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16 pages, 3854 KiB  
Article
Combined Reaction System for NH3 Decomposition and CO2 Methanation Using Hydrogen Permeable Membrane Reactor in 1D Model Analysis
by Putri Permatasari, Haruka Goto, Manabu Miyamoto, Yasunori Oumi, Yogi Wibisono Budhi and Shigeyuki Uemiya
Membranes 2024, 14(12), 273; https://doi.org/10.3390/membranes14120273 - 17 Dec 2024
Abstract
In a previous study, we developed an integrated reaction system combining NH3 decomposition and CO2 methanation within a membrane reactor, significantly enhancing reactor performance through efficient H2 separation. Ru/Ba/γ-Al2O3 and Ru/ZrO2 were employed as catalysts for [...] Read more.
In a previous study, we developed an integrated reaction system combining NH3 decomposition and CO2 methanation within a membrane reactor, significantly enhancing reactor performance through efficient H2 separation. Ru/Ba/γ-Al2O3 and Ru/ZrO2 were employed as catalysts for each reaction. To ensure the accuracy and reliability of our results, they were validated through 1D models using FlexPDE Professional Version 7.21/W64 software. Key parameters such as reactor arrangement, catalyst bed positioning, overall heat transfer coefficient, rate constants, and H2 permeance were investigated to optimize system efficiency. The study revealed that positioning the NH3 decomposition on the shell side and CO2 methanation on the tube side resulted in a better performance. Additionally, shifting the methanation catalyst bed downward by approximately one-eighth (10 mm from 80 mm) achieves the highest CO2 conversion. A sensitivity analysis identified the rate constant of the NH3 decomposition catalyst and the H2 permeance of the membrane as the most influential factors in enhancing CO2 conversion. This highlights the priority of improving membrane H2 permeance and catalytic activity for NH3 decomposition to maximize system efficiency. Full article
(This article belongs to the Section Membrane Fabrication and Characterization)
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Figure 1
<p>Schematic of reaction equipment used for NH<sub>3</sub> decomposition (<b>left</b>) and CO<sub>2</sub> methanation (<b>right</b>) reactor.</p>
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<p>The device’s dimensions (<b>upper left</b>), heat transfer in the system (<b>upper middle</b>), the position of the catalyst layer (<b>upper right</b>), and the arrangement of the reactors: arrangement 1 (<b>bottom left</b>) and arrangement 2 (<b>bottom right</b>).</p>
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<p>Catalyst performance (<b>top</b>) and comparison of experimental and simulation results (<b>middle</b>-<b>bottom</b>) for ammonia decomposition reaction (<b>left</b>) and carbon dioxide methanation (<b>right</b>).</p>
Full article ">Figure 3 Cont.
<p>Catalyst performance (<b>top</b>) and comparison of experimental and simulation results (<b>middle</b>-<b>bottom</b>) for ammonia decomposition reaction (<b>left</b>) and carbon dioxide methanation (<b>right</b>).</p>
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<p>Experimental results (<b>1</b>) vs. simulated results for conversion rate (<b>2</b>), hydrogen pressure, (<b>3</b>) and temperature profile (<b>4</b>) obtained from arrangements 1 and 2.</p>
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<p>Heat transfer from arrangement 2 and its magnification.</p>
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<p>Conversion rates of both reactions when the CO<sub>2</sub> methanation catalyst is moved.</p>
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<p>Effect of changes in heat transfer (<b>upper</b>), reaction rate constant (<b>middle</b>), and hydrogen permeance (<b>bottom</b>) on the system.</p>
Full article ">Figure 7 Cont.
<p>Effect of changes in heat transfer (<b>upper</b>), reaction rate constant (<b>middle</b>), and hydrogen permeance (<b>bottom</b>) on the system.</p>
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<p>Sensitivity analysis of CO<sub>2</sub> conversion (combined) where a (0–25) is the sensitivity analysis variable.</p>
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18 pages, 11699 KiB  
Article
Evolution of Precipitates and Microhardness of L-PBF Inconel 625 Through Relevant Thermal Treatment
by Tahmina Keya, Ralf D. Fischer, Mohanish Andurkar, Scott M. Thompson, Valentina O’Donnell, John Gahl and Barton C. Prorok
Alloys 2024, 3(4), 295-312; https://doi.org/10.3390/alloys3040018 - 17 Dec 2024
Abstract
Laser powder bed fusion (L-PBF) is a metal additive manufacturing (AM) technique that produces a unique microstructure significantly different from wrought microstructure. Inconel 625 (IN625) is an alloy widely used to manufacture complex parts, but it comes with its own unique challenges. The [...] Read more.
Laser powder bed fusion (L-PBF) is a metal additive manufacturing (AM) technique that produces a unique microstructure significantly different from wrought microstructure. Inconel 625 (IN625) is an alloy widely used to manufacture complex parts, but it comes with its own unique challenges. The alloy is prone to precipitation under elevated temperatures, which makes designing suitable heat treatment to tailor the desired microstructure and mechanical properties critical. Traditional heat treatment for wrought IN625 cannot be applied to L-PBF IN625; therefore, it is vital to understand the evolution of precipitates on the way to complete recrystallization. This study focuses on these precipitates in IN625 produced by the L-PBF technique. Heat treatments at 700 °C, 900 °C, and 1050 °C were performed separately to encourage the precipitation of strengthening γ″, the detrimental δ phase, and the dissolution of precipitates, respectively. γ″ precipitates were found in the as-printed condition and at 700 °C. δ precipitates were detected at 700 and 900 °C. Carbides and Al-rich oxides were observed in all conditions of L-PBF IN625. Texture analysis showed grain growth along the build direction with strong (100) texture at temperatures up to 900 °C. Weak and random texture with equiaxed grains was observed at 1050 °C, which is similar to wrought IN625. Full article
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<p>SEM images of the microstructure of L-PBF IN625; (<b>a</b>) as-printed, (<b>b</b>) heat-treated at 700 °C for 2 h, (<b>c</b>) heat-treated at 900 °C for 2 h, and (<b>d</b>) heat-treated at 1050 °C for 2 h.</p>
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<p>(<b>a</b>–<b>e</b>) Inverse pole figure (IPF) maps of as-printed and heat-treated L-PBF IN625 along the BD compared to wrought IN625; (<b>f</b>) grain size evolution of each sample.</p>
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<p>Pole figures (PFs) of as-printed and heat-treated L-PBF IN625 compared to wrought IN625.</p>
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<p>TEM micrographs from the (<b>a</b>) AP and (<b>c</b>) 700_2h sample; SAED patterns from the (<b>b</b>) AP and (<b>d</b>) 700_2h samples showing the presence of γ″ precipitate.</p>
