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Search Results (5,350)

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Keywords = bond strength

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16 pages, 2379 KiB  
Article
Investigation of the Effect of Indirect Ultrasonic Force and Different Cements on the Bond Strength of Glass Fiber Posts in Teeth with Different Post Space Preparation Methods
by Naz Caner, Leyla Benan Ayrancı and Bengi Gülgü
Appl. Sci. 2024, 14(20), 9523; https://doi.org/10.3390/app14209523 (registering DOI) - 18 Oct 2024
Abstract
(1) Background: The main aim of this study was to investigate the effects of different cements (Panavia V5, RelyX U200) and placement techniques (indirect ultrasonic vibration and manual method) on the bond strength of glass fiber posts in teeth with different post space [...] Read more.
(1) Background: The main aim of this study was to investigate the effects of different cements (Panavia V5, RelyX U200) and placement techniques (indirect ultrasonic vibration and manual method) on the bond strength of glass fiber posts in teeth with different post space preparation methods and to evaluate the failure types. (2) Methods: A total of 120 human upper central teeth were collected for the study. One week after root canal treatment, 10 mm long post space preparation was performed using post drills. Post spaces were irrigated in three different ways, namely NaOCl, NaOCl + EDTA solutions, and passive ultrasonic irrigation of NaOCl and EDTA solutions. Glass fiber posts were divided into two groups for resin cement systems, namely RelyX U200 (3M ESPE) or Panavia V5 (Kuraray Medical). Two different methods, namely the indirect ultrasonic vibration and the manual method, were applied for post placement. Then, 1.2 mm sections were taken from the middle and coronal regions of the inserted fiber posts for a push-out test. (3) Results: the Irrigation × Cement (p = 0.002), Cement × Section (p = 0.043) and Placement × Section (p = 0.049) pairwise interactions were statistically significant. (4) Conclusions: in our study, the effects of different post cavity preparations, different cement types, and different placement techniques on the bond strength of the fiber post were observed. Full article
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Figure 1
<p>Flowchart of the methodology.</p>
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<p>SMART-X #5 ultrasonic tip.</p>
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<p>(<b>A</b>) Cylindrical metal tip (Ø = 0.8 mm) positioned on the fiber post perpendicular to the section surface. (<b>B</b>) Representative image of the load direction and push-out test.</p>
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<p>Representative stereomicroscope images of failure modes of (<b>A</b>) adhesive failure between the dentin and cement, (<b>B</b>) adhesive failure between the post and cement, (<b>C</b>) cohesive failure of the post, and (<b>D</b>) mixed type, a combination of two or more of the other types.</p>
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<p>Interval plot diagram of bonding strength values of experimental groups.</p>
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<p>Distribution rate of failure types according to level and cement types.</p>
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18 pages, 5770 KiB  
Article
Assessment of Physical and Mechanical Parameters of Spun-Bond Nonwoven Fabric
by Inga Lasenko, Jaymin Vrajlal Sanchaniya, Sai Pavan Kanukuntla, Arta Viluma-Gudmona, Sandra Vasilevska and Sanjay Rajni Vejanand
Polymers 2024, 16(20), 2920; https://doi.org/10.3390/polym16202920 - 17 Oct 2024
Viewed by 213
Abstract
The selection of an appropriate fabric for technical applications, such as protective masks, hinges on a thorough understanding of the fabric’s physical and mechanical properties. This study addresses the challenge of selecting the optimal material structure for the upper layer of a protective [...] Read more.
The selection of an appropriate fabric for technical applications, such as protective masks, hinges on a thorough understanding of the fabric’s physical and mechanical properties. This study addresses the challenge of selecting the optimal material structure for the upper layer of a protective mask, aiming to ensure adequate breathability while providing effective filtration against airborne particles and contaminants. We assessed and compared the physical–mechanical properties of five polymer spun-bond nonwoven fabrics from different suppliers. Our comprehensive evaluation included, as follows: a visual inspection; light permeability analysis; mass and thickness measurements; elongation and tensile strength tests; breathing resistance assessments; and filter penetration tests with paraffin oil. The results revealed significant variations in performance among the samples, with one fabric consistently outperforming the others across multiple parameters. Notably, this top-performing fabric met or exceeded the EN 149:2001+A1:2009 standard for breathing resistance and filtration efficiency and, in combination with additional filter layers, met the requirements or exceeded class FFP2 (filtering face piece). This study underscores the importance of meticulous material selection and quality control in optimizing PPE (personal protective equipment) performance and user safety, providing valuable insights for mask manufacturers and healthcare professionals. Full article
(This article belongs to the Special Issue Polymers: Bio-Based Medical Textile)
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Figure 1
<p>Image of the prepared multi-layered FFP2 respirator mask utilized in this study.</p>
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<p>Microscopic surfaces of samples for morphological analysis: (<b>a</b>) S1; and (<b>b</b>) S5. Scale 2000 μm.</p>
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<p>Microscopic lateral curved surface of samples: (<b>a</b>) S1 with dangling filament (red); and (<b>b</b>) S5.</p>
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<p>Visual comparison of light permeability/propagation of nonwoven fabrics: (<b>a</b>) S2; and (<b>b</b>) S5. Scale in cm.</p>
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<p>Representative force–elongation graph of samples S1 to S5 in: (<b>a</b>) MD; and (<b>b</b>) CMD.</p>
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<p>The structure of the nonwoven material at the point of rupture with density of fibers (red): (<b>a</b>) S1; and (<b>b</b>) S5.</p>
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22 pages, 3101 KiB  
Article
Optimized Proportioning Techniques and Roadway Performance Evaluation of Colored Asphalt Pavement Materials
by Silin Fan, Shaopeng Zheng, Jian Ma, Liangliang Chen, Xiao Li and Cheng Cheng
Sustainability 2024, 16(20), 8996; https://doi.org/10.3390/su16208996 - 17 Oct 2024
Viewed by 226
Abstract
This study systematically investigated the formulation optimization, performance evaluation, and practical application of epoxy-based composite materials for colored asphalt pavement. By conducting comprehensive experiments, we optimized the composition of epoxy-based composites, verifying their excellent bonding performance, good heat resistance, and UV aging resistance [...] Read more.
This study systematically investigated the formulation optimization, performance evaluation, and practical application of epoxy-based composite materials for colored asphalt pavement. By conducting comprehensive experiments, we optimized the composition of epoxy-based composites, verifying their excellent bonding performance, good heat resistance, and UV aging resistance under various temperature conditions. The key optimized component ratios were determined as a 1:1 blend of Type I and Type II epoxy resins, 30 phr of curing agent, 10 phr of toughening agent, 5 phr of diluent, 10% filler, 12% flame retardant, and 10% pigment. At the recommended dosage of 2.0 kg/m2 of epoxy binder, the composite structure exhibited the best reinforcement effect, improving low-temperature performance significantly. Compared to ordinary asphalt mixtures, the colored pavement composite structure showed superior mechanical strength, deformation capacity, high-temperature stability (dynamic stability approximately three times higher), and water stability (TSR values up to 95.5%). Furthermore, its fatigue life decay rate was significantly lower, with fatigue limit loading frequencies more than three times those of ordinary asphalt mixtures, demonstrating excellent fatigue resistance. This study provides strong technical support and a theoretical basis for the development and practical application of colored asphalt pavement. Full article
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<p>Relationship between curing agent content and tensile properties.</p>
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<p>Relationship between the amount of toughener and tensile properties.</p>
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<p>Relationship between the amount of diluent and tensile properties and viscosity.</p>
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<p>The relationship between the amount of flame retardant and tensile properties.</p>
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<p>Dumbbell-shaped specimen after pouring.</p>
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<p>Tensile experiment.</p>
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<p>Results of epoxy binder pull-out tests with different paving amounts.</p>
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<p>Tensile and shear test results of epoxy binders at different curing temperatures.</p>
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<p>Rutting test results.</p>
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<p>Comparison of load stress between control group and color pavement fatigue test.</p>
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15 pages, 1812 KiB  
Article
Tensile and Bending Strength of Birch and Beech Lamellas Finger Jointed with Conventional and Newly Developed Finger-Joint Profiles
by Hannes Stolze and Holger Militz
Materials 2024, 17(20), 5063; https://doi.org/10.3390/ma17205063 - 17 Oct 2024
Viewed by 195
Abstract
In this study, the tensile and bending strength of birch and beech lamellas finger jointed with conventional (Standard) and newly developed finger-joint profiles (New) are presented. Polyurethane (PUR), Melamine-Urea-Formaldehyde (MUF) and Phenol-Resorcinol-Formaldehyde (PRF) adhesive systems were used to bond [...] Read more.
