[go: up one dir, main page]
More Web Proxy on the site http://driver.im/
Previous Issue
Volume 8, November
You seem to have javascript disabled. Please note that many of the page functionalities won't work as expected without javascript enabled.
 
 

J. Compos. Sci., Volume 8, Issue 12 (December 2024) – 45 articles

  • Issues are regarded as officially published after their release is announced to the table of contents alert mailing list.
  • You may sign up for e-mail alerts to receive table of contents of newly released issues.
  • PDF is the official format for papers published in both, html and pdf forms. To view the papers in pdf format, click on the "PDF Full-text" link, and use the free Adobe Reader to open them.
Order results
Result details
Section
Select all
Export citation of selected articles as:
13 pages, 2267 KiB  
Article
Effect of Carbonate Mineral Fillers on the Dielectric Properties and Fire Resistance of Polar and Non-Polar Halogen-Free Flame-Retardant Polymer Compounds
by Konstantinos G. Gatos, Nikolaos Apostolopoulos, Anastasios C. Patsidis and Georgios C. Psarras
J. Compos. Sci. 2024, 8(12), 529; https://doi.org/10.3390/jcs8120529 (registering DOI) - 14 Dec 2024
Abstract
In the present work, carbonate minerals are added in non-polar and polar polymer matrices to develop halogen-free flame-retardant composites. The examined fillers of calcium carbonate and magnesium carbonate delivered improved rheological performance in both non-polar (PE) and polar (EVA/PE) polymer compounds compared to [...] Read more.
In the present work, carbonate minerals are added in non-polar and polar polymer matrices to develop halogen-free flame-retardant composites. The examined fillers of calcium carbonate and magnesium carbonate delivered improved rheological performance in both non-polar (PE) and polar (EVA/PE) polymer compounds compared to the natural magnesium hydroxide and huntite/hydromagnesite mineral fillers. The presence of EVA in the matrix enhanced the mechanical behavior of all compounds in tensile testing. The thermal stability of the composites was particularly improved for the polar systems with the incorporation of the carbonate minerals, as this was evidenced under thermogravimetric analysis. The dielectric behavior of the fabricated systems was examined via broadband dielectric spectroscopy. The HFFR compounds attained higher values of the real part of dielectric permittivity from the unreinforced systems in the whole frequency and temperature range of the conducted tests. This behavior is ascribed to the higher permittivity values of the fillers with respect to the polymer matrices and the occurrence of interfacial polarization. All minerals improved the flame retardancy of the compounds in terms of LOI values, while the addition of EVA yielded further improvements, especially for the magnesium carbonate and the magnesium hydroxide minerals. Full article
(This article belongs to the Special Issue Feature Papers in Journal of Composites Science in 2024)
Show Figures

Figure 1

Figure 1
<p>Scanning electron microscopy images of the minerals: (<b>a</b>) magnesium carbonate, (<b>b</b>) calcium carbonate, (<b>c</b>) magnesium hydroxide, and (<b>d</b>) huntite/hydromagnesite.</p>
Full article ">Figure 2
<p>(<b>a</b>) Thermogravimetric analysis of the PE recipe matrix in comparison to the filled compounds. (<b>b</b>) Derivative of the thermogravimetric curve of the PE recipe matrix in comparison to the filled compounds.</p>
Full article ">Figure 3
<p>(<b>a</b>) Thermogravimetric analysis of the EVA/PE recipe matrix in comparison to the filled compounds. (<b>b</b>) Derivative of the thermogravimetric curve of the EVA/PE recipe matrix in comparison to the filled compounds.</p>
Full article ">Figure 4
<p>Variation of the real part of dielectric permittivity with frequency, at 30 °C, for the (<b>a</b>) PE recipe and (<b>b</b>) EVA/PE recipe-based systems.</p>
Full article ">Figure 5
<p>Variation of the real part of dielectric permittivity with temperature, at 100 Hz, for the (<b>a</b>) PE recipe and (<b>b</b>) EVA/PE recipe-based systems.</p>
Full article ">
31 pages, 10953 KiB  
Article
Immobilization of Pb2+, CrO42−, Hg2+, and Cd2+ in Coal Fly Ash/PP-g-MHBP-Based Geopolymers
by Paola M. Fonseca Alfonso, Mercedes Díaz Lagos and Edwin A. Murillo
J. Compos. Sci. 2024, 8(12), 528; https://doi.org/10.3390/jcs8120528 (registering DOI) - 14 Dec 2024
Abstract
Contamination by heavy metals (HMs) such as Pb, Cd, Cr, and Hg poses significant risks to the environment and human health owing to their toxicity and persistence. Geopolymers (GPs) have emerged as promising materials for immobilizing HMs and reducing their mobility through physical [...] Read more.
Contamination by heavy metals (HMs) such as Pb, Cd, Cr, and Hg poses significant risks to the environment and human health owing to their toxicity and persistence. Geopolymers (GPs) have emerged as promising materials for immobilizing HMs and reducing their mobility through physical encapsulation and chemical stabilization. This study explored the novel use of isotactic polypropylene functionalized in the molten state with maleinized hyperbranched polyol polyester (PP-g-MHBP) as an additive in coal fly ash (CFA)-based GPs to enhance HM immobilization. Various characterization techniques were employed, including compressive strength tests, XRD, ATR-FTIR, SEM-EDX, XPS analyses, and TCLP leaching tests, to assess immobilization effectiveness. These results indicate that although the addition of PP-g-MHBP does not actively contribute to the chemical interactions with HM ions, it acts as an inert filler within the GP matrix. CFA/PP-g-MHBP-based GPs demonstrated significant potential for Cd2+ immobilization up to 3 wt% under acidic conditions, although the retention of Pb2+, CrO42−, and Hg2+ varied according to the specific chemistry of each metal, weight percentage of the added metal, matrix structure, and regulatory standards. Notably, high immobilization percentages were achieved for CrO42− and Hg2+, although the leaching concentrations exceeded US EPA limits. These findings highlight the potential of CFA/PP-g-MHBP-based GPs for environmental applications, emphasizing the importance of optimizing formulations to enhance HM immobilization under varying conditions. Full article
Show Figures

