Nothing Special   »   [go: up one dir, main page]

You seem to have javascript disabled. Please note that many of the page functionalities won't work as expected without javascript enabled.
 
 
Sign in to use this feature.

Years

Between: -

Subjects

remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline

Journals

remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline

Article Types

Countries / Regions

remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline

Search Results (14,199)

Search Parameters:
Keywords = cracks

Order results
Result details
Results per page
Select all
Export citation of selected articles as:
16 pages, 5342 KiB  
Article
Effect of Annealing Temperature on Morphology and Electrochromic Performance of Electrodeposited WO₃ Thin Films
by Pritam J. Morankar, Rutuja U. Amate, Manesh A. Yewale and Chan-Wook Jeon
Crystals 2024, 14(12), 1038; https://doi.org/10.3390/cryst14121038 (registering DOI) - 28 Nov 2024
Abstract
The purpose of this study was to investigate the effect of annealing temperature on the structural, morphological, and electrochemical properties of tungsten trioxide (WO3) films, fabricated via electrodeposition and annealed at 50 °C, 250 °C, and 450 °C. Structural analysis using [...] Read more.
The purpose of this study was to investigate the effect of annealing temperature on the structural, morphological, and electrochemical properties of tungsten trioxide (WO3) films, fabricated via electrodeposition and annealed at 50 °C, 250 °C, and 450 °C. Structural analysis using X-ray diffraction (XRD) revealed temperature-induced modifications, transitioning from amorphous to crystalline phases. Morphological studies by field emission scanning electron microscopy (FESEM) demonstrated an increase in grain size with temperature (31 nm, 48 nm, and 53 nm) and the formation of cracks at higher annealing temperatures. Electrochemical characterization showed that the WO3 film annealed at 250 °C exhibited superior redox activity, enhanced ion diffusion, and excellent reversibility. Optical studies highlighted its exceptional performance, with 79.35% optical modulation, a coloration efficiency of 97.91 cm2/C, and rapid switching times (9.8 s for coloration and 7.5 s for bleaching). Furthermore, long-term cycling tests confirmed minimal degradation after 5000 cycles, demonstrating durability. This work provides a comprehensive understanding of the annealing temperature’s impact on WO3 films and underscores the novelty of achieving optimal electrochromic (EC) performance through temperature tuning, advancing the design of energy-efficient smart materials. Full article
(This article belongs to the Special Issue Research and Applications of Thin Films and Energy Materials)
Show Figures

Figure 1

Figure 1
<p>Visual depiction of the synthesis of WO<sub>3</sub> thin films at different annealing temperatures.</p>
Full article ">Figure 2
<p>Combined XRD spectra of W-50 °C, W-250 °C, and W-450 °C thin films prepared by electrodeposition technique.</p>
Full article ">Figure 3
<p>FE-SEM and cross-sectional images of (<b>a1</b>,<b>a2</b>) W-50 °C, (<b>b1</b>,<b>b2</b>) W-250 °C, and (<b>c1</b>,<b>c2</b>) W-450 °C samples.</p>
Full article ">Figure 4
<p>(<b>a</b>) High-resolution XPS survey spectra, (<b>b</b>) W 4f, and (<b>c</b>) O 1s spectra of W-250 °C sample.</p>
Full article ">Figure 5
<p>Cyclic voltammetry of (a) WO3, W-50 °C, W-250 °C, and W-450 °C thin films at scan rate of 20 mV/s (b–d) CV plot of W-50 °C, W-250 °C, and W-450 °C thin films at different scan rates (20–100 mV/s), and (e) plot of peak current vs. (scan rate)1/2 of all samples for the diffusion coefficient.</p>
Full article ">Figure 6
<p>Transmittance spectrum of (<b>a</b>) W-50 °C, (<b>b</b>) W-250 °C, and (<b>c</b>) W-450 °C thin films at the colored and bleached states from 300 to 1000 nm range over potential window ± 1 vs. Ag/AgCl.</p>
Full article ">Figure 7
<p>(<b>a</b>–<b>c</b>) Chronocoulometry (CC) trace of W-50 °C, W-250 °C, and W-450 °C thin films.</p>
Full article ">Figure 8
<p>Chronoamperometric response time with in situ transmittance measurements of (<b>a</b>) W-50 °C, (<b>b</b>) W-250 °C, and (<b>c</b>) W-450 °C thin films for 40 s.</p>
Full article ">Figure 9
<p>Plot of the long-term in situ optical response as a function of time of (<b>a</b>) W-50 °C, (<b>b</b>) W-250 °C, and (<b>c</b>) W-450 °C thin films for 5000 s.</p>
Full article ">
20 pages, 5861 KiB  
Article
Quantitative Seismic Damage Assessment of Resilient Concrete Columns Using Drift Ratio-Based Fractal Dimension
by Bunka Son, Ganggang Li, Zhiwei Luo and Yuping Sun
Materials 2024, 17(23), 5850; https://doi.org/10.3390/ma17235850 - 28 Nov 2024
Abstract
The objective of this paper is to develop assessment models to quantitatively evaluate the seismic damage caused to resilient concrete columns intended for buildings located in strong-earthquake-prone regions such as Japan and China. The proposed damage assessment models are based on the fractal [...] Read more.
The objective of this paper is to develop assessment models to quantitatively evaluate the seismic damage caused to resilient concrete columns intended for buildings located in strong-earthquake-prone regions such as Japan and China. The proposed damage assessment models are based on the fractal analysis of crack patterns on the surface of damaged concrete columns and expressed in the form of a fractal dimension (FD) versus transient drift ratio relationship. To calibrate the proposed damage assessment models, a total of eighty images of crack patterns for eight concrete columns were utilized. All the columns were reinforced by weakly bonded ultra-high-strength (WBUHS) rebars and tested under reversed cyclic loading. The experimental variables covered the shear span ratio of the column, the concrete strength, the axial load ratio, and the amount of steel in the WBUHS rebars. A box-counting algorithm was adopted to calculate or derive the FD of the crack pattern corresponding to each transient drift ratio. The test results reveal that the FD is an efficient image-based quantitative indicator of seismic damage degree for resilient concrete columns and correlates strongly with the transient drift ratio and is subjected to the influence of the shear span ratio. The influence of the other experimental variables on the derived FDs is, if any, little. Based on the test results, a linear equation was developed to define the relationships between the FD and transient drift ratio, and a multi-linear equation was formulated to relate the transient drift ratio to the residual drift ratio, an important index adopted in current design guidelines to measure the repairability of damaged concrete structures. To further verify the efficiency of the drift ratio-based FD in seismic damage assessment, the correlation between the FD and relative stiffness loss (RSL), an indicator used to measure the overall damage degree of concrete structures, was also examined. The driven FD exhibited very strong correlation with RSL, and an empirical equation was developed to reliably assess the overall seismic damage degree of resilient concrete columns with an FD. Full article
(This article belongs to the Section Construction and Building Materials)
Show Figures