In this study, the tensile and bending strength of birch and beech lamellas finger jointed with conventional (Standard) and newly developed finger-joint profiles (New) are presented. Polyurethane (PUR), Melamine-Urea-Formaldehyde (MUF) and Phenol-Resorcinol-Formaldehyde (PRF) adhesive systems were used to bond the finger joints. The objective of the New profiles was to reduce the stress concentrations within the finger joint by cutting the cross-grooved fingers perpendicular to the main orientation of the finger-joint profile. In the first trials of the development, larger cross-grooved fingers were cut with the aim to improve the stress distribution and to reinforce the finger joint by filling gaps in the finger joint with adhesive. As the study progressed, initial optimisations of the New profile were made. Smaller cross-grooved fingers were cut as it was assumed that they are beneficial for the manufacturing and integrity of the New profile. In combination with the MUF adhesive system, the New profile achieved the highest increase in the bending and tensile strengths compared to the Standard profile. In addition to the increased strength, other advantages such as reduced cracking in the finger joint were observed when using the New profile. The high strength and stiffness of hardwoods or other high-performance materials used in timber construction can probably be better exploited in combination with the New profile. Further tests will be carried out by considering different configurations of the New profile and different materials. Full article
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Figure 1
<p>Typical profile of a structural finger joint according to EN 15497 [<a href="#B11-materials-17-05063" class="html-bibr">11</a>]. Finger length (l<sub>j</sub>), finger pitch (p), finger angle (α), tip gap (l<sub>t</sub>), tip width (b<sub>cut</sub>) and finger base (Z) (<b>a</b>). The distribution of the longitudinal stresses in a finger joint (stresses increase from blue to red) [<a href="#B12-materials-17-05063" class="html-bibr">12</a>] (<b>b</b>).</p>
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<p>Schematic of modified finger-joint profiles, inclination of the finger-joint profile according to [<a href="#B25-materials-17-05063" class="html-bibr">25</a>] (<b>a</b>) and shifted fingers according to [<a href="#B18-materials-17-05063" class="html-bibr">18</a>,<a href="#B23-materials-17-05063" class="html-bibr">23</a>] (<b>b</b>).</p>
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<p>The experimental workflow of this study.</p>
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<p>Sketches of the produced finger shapes and their finger length.</p>
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<p>Manufacturing of the newly developed <span class="html-italic">New<sub>initial</sub></span> profile.</p>
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<p>The test setup of the tensile (<b>a</b>) and bending strength tests (<b>b</b>) with the dimensions of the birch lamella specimens.</p>
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<p><span class="html-italic">New</span> profiles after cutting (<b>a</b>), and the adhesive leakage in the finger joint with the <span class="html-italic">Standard</span> and <span class="html-italic">New<sub>intial</sub></span> profiles (<b>b</b>).</p>
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<p>Adhesive filling within the <span class="html-italic">New<sub>initial</sub></span> profile and sample images of the test specimens, which were considered representative of the adhesives, after tensile testing.</p>
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<p>The tensile strength of the finger-jointed birch and Control lamellas (<b>a</b>). The relation between the MOE before finger jointing and the tensile strength of the MUF<span class="html-italic">Ni</span>700 lamellas (<b>b</b>).</p>
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<p>Bending strength of the finger-jointed birch and Control specimens (<b>a</b>). The relation between the density and bending strength of the MUF<span class="html-italic">Ni</span>700 and MUF<span class="html-italic">Ni</span>350 finger-jointed specimens (<b>b</b>).</p>
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<p>The tensile strength of the finger-jointed beech and Control lamellas (<b>a</b>). The relation between the MOE before finger jointing and the tensile strength of the Control and MUF<span class="html-italic">Nm</span>350 lamellas (<b>b</b>).</p>
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18 pages, 32353 KiB  
Article
Numerical Simulation and Experimental Study of Deposition Behavior for Cold Sprayed Dual Nano HA/30 wt.% Ti Composite Particle
by Miao Sun, Xiao Chen, Zecheng Wu, Chengdi Li and Xianfeng Deng
Coatings 2024, 14(10), 1330; https://doi.org/10.3390/coatings14101330 - 17 Oct 2024
Viewed by 184
Abstract
Hydroxyapatite (HA, Ca10(PO4)6(OH)2) composite coatings added in the second phase could improve the mechanical properties and bonding strength. The cold spraying technique, as a technology for the deposition of solid particles at low temperatures, is [...] Read more.
Hydroxyapatite (HA, Ca10(PO4)6(OH)2) composite coatings added in the second phase could improve the mechanical properties and bonding strength. The cold spraying technique, as a technology for the deposition of solid particles at low temperatures, is employed to deposit HA ceramic composite coatings. The nano HA material possesses characteristics that enhance properties and promote interface bonding. Due to the exceptional mechanical properties of Ti material, adding Ti particles could improve the mechanical properties of nano HA/Ti composite coatings. In order to explore the deposition deformation mechanism of composite particles under different cold spraying conditions, numerical simulation and experimental testing of deposition behaviors of dual nano HA/Ti composite particles were analyzed. As the particle velocity increased from 400 m/s to 800 m/s in the numerical simulation analysis, the more serious the deposition deformation. Meanwhile, more cracking and splashing phenomena occurred on the surface of the particle. By analyzing the stress value curve of Ti and HA units under different particle velocities, it was found that the adiabatic shear instability phenomenon occurred during the particle deposition on the substrate. In addition, the degree of particle deformation increased with the decrease in the particle size. The results of the experimental investigation were consistent with that of the numerical simulation. Full article
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Figure 1
<p>The surface and cross-sectional morphologies of HA/30 wt.% Ti powders: (<b>a</b>,<b>b</b>) surface, (<b>c</b>) cross-section.</p>
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<p>The size distribution of HA/30 wt.% Ti powders.</p>
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<p>The XRD patterns of HA/30 wt.% Ti powders.</p>
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<p>The TEM micrograph of dual nano HA/30 wt.% Ti powders.</p>
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<p>Simulation meshing of spherical particle model.</p>
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<p>The spherical particle surface morphology after the random distribution.</p>
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<p>The spherical particle partial section view after the random distribution: (<b>a</b>) 10 μm, (<b>b</b>) 20 μm, (<b>c</b>) 30 μm.</p>
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<p>Simulation meshing of the substrate model.</p>
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<p>Integrated model of composite particle and substrate: (<b>a</b>) 10 μm, (<b>b</b>) 20 μm, (<b>c</b>) 30 μm.</p>
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<p>Deposition simulation morphologies of the composite particles at different particle velocities: (<b>a</b>,<b>b</b>) 400 m/s, (<b>c</b>,<b>d</b>) 500 m/s, (<b>e</b>,<b>f</b>) 600 m/s, (<b>g</b>,<b>h</b>) 700 m/s, (<b>i</b>,<b>j</b>) 800 m/s.</p>
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<p>Deposition simulation morphologies of the composite particles at different particle velocities: (<b>a</b>,<b>b</b>) 400 m/s, (<b>c</b>,<b>d</b>) 500 m/s, (<b>e</b>,<b>f</b>) 600 m/s, (<b>g</b>,<b>h</b>) 700 m/s, (<b>i</b>,<b>j</b>) 800 m/s.</p>
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<p>Compression ratio of the composite particles.</p>
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<p>Stress curves of Ti particle units of the composite particles after deposition at different particle velocities: (<b>a</b>) 400 m/s, (<b>b</b>) 500 m/s, (<b>c</b>) 600 m/s, (<b>d</b>) 700 m/s, (<b>e</b>) 800 m/s.</p>
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<p>Stress curves of HA particle units of the composite particles after deposition at different particle velocities: (<b>a</b>) 400 m/s, (<b>b</b>) 500 m/s, (<b>c</b>) 600 m/s, (<b>d</b>) 700 m/s, (<b>e</b>) 800 m/s.</p>
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<p>Stress curves of HA particle units of the composite particles after deposition at different particle velocities: (<b>a</b>) 400 m/s, (<b>b</b>) 500 m/s, (<b>c</b>) 600 m/s, (<b>d</b>) 700 m/s, (<b>e</b>) 800 m/s.</p>
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<p>Deposition simulation morphologies of the composite particles under different particle sizes: (<b>a</b>,<b>b</b>) 10 μm, (<b>c</b>,<b>d</b>) 20 μm, (<b>e</b>,<b>f</b>) 30 μm.</p>
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<p>Deposition simulation morphologies of the composite particles under different particle sizes: (<b>a</b>,<b>b</b>) 10 μm, (<b>c</b>,<b>d</b>) 20 μm, (<b>e</b>,<b>f</b>) 30 μm.</p>
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<p>Surface morphologies of the splat deposited on 316L stainless steel at different gas temperatures: (<b>a</b>) 300 °C, (<b>b</b>) 500 °C, (<b>c</b>) 700 °C.</p>
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<p>Surface morphologies of the splat deposited on Ti6Al4V at different gas temperatures: (<b>a</b>) 300 °C, (<b>b</b>) 500 °C, (<b>c</b>) 700 °C.</p>
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<p>Surface morphologies of the splat deposited on HA/Ti layer at different gas temperatures: (<b>a</b>) 300 °C, (<b>b</b>) 500 °C, (<b>c</b>) 700 °C.</p>
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<p>Morphologies of the splat deposited on 316L stainless steel at different gas temperatures: (<b>a</b>) 300 °C, (<b>b</b>) 500 °C, (<b>c</b>) 700 °C.</p>
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<p>Surface morphologies of the composite particle deposited on 316L stainless steel at a gas temperature of 300 °C: (<b>a</b>) 10 μm, (<b>b</b>) 20 μm, (<b>c</b>) 30 μm.</p>
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15 pages, 9601 KiB  
Article
Comparative Study of Unhatched and Hatched Chicken Egg Shell-Filled Glass Fibre/Polyester Composites
by Suhas Kowshik, Sathyashankara Sharma, Sathish Rao, S. V. Udaya Kumar Shetty, Prateek Jain, Pavan Hiremath, Nithesh Naik and Maitri Manjunath
J. Compos. Sci. 2024, 8(10), 432; https://doi.org/10.3390/jcs8100432 - 17 Oct 2024
Viewed by 289
Abstract
The incorporation of filler materials to enhance the properties of fibre-reinforced plastics is a prevalent practise in materials science. Calcium carbonate is a commonly used inorganic filler in composite fabrication. Eggshell, a rich source of calcium carbonate, offers an organic alternative to conventional [...] Read more.