Figure 1

Figure 1
<p>Schema of the preparation process for the CFA/PP-<span class="html-italic">g</span>-MHBP-based geopolymers.</p>
Full article ">Figure 2
<p>Volume and cumulative volume particle size distributions of CFA and PP-<span class="html-italic">g</span>-MHBP samples.</p>
Full article ">Figure 3
<p>XRD pattern of the CFA sample with internal standard.</p>
Full article ">Figure 4
<p>XRD patterns of (<b>a</b>) the CFA sample and GP1 specimen after 28 days of curing; (<b>b</b>) the GP specimens with 1.0 wt% of Pb<sup>2+</sup>, CrO<sub>4</sub><sup>2−</sup>, Hg<sup>2+</sup>, and Cd<sup>2+</sup> after 28 days of curing; (<b>c</b>) the GP specimens with 3.0 wt% of Pb<sup>2+</sup>, CrO<sub>4</sub><sup>2−</sup>, Hg<sup>2+</sup>, and Cd<sup>2+</sup> after 28 days of curing. The CFA pattern did not include internal standards.</p>
Full article ">Figure 5
<p>ATR-FTIR spectra of the CFA sample, the control GP specimen (GP1), and GP specimens containing (<b>a</b>) 1.0 wt% and (<b>b</b>) 3.0 wt% of Pb<sup>2+</sup>, CrO<sub>4</sub><sup>2−</sup>, Cd<sup>2+</sup>, and Hg<sup>2+</sup> after 28 days of curing.</p>
Full article ">Figure 6
<p>Effect of HM ion type and content on compressive strength and main transmittance minimum position in the GP specimens.</p>
Full article ">Figure 7
<p>SEM images of GPs after 28 days of curing, with 1.0 wt% and 3.0 wt% of (<b>a</b>,<b>b</b>) Pb<sup>2+</sup>, (<b>c</b>,<b>d</b>) CrO<sub>4</sub><sup>2−</sup>, (<b>e</b>,<b>f</b>) Hg<sup>2+</sup>, and (<b>g</b>,<b>h</b>) Cd<sup>2+</sup>, respectively.</p>
Full article ">Figure 8
<p>XPS survey spectra of GP1 and GP specimens containing 1 wt% Pb<sup>2+</sup>, Hg<sup>2+</sup>, CrO<sub>4</sub><sup>2−</sup>, and Cd<sup>2+</sup> after 28 days of curing.</p>
Full article ">Figure 9
<p>High-resolution XPS spectra of Si 2s, Si 2p, Al 2s, Al 2p, Na 2s, and Pb 4f peaks for the GP1 and GP specimens containing 1 wt% Pb<sup>2+</sup>, Hg<sup>2+</sup>, CrO<sub>4</sub><sup>2−</sup>, and Cd<sup>2+</sup> after 28 days of curing.</p>
Full article ">Figure 10
<p>Effects of Pb<sup>2+</sup>, CrO<sub>4</sub><sup>2−</sup>, Hg<sup>2+</sup>, and Cd<sup>2+</sup> content on the concentration in the TCLP extract, percentage of immobilization, and compressive strength of GP specimens after 28 days of curing: (<b>a</b>) Pb<sup>2+</sup>, (<b>b</b>) CrO<sub>4</sub><sup>2−</sup>, (<b>c</b>) Hg<sup>2+</sup>, and (<b>d</b>) Cd<sup>2+</sup>.</p>
Full article ">Figure 10 Cont.
<p>Effects of Pb<sup>2+</sup>, CrO<sub>4</sub><sup>2−</sup>, Hg<sup>2+</sup>, and Cd<sup>2+</sup> content on the concentration in the TCLP extract, percentage of immobilization, and compressive strength of GP specimens after 28 days of curing: (<b>a</b>) Pb<sup>2+</sup>, (<b>b</b>) CrO<sub>4</sub><sup>2−</sup>, (<b>c</b>) Hg<sup>2+</sup>, and (<b>d</b>) Cd<sup>2+</sup>.</p>
Full article ">
11 pages, 1943 KiB  
Article
An Upcycling Strategy for Polyethylene Terephthalate Fibers: All-Polymer Composites with Enhanced Mechanical Properties
by Chiara Gnoffo, Rossella Arrigo and Alberto Frache
J. Compos. Sci. 2024, 8(12), 527; https://doi.org/10.3390/jcs8120527 (registering DOI) - 14 Dec 2024
Viewed by 63
Abstract
In this work, an effective route for achieving high-performance all-polymer materials through the proper manipulation of the material microstructure and starting from a waste material is proposed. In particular, recycled polyethylene terephthalate (rPET) fibers from discarded safety belts were used as reinforcing phase [...] Read more.
In this work, an effective route for achieving high-performance all-polymer materials through the proper manipulation of the material microstructure and starting from a waste material is proposed. In particular, recycled polyethylene terephthalate (rPET) fibers from discarded safety belts were used as reinforcing phase in melt-compounded high-density polyethylene (HDPE)-based systems. The formulated composites were subjected to hot- and cold-stretching for obtaining filaments at different draw ratios. The performed characterizations pointed out that the material morphology can be profitably modified through the application of the elongational flow, which was proven able to promote significant microstructural evolutions of the rPET dispersed domains, eventually leading to the obtainment of micro-fibrillated all-polymer composites. Furthermore, tensile tests demonstrated that hot-stretched and, especially, cold-stretched materials show significantly enhanced tensile modulus and strength as compared to the unfilled HDPE filaments, likely due to the formation of a highly oriented and anisotropic microstructure. Full article
(This article belongs to the Special Issue Mechanical Properties of Composite Materials and Joints)
Show Figures

