<p>(<b>a</b>) Scanning strategy between consecutive layers and (<b>b</b>) tensile specimen details.</p>
Full article ">Figure 4
<p>X-ray diffraction patterns of A2024 powder and constructed PBF-LB/M samples: (<b>a</b>) complete XRD patterns within the range of 20~90°; and (<b>b</b>) the amplified area of the pattern, representing low intensities.</p>
Full article ">Figure 5
<p>SEM morphology of the XY section microstructure of PBF-LB/M-formed LaB<sub>6</sub>/A2024 samples: (<b>a</b>) S<sub>0</sub>, (<b>b</b>) S<sub>0.2</sub>, (<b>c</b>) S<sub>0.5</sub>, (<b>d</b>) S<sub>0.75</sub>, (<b>e</b>) S<sub>1</sub>, and (<b>c-1</b>) partial magnification of (<b>c</b>).</p>
Full article ">Figure 6
<p>Horizontal EBSD inverse pole plot (EBSD-IPF): pole plots of (<b>a</b>–<b>c</b>) S<sub>0</sub>, (<b>d</b>–<b>f</b>) S<sub>0.5</sub>, and KAM. Observe the crystal orientation along the top surface (XY plane) and the IPF color of the sample, including the code representing the grain orientation. The KAM mapping is retrieved in degrees from the EBSD-IPF mapping in (<b>a</b>,<b>d</b>).</p>
Full article ">Figure 7
<p>Average grain size of the PBF-LB/M-formed alloys. (<b>a</b>) S<sub>0</sub> and (<b>b</b>) S<sub>0.5</sub>; misorientation angle of (<b>d</b>) S<sub>0</sub> and (<b>e</b>) S<sub>0.5</sub>; and GND density of (<b>c</b>) S<sub>0</sub> and (<b>f</b>) S<sub>0.5</sub>.</p>
Full article ">Figure 8
<p>The mechanical properties of LaB<sub>6</sub>/A2024 samples prepared by LPFB. (<b>a</b>) Microhardness and (<b>b</b>) tensile performance.</p>
Full article ">Figure 9
<p>The formation mechanism and morphology of A2024 composite alloys during the PBF-LB/M process: (<b>a</b>) A2024 and (<b>b</b>) A2024 with LaB<sub>6</sub> particle addition.</p>
Full article ">Figure 10
<p>(<b>a</b>) Thinned TEM sample of LaB<sub>6</sub>/A2024 composite alloys via FIB technology; (<b>b</b>) TEM image of the LaB<sub>6</sub>/A2024 interface; (<b>c</b>–<b>j</b>) EDS mapping of Al, Cu, Mg, Mn, Fe, O, La, and B elements; (<b>k</b>,<b>l</b>) corresponding FFT and IFFT images.</p>
Full article ">
11 pages, 13214 KiB  
Article
Three-Dimensional Printing of Yttrium Oxide Transparent Ceramics via Direct Ink Writing
by Qiming Chen, Huibing Li, Weijie Han, Jian Yang, Wentao Xu and Youfu Zhou
Materials 2024, 17(13), 3366; https://doi.org/10.3390/ma17133366 - 8 Jul 2024
Viewed by 1066
Abstract
The utilization of 3D printing technology for the fabrication of intricate transparent ceramics overcomes the limitations associated with conventional molding processes, thereby presenting a highly promising solution. In this study, we employed direct ink writing (DIW) to prepare yttrium oxide transparent ceramics using [...] Read more.
The utilization of 3D printing technology for the fabrication of intricate transparent ceramics overcomes the limitations associated with conventional molding processes, thereby presenting a highly promising solution. In this study, we employed direct ink writing (DIW) to prepare yttrium oxide transparent ceramics using a ceramic slurry with excellent moldability, solid content of 45 vol%, and shear-thinning behavior. A successfully printed transparent yttrium oxide ring measuring 30 mm in diameter, 10 mm in inner diameter, and 0.9 mm in thickness was obtained from the aforementioned slurry. After de-binding and sintering procedures, the printed ceramic exhibited in-line transmittance of 71% at 850 nm. This work not only produced complex yttria transparent ceramics with intricate shapes, but also achieved in-line transmittance that was comparable to that of the CIP method (79%), which can meet certain optical applications. Full article
(This article belongs to the Section Advanced and Functional Ceramics and Glasses)
Show Figures

Figure 1

Figure 1
<p>The process of preparing printable slurry.</p>
Full article ">Figure 2
<p>(<b>a</b>) The construction of the print model; (<b>b</b>) 3D printer.</p>
Full article ">Figure 3
<p>(<b>a</b>) Viscosity curve for the slurry with different Isobam-104 content; (<b>b</b>) zeta potentials at different pH values.</p>
Full article ">Figure 4
<p>Rheological properties of the print slurry with varying solid loading: (<b>a</b>) viscosity evolution and (<b>b</b>) complex shear strain.</p>
Full article ">Figure 5
<p>TG analysis curves of 3D-printed green body from slurry with 45 vol% solid loading and 0.7 wt% Isobam-104, 0.5 wt% TAC, 1.2 wt% glycerol.</p>
Full article ">Figure 6
<p>Microstructure of the 3D-printed green body was examined (<b>a</b>) prior to de-binding and (<b>b</b>) after de-binding at a temperature of 700 °C for a duration of 3 h.</p>
Full article ">Figure 7
<p>Phase identification. The XRD of (<b>a</b>) CIP and (<b>b</b>) 3D printing exhibit a single yttrium oxide phase. PDF cards from ICDD database: Yttrium Oxide #71-0099.</p>
Full article ">Figure 8
<p>Scanning electron microscopy (SEM) images depicting the fracture surfaces of 3D printing samples sintered at varying temperatures: (<b>a</b>) 1750 °C, (<b>b</b>) 1800 °C, and (<b>c</b>) 1850 °C, as well as the fracture surface of cold isostatic pressed (CIP) samples sintered under varying temperature conditions: (<b>d</b>) 1750 °C, (<b>e</b>) 1800 °C, and (<b>f</b>) 1850 °C.</p>
Full article ">Figure 9
<p>(<b>a</b>) In-line transmittance of 3D-printed and CIP ceramics post-sintering. (<b>b</b>) In-line transmittance of 3D-printed and CIP ceramics at varying sintering temperatures at 850 nm.</p>
Full article ">
14 pages, 4920 KiB  
Article
Investigating the Anticancer Potential of Zinc and Magnesium Alloys: From Base Materials to Nanocoated Titanium Implants
by Andrij Milenin, Łukasz Niedźwiedzki, Karolina Truchan, Grzegorz Guzik, Sławomir Kąc, Grzegorz Tylko and Anna Maria Osyczka
Materials 2024, 17(13), 3365; https://doi.org/10.3390/ma17133365 - 8 Jul 2024
Viewed by 1237
Abstract
In this work, we show the in vitro anticancer potential of surgical wires, obtained from zinc (ZnMg0.004) or magnesium (MgCa0.7) alloys by spatial technology comprising casting, extrusion, and final drawing processes. We also present the selective anticancer effects of applied soluble multilayer nanocoatings [...] Read more.
In this work, we show the in vitro anticancer potential of surgical wires, obtained from zinc (ZnMg0.004) or magnesium (MgCa0.7) alloys by spatial technology comprising casting, extrusion, and final drawing processes. We also present the selective anticancer effects of applied soluble multilayer nanocoatings of zinc and magnesium onto titanium surfaces using the pulse laser deposition method. In the latter, the titanium samples were produced via 3D printing using the selective laser melting method and coated with various combinations of zinc and magnesium layers. For cytotoxicity studies, human dental pulp-derived stem cells (hDPSCs) and human osteosarcoma SaOS-2 cell line were used as representatives of healthy and cancer cells. Cells were examined against the 0.3–3.0 cm2/mL material extract ratios obtained from experimental and steel surgical wires, the latter being the current clinical industry standard. The MgCa0.7 alloy wires were approx. 1.5 times more toxic to cancer cells at all examined extract ratios vs. the extracts from steel surgical wires that exhibited comparable toxicity towards healthy and cancer cells. The ZnMg0.004 alloy wires displayed increased toxicity towards cancer cells with decreasing extract ratios. This was also reflected in the increased anticancer effectiveness, calculated based on the viability ratio of healthy cells to cancer cells, from 1.1 to 4.0 times. Healthy cell viability remained at 80–100%, whereas cancer cell survival fluctuated at 20–75%, depending on the extract ratio. Furthermore, the culture of normal or cancer cells on the surface of Zn/Mg-coated titanium allowed us to select combinations of specific coating layers that yielded a comparable anticancer effectiveness to that observed with the experimental wires that ranged between 2 and 3. Overall, this work not only demonstrates the substantial anticancer properties of the studied wires but also indicates that similar anticancer effects can be replicated with appropriate nanocoatings on titanium samples. We believe that this work lays the groundwork for the future potential development of the category of new implants endowed with anticancer properties. Full article
(This article belongs to the Special Issue Biocompatible and Bioactive Materials for Medical Applications)
Show Figures

