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17 pages, 5987 KiB  
Article
Towards Mineralogy 4.0? Atlas of 3D Rocks and Minerals: Digitally Archiving Interactive and Immersive 3D Data for Rocks and Minerals
by Andrei Ionuţ Apopei
Minerals 2024, 14(12), 1196; https://doi.org/10.3390/min14121196 (registering DOI) - 24 Nov 2024
Abstract
Mineralogy 4.0 can play a significant role in the future of geological research, education, and exploration by providing a more comprehensive and interactive understanding of rocks and minerals. This paper explores the application of digital photogrammetry and augmented reality (AR) technologies as part [...] Read more.
Mineralogy 4.0 can play a significant role in the future of geological research, education, and exploration by providing a more comprehensive and interactive understanding of rocks and minerals. This paper explores the application of digital photogrammetry and augmented reality (AR) technologies as part of Mineralogy 4.0. An atlas of 3D rocks and minerals with 915 high-quality models was created to showcase the potential of photogrammetry in the mineral sciences. The repository contains a wide range of sample types, featuring transparency, metallic luster, fluorescence, or millimetric-scale crystals. The three-dimensional rocks and minerals can also be accessed on-the-go through a mobile application that was developed for Android devices. Additionally, web applications have been developed with specific three-dimensional collections as well as three-dimensional storytelling. AR technology was also integrated into the 3D repository, allowing users to superimpose virtual 3D models of rocks and minerals onto real-world surfaces through their device’s camera. Also, a digital solution with 3D holograms of rocks and minerals was effectively implemented to provide an interactive and immersive experience. The 3D datasets of rocks and minerals can play a significant role in the geoscience community’s research, developing not only in-depth knowledge of specimens but also opening new frontiers in mineral sciences, leading towards a more advanced era of mineralogy. Full article
(This article belongs to the Special Issue Geomaterials and Cultural Heritage)
16 pages, 6496 KiB  
Article
Study on the Effects of CeO2 on the Micro-Structure and Wear Resistance of CuCrZr Plasma Cladding Coatings
by Yang Wang, Hongjun Xiang, Genrong Cao, Zhiming Qiao, Qing’ao Lv, Xichao Yuan, Chunyan Liang and Qirui Wang
Lubricants 2024, 12(12), 409; https://doi.org/10.3390/lubricants12120409 (registering DOI) - 24 Nov 2024
Abstract
The electromagnetic railgun, a novel kinetic energy weapon, has found utility in military operations due to its enhanced safety features and superior precision. This study investigates the enhancement of wear resistance in CuCrZr rails through the plasma cladding of CuCrZr-CeO2 coatings with [...] Read more.
The electromagnetic railgun, a novel kinetic energy weapon, has found utility in military operations due to its enhanced safety features and superior precision. This study investigates the enhancement of wear resistance in CuCrZr rails through the plasma cladding of CuCrZr-CeO2 coatings with a varying Cerium dioxide (CeO2) content. To enhance the wear resistance of the CuCrZr track, plasma cladding of CuCrZr-CeO2 coatings with varying CeO2 content was investigated. The impact of CeO2 content (0%, 0.1%, 0.15%, 0.2%, 0.25%, 0.3%) on the microstructure, phase composition, and mechanical properties of the CuCrZr coating was assessed using scanning electron microscopy (SEM), X-ray diffraction (XRD), EDS(Energy Dispersive Spectrometer) surface scanning, friction and wear tests, and hardness analysis. The findings indicate that a CeO2 content of 0.15% leads to a transition in the coating’s microstructure from columnar to equiaxed crystals, with the densest grain structure. Beyond 0.15% CeO2, pore defects in the coating increase, compromising mechanical properties. The coating containing 0.15% CeO2 exhibits optimal performance, with a hardness of 75.3, representing a 5.31% increase compared to CeO2-free CuCrZr coatings. Under a 10 N load, the friction coefficient decreases by approximately 17.9% to about 0.64. Moreover, the minimum wear mass is reduced by 44.7% to 3.87 mg. The aforementioned research findings hold immense importance in extending the lifespan of the electromagnetic railgun and improving its operational efficiency. Full article
19 pages, 17860 KiB  
Article
The Petrogenesis of Devonian Volcanism and Its Tectonic Significance in the Kalatag Area, Eastern Tianshan, Xinjiang, China
by Zhijie Ma, Fengmei Chai, Mingjian Cao, Xiaodong Song, Haipei Wang, Dongmei Qi and Qigui Mao
Minerals 2024, 14(12), 1195; https://doi.org/10.3390/min14121195 (registering DOI) - 24 Nov 2024
Abstract
The Kalatag mineralization belt is an important metallogenic belt of polymetallic mineral deposits in the northern part of eastern Tianshan, and its age and tectonic setting are still controversial. We identified a set of Devonian volcanic rocks hosted in the Early Palaeozoic package [...] Read more.
The Kalatag mineralization belt is an important metallogenic belt of polymetallic mineral deposits in the northern part of eastern Tianshan, and its age and tectonic setting are still controversial. We identified a set of Devonian volcanic rocks hosted in the Early Palaeozoic package of dominantly marine sediments with a small amount of terrestrial rocks. This study presents petrological, U–Pb geochronology, and geochemical data for the volcanic rocks. The ages of the rhyolite (407.2 ± 1.9 Ma) and basaltic andesite (380.4 ± 2.8 Ma) suggests that the Kalatag belt is a Devonian volcanic succession. These rocks consist mainly of marine calc–alkaline lava, tuff, pyroclastic rocks, and minor terrestrial basaltic andesite. The lavas are characterized by the enrichment of light rare earth elements and strongly depleted in Nb and Ta, typical of island arc magmatic rocks. The volcanic rocks probably originated from the partial melting of the mafic lower crust which was modified by subducted slab-related fluids. During their ascent through the crust, these volcanic rocks underwent variable extents of fractional crystallization (rhyolites) and crustal contamination (basaltic andesites). Combined with the results of previous studies, we suggest that the Devonian rocks formed in an island arc related to the northward subduction of the Northern Tianshan Ocean with a crustal thickness of ~35–40 km. Full article
(This article belongs to the Section Mineral Geochemistry and Geochronology)
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Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>(<b>A</b>) Schematic tectonic map of central Asia [<a href="#B1-minerals-14-01195" class="html-bibr">1</a>,<a href="#B3-minerals-14-01195" class="html-bibr">3</a>] showing the position of eastern Tianshan in part B. (<b>B</b>) Schematic geological map of eastern Tianshan (modified after [<a href="#B18-minerals-14-01195" class="html-bibr">18</a>]) showing the location of Kalatag within the Turpan basin. The major faults and tectonic units are divided into south Tianshan, central Tianshan, the Yamansu arc, the Dananhu–Haerlik arc, and the Angaran margin.</p>
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<p>Geological map of the Kalatag inlier showing stratigraphic, magmatic, and structural features. The isotopic ages of formation are given as a key of magmatic rocks in the arc. The location of sample sites with their isotopic ages are marked. Modified after [<a href="#B18-minerals-14-01195" class="html-bibr">18</a>].</p>
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<p>Geological section of the Kalatag core showing the Devonian volcanic rock types and their relationship with Ordovician–Silurian volcanic rocks.</p>
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<p>Columnar diagram and typical photographs of Devonian stratigraphy in Kalatag inlier. (<b>A</b>): Convoluted lamination in tuffs. (<b>B</b>): Rhyolitic structure. (<b>C</b>): Conformable contact between tuffaceous sandstone and dacite. (<b>D</b>): Bedding structure. (<b>E</b>): Maroon basaltic andesite. (<b>F</b>): Volcanic flame structure in basaltic andesite. (<b>G</b>): Bedding structure composed of sandstone and mudstone. (<b>H</b>): Volcanic breccia in tuffs. (<b>I</b>): Directional arrangement of infill in amygdaloidal andesite. (<b>J</b>): Gray–green breccia tuff. (<b>K</b>): Amygdaloid andesite.</p>
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<p>Representative hand specimen and photomicrographs of Devonian volcanic rocks in Kalatag inlier. (<b>A</b>–<b>C</b>) Rhyolite. (<b>D</b>–<b>F</b>) Dacite. (<b>G</b>–<b>I</b>) Basaltic andesite. (<b>J</b>–<b>L</b>) Andesite. (<b>M</b>–<b>O</b>) Amygdaloidal andesite. Abbreviations: Cpx = clinopyroxene; Hbl = hornblende; Ab = albite; And = andesine; Qtz = quartz; Chl = chlorite. Symbols: (–), polarized light; (+), orthogonal light.</p>
