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20 pages, 8642 KiB  
Review
Chemistry and Physics of Wet Foam Stability for Porous Ceramics: A Review
by Kamrun Nahar Fatema, Md Rokon Ud Dowla Biswas, Jung Gyu Park and Ik Jin Kim
Micro 2024, 4(4), 552-571; https://doi.org/10.3390/micro4040034 - 30 Sep 2024
Viewed by 501
Abstract
The unique structural properties of porous ceramics, such as low thermal conductivity, high surface area, controlled permeability, and low density, make this material valuable for a wide range of applications. Its uses include insulation, catalyst carriers, filters, bio-scaffolds for tissue engineering, and composite [...] Read more.
The unique structural properties of porous ceramics, such as low thermal conductivity, high surface area, controlled permeability, and low density, make this material valuable for a wide range of applications. Its uses include insulation, catalyst carriers, filters, bio-scaffolds for tissue engineering, and composite manufacturing. However, existing processing methods for porous ceramics, namely replica techniques and sacrificial templates, are complex, release harmful gases, have limited microstructure control, and are expensive. In contrast, the direct foaming method offers a simple and cost-effective approach. By modifying the surface chemistry of ceramic particles in a colloidal suspension, the hydrophilic particles are transformed into hydrophobic ones using surfactants. This method produces porous ceramics with interconnected pores, creating a hierarchical structure that is suitable for applications like nano-filters. This review emphasizes the importance of interconnected porosity in developing advanced ceramic materials with tailored properties for various applications. Interconnected pores play a vital role in facilitating mass transport, improving mechanical properties, and enabling fluid or gas infiltration. This level of porosity control allows for the customization of ceramic materials for specific purposes, including filtration, catalysis, energy storage, and biomaterials. Full article
(This article belongs to the Special Issue Advances in Micro- and Nanomaterials: Synthesis and Applications)
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Figure 1
<p>(<b>a</b>) Scheme of foams and mists that can be produced through the adsorption of colloidal particles at the gas–liquid interface. Foams and mists indicate the force balance at equilibrium for particles lyophilized to different extents. (<b>b</b>) Direct foaming process, reproduced from Ref. [<a href="#B32-micro-04-00034" class="html-bibr">32</a>].</p>
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<p>Destabilization of colloidal suspensions and Ostwald ripening significantly influence the stability and characteristics of colloidal systems, modified from Ref. [<a href="#B18-micro-04-00034" class="html-bibr">18</a>].</p>
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<p>Interparticle behavior in colloidal suspensions can be manipulated by engineering the interfacial assembly of colloidal particles through modifications to the mechanical properties of the interface, reproduced from Ref. [<a href="#B51-micro-04-00034" class="html-bibr">51</a>].</p>
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<p>Schematic of particle position at different phase interfaces as a function of its contact angle from the wettability of silica nanoparticle–surfactant nanocomposite interfacial layers, modified from Ref. [<a href="#B55-micro-04-00034" class="html-bibr">55</a>].</p>
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<p>Schematics of the chemistry and physics in wet processes for the production of porous microstructures, modified from Ref. [<a href="#B56-micro-04-00034" class="html-bibr">56</a>].</p>
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<p>Possible approaches to attach colloidal particles at air-liquid interfaces by tuning their surface-wetting properties: (<b>a</b>) stabilization of air bubbles with colloidal particles, (<b>b</b>) adsorption of partially lyophobic particles at the air-liquid interface, and (<b>c</b>) wetting properties of originally hydrophilic particles to illustrate the universality of the foaming method developed; modified from Ref. [<a href="#B61-micro-04-00034" class="html-bibr">61</a>].</p>
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<p>Diagrams depicting the arrangement of adsorbed layers on a perfect ceramic surface based on different molecular structures include (<b>a</b>) homopolymer, featuring arrangements of tails, loops, and trains; (<b>b</b>) diblock copolymer, with a compact anchor block and a longer chain block; (<b>c</b>) comb-like copolymer, showing long segments branching from a fixed backbone; and (<b>d</b>) functional, short-chain dispersant, composed of an anchoring head group and a protruding tail; reproduced from Ref. [<a href="#B6-micro-04-00034" class="html-bibr">6</a>].</p>
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<p>Foam structure diagram with bubble shape and expanded bubble shape based on volume fraction, reproduced and modified from Ref. [<a href="#B64-micro-04-00034" class="html-bibr">64</a>].</p>
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<p>Law of Laplace and Young for a single soap bubble, modified from Ref. [<a href="#B56-micro-04-00034" class="html-bibr">56</a>].</p>
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<p>Impact of contact angle on interfacial adsorption and film thinning resistance in particle-stabilized foams, modified from Ref. [<a href="#B32-micro-04-00034" class="html-bibr">32</a>].</p>
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<p>Microstructures of porous ceramics of 30 vol.% Al<sub>2</sub>O<sub>3</sub> with respect to different mole ratios of TiO<sub>2</sub>: (<b>a</b>) 1: 0, (<b>b</b>) 1: 0.25, (<b>c</b>) 1: 0.75, reproduced from Ref. [<a href="#B26-micro-04-00034" class="html-bibr">26</a>], and (<b>d</b>) FESEM imagery of porous SiC ceramics, reproduced from Ref. [<a href="#B22-micro-04-00034" class="html-bibr">22</a>].</p>
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14 pages, 2171 KiB  
Article
Enhanced Mechanical Properties of Ceramic Rod-Reinforced TWIP Steel Composites: Fabrication, Microstructural Analysis, and Heat Treatment Evaluation
by Guojin Sun, Shengzhi Zhu, Zhenggui Li and Qi Wang
Metals 2024, 14(9), 1083; https://doi.org/10.3390/met14091083 - 21 Sep 2024
Viewed by 532
Abstract
This study investigates the development and characterization of ceramic rod-reinforced TWIP (twinning-induced plasticity) steel matrix composites, produced using the lost foam casting technique. Mechanical tests revealed a substantial improvement in both flexural strength and ductility, with the composite demonstrating more than double the [...] Read more.
This study investigates the development and characterization of ceramic rod-reinforced TWIP (twinning-induced plasticity) steel matrix composites, produced using the lost foam casting technique. Mechanical tests revealed a substantial improvement in both flexural strength and ductility, with the composite demonstrating more than double the strength of unreinforced TWIP steel. Furthermore, a simple low-temperature heat treatment further enhanced these properties, increasing the flexural strength of the composite to 1023 MPa while also improving its ductility. The improvement in mechanical performance is attributed to the formation of additional twins in the TWIP steel matrix during deformation following heat treatment, which resulted in further strengthening of the matrix. Full article
(This article belongs to the Special Issue Plasticity and Metal Forming)
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<p>Schematic of the industrial CT non-destructive testing setup.</p>
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<p>Ceramic-reinforced TWIP steel matrix composite and bending test specimen. (<b>a</b>) Schematic of the composite material. (<b>b</b>) Schematic of the bending test specimen.</p>
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<p>Microstructure of the TWIP Steel Matrix under different condition. (<b>a</b>) Casting condition, (<b>b</b>) Heat treatment condition.</p>
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<p>Fracture surface of the as-cast matrix material.</p>
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<p>Mechanical properties of TWIP steel matrix before and after heat treatment. (<b>a</b>) Yield strength of TWIP steel matrix. (<b>b</b>) Tensile strength of TWIP steel matrix. (<b>c</b>) Elongation of TWIP steel matrix.</p>
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<p>Fracture surface morphology of TWIP steel matrix before and after heat treatment. (<b>a</b>) As-cast condition. (<b>b</b>) Post-heat treatment.</p>
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<p>Morphology of twins formed in the TWIP steel matrix during tensile testing. (<b>a</b>) As-cast condition. (<b>b</b>) Post-heat treatment.</p>
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<p>Ceramic rod-reinforced TWIP steel matrix composite. (<b>a</b>) Ceramic rod-reinforced TWIP steel composite. (<b>b</b>) Industrial CT non-destructive testing.</p>
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<p>Bent specimens after testing under casting conditions. (<b>a</b>) Bending strength measurement sample. (<b>b</b>) Bent specimens of ceramic rod-reinforced TWIP composite after testing. (<b>c</b>) Bent specimens of TWIP matrix after testing.</p>
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<p>Stress–strain curves of specimens under as-cast bending conditions. (<b>a</b>) TWIP steel matrix. (<b>b</b>) Ceramic rod-reinforced composite.</p>
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<p>Flexural performance of ceramic rod-reinforced TWIP steel matrix composites post-heat treatment. (<b>a</b>) Flexural Strength. (<b>b</b>) Punch Displacement.</p>
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<p>Bending curves of TWIP steel matrix composites under different conditions.</p>
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19 pages, 8177 KiB  
Article
Carbonaceous Shape-Stabilized Octadecane/Multi-Walled Carbon Nanotube Composite Materials for Enhanced Energy Storage and Electromagnetic Interference Shielding
by Maria Baikousi, Christina Gioti, Konstantinos C. Vasilopoulos, Argyri Drymiskianaki, Vassilis M. Papadakis, Zacharias Viskadourakis, Angelos Ntaflos, Dimitrios Moschovas, Alkiviadis S. Paipetis, George Kenanakis and Michael A. Karakassides
Molecules 2024, 29(18), 4363; https://doi.org/10.3390/molecules29184363 - 13 Sep 2024
Viewed by 614
Abstract
Developing materials for efficient energy storage and effective electromagnetic interference (EMI) shielding is crucial in modern technology. This study explores the synthesis and characterization of carbonaceous shape-stabilized octadecane/MWCNT (multi-walled carbon nanotube) composites, utilizing activated carbon, expanded graphite or ceramic carbon foam, as shape [...] Read more.