The incorporation of filler materials to enhance the properties of fibre-reinforced plastics is a prevalent practise in materials science. Calcium carbonate is a commonly used inorganic filler in composite fabrication. Eggshell, a rich source of calcium carbonate, offers an organic alternative to conventional inorganic fillers. This study investigates the efficacy of different types of eggshells as filler materials. Three variants, viz., unhatched raw eggshell, unhatched boiled eggshell, and post-hatched eggshell, were used to fabricate composite variants, which were then subjected to mechanical characterization and compared with unfilled composites. The results indicated that composites filled with unhatched eggshells outperformed those with post-hatched eggshells. Tensile testing revealed a significant enhancement in the tensile properties of all eggshell-filled composites in comparison to the unfilled ones. The composite variant filled with unhatched raw eggshell filler showcased the utmost tensile modulus and strength, with a notable 36% improvement in comparison with the unfilled variant. Similarly, flexural tests demonstrated a 53% increase in flexural strength for unhatched raw eggshell-filled composites over unfilled composites. SEM imaging confirmed these findings by showing crack arrests, deviations, particle distribution, and strong interfacial bonding in the eggshell-filled composites. Full article
(This article belongs to the Section Polymer Composites)
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<p>Methodology.</p>
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<p>Eggshell filler processing.</p>
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<p>Ball milling.</p>
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<p>Tensile testing in UTM.</p>
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<p>Tensile test specimens of (<b>a</b>) unfilled, (<b>b</b>) unhatched raw eggshell-filled, (<b>c</b>) unhatched boiled eggshell-filled, (<b>d</b>) post-hatched eggshell-filled composite variants.</p>
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<p>Flexural strength testing in UTM.</p>
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<p>Flexural test specimens of (<b>a</b>) unfilled, (<b>b</b>) unhatched raw eggshell-filled, (<b>c</b>) unhatched boiled eggshell-filled, (<b>d</b>) post-hatched eggshell-filled composite variants.</p>
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<p>Comparison of tensile strengths.</p>
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<p>Comparison of tensile modulus.</p>
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<p>Comparison of tensile stress–strain variation.</p>
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<p>Comparison of flexural strength.</p>
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<p>Comparison of flexural modulus.</p>
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<p>Comparison of flexural stress–strain variation.</p>
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<p>SEM images of (<b>a</b>) unobstructed crack propagation in unfilled composite; (<b>b</b>) meagre interfacial bonding of fibre and matrix in unfilled composite; (<b>c</b>) superior interfacial bonding and crack deviation in unhatched raw eggshell-filled composite; (<b>d</b>) crack deviation in unhatched raw eggshell-filled composite; (<b>e</b>) superior interfacial bonding in boiled eggshell-filled composite; (<b>f</b>) crack deviation in boiled eggshell-filled composite; (<b>g</b>) crack deviation in post-hatched eggshell-filled composite; (<b>h</b>) crack deviation in post-hatched composites.</p>
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18 pages, 2752 KiB  
Article
In-Depth Theoretical Investigations of Borazine’s Aromaticity: Tailoring Electron Delocalization through Substituent Effects
by Alex-Cristian Tomut, Ionut-Tudor Moraru and Gabriela Nemes
Molecules 2024, 29(20), 4902; https://doi.org/10.3390/molecules29204902 - 16 Oct 2024
Viewed by 287
Abstract
The current study investigates the influence of several R substituents (e.g., Me, SiH3, F, Cl, Br, OH, NH2, etc.) on the aromaticity of borazine, also known as the “inorganic benzene”. By performing hybrid DFT methods, blended with several computational [...] Read more.
The current study investigates the influence of several R substituents (e.g., Me, SiH3, F, Cl, Br, OH, NH2, etc.) on the aromaticity of borazine, also known as the “inorganic benzene”. By performing hybrid DFT methods, blended with several computational techniques, e.g., Natural Bond Orbital (NBO), Quantum Theory of Atoms in Molecules (QTAIM), Gauge-Including Magnetically Induced Current (GIMIC), Nucleus-Independent Chemical Shift (NICS), and following a simultaneous evaluation of four different aromaticity indices (para-delocalization index (PDI), multi-centre bond order (MCBO), ring current strength (RCS), and NICS parameters), it is emphasized that the aromatic character of B-substituted (B3R3N3H3) and N-substituted (B3H3N3R3) borazine derivatives can be tailored by modulating the electronic effects of R groups. It is also highlighted that the position of R substituents on the ring structure is crucial in tuning the aromaticity. Systematic comparisons of calculated aromaticity index values (i.e., via regression analyses and correlation matrices) ensure that the reported trends in aromaticity variation are accurately described, while the influence of different R groups on electron delocalization and related aromaticity phenomena is quantitatively assessed based on NBO analyses. The most relevant interactions impacting the aromatic character of investigated systems are (i) the electron conjugations occurring between the p lone pair electrons (LP) on the F, Cl, Br, O or N atoms, of R groups, and the π*(B=N) orbitals on the borazine ring (i.e., LP(R)→π*(B=N) donations), and (ii) the steric-exchange (Pauli) interactions between the same LP and the π(B=N) bonds (i.e., LP(R)↔π(B=N) repulsions), while inductive/field effects influence the aromaticity of the investigated trisubstituted borazine systems to a much lesser extent. This work highlights that although the aromatic character of borazine can be enhanced by grafting electron-donor substituents (F, OH, NH2, O, NH) on the N atoms, the stabilization due to aromaticity has only a moderate impact on these systems. By replacing the H substituents on the B atoms with similar R groups, the aromatic character of borazine is decreased due to strong exocyclic LP(R)→π*(B=N) donations affecting the delocalization of π-electrons on the borazine ring. Full article
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Graphical abstract

Graphical abstract
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<p>Equilibrium geometries of the most stable conformations for B<sub>3</sub>R<sub>3</sub>N<sub>3</sub>H<sub>3</sub> and B<sub>3</sub>H<sub>3</sub>N<sub>3</sub>R<sub>3</sub> model systems, obtained by selectively replacing the H substituents grafted on the B (<b>a</b>–<b>i</b>) and on the N (<b>j</b>–<b>r</b>) atoms with several R substituents (R = Me, SiH<sub>3</sub>, F, Cl, Br, OH, NH<sub>2</sub>, CN, and NO<sub>2</sub>).</p>
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<p>The orthonormalized electronic (MCBO and PDI) and magnetic (∫NICS<sub>π,zz</sub> and RCS) aromaticity indices computed for the B-substituted borazine model systems, represented with respect to borazine.</p>
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<p>The most relevant secondary electronic effects that impact the aromaticity of B<sub>3</sub>R<sub>3</sub>N<sub>3</sub>H<sub>3</sub> model systems: conjugation (upper part) and Pauli repulsion (lower part).</p>
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<p>The correlation between the conjugation effects and the aromaticity indices computed for the B<sub>3</sub>R<sub>3</sub>N<sub>3</sub>H<sub>3</sub> (R = F, Cl, Br, conjugated and non-conjugated OH, and non-conjugated NH<sub>2</sub>) model systems.</p>
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<p>The orthonormalized electronic (MCBO and PDI) and magnetic (∫NICS<sub>π,zz</sub> and RCS) aromaticity indices of N-substituted borazine models are represented with respect to borazine.</p>
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<p>The orthonormalized electronic (MCBO and PDI) and magnetic (∫NICS<sub>π,zz</sub> and RCS) aromaticity indices of N-substituted borazine models are represented with respect to borazine.</p>
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<p>The correlation between the Pauli repulsive interactions and the orthonormalized aromaticity indices for B<sub>3</sub>H<sub>3</sub>N<sub>3</sub>R<sub>3</sub> (R = F, Cl, Br, OH, NH<sub>2</sub>) models.</p>
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25 pages, 10644 KiB  
Article
Shear Strengthening of RC Beams Incorporating Post-Tensioned Bars and Engineered Cementitious Composite Reinforced with Palm Fronds
by Ahmed Hamoda, Aref A. Abadel, Khaled Sennah, Mizan Ahmed, Xihong Zhang and Mohamed Emara
Buildings 2024, 14(10), 3277; https://doi.org/10.3390/buildings14103277 - 16 Oct 2024
Viewed by 256
Abstract
This paper investigates, experimentally and numerically, the shear strengthening of Normal Concrete (NC) beams using post-tensioning steel bars and Engineered Cementitious Composite (ECC) reinforced with chemically cured Palm Fronds (PFs). The benefits of strain-hardening ECC and the tensile strength of PFs cured with [...] Read more.