Figure 1

Figure 1
<p>Technological production chain of ZnMg0.004 and MgCa0.7 wires: (<b>a</b>) ingot casting, (<b>b</b>) ingot cutting, (<b>c</b>) FEM simulation of extrusion, (<b>d</b>) extrusion process, view of extruded rods, (<b>e</b>) principal scheme of hot drawing process, (<b>f</b>) infrared image of hot wire drawing process, (<b>g</b>) principal scheme of cold drawing process, and (<b>h</b>) equipment for cold drawing; 1—wire; 2—wire die; 3—heating device; 4—wire heating zone length regulator.</p>
Full article ">Figure 2
<p>(<b>a</b>) PLD technique scheme and (<b>b</b>) the equipment used for this experiment.</p>
Full article ">Figure 3
<p>Examples of hip and knee joint implants manufactured from 3D SLM printed titanium.</p>
Full article ">Figure 4
<p>The coated titanium samples used for cytotoxicity testing. The material and coating thickness are written above each picture. In the case of the coating of two materials, the thickness of each layer is shown.</p>
Full article ">Figure 5
<p>The overall flowchart of the research method.</p>
Full article ">Figure 6
<p>The characteristic microstructure of the wires obtained from (<b>a</b>) ZnMg0.004 and (<b>b</b>) MgCa0.7 alloys, after their final drawing to ∅ 1 mm for (<b>a</b>) and ∅ 1.3 mm for (<b>b</b>).</p>
Full article ">Figure 7
<p>The dependence of human cancer (SaOS-2) and healthy human DPSC (hDPSC) cell viability on the wires’ extract ratio: (<b>a</b>) wires made of the MgCa0.7 alloy; (<b>b</b>) wires made of the ZnMg0.004 (ZnMg—high extract ratio, ZnMg(2)—low extract ratio experiments) alloy. Two-way ANOVA tests, * <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.001, *** <span class="html-italic">p</span> &lt; 0.0001.</p>
Full article ">Figure 8
<p>Anticancer effectivity calculated for the extracts prepared from ZnMg0.004 (ZnMg—high extract ratio, ZnMg(2)—low extract ratio experiments), MgCa0.7 (MgCa), and steel (Steel) surgical wires. R<sup>2</sup>—coefficient of determination, Pearson correlation.</p>
Full article ">Figure 9
<p>(<b>a</b>) The viability of normal human bone marrow stromal cells (BMSCs) and human cancer cells (osteosarcoma cell line SaOS-2) after 7 days of culture on titanium (Ti) substrates coated with 1 or 2 μm layers of Mg, 2 μm layer of Zn, or 2 or 4 μm layers of Zn/Mg or left uncoated. Cell viability was normalized to the material surface area (cm<sup>2</sup>) and displayed as % cell viability relative to the respective cell viability on control Ti samples (100%). Means ± SD are plotted. Two-way ANOVA tests, * <span class="html-italic">p</span> &lt; 0.05, *** <span class="html-italic">p</span> &lt; 0.0001. (<b>b</b>) Scanning electron micrographs of BMSCs and SaOS-2 on coated Ti samples after 7-day culture.</p>
Full article ">
12 pages, 1697 KiB  
Article
Electronic Properties and Mechanical Stability of Multi-Ion-Co-Intercalated Bilayered V2O5
by Chunhui Ma and Bo Zhou
Materials 2024, 17(13), 3364; https://doi.org/10.3390/ma17133364 - 8 Jul 2024
Viewed by 1011
Abstract
Incorporating metal cations into V2O5 has been proven to be an effective method for solving the poor long-term cycling performance of vanadium-based oxides as electrodes for mono- or multivalent aqueous rechargeable batteries. This is due to the existence of a [...] Read more.
Incorporating metal cations into V2O5 has been proven to be an effective method for solving the poor long-term cycling performance of vanadium-based oxides as electrodes for mono- or multivalent aqueous rechargeable batteries. This is due to the existence of a bilayer structure with a large interlayer space in the V2O5 electrode and to the fact that the intercalated ions act as pillars to support the layered structure and facilitate the diffusion of charged carriers. However, a fundamental understanding of the mechanical stability of multi-ion-co-intercalated bilayered V2O5 is still lacking. In this paper, a variety of pillared vanadium pentoxides with two types of co-intercalated ions were studied. The root-mean-square deviation of the V-O bonds and the elastic constants calculated by density functional theory were used as references to evaluate the stability of the intercalated compounds. The d-band center and electronic band structures are also discussed. Our theoretical results show that the structural characteristics and stability of the system are quite strongly influenced by the intercalating strategy. Full article
Show Figures

Figure 1

Figure 1
<p>The structure of AB-V<sub>8</sub>O<sub>20</sub>. The orange sphere represents the intercalated atom A, the blue sphere represents the intercalated atom B, and gray and red spheres represent vanadium and oxygen atoms, respectively.</p>
Full article ">Figure 2
<p>Structural changes under different intercalation combinations. (<b>a</b>–<b>f</b>) Structural changes in Li-, Na-, Mg-, Al-, K-, and Ca-dominated combinations. The bar chart shows the change in bond length, and the broken line chart shows the change in layer spacing.</p>
Full article ">Figure 3
<p>Formation energy and d-band center of different intercalation combinations.</p>
Full article ">
14 pages, 10383 KiB  
Article
Development of Carbon Black Coating on TPU Elastic Powder for Selective Laser Sintering
by Yu-Deh Chao, Shu-Cheng Liu, Dong-Quan Yeh, Ajeet Kumar, Jung-Ting Tsai, Mayur Jiyalal Prajapati and Jeng-Ywan Jeng
Materials 2024, 17(13), 3363; https://doi.org/10.3390/ma17133363 - 8 Jul 2024
Viewed by 1275
Abstract
Increased usage of selective laser sintering (SLS) for the production of end-use functional components has generated a requirement of developing new materials and process improvements to improve the applicability of this technique. This article discusses a novel process wherein carbon black was applied [...] Read more.
Increased usage of selective laser sintering (SLS) for the production of end-use functional components has generated a requirement of developing new materials and process improvements to improve the applicability of this technique. This article discusses a novel process wherein carbon black was applied to the surface of TPU powder to reduce the laser reflectivity during the SLS process. The printing was carried out with a preheating temperature of 75 °C, laser energy density of 0.028 J/mm2, incorporating a 0.4 wt % addition of carbon black to the TPU powder, and controlling the powder layer thickness at 125 μm. The mixed powder, after printing, shows a reflectivity of 13.81%, accompanied by the highest average density of 1.09 g/cm3, hardness of 78 A, tensile strength of 7.9 MPa, and elongation at break was 364.9%. Compared to commercial TPU powder, which lacks the carbon black coating, the reflectance decreased by 1.78%, mechanical properties improved by 33.9%, and there was a notable reduction in the porosity of the sintered product. Full article
Show Figures

Figure 1

Figure 1
<p>(<b>a</b>) TPU powder (<b>b</b>) Carbon black.</p>
Full article ">Figure 2
<p>The mixing process of TPU powder and carbon black. (<b>a</b>)The mixing chamber (<b>b</b>) Adding carbon black in TPU (<b>c</b>) Mixed TPU powder with carbon black (<b>d</b>) The sieved mixed powder.</p>
Full article ">Figure 3
<p>(<b>a</b>) Powder reflectivity vs. carbon ratio. (<b>b</b>) Powder size distribution.</p>
Full article ">Figure 4
<p>TPU powder for (<b>a</b>) TGA and (<b>b</b>) DSC results.</p>
Full article ">Figure 5
<p>The printed specimens’ diagram. (<b>a</b>) Printed specimens’ morphology labeled from A to L. (<b>b</b>) Printed specimens of I, L, K side view.</p>
Full article ">Figure 6
<p>Interlayer adhesion at different layer thicknesses (<b>a</b>) 100 μm (<b>b</b>) 125 μm (<b>c</b>) 150 μm.</p>
Full article ">Figure 7
<p>Preheat temperature 35 °C and laser energy (J/mm<sup>2</sup>) used (<b>a</b>) 0.011, (<b>b</b>) 0.028, (<b>c</b>) 0.044 surface; (<b>d</b>) 0.011, (<b>e</b>) 0.028, (<b>f</b>) 0.044 cross-section.</p>
Full article ">Figure 8
<p>Preheat temperature 55 °C and laser energy (J/mm<sup>2</sup>) used (<b>a</b>) 0.011, (<b>b</b>) 0.028, (<b>c</b>) 0.044 surface; (<b>d</b>) 0.011, (<b>e</b>) 0.028, (<b>f</b>) 0.044 cross-section.</p>
Full article ">Figure 9
<p>Preheat temperature 75 °C and laser energy (J/mm<sup>2</sup>) used (<b>a</b>) 0.011 (<b>b</b>) 0.028 surface; (<b>d</b>) 0.011 (<b>e</b>) 0.028 cross-section and 95 °C laser energy used (<b>c</b>) 0.011 (<b>f</b>) 0.011 surface and cross-section.</p>
Full article ">Figure 10
<p>Powder morphology of (<b>a</b>–<b>c</b>) virgin TPU, (<b>d</b>–<b>f</b>) TPU powder mixed with carbon black at room temperature, and (<b>g</b>–<b>i</b>) TPU powder mixed with carbon black at 70 °C temperature.</p>
Full article ">Figure 11
<p>Micro CT-scan of porosity distribution of (<b>a</b>) TPU04C and (<b>b</b>) Sinterit TPU.</p>
Full article ">Figure 12
<p>3D printed lattice structure.</p>
Full article ">
17 pages, 5110 KiB  
Review
Research and Progress on Organic Semiconductor Power Devices
by Fangyi Li, Jiayi Zhou, Jun Zhang and Jiang Zhao
Materials 2024, 17(13), 3362; https://doi.org/10.3390/ma17133362 - 8 Jul 2024
Cited by 2 | Viewed by 4112
Abstract
Organic semiconductor power devices have been attracting increasing attention due to their advantages such as flexibility, low fabrication cost, and sustainability. They have found wide applications in fields such as flexible electronic devices and biomedical devices. However, in the field of power applications, [...] Read more.
Organic semiconductor power devices have been attracting increasing attention due to their advantages such as flexibility, low fabrication cost, and sustainability. They have found wide applications in fields such as flexible electronic devices and biomedical devices. However, in the field of power applications, the lack of reliable organic semiconductor power devices is mainly attributed to the limited thermal stability and electrical stability of organic materials. This article provides a detailed review of the development status of organic semiconductor power devices from three aspects: device structure, organic materials, and fabrication methods. It clarifies that the future development goal is to enhance the voltage resistance and thermal stability of organic transistors through higher-performance structure design, higher-mobility materials, and higher-quality fabrication methods. The continuous innovation and development of the structures, materials, and fabrication of these devices will generate more novel devices, offering more possibilities for the application of organic semiconductor power devices. This information is of great reference value and guidance significance for engineers in related fields. Full article
(This article belongs to the Special Issue Optoelectronic Semiconductor Materials and Devices)
Show Figures