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<p>(<b>a</b>) TEM image inside a grain in the 700_2h sample; (<b>b</b>) SAED pattern from (<b>a</b>) indicating the presence of δ.</p>
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<p>(<b>a</b>) TEM thin film taken from the 900_2h sample; (<b>b</b>) bright-field TEM image of a δ precipitate on GB and (<b>c</b>) corresponding SAED pattern; (<b>d</b>) bright-field TEM image of a δ precipitate inside the grain; (<b>e</b>) HRTEM image of a δ precipitate with FFT showing γ matrix and stacking fault; (<b>f</b>) HRTEM image of a δ precipitate with (<b>g</b>) an FFT pattern of area 3 indexed for the δ precipitate.</p>
Full article ">Figure 7
<p>Carbides with corresponding EDS patterns in (<b>a</b>) AP, (<b>b</b>) 700_2h, (<b>c</b>) 900_2h, and (<b>d</b>) 1050_2h samples.</p>
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<p>Al<sub>2</sub>O<sub>3</sub> particles with EDS spectra in (<b>a</b>) TEM BF image from AP; (<b>b</b>) TEM BSE image from 700_2h; (<b>c</b>) SEM BSE image from 900_2h; and (<b>d</b>) SEM image from the 1050_2h sample.</p>
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<p>Al<sub>2</sub>O<sub>3</sub> particles on and around δ precipitates.</p>
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<p>Microhardness on L-PBF heat-treated IN625 compared to wrought IN625.</p>
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<p>Kernel average misorientation for L-PBF and wrought IN625 samples.</p>
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19 pages, 4917 KiB  
Article
Preferred Chemical Agent for Electrochemical Modification of Physical and Mechanical Parameters of Mudstone
by Xiangchen Chen, Liu Han, Gerson S. V. Tovele, Jiangrong Kong and Han Yang
Appl. Sci. 2024, 14(24), 11789; https://doi.org/10.3390/app142411789 - 17 Dec 2024
Abstract
To study the influence of electrochemically modified mediums on the physical and mechanical parameters of mudstone samples, focusing on electrolyte solutions and electrode materials, this paper combines theoretical analysis and experimental research. It analyzes the modification mechanism of mudstone through electrochemical techniques, clarifying [...] Read more.
To study the influence of electrochemically modified mediums on the physical and mechanical parameters of mudstone samples, focusing on electrolyte solutions and electrode materials, this paper combines theoretical analysis and experimental research. It analyzes the modification mechanism of mudstone through electrochemical techniques, clarifying that the main factors improving the strength of mudstone are electro-osmotic drainage consolidation and electrochemical reaction cementation. The mudstone was electrochemically modified using the controlled variable method. The mudstone sample’s hydraulic properties and shear strength were measured before and after modification. The study compared and analyzed the effectiveness of different modified materials. The results indicated that the liquid limit of the modified mudstone samples decreased by 7.874%, while the plastic limit increased by 9.499%. The type of ions introduced by the electrolyte solution influenced the cementation strength of the mudstone. AlCl3 solutions with a 10% mass fraction and CaCl2 solutions with a 25% mass fraction both effectively modify the reinforcement; however, the AlCl3 solution with a 10% mass fraction is the most effective for modifying mudstone samples. The electrochemical modification of mudstone samples with the three electrode materials (graphite, iron and aluminum) revealed that the samples modified with graphite electrodes had the highest shear strength, while those modified with aluminum electrodes had the lowest shear strength. The internal friction angle of graphite electrode-modified mudstone specimens was 26.7°, compared to the original value of 23.9°, and the cohesion was 34.4 kPa, compared to the original value of 12.3 kPa, nearly three times the original value. It is recommended to use graphite electrodes and a 10% mass fraction of AlCl3 for the electrochemical modification of this type of mudstone in engineering applications. Full article
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<p>Structure of the study on the preferential method of electrochemical modification of chemical agents.</p>
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<p>Experimental device for electrochemical modification of mudstone specimens.</p>
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<p>The experiment and results of the combined determination method of Atterberg limits. (<b>a</b>) Three moisture content samples; (<b>b</b>) test results.</p>
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<p>The combined determination method of Atterberg limits the results of modified specimens. (<b>a</b>) unmodified by the addition of 10% AlCl<sub>3</sub> solution; (<b>b</b>) modified by the addition of 10% AlCl<sub>3</sub> solution.</p>
Full article ">Figure 5
<p>Shear stress–shear displacement curves of mudstone under different water content. (<b>a</b>) <span class="html-italic">w</span> = 25%; (<b>b</b>) <span class="html-italic">w</span> = 20%; (<b>c</b>) <span class="html-italic">w</span> = 15%.</p>
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<p>The <span class="html-italic">τ</span>-<span class="html-italic">σ</span> curves of mudstone under different water content.</p>
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<p>The relationship between the modification times and the shear strength of mudstone.</p>
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<p>Shear strength of mudstone corresponds to different mass fraction electrolyte solutions (<span class="html-italic">σ</span> = 200 kPa). (<b>a</b>) CaCl<sub>2</sub>; (<b>b</b>) AlCl<sub>3</sub>.</p>
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<p>Electrode after electrochemical reaction. (<b>a</b>) Graphite electrode. (<b>b</b>) Iron electrode. (<b>c</b>) Aluminum electrode.</p>
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<p>Surface of specimens at 3 electrode conditions (10% AlCl<sub>3</sub>). (<b>a</b>) Graphite electrode. (<b>b</b>) Iron electrode. (<b>c</b>) Aluminum electrode.</p>
Full article ">Figure 11
<p>Shear strength of specimens at 3 electrode conditions (10% AlCl<sub>3</sub>).</p>
Full article ">Figure 12
<p>Shear strength parameters of graphite electrode modified specimens. (<b>a</b>) Shear stress–displacement curve; (<b>b</b>) shear stress–normal stress curve.</p>
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13 pages, 13527 KiB  
Article
Influence of High-Speed Ram Transition Position on Porosity and Mechanical Properties of Large One-Piece Die-Casting Al-Si-Mn-Mg Aluminium Alloy
by Sai Zhang, Pengfei Ren, Kangle Wang, Bo Liu and Xianming Meng
Materials 2024, 17(24), 6169; https://doi.org/10.3390/ma17246169 - 17 Dec 2024
Abstract
The high-pressure die-casting process can effectively manufacture aluminium alloy castings with complex shapes and thin wall thicknesses. However, due to the complex flow characteristics of the liquid metal during the mould-filling process, there are significant differences in the mechanical properties of different parts [...] Read more.