This paper investigates, experimentally and numerically, the shear strengthening of Normal Concrete (NC) beams using post-tensioning steel bars and Engineered Cementitious Composite (ECC) reinforced with chemically cured Palm Fronds (PFs). The benefits of strain-hardening ECC and the tensile strength of PFs cured with 6% wt Alkali NaOH solution beside post-tensioned bars have been employed herein. Seven full-scale Reinforced Concrete (RC) beams were fabricated and experimented with under three-point loading until failure. The test parameters include the strengthening technique, type, and configuration of the material used for strengthening. The strengthening process has been implemented through two techniques: Externally Bonded Reinforcement (EBR) and Near-Surface Mounted (NSM) Reinforcement. The strengthening materials have been configured and placed in horizontal, vertical, and inclined positions. The effectiveness of the strengthening methods has been evaluated by examining their cracking propagations, load-deflection responses, collapse modes, elastic stiffness, and absorbed energy. It was found that the proposed strengthening systems could significantly control the crack pattern and failure mode, and they could enhance the ultimate load amplitude up to 37% and 50% for NSM ECC with PFs and EBR post-tensioning steel bars, respectively. Nonlinear three-dimensional finite element models of the tested beams were developed and validated with the test data, where it was found that finite element models predict the structural performance of tested beams with a maximum error of only 2%. Full article
(This article belongs to the Special Issue Sustainable Development of Concrete and Composite Structures)
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<p>Reinforcement details of the tested beams [<a href="#B35-buildings-14-03277" class="html-bibr">35</a>].</p>
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<p>Schematic details of beams in group G1: (<b>a</b>) Beam P-E-H, (<b>b</b>) Beam P-E-V, and (<b>c</b>) Beam P-E-I.</p>
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<p>Schematic details of beams in group G1: (<b>a</b>) Beam P-E-H, (<b>b</b>) Beam P-E-V, and (<b>c</b>) Beam P-E-I.</p>
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<p>Schematic details of beams in group G2: (<b>a</b>) Beam Pr-E-H, (<b>b</b>) Beam Pr-E-V, and (<b>c</b>) Beam Pr-E-I.</p>
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<p>Schematic details of beams in group G2: (<b>a</b>) Beam Pr-E-H, (<b>b</b>) Beam Pr-E-V, and (<b>c</b>) Beam Pr-E-I.</p>
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<p>Uniaxial tensile tests of (<b>a</b>) concrete, (<b>b</b>) steel bars, (<b>c</b>) test set-up for PF, and (<b>d</b>) failure mode of PF.</p>
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<p>Uniaxial tensile tests of (<b>a</b>) concrete, (<b>b</b>) steel bars, (<b>c</b>) test set-up for PF, and (<b>d</b>) failure mode of PF.</p>
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<p>Stress–strain curves of the used materials. (<b>a</b>) Compressive/tensile performance of NC [<a href="#B37-buildings-14-03277" class="html-bibr">37</a>], (<b>b</b>) compressive performance of ECC [<a href="#B38-buildings-14-03277" class="html-bibr">38</a>], (<b>c</b>) tensile performance of ECC, (<b>d</b>) tensile performance of steel bars, and (<b>e</b>) tensile performance of Palm Fronds.</p>
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<p>Preparation of the strengthening process using PFs and ECC for group G1; (<b>a</b>) the chemical curing of the Palm Fronds with a 6% wt Alkali NaOH solution; (<b>b</b>) the removal of the concrete cover; (<b>c</b>) the bonding of PFs using epoxy; (<b>d</b>) the re-covering of the beam’s surface using ECC; and (<b>e</b>) the leveling of the ECC cover.</p>
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<p>Preparation of the strengthening process using PFs and ECC for group G1; (<b>a</b>) the chemical curing of the Palm Fronds with a 6% wt Alkali NaOH solution; (<b>b</b>) the removal of the concrete cover; (<b>c</b>) the bonding of PFs using epoxy; (<b>d</b>) the re-covering of the beam’s surface using ECC; and (<b>e</b>) the leveling of the ECC cover.</p>
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<p>Strengthening implementation using external post-tensioning steel bars of group G2: (<b>a</b>) Beam Pr-H, (<b>b</b>) Beam Pr-V, (<b>c</b>) Beam Pr-I, and (<b>d</b>) manual post-tensioning procedure.</p>
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<p>Test setup of the beams. (<b>a</b>) Geometric details and (<b>b</b>) the view of the experimental set-up.</p>
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<p>Typical crack and failure pattern for the control beam.</p>
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<p>Crack patterns and failure modes for group G1 strengthened with NSM PFs and ECC: (<b>a</b>) P-E-H; (<b>b</b>) P-E-V; and (<b>c</b>) P-E-I.</p>
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<p>Crack patterns and failure modes for group G1 strengthened with NSM PFs and ECC: (<b>a</b>) P-E-H; (<b>b</b>) P-E-V; and (<b>c</b>) P-E-I.</p>
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<p>Crack patterns and failure modes for post-tensioned group G2: (<b>a</b>) Pr-H, (<b>b</b>) Pr-V, and (<b>c</b>) Pr-I.</p>
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<p>Jacking load–vertical deflection relationship: (<b>a</b>) group G1 and (<b>b</b>) group G2.</p>
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<p>Elastic stiffness of beams in (<b>a</b>) group G1 and (<b>b</b>) group G2.</p>
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<p>Energy absorption capacity of beams in (<b>a</b>) group G1 and (<b>b</b>) group G2.</p>
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<p>FEM model details.</p>
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<p>Comparisons of the load-deflection relationships obtained from the FEM and experiment.</p>
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<p>Comparisons of the failure modes of the tested beams with the numerical predictions (<b>a</b>) beam B0, (<b>b</b>) P-E-H, (<b>c</b>) P-E-V, and (<b>d</b>) P-E-I.</p>
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<p>Comparisons of the failure modes of the tested beams with the numerical predictions (<b>a</b>) beam B0, (<b>b</b>) P-E-H, (<b>c</b>) P-E-V, and (<b>d</b>) P-E-I.</p>
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12 pages, 1850 KiB  
Article
Efficacy of Atmospheric Pressure Plasma Jet-Induced Surface Treatment on Wettability, Surface Topography, and Shear Bond Strength of Ceramic Surfaces for CAD-On Assembly
by Haidar Alalawi, Ziyad Al Mutairi, Omar Al Abbasi, Fatima Al Dossary, Manayer Husain, Faleh Al Ghubari, Sultan Akhtar and Moamen A. Abdalla
Prosthesis 2024, 6(5), 1228-1239; https://doi.org/10.3390/prosthesis6050088 - 16 Oct 2024
Viewed by 253
Abstract
This study evaluated the effectiveness of atmospheric pressure plasma jet (APPJ) treatment on the surface characteristics and bond strength of zirconia and lithium disilicate ceramics for CAD-on restorations. A total of 70 cylindrical-shaped specimens of lithium disilicate and 70 disc-shaped specimens of Y-TZP [...] Read more.