Figure 1

Figure 1
<p>Cross-sectional view of top-gate top-contact organic field-effect transistor.</p>
Full article ">Figure 2
<p>Cross-sectional view of top-gate bottom-contact organic field-effect transistor. (<b>a</b>) Traditional OFET, (<b>b</b>) LDR-OFET.</p>
Full article ">Figure 3
<p>Cross-sectional view of bottom-gate top-contact organic field-effect transistor.</p>
Full article ">Figure 4
<p>Cross-sectional view of top-gate bottom-contact organic field-effect transistor [<a href="#B13-materials-17-03362" class="html-bibr">13</a>]. (<b>a</b>) OTFT (<b>b</b>) HVOTFT with drain offset.</p>
Full article ">Figure 5
<p>Molecular structure diagrams. (<b>a</b>) Pentacene (<b>b</b>) DPP-DPP molecule (<b>c</b>) DPPT-TT molecule (<b>d</b>) NMe4I molecule.</p>
Full article ">Figure 6
<p>Schematic diagram of NDI molecule and its nitrogen substituent groups. (<b>a</b>) Molecular structure diagram of NDI molecule (<b>b</b>) Substitution of nitrogen substituent groups on NDI.</p>
Full article ">Figure 7
<p>AFM images of P3HT films drop-cast on S<sub>i</sub>O<sub>2</sub> substrate from different solvents [<a href="#B70-materials-17-03362" class="html-bibr">70</a>]. (<b>a</b>) CH<sub>2</sub>Cl<sub>2</sub>, (<b>b</b>) toluene, (<b>c</b>) CHCl<sub>3</sub>, (<b>d</b>) THF. The insets represent AFM topography images with a larger scale.</p>
Full article ">Figure 8
<p>Schematic diagram of spin-coating process. (<b>a</b>) Dropping a solution containing dissolved organic semiconductor onto a substrate; (<b>b</b>) off-center spin coating process.</p>
Full article ">Figure 9
<p>Flexible sample picture [<a href="#B56-materials-17-03362" class="html-bibr">56</a>]. (<b>a</b>) Photograph of the prepared flexible sample. (<b>b</b>) Polarized optical micrograph of the sample.</p>
Full article ">Figure 10
<p>(<b>a</b>) AFM image of few-layer graphene on OTMS [<a href="#B76-materials-17-03362" class="html-bibr">76</a>]; the scale bar is 5 μm. (<b>b</b>) Schematic illustration of the lithography-free process in GFET fabrication [<a href="#B76-materials-17-03362" class="html-bibr">76</a>].</p>
Full article ">
14 pages, 12957 KiB  
Article
Dynamic Response of Ti-6Al-2Zr-1Mo-1V Alloy Manufactured by Laser Powder-Bed Fusion
by Hanzhao Qin, Alafate Maierdan, Nan Li, Changshun Wang and Chenglin Li
Materials 2024, 17(13), 3361; https://doi.org/10.3390/ma17133361 - 8 Jul 2024
Viewed by 1032
Abstract
Titanium parts fabricated by additive manufacturing, i.e., laser or electron beam-powder bed fusion (L- or EB-PBF), usually exhibit columnar grain structures along the build direction, resulting in both microstructural and mechanical anisotropy. Post-heat treatments are usually used to reduce or eliminate such anisotropy. [...] Read more.
Titanium parts fabricated by additive manufacturing, i.e., laser or electron beam-powder bed fusion (L- or EB-PBF), usually exhibit columnar grain structures along the build direction, resulting in both microstructural and mechanical anisotropy. Post-heat treatments are usually used to reduce or eliminate such anisotropy. In this work, Ti-6Al-2Zr-1Mo-1V (TA15) alloy samples were fabricated by L-PBF to investigate the effect of post-heat treatment and load direction on the dynamic response of the samples. Post-heat treatments included single-step annealing at 800 °C (HT) and a hot isotropic press (HIP). The as-built and heat-treated samples were dynamically compressed using a split Hopkinson pressure bar at a strain rate of 3000 s−1 along the horizontal and vertical directions paralleled to the load direction. The microstructural observation revealed that the as-built TA15 sample exhibited columnar grains with fine martensite inside. The HT sample exhibited a fine lamellar structure, whereas the HIP sample exhibited a coarse lamellar structure. The dynamic compression results showed that post-heat treatment at 800 °C led to reduced flow stress but enhanced uniform plastic strain and damage absorption work. However, the HIP samples exhibited both higher stress, uniform plastic strain, and damage absorption work owing to the microstructure coarsening. Additionally, the load direction had a subtle influence on the flow stress, indicating the negligible anisotropy of flow stress in the samples. However, there was more significant anisotropy of the uniform plastic strain and damage absorption. The samples had a higher load-bearing capacity when dynamically compressed perpendicular to the build direction. Full article
(This article belongs to the Special Issue Microstructure Engineering of Metals and Alloys, 3rd Edition)
Show Figures

Figure 1

Figure 1
<p>Schematic diagram of the sample fabrication and preparation. (<b>a</b>,<b>b</b>) Schematic illustration of the spilt Hopkinson pressure bar (SHPB) system.</p>
Full article ">Figure 2
<p>BSE images of the TA15 samples: (<b>a</b>,<b>b</b>) as-built, (<b>c</b>) HT800, and (<b>d</b>) HIP.</p>
Full article ">Figure 3
<p>EBSD IPF maps, misorientation maps, and pole figures of the TA15 samples: (<b>a</b>,<b>d</b>,<b>g</b>) as-built, (<b>b</b>,<b>e</b>,<b>h</b>) HT800, and (<b>c</b>,<b>f</b>,<b>i</b>) HIP.</p>
Full article ">Figure 4
<p>Dynamic compression properties: true stress–strain curves of the H (<b>a</b>) and V (<b>b</b>) samples, compression properties (<b>c</b>), and their anisotropy index (<b>d</b>).</p>
Full article ">Figure 5
<p>Cross-sectional optical micrograph after dynamic compression: (<b>a</b>) as-built-H, (<b>b</b>) as-built -V, (<b>c</b>) HT800-H, (<b>d</b>) HT800-V, (<b>e</b>) HIP-H, and (<b>f</b>) HIP-V. BD and CD pertain to the build and compress direction.</p>
Full article ">Figure 6
<p>BSE images showing the microstructures of the samples after dynamic compression: (<b>a</b>) HT800-H, (<b>b</b>) HT800-V, (<b>c</b>) HIP-H, and (<b>d</b>) HIP-V. BD and CD pertain to the build and compress direction. Red dotted lines indicates the boundries of the ASBs.</p>
Full article ">Figure 7
<p>Cross-sectional optical micrographs after being dynamically compressed at 20%: (<b>a</b>) as-built-H, (<b>b</b>) as-built -V, (<b>c</b>) HT800-H, (<b>d</b>) HT800-V, (<b>e</b>) HIP-H, and (<b>f</b>) HIP-V. BD and CD pertain to the build and compress direction.</p>
Full article ">Figure 8
<p>Optical micrographs showing the microstructures of the samples after being dynamically compressed at 20%: (<b>a</b>) HT800-H, (<b>b</b>) HT800-V, (<b>c</b>) HIP-H, and (<b>d</b>) HIP-V. BD and CD pertain to the build and compress direction.</p>
Full article ">Figure 9
<p>BSE images showing the microstructures of the samples after being dynamically compressed at 20%: (<b>a</b>) HT800-H, (<b>b</b>) HT800-V, (<b>c</b>) HIP-H, and (<b>d</b>) HIP-V. BD and CD pertain to the build and compress direction. Red dotted lines indicates the boundries of the ASBs.</p>
Full article ">
10 pages, 2451 KiB  
Article
Investigation of Grain Boundary Effects in Sm0.2Ce0.8O2−x Thin Film Memristors
by Weikai Shi, Luyao Wang and Nan Yang
Materials 2024, 17(13), 3360; https://doi.org/10.3390/ma17133360 - 8 Jul 2024
Viewed by 1107
Abstract
Cerium-based materials (CeO2−x) are of significant interest in the development of vacancy-modulated resistive switching (RS) memory devices. However, the influence of grain boundaries on the performance of memristors is very limited. To fill this gap, this study explores the influence of [...] Read more.
Cerium-based materials (CeO2−x) are of significant interest in the development of vacancy-modulated resistive switching (RS) memory devices. However, the influence of grain boundaries on the performance of memristors is very limited. To fill this gap, this study explores the influence of grain boundaries in cerium-based thin film resistive random-access memory (RRAM) devices. Sm0.2Ce0.8O2−x (SDC20) thin films were deposited on (100)-oriented Nb-doped SrTiO3 (NSTO) and (110)-oriented NSTO substrates using pulsed laser deposition (PLD). Devices constructed with a Pt/SDC20/NSTO structure exhibited reversible and stable bipolar resistive switching (RS) behavior. The differences in conduction mechanisms between single-crystal and polycrystalline devices were confirmed, with single-crystal devices displaying a larger resistance window and higher stability. Combining the results of XPS and I–V curve fitting, it was confirmed that defects near the grain boundaries in the SDC-based memristors capture electrons, thereby affecting the overall performance of the RRAM devices. Full article
Show Figures