Developing materials for efficient energy storage and effective electromagnetic interference (EMI) shielding is crucial in modern technology. This study explores the synthesis and characterization of carbonaceous shape-stabilized octadecane/MWCNT (multi-walled carbon nanotube) composites, utilizing activated carbon, expanded graphite or ceramic carbon foam, as shape stabilizers for phase change materials (PCMs) to enhance thermal energy storage and EMI shielding, for energy-efficient and advanced applications. The integration of octadecane, a phase change material (PCM) with carbonaceous stabilizers ensures the material’s stability during phase transitions, while MWCNTs contribute to improved thermal storage properties and EMI shielding capabilities. The research aims to develop novel composites with dual functionality for thermal storage and EMI shielding, emphasizing the role of carbon matrices and their MWCNT composites. SEM and CT microtomography analyses reveal variations in MWCNT incorporation across the matrices, influenced by surface properties and porosity. Leaching tests, infrared spectroscopy (FT-IR) and differential scanning calorimetry (DSC) confirm the composite’s stability and high latent heat storage. The presence of nanotubes enhances the thermal properties of octadecane and ΔH values almost reached their theoretical values. EMI shielding effectiveness measurements indicate that the composites show improved electric properties in the presence of MWCNTs. Full article
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<p>FT-IR spectra of: (<b>a</b>) activated carbon samples; (<b>b</b>) expanded graphite samples; and (<b>c</b>) ceramic carbon foam samples.</p>
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<p>Photographs from filter paper after leaching tests at 80 °C for: activated carbon, expanded graphite and ceramic carbon foam samples.</p>
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<p>Microtomography CT images of: (<b>a</b>) EG; (<b>b</b>) EG/OD; and (<b>c</b>) EG/CNTs/OD. Green line is coronal (COR), blue line is sagittal (SAG) and red line is transverse (TRA) cross-sections of the samples.</p>
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<p>Scanning Electron Microscopy (SEM) images of: (<b>a</b>) AC matrix; (<b>b</b>) AC/CNTs/OD composite; (<b>c</b>,<b>d</b>) EG matrix; and (<b>e</b>,<b>f</b>) CCF/CNTs/OD composite.</p>
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<p>DSC curves for: (<b>a</b>) activated carbon samples; (<b>b</b>) ceramic carbon foam; and (<b>c</b>) expanded graphite samples.</p>
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<p>Comparative graphs for: (<b>a</b>) ΔHm% and (<b>b</b>) ΔHs% of the composites derived from DSC curves.</p>
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<p>Thermal conductivity of studied samples (AC-based samples marked with blue stars, EG-based samples marked with red dots, at 300 K.</p>
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<p>Transmission S<sub>21</sub> (<b>a</b>) and reflection S<sub>11</sub> (<b>b</b>) coefficients from 3.2 to 7.0 GHz (C-band) for AC samples.</p>
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<p>Absorption (<b>a</b>) and <span class="html-italic">SE<sub>A</sub></span> (<b>b</b>) from 3.2 to 7.0 GHz (C-band) for AC samples.</p>
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<p>Transmission S<sub>21</sub> (<b>a</b>) and reflection S<sub>11</sub> (<b>b</b>) coefficients from 3.2 to 7.0 GHz (C-band) for EG samples.</p>
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<p>Absorption (<b>a</b>) and <span class="html-italic">SE<sub>A</sub></span> (<b>b</b>) from 3.2 to 7.0 GHz (C-band) for EG samples.</p>
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<p>Transmission (<b>a</b>), absorption (<b>b</b>) and <span class="html-italic">SE<sub>A</sub></span> (<b>c</b>) of CCF samples, from 3.2 to 7.0 GHz (C-band).</p>
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12 pages, 2675 KiB  
Article
Thermal Shock Resistance of Commercial Oxide-Bonded Silicon Carbide Reticulated Foams under Concentrated Solar Radiation at PSA: A Feasibility Study
by Fernando de Almeida Costa Oliveira, José Galindo, José Rodríguez, Inmaculada Cañadas and Jorge Cruz Fernandes
Inorganics 2024, 12(9), 246; https://doi.org/10.3390/inorganics12090246 - 11 Sep 2024
Viewed by 441
Abstract
Volumetric ceramic receivers can be regarded as a promising technology to heat air above 1000 °C for solar thermal electricity production. In this study, the thermal shock behavior of commercial 10 ppi (A) and 20 ppi (B) oxide-bonded silicon carbide (ob-SiC) reticulated porous [...] Read more.
Volumetric ceramic receivers can be regarded as a promising technology to heat air above 1000 °C for solar thermal electricity production. In this study, the thermal shock behavior of commercial 10 ppi (A) and 20 ppi (B) oxide-bonded silicon carbide (ob-SiC) reticulated porous ceramic (RPC) foams was evaluated using the SF60 solar furnace at Plataforma Solar de Almería. The foams were subjected to well-controlled temperature cycles ranging from 800 to 1000, 1200, 1300 or 1400 °C, for 25, 100, and 150 cycles. The extent of the damage after thermal shock was determined by crushing tests. The damage was found to be critically dependent on both the bulk density and cell size. Decreasing both the bulk density and cell size resulted in better thermal shock resistance. The B foam exhibited approximately half the stress degradation compared to the A foam when exposed to a temperature difference of 600 K (in the range of 800 to 1400 °C) and subjected to 150 cycles. Full article
(This article belongs to the Special Issue Feature Papers in Inorganic Materials 2024)
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<p>Top view of as-received 10 ppi (<b>a</b>) and 20 ppi (<b>b</b>) ob-SiC RPC foams.</p>
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<p>Typical XRD patterns of ob-SiC RPC foam before (<b>a</b>) and after exposure at 1400 °C for 150 cycles (<b>b</b>).</p>
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<p>Temperature distribution over the exposed top surface area showing typical temperatures measured using the IR camera when the maximum temperature was set at 1400 °C.</p>
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<p>Temperature versus time graphs at ΔT = 600 K after 25 cycles (<b>a</b>) and 150 cycles (<b>b</b>) for 10 ppi ob-SiC RPC foam showing profiles measured by thermocouples B1 (black), K2 (red) and K3 (green).</p>
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<p>Typical crushing strength curves for foams A and B tested at ΔT = 600 K for 150 cycles.</p>
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<p>Experimental system showing the uncut (<b>a</b>) and in cut (<b>b</b>) guillotine positions; ob-SiC RPC samples being exposed (<b>c</b>); samples after the test at ΔT = 500 K for 100 cycles (<b>d</b>); scheme of the B- and K-type thermocouples positions (<b>e</b>); actual (nine) thermocouples positioning (<b>f</b>).</p>
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13 pages, 3464 KiB  
Article
Influence of Ceramic Size and Morphology on Interface Bonding Properties of TWIP Steel Matrix Composites Produced by Lost-Foam Casting
by Guojin Sun, Xiaoming Liu, Zhenggui Li and Qi Wang
Metals 2024, 14(9), 1003; https://doi.org/10.3390/met14091003 - 2 Sep 2024
Viewed by 563
Abstract
This study investigated the fabrication and characterization of large ceramic-reinforced TWIP (twinning-induced plasticity) steel matrix composites using the lost-foam casting technique. Various ceramic shapes and sizes, including blocky, flaky, rod-like, and granular forms, were evaluated for their suitability as reinforcement materials. The study [...] Read more.