Figure 1

Figure 1
<p>SEM micrographs for HDPE/rPET extrudates processed at 220 (<b>a</b>,<b>b</b>), 240 (<b>c</b>) and 260 (<b>d</b>) °C.</p>
Full article ">Figure 2
<p>Trend of complex viscosity (η*) and of the storage modulus (G′) as a function of the frequency (ω) for HDPE/rPET processed at 220 (<b>a</b>,<b>d</b>), 240 (<b>b</b>,<b>e</b>) and 260 (<b>c</b>,<b>f</b>) °C. The rheological functions of the neat matrix are also reported.</p>
Full article ">Figure 3
<p>SEM micrographs for HDPE95/rPET5_260 °C hot-stretched filaments at DR<sub>H</sub> 4 (<b>a</b>) and 14 (<b>b</b>).</p>
Full article ">Figure 4
<p>Tensile modulus (<b>a</b>), tensile strength (<b>b</b>) and elongation at break (<b>c</b>) for HDPE and HDPE/rPET filaments as a function of DR<sub>H</sub>.</p>
Full article ">Figure 5
<p>Tensile modulus (<b>a</b>), tensile strength (<b>b</b>) and elongation at break (<b>c</b>) for HDPE and HDPE/rPET filaments as a function of DR<sub>C</sub>.</p>
Full article ">
13 pages, 3213 KiB  
Article
Tailored Compositions of Ni-Ti-Sn Nanopowders Deposited on Polymer Fiber Optics Through Flash Evaporation
by Elango Natarajan, Anil Chouhan, Santheraleka Ramanathan, Kalaimani Markandan, Santhosh Mozhuguan Sekar, Chun Kit Ang, Nagarajan Deivanayagampillai and Gérald Franz
J. Compos. Sci. 2024, 8(12), 526; https://doi.org/10.3390/jcs8120526 - 13 Dec 2024
Viewed by 206
Abstract
Fiber coatings protect the glass surface of fiber from extrinsic environmental factors. The coating of shape memory alloy over fiber is useful in sensor fabrication where the state of deformation is affected by the phase transformation of the coated material. In addition, coated [...] Read more.
Fiber coatings protect the glass surface of fiber from extrinsic environmental factors. The coating of shape memory alloy over fiber is useful in sensor fabrication where the state of deformation is affected by the phase transformation of the coated material. In addition, coated plastic fibers can be used in elevated temperature environments. To this end, the present research aims to investigate the effect of the Ni-Ti-Sn composite coating over the fiber. Homogeneous particle distribution, agglomeration, porosity and the ability to obtain uniform coating thickness have been general concerns in fiber coatings. Hence, the present study comprehensively investigated the mechanical and thermal behavior as well as morphological properties of Ni-Ti-Sn nanopowders deposited on polymer fiber optics. Five sets of polyamide-coated samples with different Ni-Ti-Sn proportions were fabricated and characterized. Morphological studies confirmed that an even coating thickness enhanced the mechanical integrity and optical performance. The optimum composition demonstrated superior tensile strength of 29.5 MPa and a 25% increase in elongation compared to the uncoated sample. The Ni-Ti-Sn alloy composition investigated in the present study is promising for industrial applications where thermal stability and mechanical performance are warranted. Full article
(This article belongs to the Special Issue Polymer Composites and Fibers, 3rd Edition)
Show Figures