Figure 1

Figure 1
<p>X-ray Diffraction (XRD) Spectrum and Atomic Force Microscopy (AFM) Images of Single-Crystal and Polycrystalline Devices: (<b>a</b>,<b>d</b>) high-resolution XRD spectrum of the SDC20 thin film. (<b>b</b>,<b>e</b>) Swinging curve at the (200) peak position of the SDC20 thin film. (<b>c</b>,<b>f</b>) Two-dimensional AFM image of the SDC20 thin film.</p>
Full article ">Figure 2
<p>Electrical performance characterization of single-crystal (<b>a</b>–<b>f</b>) and polycrystalline (<b>g</b>–<b>i</b>) devices: (<b>a</b>) Schematic diagram of the device structure. (<b>b</b>) Typical I–V characteristic curves over 50 repeated switching cycles. (<b>c</b>) Multi-step set process of the device under a +5 V scanning voltage. (<b>d</b>) Synaptic testing of the device. (<b>e</b>) Endurance test over 500 consecutive reset-set cycles, read at 0.5 V. (<b>f</b>) Retention tests for HRS and LRS after reset and set operations, respectively, read at 0.5 V. (<b>g</b>) Typical I–V characteristic curves over 50 repeated switching cycles. (<b>h</b>) Endurance test over 100 consecutive reset-set cycles, read at 1.1 V. (<b>i</b>) Synaptic testing of the device.</p>
Full article ">Figure 3
<p>Fitting of I–V curves of the device in the positive voltage range with two different conduction models: (<b>a</b>) single-crystal devices: space-charge limited conduction and (<b>b</b>) polycrystalline devices: Poole−Frenkel emission.</p>
Full article ">Figure 4
<p>(<b>a</b>) The Ce 3<span class="html-italic">d</span> XPS spectra of polycrystalline SDC thin films at various etching depths. (<b>b</b>) Elemental analysis of polycrystalline SDC thin films at different etching depths. (<b>c</b>) TEM images of polycrystalline SDC thin films. (<b>d</b>) Schematic illustration of oxygen vacancy distribution within the bulk of SDC20 thin film. (<b>e</b>) Conduction mechanism analysis of the polycrystalline device.</p>
Full article ">
11 pages, 8775 KiB  
Article
Modification of Microstructure and Mechanical Properties of Extruded AZ91-0.4Ce Magnesium Alloy through Addition of Ca
by Fengtao Ni, Jian Peng, Xiangquan Liu, Pan Gao, Zhongkui Nie, Jie Hu and Dong Zhao
Materials 2024, 17(13), 3359; https://doi.org/10.3390/ma17133359 - 8 Jul 2024
Cited by 2 | Viewed by 958
Abstract
The effect of the addition of alkali earth element Ca on the microstructure and mechanical properties of extruded AZ91-0.4Ce-xCa (x = 0, 0.4, 0.8, 1.2 wt.%) alloys was studied by using scanning electron microscopy, transmission electron microscopy, and tensile tests. The results showed [...] Read more.
The effect of the addition of alkali earth element Ca on the microstructure and mechanical properties of extruded AZ91-0.4Ce-xCa (x = 0, 0.4, 0.8, 1.2 wt.%) alloys was studied by using scanning electron microscopy, transmission electron microscopy, and tensile tests. The results showed that the addition of Ca could significantly refine the second phase and grain size of the extruded AZ91-0.4Ce alloy. The refinement effect was most obvious when 0.8 wt.% of Ca was added, and the recrystallized grain size was 4.75 μm after extrusion. The addition of Ca resulted in the formation of a spherical Al2Ca phase, which effectively suppressed the precipitation of the β-Mg17Al12 phase, promoted dynamic recrystallization and grain refinement, impeded dislocation motion, and exerted a positive influence on the mechanical properties of the alloy. The yield strength (YS), ultimate tensile strength (UTS), and elongation (EL) of the AZ91-0.4Ce-0.8Ca alloy were 238.7 MPa, 338.3 MPa, and 10.8%, respectively. Full article
(This article belongs to the Special Issue Welding, Joining, and Additive Manufacturing of Metals and Alloys)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Microstructure scanning and energy spectrum analysis of as-cast AZ91-0.4Ce-xCa (x = 0, 0.4, 0.8, 1.2 wt.%) alloys. (<b>a</b>) AZ91-0.4Ce alloy, (<b>b</b>) AZ91-0.4Ce-0.4Ca alloy, (<b>c</b>) AZ91-0.4Ce-0.8Ca alloy, and (<b>d</b>) AZ91-0.4Ce-1.2Ca alloy. (<b>a1</b>–<b>d1</b>) correspond to selected parts in box (<b>a</b>–<b>d</b>), respectively.</p>
Full article ">Figure 2
<p>XRD pattern of extruded AZ91-0.4Ce-xCa (x = 0, 0.4, 0.8, 1.2 wt.%) alloys.</p>
Full article ">Figure 3
<p>Microstructure scanning and energy spectrum analysis of extruded AZ91-0.4Ce-xCa (x = 0, 0.4, 0.8, 1.2 wt.%) alloys. (<b>a</b>) AZ91-0.4Ce alloy, (<b>b</b>) AZ91-0.4Ce-0.4Ca alloy, (<b>c</b>) AZ91-0.4Ce-0.8Ca alloy, and (<b>d</b>) AZ91-0.4Ce-1.2Ca alloy.</p>
Full article ">Figure 4
<p>Extruded AZ91-0.4Ce-xCa (x = 0, 0.4, 0.8, 1.2 wt.%) alloys’ pole figure and inverse pole figure. (<b>a</b>) AZ91-0.4Ce alloy, (<b>b</b>) AZ91-0.4Ce-0.4Ca alloy, (<b>c</b>) AZ91-0.4Ce-0.8Ca alloy, and (<b>d</b>) AZ91-0.4Ce-1.2Ca alloy.</p>
Full article ">Figure 5
<p>Mechanical properties of extruded AZ91-0.4Ce-xCa (x = 0, 0.4, 0.8, 1.2 wt.%) alloys at room temperature: (<b>a</b>) stress–strain curve; (<b>b</b>) variation trend of UTS, YS, and EL.</p>
Full article ">Figure 6
<p>Effect of second-phase distribution and size on grain growth. (<b>a</b>) Coarse second phase; (<b>b</b>) fine dispersion of second phase (red arrows represent direction of grain boundary movement).</p>
Full article ">Figure 7
<p>(<b>a</b>–<b>c</b>) Bright-field transmission electron microscope (TEM) micrographs of the as-extruded AZ91-0.4Ce-0.8Ca alloy; (<b>e</b>,<b>f</b>) the corresponding diffraction patterns of the selected particles taken from (<b>a</b>,<b>b</b>), indicated by the arrows A, B, respectively; (<b>d</b>) a high-resolution TEM (HRTEM) image of the zone C in (<b>c</b>); (<b>g</b>) an inverse fast Fourier transform (IFFT) image of the zone D in (<b>d</b>) (remark: the “T”-shaped symbols represent the dislocations).</p>
Full article ">Figure 8
<p>The Statistical of the recrystallization grains and the Schmid factor of extruded AZ91-0.4Ce-xCa (x = 0, 0.4, 0.8, 1.2 wt.%) alloys. (<b>a</b>) AZ91-0.4Ce alloy, (<b>b</b>) AZ91-0.4Ce-0.4Ca alloy, (<b>c</b>) AZ91-0.4Ce-0.8Ca alloy, and (<b>d</b>) AZ91-0.4Ce-1.2Ca alloy.</p>
Full article ">
27 pages, 10839 KiB  
Article
Feasibility and Application of Local Closed-Loop Materials to Produce Compressed and Stabilized Earth Blocks
by Catalina Reyna-Ruiz, José Manuel Gómez-Soberón and María Neftalí Rojas-Valencia
Materials 2024, 17(13), 3358; https://doi.org/10.3390/ma17133358 - 7 Jul 2024
Viewed by 1717
Abstract
The validation of a feasible application for the production of sustainable bricks with local materials in humid and hot climates, which would allow the current housing needs of a constantly growing population with scarce economic resources to be met while also reducing energy [...] Read more.
The validation of a feasible application for the production of sustainable bricks with local materials in humid and hot climates, which would allow the current housing needs of a constantly growing population with scarce economic resources to be met while also reducing energy inputs for climate control, is a current challenge without a definitive solution. Therefore, this research studied the incorporation of local aggregates and two second-generation materials to produce lime-stabilized Compressed Earth Blocks (CSEBs) using a semi-automatic machine for their manufacture. An initial matrix was designed as a baseline, and three more were developed with variations to incorporate second-generation materials individually and as mixtures. The stabilizer was added in concentrations of 5, 10, and 15%, resulting in a total of 12 batches of CSEBs. Eleven of the studied batches exceed the normative limits for simple compressive strength and initial water absorption coefficient. The best result of simple compressive strength was obtained in two batches of the same matrix that used construction demolition waste (CDW), reaching 4.3 MPa (43% above the minimum limit established by the most restrictive regulations and 115% above the least restrictive). It was possible to produce sustainable bricks in situ with average ambient temperatures of 32 °C and relative humidity of 91%. Full article
(This article belongs to the Section Construction and Building Materials)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Aggregates and stabilizers.</p>
Full article ">Figure 2
<p>Particle size distribution of aggregates and ideal reference soil and their finesse module.</p>
Full article ">Figure 3
<p>Proctor test for soils.</p>
Full article ">Figure 4
<p>Liquid limit (LL) test results of the studied soils.</p>
Full article ">Figure 5
<p>Mixing machine, exterior and interior view with the blades.</p>
Full article ">Figure 6
<p>Adopress 3000—CEB Making Machine and its parts.</p>
Full article ">Figure 7
<p>Temperature and relative humidity during the curing phase of the specimens.</p>
Full article ">Figure 8
<p>CSEB, one specimen per batch of the four matrices at T<sub>2</sub>, for size reference, the ruler has a total length of 30 cm.</p>
Full article ">Figure 9
<p>Construction diagram of the structural frame with its list of materials.</p>
Full article ">Figure 10
<p>Field test apparatus to determine simple compressive strength in CSEB.</p>
Full article ">Figure 11
<p>Schematic representation of the Int Abs Coeff<sub>(10)</sub> test arrangement. Original drawing inspired by the three cited norms [<a href="#B74-materials-17-03358" class="html-bibr">74</a>,<a href="#B75-materials-17-03358" class="html-bibr">75</a>,<a href="#B76-materials-17-03358" class="html-bibr">76</a>].</p>
Full article ">Figure 12
<p>Linear tolerances, original drawing inspired by SI: 1077:1997 [<a href="#B80-materials-17-03358" class="html-bibr">80</a>].</p>
Full article ">Figure 13
<p>Height of the blocks determined by the bulk weight and the heights at T<sub>1</sub> and T<sub>2</sub>.</p>
Full article ">Figure 14
<p>Average weights at T<sub>1</sub> and T<sub>2</sub> and the percentage variation.</p>
Full article ">Figure 15
<p>Average volume at T<sub>1</sub> and T<sub>2</sub> and the percentage variation.</p>
Full article ">Figure 16
<p>Average density at T<sub>1</sub> and T<sub>2</sub> and the percentage variation.</p>
Full article ">Figure 17
<p>Results of simple compressive strength by matrix at different lime concentrations.</p>
Full article ">Figure 18
<p>Int Abs Coeff<sub>(10)</sub> results per matrix at different lime concentrations.</p>
Full article ">Figure 19
<p>Ranking results of simple compression strength and Int Abs Coeff<sub>(10)</sub>.</p>
Full article ">
16 pages, 4524 KiB  
Article
The Effect of Rapeseed Oil Biopolyols and Cellulose Biofillers on Selected Properties of Viscoelastic Polyurethane Foams
by Tomasz Prociak, Dariusz Bogdal, Maria Kuranska, Olga Dlugosz and Mark Kubik
Materials 2024, 17(13), 3357; https://doi.org/10.3390/ma17133357 - 7 Jul 2024
Cited by 1 | Viewed by 867
Abstract
This paper presents the results of research on polyurethane viscoelastic foams (PUVFs) modified with biomaterials. This investigation looked at the effect of the biomaterials on the foaming processes, as well as the acoustical and selected physical-mechanical properties of the foams. Various types of [...] Read more.
This paper presents the results of research on polyurethane viscoelastic foams (PUVFs) modified with biomaterials. This investigation looked at the effect of the biomaterials on the foaming processes, as well as the acoustical and selected physical-mechanical properties of the foams. Various types of rapeseed oil biopolyols and microcellulose were used to modify the materials. The analysis of properties covered a reference biopolyol-free sample and materials containing 10 wt.%, 20 wt.%, and 30 wt.% of different types of biopolyols in the mixture of polyol components. The biopolyols differed in terms of functionality and hydroxyl value (OHv). Next, a selected formulation was modified with various microcellulose biofillers in the amount of 0.5–2 wt.%. The PUVFs, with apparent densities of more than 210 kg/m3 and open-cell structures (more than 85% of open cells), showed a slow recovery to their original shape after deformation when the pressure force was removed. They were also characterized by a tensile strength in the range of 156–264 kPa, elongation at break of 310–510%, hardness of 8.1–23.1 kPa, and a high comfort factor of 3.1–7.1. The introduction of biopolyols into the polyurethane system resulted in changes in sound intensity levels of up to 31.45%, while the addition of fillers resulted in changes in sound intensity levels of up to 13.81%. Full article
(This article belongs to the Section Polymeric Materials)
Show Figures