Figure 1

Figure 1
<p>Remapping of sample image of the crack pattern taken at R = 1.0% (specimen S17N10FC50); (<b>a</b>) original; (<b>b</b>) remapped.</p>
Full article ">Figure 2
<p>Example of dividing the target by boxes with the size <math display="inline"><semantics> <mrow> <mi>r</mi> </mrow> </semantics></math>; (<b>a</b>) H; (<b>b</b>) H/2; (<b>c</b>) H/4; (<b>d</b>) H/8; (<b>e</b>) H/16; (<b>f</b>) H/32.</p>
Full article ">Figure 2 Cont.
<p>Example of dividing the target by boxes with the size <math display="inline"><semantics> <mrow> <mi>r</mi> </mrow> </semantics></math>; (<b>a</b>) H; (<b>b</b>) H/2; (<b>c</b>) H/4; (<b>d</b>) H/8; (<b>e</b>) H/16; (<b>f</b>) H/32.</p>
Full article ">Figure 3
<p>The driven FD for the exemplar image taken at R = 1.0% (specimen S17N10FC50).</p>
Full article ">Figure 4
<p>Flowchart of calculating FD using box-counting algorithm.</p>
Full article ">Figure 5
<p>Reinforcement details and dimensions of specimens (in mm): (<b>a</b>) elevation; (<b>b</b>) section.</p>
Full article ">Figure 6
<p>Loading apparatus.</p>
Full article ">Figure 7
<p>Definition of drift ratio R and loading protocol: (<b>a</b>) definition of R; (<b>b</b>) loading program.</p>
Full article ">Figure 8
<p>Observed propagation of cracks for specimens with a/D ratio of 1.7: (<b>a</b>) S17N10FC50; (<b>b</b>) S17N21FC50; (<b>c</b>) S17N10FC40; (<b>d</b>) S17N21FC40.</p>
Full article ">Figure 9
<p>Observed propagation of cracks for specimens with a/D ratio of 2.5: (<b>a</b>) S25N10FC50; (<b>b</b>) S25N21FC50; (<b>c</b>) S25N10FC40; (<b>d</b>) S25N21FC40.</p>
Full article ">Figure 10
<p>Measured V-R relationships: (<b>a</b>) specimens with a/D = 1.7; (<b>b</b>) specimens with a/D = 2.5.</p>
Full article ">Figure 11
<p>Idealization of damage states for ductile concrete structures and/or columns [<a href="#B16-materials-17-05850" class="html-bibr">16</a>,<a href="#B17-materials-17-05850" class="html-bibr">17</a>].</p>
Full article ">Figure 12
<p>Measured residual crack widths: (<b>a</b>) flexural crack; (<b>b</b>) shear crack.</p>
Full article ">Figure 13
<p>Measured residual drift ratios: (<b>a</b>) specimens with a/D = 1.7; (<b>b</b>) specimens with a/D = 2.5.</p>
Full article ">Figure 14
<p>Example of propagation of crack pattern and corresponding FDs (S17N10FC50).</p>
Full article ">Figure 15
<p>Fractal dimension (FD) versus transient drift ratio (R<sub>p</sub>) relationships: (<b>a</b>) specimens with a/D = 1.7; (<b>b</b>) specimens with a/D = 2.5.</p>
Full article ">Figure 16
<p>Definitions of initial stiffness and secant stiffness at different loads and drift ratios.</p>
Full article ">Figure 17
<p>Relative stiffness loss (RSL) versus fractal dimension relationships: (<b>a</b>) specimens with a/D = 1.7; (<b>b</b>) specimens with a/D = 2.5.</p>
Full article ">
21 pages, 3921 KiB  
Article
CFF-Net: Cross-Hierarchy Feature Fusion Network Based on Composite Dual-Channel Encoder for Surface Defect Segmentation
by Ke’er Qian, Xiaokang Ding, Xiaoliang Jiang, Yingyu Ji and Ling Dong
Electronics 2024, 13(23), 4714; https://doi.org/10.3390/electronics13234714 - 28 Nov 2024
Abstract
In industries spanning manufacturing to software development, defect segmentation is essential for maintaining high standards of product quality and reliability. However, traditional segmentation methods often struggle to accurately identify defects due to challenges like noise interference, occlusion, and feature overlap. To solve these [...] Read more.
In industries spanning manufacturing to software development, defect segmentation is essential for maintaining high standards of product quality and reliability. However, traditional segmentation methods often struggle to accurately identify defects due to challenges like noise interference, occlusion, and feature overlap. To solve these problems, we propose a cross-hierarchy feature fusion network based on a composite dual-channel encoder for surface defect segmentation, called CFF-Net. Specifically, in the encoder of CFF-Net, we design a composite dual-channel module (CDCM), which combines standard convolution with dilated convolution and adopts a dual-path parallel structure to enhance the model’s capability in feature extraction. Then, a dilated residual pyramid module (DRPM) is integrated at the junction of the encoder and decoder, which utilizes the expansion convolution of different expansion rates to effectively capture multi-scale context information. In the final output phase, we introduce a cross-hierarchy feature fusion strategy (CFFS) that combines outputs from different layers or stages, thereby improving the robustness and generalization of the network. Finally, we conducted comparative experiments to evaluate CFF-Net against several mainstream segmentation networks across three distinct datasets: a publicly available Crack500 dataset, a self-built Bearing dataset, and another publicly available SD-saliency-900 dataset. The results demonstrated that CFF-Net consistently outperformed competing methods in segmentation tasks. Specifically, in the Crack500 dataset, CFF-Net achieved notable performance metrics, including an Mcc of 73.36%, Dice coefficient of 74.34%, and Jaccard index of 59.53%. For the Bearing dataset, it recorded an Mcc of 76.97%, Dice coefficient of 77.04%, and Jaccard index of 63.28%. Similarly, in the SD-saliency-900 dataset, CFF-Net achieved an Mcc of 84.08%, Dice coefficient of 85.82%, and Jaccard index of 75.67%. These results underscore CFF-Net’s effectiveness and reliability in handling diverse segmentation challenges across different datasets. Full article
24 pages, 13589 KiB  
Review
Recent Advancements in Guided Ultrasonic Waves for Structural Health Monitoring of Composite Structures
by Mohad Tanveer, Muhammad Umar Elahi, Jaehyun Jung, Muhammad Muzammil Azad, Salman Khalid and Heung Soo Kim
Appl. Sci. 2024, 14(23), 11091; https://doi.org/10.3390/app142311091 - 28 Nov 2024
Abstract
Structural health monitoring (SHM) is essential for ensuring the safety and longevity of laminated composite structures. Their favorable strength-to-weight ratio renders them ideal for the automotive, marine, and aerospace industries. Among various non-destructive testing (NDT) methods, ultrasonic techniques have emerged as robust tools [...] Read more.
Structural health monitoring (SHM) is essential for ensuring the safety and longevity of laminated composite structures. Their favorable strength-to-weight ratio renders them ideal for the automotive, marine, and aerospace industries. Among various non-destructive testing (NDT) methods, ultrasonic techniques have emerged as robust tools for detecting and characterizing internal flaws in composites, including delaminations, matrix cracks, and fiber breakages. This review concentrates on recent developments in ultrasonic NDT techniques for the SHM of laminated composite structures, with a special focus on guided wave methods. We delve into the fundamental principles of ultrasonic testing in composites and review cutting-edge techniques such as phased array ultrasonics, laser ultrasonics, and nonlinear ultrasonic methods. The review also discusses emerging trends in data analysis, particularly the integration of machine learning and artificial intelligence for enhanced defect detection and characterization through guided waves. This review outlines the current and anticipated trends in ultrasonic NDT for SHM in composites, aiming to aid researchers and practitioners in developing more effective monitoring strategies for laminated composite structures. Full article
(This article belongs to the Special Issue Application of Ultrasonic Non-destructive Testing)
18 pages, 3048 KiB  
Article
Active Polypropylene Fibers for Controlling Shrinkage Cracks in Cement-Stabilized Materials
by Haibo Cao, Jing Li, Tuanjie Chen, Haisheng Ren and Zhu Qiao
Crystals 2024, 14(12), 1033; https://doi.org/10.3390/cryst14121033 - 28 Nov 2024
Abstract
Conventional polypropylene fibers, characterized by their smooth surfaces, exhibit relatively weak bonding with cement-based materials, limiting their effectiveness in enhancing these materials’ mechanical properties. This study investigates a graft-modified approach to activating polypropylene fibers, introducing amide groups onto their surfaces to improve fiber–matrix [...] Read more.
Conventional polypropylene fibers, characterized by their smooth surfaces, exhibit relatively weak bonding with cement-based materials, limiting their effectiveness in enhancing these materials’ mechanical properties. This study investigates a graft-modified approach to activating polypropylene fibers, introducing amide groups onto their surfaces to improve fiber–matrix interaction. The active polypropylene fibers were produced using an ultraviolet (UV) grafting technique, where maleic anhydride was first used to graft carboxyl groups onto the fiber surfaces, followed by acylation with diethylenetriamine to introduce amide bonds. The optimal experimental conditions were identified by using the degree of amidation as the response metric. Fourier-transform infrared (FTIR) spectroscopy and scanning electron microscopy (SEM) confirmed successful amination and surface activation, with a marked increase in specific surface area. The water contact angle of the active polypropylene fibers decreased significantly from 106.3° to 39.9°, indicating greatly improved wettability by the cement slurry and enhanced bonding strength between the fibers and the cement matrix. To evaluate the effects of the modified fibers, cement-stabilized macadam specimens incorporating various fiber contents were prepared and tested to determine their mechanical properties and shrinkage performance. The results indicated that, compared to conventional polypropylene fibers, the activated polypropylene fibers increased the 28-day compressive strength of CSM by 6.56%, enhanced tensile strength by 4.94%, reduced the rebound modulus by 7.42%, decreased the drying shrinkage coefficient by 25.55%, and lowered the thermal shrinkage coefficient by 13.16%. These findings demonstrate that the chemical bonding between the active polypropylene fibers and the cement matrix is significantly enhanced, leading to improved overall performance in crack resistance, material toughening, and shrinkage mitigation. Full article
(This article belongs to the Section Inorganic Crystalline Materials)
Show Figures