This study investigated the fabrication and characterization of large ceramic-reinforced TWIP (twinning-induced plasticity) steel matrix composites using the lost-foam casting technique. Various ceramic shapes and sizes, including blocky, flaky, rod-like, and granular forms, were evaluated for their suitability as reinforcement materials. The study found that rod-like and granular ceramics exhibited superior structural integrity and formed strong interfacial bonds with the TWIP steel matrix compared to blocky and flaky ceramics, which suffered from cracking and fragmentation. Detailed microstructural analysis using scanning electron microscopy (SEM) and industrial computed tomography (CT) revealed the mechanisms influencing the composite formation. The results demonstrated that rod-like and granular ceramics are better for reinforcing TWIP steel composites, providing excellent mechanical stability and enhanced performance. This work contributes to the development of advanced composite structures with potential applications in industries requiring high-strength and durable materials. Full article
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Figure 1
<p>Schematic of the fabrication process for large ceramic-reinforced TWIP steel matrix composites.</p>
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<p>Large fabricated ceramic-reinforced TWIP steel matrix composite samples.</p>
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<p>Schematic of the working principle of industrial CT scanning.</p>
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<p>Industrial CT results for plate and block ceramic-reinforced TWIP steel matrix composites. (<b>a</b>) Internal structure of plate ceramic reinforcement; (<b>b</b>) internal structure of block ceramic reinforcement.</p>
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<p>Industrial CT results for rod and particle ceramic-reinforced TWIP steel matrix composites. (<b>a</b>) Internal structure of rod ceramic reinforcement; (<b>b</b>) internal structure of granular ceramic reinforcement.</p>
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<p>Microstructural observations at the interface of large ceramics and the TWIP steel matrix. (<b>a</b>) Macroscopic interfacial bonding; (<b>b</b>) secondary electron SEM morphology; (<b>c</b>) backscattered electron SEM morphology.</p>
Full article ">Figure 6 Cont.
<p>Microstructural observations at the interface of large ceramics and the TWIP steel matrix. (<b>a</b>) Macroscopic interfacial bonding; (<b>b</b>) secondary electron SEM morphology; (<b>c</b>) backscattered electron SEM morphology.</p>
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<p>Elemental line distribution at the ceramic and TWIP steel matrix interface. (<b>a</b>) SEM microstructure of interface; (<b>b</b>) Si distribution at the interface; (<b>c</b>) Fe distribution at the interface; (<b>d</b>) C distribution at the interface.</p>
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<p>Elemental line distribution at the ceramic and TWIP steel matrix interface. (<b>a</b>) SEM microstructure of interface; (<b>b</b>) Si distribution at the interface; (<b>c</b>) Fe distribution at the interface; (<b>d</b>) C distribution at the interface.</p>
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26 pages, 7620 KiB  
Review
Properties, Treatment and Resource Utilization of Bauxite Tailings: A Review
by Yuansheng Peng, Zhongping Chen, Xiaohui Sun, Yuefu Zhou and Xiaoduo Ou
Sustainability 2024, 16(16), 6948; https://doi.org/10.3390/su16166948 - 14 Aug 2024
Viewed by 1493
Abstract
A substantial amount of bauxite tailings (BTs) at abandoned mine sites have been stored in waste reservoirs for long periods, leading to significant land occupation and environmental degradation. Although many studies of the resource utilization of BTs were conducted to address this challenge, [...] Read more.
A substantial amount of bauxite tailings (BTs) at abandoned mine sites have been stored in waste reservoirs for long periods, leading to significant land occupation and environmental degradation. Although many studies of the resource utilization of BTs were conducted to address this challenge, there is still a lack of efforts to systematically review the state of the art in BTs. In the present paper, a systematic literature review was carried out to summarize and analyze the properties, treatment, and resource utilization of BTs. Physical characteristics and the mineral and chemical composition of BTs are introduced. The efficacy of physical, chemical, and microbial treatment methods for BTs in terms of dehydration are outlined, and their respective benefits and limitations are discussed. Moreover, the extraction process of valuable elements (e.g., Si, Al, Fe, Li, Na, Nd, etc.) from BTs is examined, and the diverse applications of BTs in adsorption materials, ceramic materials, cementitious materials, lightweight aggregates, foamed mixture lightweight soil, among others, are studied. Finally, an efficient and smart treatment strategy for BTs was proposed. The findings of the present review provide a scientific basis and reference for future research focusing on the treatment and resource utilization of BTs. Full article
(This article belongs to the Section Waste and Recycling)
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<p>Production process of BTs and consequent environmental problems.</p>
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<p>Cumulative size curves of the investigated BTs. (Data are from Refs. [<a href="#B25-sustainability-16-06948" class="html-bibr">25</a>,<a href="#B29-sustainability-16-06948" class="html-bibr">29</a>,<a href="#B30-sustainability-16-06948" class="html-bibr">30</a>,<a href="#B31-sustainability-16-06948" class="html-bibr">31</a>]).</p>
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<p>Back-scattered electron (BSE) images obtained from the SEM study.</p>
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<p>Suggested model test for the treatment of BTs.</p>
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<p>Effects of biochemical treatment and quicklime treatment: (<b>a</b>,<b>b</b>) represent <span class="html-italic">a<sub>v</sub>-P</span> curves for BTs; (<b>c</b>,<b>d</b>) represent pore volume percentage under different treatment; (<b>e</b>,<b>f</b>) represent BSE images to show microstructure of quicklime treatment and biochemical treatment, respectively. (Data are from Ou et al. [<a href="#B59-sustainability-16-06948" class="html-bibr">59</a>]).</p>
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<p>Recovery of elements of BTs: (<b>a</b>) maximum recovery; (<b>b</b>–<b>d</b>) represent the effect of leaching duration, particle sizes, and temperature on the recovery, respectively. (Data are from Refs. [<a href="#B32-sustainability-16-06948" class="html-bibr">32</a>,<a href="#B38-sustainability-16-06948" class="html-bibr">38</a>]).</p>
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<p>BSE images of the zeolite samples: (<b>a</b>,<b>b</b>) represent the zeolite 4A samples synthesized by two methods; (<b>c</b>,<b>d</b>) represent the zeolite X and zeolite Y samples, respectively [<a href="#B13-sustainability-16-06948" class="html-bibr">13</a>,<a href="#B14-sustainability-16-06948" class="html-bibr">14</a>,<a href="#B15-sustainability-16-06948" class="html-bibr">15</a>,<a href="#B16-sustainability-16-06948" class="html-bibr">16</a>].</p>
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<p>Synthesis of zeolite from BTs.</p>
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<p>Maximum removal efficiency: (<b>a</b>) heavy metal ions; (<b>b</b>) CO<sub>2.</sub> (Data are from Refs. [<a href="#B14-sustainability-16-06948" class="html-bibr">14</a>,<a href="#B15-sustainability-16-06948" class="html-bibr">15</a>,<a href="#B16-sustainability-16-06948" class="html-bibr">16</a>,<a href="#B34-sustainability-16-06948" class="html-bibr">34</a>,<a href="#B66-sustainability-16-06948" class="html-bibr">66</a>]).</p>
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<p>Carbonation conversion of CaO-based adsorbent prepared with different BTs/CaO ratios: (<b>a</b>) Refs. [<a href="#B17-sustainability-16-06948" class="html-bibr">17</a>,<a href="#B52-sustainability-16-06948" class="html-bibr">52</a>]; (<b>b</b>) Ref. [<a href="#B4-sustainability-16-06948" class="html-bibr">4</a>].</p>