This study evaluated the effectiveness of atmospheric pressure plasma jet (APPJ) treatment on the surface characteristics and bond strength of zirconia and lithium disilicate ceramics for CAD-on restorations. A total of 70 cylindrical-shaped specimens of lithium disilicate and 70 disc-shaped specimens of Y-TZP zirconia were machined, thermally processed, surface-treated, and then resin-bonded. The specimens were grouped according to the following surface treatments: no surface treatment, sandblasting, plasma, sandblasting followed by plasma, sandblasting followed by universal adhesive, plasma followed by universal adhesive, and sandblasting and plasma treatment followed by universal adhesive. The treated surfaces were subjected to a wettability assessment via contact angle measurement and a topography assessment using scanning electron microscopy (SEM). The cemented assembly was subjected to shear bond strength testing with a universal testing machine, and the results were imported to SPSS 23.0 for statistical analysis. The results show that APPJ treatment induced a significantly low contact angle for both ceramics with no surface alteration upon scanning. Moreover, APPJ treatment produced a bonded assembly with a shear bond strength comparable to sandblasting. In conclusion, APPJ treatment should be considered an efficient surface treatment with a non-destructive nature that surpasses sandblasting with the provision of a high shear bond strength between CAD-on ceramics. Full article
(This article belongs to the Special Issue Advancements in Adhesion Techniques and Materials in Prosthodontics)
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<p>Testing setup chart and specimen grouping.</p>
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<p>Specimen assembly.</p>
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<p>The contact angle of zirconia/lithium disilicate specimens after different surface treatments. (<b>A</b>) no treatment; (<b>B</b>) sandblasting; (<b>C</b>) plasma; and (<b>D</b>) plasma and sandblasting.</p>
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<p>Scanning electron microscopy images of zirconia/lithium disilicate specimens after different surface treatments. (<b>A</b>) no treatment; (<b>B</b>) sandblasting; (<b>C</b>) plasma; and (<b>D</b>) plasma and sandblasting.</p>
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24 pages, 26404 KiB  
Article
Effects of Different Surface Treatment Methods on Laser Welding of Aluminum Alloy and Glass
by Changjun Chen, Lei Li, Min Zhang and Wei Zhang
Coatings 2024, 14(10), 1318; https://doi.org/10.3390/coatings14101318 (registering DOI) - 15 Oct 2024
Viewed by 378
Abstract
Hermetic glass-to-metal sealing (GMTS) technology combines metal and glass and can be used to construct vacuum tubes; electric discharge tubes; semiconductor diodes; reed switches; and pressure-tight glass-to-metal windows, optical windows, and lenses in electronics or electronic systems. The hermetic and mechanically strong seals [...] Read more.
Hermetic glass-to-metal sealing (GMTS) technology combines metal and glass and can be used to construct vacuum tubes; electric discharge tubes; semiconductor diodes; reed switches; and pressure-tight glass-to-metal windows, optical windows, and lenses in electronics or electronic systems. The hermetic and mechanically strong seals engineered using GTMS are highly reliable, making them suitable for deployment in harsh environments and for applications requiring high performance. However, it has always been challenging to precisely and robustly join glass and metal due to the significant disparities in their properties. In this study, the laser transmission welding of borosilicate glass and aluminum alloy using a pulsed Nd:YAG laser to achieve hermetic glass–metal seals was experimentally investigated. This research focused on various processing parameters and the influence of surface conditions on bonding quality. Three different types of surfaces—a polished surface, a surface subjected to preoxidation, and a laser-modified surface—were compared. To evaluate the weld strength, shear-tensile separation forces were measured. The analysis of fracture and separation encompassed detailed examinations of the weld morphology, microstructure, and elemental composition. The results revealed that increasing the laser welding energy initially enhanced the weld strength until a saturation point was reached. Among the three different surface treatments tested, the laser surface modification of aluminum alloy yielded the highest weld strength. The maximum achieved bond force exceeded 35.38 N, demonstrating the feasibility of using cost-effective pulsed laser welding for glass-to-metal sealing. The results were significantly better than those from previous research in which aluminum alloy surfaces were pretreated using microarc oxidation. Full article
(This article belongs to the Special Issue Laser-Assisted Processes and Thermal Treatments of Materials)
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<p>Welding schematic diagram for the laser welding glass to aluminum alloy (<b>left picture</b>); shear force test diagram (<b>right picture</b>).</p>
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<p>Macroscopic morphology of aluminum alloy after furnace oxidation at different temperatures: (<b>a</b>) not oxidized; (<b>b</b>) 450 °C; (<b>c</b>) 500 °C; (<b>d</b>) 600 °C.</p>
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<p>Trend of absorbance on aluminum alloy surface when different high-temperature oxidation parameters are used.</p>
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<p>High-temperature oxidation cross-section, surface morphology, and EDS results: (<b>a</b>,<b>a1</b>) no high-temperature oxidation was performed; (<b>b</b>,<b>b1</b>) after high-temperature oxidation; (<b>a</b>,<b>b</b>) cross-section; (<b>a1</b>,<b>b1</b>).</p>
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<p>High-temperature oxidation cross-section, surface morphology, and EDS results: (<b>a</b>,<b>a1</b>) no high-temperature oxidation was performed; (<b>b</b>,<b>b1</b>) after high-temperature oxidation; (<b>a</b>,<b>b</b>) cross-section; (<b>a1</b>,<b>b1</b>).</p>
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<p>Morphology of welded fracture after thermal oxidation: (<b>a</b>) aluminum alloy side; (<b>b</b>) glass side.</p>
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<p>Morphology of welded fracture after thermal oxidation: (<b>a</b>) aluminum alloy side; (<b>b</b>) glass side.</p>
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<p>EDS spot scan spectrum of high-temperature oxidized aluminum alloy and glass weld fracture: (<b>a</b>) aluminum alloy side; (<b>b</b>) glass side.</p>
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<p>Schematic diagram of welding after thermal oxidation.</p>
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<p>Three-dimensional scanning of alloy surface after grinding with different mesh sandpaper ((<b>a</b>): 180; (<b>b</b>): 600; (<b>c</b>): 1000; (<b>d</b>): 2000).</p>
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<p>Schematic material exchange diagram.</p>
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<p>Schematic diagram for the welding of the samples polished with 180-mesh sandpaper.</p>
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<p>Fracture morphology after shear test for the samples polished using different mesh sandpaper. ((<b>a</b>): 180 mesh; (<b>b</b>): 600 mesh; (<b>c</b>): 1000 mesh).</p>
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<p>Fracture morphology after shear test for the samples polished using different mesh sandpaper. ((<b>a</b>): 180 mesh; (<b>b</b>): 600 mesh; (<b>c</b>): 1000 mesh).</p>
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<p>Fracture observed using three-dimensional scanning for different mesh sandpaper. ((<b>a</b>): 180; (<b>b</b>): 600; (<b>c</b>): 1000).</p>
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<p>Schematic diagram of the laser scan track.</p>
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<p>Aluminum alloy substrate surface melted with different laser powers ((<b>a</b>): 150 W; (<b>b</b>): 200 W; (<b>c</b>): 250 W; (<b>d</b>): 300 W).</p>
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<p>Three-dimensional morphology of samples treated with different laser powers. (<b>a</b>): untreated; (<b>b</b>): 150 W; (<b>c</b>): 200 W; (<b>d</b>): 250 W; (<b>e</b>): 300 W).</p>
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<p>Cross-section of aluminum alloy’s microstructure after laser treatment and EDS results.</p>