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<p>Representative cathodoluminescence images of measured zircons with concordia diagrams and weighting diagrams for rhyolite (<b>A</b>,<b>B</b>) and basaltic andesite (<b>C</b>,<b>D</b>) of Devonian rock in Kalatag inlier.</p>
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<p>Binary plot of the LOI versus active elements for the Devonian volcanic rocks of the Kalatag inlier, with basaltic andesite having a high LOI, implicating strong alteration.</p>
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<p>Discrimination diagrams for the main Devonian volcanic rocks in the Kalatag inlier. (<b>A</b>) Zr/TiO<sub>2</sub> vs. Nb/Y [<a href="#B32-minerals-14-01195" class="html-bibr">32</a>]; (<b>B</b>) Th vs. Co [<a href="#B33-minerals-14-01195" class="html-bibr">33</a>].</p>
Full article ">Figure 9
<p>Binary diagrams clearly show the correlations of SiO₂ with the major and trace elements of the Devonian volcanic rocks in the Kalatag inlier. Values are given in wt% for oxides and in ppm for trace elements.</p>
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<p>Chondrite-normalized REE diagrams (<b>A</b>,<b>C</b>) and primitive mantle-normalized trace element diagrams (<b>B</b>,<b>D</b>) for the main Devonian volcanic rocks in the Kalatag inlier. Data for the average chondrite, primitive mantle, enriched MORB (E–MORB), normal MORB (N–MORB), ocean island basalt (OIB), upper crust, and lower crust are from [<a href="#B34-minerals-14-01195" class="html-bibr">34</a>].</p>
Full article ">Figure 11
<p>Diagrams of Devonian volcanic petrogenesis and magma source characterization. (<b>A</b>) La/Sm vs. La [<a href="#B37-minerals-14-01195" class="html-bibr">37</a>]. (<b>B</b>) La/Ba vs. La/Nb [<a href="#B25-minerals-14-01195" class="html-bibr">25</a>]. (<b>C</b>) Ba/Th vs. Th/Nb [<a href="#B40-minerals-14-01195" class="html-bibr">40</a>]. (<b>D</b>) La/Sm vs. Sm/Yb [<a href="#B42-minerals-14-01195" class="html-bibr">42</a>]. (PYX = pyroxene-dominated; AMPH = amphibole-dominated; GAR = garnet-dominated.)</p>
Full article ">Figure 12
<p>Tectonic discrimination diagrams for the Devonian volcanic rocks in Kalatag. (<b>A</b>) Th/Yb vs. Nb/Yb [<a href="#B35-minerals-14-01195" class="html-bibr">35</a>]; (<b>B</b>) Hf/3–Th–Ta [<a href="#B45-minerals-14-01195" class="html-bibr">45</a>]; (<b>C</b>) lg (Eu/Pb) vs. lg (TFe/Ga) [<a href="#B46-minerals-14-01195" class="html-bibr">46</a>]; (<b>D</b>) Nb vs. Y [<a href="#B45-minerals-14-01195" class="html-bibr">45</a>]. Abbreviations: E–MORB = enriched mid-ocean ridge basalt; N–MORB = normal mid-ocean ridge basalt; OIB = oceanic island basalt.</p>
Full article ">Figure 13
<p>Schematic diagram showing the geodynamic setting of the Dananhu–Haerlik arc during the Devonian period. (<b>A</b>) The acidic volcanic rocks erupted in the marine facies at ~407 Ma. (<b>B</b>) Basaltic andesite eruptions in terrestrial facies at ~380 Ma. (<b>C</b>) Andesitic rocks erupted in the marine facies at &lt;380 Ma.</p>
Full article ">
17 pages, 7710 KiB  
Article
Tribological Properties of SPS Reactive Sintered Al/MoS2 Composites
by Marek Kostecki, Krzysztof Kulikowski, Dorota Moszczyńska and Andrzej Roman Olszyna
Metals 2024, 14(12), 1326; https://doi.org/10.3390/met14121326 (registering DOI) - 24 Nov 2024
Viewed by 108
Abstract
In search of opportunities to improve mechanical properties and abrasion resistance, composites based on aluminum reinforced with MoS2 particles were produced. The authors’ previous research indicated the possibility of obtaining hard dispersion precipitates of the Al12Mo intermetallic phase as a [...] Read more.
In search of opportunities to improve mechanical properties and abrasion resistance, composites based on aluminum reinforced with MoS2 particles were produced. The authors’ previous research indicated the possibility of obtaining hard dispersion precipitates of the Al12Mo intermetallic phase as a result of the reaction of the composite components at a temperature exceeding 550 °C during the SPS (Spark Plasma Sintering) process. This work focused on optimizing the SPS consolidation process and assessing the microstructure and mechanical properties of the obtained materials. A series of experiments proved that by increasing the amount of the strengthening phase and increasing the process temperature, a significant amount of Al12Mo and Al5Mo strengthening phases is produced. Exceptionally good dispersion of reinforcing particles and the presence of layered MoS2 crystals, while ensuring optimal parameters of the synthesis process, lead to a change in friction mechanisms and improved abrasion resistance through an approximately 30-fold decrease in the wear factor. Full article
(This article belongs to the Special Issue Feature Papers in Metal Matrix Composites—2nd Edition)
Show Figures

Figure 1

Figure 1
<p>Powder morphologies of (<b>a</b>) MoS<sub>2</sub> and (<b>b</b>) Al+ MoS<sub>2</sub> 10% vol. mixture.</p>
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<p>Microstructure of Al+ 5% vol. MoS<sub>2</sub> sinters obtained at (<b>a</b>) 600 °C and (<b>b</b>) 650 °C (sintering time 4 min.).</p>
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<p>Microstructure of Al+ 10% vol. MoS<sub>2</sub> sinters obtained at (<b>a</b>) 600 °C and (<b>b</b>) 650 °C (sintering time 16 min.).</p>
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<p>Diffraction pattern of the Al + 10% vol. MoS<sub>2</sub>. sample sintered at 650 °C (10 min.).</p>
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<p>Microstructure of Al+ 10% vol. MoS<sub>2</sub> sinter (650 °C/16 min): (<b>a</b>) precipitation of the intermetallic phase inside Al grains and (<b>b</b>) MoS<sub>2</sub> flakes on the boundary of the powder particles.</p>
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<p>Apparent density of the Al/MoS<sub>2</sub> sinters.</p>
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<p>Open porosity of Al/MoS<sub>2</sub> sinters.</p>
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<p>Vickers hardness HV2 of Al/MoS<sub>2</sub> sinters.</p>
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<p>The course of changes in the friction coefficient during the wear resistance test of Al/MoS<sub>2</sub> composites.</p>
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<p>Average friction coefficient in the steady-state friction (range 200–1000 revolutions) of Al/MoS<sub>2</sub> composites.</p>
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<p>SEM micrographs of worn surfaces of Al-10% vol. MoS<sub>2</sub> composite sintered at 550 °C; (<b>a</b>–<b>c</b>) show different magnification of the same spot.</p>
Full article ">Figure 12
<p>SEM micrographs of worn surfaces of Al-10% vol. MoS<sub>2</sub> composite sintered at 600 °C; (<b>a</b>–<b>c</b>) show different magnification of the same spot.</p>
Full article ">Figure 13
<p>SEM micrographs of worn surfaces of Al-10% vol. MoS<sub>2</sub> composite sintered at 650 °C; (<b>a</b>–<b>c</b>) show different magnification of the same spot.</p>
Full article ">Figure 14
<p>Material consumption rates during the ball-on-disc test of Al/MoS<sub>2</sub> composites.</p>
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<p>Surface topography of the wear traces from the ball-on-disc method of Al-10% vol. MoS<sub>2</sub> composites sintered at various temperatures.</p>
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<p>Wear track cross-section profiles after ball-on-disc tests of Al-10% vol. MoS<sub>2</sub> composites.</p>
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<p>SEM micrographs of the worn surfaces of Al-5% vol. MoS<sub>2</sub> composite, sintered at 600 °C; (<b>a</b>–<b>c</b>) show different magnification of the same spot.</p>
Full article ">Figure 18
<p>SEM micrographs of worn surfaces of Al-5% vol. MoS<sub>2</sub> composite, sintered at 650 °C; (<b>a</b>–<b>c</b>) show different magnification of the same spot.</p>
Full article ">
15 pages, 10816 KiB  
Article
Naphthalene-Containing Epoxy Resin: Phase Structure, Rheology, and Thermophysical Properties
by Svetlana O. Ilyina, Irina Y. Gorbunova, Anastasiya Y. Yadykova, Anna V. Vlasova, Michael L. Kerber and Sergey O. Ilyin
Polymers 2024, 16(23), 3264; https://doi.org/10.3390/polym16233264 (registering DOI) - 24 Nov 2024
Viewed by 152
Abstract
Naphthalene is a fungicide that can also be a phase-change agent owing to its high crystallization enthalpy at about 80 °C. The relatively rapid evaporation of naphthalene as a fungicide and its shape instability after melting are problems solved in this work by [...] Read more.