The high-pressure die-casting process can effectively manufacture aluminium alloy castings with complex shapes and thin wall thicknesses. However, due to the complex flow characteristics of the liquid metal during the mould-filling process, there are significant differences in the mechanical properties of different parts of the casting. This paper analyses the effect of the high-speed ram transition position on porosity and mechanical properties of Al-Si-Mn-Mg aluminium alloys in the high-pressure die-casting (HPDC) process, comparing the 1160 mm and 1200 mm positions. Using a comprehensive methodology that combines CT, tensile tests, and SEM, the research demonstrates that the 1160 mm position improves mechanical properties and reduces porosity, with a larger gap at the near-end of the casting, where the yield limit and elongation of the casting increased by 13% and 25% at 1160 mm compared to 1200 mm, respectively. This result shows that appropriate adjustment of the high-speed ram transition position can effectively optimise the organisational structure of thin-walled castings, and then improve their mechanical properties. Full article
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<p>The configuration of (<b>a</b>) HPDC casting, (<b>b</b>) a testing sample, and (<b>c</b>) process parameters. (<b>d</b>) X-ray CT scanning equipment and principle. (<b>e</b>) X-ray CT scan, (<b>f</b>) OM, and (<b>g</b>) SEM results.</p>
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<p>Schematic diagram of high- and low-speed switching points.</p>
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<p>Sample 1, Sample 2, Sample 3, and Sample 4 CT scan results. (<b>a</b>) Air holes, (<b>b</b>) shrinkage holes, (<b>c</b>) air-shrinkage holes.</p>
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<p>(<b>a</b>) Sample 1 pore size distribution in the thickness direction of the sample. (<b>b</b>) Sample 2 pore size distribution in the thickness direction of the sample. (<b>c</b>) Sample 3 pore size distribution in the thickness direction of the sample. (<b>d</b>) Sample 4 pore size distribution in the thickness direction of the sample. (<b>e</b>) Statistical analyses of pore information.</p>
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<p>Tensile fracture locations and X-ray CT results: (<b>a</b>) Sample 1; (<b>b</b>) Sample 2; (<b>c</b>) Sample 3; (<b>d</b>) Sample 4.</p>
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<p>Distribution of mechanical properties at near-end and far-end: (<b>a</b>) stress–strain data at near-end; (<b>b</b>) stress–strain data at far-end; (<b>c</b>) mechanical property statistics at near-end; (<b>d</b>) mechanical property statistics at far-end.</p>
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<p>As-cast microstructure of proximal and distal ends at 1160 mm and 1200 mm states.</p>
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<p>Proximal and distal fracture morphology at 1160 mm and 1200 mm: (1), (2), and (3) are localised morphology of the respective fracture ports; (4), (5), and (6) are the EDS images of the respective fracture (1) position; (7) is the atomic percentage.</p>
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17 pages, 1581 KiB  
Article
The Influence of the Spatial Co-Registration Error on the Estimation of Growing Stock Volume Based on Airborne Laser Scanning Metrics
by Marek Lisańczuk, Krzysztof Mitelsztedt and Krzysztof Stereńczak
Remote Sens. 2024, 16(24), 4709; https://doi.org/10.3390/rs16244709 - 17 Dec 2024
Abstract
Remote sensing (RS)-based forest inventories are becoming increasingly common in forest management. However, practical applications often require subsequent optimisation steps. One of the most popular RS-based forest inventory methods is the two-phase inventory with regression estimator, commonly referred to as the area-based approach [...] Read more.
Remote sensing (RS)-based forest inventories are becoming increasingly common in forest management. However, practical applications often require subsequent optimisation steps. One of the most popular RS-based forest inventory methods is the two-phase inventory with regression estimator, commonly referred to as the area-based approach (ABA). There are many sources of variation that contribute to the overall performance of this method. One of them, which is related to the core aspect of this method, is the spatial co-registration error between ground measurements and RS data. This error arises mainly from the imperfection of the methods for positioning the sample plots under the forest canopy. In this study, we investigated how this positioning accuracy affects the area-based growing stock volume (GSV) estimation under different forest conditions and sample plot radii. In order to analyse this relationship, an artificial co-registration error was induced in a series of simulations and various scenarios. The results showed that there were minimal differences in ABA inventory performance for displacements below 4 m for all stratification groups except for deciduous sites, where sub-metre plot positioning accuracy was justified, as site- and terrain-related factors had some influence on GSV estimation error (r up to 0.4). On the other hand, denser canopy and spatially homogeneous stands mitigated the negative aspects of weaker GNSS positioning capabilities under broadleaved forest types. In the case of RMSE, the results for plots smaller than 400 m2 were visibly inferior. The BIAS behaviour was less strict in this regard. Knowledge of the actual positioning accuracy as well as the co-registration threshold required for a particular stand type could help manage and optimise fieldwork, as well as better distinguish sources of statistical uncertainty. Full article
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<p>Distribution of GSV estimation error due to co-registration shift and plot area.</p>
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19 pages, 15518 KiB  
Article
Powder Metallurgy Processing to Enhance Superelasticity and Shape Memory in Polycrystalline Cu–Al–Ni Alloys: Reference Material for Additive Manufacturing
by Mikel Pérez-Cerrato, Jose F. Gómez-Cortés, Ernesto Urionabarrenetxea, Isabel Ruiz-Larrea, Fernando Carreño, Ízaro Ayesta, María L. Nó, Nerea Burgos and Jose M. San Juan
Materials 2024, 17(24), 6165; https://doi.org/10.3390/ma17246165 - 17 Dec 2024
Abstract
Shape memory alloys (SMAs) are functional materials with a wide range of applications, from the aerospace sector to the biomedical field. Nowadays, there is a worldwide interest in developing SMAs through powder metallurgy like additive manufacturing (AM), which allows innovative building processes. However, [...] Read more.