Figure 1

Figure 1
<p>An overview image of PUVFs with a thickness of 20 mm.</p>
Full article ">Figure 2
<p>Schematic diagram showing how the sound properties of PUVFs were studied (1—computer with audio software Audacity 3.1.3, 2—interface, sound-level preamplifier Focusrite Scarlett 4i4 3rd generation, 3—microphone (output device, Precision Reference Microphone, PreSonus, Frequency Response from 20 Hz to 20 kHz), 4—soundproofed measurement tunnel (Kundt’s tube), 5—acoustic barrier with sample location, 6—loudspeaker Sony SRS-XB12.</p>
Full article ">Figure 3
<p>Characteristic times for foaming processes of foam series 1 (<b>a</b>) and series 2 (<b>b</b>).</p>
Full article ">Figure 4
<p>Recovery time of PUR materials from series 1 (<b>a</b>) and series 2 (<b>b</b>).</p>
Full article ">Figure 4 Cont.
<p>Recovery time of PUR materials from series 1 (<b>a</b>) and series 2 (<b>b</b>).</p>
Full article ">Figure 5
<p>Closed cell contents in PUR materials from series 1 (<b>a</b>) and series 2 (<b>b</b>).</p>
Full article ">Figure 5 Cont.
<p>Closed cell contents in PUR materials from series 1 (<b>a</b>) and series 2 (<b>b</b>).</p>
Full article ">Figure 6
<p>SEM images of PUVFs (REF, modified with biopolyols and both biopolyol and biofillers).</p>
Full article ">Figure 7
<p>Change in sound intensity level of PUVFs for the frequencies 63 Hz, 125 Hz, 250 Hz, 500 Hz, 1000 Hz, 2000 Hz, 4000 Hz, 8000 Hz: series 1 (<b>a</b>), Detail series 1 (<b>b</b>), series 2 (<b>c</b>), Detail series 2 (<b>d</b>).</p>
Full article ">Figure 7 Cont.
<p>Change in sound intensity level of PUVFs for the frequencies 63 Hz, 125 Hz, 250 Hz, 500 Hz, 1000 Hz, 2000 Hz, 4000 Hz, 8000 Hz: series 1 (<b>a</b>), Detail series 1 (<b>b</b>), series 2 (<b>c</b>), Detail series 2 (<b>d</b>).</p>
Full article ">Figure 8
<p>FTIR spectra of REF and biopolyol-modified PUVFs (BP1).</p>
Full article ">Figure 9
<p>Elongation at break and tensile strength of reference material and materials modified with biopolyols (<b>a</b>,<b>b</b>) and biofillers (<b>c</b>,<b>d</b>).</p>
Full article ">Figure 10
<p>Hardness and comfort factor of reference material and materials modified with biopolyols (<b>a</b>,<b>b</b>) and biofillers (<b>c</b>,<b>d</b>).</p>
Full article ">
8 pages, 2729 KiB  
Communication
A Zn-Ca-Based Metallic Glass Composite Material for Rapid Degradation of Azo Dyes
by Gaojiong Wang, Xin Wang, Wei Yang, Lichen Zhao and Yumin Qi
Materials 2024, 17(13), 3356; https://doi.org/10.3390/ma17133356 - 7 Jul 2024
Viewed by 978
Abstract
The catalytic capabilities of metals in degrading azo dyes have garnered extensive interest; however, selecting highly efficient metals remains a significant challenge. We have developed a Zn-Ca-based metallic glass composite which shows outstanding degradation efficiency for Direct Blue 6. This alloy comprises a [...] Read more.
The catalytic capabilities of metals in degrading azo dyes have garnered extensive interest; however, selecting highly efficient metals remains a significant challenge. We have developed a Zn-Ca-based metallic glass composite which shows outstanding degradation efficiency for Direct Blue 6. This alloy comprises a Zn2Ca crystalline phase and an amorphous matrix, allowing for the degradation of azo dyes within minutes in a wide temperature range of 0–60 °C. Kinetic calculations reveal an exceptionally low activation energy of 8.99 kJ/mol. The rapid degradation is attributed to the active element Ca and the unique amorphous structure of the matrix, which not only facilitates abundant redox conditions but also minimizes the hydrolysis of the active element. The newly developed metallic glass composite exhibits a notably higher azo dye degradation rate compared to those of general metallic glasses, offering a new avenue for the rapid degradation of azo dyes. This paper holds significant importance for the development of novel azo dye wastewater treatment agents. Full article
(This article belongs to the Special Issue Physical Metallurgy of Metals and Alloys II)
Show Figures

Figure 1

Figure 1
<p>(<b>a</b>) Metallographic microscope photo of powder sample; (<b>b</b>) particle size statistic histogram; (<b>c</b>) XRD pattern; (<b>d</b>) DSC curve.</p>
Full article ">Figure 2
<p>(<b>a</b>) Optical photos of residual solutions degraded for different times at different temperatures; (<b>b</b>–<b>e</b>) absorption spectra of residual solutions degraded for different times at 0, 20, 40, and 60 °C, respectively; (<b>f</b>) relative absorbance vs. degradation time curves at different temperatures; (<b>g</b>) azo dye removal rate; (<b>h</b>) degradation reaction kinetics curves at different temperatures, fitted according to second-order reaction kinetics equations; (<b>i</b>) Arrhenius equation fitting diagram.</p>
Full article ">Figure 3
<p>SEM images of the Zn<sub>45</sub>Mg<sub>11</sub>Ca<sub>40</sub>Sr<sub>4</sub> alloy powder after degrading DB6 for 60 min at different magnifications: (<b>a</b>) 500×; (<b>b</b>) 2000×; (<b>c</b>) 10,000×; (<b>d</b>) 20,000×.</p>
Full article ">Figure 4
<p>XPS spectra of the Zn<sub>45</sub>Mg<sub>11</sub>Ca<sub>40</sub>Sr<sub>4</sub> alloy powder before and after azo dye degradation test: (<b>a</b>) Ca 2p; (<b>b</b>) Mg 1s; (<b>c</b>) Zn 2p; (<b>d</b>) O 1s.</p>
Full article ">
12 pages, 2490 KiB  
Article
Impact of Scattering Foil Composition on Electron Energy Distribution in a Clinical Linear Accelerator Modified for FLASH Radiotherapy: A Monte Carlo Study
by James C. L. Chow and Harry E. Ruda
Materials 2024, 17(13), 3355; https://doi.org/10.3390/ma17133355 - 7 Jul 2024
Viewed by 1197
Abstract
This study investigates how scattering foil materials and sampling holder placement affect electron energy distribution in electron beams from a modified medical linear accelerator for FLASH radiotherapy. We analyze electron energy spectra at various positions—ionization chamber, mirror, and jaw—to evaluate the impact of [...] Read more.
This study investigates how scattering foil materials and sampling holder placement affect electron energy distribution in electron beams from a modified medical linear accelerator for FLASH radiotherapy. We analyze electron energy spectra at various positions—ionization chamber, mirror, and jaw—to evaluate the impact of Cu, Pb-Cu, Pb, and Ta foils. Our findings show that close proximity to the source intensifies the dependence of electron energy distribution on foil material, enabling precise beam control through material selection. Monte Carlo simulations are effective for designing foils to achieve desired energy distributions. Moving the sampling holder farther from the source reduces foil material influence, promoting more uniform energy spreads, particularly in the 0.5–10 MeV range for 12 MeV electron beams. These insights emphasize the critical role of tailored material selection and sampling holder positioning in optimizing electron energy distribution and fluence intensity for FLASH radiotherapy research, benefiting both experimental design and clinical applications. Full article
(This article belongs to the Special Issue Artificial Intelligence in Materials Science and Engineering)
Show Figures