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<p>Surface SEM image of aluminum alloy’s microstructure after laser treatment and EDS results.</p>
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<p>Shear force test results with different laser powers.</p>
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<p>Fracture EDS images of samples subjected to different laser pretreatment powers. (<b>left</b>: metal side; <b>right</b>: glass side; (<b>a</b>): 150 W; (<b>b</b>): 200 W; (<b>c</b>): 250 W; (<b>d</b>): 300 W).</p>
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<p>Fracture EDS images of samples subjected to different laser pretreatment powers. (<b>left</b>: metal side; <b>right</b>: glass side; (<b>a</b>): 150 W; (<b>b</b>): 200 W; (<b>c</b>): 250 W; (<b>d</b>): 300 W).</p>
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<p>Fracture EDS images of samples subjected to different laser pretreatment powers. (<b>left</b>: metal side; <b>right</b>: glass side; (<b>a</b>): 150 W; (<b>b</b>): 200 W; (<b>c</b>): 250 W; (<b>d</b>): 300 W).</p>
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<p>Fracture EDS images of samples subjected to different laser pretreatment powers. (<b>left</b>: metal side; <b>right</b>: glass side; (<b>a</b>): 150 W; (<b>b</b>): 200 W; (<b>c</b>): 250 W; (<b>d</b>): 300 W).</p>
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<p>The weld cross-sections of the samples subjected to different laser pretreatment powers and EDS map analysis results ((<b>a</b>): 150 W; (<b>b</b>): 200 W; (<b>c</b>): 250 W; (<b>d</b>): 300 W).</p>
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<p>The weld cross-sections of the samples subjected to different laser pretreatment powers and EDS map analysis results ((<b>a</b>): 150 W; (<b>b</b>): 200 W; (<b>c</b>): 250 W; (<b>d</b>): 300 W).</p>
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<p>Surface morphology of aluminum alloy following different surface treatments: (<b>a</b>) not processed; (<b>b</b>) laser surface treatment; (<b>c</b>) thermal oxidation at 500 °C for 6 h; (<b>d</b>) 180-mesh sandpaper sanding.</p>
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<p>Trend of absorbance of aluminum alloy surface following different surface treatments.</p>
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<p>Temperature-dependent <sup>18</sup>O, <sup>30</sup>Si and <sup>26</sup>Al diffusion in 2/1-mullite single crystals parallel to the b ([0 1 0]) and c ([0 0 1]) axes. Note that the atomic diffusion of species is isotropic with respect to the mullite crystal structure. <span class="html-italic">T</span>, temperature; <span class="html-italic">D</span>, diffusion coefficients ([<a href="#B28-coatings-14-01318" class="html-bibr">28</a>,<a href="#B29-coatings-14-01318" class="html-bibr">29</a>,<a href="#B30-coatings-14-01318" class="html-bibr">30</a>,<a href="#B31-coatings-14-01318" class="html-bibr">31</a>]). (Oxygen has three types of isotope, i.e., <sup>17</sup>O, <sup>18</sup>O, <sup>16</sup>O; Silicon also has three types of isotope, <sup>28</sup>Si, <sup>29</sup>Si, <sup>30</sup>Si. And aluminium has a total of 24 types of isotope. Then, here <sup>18</sup>O, <sup>30</sup>Si and <sup>26</sup>Al mean that the elements of isotope are selected in this experiment).</p>
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<p>Comparison of the test results for the surface roughness and shear forces of the specimens after welding with different pretreatment methods.</p>
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20 pages, 15874 KiB  
Article
Study on the Performance of High-Performance Mortar (HPM) Prepared Using Sodium-Silicate-Modified Graphite Tailing Sand
by Ruixin Jiang, Zhengjun Wang, Yingxin Du and Yajing Wen
Buildings 2024, 14(10), 3269; https://doi.org/10.3390/buildings14103269 (registering DOI) - 15 Oct 2024
Viewed by 299
Abstract
In order to rationalize the consumption of graphite tailing sand and reduce its pollution of the environment—with sodium silicate being a commonly used activator for improving the strength of concrete composites—in this study, the joint effects of sodium silicate (SS) and graphite tail [...] Read more.
In order to rationalize the consumption of graphite tailing sand and reduce its pollution of the environment—with sodium silicate being a commonly used activator for improving the strength of concrete composites—in this study, the joint effects of sodium silicate (SS) and graphite tail sand (GT) on the strength and frost resistance of graphite tail sand high-performance mortar (GT-HPM) were investigated. Experiments were conducted to evaluate the bulk density, water absorption, compressive strength, speed of sound, and working performance status of GT-HPM before and after freezing and thawing at different SS dosages and different GT substitution rates. The microstructural properties of GT-HPM were also analyzed by X-ray diffraction (XRD), Fourier-transform infrared spectroscopy (FT-IR), and scanning electron microscopy (SEM/EDS). The results showed that 4% SS doping improved the performance of GT-HPM more obviously. Moreover, with an increase in the GT substitution rate, the mechanical properties and frost resistance of GT-HPM increased firstly and then decreased, and the best performance of GT-HPM was obtained when the GT substitution rate was 20%. At 6% SS doping, the performance of GT-HPM gradually decreased with the increase in the graphite tailing sand substitution rate. FT-IR testing showed that there was no significant change with the type of hydration products used, and the Si–O–T absorption peak and average bond length of GT-4 were the largest. SS and GT promoted the generation of hydration products. Microstructural analysis showed that 4% SS promoted the hydration reaction; in addition, an appropriate amount of GT improved the pore structure of HPM, increased the strength and frost resistance, and provided fundamental insights for the subsequent comprehensive utilization of graphite tailing sand. Full article
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<p>Particle size distribution of materials in GT-HPM.</p>
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<p>Flowchart of the test.</p>
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<p>Velocity of sound test principle.</p>
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<p>Freeze–thaw test chamber temperature–time curve.</p>
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<p>Water absorption and wet-packing density.</p>
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<p>GT-HPM compressive damage section.</p>
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<p>Variation in GT-HPM compressive strength and sound velocity values at different ages.</p>
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<p>Graphite tailing substitution rate versus compressive strength and sound velocity fit.</p>
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<p>Changes in GT-HPM performance before and after freeze–thaw cycles. (<b>a</b>) The mass loss of GT-HPM after freeze–thaw test; (<b>b</b>) the RDME of GT-HPM after freeze–thaw test; (<b>c</b>) the change in the strength of GT-HPM before and after freeze–thaw; (<b>d</b>) the strength change of GT-HPM after freeze–thaw test.</p>
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<p>GT-HPM reaction mechanism diagram. (<b>a</b>) Freeze–thaw cycle damage mechanism diagram; (<b>b</b>) alkali exciter reaction mechanism diagram.</p>
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<p>FTIR spectra of GT-HPM after freezing and thawing.</p>
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<p>XRD pattern of GT-HPM samples after freeze–thaw cycles.</p>
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<p>SEM images of GT-HPM samples after freeze–thaw cycles.</p>
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<p>EDS results of GT-HPM samples after freeze–thaw cycles.</p>
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20 pages, 5077 KiB  
Article
The Effect of Inorganic Filler Content on the Properties of BPA-Free Bulk-Fill Dental Resin Composites
by Huilin Deng, Fang Liu and Jingwei He
Materials 2024, 17(20), 5040; https://doi.org/10.3390/ma17205040 (registering DOI) - 15 Oct 2024
Viewed by 286
Abstract
This study aimed to enhance the performance of dental resin composites (DRCs) by increasing the content of inorganic fillers while addressing potential health risks associated with Bisphenol A (BPA). To achieve this, the BPA-based resin monomer Bis-GMA was replaced with BPA-free Bis-EFMA. The [...] Read more.