Shape memory alloys (SMAs) are functional materials with a wide range of applications, from the aerospace sector to the biomedical field. Nowadays, there is a worldwide interest in developing SMAs through powder metallurgy like additive manufacturing (AM), which allows innovative building processes. However, producing SMAs using AM techniques is particularly challenging because of the microstructure required to obtain optimal functional properties. This aspect is critical in the case of Cu–Al–based SMAs, due to their high elastic anisotropy, making them brittle in polycrystalline form. In this work, we approached the processing of a Cu–Al–Ni SMA following a specific powder metallurgy route: gas atomization of a pre-alloyed melt; compaction of the atomized powders through hot isostatic pressing; and a final hot rolling plus thermal treatments. Then, the microstructure of the material was characterized by electron microscopy showing a specific [001] texture in the rolling direction that improved the functional behavior. The successive processing steps produce an increase of about 40 °C in the martensitic transformation temperatures, which can be well controlled and reproduced through the developed methodology. The thermomechanical functional properties of superelasticity and shape memory were evaluated on the final SMA. Outstanding, fully recoverable superelastic behavior of 4.5% in tension, as well as a ±5% full shape memory recovery in bending, were reported for many cycles. These experiments demonstrate the enhanced mechanical and functional properties obtained in polycrystalline Cu–Al–Ni SMAs by powder metallurgy. The present results pave the road for producing this kind of SMA with the new AM technologies, which always produce polycrystalline components and can improve their processes taking the powder metallurgy SMA, here produced, as reference material. Full article
(This article belongs to the Special Issue Advances in Materials Processing (3rd Edition))
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<p>Flow chart of the complete processing procedure, in blue cases at the left, together with the characterizations performed along the study; microstructure in red and functional in green.</p>
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<p>(<b>a</b>) SEM-SE image of a powder grain. The martensite variants can be appreciated on its surface in some of the grains. (<b>b</b>) DSC results for the powder material. (<b>c</b>) Phase-transformed fractions n(T) obtained by integration of the DSC results in (<b>b</b>), which are used for the determination of the MT temperatures.</p>
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<p>(<b>a</b>) Sample produced using a conventional method of powder metallurgy, HIP followed by hot rolling down to 1.1 mm thickness. (<b>b</b>) Dog-bone-shaped sample cut by EDM from the plate in (<b>a</b>), for the realizations of tensile mechanical tests.</p>
Full article ">Figure 4
<p>Microstructure of the Cu–Al–Ni HR sample. (<b>a</b>) Optical microscope image of the alloy after HIP but before the lamination process. (<b>b</b>) Optical microscope image depicting the elongation of the grains along the direction of the lamination (x direction). (<b>c</b>,<b>d</b>) SEM (BSE) images taken at 20 KV showing some precipitates at the grain boundaries as well as the oxide nanoparticles coming from the surface of the powder particles, which remain decorating the grain boundaries.</p>
Full article ">Figure 5
<p>(<b>a</b>) EBSD map of the Cu–Al–Ni HR sample taken at room temperature in martensite, with a step size of 50 nm. (<b>b</b>) All variants correspond to the β’<sub>3</sub> martensite, with the orientations indicated in the figures. The red interfaces are twin I, the greens are twin II, and the blues are the twin compound.</p>
Full article ">Figure 6
<p>(<b>a</b>) EBSD map of the Cu–Al–Ni HR sample taken at 145 °C in austenite where the high-angle grain boundaries (θ ≥ 10°) are plotted; some boundaries are not closed because the disorientations below 10° are not plotted. (<b>b</b>) Inverse pole figures showing the crystallographic orientation densities (in arbitrary units on the right bar) corresponding to the rolling direction (X axis) and to the perpendicular to the rolling plane (Z axis). (<b>c</b>) Plot of the relative frequency of the grain boundaries as a function of their disorientation.</p>
Full article ">Figure 7
<p>Transformation temperatures measured by DSC. (<b>a</b>) Transformation curves for the alloyed powders (in blue), HIPed samples (in green), and HR samples (in red). (<b>b</b>) Transformed martensite fraction for the curves presented in (<b>a</b>).</p>
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<p>Tensile superelastic effect observed for the hot-rolled sample at different values of the maximum strain, up to 4.75%.</p>
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<p>(<b>a</b>) SE at different temperatures, from 120 up to 170 °C every 5 °C, at 1.2% maximum strain. (<b>b</b>) Clausius–Clapeyron coefficient fitted from the data obtained in (<b>a</b>).</p>
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<p>Sequence of the images showing the initial strained sample in martensite in the left image, and the evolution of the shape memory recovery by heating until the complete transformation to austenite, in the right image.</p>
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2 pages, 1809 KiB  
Correction
Correction: Zhang et al. Astaxanthin Alleviates Early Brain Injury Following Subarachnoid Hemorrhage in Rats: Possible Involvement of Akt/Bad Signaling. Mar. Drugs 2014, 8, 4291
by Xiang-Sheng Zhang, Xin Zhang, Qi Wu, Wei Li, Qing-Rong Zhang, Chun-Xi Wang, Xiao-Ming Zhou, Hua Li, Ji-Xin Shi and Meng-Liang Zhou
Mar. Drugs 2024, 22(12), 563; https://doi.org/10.3390/md22120563 - 17 Dec 2024
Abstract
Errors in Figures [...] Full article
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<p>(<b>A</b>) Representative photomicrographs of Nissl (<b>A1</b>–<b>D1</b>) and TUNEL (<b>A2</b>–<b>D2</b>) staining in the cerebral cortex at 24 h after SAH and (<b>B</b>) quantitative analysis of neuronal survival (<b>b1</b>) and the apoptotic index (<b>b2</b>). As shown in the Nissl staining, in the sham group, the neuronal cell outline was clear and the structure compact, with abundant cytoplasm and Nissl bodies. However, evident neuronal loss and neuronal degeneration were observed in the SAH group and SAH + vehicle groups. Treatment with ATX significantly increased the proportion of surviving neurons. The TUNEL staining showed that the rats in the sham group display rare apoptotic cells in the cortex, while obvious TUNEL-positive cells could be observed in the SAH group and SAH + vehicle groups. In contrast, the proportion of apoptotic cell death decreased significantly in the SAH + ATX group. Values are represented as the mean ± SEM. *** <span class="html-italic">p</span> &lt; 0.001, ** <span class="html-italic">p</span> &lt; 0.01, * <span class="html-italic">p</span> &lt; 0.05, <sup>ns</sup> <span class="html-italic">p</span> &gt; 0.05.</p>
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<p>Representative Western blots (<b>A</b>) and quantitative analysis of p-Akt, p-Bad and caspase-3 (<b>B</b>) in the cortex of the SAH + ATX and SAH + ATX + LY294002 groups. The levels of p-Akt and p-Bad were high in the SAH + ATX group. After LY294002 treatment, the high levels of p-Akt and p-Bad were significantly decreased. In contrast to the low level of caspase-3 in the SAH + ATX group, LY294002 treatment significantly upregulated the level of caspase-3 in the cortex. Results are expressed as the means ± SEM. ** <span class="html-italic">p</span> &lt; 0.01, * <span class="html-italic">p</span> &lt; 0.05.</p>
Full article ">
16 pages, 4329 KiB  
Article
Porphyrin-Based Aluminum Metal-Organic Framework with Copper: Pre-Adsorption of Water Vapor, Dynamic and Static Sorption of Diethyl Sulfide Vapor, and Sorbent Regeneration
by Mohammad Shahwaz Ahmad and Alexander Samokhvalov
Materials 2024, 17(24), 6160; https://doi.org/10.3390/ma17246160 - 17 Dec 2024
Viewed by 70
Abstract
Metal–organic frameworks (MOFs) are hybrid inorganic–organic 3D coordination polymers with metal sites and organic linkers, which are a “hot” topic in the research of sorption, separations, catalysis, sensing, and environmental remediation. In this study, we explore the molecular mechanism and kinetics of interaction [...] Read more.