Figure 1

Figure 1
<p>(<b>a</b>) Schematic illustration of flash evaporation process of coating optical fiber with Ni-Ti-Sn nanopowders. (<b>b</b>) Digital image of optical fiber used in the study. HPM images of uncoated fiber at (<b>c</b>) 5× and (<b>d</b>) 20× magnification.</p>
Full article ">Figure 2
<p>HPM images of Ni-Tn-Sn coated fibers classified into five sets as stated above. For each set, (<b>a</b>–<b>c</b>) denote the optical microscopic image at 5×, 20×, and 50× magnification.</p>
Full article ">Figure 3
<p>FESEM images of Ni-Ti-Sn coated fibers. (<b>a</b>–<b>e</b>) FESEM image of Set 1–Set 5, respectively. Electron microscopic image of coated fiber as insets in each figure.</p>
Full article ">Figure 4
<p>FTIR spectra consisting of uncoated and coated fibers with varying compositions of Ni-Ti-Sn.</p>
Full article ">Figure 5
<p>(<b>a</b>) Trend of force exerted by optical fiber over a range of applied strains; (<b>b</b>) tensile strength and (<b>c</b>) elongation of the optical fiber coated with Ni-Ti-Sn nanopowders.</p>
Full article ">Figure 6
<p>(<b>a</b>) Thermal analysis of Ni-Ti-Sn coated fibers evaluated through (<b>a</b>) thermogravimetric analysis and (<b>b</b>) differential thermal analysis.</p>
Full article ">Figure 7
<p>FESEM images of fractured fibers coated with varying compositions of Ni-Ti-Sn. (<b>a</b>–<b>e</b>) denotes Set 1–Set 5; where part (<b>i</b>) and (<b>ii</b>) reveal the electron microscopic view of the cross-sectional fiber and surface region, respectively.</p>
Full article ">
12 pages, 5986 KiB  
Article
Finite Element Analysis of Cutting Temperature in Precision Cutting of Composite Energetic Material
by Caiwei Xiao, Shijin Lu, Wenxin Zhang, Junjie Zhang and Junwei Liu
J. Compos. Sci. 2024, 8(12), 525; https://doi.org/10.3390/jcs8120525 - 13 Dec 2024
Viewed by 237
Abstract
While ensuring thermal safety is critically required in the operation of the composite energetic material, the cutting temperature is a crucial parameter that must be investigated and controlled in its cutting process to avoid thermal explosion. In this paper, we elucidate the mechanisms [...] Read more.
While ensuring thermal safety is critically required in the operation of the composite energetic material, the cutting temperature is a crucial parameter that must be investigated and controlled in its cutting process to avoid thermal explosion. In this paper, we elucidate the mechanisms of heat generation and conduction during the cutting process of a composite energetic material by establishing a microstructure-based finite element (FE) simulation model considering thermal effects. Specifically, we simulated the cutting process of the composite energetic material by FE simulations, with a focus on the variations in the cutting force, the initiation and conduction of the cutting temperature, and the correlation of the damage behavior of the composite energetic material. Subsequently, we conducted a parametric investigation of the effect of cutting speed on the damage behavior and cutting response of the composite energetic material. This paper provides valuable insights for the exploration of the cutting processes of composite energetic materials. Full article
(This article belongs to the Section Composites Modelling and Characterization)
Show Figures