Figure 1

Figure 1
<p>Ultraviolet grafting process of maleic anhydride onto polypropylene fibers.</p>
Full article ">Figure 2
<p>Activation process of polypropylene fiber grafts.</p>
Full article ">Figure 3
<p>FTIR spectra of fibers.</p>
Full article ">Figure 4
<p>SEM images of fibers before and after modifications.</p>
Full article ">Figure 5
<p>Water contact angle of fibers.</p>
Full article ">Figure 6
<p>Microscopic morphology of fiber-enhanced cement-stabilized macadam specimens. (<b>a</b>) is cement-stabilized macadam specimens with ordinary polypropylene fibers; (<b>b</b>) is cement-stabilized macadam specimens with active polypropylene fibers.</p>
Full article ">Figure 7
<p>Trend of compressive strength.</p>
Full article ">Figure 8
<p>Trend of tensile strength.</p>
Full article ">Figure 9
<p>Trend of flexural tensile strength.</p>
Full article ">Figure 10
<p>Trend of rebound modulus.</p>
Full article ">Figure 11
<p>Dry shrinkage coefficient variation.</p>
Full article ">Figure 12
<p>Variation in temperature shrinkage coefficient.</p>
Full article ">
20 pages, 7244 KiB  
Article
Small-Scale and Large-Scale Modeling of Fiber-Reinforced Concrete Girders
by Aleksandar Landović, Arpad Čeh, Anka Starčev-Ćurčin and Miloš Šešlija
Buildings 2024, 14(12), 3812; https://doi.org/10.3390/buildings14123812 - 28 Nov 2024
Abstract
Experimental and computational research on the behavior of small-scale and large-scale fiber-reinforced concrete (FRC) beams is presented in this paper. The experimental part included the small-scale bending tests, which were conducted on three 1.3 m long by 0.1 m wide by 0.15 m [...] Read more.
Experimental and computational research on the behavior of small-scale and large-scale fiber-reinforced concrete (FRC) beams is presented in this paper. The experimental part included the small-scale bending tests, which were conducted on three 1.3 m long by 0.1 m wide by 0.15 m high rectangular simply supported beams, and the large-scale test that was conducted on 12.8 m long by 0.2 m wide by 1.3 m two-chords girder. The concrete mixture in the large-scale test was designed with environmentally more justifiable supplementary materials (binder and fibers), striving for sustainable excellence. To accurately predict the mechanical behavior of tested models, a numerical model incorporating the real nonlinear materials laws is used. A numerical model based on finite element analysis (FEA) is developed. The FEA model is created using a smeared crack approach with a constitutive law for the tensile behavior of FRC derived from an inverse analysis based on prism bending tests. The numerical model is validated against experimental results and the accuracy of numerical predictions based on finite element modeling showed a good correlation with the test data. The FEA-based model makes it easier to predict how FRC structures fail under transversal loading and can serve as a foundation for creating new design processes. Additionally, the presented research is aimed at the feasibility of recycled steel FRC field application in building structures. The usage of recycled steel fibers could achieve environmental benefits through the adoption of sustainable materials. The present study showcased the possibility of modeling reinforced concrete structural building parts made with recycled steel fibers using available software. Full article
(This article belongs to the Section Building Structures)
Show Figures

Figure 1

Figure 1
<p>Dimensions of the beam and reinforcement.</p>
Full article ">Figure 2
<p>(<b>a</b>) Test setup of the beam; (<b>b</b>) cracks on the side of the beam; (<b>c</b>) crack at failure.</p>
Full article ">Figure 3
<p>The geometry of the girder.</p>
Full article ">Figure 4
<p>Reinforcement of the girder.</p>
Full article ">Figure 5
<p>(<b>a</b>) Applied recycled steel fibers; (<b>b</b>) distribution of recycled steel fibers in concrete.</p>
Full article ">Figure 6
<p>Girder with second-phase loading.</p>
Full article ">Figure 7
<p>(<b>a</b>) Lifting of the support; (<b>b</b>) cracks in the final load phase at the measuring Point G; (<b>c</b>) cracks in the final load phase at the measuring Point A.</p>
Full article ">Figure 8
<p>Crack distribution and width in the final load phase.</p>
Full article ">Figure 9
<p>Finite element mesh, supports, and loading.</p>
Full article ">Figure 10
<p>Schematic representation of the maximum load.</p>
Full article ">Figure 11
<p>Reactions of a continuous beam due to unit distributed load.</p>
Full article ">Figure 12
<p>Finite element mesh, supports, and loading of the large girder.</p>
Full article ">Figure 13
<p>Stress–strain relationship of reinforcing steel.</p>
Full article ">Figure 14
<p>Stress–strain response of FRC in tension.</p>
Full article ">Figure 15
<p>Relationship between load and deflection at the mid-span: (<b>a</b>) experimental and FEM results; (<b>b</b>) characteristic points from FEM analysis.</p>
Full article ">Figure 16
<p>Normal stresses in beam: (<b>a</b>) before crack development; (<b>b</b>) after crack development.</p>
Full article ">Figure 17
<p>Cracks in beam at peak load.</p>
Full article ">Figure 18
<p>Normal stresses in reinforcement at peak load.</p>
Full article ">Figure 19
<p>Relationship between load and deflection at the mid-span.</p>
Full article ">Figure 20
<p>Deformations of the girder: (<b>a</b>) at service load; (<b>b</b>) at peak load.</p>
Full article ">Figure 21
<p>Normal stresses in girder.</p>
Full article ">Figure 22
<p>Cracks due to self-weight and maximal experimental load.</p>
Full article ">Figure 23
<p>Cracks in beam at peak load.</p>
Full article ">
12 pages, 3089 KiB  
Article
Effect of Dielectric Layer on Miniaturized Patch Antenna Sensor
by Caifeng Chen, Lei Zou, Chenglong Bi and Andong Wang
Sensors 2024, 24(23), 7608; https://doi.org/10.3390/s24237608 - 28 Nov 2024
Abstract
Miniature patch antenna sensors have great potential in the field of structural health monitoring for crack propagation detection due to their small size and high sensitivity. A primary research focus has been achieving efficient miniaturization, with the performance of the dielectric layer playing [...] Read more.
Miniature patch antenna sensors have great potential in the field of structural health monitoring for crack propagation detection due to their small size and high sensitivity. A primary research focus has been achieving efficient miniaturization, with the performance of the dielectric layer playing a pivotal role. Studies have demonstrated that increasing the relative dielectric constant (εr) of the dielectric layer can reduce antenna size, but higher dielectric losses (tanδ) can lower radiation efficiency. This study identifies the optimal dielectric properties by examining the interplay between εr and tanδ to balance size reduction and radiation efficiency. Additionally, while increasing the dielectric layer’s thickness improves bandwidth and radiation efficiency, a thinner layer is preferred to maintain overall performance without compromising radiation efficiency. Furthermore, the resonant frequency of the smaller-sized patch antenna sensor exhibits greater detection sensitivity to crack propagation. These insights provide useful guidance for selecting effective dielectric layers and assist in the miniaturization design of antenna sensors. Full article
Show Figures