Naphthalene is a fungicide that can also be a phase-change agent owing to its high crystallization enthalpy at about 80 °C. The relatively rapid evaporation of naphthalene as a fungicide and its shape instability after melting are problems solved in this work by its placement into a cured epoxy matrix. The work’s research materials included diglycidyl ether of bisphenol A as an epoxy resin, 4,4′-diaminodiphenyl sulfone as its hardener, and naphthalene as a phase-change agent or a fungicide. Their miscibility was investigated by laser interferometry, the rheological properties of their blends before and during the curing by rotational rheometry, the thermophysical features of the curing process and the resulting phase-change materials by differential scanning calorimetry, and the blends’ morphologies by transmission optical and scanning electron microscopies. Naphthalene and epoxy resin were miscible when heated above 80 °C. This fact allowed obtaining highly concentrated mixtures containing up to 60% naphthalene by high-temperature homogeneous curing with 4,4′-diaminodiphenyl sulfone. The initial solubility of naphthalene was only 19% in uncured epoxy resin but increased strongly upon heating, reducing the viscosity of the reaction mixture, delaying its gelation, and slowing cross-linking. At 20–40% mass fraction of naphthalene, it almost entirely retained its dissolved state after cross-linking as a metastable solution, causing plasticization of the cured epoxy polymer and lowering its glass transition temperature. At 60% naphthalene, about half dissolved within the cured polymer, while the other half formed coarse particles capable of crystallization and thermal energy storage. In summary, the resulting phase-change material stored 42.6 J/g of thermal energy within 62–90 °C and had a glass transition temperature of 46.4 °C at a maximum naphthalene mass fraction of 60% within the epoxy matrix. Full article
(This article belongs to the Special Issue Epoxy Resins and Epoxy-Resins-Based Polymer Materials II)
Show Figures

Figure 1

Figure 1
<p>Interferograms of a mutual diffusion zone of naphthalene (<b>left</b>) and epoxy resin (<b>right</b>) during sequential heating to 40 (<b>a</b>), 58 (<b>b</b>), and 82 °C (<b>c</b>) and then cooling to 28 °C (<b>d</b>).</p>
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<p>Phase diagram for mixtures of epoxy resin and naphthalene.</p>
Full article ">Figure 3
<p>Dependences of viscosity on shear rate (<b>a</b>) and storage and loss moduli on angular frequency (<b>b</b>) for mixtures of epoxy resin, hardener, and naphthalene at 25 °C. The legends indicate the mass fraction of naphthalene.</p>
Full article ">Figure 4
<p>Viscosity during the curing of epoxy compositions in the mode of smooth temperature increase at a rate of 2 °C/min with a shear rate of 100 s<sup>−1</sup> in normal (<b>a</b>) and reciprocal (<b>b</b>) coordinates. The legends indicate the mass fraction of naphthalene.</p>
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<p>Heat flow during the curing of epoxy compositions at a heating rate of 2 °C/min. The legend indicates the mass fraction of naphthalene.</p>
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<p>DSC thermograms of cured epoxy compositions containing naphthalene whose mass fraction is near the curves. The arrows indicate glass transitions. The inset shows data for pure naphthalene.</p>
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<p>Microphotographs in a thin layer of cured epoxy compositions containing naphthalene whose mass fraction is indicated.</p>
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<p>SEM images of the cross-sectional areas of cured epoxy compositions containing naphthalene whose mass fraction is indicated.</p>
Full article ">
18 pages, 3841 KiB  
Article
The New Interpretation of the Photothermal Spectra of CdTe Samples After Different Surface Treatments
by Jacek Zakrzewski, Mirosław Maliński, Mohammed Boumhamdi, Janusz Strzelecki and Karol Strzałkowski
Crystals 2024, 14(12), 1019; https://doi.org/10.3390/cryst14121019 (registering DOI) - 24 Nov 2024
Viewed by 239
Abstract
This article presents new research on the surface condition of bulk crystal samples after the following stages of surface treatment: grinding, polishing, and etching. Furthermore, it shows how the surface condition affects the photothermal signal’s spectral amplitude and phase characteristics (PZE). A new [...] Read more.
This article presents new research on the surface condition of bulk crystal samples after the following stages of surface treatment: grinding, polishing, and etching. Furthermore, it shows how the surface condition affects the photothermal signal’s spectral amplitude and phase characteristics (PZE). A new theoretical interpretation of the photothermal spectra of CdTe samples after different surface treatments is proposed. We demonstrate that the piezoelectric method is susceptible to the surface condition, and it allows for the estimation of the thickness of surface-damaged layers of samples, and for the analysis of their thermal parameters. The roughness of surfaces obtained from the AFM pictures is estimated and compared to the photothermal results. Full article
(This article belongs to the Section Inorganic Crystalline Materials)
Show Figures

Figure 1

Figure 1
<p>Theoretical amplitude PZE spectra for three thicknesses of the damaged surface layer; description of the lines: continuous <span class="html-italic">l</span> = 0 μm, dashed <span class="html-italic">l</span> = 1 μm, dash-dot <span class="html-italic">l</span> = 2 μm.</p>
Full article ">Figure 2
<p>Theoretical phase PZE spectra—for three thicknesses of the damaged surface layer; description of the lines: continuous <span class="html-italic">l</span> = 0 μm, dashed <span class="html-italic">l</span> = 1 μm, dash-dot <span class="html-italic">l</span> = 2 μm.</p>
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<p>Theoretical amplitude PZE spectra for several surface layer thicknesses. Line description: continuous <span class="html-italic">l</span> = 0 μm, dashed <span class="html-italic">l</span> = 0.1 μm, dash-dot <span class="html-italic">l</span> = 0.3 μm.</p>
Full article ">Figure 4
<p>Theoretical phase PZE spectra for several surface layer thicknesses. Line description: continuous <span class="html-italic">l</span> = 0 μm, dashed <span class="html-italic">l</span> = 0.1 μm, dash-dot <span class="html-italic">l</span> = 0.3 μm.</p>
Full article ">Figure 5
<p>The amplitude (<b>a</b>) and phase (<b>b</b>) spectra of CdTe for the ground sample were measured for different frequencies (back—12 Hz, red—76 Hz, green—126 Hz, blue—226 Hz.</p>
Full article ">Figure 6
<p>Experimental amplitude (<b>a</b>) and phase (<b>b</b>) PZE spectra of CdTe after different surface treatments at <span class="html-italic">f</span> = 126 Hz. Green line—ground sample, red line—polished sample, black line—etched sample.</p>
Full article ">Figure 7
<p>Experimental and theoretical amplitude and phase PZE spectra of CdTe samples measured at <span class="html-italic">f</span> = 126 Hz. Circles are experimental data; solid lines are theoretical characteristics for different cases: (<b>a</b>) amplitude PZE spectrum after grinding and the surface layer thickness <span class="html-italic">l</span> = 4.5 µm. (<b>b</b>) phase PZE spectrum after grinding and the surface layer thickness <span class="html-italic">l</span> = 4.5 µm. (<b>c</b>) amplitude PZE spectrum after polishing and the surface layer thickness <span class="html-italic">l</span> = 3.2 µm. (<b>d</b>) phase PZE spectrum after polishing and the surface layer thickness <span class="html-italic">l</span> = 3.2 µm. (<b>e</b>) amplitude PZE spectrum after etching and the thickness of the layer <span class="html-italic">l</span> = 0.12 µm. (<b>f</b>) phase PZE spectrum after etching and the thickness of the layer <span class="html-italic">l</span> = 0.12 µm.</p>
Full article ">Figure 7 Cont.