Figure 1

Figure 1
<p>FE model of cutting of composite energetic materials containing Al.</p>
Full article ">Figure 2
<p>Variation of machining force with cutting length in cutting process of composite energetic material.</p>
Full article ">Figure 3
<p>Cutting configuration of composite energetic material with a cutting length of (<b>a</b>) 2.75 μm, (<b>b</b>) 14.85 μm, (<b>c</b>) 23.10 μm, (<b>d</b>) 51.15 μm, (<b>e</b>) 73.15 μm, (<b>f</b>) 111.65 μm, (<b>g</b>) 156.75 μm, (<b>h</b>) 193.05 μm and (<b>i</b>) 314.60 μm.</p>
Full article ">Figure 4
<p>(<b>a</b>) Typical chip profile [<a href="#B4-jcs-08-00525" class="html-bibr">4</a>] and (<b>b</b>) machined surface morphology [<a href="#B28-jcs-08-00525" class="html-bibr">28</a>] in energetic material cutting experiments.</p>
Full article ">Figure 5
<p>Variation of maximum cutting temperature with cutting length in cutting of composite energetic material.</p>
Full article ">Figure 6
<p>Distribution of the highest temperature point in the workpiece when the cutting length is (<b>a</b>) 2.75 μm, (<b>b</b>) 14.85 μm, (<b>c</b>) 23.10 μm, (<b>d</b>) 51.15 μm, (<b>e</b>) 73.15 μm, (<b>f</b>) 111.65 μm, (<b>g</b>) 156.75 μm, (<b>h</b>) 193.05 μm and (<b>i</b>) 314.60 μm.</p>
Full article ">Figure 7
<p>Variation of the maximum temperature point at different cutting lengths with cutting length.</p>
Full article ">Figure 8
<p>Variation of cutting force with cutting length in cutting of composite energetic material under different cutting speeds.</p>
Full article ">Figure 9
<p>Cutting configuration of composite energetic material at a cutting length of 340 μm when the cutting speed is (<b>a</b>) 40 m/min, (<b>b</b>) 60 m/min, (<b>c</b>) 80 m/min and (<b>d</b>) 100 m/min.</p>
Full article ">Figure 10
<p>Variation of maximum cutting temperature of (<b>a</b>) HMX, (<b>b</b>) HTPB and (<b>c</b>) Al with cutting length in cutting of composite energetic material under different cutting speeds.</p>
Full article ">
20 pages, 6155 KiB  
Article
A Comprehensive Framework for the Design and Optimisation of Limestone-Calcined Clay Cement: Integrating Mechanical, Environmental, and Financial Performance
by Guangtong Huang, Yue Liu, Tom Benn, Li Luo, Tianyu Xie and Yan Zhuge
J. Compos. Sci. 2024, 8(12), 524; https://doi.org/10.3390/jcs8120524 (registering DOI) - 12 Dec 2024
Viewed by 349
Abstract
Limestone-calcined clay (LC3) cement has emerged as a promising low-carbon alternative to ordinary Portland cement (OPC), offering significant potential to reduce carbon emissions while maintaining comparable mechanical performance. However, the absence of a prediction model for the formulation of the LC3 system presents [...] Read more.
Limestone-calcined clay (LC3) cement has emerged as a promising low-carbon alternative to ordinary Portland cement (OPC), offering significant potential to reduce carbon emissions while maintaining comparable mechanical performance. However, the absence of a prediction model for the formulation of the LC3 system presents challenges for optimisation within the evolving concrete industry. This study introduces a multi-objective optimisation (MOO) framework to design the optimal LC3 system, aiming to maximise compressive strength while minimising environmental and economic costs, simultaneously. The MOO framework integrates a regularised multivariate polynomial regression (MPR) model, achieving an R2 of 0.927 and MSE of 3.445 for mechanical performance prediction. Additionally, life cycle assessment quantifies the environmental impact, and collected market prices contribute to financial considerations of the LC3 system. Utilising a dataset of 366 LC3 mortar mixtures, the optimisation challenges the conventional 2:1 calcined clay-to-limestone ratio (CC:LS). For high strength (≥65 MPa), target a CC:LS ratio of 1:1 to 1.6:1; for lower strength (<65 MPa), increase calcined clay content, resulting in a CC:LS ratio of 1.6:1 to 2:1. The proposed framework serves as a valuable starting point to enhance the efficiency of LC3 system design and help decision-making to achieve desired mechanical, economic, and environmental objectives. Full article
(This article belongs to the Special Issue Sustainable Composite Construction Materials, Volume II)
Show Figures