Figure 1

Figure 1
<p>Structure of a coaxial antenna sensor: (<b>a</b>) size of the antenna; (<b>b</b>) position of the feed point.</p>
Full article ">Figure 2
<p>The optimized reflection coefficient of antenna sensors with varying relative dielectric constants of the dielectric layer: (<b>a</b>) S<sub>11</sub>; (<b>b</b>) VSWR.</p>
Full article ">Figure 3
<p>The optimized reflection coefficient of antenna sensors with varying dielectric losses of the dielectric layer: (<b>a</b>) S<sub>11</sub>; (<b>b</b>) VSWR.</p>
Full article ">Figure 4
<p>S<sub>11</sub> and VSWR curves of antenna sensors with varying relative dielectric constant of the dielectric layer at different specified radiation efficiencies: (<b>a</b>,<b>b</b>) 40%; (<b>c</b>,<b>d</b>) 50%; (<b>e</b>,<b>f</b>) 60%.</p>
Full article ">Figure 5
<p>Relationship between relative dielectric constant and critical dielectric loss under predetermined radiation efficiencies: (<b>a</b>) 40%; (<b>b</b>) 50%; (<b>c</b>) 60%.</p>
Full article ">Figure 6
<p>The optimized reflection coefficient of antenna sensors with varying dielectric layer thicknesses: (<b>a</b>) S<sub>11</sub>; (<b>b</b>) VSWR.</p>
Full article ">Figure 7
<p>(<b>a</b>) Relationship between dielectric layer thickness and antenna radiation efficiency; (<b>b</b>) electric field distribution and intensity within dielectric layers of varying thicknesses.</p>
Full article ">Figure 8
<p>Three different-sized antenna sensors: (<b>a</b>) large-sized with Arlon CuClad233 as the dielectric layer; (<b>b</b>) medium-sized with Rogers TMM4 as the dielectric layer; and (<b>c</b>) small-sized with Arlon AR1000 as the dielectric layer. Relationship between resonant frequency and crack propagation for antenna sensors: (<b>d</b>) large-sized; (<b>e</b>) medium-sized; and (<b>f</b>) small-sized. Surface current density profiles on the ground plane of the antenna sensors: (<b>g</b>) large-sized; (<b>h</b>) medium-sized; and (<b>i</b>) small-sized.</p>
Full article ">
25 pages, 16865 KiB  
Review
Magnetic Nanocomposites Based on Iron Oxides as Catalysts of Oxidation Reactions
by Svetlana I. Pomogailo, Evgeny G. Chepaikin, Olga N. Bubelo, Rosa I. Jussupkaliyeva and Leonid M. Kustov
Crystals 2024, 14(12), 1031; https://doi.org/10.3390/cryst14121031 - 28 Nov 2024
Abstract
This review analyzes the use of magnetite-based catalysts in various oxidation reactions. It is shown that magnetite-based catalysts are the most promising candidates from the standpoint of easy separation from the reaction zone and reusability. Diverse examples of the use of magnetite-based composites [...] Read more.
This review analyzes the use of magnetite-based catalysts in various oxidation reactions. It is shown that magnetite-based catalysts are the most promising candidates from the standpoint of easy separation from the reaction zone and reusability. Diverse examples of the use of magnetite-based composites are discussed, including the following reactions: partial oxidation of methane to formaldehyde; the oxidation of cycloalkanes into alcohols and ketones; the oxidation of alkenes and alcohols with the major focus made on benzylic alcohol oxidation; oxidative cracking of alkenes; Fenton-type reactions with H2O2 as a benign oxidant; the removal of dyestuff in water (including wastewater by oxidation); reactions of sulfides and thiols; the oxidation of 5-hydroxymethylfurfural as a platform chemical to 2,5-diformylfuran; the oxidation of D-glucose to D-gluconic acid; and the electrocatalytic oxidation of methanol and ethanol. The most important and best-studied applications of magnetic nanoparticles in the oxidation reactions are believed to be the oxidation of diverse benzylic alcohols and D-glucose, and Fenton-like reactions aiming at the removal of S- and N-compounds from ware and fuels. Magnetic nanocomposites are determined as the materials meeting a range of criteria: (1) they should be magnetic, (2) they contain nanoparticles, and (3) they consist of two (or more) nanocomponents. The core–shell materials with magnetic nanoparticles used as a core or as decorating nanoparticles are discussed in the review. Three main types of magnetic nanocomposites can be distinguished: (1) the systems where the magnetic phase is active in the considered reaction, for instance, Fenton-like oxidation; (2) the systems containing active metal nanoparticles supported onto the magnetic nanoparticles; and (3) materials with magnetic nanoparticles as a core coated with one or two shells (porous or non-porous), with the magnetic nanoparticles being active or not in the title reaction. Magnetic nanoparticles exhibit a number of advantages compared with supported non-magnetic catalysts of oxidation reactions. The advantages include the possibility of separation from the reaction medium (5–10 times) without a significant loss of the activity, their non-toxicity, low cost, and availability, and the easy preparation of these materials. The drawbacks may include the leaching of active components; a decrease in saturation magnetization in comparison with the bulk magnetite; a limited accessibility of active sites due to diffusion through the shells; the complicated composition and structure of the nanomaterials; a decrease in the activity and specific surface area; and a limited number of magnetic compounds with acceptable characteristics. Nevertheless, the advantages of magnetic nanocatalysts stimulate their wide use in liquid-phase oxidation reactions, which will be discussed in the review. Future perspectives on the use of magnetic composites are considered. Full article
Show Figures

Figure 1

Figure 1
<p>The proposed mechanism of the oxidation of alcohols with oxygen using MNS-TEG-IL-TEMPO-Br. Reproduced with permission from [<a href="#B6-crystals-14-01031" class="html-bibr">6</a>].</p>
Full article ">Figure 2
<p>The oxidation reaction of styrene to benzaldehyde and 2-phenyloxyrane.</p>
Full article ">Figure 3
<p>Fe<sub>3</sub>O<sub>4</sub>@Fe-CeO<sub>2</sub>/Ag nanocatalyst.</p>
Full article ">Figure 4
<p>The scheme of the preparation of the Fe<sub>3</sub>O<sub>4</sub>@MMS@ IL-WO<sub>4</sub><sup>2</sup> nanocatalyst and its use in the oxidation of alcohols. Reproduced with permission from [<a href="#B16-crystals-14-01031" class="html-bibr">16</a>].</p>
Full article ">Figure 5
<p>Preparation of Co@GO/Fe<sub>3</sub>O<sub>4</sub>/L-dopa. Reproduced with permission from [<a href="#B18-crystals-14-01031" class="html-bibr">18</a>].</p>
Full article ">Figure 6
<p>Conversion of biomass into 2,5-diformylfurane.</p>
Full article ">Figure 7
<p>The diagram of electron transfer and the formation of active sites between Fe-Zr double active centers. Reproduced with permission from [<a href="#B23-crystals-14-01031" class="html-bibr">23</a>].</p>
Full article ">Figure 8
<p>The oxidation of methylphenyl sulfide on the catalyst MNSPs-PhSO<sub>4</sub>-Sc(OTf).</p>
Full article ">Figure 9
<p>The mechanism of sulfide oxidation on a Sc-based catalyst. Reproduced with permission from [<a href="#B28-crystals-14-01031" class="html-bibr">28</a>].</p>
Full article ">Figure 10
<p>Fe<sub>3</sub>O<sub>4</sub>@SiO<sub>2</sub>-tris(triazine-triamide)-Br<sub>3</sub> catalyst and its activity towards the oxidation of sulfides. Reproduced with permission from [<a href="#B29-crystals-14-01031" class="html-bibr">29</a>].</p>
Full article ">
20 pages, 7648 KiB  
Article
Characterization of Myrrh Extract Effect on Polylactide and Polypropylene Melt Spun Multifilament Yarn Structure and Properties
by Evaldas Bolskis, Egidijus Griškonis, Mindaugas Marksa, Lina Ragelienė and Erika Adomavičiūtė
Materials 2024, 17(23), 5843; https://doi.org/10.3390/ma17235843 - 28 Nov 2024
Abstract
Myrrh has unique medicinal properties: it is an anti-inflammatory, antifungal, and antibacterial material. The aim of this study was to assess the influence of ethanolic myrrh extract on the production and properties of modified PP and PLA melt spun yarns. In this work, [...] Read more.
Myrrh has unique medicinal properties: it is an anti-inflammatory, antifungal, and antibacterial material. The aim of this study was to assess the influence of ethanolic myrrh extract on the production and properties of modified PP and PLA melt spun yarns. In this work, multifilament yarns of polylactide (PLA) and polypropylene (PP) containing 10 wt% myrrh resin at different melt-spinning drawing ratios (DRs) were prepared. The results of scanning electron microscopy revealed that the multifilament yarns from polymers covered by myrrh resin extract had a smooth surface without cracks or visible myrrh derivatives. The influence of myrrh resin on the mechanical properties of PP and PLA multifilament yarns was analyzed, and it was found that the presence of myrrh (PP/M, PLA/M) increased tenacity (cN/tex) and decreased the tensile strain (%) of melt spun yarns obtained at different draw ratios (DRs). During optical analysis, it was found that the absorbance of yarns increased in the entire UV region of the spectra, which was most likely determined by the presence of myrrh. The degree of crystallinity and the wetting angle of PP/M and PLA/M multifilament yarns increased compared with the pure PLA and PP multifilament yarns. This study concludes that the presence of myrrh derivatives influences PLA yarns degradation rate and antibacterial effects against Gram-positive bacteria. Full article
Show Figures