This study aimed to enhance the performance of dental resin composites (DRCs) by increasing the content of inorganic fillers while addressing potential health risks associated with Bisphenol A (BPA). To achieve this, the BPA-based resin monomer Bis-GMA was replaced with BPA-free Bis-EFMA. The study then explored the impact of varying inorganic filler contents on the physiochemical properties of Bis-EFMA-based bulk-fill dental resin composites (BF-DRCs). Four distinct Bis-EFMA-based BF-DRCs were formulated, each with different inorganic filler contents ranging from 70 wt% to 76 wt%. The study tested the depth of cure (DOC), double-bond conversion (DC), water sorption (WS), solubility (SL), and cytotoxicity of the system. It notably investigated the effects of increasing filler content on mechanical properties through flexural strength (FS), flexural modulus (FM), Vickers microhardness (VHN), and wear resistance, as well as the impact on polymerization shrinkage, including volumetric shrinkage (VS) and shrinkage stress (SS). To assess the commercial application potential of Bis-EFMA-based BF-DRC, the research used the commercially available BF-DRC Filtek Bulk-Fill Posterior (FBF) as a control. The results indicated that a higher filler content did not affect the DOC of Bis-EFMA-based BF-DRCs. Inorganic fillers at higher concentrations significantly enhanced overall mechanical properties while significantly reducing volumetric shrinkage (VS; p < 0.05). When the concentration of inorganic fillers in the resin system reached 76 wt%, most of the performance of the Bis-EFMA-based BF-DRC surpassed that of the commercial control FBF, except for FS, FM, and SS. These findings highlight the potential of Bis-EFMA-based BF-DRC as a long-term restorative material for dental applications. Full article
(This article belongs to the Special Issue Recent Research in Restorative Dental Materials)
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<p>The structures of the resin monomer [<a href="#B13-materials-17-05040" class="html-bibr">13</a>,<a href="#B18-materials-17-05040" class="html-bibr">18</a>]. In the structural formula of Bis-GMA, the red-highlighted section represents the core structure of Bisphenol A. The chemical formulas were drawn using ChemDraw 18.0.</p>
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<p>Schematic diagram of the preparation and testing of DRCs.</p>
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<p>ATR-FTIR spectra of DRCs before and after irradiation at 1636 and 1720 cm<sup>−1</sup>.</p>
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<p>SEM images depict the micro-filler particles utilized as additional fillers for BF-DRCs: (<b>a</b>) SCHOTT<sup>®</sup> UltraFine silanated inorganic glass fillers, and the section morphology of DRCs: (<b>b</b>) DRCs of FBF, (<b>c</b>) DRCs of UBT/Filler (30/70), (<b>d</b>) DRCs of UBT/Filler (28/72), (<b>e</b>) DRCs of UBT/Filler (26/74), and (<b>f</b>) DRCs of UBT/Filler (24/76).</p>
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<p>Shrinkage stress versus time curves of DRCs.</p>
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<p>Flexural strength and modulus before and after water immersion of DRCs. <sup>a,b,c</sup> Different lowercase superscript letters indicate differences in FS or FM before water immersion with the same composition and proportion (<span class="html-italic">p</span> &lt; 0.05). <sup>A,B,C</sup> Different capital superscript letters indicate differences in FS or FM after water immersion with the same composition and proportion (<span class="html-italic">p</span> &lt; 0.05). * Asterisk indicates a significant difference between before and after water immersion (<span class="html-italic">p</span> &lt; 0.05). Bar graphs were created using GraphPad Prism 9.5.</p>
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<p>(<b>a</b>) Volume wear of dental resin composites (<span class="html-italic">p</span> = 0.000). (<b>b</b>–<b>f</b>) Surface morphology (triangle annotation) and 3D profile scanning images (20×) of samples after wear testing. The image within the dashed box shows an enlarged view of the wear marks at the triangular identifier. (<b>b</b>) DRCs of FBF, (<b>c</b>) DRCs of UBT/Filler (30/70), (<b>d</b>) DRCs of UBT/Filler (28/72), (<b>e</b>) DRCs of UBT/Filler (26/74), and (<b>f</b>) DRCs of UBT/Filler (24/76). * Asterisk indicates a significant difference between different groups (<span class="html-italic">p</span> &lt; 0.05). Bar graphs were created using GraphPad Prism 9.5.</p>
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<p>Cell viability of DRCs (100%, 50%, and 25% extract). The dashed line indicates that cell activity has reached 70%. Bar graphs were created using GraphPad Prism 9.5.</p>
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15 pages, 1991 KiB  
Article
Mechanical, Adhesive and Surface Properties of a Zirconia-Reinforced Lithium Silicate CAD/CAM Ceramic Exposed to Different Etching Protocols
by Fabián Murillo-Gómez, José Roberto Hernández-Víquez, José Roberto Sauma-Montes de Oca, Cristina Vargas-Vargas, Natalia González-Vargas, José Roberto Vega-Baudrit and Daniel Chavarría-Bolaños
Materials 2024, 17(20), 5039; https://doi.org/10.3390/ma17205039 (registering DOI) - 15 Oct 2024
Viewed by 330
Abstract
The aim of this investigation was to evaluate the effect of etching protocols on bond strength, surface roughness, and mechanical properties of a zirconia-reinforced lithium silicate (ZLS) CAD/CAM-ceramic. In total, 100 bars (ISO 6872), 75 plaques, and 25 cubes were cut from ZLS [...] Read more.
The aim of this investigation was to evaluate the effect of etching protocols on bond strength, surface roughness, and mechanical properties of a zirconia-reinforced lithium silicate (ZLS) CAD/CAM-ceramic. In total, 100 bars (ISO 6872), 75 plaques, and 25 cubes were cut from ZLS blocks(Vita Suprinity®). The surfaces were standardized, crystallized and divided into five groups: 1. control (no/treatment-C), 2. 5%-Hydrofluoric-acid (HF)/20 s (HF5%20s), 3.HF5%60s, 4.HF10%20s, and 5.HF10%60s. Flexural strength (FS) (three-point bending test, 1 mm/min), roughness (Pa), and micro-shear bond-strength (µSBS) tests were performed. The data were statistically analyzed with one-way ANOVA, Tukey’s test (p ˂ 0.05) and Weibull (FS data). C showed higher Pa (1.176 ± 0.370 µm) than HF10%60s (0.627 ± 0.236 µm) and all other groups. Groups C and 20 s showed the most irregular surface patterns. The FS results were not influenced by etching protocols, while the Weibull modulus was, with the 5%HF groups being the most reliable (m: 5.63/6.70), while C and HF10%60s (m: 2.78/2.73) were the least reliable. All fractures originated from surface defects on the treated side of specimens. The 5%HF groups showed higher µSBS (20 s: 21.35 ± 4.70 MPa; 60 s: 23.50 ± 4.27 MPa) than the 10%HF groups (20 s: 14.51 ± 2.47 MPa; 60 s: 16.54 ± 3.12 MPa) and C (6.46 ± 2.71 MPa). The most prevalent failure pattern was “mixed” for etched groups, and “adhesive” for C. Etching protocols affect the evaluated properties by roughening materials’ surface and, in some cases, regularizing surface defects. The best overall outcomes were achieved when applying 5%HF. Full article
(This article belongs to the Special Issue Advanced Dental Materials: From Design to Application, Second Volume)
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<p>Schematic representation of all specimens prepared for this study.</p>
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<p>Graphical representation of <a href="#materials-17-05039-t001" class="html-table">Table 1</a> containing roughness mean values and standard deviations (expressed in MPa) from each group. Different letters represent significant statistical differences.</p>
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<p>Surface micromorphology of zirconia-reinforced lithium silicate ceramic (ZLS) after being treated with the different etching protocols. SEM (Scanning Electron Microscope) images showing the typical surface morphology produced by the experimental groups: (<b>a</b>) control group (no etching); (<b>b</b>) HF5%20s group; (<b>c</b>) HF5%60s group; (<b>d</b>) HF10%20s group; and (<b>e</b>) HF10%60s group.</p>
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<p>Weibull modulus plots for each group. The left plot shows the graphical Weibull modulus corresponding to all experimental groups (control: blue; HF5%20s: red; HF5%60s: green; HF10%20s: purple; HF10%60s: gray). Right side plots show a separate graphical representation for each groups’ Weibull modulus. All Weibull plots represent a curve relating the probability of failure % (<span class="html-italic">Y</span>-axis) and flexural strength in MPa (<span class="html-italic">X</span>-axis). The Weibull characteristic strength is pointed with the discontinuous red horizontal line, across a 63.2% probability of failure.</p>
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<p>Representative SEM images (60×) from each group regarding fractographic analysis: (<b>a</b>) control group (no etching); (<b>b</b>) HF5%20s group; (<b>c</b>) HF5%60s group; (<b>d</b>) HF10%20s group; and (<b>e</b>) HF10%60s group. The discontinuous semicircle points to the origin of fracture for each group, which was located at surface defects on the treated side (tensile side), showing that the main direction of fracture propagation (arrows) to the compression side compression curl area is also notorious.</p>
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<p>Graphical representation of <a href="#materials-17-05039-t003" class="html-table">Table 3</a> containing microshear bond strength mean values and standard deviations (expressed in MPa) from each group. Different letters represent significant statistical differences.</p>
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<p>Representative SEM photo-micrographs of the most prevalent failure patterns obtained from microshear bond strength test: (<b>a</b>) adhesive failure, (<b>b</b>) mixed failure.</p>
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12 pages, 2123 KiB  
Article
Impact of Bioactivity on Push-Out Bond Strength of AH Plus Bioceramic versus BC Bioceramic Root Canal Sealers
by Sawsan T. Abu Zeid and Arwa S. Alnoury
Appl. Sci. 2024, 14(20), 9366; https://doi.org/10.3390/app14209366 - 14 Oct 2024
Viewed by 304
Abstract
This study compared the push-out bond strength and adaptation of the recently developed AH Plus bioceramic (AHP-Bio) root canal sealer with Bioceramic Endosequence (BC) and AH Plus (AHP) sealers when exposed to simulated body fluid for inducing bioactivity. Cross-section discs of 1 mm [...] Read more.