Metal–organic frameworks (MOFs) are hybrid inorganic–organic 3D coordination polymers with metal sites and organic linkers, which are a “hot” topic in the research of sorption, separations, catalysis, sensing, and environmental remediation. In this study, we explore the molecular mechanism and kinetics of interaction of the new copper porphyrin aluminum metal–organic framework (actAl-MOF-TCPPCu) compound 4 with a vapor of the volatile organic sulfur compound (VOSC) diethyl sulfide (DES). First, compound 4 was synthesized by post-synthetic modification (PSM) of Al-MOF-TCPPH2 compound 2 by inserting Cu2+ ions into the porphyrin ring and characterized by complementary qualitative and quantitative chemical, structural, and spectroscopic analysis. Second, the interaction of compound 4 with DES vapor was analyzed dynamically by the novel method of in situ time-dependent attenuated total reflectance Fourier transform infrared (ATR-FTIR) spectroscopy at controlled humidity levels. The sorbent–adsorbate interactions, as analyzed by the shifts in IR peaks, indicate that the bonding includes the hydroxy O-H, carboxylate COO, and phenyl groups. The kinetics of sorption obeys the Langmuir pseudo-first-order rate law. The pre-adsorption of water vapor by compound 4 at the controlled relative humidity under static (equilibrium) conditions yields the binary stoichiometric adsorption complex (Al-MOF-TCPPCu)1.0(H2O)8.0. The pre-adsorption of water vapor makes the subsequent sorption of DES slower, while the kinetics obey the same rate law. Then, static pre-adsorption of water vapor was followed by static sorption of DES vapor, and the ternary adsorption complex (Al-MOF-TCPPCu)1.0(H2O)8.0(DES)3.8 was obtained. Despite the pre-adsorption of significant amounts of water, the binary complex adsorbs a large amount of DES: ca. 36.6 wt. % (per compound 4). Finally, the ternary complex is facilely regenerated by gentle heating under vacuum. Compound 4 and related MOFs are promising for adsorptive removal of vapor of DES and related VOSCs from dry and humid air. Full article
(This article belongs to the Special Issue Adsorbents and Their Applications (Second Volume))
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Graphical abstract

Graphical abstract
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<p>Diethyl sulfide and its presence in nature, technology, and the environment.</p>
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<p>The 2D molecular structure of the structural unit of copper-containing porphyrin aluminum MOF, compound <b>4</b> actAl-MOF-TCPPCu.</p>
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<p>Powder XRD patterns of activated compounds: (<b>a</b>) compound <b>2</b> actAl-MOF-TCPPH<sub>2</sub>; (<b>b</b>) the target compound <b>4</b> actAl-MOF-TCPPCu.</p>
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<p>The starting in situ time-dependent ATR-FTIR spectra of compound 4 in the flow of DES vapor. (<b>a</b>) High wavenumbers; (<b>b</b>) mid-IR; (<b>c</b>) low wavenumbers.</p>
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<p>The proposed model of bonding DES molecules to compound <b>4</b>.</p>
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<p>Kinetics of in situ sorption of DES vapor by the activated compound <b>4</b>. (<b>a</b>) Integration of IR peak due to the asymmetric CH<sub>2</sub> stretching at 2965 cm<sup>−1</sup>; (<b>b</b>) kinetic analysis of the integrated peak.</p>
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<p>The in situ time-dependent ATR-FTIR spectra of the binary adsorption complex hydAl-MOF-TCPPCu in the flow of DES vapor. (<b>a</b>) High wavenumber range; (<b>b</b>) mid-IR range; (<b>c</b>) low wavenumber range.</p>
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<p>Kinetics of in situ sorption of DES vapor by compound <b>4hyd</b>. (<b>a</b>) Integrated IR peak of asymmetric CH<sub>2</sub> stretching; (<b>b</b>) formal kinetic analysis of peak area in time.</p>
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<p>Powder XRD patterns of sorbent compound 4 and its adsorption complexes. (<b>a</b>) actAl-MOF-TCPPCu and hydAl-MOF-TCPPCu (binary adsorption complex). (<b>b</b>) hydAl-MOF-TCPPCu and DES-hydAl-MOF-TCPPCu (ternary adsorption complex). (<b>c</b>) actAl-MOF-TCPPCu and regAl-MOF-TCPPCu (regenerated ternary adsorption complex).</p>
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3 pages, 170 KiB  
Correction
Correction: Kannampuzha et al. A Systematic Role of Metabolomics, Metabolic Pathways, and Chemical Metabolism in Lung Cancer. Vaccines 2023, 11, 381
by Sandra Kannampuzha, Anirban Goutam Mukherjee, Uddesh Ramesh Wanjari, Abilash Valsala Gopalakrishnan, Reshma Murali, Arunraj Namachivayam, Kaviyarasi Renu, Abhijit Dey, Balachandar Vellingiri, Harishkumar Madhyastha and Raja Ganesan
Vaccines 2024, 12(12), 1421; https://doi.org/10.3390/vaccines12121421 - 17 Dec 2024
Viewed by 35
Abstract
Following the publication of paper [...] Full article
13 pages, 6566 KiB  
Article
Optimization of Strength and Plasticity in Layered Aluminum Composites Through High-Pressure Torsion Treatment
by Alexey Evstifeev, Aydar Mavlyutov, Artem Voropaev and Darya Volosevich
Metals 2024, 14(12), 1445; https://doi.org/10.3390/met14121445 - 17 Dec 2024
Viewed by 93
Abstract
The development of high-strength aluminum alloys with improved ductility is a crucial challenge for modern materials science, as high strength and ductility tend to be mutually exclusive properties. In this work, the composite material was fabricated using wire arc additives manufactured from AA1050 [...] Read more.