<p>Experimental and theoretical amplitude and phase PZE spectra of CdTe samples measured at <span class="html-italic">f</span> = 126 Hz. Circles are experimental data; solid lines are theoretical characteristics for different cases: (<b>a</b>) amplitude PZE spectrum after grinding and the surface layer thickness <span class="html-italic">l</span> = 4.5 µm. (<b>b</b>) phase PZE spectrum after grinding and the surface layer thickness <span class="html-italic">l</span> = 4.5 µm. (<b>c</b>) amplitude PZE spectrum after polishing and the surface layer thickness <span class="html-italic">l</span> = 3.2 µm. (<b>d</b>) phase PZE spectrum after polishing and the surface layer thickness <span class="html-italic">l</span> = 3.2 µm. (<b>e</b>) amplitude PZE spectrum after etching and the thickness of the layer <span class="html-italic">l</span> = 0.12 µm. (<b>f</b>) phase PZE spectrum after etching and the thickness of the layer <span class="html-italic">l</span> = 0.12 µm.</p>
Full article ">Figure 7 Cont.
<p>Experimental and theoretical amplitude and phase PZE spectra of CdTe samples measured at <span class="html-italic">f</span> = 126 Hz. Circles are experimental data; solid lines are theoretical characteristics for different cases: (<b>a</b>) amplitude PZE spectrum after grinding and the surface layer thickness <span class="html-italic">l</span> = 4.5 µm. (<b>b</b>) phase PZE spectrum after grinding and the surface layer thickness <span class="html-italic">l</span> = 4.5 µm. (<b>c</b>) amplitude PZE spectrum after polishing and the surface layer thickness <span class="html-italic">l</span> = 3.2 µm. (<b>d</b>) phase PZE spectrum after polishing and the surface layer thickness <span class="html-italic">l</span> = 3.2 µm. (<b>e</b>) amplitude PZE spectrum after etching and the thickness of the layer <span class="html-italic">l</span> = 0.12 µm. (<b>f</b>) phase PZE spectrum after etching and the thickness of the layer <span class="html-italic">l</span> = 0.12 µm.</p>
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<p>Experimental and theoretical amplitude and phase PZE spectra of CdTe-etched samples measured in the front configuration at <span class="html-italic">f</span> = 12 Hz. Circles are experimental data; solid lines are theoretical characteristics. Fitting parameters: <span class="html-italic">E<sub>g</sub></span> = 1.50 eV, <span class="html-italic">l</span> = 0.15 µm, <span class="html-italic">α</span><sub>2</sub> = <span class="html-italic">α</span><sub>1</sub>/50, <span class="html-italic">λ</span><sub>2</sub> = <span class="html-italic">λ</span><sub>1</sub>/1.</p>
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<p>Experimental and theoretical amplitude and phase PZE spectra of etched CdTe samples measured in the front configuration at <span class="html-italic">f</span> = 12 Hz. Circles are experimental data; solid lines are theoretical characteristics.</p>
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<p>AFM images of one of the selected areas for polished samples.</p>
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<p>AFM images of one of the selected areas for etched samples.</p>
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<p>The cross-section for the sample after etching. The roughness and the thickness of the damaged sample are presented.</p>
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19 pages, 1248 KiB  
Article
Atomic Force Microscopy as a Means to Analyze Vickers Indentation Experiments: Crack Morphology, Fracture Toughness, and Indentation Profile
by Patricia Vivanco-Chávez, Michael Klichowicz, Oleg Popov, Holger Lieberwirth, Gerhard Heide and Florian Mertens
Minerals 2024, 14(12), 1193; https://doi.org/10.3390/min14121193 (registering DOI) - 23 Nov 2024
Viewed by 263
Abstract
Studies of micro/nanoscale mechanical properties of materials are scarce and the determination of the corresponding parameters such as fracture toughness (KIC) and Vickers hardness number (HV) at those scales remains a challenge. In the presented work, a methodological approach was [...] Read more.
Studies of micro/nanoscale mechanical properties of materials are scarce and the determination of the corresponding parameters such as fracture toughness (KIC) and Vickers hardness number (HV) at those scales remains a challenge. In the presented work, a methodological approach was applied that provides detailed insight on the elastic/plastic behavior of minerals subjected to Vickers indentation experiments. In this research, five samples were analyzed: one fused silica sample (reference material), two synthetic quartz crystals (differently cut, SQ and SQX), and two quartz grains from polished sections of granite and granodiorite rock. The applied methodology was predominantly based on qualitative and quantitative morphology measurements by Atomic Force Microscopy (AFM). This analysis shows the dominant presence of either Primary Radial Cracks (PRC) or Secondary Radial Cracks (SRC) in both natural (mineral) quartz grains and synthetic quartz crystals, and Cone Cracks (CC) in fused silica. Moreover, the parameters associated with the indentation (e.g., length of the cracks, the depth of residual indentation, and the indentation mark size) allowed the reconstruction of the indentation profile model and the determination of KIC and HV with enhanced accuracy. Full article
10 pages, 521 KiB  
Article
Carbon Dioxide Hydrate Formation in Porous Media Under Dynamic Conditions for CO2 Storage in Low-Temperature Water Zones
by Md Nahin Mahmood, Muhammad Towhidul Islam and Boyun Guo
Appl. Sci. 2024, 14(23), 10860; https://doi.org/10.3390/app142310860 (registering DOI) - 23 Nov 2024
Viewed by 331
Abstract
Injecting carbon dioxide (CO2) into subsea water zones, where the in situ temperatures are below the hydrate-forming temperature of CO2, has been recently proposed to lock CO2 inside the water zones in a solid hydrate form. It is [...] Read more.