Figure 1

Figure 1
<p>Principal scheme of equipment for measurement of yarn liquid contact angle: (1) Stereoscopic microscope, (2) digital camera, (3) computer, (4) yarn anchorage system, (5) pipette, (6) light source, (7) drop of liquid on the yarn, (8) picture of the video record [<a href="#B53-materials-17-05843" class="html-bibr">53</a>].</p>
Full article ">Figure 2
<p>Bacterial suspension dilution scheme.</p>
Full article ">Figure 3
<p>GC/MS chromatograms of ethanolic myrrh extract.</p>
Full article ">Figure 4
<p>SEM images of (<b>a</b>) PLA3, (<b>b</b>) PLA/M3, (<b>c</b>) PP3, and (<b>d</b>) PP/M3.</p>
Full article ">Figure 5
<p>The dependence on linear density of PP, PP/M, PLA, and PLA/M melt spun yarns at different draw ratios (DRs).</p>
Full article ">Figure 6
<p>The dependence of the tenacity of melt spun yarns PP, PP/M, PLA, and PLA/M on different draw ratio (DR).</p>
Full article ">Figure 7
<p>The dependence of the tensile strain of melt spun yarns ((<b>a</b>)—PP, PP/M; (<b>b</b>)—PLA, PLA/M) on different draw ratios (DRs).</p>
Full article ">Figure 8
<p>UV–Vis spectra of (<b>a</b>) PLA3 and PLA/M3; (<b>b</b>) PP3 and PP/M3.</p>
Full article ">Figure 9
<p>DSC thermograms of (<b>a</b>) PLA3 and PLA/M3; (<b>b</b>) PP3 and PP/M3.</p>
Full article ">Figure 10
<p>Raman spectra of (<b>a</b>) pure PLA3 and PLA/M3; (<b>b</b>) pure PP3 and PP/M3.</p>
Full article ">Figure 11
<p>Comparative Raman spectra of the wavenumber region 1350–1500 cm<sup>−1</sup>.</p>
Full article ">Figure 12
<p>Weight loss of PLA3 and PLA/M3 multifilament yarns.</p>
Full article ">
13 pages, 6097 KiB  
Article
Reduced Graphene Oxide Reinforces Boron Carbide with High-Pressure and High-Temperature Sintering
by Xiaonan Wang, Dianzhen Wang, Kaixuan Rong, Qiang Tao and Pinwen Zhu
Materials 2024, 17(23), 5838; https://doi.org/10.3390/ma17235838 - 28 Nov 2024
Viewed by 46
Abstract
Introducing a second phase has been an effective way to solve the brittleness of boron carbide (B4C) for its application. Though reduced graphene oxide (rGO) is an ideal candidate for reinforcing the B4C duo’s two-dimensional structure and excellent mechanical [...] Read more.
Introducing a second phase has been an effective way to solve the brittleness of boron carbide (B4C) for its application. Though reduced graphene oxide (rGO) is an ideal candidate for reinforcing the B4C duo’s two-dimensional structure and excellent mechanical properties, the toughness is less than 6 MPa·m1/2, or the hardness is lower than 30 GPa in B4C–graphene composites. A barrier to enhancing toughness is the weak interface strength between rGO and B4C, which limits the bridging and pull-out toughening effects of rGO. In this work, internal stress was introduced using a high-pressure and high-temperature (HPHT) method with B4C–rGO composites. The optimal hardness and toughness values for the B4C-2 vol% rGO composite reached 30.1 GPa and 8.6 MPa·m1/2, respectively. The improvement in toughness was 4 times higher than that of pure B4C. The internal stress in the composite increased gradually from 2.3 GPa to 3.3 GPa with an increase in rGO content from 1 vol% to 3 vol%. Crack deflection, bridging, and rGO pull-out are responsible for the improvement in toughness. Moreover, the high internal stress contributed to the formation of good interface strength by embedding rGO into the B4C matrix particles, which further enhanced the dissipation of the crack energy during the pull-out process and led to high toughness. This work provides new insights into synthesizing high-toughness B4C matrix composites. Full article
Show Figures

Figure 1

Figure 1
<p>Relative density of the B<sub>4</sub>C–rGO composites with different rGO contents synthesized at different temperatures.</p>
Full article ">Figure 2
<p>XRD patterns of as-sintered B<sub>4</sub>C–rGO composites. (<b>a</b>) Samples with different rGO contents synthesized at 5 GPa/1400 °C/10 min; (<b>b</b>) B<sub>4</sub>C-2 <span class="html-italic">vol%</span> rGO composites synthesized at 1400–1600 °C.</p>
Full article ">Figure 3
<p>Hardness and fracture toughness profiles of B<sub>4</sub>C–rGO composites. (<b>a</b>–<b>c</b>) Influence of loading force and temperature on the Vickers hardness for samples with different rGO contents; the insets in (<b>a</b>–<b>c</b>) are optical microscopic images of the Vickers indentation at a 9.8 N load; (<b>d</b>) fracture toughness versus rGO content and temperature.</p>
Full article ">Figure 4
<p>SEM images of fracture surface for samples with different rGO contents ((<b>a</b>) 1 <span class="html-italic">vol%</span>, (<b>c</b>) 2 <span class="html-italic">vol%</span>, and (<b>e</b>) 3 <span class="html-italic">vol%</span>) synthesized at 5 GPa/1500 °C/10 min; (<b>b</b>,<b>d</b>,<b>f</b>) shown at a higher magnification.</p>
Full article ">Figure 5
<p>(<b>a</b>) SEM image of Vickers hardness indentation produced at a load of 9.8 N on the polished surface of B<sub>4</sub>C-2 <span class="html-italic">vol%</span> rGO sample synthesized at 5 GPa/1500 °C/10 min; (<b>b</b>) pull-out of rGO; (<b>c</b>) crack bridging and deflection; (<b>d</b>) EDS hierarchical image of element distribution in (<b>c</b>); (<b>e</b>) Raman spectra of B<sub>4</sub>C-2 <span class="html-italic">vol%</span> rGO sample, taken from a crack caused by Vickers indentation; (<b>f</b>) Raman spectra of un-sintered mixed powers.</p>
Full article ">Figure 6
<p>(<b>a</b>,<b>d</b>) TEM images of B<sub>4</sub>C-<span class="html-italic">2 vol%</span> rGO composite synthesized at 5 GPa/1500 °C/10 min; (<b>b</b>,<b>e</b>) HRTEM image of the square area in (<b>a</b>,<b>d</b>), respectively; (<b>c</b>,<b>f</b>) higher magnification of (<b>b</b>,<b>e</b>).</p>
Full article ">Figure 7
<p>C 1s XPS spectra of GO powders (<b>a</b>) and rGO after HPHT sintering at 5 GPa/1500 °C/10 min (<b>b</b>).</p>
Full article ">Figure 8
<p>Raman spectra of un-sintered mixed powers and B<sub>4</sub>C–rGO composites with different rGO contents synthesized at 5 GPa/1500 °C/10 min.</p>
Full article ">Figure 9
<p>Plot of the Vickers hardness and fracture toughness of this work in comparison with previous reports.</p>
Full article ">
39 pages, 17841 KiB  
Review
Low-Temperature Cracking and Improvement Methods for Asphalt Pavement in Cold Regions: A Review
by Rui Ma, Yiming Li, Peifeng Cheng, Xiule Chen and Aoting Cheng
Buildings 2024, 14(12), 3802; https://doi.org/10.3390/buildings14123802 - 28 Nov 2024
Viewed by 100
Abstract
The advantages of asphalt pavement in terms of driving comfort, construction efficiency, and ease of maintenance have established it as the predominant choice for high-grade pavements at present. However, being highly sensitive to temperature and stress, asphalt performance is significantly influenced by external [...] Read more.
The advantages of asphalt pavement in terms of driving comfort, construction efficiency, and ease of maintenance have established it as the predominant choice for high-grade pavements at present. However, being highly sensitive to temperature and stress, asphalt performance is significantly influenced by external environmental conditions and loading, making it susceptible to various distress phenomena. Particularly in high-latitude regions, asphalt pavement cracking severely limits asphalt pavement’s functional performance and service lifespan under cold climatic conditions. To enhance the low-temperature cracking resistance of asphalt pavement in cold regions, tools such as VOS viewer 1.6.20 and Connected Papers were utilized to systematically organize, analyze, and summarize relevant research from the past 40 years. The results reveal that temperature shrinkage cracks and thermal fatigue cracks represent the primary forms of asphalt pavement distress in these regions. Cracking in asphalt pavement in cold regions is primarily influenced by structural design, pavement materials, construction technology, and climatic conditions. Among these factors, surface layer stiffness, base layer type, and the rate of temperature decrease exert the most significant impact on cracking resistance, collectively accounting for approximately 45.4% of all cracking-related factors. The low-temperature performance of asphalt pavement can be effectively improved through several strategies, including adopting full-thickness asphalt pavement with a skeleton-dense structure or reduced average particle size, incorporating functional layers, appropriately increasing the thickness of the upper layer and the compaction temperature of the lower layer, utilizing continuous surface layer construction techniques, and applying advanced materials. High-performance modifiers such as SBR and SBS, nanomaterials with good low-temperature performance, and warm mixing processes designed for cold regions have proven particularly effective. Among various improvement methods, asphalt modification has demonstrated superior effectiveness in enhancing the deformation capacity of asphalt and its mixtures, significantly boosting the low-temperature performance of asphalt pavements. Asphalt modification accounts for approximately 50% of the improvement methods evaluated in this study, with an average improvement in low-temperature performance reaching up to 143%. This paper provides valuable insights into the underlying causes of cracking distress in asphalt pavements in cold regions and offers essential guidance for improving the service quality of such pavements in these challenging environments. Full article
(This article belongs to the Section Building Materials, and Repair & Renovation)
Show Figures