The development of high-strength aluminum alloys with improved ductility is a crucial challenge for modern materials science, as high strength and ductility tend to be mutually exclusive properties. In this work, the composite material was fabricated using wire arc additives manufactured from AA1050 (commercially pure aluminum) and AA5056 (an Al–Mg system alloy) aluminum alloys. It was demonstrated that the addition of a lower-strength material into a high-strength matrix enhances the potential for deformation localization and results in an increased plasticity of the composite material. A further strengthening of the composite material was achieved through its deformation by a high-pressure torsion (HPT) technique. The mechanical properties of the material were thoroughly investigated before and after the HPT treatment. Static strength and plasticity were analyzed as a function of the deformation degree. Microstructural analysis was performed using scanning electron microscopy and X-ray diffraction. The optimal deformation route, providing the best combination of mechanical properties, was experimentally identified, along with key microstructural parameters of the formed composite with a bimodal grain structure. A deformation level corresponding to 36% of shear stress provides a yield stress of up to 570 MPa, an ultimate tensile strength of up to 664 MPa, and a relative elongation to failure of up to 7%. As a result of the deformation treatment, characteristic substructures with dimensions of ~250 nm and >1000 nm are formed, with a volume ratio of approximately 80/20. Full article
(This article belongs to the Section Additive Manufacturing)
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<p>WAAM installation based on Fronius and Fanuc equipment (<b>a</b>); schematic representation of the WAAM technology process (<b>b</b>); and WAAM sample as a combination of AA5056 and AA1050 aluminum alloys (<b>c</b>).</p>
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<p>The arrangement of specimens within the composite volume: (<b>a</b>) single 2.5 mm thick layer of AA1050; (<b>b</b>) alternating 2.5 mm thick layers of AA1050 and 5 mm thick layers of AA5056; and (<b>c</b>) the clamping of the specimen within the grips.</p>
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<p>Configuration of samples for HPT processing obtained by WAAM.</p>
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<p>Stress–strain diagrams of composite materials: (<b>a</b>) measured based on the initial length of the working part, and (<b>b</b>) measured based on the localization of plastic deformation in the pure aluminum strip. Adapted from Ref. [<a href="#B31-metals-14-01445" class="html-bibr">31</a>].</p>
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<p>The view of the tensile testing process and the fracture surface of the central part of the 1L_45 sample (<b>a</b>–<b>c</b>) and the 1L_90 sample (<b>d</b>–<b>f</b>).</p>
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<p>The view of the tensile testing process and the fracture surface of the central part of the 1L_45 sample (<b>a</b>–<b>c</b>) and the 1L_90 sample (<b>d</b>–<b>f</b>).</p>
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<p>Stress–strain diagrams for composite material samples with varying degrees of deformation (<b>a</b>), and dependences of the yield stress (σ<sub>0.2</sub>), ultimate tensile strength (σ<sub>UTS</sub>), and relative elongation to failure (δ) on the degree of deformation for the composite material with the initial configuration of 2L (<b>b</b>). The area of the optimal combination of properties is circled in red.</p>
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<p>EDX results: Mg distribution (<b>a</b>) and the location of the EDX specimen (the inset) and results of Mg content determination on line 1 (<b>b</b>).</p>
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<p>Mg distribution in the 2L_HPT_1 composite sample (<b>a</b>), the chemical profile of the Mg content along lines 1 (<b>b</b>) and 2 (<b>c</b>).</p>
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<p>XRD pattern of the 1L_HPT_2 composite sample.</p>
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11 pages, 2922 KiB  
Article
The Trace-Element Characteristics of Chrysoberyl: Insights from Compositional and Spectroscopic Analyses
by Linling Dong, Yimiao Liu, Xinxin Gao and Ren Lu
Minerals 2024, 14(12), 1280; https://doi.org/10.3390/min14121280 - 17 Dec 2024
Viewed by 119
Abstract
To characterize the trace-element characteristics of chrysoberyl, we studied twenty-six chrysoberyl samples from various localities by using laser ablation inductively coupled plasma mass spectrometry (LA–ICP–MS), photoluminescence (PL), and ultraviolet–visible–near-infrared (UV–Vis–NIR) spectroscopy. Chemical analysis has confirmed the existence of trace elements, including Fe, Ti, [...] Read more.
To characterize the trace-element characteristics of chrysoberyl, we studied twenty-six chrysoberyl samples from various localities by using laser ablation inductively coupled plasma mass spectrometry (LA–ICP–MS), photoluminescence (PL), and ultraviolet–visible–near-infrared (UV–Vis–NIR) spectroscopy. Chemical analysis has confirmed the existence of trace elements, including Fe, Ti, Ga, Sn, B, Cr, and V. The phenomenon of ionic isomorphic substitution frequently occurs at lattice sites within chrysoberyl. Notably, the isomorphic substitution of Al3+ in octahedral sites is significant, with the primary substituting elements being Fe, Ti, Cr, V, Ga, and Sn. The PL spectra of chrysoberyl samples exhibit sharp peaks at 678 and 680 nm, which are attributed to Cr3+, even in samples in which the Cr concentration is below the detection limit of LA-ICP-MS. This demonstrates the high-sensitivity feature of PL spectroscopy. The UV–Vis–NIR spectra of chrysoberyl samples consistently exhibit a band at 440 nm, and strong double narrow bands near 367 nm and 375 nm are observed. These spectral features are associated with Fe3+ chromophores—specifically, Fe3+-Fe3+ pairs or clusters and Fe3+ ions, respectively. By combining LA–ICP–MS analysis and PL mapping on a sample exhibiting color zoning, it has been found that the darker sections contain a higher concentration of Cr compared to the lighter sections, while the concentrations of other elements remain largely consistent. In other words, subtle variations in Cr concentration may be the underlying cause of color zoning in chrysoberyl. Full article
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<p>Rough and polished chrysoberyl samples from various localities: (<b>A</b>) Myanmar; (<b>B</b>) Sri Lanka; (<b>C</b>) Tanzania; (<b>D</b>) India; (<b>E</b>) Brazil.</p>
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<p>The photoluminescence spectra of chrysoberyl samples. The spectral directions are in the same orientation. (<b>A</b>) Increasing Cr concentration; (<b>B</b>) Cr concentrations below the detection limit of LA-ICP-MS.</p>
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<p>The UV–Vis–NIR spectra of chrysoberyl samples. The spectral directions are in the same orientation.</p>
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<p>The elemental ternary plots illustrate the relationships between chemical composition and origins. (<b>A</b>) The Fe-Ti-Sn diagram; (<b>B</b>) The Fe-Ti-Ga diagram; (<b>C</b>) The Fe-Ga-Sn diagram; (<b>D</b>) The B-V-Cr diagram.</p>
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<p>An approximate linear negative correlation between the content of Al and the content of octahedral-site substituting metal ions (Me<sup>n+</sup>). The dashed line represents the linear fit for the content of Al and Me<sup>n+</sup>.</p>
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<p>The relationship between trace elements and Me<sup>n+</sup> concentration in chrysoberyl samples. (<b>A</b>) The relationship between Me<sup>n+</sup> and Fe. The dashed line represents the linear fit for the content of Fe and Me<sup>n+</sup>; (<b>B</b>) the relationship between Me<sup>n+</sup> and Ti. The dashed line is the approximation of the content of Ti and Me<sup>n+</sup>.</p>
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<p>The UV–Vis–NIR spectra of chrysoberyl sample S3. CIE L*a*b* coordinates of color circles here are calculated under D65 light for a 1 cm wafer thickness to demonstrate color features of chrysoberyl at the different sections of the zoning.</p>
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<p>Laser PL mapping of chrysoberyl sample S3: (<b>A</b>) at 678 nm; (<b>B</b>) at 680 nm; (<b>C</b>) schematic diagram of the test area.</p>
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22 pages, 14390 KiB  
Article
Research on the Weldability and Service Performance of 7075 Aluminum Alloy Welding Wire Prepared by Spray Forming–Extrusion–Drawing
by Chunkai Zhou, Xiaoping Li and Gao Hua
Metals 2024, 14(12), 1443; https://doi.org/10.3390/met14121443 - 17 Dec 2024
Viewed by 129
Abstract
A large number of MIG welding tests were carried out on a 3 mm thick 7075 aluminum alloy plate prepared by the self-developed jet forming–extrusion–drawing process of 7075 high-strength aluminum alloy welding wire, and the welding process of the welding wire and the [...] Read more.