Injecting carbon dioxide (CO2) into subsea water zones, where the in situ temperatures are below the hydrate-forming temperature of CO2, has been recently proposed to lock CO2 inside the water zones in a solid hydrate form. It is a common concern that CO2 may form hydrates during the injection period, which would reduce well injectivity. CO2 injection into sandstone cores under simulated subsea temperatures ranging from 0 °C to 5 °C was investigated in this study. Experimental results show that flowing CO2 at Darcy velocity 0.033 cm/s begins to form hydrate in the sandstone core at dynamic pressures higher than the minimum required pressure under static conditions. At temperatures changing from 0 °C to 5 °C, the observed hydrate-forming pressure changes from 1.87 to 2.5 times the pressures required for CO2 hydrates under static conditions. The reason why the required minimum pressure for CO2 to form hydrates in dynamic conditions is higher than that in static conditions is attributed to the shear rate effect of flowing fluids that should slow down the growth of hydrate crystals and/or break down formed hydrate films in the dynamic conditions. Therefore, higher pressure energy, or fugacity, is required to promote the growth of hydrate crystals and hydrate films in dynamic conditions. More rigorous investigations in this area are needed in the future. Full article
23 pages, 811 KiB  
Review
Exploring Post-Quantum Cryptography: Review and Directions for the Transition Process
by Kanza Cherkaoui Dekkaki, Igor Tasic and Maria-Dolores Cano
Technologies 2024, 12(12), 241; https://doi.org/10.3390/technologies12120241 (registering DOI) - 23 Nov 2024
Viewed by 329
Abstract
As quantum computing advances, current cryptographic protocols are increasingly vulnerable to quantum attacks, particularly those based on Public Key Infrastructure (PKI) like RSA or Elliptic Curve Cryptography (ECC). This paper presents a comprehensive review of Post-Quantum Cryptography (PQC) as a solution to protect [...] Read more.
As quantum computing advances, current cryptographic protocols are increasingly vulnerable to quantum attacks, particularly those based on Public Key Infrastructure (PKI) like RSA or Elliptic Curve Cryptography (ECC). This paper presents a comprehensive review of Post-Quantum Cryptography (PQC) as a solution to protect digital systems in the quantum era. We provide an in-depth analysis of various quantum-resistant cryptographic algorithms, including lattice-based, code-based, hash-based, isogeny-based, and multivariate approaches. The review highlights the National Institute of Standards and Technology (NIST) PQC standardization process, highlighting key algorithms, such as CRYSTALS–Kyber, CRYSTALS–Dilithium, Falcon, and SPHINCS+, and discusses the strengths, vulnerabilities, and implementation challenges of the leading algorithms. In addition, we explore transition strategies for organizations, emphasizing hybrid cryptography to ensure backward compatibility during migration. This study offers key insights into the future of cryptographic standards and the critical steps necessary to prepare for the transition from classical to quantum-resistant systems. Full article
(This article belongs to the Section Information and Communication Technologies)
16 pages, 1711 KiB  
Article
A Reflective Terahertz Point Source Meta-Sensor with Asymmetric Meta-Atoms for High-Sensitivity Bio-Sensing
by Luwei Zheng, Kazuki Hara, Hironaru Murakami, Masayoshi Tonouchi and Kazunori Serita
Biosensors 2024, 14(12), 568; https://doi.org/10.3390/bios14120568 (registering DOI) - 23 Nov 2024
Viewed by 138
Abstract
Biosensors operating in the terahertz (THz) region are gaining substantial interest in biomedical analysis due to their significant potential for high-sensitivity trace-amount solution detection. However, progress in compact, high-sensitivity chips and methods for simple, rapid and trace-level measurements is limited by the spatial [...] Read more.
Biosensors operating in the terahertz (THz) region are gaining substantial interest in biomedical analysis due to their significant potential for high-sensitivity trace-amount solution detection. However, progress in compact, high-sensitivity chips and methods for simple, rapid and trace-level measurements is limited by the spatial resolution of THz waves and their strong absorption in polar solvents. In this work, a compact nonlinear optical crystal (NLOC)-based reflective THz biosensor with a few arrays of asymmetrical meta-atoms was developed. A near-field point THz source was locally generated at a femtosecond-laser-irradiation spot via optical rectification, exciting only the single central meta-atom, thereby inducing Fano resonance. The reflective resonance response demonstrated dependence on several aspects, including structure asymmetricity, geometrical size, excitation point position, thickness and array-period arrangement. DNA samples were examined using 1 μL applied to an effective sensing area of 0.234 mm2 (484 μm × 484 μm) for performance evaluation. The developed Fano resonance sensor exhibited nearly double sensitivity compared to that of symmetrical sensors and one-gap split ring resonators. Thus, this study advances liquid-based sensing by enabling easy, rapid and trace-level measurements while also driving the development of compact and highly sensitive THz sensors for biological samples. Full article
(This article belongs to the Section Optical and Photonic Biosensors)
16 pages, 5888 KiB  
Article
Development and Characterization of Ammonia Removal Moving Bed Biofilms for Landfill Leachate Treatment
by Rossana Petrilli, Attilio Fabbretti, Kathleen Pucci, Graziella Pagliaretta, Valerio Napolioni and Maurizio Falconi
Microorganisms 2024, 12(12), 2404; https://doi.org/10.3390/microorganisms12122404 (registering DOI) - 23 Nov 2024
Viewed by 211
Abstract
Urbanization growth has intensified the challenge of managing and treating increasing amounts of municipal solid waste (MSW). Landfills are commonly utilized for MSW disposal because of their low construction and operation costs. However, this practice produces huge volumes of landfill leachate, a highly [...] Read more.
Urbanization growth has intensified the challenge of managing and treating increasing amounts of municipal solid waste (MSW). Landfills are commonly utilized for MSW disposal because of their low construction and operation costs. However, this practice produces huge volumes of landfill leachate, a highly polluting liquid rich in ammoniacal nitrogen (NH3-N), organic compounds, and various heavy metals, making it difficult to treat in conventional municipal wastewater treatment plants (WWTPs). In recent years, research has shown that microbial biofilms, developed on carriers of different materials and called “moving bed biofilm reactors” (MBBRs), may offer promising solutions for bioremediation. This study explored the biofilm development and the nitrification process of moving bed biofilms (MBBs) obtained from high ammonia-selected microbial communities. Using crystal violet staining and confocal laser-scanning microscopy, we followed the biofilm formation stages correlating nitrogen removal to metagenomic analyses. Our results indicate that MBBs unveiled a 10-fold more enhanced nitrification rate than the dispersed microbial community present in the native sludge of the Porto Sant’Elpidio (Italy) WWTP. Four bacterial families, Chitinophagaceae, Comamonadaceae, Sphingomonadaceae, and Nitrosomonadaceae, accumulate in structured biofilms and significantly contribute to the high ammonium removal rate of 80% in 24 h as estimated in leachate-containing wastewaters. Full article
(This article belongs to the Collection Biodegradation and Environmental Microbiomes)
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Figure 1

Figure 1
<p>Analysis of biofilm formation using CLSM. Staining of sludge (<b>A</b>) and G5-2 (<b>B</b>) MBBs was carried out with SYTO9 and PI fluorescent dyes, followed by CLSM analysis as described in <a href="#sec2-microorganisms-12-02404" class="html-sec">Section 2</a>. Both dyes intercalate with nucleic acids but, while SYTO9 penetrates both living and dead cells, PI can only pass through damaged membranes and displaces SYTO9, allowing differentiation between live (green) and dead (red) cells [<a href="#B31-microorganisms-12-02404" class="html-bibr">31</a>,<a href="#B32-microorganisms-12-02404" class="html-bibr">32</a>]. Stacks of images were taken at random areas on the HPDE sheets, and each stack contained 10 images.</p>