Figure 1

Figure 1
<p>Oxides information of collected LC3 cement binder materials.</p>
Full article ">Figure 2
<p>Dataset distribution of the variables: (<b>a</b>) CC, (<b>b</b>) LS, (<b>c</b>) GYP, (<b>d</b>) OPC, (<b>e</b>) sand, (<b>f</b>) water, (<b>g</b>) SP, (<b>h</b>) KC_CC, (<b>i</b>) Temp, (<b>j</b>) PS and (<b>k</b>) age; output variable: (<b>l</b>) CS.</p>
Full article ">Figure 3
<p>Pearson correlation of variables.</p>
Full article ">Figure 4
<p>Procedures to construct a multivariate polynomial regression prediction model.</p>
Full article ">Figure 5
<p>Training and testing set performance under different degree of polynomial.</p>
Full article ">Figure 6
<p>The effect of hyperparameter α on model prediction.</p>
Full article ">Figure 7
<p>Errors between actual and predicted CS: (<b>a</b>) training set and (<b>b</b>) testing set.</p>
Full article ">Figure 8
<p>Predicted vs. actual mortar compressive strength: (<b>a</b>) training set and (<b>b</b>) testing set.</p>
Full article ">Figure 9
<p>Results of partial dependence analysis for input variables: (<b>a</b>) CC, (<b>b</b>) LS, (<b>c</b>) GYP, (<b>d</b>) OPC, (<b>e</b>) sand, (f) water, (<b>g</b>) SP, (<b>h</b>) KC_CC, (<b>i</b>) Temp, (<b>j</b>) PS and (<b>k</b>) age.</p>
Full article ">Figure 10
<p>Multi-objective Pareto-optimal solution with the corresponding TOPSIS score: (<b>a</b>) 75 MPa ≤ CS ≤ 85 MPa, (<b>b</b>) 65 MPa ≤ CS ≤ 75 MPa, (<b>c</b>) 55 MPa ≤ CS ≤ 65 MPa, (<b>d</b>) 45 MPa ≤ CS ≤ 55 MPa, (<b>e</b>) 35 MPa ≤ CS ≤ 45 MPa and (<b>f</b>) the optimal solution for each strength interval.</p>
Full article ">Figure 11
<p>(<b>a</b>–<b>k</b>): Optimal solution for different compressive strength interval; (<b>l</b>): CC to LS ratio and OPC replacement percentage of the optimal solution.</p>
Full article ">
20 pages, 7573 KiB  
Review
A Critical Review of Natural and Synthetic Polymer-Based Biological Apatite Composites for Bone Tissue Engineering
by Wasan Alkaron, Alaa Almansoori, Csaba Balázsi and Katalin Balázsi
J. Compos. Sci. 2024, 8(12), 523; https://doi.org/10.3390/jcs8120523 (registering DOI) - 12 Dec 2024
Viewed by 300
Abstract
During the past decade, there has been a continued increase in the demand for bone defect repair and replacement resulting from long-term illnesses or traumatic incidents. To address these challenges, tissue engineering research has focused on biomedical applications. This field concentrated on the [...] Read more.
During the past decade, there has been a continued increase in the demand for bone defect repair and replacement resulting from long-term illnesses or traumatic incidents. To address these challenges, tissue engineering research has focused on biomedical applications. This field concentrated on the development of suitable materials to enhance biological functionality and bone integration. Toward this aim, it is necessary to develop a proper material that provides good osseointegration and mechanical behavior by combining biopolymers with ceramics, which increase their mechanical stability and mineralization process. Hydroxyapatite (HAp) is synthesized from natural resources owing to its unique properties; for example, it can mimic the composition of bones and teeth of humans and animals. Biopolymers, including chitosan and alginate, combined with HAp, offer good chemical stability and strength required for tissue engineering. Composite biomaterials containing hydroxyapatite could be a potential substitute for artificial synthetic bone grafts. Utilizing various polymers and fabrication methodologies would efficiently customize physicochemical properties and suitable mechanical properties in synergy with biodegradation, thus enhancing their potential in bone regeneration. This review summarizes the commonly used polymers in tissue engineering, emphasizing their advantages and limitations. This paper also highlights recent advances in the production and investigation of HAp-based polymer composites used in biomedical applications. Full article
(This article belongs to the Special Issue Biopolymeric Matrices Reinforced with Natural Fibers and Nanofillers)
Show Figures