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<p>FE-SEM/EDX of metal-biochar [<a href="#B56-sustainability-16-06948" class="html-bibr">56</a>]: (<b>a</b>) CV; (<b>b</b>) C1B0.5; (<b>c</b>) C1B1; and (<b>d</b>) C1B2. Note: C1B0.5, C1B1, and C1B2 represent the mass ratios of CV to BTs of 1:0.5, 1:1 and 1:2, respectively.</p>
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<p>The flexural strength of ceramics varies with temperature. (Data are from Refs. [<a href="#B19-sustainability-16-06948" class="html-bibr">19</a>,<a href="#B20-sustainability-16-06948" class="html-bibr">20</a>,<a href="#B70-sustainability-16-06948" class="html-bibr">70</a>]).</p>
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<p>Compressive strength of mortar including coarse BTs and fine BTs at different activation temperatures (Data are from Zhou et al. [<a href="#B23-sustainability-16-06948" class="html-bibr">23</a>]).</p>
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<p>Hydration heat evolution rate (<b>a</b>) and cumulative hydration heat curves (<b>b</b>) of paste samples for 72 h (Data are from Zhou et al. [<a href="#B30-sustainability-16-06948" class="html-bibr">30</a>]). Note: T0 is the pure cement; T80-20 signifies that the separation frequency of BTs is 80 Hz and the BTs content is 20% by weight; others are similar.</p>
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<p>Effect of clinker to gypsum ratio (<b>a</b>) and elevated temperature (<b>b</b>) on the compressive strength of mortars. (Data are from Refs. [<a href="#B22-sustainability-16-06948" class="html-bibr">22</a>,<a href="#B36-sustainability-16-06948" class="html-bibr">36</a>]).</p>
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<p>Autogenous shrinkage of mortars (Data are from Yang et al. [<a href="#B1-sustainability-16-06948" class="html-bibr">1</a>]). Note: REF represents the mortar without LWA; M0, MF, and MC represent the mortars mixed with LWA, LWA + 10 wt% CaF<sub>2</sub>, and LWA + 20 wt% CaCO<sub>3</sub>, respectively.</p>
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<p>Mechanical properties of 3D printing mortar at different curing ages (<b>a</b>) Compressive strength; (<b>b</b>) Flexural strength. (Date are from Zhou et al. [<a href="#B31-sustainability-16-06948" class="html-bibr">31</a>]).</p>
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<p>Characteristics of FMLSB: (<b>a</b>) relationship between unconfined compressive strength and area porosity; (<b>b</b>) XRD analysis. Note: S = C-S-H, C = C-H, E = AFt, H = C-A-S-H, A = C-A-H, B = C<sub>2</sub>S or C3S, G = CaSO<sub>4</sub>·2H<sub>2</sub>O, D = SiO<sub>2</sub>, O = CaCO<sub>3</sub>; B0, B10, B20, B30, and B40 represent the replacement ratio of BTs for cement at 0%, 10%, 20%, 30%, and 40% by weight, respectively. (Date are from Peng et al. [<a href="#B5-sustainability-16-06948" class="html-bibr">5</a>]).</p>
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<p>Treatment and resource utilization strategy of BTs.</p>
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17 pages, 4247 KiB  
Article
Conventional Manufacturing by Pouring Versus Additive Manufacturing Technology of β-Tricalcium Phosphate Bone Substitute Implants
by Tanja Zöller, Hagen Schmal, Matthias Ahlhelm, Hermann O. Mayr and Michael Seidenstuecker
Biomedicines 2024, 12(8), 1800; https://doi.org/10.3390/biomedicines12081800 - 8 Aug 2024
Viewed by 612
Abstract
The aim of the study was to compare conventional sintering with additive manufacturing techniques for β-TCP bioceramics, focusing on mechanical properties and biocompatibility. A “critical” bone defect requires surgical intervention beyond simple stabilization. Autologous bone grafting is the gold standard treatment for such [...] Read more.
The aim of the study was to compare conventional sintering with additive manufacturing techniques for β-TCP bioceramics, focusing on mechanical properties and biocompatibility. A “critical” bone defect requires surgical intervention beyond simple stabilization. Autologous bone grafting is the gold standard treatment for such defects, but it has its limitations. Alloplastic bone grafting with synthetic materials is becoming increasingly popular. The use of bone graft substitutes has increased significantly, and current research has focused on optimizing these substitutes, whereas this study compares two existing manufacturing techniques and the resulting β-TCP implants. The 3D printed β-TCP hybrid structure implant was fabricated from two components, a column structure and a freeze foam, which were sintered together. The conventionally fabricated ceramics were fabricated by casting. Both scaffolds were characterized for porosity, mechanical properties, and biocompatibility. The hybrid structure had an overall porosity of 74.4 ± 0.5%. The microporous β-TCP implants had a porosity of 43.5 ± 2.4%, while the macroporous β-TCP implants had a porosity of 61.81%. Mechanical testing revealed that the hybrid structure had a compressive strength of 10.4 ± 6 MPa, which was significantly lower than the microporous β-TCP implants with 32.9 ± 8.7 MPa. Biocompatibility evaluations showed a steady increase in cell proliferation over time for all the β-TCP implants, with minimal cytotoxicity. This study provides a valuable insight into the potential of additive manufacturing for β-TCP bioceramics in the treatment of bone defects. Full article
(This article belongs to the Section Biomedical Engineering and Materials)
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<p>Test setup for the uniaxial compression test using the RMS implant as an example: (<b>A</b>) RMS implant with 6 mm height before the test; (<b>B</b>) RMS implant with 6 mm height after the test.</p>
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<p>Overview of the scaffolds used: (<b>A</b>) macroporous β-TCP from Curasan (6 and 20 mm length) left and center; microporous β-TCP from RMS; (<b>B</b>) hybrid structure, side and top view; the RMS scaffold was shortened to 20 mm before the test in order to make it comparable with the Cursan scaffold.</p>
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<p>µCT reconstructions of the different scaffolds; the pore size ranges from 0.001 to 0.316 µm in the false color images.</p>
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<p>Overview of compressive strength and maximum failure load of the different samples. (<b>A</b>) Compressive strength as a function of sample origin; (<b>B</b>) maximum failure loads of the samples; (<b>C</b>) compressive strength of samples of different origin (manufacturing process) after degradation test according to ISO EN 10993-14 in Tris buffer with pH 7.4 for 60 days; (<b>D</b>) compressive strength of β-TCP samples (different production) after degradation in Tris buffer with pH 5.0 for 60 days; (*) statistically significant difference with <span class="html-italic">p</span> &lt; 0.05.</p>
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<p>Course of cell growth on the surface according to 3, 7, and 10 days for hybrid structure; microporous TCP; macroporous TCP; 3D growth control and 2D growth control (Thermanox Coverslip); images in 5× magnification, images taken with Olympus BX-53 fluorescence microscope.</p>
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<p>(<b>A</b>) Cell proliferation after 3, 7, and 10 days on the different samples; (<b>B</b>) cytotoxicity curves of all samples after 1, 2, and 3 days.</p>
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12 pages, 7443 KiB  
Article
The Effect of Flux on a Waste-Derived Foamed Ceramic: Analysis of Microstructure and Properties
by Zhiwu Zuo, Minghao Mu, Xue Liu and Congcong Jiang
Crystals 2024, 14(8), 682; https://doi.org/10.3390/cryst14080682 - 26 Jul 2024
Viewed by 538
Abstract
Foamed ceramics with high closed porosity were prepared using granite scrap as the raw material and silicon carbide as a foaming agent, and the effects of Na2O, K2O, and MgO on the pore structure and properties of the foamed [...] Read more.