Figure 1

Figure 1
<p>Distribution of cold regions in China (Alberts projection) [<a href="#B2-buildings-14-03802" class="html-bibr">2</a>].</p>
Full article ">Figure 2
<p>The proportion of asphalt pavement distress in cold regions.</p>
Full article ">Figure 3
<p>Literature growth diagram.</p>
Full article ">Figure 4
<p>VOS viewer density view.</p>
Full article ">Figure 5
<p>VOS viewer relational view.</p>
Full article ">Figure 6
<p>A PRISMA flow chart of the literature review.</p>
Full article ">Figure 7
<p>Temperature shrinkage cracks [<a href="#B9-buildings-14-03802" class="html-bibr">9</a>]. (<b>a</b>) A thermal stress curve of pavement with different cooling amplitudes throughout the day. (<b>b</b>) The maximum thermal stresses in the structural layers of pavements at different cooling rates.</p>
Full article ">Figure 8
<p>Thermal fatigue cracks. (<b>a</b>) Daily variation in thermal stress on pavement structure [<a href="#B9-buildings-14-03802" class="html-bibr">9</a>]. (<b>b</b>) Daily variation in thermal stress at different depths [<a href="#B9-buildings-14-03802" class="html-bibr">9</a>]. (<b>c</b>) Vertical deformation curves of pavements throughout year [<a href="#B14-buildings-14-03802" class="html-bibr">14</a>].</p>
Full article ">Figure 9
<p>Reflection cracking mechanism.</p>
Full article ">Figure 10
<p>Aging cracks. (<b>A</b>) Physical hardening ratio of AC and SMA at −20 °C [<a href="#B21-buildings-14-03802" class="html-bibr">21</a>]. (<b>B</b>) Changes in asphalt components [<a href="#B22-buildings-14-03802" class="html-bibr">22</a>]. (<b>C</b>) Microstructure of asphalt degraded by pseudomonas aeruginosa at different times ((a) undegraded control group; (b) degradation for 15 days; (c) degradation for 30 days; (d) degradation for 45 days) [<a href="#B23-buildings-14-03802" class="html-bibr">23</a>].</p>
Full article ">Figure 11
<p>Factor radar chart [<a href="#B24-buildings-14-03802" class="html-bibr">24</a>].</p>
Full article ">Figure 12
<p>Proportion diagram of influencing factors [<a href="#B25-buildings-14-03802" class="html-bibr">25</a>].</p>
Full article ">Figure 13
<p>Influencing factors. (<b>A</b>) <b>a</b>. Daily average temperature T<sub>max</sub>-T<sub>min</sub> temperature gradient diagram. <b>b</b>. Temperature gradient calculation of highest and lowest temperature of road surface [<a href="#B51-buildings-14-03802" class="html-bibr">51</a>]. (<b>B</b>) Flexural tensile strength of asphalt mixture after ultraviolet aging [<a href="#B54-buildings-14-03802" class="html-bibr">54</a>]. (<b>C</b>) Freeze–thaw cycles in fracture stress test results [<a href="#B55-buildings-14-03802" class="html-bibr">55</a>].</p>
Full article ">Figure 14
<p>Evaluation method. (<b>a</b>) Burgers model [<a href="#B71-buildings-14-03802" class="html-bibr">71</a>]. (<b>b</b>) Creep model fitting [<a href="#B71-buildings-14-03802" class="html-bibr">71</a>]. (<b>c</b>) Relationship curve between T<sub>g</sub> of asphalt and asphalt mixture and flexural failure strain ε of mixture [<a href="#B73-buildings-14-03802" class="html-bibr">73</a>]. (<b>d</b>) Three-plate skateboard viscometer [<a href="#B79-buildings-14-03802" class="html-bibr">79</a>]. (<b>e</b>) Correlation between limiting phase angle temperature and BBR [<a href="#B82-buildings-14-03802" class="html-bibr">82</a>]. (<b>f</b>) Correlation between limiting phase angle temperature and EBBR [<a href="#B82-buildings-14-03802" class="html-bibr">82</a>].</p>
Full article ">Figure 15
<p>Continuous construction machinery scheme [<a href="#B84-buildings-14-03802" class="html-bibr">84</a>]. (<b>a</b>) Construction equipment layout. (<b>b</b>) Material transfer scheme.</p>
Full article ">Figure 16
<p>Comparison of different paving compaction processes [<a href="#B85-buildings-14-03802" class="html-bibr">85</a>].</p>
Full article ">Figure 17
<p>The influence of the continuous paving and compaction process (the red circle is a local enlarged image) [<a href="#B86-buildings-14-03802" class="html-bibr">86</a>]. (<b>a</b>) The corresponding relationship between the times of lower layer compaction and the maximum principal stress. (<b>b</b>) The corresponding relationship between the lower layer compaction temperature and the maximum principal stress. (<b>c</b>) The relationship between the thickness of the upper layer and the maximum principal stress (different braking conditions).</p>
Full article ">Figure 18
<p>Pavement structure.</p>
Full article ">Figure 19
<p>Principle of stress-absorbing layer improvement [<a href="#B89-buildings-14-03802" class="html-bibr">89</a>].</p>
Full article ">Figure 20
<p>A 400× fluorescence micrograph ((<b>a</b>) 2% SBR-modified asphalt; (<b>b</b>) 4% SBR-modified asphalt; (<b>c</b>) 6% SBR-modified asphalt; (<b>d</b>) 8% SBR-modified asphalt) [<a href="#B95-buildings-14-03802" class="html-bibr">95</a>].</p>
Full article ">Figure 21
<p>Low-temperature performance of 2, 4, 6, and 8% SBR-modified asphalt ((<b>a</b>) stiffness modulus S value; (<b>b</b>) creep rate m value) [<a href="#B95-buildings-14-03802" class="html-bibr">95</a>].</p>
Full article ">Figure 22
<p>NR-modified binder with 100× magnification [<a href="#B96-buildings-14-03802" class="html-bibr">96</a>].</p>
Full article ">Figure 23
<p>Fluorescence micrograph of SBS-modified high-permeability asphalt (F300) [<a href="#B107-buildings-14-03802" class="html-bibr">107</a>].</p>
Full article ">Figure 24
<p>Maximum bending strain of best oil–stone ratio of SEBS at low temperature [<a href="#B113-buildings-14-03802" class="html-bibr">113</a>].</p>
Full article ">Figure 25
<p>Ductility change curve of TPS with different dosages [<a href="#B116-buildings-14-03802" class="html-bibr">116</a>].</p>
Full article ">Figure 26
<p>Microstructure diagram. (<b>a</b>) SEM diagram of diatomite [<a href="#B117-buildings-14-03802" class="html-bibr">117</a>]. (<b>b</b>) OMMT through-layer structure [<a href="#B118-buildings-14-03802" class="html-bibr">118</a>]. (<b>c</b>) SEM diagram of tourmaline lamellar structure [<a href="#B119-buildings-14-03802" class="html-bibr">119</a>]. (<b>d</b>) SEM diagram of basalt fiber [<a href="#B120-buildings-14-03802" class="html-bibr">120</a>].</p>
Full article ">Figure 27
<p>Influencing factors of nano-process. (<b>a</b>) Ductility and nano-modifier content. (<b>b</b>) Effect of preparation time on ductility. (<b>c</b>) Effect of temperature on ductility [<a href="#B137-buildings-14-03802" class="html-bibr">137</a>].</p>
Full article ">Figure 28
<p>Creep stiffness of different nanomaterial particle sizes [<a href="#B137-buildings-14-03802" class="html-bibr">137</a>]. (<b>a</b>) Effect of nano-SiC particle size on stiffness. (<b>b</b>) Effect of nano-ZnO particle size on stiffness.</p>
Full article ">Figure 29
<p>Analysis of improvement methods. (<b>a</b>) Proportion of types of low-temperature performance improvement methods. (<b>b</b>) Comparison of improvement effects.</p>
Full article ">
16 pages, 12125 KiB  
Article
Impact of Sintering Aid Type and Content on the Mechanical Properties of Digital Light Processing 3D-Printed Si3N4 Ceramics
by Qing Qin, Lin Han, Gang Xiong, Zihan Guo, Junwei Huang, Yujuan Zhang, Zhen Shen and Changchun Ge
Materials 2024, 17(23), 5830; https://doi.org/10.3390/ma17235830 - 27 Nov 2024
Viewed by 300
Abstract
Digital light processing (DLP) 3D-printed Si₃N₄ ceramics, known for their exceptional performance, offer distinct advantages in meeting the high-strength and complex structural demands of industries such as aerospace, semiconductors, healthcare, automotive, energy, and machinery. However, due to Si₃N₄’s strong chemical stability, low diffusion [...] Read more.
Digital light processing (DLP) 3D-printed Si₃N₄ ceramics, known for their exceptional performance, offer distinct advantages in meeting the high-strength and complex structural demands of industries such as aerospace, semiconductors, healthcare, automotive, energy, and machinery. However, due to Si₃N₄’s strong chemical stability, low diffusion rate, low self-sintering ability, and high melting point, achieving densification under conventional sintering conditions is challenging. As a result, sintering additives are essential to promote the sintering process, lower the sintering temperature, improve densification, and enhance performance. In this study, 45 vol% Si₃N₄ slurries were prepared using DLP 3D printing technology, incorporating nine different combinations of sintering additives, including aluminum oxide (Al2O3), yttrium oxide (Y2O3), and aluminum nitride (AlN), in various ratios with Si3N4. The slurries were then sintered at 1800 °C for 2 h under a 1 MPa N2 atmosphere. Additionally, the phase composition, microstructure, grain distribution, and crack propagation of the materials. The results showed that a Si3N4 to Al2O3 and Y2O3 ratio of 95:2.5:2.5 produced elongated β-Si3N4 grain structures and enhanced density, achieving a maximum Vickers hardness of 12.88 ± 0.52 GPa. Additionally, the synergistic toughening effect of the rod-like β-Si3N4 grains and sintering aids significantly improved the fracture toughness of the Si3N4 ceramic matrix, with a flexural strength of 540.63 ± 10.05 MPa and a fracture toughness of 4.92 ± 0.07 MPa·m1/2. This study lays the foundation for the future application of 3D-printed Si3N4 ceramics, optimization of sintering aid combinations at different ratios, and performance enhancement in extreme environments. Full article
Show Figures