Figure 1

Figure 1
<p>PDD curves measured and Monte Carlo simulated with circular field (cutout) sizes equal to 2 and 10 cm diameter using the 12 MeV electron beams.</p>
Full article ">Figure 2
<p>Schematic diagram showing the scattering foil containing three layers. The scattering foil (green) is surrounded by stainless steel (aquamarine) and air (blue).</p>
Full article ">Figure 3
<p>Schematic diagram showing the Monte Carlo model of the modified linac.</p>
Full article ">Figure 4
<p>Electron energy distribution at the position of ionization (ion) chamber as shown in <a href="#materials-17-03355-f003" class="html-fig">Figure 3</a>. The correlation coefficients (4th-order polynomial fitting) for the Pb and Cu, Pb, Cu, and Ta curves are 0.647, 0.664, 0.619, and 0.729, respectively.</p>
Full article ">Figure 5
<p>Electron energy distribution at the position of mirror as shown in <a href="#materials-17-03355-f003" class="html-fig">Figure 3</a>. The correlation coefficients (4th-order polynomial fitting) for the Pb and Cu, Pb, Cu, and Ta curves are 0.576, 0.589, 0.552, and 0.652, respectively.</p>
Full article ">Figure 6
<p>Electron energy distribution at the position of jaw as shown in <a href="#materials-17-03355-f003" class="html-fig">Figure 3</a>. The correlation coefficients (4th order polynomial fitting) for the Pb and Cu, Pb, Cu, and Ta curves are 0.633, 0.646, 0.618, and 0.692, respectively.</p>
Full article ">
17 pages, 8487 KiB  
Article
Strength Optimisation of Hybrid Bolted/Bonded Composite Joints Based on Finite Element Analysis
by Raphael Blier, Leila Monajati, Masoud Mehrabian and Rachid Boukhili
Materials 2024, 17(13), 3354; https://doi.org/10.3390/ma17133354 - 6 Jul 2024
Cited by 1 | Viewed by 1168
Abstract
A finite element analysis (FEA) was conducted to examine the behaviour of single-lap quasi-isotropic (QI) and cross-ply (CP) hybrid bolted/bonded (HBB) configurations subjected to tensile shear loading. Several critical design factors influencing the composite joint strength, failure conditions, and load-sharing mechanisms that would [...] Read more.
A finite element analysis (FEA) was conducted to examine the behaviour of single-lap quasi-isotropic (QI) and cross-ply (CP) hybrid bolted/bonded (HBB) configurations subjected to tensile shear loading. Several critical design factors influencing the composite joint strength, failure conditions, and load-sharing mechanisms that would optimise the joining performance were assessed. The study of the stress concentration around the holes and along the adhesive layer highlights the fact that the HBB joints benefit from significantly lower stresses compared to only bolted joints, especially for CP configurations. The simulation results confirmed the redundancy of the middle bolt in a three-bolt HBB joint. The stiffness and plastic behaviour of the adhesive were found to be important factors that define the transition of the behaviour of the joint from a bolted type, where load sharing is predominant, to a bonded joint. The load-sharing potential, known as an indicator of the joint’s performance, is improved by reducing the overlap length, using a low-stiffness, high-plasticity adhesive, and using thicker laminates in the QI layup configuration. Enhancing both the ratio of the edge distance to the hole diameter and washer size proves advantageous in reducing stresses within the adhesive layer, thereby improving the joint strength. Full article
(This article belongs to the Special Issue Manufacturing and Mechanics of Materials, Volume II)
Show Figures

Figure 1

Figure 1
<p>Joint model.</p>
Full article ">Figure 2
<p>First-Order Solid Hexahedral Reduced Integration (C3D8R) Element.</p>
Full article ">Figure 3
<p>OB and HBB joints model boundary conditions (shown for QI layup).</p>
Full article ">Figure 4
<p>Nodes (in red) at which reaction forces are extracted (shown for QI layup).</p>
Full article ">Figure 5
<p>Maximum longitudinal stress σ<sub>x</sub> at different holes in CP layups.</p>
Full article ">Figure 6
<p>Maximum longitudinal stress σx at different holes in QI layups.</p>
Full article ">Figure 7
<p>Maximum shear stress S<sub>xy</sub> in 0° plies at hole B3 for the CP12 and QI12 joints.</p>
Full article ">Figure 8
<p>Stress distribution along the centreline of the adhesive layer for the CP12-HBB joint at 8.5 kN.</p>
Full article ">Figure 9
<p>Stress distribution in the laminate and the adhesive in CP12-HBB joints at 8 kN.</p>
Full article ">Figure 10
<p>Effect of the secondary bending on the HBB joint, in the case of the CP12-HBB Joint at 8 kN (Deformation Scale 50×).</p>
Full article ">Figure 11
<p>Peel σ<sub>z</sub> and shear stress S<sub>xz</sub> distribution along the adhesive edge in the QI12 HBB and bonded joints at 12.5 kN.</p>
Full article ">Figure 12
<p>Effect of the middle bolt in the tensile σ<sub>x</sub> and shear stress S<sub>xy</sub> distribution around the critical hole in CP12-HBB joints at 14 kN.</p>
Full article ">Figure 13
<p>Effect of the middle bolt on the peel σ<sub>z</sub> and shear stress S<sub>xz</sub> at the overlap ends along the adhesive edge in the CP12-HBB joints at 14 kN.</p>
Full article ">Figure 14
<p>Tensile stress–strain curves of adhesives 1 and 2.</p>
Full article ">Figure 15
<p>Hole overclosure for various overlap lengths and adhesives in CP12-HBB joints.</p>
Full article ">Figure 16
<p>Peel σ<sub>z</sub> and shear S<sub>xz</sub> stresses at the overlap end along the adhesive edge for various overlap lengths in CP12-HBB joints using adhesive 1 at 10 kN.</p>
Full article ">Figure 17
<p>Maximum principal plastic strain for different overlap lengths and adhesives in CP12-HBB joints.</p>
Full article ">Figure 18
<p>Hole overclosure for different joint parameters and adhesives in HBB with an OL of 114.3 mm.</p>
Full article ">Figure 19
<p>Geometric parameters.</p>
Full article ">Figure 20
<p>Peel σ<sub>z</sub> and shear S<sub>xz</sub> stresses at the overlap end along the adhesive edge in QI12-HBB joints with various e/d ratios at 12.5 kN.</p>
Full article ">Figure 21
<p>Tensile σx and shear stress Sxy distribution with various e/d ratios around the critical hole in QI12-HBB joints at 12.5 kN.</p>
Full article ">Figure 22
<p>Mesh plot for large washer configuration for QI12-HBB (e/d = 2).</p>
Full article ">Figure 23
<p>Peel σ<sub>z</sub> and shear S<sub>xz</sub> stresses at the overlap end along the adhesive edge in QI12-HBB joints with different washer sizes at 12.5 kN.</p>
Full article ">
15 pages, 6521 KiB  
Article
Preparation and Immobilization Mechanism of Red Mud/Steel Slag-Based Geopolymers for Solidifying/Stabilizing Pb-Contaminated Soil
by Xinyang Wang and Yongjie Xue
Materials 2024, 17(13), 3353; https://doi.org/10.3390/ma17133353 - 6 Jul 2024
Cited by 1 | Viewed by 1225
Abstract
Pb-contaminated soil poses serious hazards to humans and ecosystems and is in urgent need of remediation. However, the extensive use of traditional curing materials such as ordinary Portland cement (OPC) has negatively impacted global ecology and the climate, so there is a need [...] Read more.
Pb-contaminated soil poses serious hazards to humans and ecosystems and is in urgent need of remediation. However, the extensive use of traditional curing materials such as ordinary Portland cement (OPC) has negatively impacted global ecology and the climate, so there is a need to explore low-carbon and efficient green cementitious materials for the immobilization of Pb-contaminated soils. A red mud/steel slag-based (RM/SS) geopolymer was designed and the potential use of solidifying/stabilizing heavy metal Pb pollution was studied. The Box–Behnken design (BBD) model was used to design the response surface, and the optimal preparation conditions of RM/SS geopolymer (RSGP) were predicted by software of Design-Expert 8.0.6.1. The microstructure and phase composition of RSGP were studied by X-ray diffractometer, Fourier transform infrared spectrometer, scanning electron microscopy and X-ray photoelectron spectroscopy, and the immobilization mechanism of RSGP to Pb was revealed. The results showed that when the liquid–solid ratio is 0.76, the mass fraction of RM is 79.82% and the modulus of alkali activator is 1.21, the maximum unconfined compressive strength (UCS) of the solidified soil sample is 3.42 MPa and the immobilization efficiency of Pb is 71.95%. The main hydration products of RSGP are calcium aluminum silicate hydrate, calcium silicate hydrate and nekoite, which can fill the cracks in the soil, form dense structures and enhance the UCS of the solidified soil. Pb is mainly removed by lattice immobilization, that is, Pb participates in geopolymerization by replacing Na and Ca to form Si-O-Pb or Al-O-Pb. The remaining part of Pb is physically wrapped in geopolymer and forms Pb(OH)2 precipitate in a high-alkali environment. Full article
(This article belongs to the Special Issue Advances in Natural Building and Construction Materials)
Show Figures