Figure 1

Figure 1
<p>A classification of biodegradable polymers, with examples, based on their source.</p>
Full article ">Figure 2
<p>Schematic diagram of natural sources and synthesis methods for HAp.</p>
Full article ">Figure 3
<p>Schematic diagram of the solvent/casting solution process.</p>
Full article ">Figure 4
<p>SEM images of composite films immersed in simulated body fluid at a temperature of 36.5 °C for (<b>a</b>) 1, (<b>b</b>) 7, (<b>c</b>) 14, and (<b>d</b>) 21 days. Reproduced with permission [<a href="#B83-jcs-08-00523" class="html-bibr">83</a>].</p>
Full article ">Figure 5
<p>Schematic diagram of the freeze-drying process.</p>
Full article ">Figure 6
<p>Morphology of (<b>a</b>) a less dispersed film (−20 °C) and (<b>b</b>) a well dispersed film (−78 °C) [<a href="#B95-jcs-08-00523" class="html-bibr">95</a>].</p>
Full article ">Figure 7
<p>Schematic diagram of the electrospinning process.</p>
Full article ">Figure 8
<p>SEM of cell scaffolds cultured, at different magnifications (<b>a1</b>,<b>a2</b>), for 1 day, (<b>b1</b>,<b>b2</b>) 7 days, (<b>c1</b>,<b>c2</b>) and 14 days. Yellow marks show the anchorage sites of the cells. Reproduced with permission [<a href="#B108-jcs-08-00523" class="html-bibr">108</a>].</p>
Full article ">Figure 9
<p>SEM micrographs of scaffolds produced by electrospinning. (<b>a</b>) Chitosan/polyvinylalcohol (Chi/PVA) fibers, (<b>b</b>) Chi/PVA + 2% hydroxyapatite (HAp) (uncrosslinked), (<b>c</b>) Chi/PVA + 5% HAp (uncrosslinked), (<b>d</b>) Chi/PVA + 5% HAp (crosslinked) [<a href="#B109-jcs-08-00523" class="html-bibr">109</a>].</p>
Full article ">Figure 10
<p>(<b>a</b>) Photograph of n-HAp/PCL, (<b>b</b>) SEM micrographs of n-HAp/PCL, and (<b>c</b>) m-HAp/PCL [<a href="#B112-jcs-08-00523" class="html-bibr">112</a>].</p>
Full article ">Figure 11
<p>SEM microstructures of coatings deposited from methanolic (<b>a</b>–<b>c</b>), ethanolic (<b>d</b>–<b>f</b>), and isopropanolic (<b>g</b>–<b>i</b>) suspensions containing 0.5 g/L chitosan and 2 g/L (<b>a</b>,<b>d</b>,<b>g</b>), 5 g/L (<b>b</b>,<b>e</b>,<b>h</b>), and 10 g/L (<b>c</b>,<b>f</b>,<b>i</b>) HAp nanoparticles at 60 V/cm. Reproduced with permission [<a href="#B115-jcs-08-00523" class="html-bibr">115</a>].</p>
Full article ">
20 pages, 6610 KiB  
Review
Smart Polymer Composites for Electrical Heating: A Review
by Alexandr V. Shchegolkov, Aleksei V. Shchegolkov, Vladimir V. Kaminskii and Maxim A. Chumak
J. Compos. Sci. 2024, 8(12), 522; https://doi.org/10.3390/jcs8120522 (registering DOI) - 12 Dec 2024
Viewed by 507
Abstract
The paper presents an overview of conductive polymer composites based on thermosetting materials, thermoplastics, and elastomers modified with carbon nanotubes (CNTs). To impart conductive properties to polymers, metal, carbon-dispersed materials, or their combinations are used. The inclusion of dispersed materials in polymers is [...] Read more.
The paper presents an overview of conductive polymer composites based on thermosetting materials, thermoplastics, and elastomers modified with carbon nanotubes (CNTs). To impart conductive properties to polymers, metal, carbon-dispersed materials, or their combinations are used. The inclusion of dispersed materials in polymers is associated with their microstructural features, as well as with polymerization methods. Such polymerization methods as melt mixing, solution technology, and introduction of fillers into the liquid phase of the composite with subsequent polymerization due to the use of a catalyst are known. Polymer composites that are capable of conducting electric current and changing their properties under the influence of an electric field, i.e., having one or more functional purposes, are called “smart” or intelligent. One such application is electric heating elements with the function of adaptive energy consumption or the effect of self-regulation of temperature depending on the surrounding conditions. A wide variety of polymers and dispersed materials with conductive properties determines a wide range of functional capabilities of the composite, including a positive temperature coefficient of resistance (PTCR) required to control temperature properties. The most effective filler in a polymer for obtaining a composite with desired properties is carbon nanomaterials, in particular, CNT. This is due to the fact that CNTs are a nanosized material with a high bulk density at a low weight, which allows for high electrical conductivity. Calculation of model parameters of polymer composites containing carbon nanostructures can be carried out using neural networks and machine learning, which give a fundamentally new result. The article contains sections with an assessment of various types of polymer matrices based on thermosets, thermoplastics, and elastomers. To impart electrically conductive properties, various options for fillers based on Ag, Au, Cu, Ni, Fe, and CNTs are considered. Methods for introducing dispersed fillers into polymer matrices are presented. Functional composites with a positive temperature coefficient and methods for their regulation are considered. The mechanisms of various electrophysical processes in conductive composites are considered, taking into account the resulting electrical conductivity based on the tunnel effect and hopping conductivity. An analysis of electric heaters based on various polymer matrices and dispersed fillers is carried out, taking into account their operating modes. Thus, the conducted review of modern scientific and practical research in the field of obtaining electrically conductive composites based on various types of polymer matrices with nanosized additives allows us to assess the prospects for the formation of functional composites for electrical heating, taking into account the mechanisms of electrical conductivity and new technologies based on machine learning and neural networks. Full article
Show Figures