This study compared the push-out bond strength and adaptation of the recently developed AH Plus bioceramic (AHP-Bio) root canal sealer with Bioceramic Endosequence (BC) and AH Plus (AHP) sealers when exposed to simulated body fluid for inducing bioactivity. Cross-section discs of 1 mm thick slices from obturated root canals were prepared and either kept dry or immersed in serum for 30 days. All discs were evaluated using scanning electron microscopy (SEM) and then subjected to a push-out test. The failure modes were also determined. The data were statistically analyzed using an ANOVA test at p < 0.05. In both environments, the BC sealer recorded the greatest bond strength, while the AHP-Bio sealer recorded the lowest mean values. However, bond strength was significantly improved after immersion in serum (p < 0.001). The chi-square test and Fisher’s exact test revealed a significant difference in failure mode among the tested groups at p < 0.001. The predominant failure mode was cohesive failure in both bioceramic sealers, with the greatest value for AHP-Bio (70%), and adhesive failure for AHP/gutta-percha (60%, 80%) in both environments. SEM revealed good dentin adaptation of the three sealers, with marked decreases in gaps at the bioceramic/dentin interface after immersion in serum. In conclusion, although BC exhibited greater push-out bond strength than AHP-Bio, the latter achieved good displacement resistance that increased when the sealer was exposed to simulated body fluid (serum). Full article
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<p>Stereomicroscopic photographs (at 50× magnification) showing the different failure mode categories of the root canal cross-sections and detached gutta-percha after the push-out test: (<b>A</b>) adhesive failure at the sealer/dentin interface, (<b>B</b>) adhesive failure at the sealer/gutta-percha interface, (<b>C</b>) cohesive failure of the sealer and (<b>D</b>) mixed failure.</p>
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<p>The bar chart showing the means ± standard deviations of push-out bond strength (MPa) for all experimental groups, both in the dry condition and after immersion in serum. The asterisk (*) represents the significant greatest mean value (<span class="html-italic">p</span> &lt; 0.001), while ≠ indicates no significant difference between sealers of the same symbol.</p>
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<p>Bar chart of frequency (%) of failure mode categories in all tested groups after push-out test.</p>
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<p>Scanning electron microscopy photographs (at 2000× magnification) for root canal cross-sections obturated with BC, AHP-Bio and AHP root canal sealers in the dry condition (<b>A</b>–<b>C</b>) and after immersion in serum (<b>D</b>–<b>F</b>), showing the status of the sealer layer (s), sealer/dentin interface (S/D, indicated by white arrows) and sealer/gutta-percha interface (S/GP, indicated by orange arrows). The thin arrows indicate close contact areas, and the wide arrows indicate gaps/voids. The letter “d” mentioned to dentin, letter “s” mentioned to sealer, and letter “gp” mentioned to gutta-percha.</p>
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35 pages, 20755 KiB  
Review
Cyclization Strategies in Carbonyl–Olefin Metathesis: An Up-to-Date Review
by Xiaoke Zhang
Molecules 2024, 29(20), 4861; https://doi.org/10.3390/molecules29204861 - 14 Oct 2024
Viewed by 415
Abstract
The metathesis reaction between carbonyl compounds and olefins has emerged as a potent strategy for facilitating swift functional group interconversion and the construction of intricate organic structures through the creation of novel carbon–carbon double bonds. To date, significant progress has been made in [...] Read more.
The metathesis reaction between carbonyl compounds and olefins has emerged as a potent strategy for facilitating swift functional group interconversion and the construction of intricate organic structures through the creation of novel carbon–carbon double bonds. To date, significant progress has been made in carbonyl–olefin metathesis reactions, where oxetane, pyrazolidine, 1,3-diol, and metal alkylidene have been proved to be key intermediates. Recently, several reviews have been disclosed, focusing on distinct catalytic approaches for achieving carbonyl–olefin metathesis. However, the summarization of cyclization strategies for constructing aromatic heterocyclic frameworks through carbonyl–olefin metathesis reactions has rarely been reported. Consequently, we present an up-to-date review of the cyclization strategies in carbonyl–olefin metathesis, categorizing them into three main groups: the formation of monocyclic compounds, bicyclic compounds, and polycyclic compounds. This review delves into the underlying mechanism, scope, and applications, offering a comprehensive perspective on the current strength and the limitation of this field. Full article
(This article belongs to the Special Issue Cyclization Reactions in Organic Synthesis: Recent Developments)
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<p>Strategies for carbonyl–olefin metathesis.</p>
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<p>The classification of carbonyl–olefin metathesis.</p>
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<p>The synthesis of cycloalkenes via carbonyl–olefin metathesis reaction.</p>
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<p>Olefinic ester ring-closing metathesis: using a reduced titanium akylidene.</p>
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<p>Diversity-oriented synthesis of carbocyclic.</p>
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<p>Catalytic intramolecular carbonyl–olefin reaction.</p>
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<p>Iron(III)-catalyzed carbonyl–olefin metathesis.</p>
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<p>FeCl<sub>3</sub>-catalyzed ring-closing carbonyl–olefin metathesis.</p>
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<p>The synthesis of 3-aryl-2,5-dihydropyrroles.</p>
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<p>Catalytic carbonyl–olefin metathesis of aliphatic ketones.</p>
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<p>Catalytic, transannular carbonyl–olefin metathesis reactions.</p>
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<p>Tetrahydropyridines via FeCl<sub>3</sub>-catalyzed carbonyl–olefin metathesis.</p>
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<p>Gallium-catalyzed tandem carbonyl–olefin metathesis/transfer hydrogenation.</p>
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<p>Super-electrophilic aluminum (III)-ion pair-catalyzed carbonyl–olefin metathesis.</p>
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<p>AuCl<sub>3</sub>-catalyzed ring-closing carbonyl–olefin metathesis.</p>
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<p>The synthesis of cyclopentene mediated by bis(perchlorocatecholato) germane.</p>
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<p>InCl<sub>3</sub>-catalyzed intramolecular carbonyl–olefin metathesis.</p>
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<p>Intramolecular cycloreversion mediated by BF<sub>3</sub>.Et<sub>2</sub>O.</p>
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<p>Brønsted acid-catalyzed carbonyl–olefin metathesis.</p>
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<p>The synthesis of 2,5-dihydropyrroles via carbonyl–olefin metathesis reactions.</p>
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<p>Carbonyl–olefin metathesis catalyzed by HFIP and <span class="html-italic">p</span>TSA.</p>
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<p>Brønsted acid-catalyzed intramolecular carbonyl–olefin metathesis reactions.</p>
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<p>Tropylium-promoted carbonyl–olefin metathesis reactions.</p>
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<p>Carbonyl–olefin metathesis catalyzed by molecular iodine.</p>
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<p>Iodonium-catalyzed carbonyl–olefin metathesis reactions.</p>
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<p>Al-catalyzed carbonyl–olefin metathesis reactions.</p>
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<p>Au-catalyzed carbonyl–olefin metathesis reactions.</p>
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<p>Titanocene alkylidene complex-catalyzed carbonyl–olefin metathesis reactions.</p>
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<p>The construction of the JKL, OPQ, and UVW ring systems of Maitotoxin.</p>
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<p>Approach to 1,4-dihydroquinoline via carbonyl–olefin metathesis reactions.</p>
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<p>Approach to fused ether ring systems via carbonyl–olefin metathesis reactions.</p>
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<p>Olefinic ester cyclizations using Takai–Utimoto-reduced titanium alkylidenes.</p>
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<p>Ti alkylidenes mediated carbonyl–olefin metathesis reactions.</p>
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<p>Olefinic lactone cyclization to macrocycles.</p>
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<p>Olefinic amide and olefinic lactam cyclizations.</p>
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<p>Photoprotolytic-mediated carbonyl–olefin metathesis reactions.</p>
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<p>The synthesis of bicyclic compounds via photoinduced intramolecular cyclization.</p>
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<p>The synthesis of bicyclic compounds mediated by TfOH.</p>
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<p>BF<sub>3</sub>.Et<sub>2</sub>O mediated intramolecular carbonyl–olefin metathesis.</p>
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<p>Carbocation-catalyzed ring-closing aldehyde–olefin metathesis.</p>
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<p>Hydrazine-catalyzed ring-closing carbonyl–olefin metathesis.</p>
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<p>Synthesis of 1,2-dihydroquinolines via ring-closing carbonyl–olefin metathesis.</p>
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<p>Ring-closing carbonyl–olefin metathesis catalyzed by titanium reagents.</p>
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<p>Olefin metathesis in cyclic ether formation.</p>
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<p>The application of olefin metathesis.</p>
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<p>Two-directional olefinic ester ring-closing metathesis.</p>
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<p>The synthesis of tricycle compound.</p>
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<p>Polycyclic aromatic hydrocarbons via iron(III)-catalyzed carbonyl–olefin metathesis.</p>
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<p>Synthesis of angucycline derivatives using carbonyl–olefin metathesis.</p>
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<p>Brønsted acid-catalyzed carbonyl–olefin metathesis. A represents the yield obtained under condition 1); B represents the yield obtained under condition 2); C represents the yield obtained under condition 3).</p>
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<p>Hydrazine-catalyzed ring-closing carbonyl–olefin metathesis.</p>
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