A large number of MIG welding tests were carried out on a 3 mm thick 7075 aluminum alloy plate prepared by the self-developed jet forming–extrusion–drawing process of 7075 high-strength aluminum alloy welding wire, and the welding process of the welding wire and the change in the performance of the welded joint after T6 heat treatment were studied. The results show that the self-developed wire has a good forming joint and a wide welding process window: the welding speed is 5–7 mm/s, and the welding current is 100–150 A. The main precipitated phases in the joint were η(MgZn2), S(CuMgAl2), Mg2Si, and Al13Fe4, which were continuously distributed at the grain boundaries in the form of coarse networks or long strips, which was an important reason for the weak performance of the joints. After the heat treatment of T6, the precipitated phase in the joint was greatly reduced, the element segregation phenomenon was improved, and the residual precipitated phase was mainly Al13Fe4 and a small amount of insoluble phase Fe and Si, and the recrystallization size of the heat-affected zone was refined. Through heat treatment, the average microhardness of the joint was increased from 110 HV to 150.24 HV, and the tensile strength was increased from 326 MPa to 536 MPa, reaching 97.5% of the strength of the base metal, indicating that the softening phenomenon was significantly improved after heat treatment, and the joint had excellent performance. Full article
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<p>Welding schematic diagram and schematic diagram: (<b>a</b>) schematic diagram of welding method; (<b>b</b>) hardness point; (<b>c</b>) tensile specimens; (<b>d</b>) bending specimens.</p>
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<p>Macroscopic formability of the weld.</p>
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<p>Macroscopic morphology results of welds.</p>
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<p>Comparison of weld morphology: (<b>a</b>) 5XXX; (<b>b</b>) 7 XXX.</p>
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<p>Metallographic structure of welded joints: (<b>a</b>) the center of the weld; (<b>b</b>) fusion zone.</p>
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<p>Statistics of joint porosity: (<b>a</b>) porosity of the weld zone; (<b>b</b>) porosity of the fusion zone.</p>
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<p>Metallographic structure of welded joints before heat treatment: (<b>a</b>) fusion zone (100×); (<b>b</b>) weld zone (100×); (<b>c</b>) fusion zone (200×); (<b>d</b>) weld zone (200×).</p>
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<p>Grains in each area of the welded joint after heat treatment: (<b>a</b>) fusion zone (100×); (<b>b</b>) weld zone (100×); (<b>c</b>) fusion zone (200×); (<b>d</b>) weld zone (200×).</p>
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<p>EBSD grain orientation distribution diagrams of the joints before and after heat treatment: (<b>a</b>) fusion zone; (<b>b</b>) fusion zone (T6); (<b>c</b>) weld area; (<b>d</b>) weld zone (T6).</p>
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<p>Grain size distribution of welded joints before and after heat treatment: (<b>a</b>) heat-affected zone; (<b>b</b>) weld zone (<b>c</b>); heat-affected zone (T6); (<b>d</b>) weld zone (T6).</p>
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<p>Grain pole diagram of welded joints before and after heat treatment: (<b>a</b>) fusion zone; (<b>b</b>) weld area; (<b>c</b>) fusion zone (T6); (<b>d</b>) weld zone (T6).</p>
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<p>Grain pole diagram of welded joints before and after heat treatment: (<b>a</b>) fusion zone; (<b>b</b>) weld area; (<b>c</b>) fusion zone (T6); (<b>d</b>) weld zone (T6).</p>
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<p>Phase Diagram of Alloys: (<b>a</b>) Equilibrium diagram of Al-Zn-Mg-Cu series alloys; (<b>b</b>) X-ray diffraction patterns of the weld zone.</p>
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<p>EDS surface scanning of welded joints before and after heat treatment: (<b>a</b>) fusion zone; (<b>b</b>) weld zone (<b>c</b>); fusion zone (T6); (<b>d</b>) weld zone (T6).</p>
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<p>EDS surface scanning of welded joints before and after heat treatment: (<b>a</b>) fusion zone; (<b>b</b>) weld zone (<b>c</b>); fusion zone (T6); (<b>d</b>) weld zone (T6).</p>
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<p>SEM diagram of the precipitated phase of the welded joint before and after heat treatment: (<b>a</b>) fusion zone; (<b>b</b>) fusion zone (T6); (<b>c</b>) fusion zone; (<b>d</b>) weld zone; (<b>e</b>) fusion zone (T6); (<b>f</b>) weld zone (T6).</p>
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<p>The distribution of microhardness of welded joints of non-heat-treated and heat-treated.</p>
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<p>Stress–strain curves.</p>
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<p>Metallographic positions of welded joints after heat treatment.</p>
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<p>Morphology of SEM fractures of welded joints before and after heat treatment: (<b>a</b>,<b>c</b>) fracture morphology before heat treatment; (<b>b</b>,<b>d</b>) fracture morphology after heat treatment.</p>
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<p>Bending specimens of welded joints before and after heat treatment.</p>
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23 pages, 3754 KiB  
Systematic Review
Lymph Node Dissection of Choice in Older Adult Patients with Gastric Cancer: A Systematic Review and Meta-Analysis
by Camilo Ramírez-Giraldo, Violeta Avendaño-Morales, Isabella Van-Londoño, Daniela Melo-Leal, María Isabel Camargo-Areyanes, Luis Carlos Venegas-Sanabria, Juan Pablo Vargas Vargas, Edgar Javier Aguirre-Salamanca and Andrés Isaza-Restrepo
J. Clin. Med. 2024, 13(24), 7678; https://doi.org/10.3390/jcm13247678 - 17 Dec 2024
Viewed by 206
Abstract
Background: Although the current literature has shown an increasing interest in surgical treatment of gastric cancer (GC) in older adults in recent years, there is still no consensus on proper management in this subgroup of patients. This study was designed with the objective [...] Read more.