Foamed ceramics with high closed porosity were prepared using granite scrap as the raw material and silicon carbide as a foaming agent, and the effects of Na2O, K2O, and MgO on the pore structure and properties of the foamed ceramics were investigated. The results show that both Na2O and K2O could reduce the viscosity of the melt and promote the formation of the liquid phase, and the increase in content could enhance the foaming ability of the blank. When the dosage of Na2O was 4–6 wt% and the dosage of K2O was 6–8 wt%, the homogeneity of the pore structure of the foamed ceramics could be effectively improved, and the samples exhibited an optimal performance, including a bulk density of 510.36–593.33 kg/m3, a closed porosity of 68.24–78.04%, a compressive strength of 1.33–2.66 MPa, and a water absorption capacity of 0.57–1.31%. A further increase in the Na2O and K2O dosages destroyed the uniformity of the pore structure, resulting in a large number of irregular macropores. MgO had a slight effect on regulating the pore structure of the foamed ceramics, and the increase in dosage promoted the precipitation of forsterite crystals, creating conditions suitable for the preparation of foamed ceramics with small pores. Full article
(This article belongs to the Section Polycrystalline Ceramics)
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<p>Pore structure morphology and pore size distribution of foamed ceramics with different Na<sub>2</sub>O dosages.</p>
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<p>The porosity and water absorption of foamed ceramics with different Na<sub>2</sub>O dosages. (<b>a</b>) Open porosity and closed porosity, (<b>b</b>) Water absorption.</p>
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<p>XRD pattern of samples with different Na<sub>2</sub>O dosages.</p>
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<p>The bulk density and compressive strength of foamed ceramics with different Na<sub>2</sub>O admixtures.</p>
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<p>Pore structure morphology and pore size distribution of foamed ceramics with different K<sub>2</sub>O dosages.</p>
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<p>XRD patterns of samples with different K<sub>2</sub>O dosages.</p>
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<p>The physical properties of samples with different K<sub>2</sub>O dosages. (<b>a</b>) Open porosity and closed porosity, (<b>b</b>) Bulk density, compressive strength and water absorption.</p>
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<p>Pore structure morphology and pore size distribution of foamed ceramics with different MgO dosages.</p>
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<p>XRD pattern of samples with different MgO dosages.</p>
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<p>The physical properties of samples with different MgO dosages.</p>
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12 pages, 2192 KiB  
Article
Mechanism Study on the Effect of Surface Electrical Property on Microbial Membrane Formation Efficiency of TiO2-SiC Composite Filler in Recirculating Aquaculture System
by Jiaxin Li, Ze Hong, Jingying Ouyang, Han Zheng and Ying Liu
Materials 2024, 17(14), 3501; https://doi.org/10.3390/ma17143501 - 15 Jul 2024
Viewed by 606
Abstract
Recirculating aquaculture systems (RASs) offer significant advantages in aquaculture by markedly decreasing water usage and increasing culture density. A vital component within a RAS is the filler material, which serves as a surface for microbial colonization. Effective microbial treatment is crucial for the [...] Read more.
Recirculating aquaculture systems (RASs) offer significant advantages in aquaculture by markedly decreasing water usage and increasing culture density. A vital component within a RAS is the filler material, which serves as a surface for microbial colonization. Effective microbial treatment is crucial for the efficient operation of a RAS as it assists in purifying the wastewater generated within the system. Nevertheless, traditional fillers often show low efficiency in biofilm formation. The commercial silicon carbide used in this study is a foam ceramic filter with a density of about 0.4–0.55 g/cm3, a number of holes of about 10, and a through porosity of 80.9%, with a diameter of about 5 cm. This research investigates the utilization of a titanium dioxide–silicon carbide (TiO2-SiC) composite filler to improve the purification efficiency of ammonia nitrogen and chemical oxygen demand (COD) in aquaculture wastewater. The study involved the application of titanium dioxide films onto the surface of silicon carbide to produce the composite filler. This method takes advantage of the dipole interaction between titanium dioxide and microorganisms, which enhances biofilm culturing efficiency on the silicon carbide surface. The performance of three different fillers was assessed for their ability to purify aquaculture wastewater. Results showed that the TiO2-SiC composite filler was 1.67 times more effective in removing COD and 1.07 times more effective in removing ammonia nitrogen compared to using silicon carbide alone. These results demonstrate that the incorporation of a titanium dioxide coating substantially boosts the microbial colonization efficiency of silicon carbide, thereby enhancing the overall wastewater purification efficiency in RAS. Full article
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<p>XRD characterization of titanium dioxide thin films.</p>
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<p>Surface electrical properties of titanium dioxide thin films and single SiCs at different pH values.</p>
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<p>The removal rate of COD value in purifying aquaculture wastewater with four types of fillers.</p>
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<p>The rate of change of COD value in four types of fillers during film hanging.</p>
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<p>The removal rate of ammonia nitrogen concentration in purifying aquaculture wastewater with four types of fillers.</p>
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<p>Result pictures of three kinds of TiO<sub>2</sub>/SiC composite fillers after 21 days of film hanging and state diagram of single TiO<sub>2</sub> before and after annealing.</p>
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15 pages, 25363 KiB  
Article
Atomic-Scale Insights into the Effects of the Foaming Degree on the Glass–Ceramic Matrix Derived from Waste Glass and Incineration Bottom Ash
by Ying Wei, Ziwei Chen and Hao Wang
Materials 2024, 17(12), 2820; https://doi.org/10.3390/ma17122820 - 10 Jun 2024
Cited by 1 | Viewed by 804
Abstract
Precise management of the inverse correlation between the total porosity and compressive strength is crucial for the progress of foaming glass–ceramics (FGCs). To deeply understand this relationship, we investigated the atomic-level transformations of five CO2-foaming FGC samples using molecular dynamics simulation. [...] Read more.