Figure 1

Figure 1
<p>Different application fields of Si<sub>3</sub>N<sub>4</sub> ceramics.</p>
Full article ">Figure 2
<p>DLP 3D printing process.</p>
Full article ">Figure 3
<p>XRD patterns of obtained Si<sub>3</sub>N<sub>4</sub> ceramic samples sintered at 1800 °C for 2 h with different samples.</p>
Full article ">Figure 4
<p>SEM micrographs of Si<sub>3</sub>N<sub>4</sub> ceramics with different samples.</p>
Full article ">Figure 5
<p>SEM micrographs and grains diameter distributions of Si<sub>3</sub>N<sub>4</sub> ceramics after ion etching for 300 s for different samples.</p>
Full article ">Figure 6
<p>Mapping of Si<sub>3</sub>N<sub>4</sub> ceramics with different samples.</p>
Full article ">Figure 7
<p>(<b>a</b>) Shrinkage rate and (<b>b</b>) relative density of different samples.</p>
Full article ">Figure 8
<p>The mechanical performance of sintered samples with different samples.</p>
Full article ">Figure 9
<p>SEM micrographs of Vickers indents and crack propagation for samples N1–N9.</p>
Full article ">Figure 10
<p>(<b>a</b>) SEM image of the N1 sample after 300 s of particle etching post gas pressure sintering; (<b>b</b>) Schematic diagram illustrating the fracture and toughening mechanisms present in the N1 sample.</p>
Full article ">
7 pages, 1334 KiB  
Article
Preparation of Diamond Films with Cracked Textures on Stainless Steel Using W/W-N Film as an Interlayer
by Xiao Li, Yule Shan, Fan Xia, Chengke Chen, Shaohua Lu and Xiaojun Hu
Coatings 2024, 14(12), 1494; https://doi.org/10.3390/coatings14121494 - 27 Nov 2024
Viewed by 251
Abstract
The growth of diamond film with texture on stainless steel can significantly improve its wear properties, while conventional methods such as laser etching and ultrasonic vibration superimposed machining suffered from complex processes and extra equipment. Here, we propose a simple new method to [...] Read more.
The growth of diamond film with texture on stainless steel can significantly improve its wear properties, while conventional methods such as laser etching and ultrasonic vibration superimposed machining suffered from complex processes and extra equipment. Here, we propose a simple new method to prepare textured diamond film on stainless steel without any special apparatus. In this method, a W/W-N interlayer was first deposited on the stainless steel surface, and then the sample with the interlayer was put into a hot filament chemical vapor deposition (HFCVD) chamber to grow diamond films. The interlayer becomes cracked during the warm-up stage due to the large tensile stress formed by the thermal expansion coefficient difference between the interlayer and the steel. Then the deposited diamond films copy the morphology of the interlayer, forming the textured diamond film. The textured diamond film exhibits a small amount of stress, ~3.4 GPa, and greatly improved wear resistance. Our results provide a way to prepare textured diamond films with good wear resistance. Full article
16 pages, 2023 KiB  
Article
Statistical Evaluation of Uniform Temperature and Thermal Gradients for Composite Girder of Tibet Region Using Meteorological Data
by Yujuan Liu, Zhiyuan Ma and Jiang Liu
Buildings 2024, 14(12), 3798; https://doi.org/10.3390/buildings14123798 - 27 Nov 2024
Viewed by 226
Abstract
To accurately assess the temperature action and effect of steel-concrete composite girder bridges in plateau and cold areas, this paper investigated nearly 50 years of historical meteorological data from 26 meteorological observation stations in the Tibet region of China. Based on the most [...] Read more.
To accurately assess the temperature action and effect of steel-concrete composite girder bridges in plateau and cold areas, this paper investigated nearly 50 years of historical meteorological data from 26 meteorological observation stations in the Tibet region of China. Based on the most unfavorable extreme meteorological data at each meteorological station, a finite element model was used to analyze the temperature field of the composite girder. The most unfavorable values of temperature were obtained. The regional differences in temperature actions at different meteorological stations were analyzed, and the isotherm maps of the extreme values of the uniform temperature and thermal gradients were further obtained based on spatial interpolation methods in the ArcGIS program. The study shows that the uniform temperature is significantly affected by the climatic environment, and the isotherm maps provide a visual representation of the geographic distribution pattern of temperature extremes. The maximum and minimum uniform temperatures in Tibet range from 18.28 °C to 42.27 °C and from −41.07 °C to 4.71 °C respectively. The maximum regional difference of positive and negative thermal gradient reaches 11.32 °C and 7.69 °C respectively. The temperature effects calculated using the most unfavorable values of the isotherm map are all more unfavorable than the specification calculations. In particular, the tensile stress of the concrete under the positive thermal gradient reaches 2.91 MPa, which exceeds the standard value of the tensile strength of concrete. This is a significant risk factor for cracking. The compressive stress of the steel girder under a negative thermal gradient reaches 19.35 MPa, which represents a 136% increase compared to the specified value. This increase elevates the risk of instability in the steel girder. Full article