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<p>Bio-repetitive re-inoculum assay using G5-2 and G5-4 MBBs. Bio-carriers of G5-2 and G5-4 (30 pieces each) were incubated in 30 mL of LMM at 28 °C. The NH<sub>4</sub><sup>+</sup>-N was adjusted to ≅350 mg/L and monitored, using Nessler’s test, as a function of time for the whole duration of Bio-RRIA (<b>A</b>) (see body text). Samples from Bio-RRIA were withdrawn at indicated NH<sub>4</sub><sup>+</sup>-N falls for total nitrogen, nitrite, and nitrate determinations of G5-2 (<b>B</b>) and G5-4 (<b>C</b>) biofilms. Total nitrogen is the sum of ammonia remaining, nitrites, nitrates, and organic nitrogen compounds from leachate. Leachate composition is reported in <a href="#app1-microorganisms-12-02404" class="html-app">Supplementary Table S2</a>.</p>
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<p>Effect of the temperature on Bio-RRIA by G1-2, G5-2 and G5-4 MBBs. The G1-2 (red circle), G5-2 (blue square), and G5-4 (green triangle) MBBs were incubated at 30 °C (<b>A</b>), 23 °C (<b>B</b>), 18 °C (<b>C</b>) and 10 °C (<b>D</b>). and then subjected to Bio-RRIA essentially as described in the body text and in the legend of <a href="#microorganisms-12-02404-f002" class="html-fig">Figure 2</a>A.</p>
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<p>Bio-repetitive re-inoculum assay by sludge MBBs. Sludge samples were taken at different periods from the Porto Sant’Elpidio MWWTP and used for K1 bio-carriers preparation. Biofilms were investigated for their efficiency in NH<sub>4</sub><sup>+</sup>-N removal in Bio-RRIA experiments performed as described in the body text and in the Legend of <a href="#microorganisms-12-02404-f002" class="html-fig">Figure 2</a>A. Four representative sludges, indicated with SL1 (<b>A</b>), SL2 (<b>B</b>), SL3 (<b>C</b>) and SL4 (<b>D</b>), are shown.</p>
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<p>Change of biofilm population from selected microbial communities. Relative abundance, expressed as a percentage of total operational taxonomic units (OTUs), of the most prevalent families (<b>A</b>,<b>B</b>) and species (<b>C</b>,<b>D</b>) in the biofilms derived from G5-2 and G5-4 cultures are shown. Samples for species identification by 16S rRNA NGS were the bacterial cultures used for biofilm formation (gray bars) and MBBs taken on the 1st day (green bars), on the 10th day (red bars), and on the 15th day (dark blue bars) of Bio-RRIA reported in <a href="#microorganisms-12-02404-f002" class="html-fig">Figure 2</a>A. The bar graph shows only families and species that contributed more than 4% to the total bacterial community in at least one point.</p>
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<p>Stacked bar chart of MBBs from native sludges. Relative abundance, expressed as a percentage of total operational taxonomic units (OTUs), of the most prevalent families in biofilm-derived sludges SL2, SL3, and LSL4. Bacteria identification was carried out using 16S rRNA NGS, and values represent the average ± standard deviation of at least three points taken during Bio-RRIA experiments, as shown in <a href="#microorganisms-12-02404-f004" class="html-fig">Figure 4</a>. Only families that contributed more than 3% to the total bacterial community are reported. Analysis of variance across the three samples shows a statistically significant difference in their microbial composition (<span class="html-italic">p</span> &lt; 0.05).</p>
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22 pages, 6102 KiB  
Article
Thin Films of BaM Hexaferrite with an Inclined Orientation of the Easy Magnetization Axis: Crystal Structure and Magnetic Properties
by Boris Krichevtsov, Alexander Korovin, Vladimir Fedorov, Sergey Suturin, Aleksandr A. Levin, Andrey Telegin, Elena Balashova and Nikolai Sokolov
Nanomaterials 2024, 14(23), 1883; https://doi.org/10.3390/nano14231883 (registering DOI) - 23 Nov 2024
Viewed by 233
Abstract
Thin (~50 nm thick) BaM hexaferrite (BaFe12O19) films were grown on (1–102) and (0001) cut α-Al2O3 (sapphire) substrates via laser molecular beam epitaxy using a one- or two-stage growth protocol. The advantages of a two-stage protocol [...] Read more.
Thin (~50 nm thick) BaM hexaferrite (BaFe12O19) films were grown on (1–102) and (0001) cut α-Al2O3 (sapphire) substrates via laser molecular beam epitaxy using a one- or two-stage growth protocol. The advantages of a two-stage protocol are shown. The surface morphology, structural and magnetic properties of films were studied using atomic force microscopy, reflected high-energy electron diffraction, three-dimensional X-ray diffraction reciprocal space mapping, powder X-ray diffraction, magneto-optical, and magnetometric methods. Annealed BaFe12O19/Al2O3 (1–102) structures consist of close-packed islands epitaxially bonded to the substrate. The hexagonal crystallographic axis and the easy axis (EA) of the magnetization of the films are deflected from the normal to the film by an angle of φ~60°. The films exhibit magnetic hysteresis loops for both in-plane Hin-plane and out-of-plane Hout-of-plane magnetic fields. The shape of Mout-of-plane(Hin-plane) and Min-plane(Hin-plane) hysteresis loops strongly depends on the azimuth θ of the Hin plane, confirming the tilted orientation of the EA. The Mout-of-plane(Hout-of-plane) magnetization curves are caused by the reversible rotation of magnetization and irreversible magnetization jumps associated with the appearance and motion of domain walls. In the absence of a magnetic field, the magnetization is oriented at an angle close to φ. Full article
(This article belongs to the Special Issue Magnetization and Magnetic Disorder at the Nanoscale)
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Figure 1

Figure 1
<p>(<b>a</b>,<b>b</b>) AFM images of annealed sample #1 (BaFe<sub>12</sub>O<sub>19</sub>/Al<sub>2</sub>O<sub>3</sub> (1–102) at different scales.</p>
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<p>Cross-section of 3D RHEED of a sample #1 grown on Al<sub>2</sub>O<sub>3</sub> (1–102) (<b>a</b>) before and (<b>b</b>) after annealing at 1000 °C. The 3D RHEED projections onto a plane are presented, in which the horizontal axes of (<b>a</b>,<b>b</b>) are parallel to the [−2–241]<sub>BaM</sub> direction, and the vertical axes are parallel to [11–24]<sub>BaM</sub>.</p>
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<p>XRD patterns of the BaM film prepared on an Al<sub>2</sub>O<sub>3</sub> (1–102) substrate (sample #1) and a virgin substrate on a logarithmic scale. The Miller-Bravais indices <span class="html-italic">hkil</span> are indicated for the observed reflections of the hexagonal BaM phase of the film and for reflections of the rhombohedral (in a hexagonal setting) α-Al<sub>2</sub>O<sub>3</sub> phase of the substrate. The symbol <span class="html-italic">K<sub>ß</sub></span> marks reflections arising from residual Cu-<span class="html-italic">K<sub>ß</sub></span> radiation. The observed BaM reflections are shown by triangle symbols at the Bragg angles according to the PDF-2 card 01-075-9113. The space group of the BaM phase is indicated in the figure.</p>
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<p>(<b>a</b>) Three cross-sections of reciprocal space taken by XRD from sample #1 for different crystallographic substrate orientations: (<b>a</b>) a[11–20], (<b>b</b>) m[1–100], and (<b>c</b>) r[1–102], where a, m, and r are the normals to A-, M-, and R-cuts of the Al<sub>2</sub>O<sub>3</sub> substrate. Red circles are model positions for reflections from the BaM hexaferrite lattice. Blue circles correspond to the model positions for reflections from the Al<sub>2</sub>O<sub>3</sub> substrate. White spots are observed XRD reflections from the substrate and BaM hexaferrite film. Yellow arrows in (<b>a</b>) indicate rotation of 1.2° around m [1–100] axis of BaM. The origin of coordinates on (<b>a</b>–<b>c</b>) is indicated by a circle with a dot in the center and marked with the number 0. (<b>d</b>) Schematic representation of substrate and film orientations.</p>
Full article ">Figure 4 Cont.