Figure 1

Figure 1
<p>XRD of soil, RM and SS.</p>
Full article ">Figure 2
<p>GS preparation process flow chart.</p>
Full article ">Figure 3
<p>(<b>a</b>) The contours and (<b>b</b>) response surfaces of the interaction of B (the mass fraction of RM) and C (modulus of alkali activator) on UCS.</p>
Full article ">Figure 4
<p>(<b>a</b>) The contours and (<b>b</b>) response surfaces of the interaction of A (liquid–solid ratio) and C (modulus of alkali activator) on immobilization efficiency of Pb.</p>
Full article ">Figure 5
<p>(<b>a</b>) The contours and (<b>b</b>) response surfaces of the interaction of B (the mass fraction of RM) and C (modulus of alkali activator) on immobilization efficiency of Pb.</p>
Full article ">Figure 6
<p>Residual plot (<b>a</b>) UCS and (<b>b</b>) immobilization efficiency of Pb.</p>
Full article ">Figure 7
<p>Predicted vs. actual experimental data of (<b>a</b>) UCS and (<b>b</b>) immobilization efficiency of Pb.</p>
Full article ">Figure 8
<p>(<b>a</b>) XRD and (<b>b</b>) FTIR of RSGP and RSGP-Pb.</p>
Full article ">Figure 9
<p>SEM of (<b>a</b>) RSGP and (<b>b</b>) RSGP-Pb.</p>
Full article ">Figure 10
<p>XPS of (<b>a</b>) O 1s, (<b>b</b>) Si 2p, (<b>c</b>) Al 2p and (<b>d</b>) Pb 4f of RSGP and RSGP-Pb.</p>
Full article ">
20 pages, 5923 KiB  
Article
Engineered Mesoporous Silica-Based Nanoparticles: Characterization of Surface Properties
by Antonio Grisolia, Marzia De Santo, Manuela Curcio, Palmira Alessia Cavallaro, Catia Morelli, Antonella Leggio and Luigi Pasqua
Materials 2024, 17(13), 3352; https://doi.org/10.3390/ma17133352 - 6 Jul 2024
Cited by 2 | Viewed by 1492
Abstract
Mesoporous silica-based nanomaterials have emerged as multifunctional platforms with applications spanning catalysis, medicine, and nanotechnology. Since their synthesis in the early 1990s, these materials have attracted considerable interest due to their unique properties, including high surface area, tunable pore size, and customizable surface [...] Read more.
Mesoporous silica-based nanomaterials have emerged as multifunctional platforms with applications spanning catalysis, medicine, and nanotechnology. Since their synthesis in the early 1990s, these materials have attracted considerable interest due to their unique properties, including high surface area, tunable pore size, and customizable surface chemistry. This article explores the surface properties of a series of MSU-type mesoporous silica nanoparticles, elucidating the impact of different functionalization strategies on surface characteristics. Through an extensive characterization utilizing various techniques, such as FTIR, Z-potential, and nitrogen adsorption porosimetry, insights into the surface modifications of mesoporous silica nanoparticles are provided, contributing to a deeper understanding of their nanostructure and related interactions, and paving the way to possible unexpected actionability and potential applications. Full article
(This article belongs to the Special Issue Physical Synthesis, Properties and Applications of Nanoparticles)
Show Figures

Figure 1

Figure 1
<p>SEM micrograph image of MSN<sub>AS</sub>.</p>
Full article ">Figure 2
<p>TEM micrograph image of MSN<sub>AS</sub> (scale bar 100 nm).</p>
Full article ">Figure 3
<p>XRD pattern of synthesized MSU-x: MSN<sub>AS</sub>.</p>
Full article ">Figure 4
<p>FTIR pattern of synthesized MSU-x: MSN<sub>AS</sub>.</p>
Full article ">Figure 5
<p>TGA-DSC pattern of synthesized MSU-x: MSN<sub>AS</sub>.</p>
Full article ">Figure 6
<p>DSC: onset, end, peak, and enthalpy values.</p>
Full article ">Figure 7
<p>Zeta-potential pattern of synthesized MSU-x: MSN<sub>AS</sub>.</p>
Full article ">Figure 8
<p>Z-potential graphs comparison of sample (<b>a</b>) MSN-Ap vs. FOL-MSN and (<b>b</b>) FOL-MSN vs. FOL-MSN-EXT.</p>
Full article ">Figure 9
<p>Z-potential graphs comparison of sample (<b>a</b>) FOL-MSN-EXT vs. FOL-MSN-DIOL; (<b>b</b>) FOL-MSN-EXT vs. FOL-MSN-NH<sub>2</sub>; (<b>c</b>) FOL-MSN-NH<sub>2</sub> vs. FOL-MSN-COOH; (<b>d</b>) FOL-MSN-COOH vs. FOL-MSN-HYD.</p>
Full article ">Figure 10
<p>FTIR spectra overlap of MSN-AP, FOL-MSN, and FOL-MSN-EXT samples.</p>
Full article ">Figure 11
<p>FTIR spectra overlap of MSN-FOL-EXT and MSN-FOL-GLY and MSN-FOL-DIOL samples.</p>
Full article ">Figure 12
<p>FTIR spectra overlap of FOL-MSN-EXT, FOL-MSN-NH<sub>2</sub>, FOL-MSN-COOH, and FOL-MSN-HYD samples.</p>
Full article ">Figure 13
<p>Adsorption isotherm overlap of (<b>a</b>) MSN<sub>AS</sub>, MSN-AP, FOL-MSN and FOL-MSN-EXT samples; (<b>b</b>) FOL-MSN-NH<sub>2</sub>, FOL-MSN-EXT, FOL-MSN-COOH, and FOL-MSN-HYD samples; (<b>c</b>) FOL-MSN-EXT vs. FOL-MSN-DIOL samples.</p>
Full article ">Scheme 1
<p>Workflow diagram of MSN grafting protocols.</p>
Full article ">Scheme 2
<p>Graphical representation of grafting of MSN<sub>AS</sub>.</p>
Full article ">Scheme 3
<p>Flow chart of results and scientific contribution.</p>
Full article ">
15 pages, 4986 KiB  
Article
Relevant Aspects in the Mechanical and Aging Degradation of NiTi Alloy with R-Phase in Endodontic Files
by Patricia Sánchez, Benedetta Vidi, Cristina Rico, Jesús Mena-Alvarez, Javier Gil and Juan Manuel Aragoneses
Materials 2024, 17(13), 3351; https://doi.org/10.3390/ma17133351 - 6 Jul 2024
Viewed by 784
Abstract
One of the most important challenges in endodontics is to have files that have excellent flexibility, toughness, and high fatigue life. Superelastic NiTi alloys have been a breakthrough and the new R-phase NiTi alloys promise to further optimize the good properties of NiTi [...] Read more.
One of the most important challenges in endodontics is to have files that have excellent flexibility, toughness, and high fatigue life. Superelastic NiTi alloys have been a breakthrough and the new R-phase NiTi alloys promise to further optimize the good properties of NiTi alloys. In this work, two austenitic phase endodontic files with superelastic properties (Protaper and F6) and two austenitic phase files with the R-phase (M-wire and Reciproc) have been studied. The transformation temperatures were studied by calorimetry. Molds reproducing root canals at different angles (30, 45, and 70°) were obtained with cooling and loads simulating those used in the clinic. Mechanical cycles of different files were realized to fracture. Transformation temperatures were determined at different number of cycles. The different files were heat treated at 300 and 500 °C as the aging process, and the transformation temperatures were also determined. Scanning and transmission electron microscopy was used to observe the fractography and precipitates of the files. The results show that files with the R-phase have higher fracture cycles than files with only the austenitic phase. The fracture cycles depend on the angle of insertion in the root canal, with the angle of 70° being the one with the lowest fracture cycles in all cases. The R-Phase transformation increases the energy absorbed by the NiTi to produce the austenitic to R-phase and to produce the martensitic transformation causing the increase in the fracture cycles. Mechanical cycling leads to significant increases in the transformation temperatures Ms and Af as well as Rs and Rf. No changes in the transformation temperatures were observed for aging at 300 °C, but the appearance of Ni4Ti3 precipitates was observed in the aging treatments to the Nickel-rich files that correspond to those with the R transition. These results should be considered by endodontists to optimize the type of files for clinical therapy. Full article
(This article belongs to the Special Issue Orthodontic Materials: Properties and Effectiveness of Use)
Show Figures

Figure 1

Figure 1
<p>Different NiTi endodontic files studied. Reciproc and M wire present R-phase.</p>
Full article ">Figure 2
<p>Scheme of the different molds for endodontics tests. The 30°, 45° and 70° angles were used, which are common angles in clinical practice [<a href="#B21-materials-17-03351" class="html-bibr">21</a>].</p>
Full article ">Figure 3
<p>Thermograms of F6 and Protaper endodontic files (heating and cooling cycles). Three different samples studied for each type of files.</p>
Full article ">Figure 4
<p>Thermograms of M-wire and Reciproc endodontic files (heating and cooling cycles). Three different samples studied for each type of files. In the thermograms the peaks of R-phase are identified.</p>
Full article ">Figure 5
<p>Number of cycles to fracture for different types of files and different angles. Letters signify statistically significant differences with a <span class="html-italic">p</span> &lt; 0.01 with respect to the number of cycles to fracture. When the letters are equal there are no statistically significant differences between them. If the letters are different, it means that there are statistically significant differences with a <span class="html-italic">p</span> &lt; 0.01.</p>
Full article ">Figure 6
<p>M<sub>s</sub> and A<sub>f</sub> transformation temperatures at different number of cycles for test realized at 45° with Protaper and F6 files.</p>
Full article ">Figure 7
<p>M<sub>s</sub> and A<sub>f</sub> transformation temperatures and R<sub>s</sub> and R<sub>f</sub> for the R transition at different number of cycles for test realized at 45° with Reciproc and M-wire files.</p>
Full article ">Figure 8
<p>Transformation temperatures for each type of file treated at 300 °C for different times.</p>
Full article ">Figure 9
<p>Transformation temperatures for each type of file treated at 500 °C for different times.</p>
Full article ">Figure 10
<p>Precipitates observed by Transmission Electron Microscope produced by aging in Ni-rich samples.</p>
Full article ">Figure 11
<p>Fractography of the NiTi endodontic file. In this case, it corresponds to the M-wire.</p>
Full article ">
11 pages, 3241 KiB  
Article
Detecting Internal Defects in FRP-Reinforced Concrete Structures through the Integration of Infrared Thermography and Deep Learning
by Pengfei Pan, Rongpeng Zhang, Yi Zhang and Hongbo Li
Materials 2024, 17(13), 3350; https://doi.org/10.3390/ma17133350 - 6 Jul 2024
Cited by 1 | Viewed by 1140
Abstract
This study represents a significant advancement in structural health monitoring by integrating infrared thermography (IRT) with cutting-edge deep learning techniques, specifically through the use of the Mask R-CNN neural network. This approach targets the precise detection and segmentation of hidden defects within the [...] Read more.
This study represents a significant advancement in structural health monitoring by integrating infrared thermography (IRT) with cutting-edge deep learning techniques, specifically through the use of the Mask R-CNN neural network. This approach targets the precise detection and segmentation of hidden defects within the interfacial layers of Fiber-Reinforced Polymer (FRP)-reinforced concrete structures. Employing a dual RGB and thermal camera setup, we captured and meticulously aligned image data, which were then annotated for semantic segmentation to train the deep learning model. The fusion of the RGB and thermal imaging significantly enhanced the model’s capabilities, achieving an average accuracy of 96.28% across a 5-fold cross-validation. The model demonstrated robust performance, consistently identifying true negatives with an average specificity of 96.78% and maintaining high precision at 96.42% in accurately delineating damaged areas. It also showed a high recall rate of 96.91%, effectively recognizing almost all actual cases of damage, which is crucial for the maintenance of structural integrity. The balanced precision and recall culminated in an average F1-score of 96.78%, highlighting the model’s effectiveness in comprehensive damage assessment. Overall, this synergistic approach of combining IRT and deep learning provides a powerful tool for the automated inspection and preservation of critical infrastructure components. Full article
(This article belongs to the Section Construction and Building Materials)
Show Figures