Precise management of the inverse correlation between the total porosity and compressive strength is crucial for the progress of foaming glass–ceramics (FGCs). To deeply understand this relationship, we investigated the atomic-level transformations of five CO2-foaming FGC samples using molecular dynamics simulation. The short-range and intermediate-range structures of the FGCs with varying total porosities (36.68%, 66.28%, 66.96%, 72.21%, and 79.88%) in the system were elucidated. Na cations were observed to exhibit a strong interaction with CO2, accumulating at the surface of the pore wall and influencing the oxygen species. Therefore, the change in the atomic structure of the matrix was accompanied by an increase in the total porosity with an increasing CO2 content. Specifically, as the total porosity increased, the bridging oxygen content within the FGCs rose accordingly. However, once the total porosity exceeded 66.96%, the bridging oxygen content began to decline. This observation was significant considering the role of the bridging oxygen content in forming a continuous cross-linked network of chemical bonds, which contributed to the enhanced mechanical strength. Consequently, the influence of the total porosity on the oxygen species resulted in a two-stage reduction in the compressive strength. This study offers valuable insights for the development of high-strength lightweight FGCs. Full article
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<p>Compression strength vs. total porosity for FGCs.</p>
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<p>Structural configurations in the last picosecond of the samples with the total porosities of 36.68% (<b>a</b>), 66.28% (<b>b</b>), 66.96% (<b>c</b>), 72.21% (<b>d</b>), and 79.88% (<b>e</b>).</p>
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<p>(<b>a</b>) Temperature, pressure, and internal energy of the simulated system the during the foaming process. (<b>b</b>) Equilibrium internal energy–time curves of samples with different TPs.</p>
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<p>Statistical system information obtained by AAMD simulations: PDF curves (<b>a</b>,<b>b</b>) and CN curves (<b>c</b>) of pairs (O* and O mean the oxygen in CO<sub>2</sub> and FGCs melt, respectively).</p>
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<p>SEM image of FGC accompanied by elemental distributions obtained from energy-dispersive X-ray spectroscopy.</p>
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<p>Quantitative Si-related structural information: (<b>a</b>) concentration variation in the Q<sup>i</sup>(Si) units; snapshots of the location distribution of different types of Q<sup>i</sup>(Si) units with TPs of 36.68% (<b>b</b>), 66.28% (<b>c</b>), 66.96% (<b>d</b>), 72.21% (<b>e</b>), and 79.88% (<b>f</b>).</p>
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<p>Quantitative information of the Al-related structure and oxygen species and the supporting evidence in the spectra: the concentration variation in the Al-related units (<b>a</b>) and oxygen species (<b>b</b>) (NBO or O<sub>nb</sub> means non-bridging oxygen, FO means free oxygen, and TO means tricluster oxygen); (<b>c</b>) degree of depolymerization, NBO/T, where T denotes the network-forming Si and Al, and the average residual charge per the O atom.</p>
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<p>FTIR spectra of the samples.</p>
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<p>Comparison of samples in total and major partial neutron structure factors.</p>
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18 pages, 12354 KiB  
Article
Characterization of Porous β-Type Tricalcium Phosphate Ceramics Formed via Physical Foaming with Freeze-Drying
by Kazuaki Hashimoto, Hiroto Oikawa and Hirobumi Shibata
Int. J. Mol. Sci. 2024, 25(10), 5363; https://doi.org/10.3390/ijms25105363 - 14 May 2024
Viewed by 618
Abstract
Porous β-tricalcium phosphate (Ca3(PO4)2; β-TCP) was prepared via freeze-drying and the effects of this process on pore shapes and sizes were investigated. Various samples were prepared by freezing β-TCP slurries above a liquid nitrogen surface at −180 [...] Read more.
Porous β-tricalcium phosphate (Ca3(PO4)2; β-TCP) was prepared via freeze-drying and the effects of this process on pore shapes and sizes were investigated. Various samples were prepared by freezing β-TCP slurries above a liquid nitrogen surface at −180 °C with subsequent immersion in liquid nitrogen at −196 °C. These materials were then dried under reduced pressure in a freeze-dryer, after which they were sintered with heating. Compared with conventional heat-based drying, the resulting pores were more spherical, which increased both the mechanical strength and porosity of the β-TCP. These materials had a wide range of pore sizes from 50 to 200 µm, with the mean and median values both approximately 100 µm regardless of the freeze-drying conditions. Mercury porosimetry data showed that the samples contained small, interconnected pores with sizes of 1.24 ± 0.25 µm and macroscopic, interconnected pores of 25.8 ± 4.7 µm in size. The effects of nonionic surfactants having different hydrophilic/lipophilic balance (HLB) values on foaming and pore size were also investigated. Materials made with surfactants having lower HLB values exhibited smaller pores and lower porosity, whereas higher HLB surfactants gave higher porosity and slightly larger macropores. Even so, the pore diameter could not be readily controlled solely by adjusting the HLB value. The findings of this work indicated that high porosity (>75%) and good compressive strength (>2 MPa) can both be obtained in the same porous material and that foaming agents with HLB values between 12.0 and 13.5 were optimal. Full article
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<p>XRD patterns for porous samples fabricated in this work. The specimen names in the figure are given in <a href="#sec3-ijms-25-05363" class="html-sec">Section 3</a>.</p>
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<p>FT-IR spectra of porous samples fabricated in this work. The specimen names in the figure are given in <a href="#sec3-ijms-25-05363" class="html-sec">Section 3</a>.</p>
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<p>Photographic images of (<b>a</b>) 30-30, (<b>b</b>) 0-30, and (<b>c</b>) 30-20 specimens, showing (t) top view and (s) side view.</p>
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<p>SEM images of cross-sections of (<b>a</b>) 0-10, (<b>b</b>) 20-10, (<b>c</b>) 30-10, and (<b>d</b>) 240-0 specimens, showing (<b>i</b>) top, (<b>ii</b>) center, and (<b>iii</b>) bottom sections (Secondary electron detector, high vacuum mode, accelerated voltage 5 kV).</p>
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<p>SEM images of cross-sections of (<b>a</b>) 10-20, (<b>b</b>) 20-20, (<b>c</b>) 30-20, and (<b>d</b>) heat-dried specimens, showing (<b>i</b>) top, (<b>ii</b>) center, and (<b>iii</b>) bottom sections (Secondary electron detector, high vacuum mode, accelerated voltage 5 kV).</p>
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<p>Typical time–temperature curves of water during freezing processes. (a) slow freezing, (b) rapid freezing and (c) super-quick freezing.</p>
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<p>Pore size histograms for various porous β-TCP specimens.</p>
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<p>Schematic illustration showing pore formation in foams using different drying methods.</p>
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<p>Bulk density and porosity values for porous β-TCP specimens as determined using the Archimedes method. The directions of the arrows indicate the relationship between the axes in the figure. The numerical values for porosity indicate closed porosity in the upper part and open porosity in the lower part. Data on heat-drying were sourced from reference [<a href="#B35-ijms-25-05363" class="html-bibr">35</a>].</p>
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<p>Compressive strength for porous β-TCP specimens fabricated in this work. Data on heat-drying were sourced from reference [<a href="#B35-ijms-25-05363" class="html-bibr">35</a>].</p>
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<p>Pore distributions for porous β-TCP specimens fabricated using different drying methods as determined with the mercury injection method. Data on heat-drying were sourced from reference [<a href="#B35-ijms-25-05363" class="html-bibr">35</a>].</p>
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<p>SEM images of cross-sections of porous β-TCP specimens fabricated using nonionic surfactants (<b>a</b>) BT-5, (<b>b</b>) BT-7, (<b>c</b>) BT-9, and (<b>d</b>) BT-12, showing (<b>i</b>) top, (<b>ii</b>) center, and (<b>iii</b>) bottom sections (Secondary electron detector, high vacuum mode, accelerated voltage 5 kV).</p>
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<p>Pore size histograms for porous β-TCP specimens fabricated using different nonionic surfactants.</p>
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<p>Bulk density and porosity values for porous β-TCP specimens fabricated using different nonionic surfactants. The directions of the arrows indicate the relationship between the axes in the figure. The numerical values for porosity indicate closed porosity in the upper part and open porosity in the lower part.</p>
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<p>Compressive strength of porous β-TCP specimens fabricated using different nonionic surfactants.</p>
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<p>SEM images of fracture surfaces of specimens broken by mechanical stress; (<b>a</b>) 30-20, (<b>b</b>) BT-12, and (<b>c</b>) heat-dried specimens; (<b>i</b>) magnification of 50× and (<b>ii</b>) 500× (Secondary electron detector, high vacuum mode, accelerated voltage 5 kV).</p>
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<p>Schematic illustration showing the pre-freezing process.</p>
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15 pages, 4985 KiB  
Article
Research on Online Monitoring Technology and Filtration Process of Inclusions in Aluminum Melt
by Yunfei Wu, Hao Yan, Jiahao Wang, Jincan Zheng, Xianzhao Na and Xiaodong Wang
Sensors 2024, 24(9), 2757; https://doi.org/10.3390/s24092757 - 26 Apr 2024
Viewed by 719
Abstract
Online monitoring and real-time feedback on inclusions in molten metal are essential for metal quality control. However, existing methods for detecting aluminum melt inclusions face challenges, including interference, prolonged processing times, and latency. This paper presents the design and development of an online [...] Read more.