(This article belongs to the Special Issue Advances in Steel–Concrete Composite Structures)
21 pages, 6499 KiB  
Article
Influence of Cu Content Variation on the Tribological Properties of Ni60CuMo with Sandwich-Structured Composite Coatings by Laser Cladding
by Fengqin Ji, Xincheng Li, Songyang Zhang and Ming Pang
Micromachines 2024, 15(12), 1429; https://doi.org/10.3390/mi15121429 - 27 Nov 2024
Viewed by 229
Abstract
To enhance the tribological properties of the coatings and to inhibit cracking, sandwich-structured composite coatings were fabricated, consisting of a Ni60CuMo/IN718 transition layer and a Ni60CuMo/Ni-coated Cu wear-resistant layer with four different Ni-coated Cu contents. The results indicate that the transition layer inhibits [...] Read more.
To enhance the tribological properties of the coatings and to inhibit cracking, sandwich-structured composite coatings were fabricated, consisting of a Ni60CuMo/IN718 transition layer and a Ni60CuMo/Ni-coated Cu wear-resistant layer with four different Ni-coated Cu contents. The results indicate that the transition layer inhibits the crack formation in the coating, and the refined grain structure stabilizes its average hardness at approximately 485 HV0.5. Increasing the Cu content in the wear-resistant layer exacerbates the segregation of the Cu-rich solid solution phases and refines the in situ-generated Cr7C3, TiC, and NbC phases. The average hardness of the wear-resistant layer decreases from 474 HV0.5 to 408 HV0.5 as the Ni-coated Cu content increases from zero to 75%. The coating with 50% Ni-coated Cu has the best Cu self-lubricating properties and exhibits the best wear resistance at both room and high temperatures. At room temperature, abrasive wear is the primary wear mechanism in the coatings. Although the ductility of the coatings is improved with increasing Cu content, excessive Cu reduces the hardness and load-bearing capacity. At 300 °C, oxidation wear becomes the dominant wear mechanism, accompanied by plastic deformation and three-body wear as the Cu content increases. At 500 °C, severe oxidation wear is the dominant mechanism, with excessive Cu leading to oxidation film failure. Full article
(This article belongs to the Special Issue Future Prospects of Additive Manufacturing)
Show Figures

Figure 1

Figure 1
<p>Schematic of laser cladding of multilayer structural coatings.</p>
Full article ">Figure 2
<p>Macroscopic morphologies and penetration test results of the studied coatings for (<b>a1</b>,<b>a2</b>) C1 coating, (<b>b1</b>,<b>b2</b>) C2 coating, (<b>c1</b>,<b>c2</b>) C3 coating, and (<b>d1</b>,<b>d2</b>) C4 coating.</p>
Full article ">Figure 3
<p>Normalized X-ray diffraction diagram of the four studied coatings with different Cu contents.</p>
Full article ">Figure 4
<p>The microstructure of the four wear-resistant layers with different Cu contents. (<b>a1</b>–<b>d1</b>) is the upper area for C1–C4 coatings, (<b>a2</b>–<b>d2</b>) is the lower area for C1–C4 coatings.</p>
Full article ">Figure 5
<p>The mechanism of microstructure forming during the preparation of the wear-resistant layer. (<b>a</b>) the laser cladding processes of transition layer and wear-resistant layer, (<b>b</b>) the Ti and Nb elements in the transition layer diffused into the wear-resistant layer, (<b>c1,c2</b>) the elements floating up from the transition layer form the reinforced phases in the molten pool of the wear-resistant layer, (<b>c3</b>) minimal Cu segregation in the Cu-poor wear-resistant layer, (<b>c4</b>) pronounced Cu segregation in the Cu-rich wear-resistant layer.</p>
Full article ">Figure 6
<p>Microstructure of transition layers of the four studied coatings. (<b>a</b>) C1 coating, (<b>b</b>) C2 coating, (<b>c</b>) C3 coating, and (<b>d</b>) C4 coating.</p>
Full article ">Figure 7
<p>Hardness distribution at different locations from the surface of the coating to the substrate.</p>
Full article ">Figure 8
<p>Coefficient of the friction curves of the studied coatings at RT, 300 °C, and 500 °C, respectively.</p>
Full article ">Figure 9
<p>Wear rate of the studied coatings at room temperature, 300 °C, and 500 °C.</p>
Full article ">Figure 10
<p>Worn morphologies of the studied coatings at room temperature. (<b>a1</b>,<b>a2</b>) C1 Coating, (<b>b1</b>,<b>b2</b>) C2 Coating, (<b>c1</b>,<b>c2</b>) C3 Coating, (<b>d1</b>,<b>d2</b>) C4 Coating.</p>
Full article ">Figure 11
<p>Worn morphologies of the studied coatings at 300 °C. (<b>a1</b>,<b>a2</b>) C1 Coating, (<b>b1</b>,<b>b2</b>) C2 Coating, (<b>c1</b>,<b>c2</b>) C3 Coating, (<b>d1</b>,<b>d2</b>) C4 Coating.</p>
Full article ">Figure 12
<p>Worn morphologies of the studied coatings at 500 °C. (<b>a1</b>,<b>a2</b>) C1 Coating, (<b>b1</b>,<b>b2</b>) C2 Coating, (<b>c1</b>,<b>c2</b>) C3 Coating, (<b>d1</b>,<b>d2</b>) C4 Coating.</p>
Full article ">Figure 13
<p>Schematic diagrams of wear mechanisms of the studied coatings. (<b>a1</b>–<b>a3</b>) Cu-poor, Cu-rich, and Cu-excessive coatings at RT; (<b>b1</b>–<b>b3</b>) Cu-poor, Cu-rich, and Cu-excessive coatings at 300 °C; <b>(c1</b>–<b>c3</b>) Cu-poor, Cu-rich and Cu-excessive coatings at 500 °C.</p>
Full article ">Figure 13 Cont.
<p>Schematic diagrams of wear mechanisms of the studied coatings. (<b>a1</b>–<b>a3</b>) Cu-poor, Cu-rich, and Cu-excessive coatings at RT; (<b>b1</b>–<b>b3</b>) Cu-poor, Cu-rich, and Cu-excessive coatings at 300 °C; <b>(c1</b>–<b>c3</b>) Cu-poor, Cu-rich and Cu-excessive coatings at 500 °C.</p>
Full article ">
Back to TopTop