Figure 1

Figure 1
<p>Proposed framework.</p>
Full article ">Figure 2
<p>(<b>a</b>) Unbonded damage image; (<b>b</b>) bonded damage image; (<b>c</b>) bonded thermal image; and (<b>d</b>) fusion image.</p>
Full article ">Figure 3
<p>Specimens: (<b>a</b>) unbonded concrete and (<b>b</b>) bonded concrete.</p>
Full article ">Figure 4
<p>Database used in this study. (<b>a</b>) Open-source dataset [<a href="#B43-materials-17-03350" class="html-bibr">43</a>]. (<b>b</b>) Dataset of this study.</p>
Full article ">Figure 4 Cont.
<p>Database used in this study. (<b>a</b>) Open-source dataset [<a href="#B43-materials-17-03350" class="html-bibr">43</a>]. (<b>b</b>) Dataset of this study.</p>
Full article ">Figure 5
<p>Loss curve and accuracy curve.</p>
Full article ">
21 pages, 5652 KiB  
Article
Dynamic Adhesive Behavior and Biofilm Formation of Staphylococcus aureus on Polylactic Acid Surfaces in Diabetic Environments
by María Fernández-Grajera, Miguel A. Pacha-Olivenza, María Coronada Fernández-Calderón, María Luisa González-Martín and Amparo M. Gallardo-Moreno
Materials 2024, 17(13), 3349; https://doi.org/10.3390/ma17133349 - 6 Jul 2024
Cited by 1 | Viewed by 1074
Abstract
Interest in biodegradable implants has focused attention on the resorbable polymer polylactic acid. However, the risk of these materials promoting infection, especially in patients with existing pathologies, needs to be monitored. The enrichment of a bacterial adhesion medium with compounds that are associated [...] Read more.
Interest in biodegradable implants has focused attention on the resorbable polymer polylactic acid. However, the risk of these materials promoting infection, especially in patients with existing pathologies, needs to be monitored. The enrichment of a bacterial adhesion medium with compounds that are associated with human pathologies can help in understanding how these components affect the development of infectious processes. Specifically, this work evaluates the influence of glucose and ketone bodies (in a diabetic context) on the adhesion dynamics of S. aureus to the biomaterial polylactic acid, employing different approaches and discussing the results based on the physical properties of the bacterial surface and its metabolic activity. The combination of ketoacidosis and hyperglycemia (GK2) appears to be the worst scenario: this system promotes a state of continuous bacterial colonization over time, suppressing the stationary phase of adhesion and strengthening the attachment of bacteria to the surface. In addition, these supplements cause a significant increase in the metabolic activity of the bacteria. Compared to non-enriched media, biofilm formation doubles under ketoacidosis conditions, while in the planktonic state, it is glucose that triggers metabolic activity, which is practically suppressed when only ketone components are present. Both information must be complementary to understand what can happen in a real system, where planktonic bacteria are the ones that initially colonize a surface, and, subsequently, these attached bacteria end up forming a biofilm. This information highlights the need for good monitoring of diabetic patients, especially if they use an implanted device made of PLA. Full article
Show Figures

Figure 1

Figure 1
<p>Microscopy images taken at 0 min (1), 0.5 min (2), 10 min (3), 180 min (4), and 300 min (5) during the dynamic bacterial adhesion experiments of <span class="html-italic">S. aureus</span> to the PLA surface into each experimental condition. Scale bar in the bottom right corner represents 36 µm.</p>
Full article ">Figure 2
<p>Example of the exponential fit of the system enriched with 0.9 g/L glucose on growth and adhesion (G1). Images taken every 30 s during the first 10 min. Images taken every 60 s during the next 10 min. Images taken every 5 min from 20 min to 3 h. Images taken every 15 min from 3 h to 5 h.</p>
Full article ">Figure 3
<p>Parameters obtained from the exponential approximation of bacterial adhesion curves. A is the characteristic time of the system based on the exponential fit. <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>n</mi> </mrow> <mrow> <mn>300</mn> </mrow> </msub> </mrow> </semantics></math> is the bacterial coverage density corresponding to 300 min of adhesion. The left ordinate axis corresponds to the values of parameter <span class="html-italic">A</span>. The right ordinate axis corresponds to the data of parameter <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>n</mi> </mrow> <mrow> <mn>300</mn> </mrow> </msub> </mrow> </semantics></math>.</p>
Full article ">Figure 4
<p>Approximation by sections of the evolution of bacterial adhesion on PLA (without diabetic enrichment in growth and adhesion). Images taken every 30 s during the first 10 min. Images taken every 60 s during next 10 min. Images taken every 5 min from 20 min to 3 h. Images taken every 15 min from 3 h to 5 h.</p>
Full article ">Figure 5
<p>Approximation by sections of the evolution of bacterial adhesion on PLA when growth and adhesion are enriched with 0.9 g/L glucose (G1). Images taken every 30 s during the first 10 min. Images taken every 60 s during next 10 min. Images taken every 5 min from 20 min to 3 h. Images taken every 15 min from 3 h to 5 h.</p>
Full article ">Figure 6
<p>Approximation by sections of the evolution of bacterial adhesion on PLA when growth and adhesion are enriched with 1.9 g/L glucose (G2). Images taken every 30 s during the first 10 min. Images taken every 60 s during next 10 min. Images taken every 5 min from 20 min to 3 h. Images taken every 15 min from 3 h to 5 h.</p>
Full article ">Figure 7
<p>Approximation by sections of the evolution of bacterial adhesion on PLA when growth and adhesion are enriched with 1 mmol/L of ketone bodies (K1). Images taken every 30 s during the first 10 min. Images taken every 60 s during next 10 min. Images taken every 5 min from 20 min to 3 h. Images taken every 15 min from 3 h to 5 h.</p>
Full article ">Figure 8
<p>Approximation by sections of the evolution of bacterial adhesion on PLA when growth and adhesion are enriched with 9 mmol/L of ketone bodies (K2). Images taken every 30 s during the first 10 min. Images taken every 60 s during next 10 min. Images taken every 5 min from 20 min to 3 h. Images taken every 15 min from 3 h to 5 h.</p>
Full article ">Figure 9
<p>Approximation by sections of the evolution of bacterial adhesion on PLA when growth and adhesion are enriched with 0.9 g/L glucose and 1 mmol/L of ketone bodies (GK1). Images taken every 30 s during the first 10 min. Images taken every 60 s during next 10 min. Images taken every 5 min from 20 min to 3 h. Images taken every 15 min from 3 h to 5 h.</p>
Full article ">Figure 10
<p>Approximation by sections of the evolution of bacterial adhesion on PLA when growth and adhesion are enriched with 1.9 g/L glucose and 9 mmol/L of ketone bodies (GK2). Images taken every 30 s during the first 10 min. Images taken every 60 s during next 10 min. Images taken every 5 min from 20 min to 3 h. Images taken every 15 min from 3 h to 5 h.</p>
Full article ">Figure 11
<p>Parameters obtained from the approximation by sections of bacterial adhesion curves. <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>j</mi> </mrow> <mrow> <mn>0</mn> </mrow> </msub> </mrow> </semantics></math> is the initial adhesion rate during the first 10 min. <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>j</mi> </mrow> <mrow> <mi>f</mi> </mrow> </msub> </mrow> </semantics></math> is the adhesion rate at the end of the adhesion experiment. <span class="html-italic">D</span> is the percentage of reduction decrease. <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>n</mi> </mrow> <mrow> <mi mathvariant="normal">e</mi> </mrow> </msub> </mrow> </semantics></math> is the bacterial coverage density corresponding to the steady state of adhesion.</p>
Full article ">Figure 12
<p>Zeta potential of the different systems analyzed in this work.</p>
Full article ">Figure 13
<p>Percentage of the relative light units (RLU %) of the bacteria cultured in media enriched with glucose and/or ketone bodies, compared to the control samples before contact with PBS. The data are presented for samples before (no-striped columns) and after 300 min (striped columns) of contact with PBS with the same enrichment as culture media. Significant differences (<span class="html-italic">p</span> &lt; 0.05) among samples before contact with PBS are marked as A, B, C, D, E, and F with respect to control samples G1, G2, K1, K2, and GK1, respectively. Significant differences (<span class="html-italic">p</span> &lt; 0.05) among samples after 300 min contact with PBS are marked as H, I, J, K, L, and M with respect to control samples G1, G2, K1, K2, and GK1, respectively; control samples before contact with PBS have been taken as reference. Labels marked with * indicate significant difference (<span class="html-italic">p</span> &lt; 0.05) between the samples after and before contact with enriched PBS, as indicated in the label.</p>
Full article ">Figure 14
<p>Percentage of the relative light units (RLU %) obtained from biofilms cultured in media enriched with glucose and/or ketone bodies, relative to the biofilm control growth in non-enriched media. Significant differences (<span class="html-italic">p</span> &lt; 0.05) among samples are indicated by *, ^, +, ¬, ″, and ~ with respect to control samples, G1, G2, K1, K2, and GK1, respectively.</p>
Full article ">
Previous Issue
Next Issue
Back to TopTop