Online monitoring and real-time feedback on inclusions in molten metal are essential for metal quality control. However, existing methods for detecting aluminum melt inclusions face challenges, including interference, prolonged processing times, and latency. This paper presents the design and development of an online monitoring system for molten metal inclusions. Initially, the system facilitates real-time adjustment of signal acquisition parameters through a multiplexer. Subsequently, it employs a detection algorithm capable of swiftly extracting pulse peaks, with this task integrated into our proprietary host computer software to ensure timely detection and data visualization. Ultimately, we developed a monitoring device integrated with this online monitoring system, enabling the online monitoring of the aluminum alloy filtration process. Our findings indicate that the system can accurately measure the size and concentration of inclusions during the filtration process in real time, offering enhanced detection speed and stability compared to the industrial LiMCA CM (liquid metal cleanliness analyzer continuous monitoring) standard. Furthermore, our evaluation of the filtration process demonstrates that the effectiveness of filtration significantly improves with the increase in inclusion sizes, and the synergistic effect of combining CFF (ceramic foam filter) and MCF (metallics cartridge filter) filtration methods exceeds the performance of the CFF method alone. This system thus provides valuable technical support for optimizing filtration processes and controlling inclusion quality. Full article
(This article belongs to the Section Industrial Sensors)
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<p>Schematic diagram of the principle of the electrical sensing zone method, (The red arrow is the direction of molten metal flow).</p>
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<p>Schematic diagram of non-metallic inclusions online monitoring system.</p>
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<p>Experimental measuring setup.</p>
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<p>Schematic diagram of the signal acquisition module.</p>
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<p>The software interface and functional area division of the host computer.</p>
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<p>Signal process principle of peak detection algorithm: (<b>a</b>) principle of the peak detection algorithm in LiMCA products; (<b>b</b>) principle of the peak algorithm utilized in this work.</p>
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<p>Comparison of the test results of the self-developed experimental measuring device and LiMCA CM.</p>
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<p>Schematic diagram of the filtering process, (The black arrows in the diagram show the direction of molten metal flow). (<b>a</b>) SNIF (spinning nozzle inert flotation); (<b>b</b>) CFF (ceramic foam filter); (<b>c</b>) MCF (metallics cartridge filter).</p>
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<p>The average concentration distribution of inclusions of each size post-SNIF, post-CFF, and post-MCF.</p>
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<p>Average concentration of a set of inclusions at 10 μm after SNIF, CFF, and MCF.</p>
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<p>Changes in N20, N40, N60, and N80 counts after SNIF, CFF, and MCF with measurement time: (<b>a</b>) N20 data; (<b>b</b>) N40 data; (<b>c</b>) N60 data; (<b>d</b>) N80 data.</p>
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15 pages, 16956 KiB  
Article
Corrosion Behavior of 30 ppi TAD3D/5A05Al Composite in Neutral Salt Spray Corrosion
by Zishen Li, Hongliang Yang, Yuxin Chen, Gaofeng Fu and Lan Jiang
Metals 2024, 14(5), 488; https://doi.org/10.3390/met14050488 - 23 Apr 2024
Viewed by 891
Abstract
This study created ceramic preforms with a 3D network structure (TAD3D) by using treated aluminum dross (TAD) and kaolin slurry, with 30 ppi polyurethane foam as a template via the sacrificial template method. TAD3D/5A05Al composites were then produced via [...] Read more.
This study created ceramic preforms with a 3D network structure (TAD3D) by using treated aluminum dross (TAD) and kaolin slurry, with 30 ppi polyurethane foam as a template via the sacrificial template method. TAD3D/5A05Al composites were then produced via pressureless infiltration of 5A05Al aluminum alloy into TAD3D. The corrosion behavior and resistance of TAD3D/5A05Al in salt spray were assessed via neutral salt spray corrosion (NSS), scanning electron microscopy (SEM), potentiodynamic polarization (PDP), and electrochemical impedance spectroscopy (EIS) tests. The results showed that after 24 to 360 h of NSS corrosion, the corrosion of the 5A05 matrix was primarily pitting, with pits expanding and deepening over time, and showing a tendency to interconnect. The main corrosion products were MgAl2O4, Al(OH)3, and Al2O3. As corrosion progressed, these products increased and filled cracks, pits, and grooves at the composite interface on the material’s surface. Corrosion products transferred to the grooves at the composite interface and grew on the ceramic surface. Corrosion products on the ceramic framework and the Al matrix can form a continuous passivation film covering the composite surface. PDP and EIS results indicated that the composite’s corrosion resistance decreased by 240 h but increased after that time. After 240 h, the surface passivation film can weaken corrosion effects and enhance the composite’s resistance, although it remained weaker than that of the uncorroded samples. Additionally, grooves at the composite interface deepened over time, with loosely structured corrosion products inside, potentially leading to severe localized corrosion. Full article
(This article belongs to the Section Metal Matrix Composites)
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<p>Manufacturing process of the TAD<sub>3D</sub>/5A05Al composite material.</p>
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<p>The raw materials, process, and samples for preparing TAD<sub>3D</sub>/5A05Al composite materials: (<b>a</b>) SEM of treated aluminum dross; (<b>b</b>) TAD<sub>3D</sub>; (<b>c</b>) TAD<sub>3D</sub>/5A05Al.</p>
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<p>OM and SEM image of TAD<sub>3D</sub>/5A05Al: (<b>a</b>) OM image of TAD<sub>3D</sub>; (<b>b</b>) OM image of 5A05Al; (<b>c-1</b>,<b>c-2</b>) OM image of composite interface; (<b>d-1</b>,<b>e-1</b>) SEM image of β-phase; (<b>d-2</b>–<b>d-4</b>,<b>e-2</b>–<b>e-4</b>) EDS point scan spectrum.</p>
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<p>SEM and EDS of TAD<sub>3D</sub>/5A05Al: (<b>a</b>) SEM of composite interface; (<b>b-1</b>) O; (<b>b-2</b>) Si; (<b>b-3</b>) Fe; (<b>b-4</b>) Mg; (<b>b-5</b>) Al; (<b>b-6</b>) Mn.</p>
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<p>SEM images of 5A05Al matrix in TAD<sub>3D</sub>/5A05Al after removing corrosion products at different NSS corrosion durations: (<b>a-1</b>–<b>a-3</b>) 24 h; (<b>b-1</b>–<b>b-3</b>) 72 h; (<b>c-1</b>–<b>c-3</b>) 144 h; (<b>d-1</b>–<b>d-3</b>) 240 h; (<b>e-1</b>–<b>e-3</b>) 360 h.</p>
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<p>SEM images of the interface in TAD<sub>3D</sub>/5A05Al with corrosion products after NSS corrosion for different durations: (<b>a-1</b>–<b>a-3</b>) 24 h; (<b>b-1</b>–<b>b-3</b>) 72 h; (<b>c-1</b>–<b>c-3</b>) 144 h; (<b>d-1</b>–<b>d-3</b>) 240 h; (<b>e-1</b>–<b>e-3</b>) 360 h.</p>
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<p>EDS point scan images of corrosion products at the interface in TAD<sub>3D</sub>/5A05 after 72 h of NSS corrosion: (<b>a</b>) SEM image; (<b>b-1</b>–<b>b-3</b>) energy spectrum and composition.</p>
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<p>SEM images and EDS of the interface in TAD<sub>3D</sub>/5A05Al after removing corrosion products at different NSS corrosion durations: (<b>a-1</b>–<b>a-3</b>) SEM of 24 h sample; (<b>a-4</b>) EDS of 24 h sample; (<b>b-1</b>–<b>b-3</b>) SEM of 240 h sample; (<b>b-4</b>) EDS of 240 h sample.</p>
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<p>PDP of TAD<sub>3D</sub>/5A05Al with corrosion products after different NSS durations in 3.5% NaCl.</p>
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<p>EIS of TAD<sub>3D</sub>/5A05Al with corrosion products after different NSS durations: (<b>a</b>) Nyquist diagram; (<b>b</b>) Bode diagram (|<span class="html-italic">Z</span>|-<span class="html-italic">F</span>); (<b>c</b>) Bode diagram (<span class="html-italic">θ</span>-<span class="html-italic">F</span>).</p>
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21 pages, 11311 KiB  
Article
Investigating the Impact Behavior of Carbon Fiber/Polymethacrylimide (PMI) Foam Sandwich Composites for Personal Protective Equipment
by Xinyu Zhang, Miao Tian, Jun Li and Xinggang Chen
Materials 2024, 17(7), 1683; https://doi.org/10.3390/ma17071683 - 6 Apr 2024
Viewed by 1223
Abstract
To improve the shock resistance of personal protective equipment and reduce casualties due to shock wave accidents, this study prepared four types of carbon fiber/polymethacrylimide (PMI) foam sandwich panels with different face/back layer thicknesses and core layer densities and subjected them to quasi-static [...] Read more.