<p>(<b>a</b>) Three cross-sections of reciprocal space taken by XRD from sample #1 for different crystallographic substrate orientations: (<b>a</b>) a[11–20], (<b>b</b>) m[1–100], and (<b>c</b>) r[1–102], where a, m, and r are the normals to A-, M-, and R-cuts of the Al<sub>2</sub>O<sub>3</sub> substrate. Red circles are model positions for reflections from the BaM hexaferrite lattice. Blue circles correspond to the model positions for reflections from the Al<sub>2</sub>O<sub>3</sub> substrate. White spots are observed XRD reflections from the substrate and BaM hexaferrite film. Yellow arrows in (<b>a</b>) indicate rotation of 1.2° around m [1–100] axis of BaM. The origin of coordinates on (<b>a</b>–<b>c</b>) is indicated by a circle with a dot in the center and marked with the number 0. (<b>d</b>) Schematic representation of substrate and film orientations.</p>
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<p>(<b>a</b>) PMOKE hysteresis loop in sample #1 for different maximal values of out-of-plane magnetic field (<span class="html-italic">H</span><sup>m</sup><sub>out-of-plane</sub> = 7 kOe (red hollow triangles), 12 kOe (blue half-colored squares), and 17 kOe (green solid circles)). (<b>b</b>) Comparison of the experimental loop (red hollow circles) and that (blue solid line) calculated using the Stoner–Wohlfarth model for the values 4<span class="html-italic">πM</span><sub>s</sub> = 4.5 kG, <span class="html-italic">H</span><sub>a</sub> = 18 kOe, <span class="html-italic">φ</span> = 62°. (<b>c</b>) Magnetization curve <span class="html-italic">M</span>(<span class="html-italic">H</span>) measured using VSM after subtracting the linear part in <span class="html-italic">H</span> that appears in high fields caused by substrate magnetic susceptibility and film magnetization rotation. Lines connecting the symbols in (<b>a</b>–<b>c</b>) are guides for the eye.</p>
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<p>Sample #1. (<b>a</b>) Hysteresis PMOKE loops for various in-plane magnetic field <b>H</b><sub>in-plane</sub> orientations (red, blue, and black solid squares). Azimuths <span class="html-italic">θ</span> of in-plane magnetic field for the corresponding hysteresis loops are shown by arrows. Left and right insets in the top of (<b>a</b>) show mutual orientation of EA and magnetic field for <span class="html-italic">θ</span> = 0° and 90°. Blue (for <span class="html-italic">θ</span> = 38°, 83°, 292°, and 340°) and red (for <span class="html-italic">θ</span> = 132°, 174°, 220°, and 255°) symbols correspond to different sign of scalar product <b>uH,</b> where <b>u</b> is unit vector along EA. Black symbols (for <span class="html-italic">θ</span> = 87°) correspond to the orthogonal mutual orientation of <b>u</b> and <b>H</b>. Angular dependence of (<b>b</b>) the coercive field <span class="html-italic">H</span><sub>c</sub> and (<b>c</b>) the remnant value of PMOKE. Symbols (red half-colored circles) represent the experimental points. Lines connecting the symbols in the PMOKE loops in (<b>a</b>) and blue solid lines in (<b>b</b>) (thick line) and (<b>c</b>) (fine line) are provided as a guide for the eye.</p>
Full article ">Figure 6 Cont.
<p>Sample #1. (<b>a</b>) Hysteresis PMOKE loops for various in-plane magnetic field <b>H</b><sub>in-plane</sub> orientations (red, blue, and black solid squares). Azimuths <span class="html-italic">θ</span> of in-plane magnetic field for the corresponding hysteresis loops are shown by arrows. Left and right insets in the top of (<b>a</b>) show mutual orientation of EA and magnetic field for <span class="html-italic">θ</span> = 0° and 90°. Blue (for <span class="html-italic">θ</span> = 38°, 83°, 292°, and 340°) and red (for <span class="html-italic">θ</span> = 132°, 174°, 220°, and 255°) symbols correspond to different sign of scalar product <b>uH,</b> where <b>u</b> is unit vector along EA. Black symbols (for <span class="html-italic">θ</span> = 87°) correspond to the orthogonal mutual orientation of <b>u</b> and <b>H</b>. Angular dependence of (<b>b</b>) the coercive field <span class="html-italic">H</span><sub>c</sub> and (<b>c</b>) the remnant value of PMOKE. Symbols (red half-colored circles) represent the experimental points. Lines connecting the symbols in the PMOKE loops in (<b>a</b>) and blue solid lines in (<b>b</b>) (thick line) and (<b>c</b>) (fine line) are provided as a guide for the eye.</p>
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<p>(<b>a</b>) Hysteresis loops in sample #1 measured by using VSM for various azimuths <span class="html-italic">θ</span> of in-plane magnetic field <b>H</b><sub>in-plane</sub> (red, blue, and black solid squares). The loops were obtained after subtracting the linear part in <span class="html-italic">H</span>, which appears in high fields and is caused mainly by the substrate magnetization. Blue (for <span class="html-italic">θ</span> = 0°, 30°, 60°, 300°, and 360°) and red (for <span class="html-italic">θ</span> = 120°, 150°, 180°, 210°, and 240°) symbols in (<b>a</b>) correspond to different sign of scalar product <b>uH</b>. Black symbols (for <span class="html-italic">θ</span> = 90° and 270°) correspond to orthogonal mutual orientation of <b>u</b> and <b>H</b>. Angular dependence of (<b>b</b>) the coercive field <span class="html-italic">H</span><sub>c</sub> and (<b>c</b>) the remnant magnetization <span class="html-italic">M</span><sub>rem</sub>. The experimental points in (<b>b</b>,<b>c</b>) are shown by red half-colored circles. Lines connecting the symbols in the PMOKE loops in (<b>a</b>) and thick blue solid lines in (<b>b</b>,<b>c</b>) are provided as a guide for the eye.</p>
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<p>PMOKE hysteresis loop (<b>a</b>) in sample #2 after annealing (first stage of protocol) and (<b>b</b>) in sample #3 (second stage). Blue solid and green dashed lines in panel (<b>b</b>) show the decomposition of the loop into two loops. (<b>c</b>) Magnetization curve of sample #3 measured by using VSM. Red solid circles in (<b>a</b>) and red half-colored circles in (<b>b</b>,<b>c</b>) are experimental points. Lines connecting the symbols in (<b>a</b>–<b>c</b>) are a guide for the eye.</p>
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<p>PMOKE hysteresis loop (<b>a</b>) in sample #4 (first stage of protocol) and (<b>b</b>) in sample #5 (second stage). Red (hollow circles) and blue (solid circles) symbols in (<b>b</b>) correspond to experimental points obtained using various maximal values of magnetic field. Lines connecting the symbols in (<b>a</b>,<b>b</b>) are a guide for the eye.</p>
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10 pages, 5511 KiB  
Article
Investigating Structural and Surface Modifications in Ion-Implanted 4H-SiC for Enhanced Dopant Distribution Analysis in Power Semiconductors
by Taehun Jang, Mirang Byeon, Minji Kang, Sang-Gil Lee, Ji Hyun Lee, Sang-Geul Lee, Won Ja Min and Tae Eun Hong
Materials 2024, 17(23), 5734; https://doi.org/10.3390/ma17235734 (registering DOI) - 23 Nov 2024
Viewed by 212
Abstract
This study aims to develop a reference material that enables precise management of dopant distribution in power semiconductors. We thoroughly investigate the structural and surface properties of 4H-silicon carbide (4H-SiC) single crystals implanted without annealing using aluminum (Al) and phosphorus (P) ions. Ion-implanted [...] Read more.