Background: Although the current literature has shown an increasing interest in surgical treatment of gastric cancer (GC) in older adults in recent years, there is still no consensus on proper management in this subgroup of patients. This study was designed with the objective of evaluating the current evidence that compares limited lymph node dissection with extended lymph node dissection in older adult patients (≥65 years) coursing with resectable GC. Methods: A systematic review of PubMed, Cochrane library, and ScienceDirect was performed according to PRISMA guidelines. All studies before 2018 were selected using a systematic review by Mogal et al. Studies were eligible for this meta-analysis if they were randomized controlled trials or non-randomized comparative studies comparing limited lymph node dissection versus extended lymph node dissection in patients with resectable GC taken to gastrectomy. Results: Seventeen studies and a total of 5056 patients were included. There were not any statistically significant differences in OS (HR = 1.04, CI95% = 0.72–1.51), RFS (HR = 0.92, CI95% = 0.62–1.38), or CSS (HR = 1.24, CI95% = 0.74–2.10) between older adult patients taken to limited and extended lymphadenectomy in addition to gastrectomy as the current surgical treatment for GC. Although a higher rate of major complications was observed in the extended lymphadenectomy group, this difference was not statistically significant in incidence between both groups of patients (OR = 1.92, CI95% = 0.75–4.91). Conclusions: Limited lymphadenectomy must be considered as the better recommendation for surgical treatment for GC in older adult patients, considering the oncological outcomes and lower rates of complications compared with more radical lymph node dissections. Full article
(This article belongs to the Section Gastroenterology & Hepatopancreatobiliary Medicine)
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<p>Flowchart representing information flow in each different stage of this systematic revision using PRISMA.</p>
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<p>Forest plot for OS comparing limited versus extended lymphadenectomy [<a href="#B4-jcm-13-07678" class="html-bibr">4</a>,<a href="#B17-jcm-13-07678" class="html-bibr">17</a>,<a href="#B18-jcm-13-07678" class="html-bibr">18</a>,<a href="#B70-jcm-13-07678" class="html-bibr">70</a>,<a href="#B71-jcm-13-07678" class="html-bibr">71</a>,<a href="#B72-jcm-13-07678" class="html-bibr">72</a>].</p>
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<p>Forest plot for RFS comparing limited versus extended lymphadenectomy [<a href="#B4-jcm-13-07678" class="html-bibr">4</a>,<a href="#B17-jcm-13-07678" class="html-bibr">17</a>,<a href="#B18-jcm-13-07678" class="html-bibr">18</a>,<a href="#B70-jcm-13-07678" class="html-bibr">70</a>].</p>
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<p>Forest plot for CSS comparing limited versus extended lymphadenectomy [<a href="#B4-jcm-13-07678" class="html-bibr">4</a>,<a href="#B17-jcm-13-07678" class="html-bibr">17</a>,<a href="#B70-jcm-13-07678" class="html-bibr">70</a>,<a href="#B71-jcm-13-07678" class="html-bibr">71</a>,<a href="#B72-jcm-13-07678" class="html-bibr">72</a>].</p>
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<p>Forest plot for complications with Clavien–Dindo ≥ 3 comparing limited versus extended lymphadenectomy [<a href="#B4-jcm-13-07678" class="html-bibr">4</a>,<a href="#B17-jcm-13-07678" class="html-bibr">17</a>,<a href="#B18-jcm-13-07678" class="html-bibr">18</a>,<a href="#B70-jcm-13-07678" class="html-bibr">70</a>,<a href="#B71-jcm-13-07678" class="html-bibr">71</a>,<a href="#B72-jcm-13-07678" class="html-bibr">72</a>].</p>
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<p>Forest plot for age as a risk factor for OS [<a href="#B69-jcm-13-07678" class="html-bibr">69</a>,<a href="#B73-jcm-13-07678" class="html-bibr">73</a>,<a href="#B76-jcm-13-07678" class="html-bibr">76</a>,<a href="#B77-jcm-13-07678" class="html-bibr">77</a>,<a href="#B81-jcm-13-07678" class="html-bibr">81</a>,<a href="#B82-jcm-13-07678" class="html-bibr">82</a>,<a href="#B83-jcm-13-07678" class="html-bibr">83</a>,<a href="#B84-jcm-13-07678" class="html-bibr">84</a>,<a href="#B85-jcm-13-07678" class="html-bibr">85</a>,<a href="#B86-jcm-13-07678" class="html-bibr">86</a>].</p>
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1 pages, 137 KiB  
Retraction
RETRACTED: Choi et al. Distribution Pattern and Brood Parasitism Characteristics of an Endangered Fish, Pseudopungtungia nigra, in the Geum River Basin, South Korea. Fishes 2022, 7, 321
by Jong-Yun Choi, Hany Chang and Seong-Ki Kim
Fishes 2024, 9(12), 518; https://doi.org/10.3390/fishes9120518 - 17 Dec 2024
Viewed by 40
Abstract
The journal Fishes retracts the article titled “Distribution Pattern and Brood Parasitism Characteristics of an Endangered Fish, Pseudopungtungia nigra, in the Geum River Basin, South Korea” [...] Full article
5 pages, 1451 KiB  
Correction
Correction: Kim et al. Spatial Distribution Pattern of the Mesozooplankton Community in Ross Sea Region Marine Protected Area (RSR MPA) during Summer. Diversity 2024, 16, 174
by Sung Hoon Kim, Wuju Son, Jeong-Hoon Kim and Hyoung Sul La
Diversity 2024, 16(12), 766; https://doi.org/10.3390/d16120766 - 17 Dec 2024
Viewed by 81
Abstract
The authors realized that there were critical inaccuracies in their environmental data analysis, specifically related to chlorophyll (chl) and nutrient concentrations [...] Full article
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<p>Spatial pattern of the surface environmental parameters in the RSR MPA.</p>
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<p>Spatial pattern of the average environmental parameters in the RSR MPA.</p>
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<p>Canonical analysis of principal coordinates (CAP) plots according to the mesozooplankton abundance data showing correlations with the dominant species (<b>A</b>) and environmental parameters (<b>B</b>). Ai, Appendicularia indet.; Ca, <span class="html-italic">Calanoides acutus</span>; Cn, Cirriped nauplius; Cp, <span class="html-italic">Calanus propinquus</span>; Ec, <span class="html-italic">Euphausia</span> calyptopis; Fl, Fish larvae; Lr, <span class="html-italic">Limacina rangii</span>; Mg, <span class="html-italic">Metridia gerlachei</span>; Oi, Ostracoda indet.; Os, <span class="html-italic">Oithona</span> spp.; Pa, <span class="html-italic">Paraeuchaeta antarctica</span>; Pl, Polychaeta larvae; Ss, <span class="html-italic">Sagitta</span> sp.; S2, Siphonophore 2; Ta, <span class="html-italic">Triconia antarctica</span>.</p>
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