To improve the shock resistance of personal protective equipment and reduce casualties due to shock wave accidents, this study prepared four types of carbon fiber/polymethacrylimide (PMI) foam sandwich panels with different face/back layer thicknesses and core layer densities and subjected them to quasi-static compression, low-speed impact, high-speed impact, and non-destructive tests. The mechanical properties and energy absorption capacities of the impact-resistant panels, featuring ceramic/ultra-high molecular-weight polyethylene (UHMWPE) and carbon fiber/PMI foam structures, were evaluated and compared, and the feasibility of using the latter as a raw material for personal impact-resistant equipment was also evaluated. For the PMI sandwich panel with a constant total thickness, increasing the core layer density and face/back layer thickness enhanced the energy absorption capacity, and increased the peak stress of the face layer. Under a constant strain, the energy absorption value of all specimens increased with increasing impact speed. When a 10 kg hammer impacted the specimen surface at a speed of 1.5 m/s, the foam sandwich panels retained better integrity than the ceramic/UHMWPE panel. The results showed that the carbon fiber/PMI foam sandwich panels were suitable for applications that require the flexible movement of the wearer under shock waves, and provide an experimental basis for designing impact-resistant equipment with low weight, high strength, and high energy absorption capacities. Full article
(This article belongs to the Special Issue Recent Progress in Functional Materials and Their Applications)
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<p>Basic structure of a bomb suit and hard insert plate.</p>
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<p>Microstructure of PMI foam.</p>
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<p>Structural diagrams of the two specimens.</p>
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<p>Stress–strain curve under quasi-static compression.</p>
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<p>Stress–strain curve under low-speed impact: (<b>a</b>) A-1; (<b>b</b>) A-2; (<b>c</b>) B-1; (<b>d</b>) B-2; (<b>e</b>) C.</p>
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<p>Force–time curve of specimens under low-speed impact: (<b>a</b>) force–time curves of specimens A-1 and B-1; (<b>b</b>) force–time curves of specimens A-2 and B-2; (<b>c</b>) force–time curves of specimen C.</p>
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<p>Images of five specimens damaged due to low-speed impact.</p>
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<p>Computer tomography images showing the damaged face and core layers.</p>
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<p>Images showing damaged glue nail.</p>
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<p>Stress–strain curves obtained under high-speed impact.</p>
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<p>Force–time curves obtained under high-speed compression: (<b>a</b>) A-1; (<b>b</b>) A-2; (<b>c</b>) B-1; (<b>d</b>) B-2.</p>
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<p>Energy absorption curves of the specimens: (<b>a</b>) quasi-static compression; (<b>b</b>) low-speed impact; (<b>c</b>) high-speed impact.</p>
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13 pages, 5144 KiB  
Article
Microstructure, Mechanical Property and Thermal Conductivity of Porous TiCO Ceramic Fabricated by In Situ Carbothermal Reduction of Phenolic Resin and Titania
by Xiaoyu Cao, Chenhuan Wang, Yisheng Li, Zehua Zhang and Lei Feng
Nanomaterials 2024, 14(6), 515; https://doi.org/10.3390/nano14060515 - 13 Mar 2024
Cited by 1 | Viewed by 1068
Abstract
The porous TiCO ceramic was synthesized through a one-step sintering method, utilizing phenolic resin, TiO2 powder, and KCl foaming agent as raw materials. Ni(NO3)2·6H2O was incorporated as a catalyst to facilitate the carbothermal reaction between the [...] Read more.
The porous TiCO ceramic was synthesized through a one-step sintering method, utilizing phenolic resin, TiO2 powder, and KCl foaming agent as raw materials. Ni(NO3)2·6H2O was incorporated as a catalyst to facilitate the carbothermal reaction between the pyrolytic carbon and TiO2 powder. The influence of Ni(NO3)2·6H2O catalyst content (0, 5, 10 wt.% of the TiO2 powder) on the microstructure, compressive strength, and thermal conductivity of the resultant porous TiCO ceramic was examined. X-ray diffraction and X-ray photoelectron spectroscopy results confirmed the formation of TiC and TiO in all samples, with an increase in the peak of TiC and a decrease in that of TiO as the Ni(NO3)2·6H2O content increased from 0% to 10%. Scanning electron microscopy results demonstrated a morphological change in the pore wall, transforming from a honeycomb-like porous structure composed of well-dispersed carbon and TiC-TiO particles to rod-shaped TiC whiskers, interconnected with each other as the catalyst content increased from 0% to 10%. Mercury intrusion porosimetry results proved a dual modal pore-size distribution of the samples, comprising nano-scale pores and micro-scale pores. The micro-scale pore size of the samples minorly changed, while the nano-scale pore size escalated from 52 nm to 138 nm as the catalyst content increased from 0 to 10%. The morphology of the pore wall and nano-scale pore size primarily influenced the compressive strength and thermal conductivity of the samples by affecting the load-bearing capability and solid heat-transfer conduction path, respectively. Full article
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<p>Fabrication process of the porous TiCO ceramic.</p>
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<p>XRD patterns of the as-received TiCO ceramic with different catalyst contents.</p>
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<p>XPS patterns of the as-received TiCO ceramic: TiCO-0 (<b>a</b>), TiCO-5 (<b>b</b>), TiCO-10 (<b>c</b>).</p>
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<p>SEM images of the monolithic resin after cured (<b>a</b>) and sintered (<b>b</b>), and KCl/Ni(NO<sub>3</sub>)<sub>2</sub>·6H<sub>2</sub>O-5/resin after cured (<b>c</b>) and sintered (<b>d</b>), and the EDS results (<b>e</b>).</p>
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<p>SEM images of the as-received porous TiCO ceramic: TiCO-0 (<b>a</b>), TiCO-5 (<b>b</b>), TiCO-10 (<b>c</b>), and the EDS results (<b>d</b>).</p>
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<p>Log differential intrusion versus pore-size diameter of the as-received porous TiCO ceramic: TiCO-0 (<b>a</b>), TiCO-5 (<b>b</b>), TiCO-10 (<b>c</b>), average size of micro-scale pore and nano-scale pore (<b>d</b>) of the porous TiCO ceramic with different catalyst contents.</p>
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<p>The strain–stress curves (<b>a</b>); Compressive strength and porosity (<b>b</b>) of the samples with different catalyst contents.</p>
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<p>Thermal diffusivity (<b>a</b>) and thermal conductivity (<b>b</b>) of the samples with different catalyst contents.</p>
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<p>The schematic illustration of the pore wall of the porous TiCO ceramic: TiCO-0 (<b>a</b>), TiCO-5 (<b>b</b>), TiCO-10 (<b>c</b>).</p>
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<p>Comparison of the porosity and thermal conductivities of the porous TiCO ceramic to those of other porous carbide ceramics previously reported [<a href="#B16-nanomaterials-14-00515" class="html-bibr">16</a>,<a href="#B21-nanomaterials-14-00515" class="html-bibr">21</a>,<a href="#B39-nanomaterials-14-00515" class="html-bibr">39</a>,<a href="#B40-nanomaterials-14-00515" class="html-bibr">40</a>].</p>
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