This study aims to develop a reference material that enables precise management of dopant distribution in power semiconductors. We thoroughly investigate the structural and surface properties of 4H-silicon carbide (4H-SiC) single crystals implanted without annealing using aluminum (Al) and phosphorus (P) ions. Ion-implanted 4H-SiC was thoroughly evaluated using advanced techniques, including X-ray diffraction (XRD), field emission transmission electron microscopy (FE-TEM), atomic force microscopy (AFM), time of flight medium energy ion scattering (ToF-MEIS), and secondary ion mass spectrometry (SIMS). The evaluated results indicate that, without post-annealing, ion-implanted 4H-SiC can serve as an effective reference material for the precise control of trace elements and the quantitative monitoring of dopant distribution in power semiconductor applications. Full article
(This article belongs to the Special Issue Advances in Materials Science for Engineering Applications)
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<p>(<b>a</b>) XRD omega rocking curves of 4H-SiC single crystals with three different ion-implanted samples and RSM images obtained from three different ion-implanted samples: (<b>b</b>) none, (<b>c</b>) Al, and (<b>d</b>) P ion.</p>
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<p>Planar TEM images and SAED patterns of 4H-SiC single crystal for three distinct ion-implanted samples: (<b>a</b>) none, (<b>b</b>) Al, and (<b>c</b>) P ion implantation.</p>
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<p>Cross-sectional TEM images and SAED patterns of 4H-SiC single crystals at low (<b>a</b>–<b>c</b>) and high (<b>d</b>–<b>f</b>) magnification for three ion-implanted samples, S1, S2, and S3. Red square areas in (<b>a</b>–<b>c</b>) are the areas measured by high-magnification TEM in (<b>d</b>–<b>f</b>).</p>
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<p>2D and 3D AFM images of a 4H-SiC single crystal under three different ion implantation conditions: (<b>a</b>) none, (<b>b</b>) Al ions, and (<b>c</b>) P ions (S1, S2, and S3).</p>
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<p>ToF-MEIS spectra of the ion-implanted 4H-SiC single crystal samples with three different conditions, namely none, Al, and P ion implantation (S1, S2, and S3).</p>
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<p>SIMS depth profiles of 4H-SiC single crystals with two different ion-implanted samples ((<b>a</b>) S2 and (<b>b</b>) S3).</p>
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10 pages, 4742 KiB  
Article
Tellurium Photonic Crystal-Based Terahertz Polarization Splitter Using a Diamond-Shaped Ferrite Pillar Array
by Haiping Zhang, Zhifeng Zeng and Yong Wang
Crystals 2024, 14(12), 1015; https://doi.org/10.3390/cryst14121015 (registering DOI) - 23 Nov 2024
Viewed by 292
Abstract
A T-shaped photonic crystal waveguide was designed with square lattice tellurium photonic crystals. A diamond-shaped ferrite pillar array was inserted in the junction of the waveguide to make a novel terahertz polarization splitter. Both transverse electric and transverse magnetic modes were numerically investigated [...] Read more.
A T-shaped photonic crystal waveguide was designed with square lattice tellurium photonic crystals. A diamond-shaped ferrite pillar array was inserted in the junction of the waveguide to make a novel terahertz polarization splitter. Both transverse electric and transverse magnetic modes were numerically investigated by the plane wave expansion method, which used complete photonic band gaps covering from 0.138 THz to 0.144 THz. In this frequency domain of the fully polarized band gaps, the transmission efficiency of the photonic crystal waveguide was up to −0.21 dB and −1.67 dB for the transverse electric and transverse magnetic modes, respectively. Under the action of a DC magnetic field, the THz waves were rotated 90 degrees by the diamond-shaped ferrite pillar array. Transverse electric waves or transverse magnetic waves can be separated by a polarization isolator (six smaller tellurium rods) from the fixed waves. The characteristics of the designed polarization splitter were analyzed by the finite element method, and its transmission efficiency was optimized to 95 percent by fine-tuning the radii of the thirteen ferrite pillars. A future integrated communication network of sky–earth–space will require fully polarized devices in the millimeter and terahertz wavebands. The envisaged polarization splitter has a unique function and provides a promising method for the realization of fully polarized 6G devices. Full article
(This article belongs to the Special Issue Metamaterials and Their Devices)
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<p>The tridimensional figure of the PC-based PBS.</p>
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<p>The detailed structural parameters in a plane figure for the designed PBS.</p>
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<p>The PBGs of the SLTRAs for both the TE and TM modes: three TE-mode PBGs (marked in blue) and two TM-mode PBGs (marked in red) around the normalized frequency domain from 0.15(<span class="html-italic">a</span>/<span class="html-italic">λ</span>) to 0.41(<span class="html-italic">a</span>/<span class="html-italic">λ</span>).</p>
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<p>The transmission characteristics of the T-shaped PCW for the TE mode in the increasing frequency domain.</p>
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<p>The transmission characteristics of the T-shaped PCW for the TM mode in the increasing frequency domain.</p>
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<p>The transmission characteristics of the PBS: (<b>a</b>) the planar view of the transmission path for the TE mode; (<b>b</b>) the altitudinal view; and (<b>c</b>) the transmission efficiency and isolation of the PBS for TE waves in the frequency domain from 136 to 144 GHz.</p>
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<p>The transmission characteristics of the PBS: (<b>a</b>) the planar view of the transmission path for the TM mode; (<b>b</b>) the altitudinal view; and (<b>c</b>) the transmission efficiency and isolation of the PBS for TM waves in the frequency domain from 136 to 144 GHz.</p>
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16 pages, 26558 KiB  
Article
Facile Preparation of Ultrafine Porous Copper Powders for Accelerating the Thermal Decomposition of Ammonium Perchlorate
by Dayong Li, Yuling Shao, Shengquan Chang, Yanggang Huang, Yong Kou, Lei Xiao and Gazi Hao
Materials 2024, 17(23), 5728; https://doi.org/10.3390/ma17235728 (registering DOI) - 23 Nov 2024
Viewed by 337
Abstract
In this study, we innovatively proposed a facile method to synthesize ultrafine porous copper (Cu) powders under mild conditions by utilizing the reduction properties of reduced iron (Fe) powders. The results showed that Cu2+ was easily reduced to Cu at 1.05–1.1 times [...] Read more.
In this study, we innovatively proposed a facile method to synthesize ultrafine porous copper (Cu) powders under mild conditions by utilizing the reduction properties of reduced iron (Fe) powders. The results showed that Cu2+ was easily reduced to Cu at 1.05–1.1 times the theoretical iron powder content for a reaction time of 10~20 min at 20~25 °C. The obtained Cu powders with an average diameter of 10.2 μm did not show significant differences in crystal structure and purity compared to the commercial Cu powders with an average diameter of 6.6 μm, but the prepared Cu powders showed a loose and porous structure, which demonstrates their higher potential in catalyzing energetic materials. The ultrafine porous Cu powder resulted in a significant decrease in the high decomposition temperature of ammonium perchlorate (AP) from 441.3 °C to 364.2 °C at only 1% of the dosage, and also slightly advanced its low decomposition temperature, which confirmed its remarkable catalytic activity in the field of energetic materials. These meaningful results will provide a new method for the preparation of Cu powders and promote the development of the chemical reduction method for the preparation of ultrafine porous Cu powders, which is expected to promote the application of ultrafine porous Cu powders in the field of energetic materials catalysis. Full article
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<p>Illustration of the synthesis of ultrafine porous Cu powders via chemical reduction.</p>
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<p>SEM and particle size of different samples: (<b>a</b>) the reduced Fe powders; (<b>b</b>) the obtained Cu powders; (<b>c</b>) commercial Cu powders.</p>
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<p>XRD patterns of different samples: (a) the reduced Fe powders; (b) the obtained Cu powders; (c) commercial Cu powders.</p>
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<p>EDS spectra of different samples: (<b>a</b>) the obtained Cu powders; (<b>b</b>) commercial Cu powders.</p>
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<p>TG curves of (a) the obtained Cu powders and (b) commercial Cu powders.</p>
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<p>TG curves for the thermal decomposition of different samples: (a) raw AP; (b) M1; (c) M2.</p>
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<p>DSC curves for the thermal decomposition of different samples: (a) raw AP; (b) M1; (c) M2.</p>
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<p>DSC curves for the decomposition of pure AP at different heating rates.</p>
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<p>DSC curves for the decomposition of M1 at different heating rates.</p>
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<p>DSC curves for the decomposition of M2 at different heating rates.</p>
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<p>The relationship between activation energy and α of different samples.</p>
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<p>Thermal decomposition kinetic modeling of different samples.</p>
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