Figure 1

Figure 1
<p>Scheme for obtaining an epoxy composite containing Al<sub>2</sub>O<sub>3</sub>.</p>
Full article ">Figure 2
<p>Scheme for obtaining an epoxy composite containing MoS<sub>2</sub> nanosheets and uniformly distributed CNTs [<a href="#B13-jcs-08-00522" class="html-bibr">13</a>].</p>
Full article ">Figure 3
<p>TEM images: (<b>a</b>)—non-stratified MMT; (<b>b</b>)—stratified MMT [<a href="#B18-jcs-08-00522" class="html-bibr">18</a>].</p>
Full article ">Figure 4
<p>SEM images of some studied composites in a fresh state (unconditioned samples) at different magnifications: (<b>a</b>) LLD 190 (50,000×); (<b>b</b>) LLD 192 (50,000×); (<b>c</b>) LLD 192 (5000×); (<b>d</b>) LLD 122 (20,000×) [<a href="#B19-jcs-08-00522" class="html-bibr">19</a>].</p>
Full article ">Figure 5
<p>SEM of polyethylene/graphite [<a href="#B21-jcs-08-00522" class="html-bibr">21</a>].</p>
Full article ">Figure 6
<p>SEM and EDX images of elastomer(s) with Ni and MWCNTs: (<b>a</b>)—SEM snapshot; (<b>b</b>)—EDX of Ni, with Cu and MWCNTs; (<b>c</b>)—SEM snapshot; (<b>d</b>)—EDX of Cu [<a href="#B32-jcs-08-00522" class="html-bibr">32</a>].</p>
Full article ">Figure 7
<p>Film-fabrication process [<a href="#B50-jcs-08-00522" class="html-bibr">50</a>].</p>
Full article ">Figure 8
<p>The mechanism of change in dispersion and aspect ratio of CNTs under the action of shear forces during three-roll grinding [<a href="#B51-jcs-08-00522" class="html-bibr">51</a>].</p>
Full article ">Figure 9
<p>Five main stages of research [<a href="#B110-jcs-08-00522" class="html-bibr">110</a>].</p>
Full article ">Figure 10
<p>Architecture of an ANN (circles are neurons in each layer) [<a href="#B110-jcs-08-00522" class="html-bibr">110</a>].</p>
Full article ">
8 pages, 3255 KiB  
Article
Reduction in Core Loss of Soft Magnetic Composites with TiO2 Coated Fe Powder
by Sunwoo Lee, Sungjoon Choi, Jae-Hyoung You, Jung-Woo Lee, Sang-Im Yoo and Chan Park
J. Compos. Sci. 2024, 8(12), 521; https://doi.org/10.3390/jcs8120521 - 12 Dec 2024
Viewed by 348
Abstract
This study demonstrates the improvement of core loss through the reduction of eddy current loss in soft magnetic composites (SMCs) composed of TiO2-coated Fe powder and epoxy resin. A thin and uniform TiO2 insulating layer was successfully deposited on the [...] Read more.
This study demonstrates the improvement of core loss through the reduction of eddy current loss in soft magnetic composites (SMCs) composed of TiO2-coated Fe powder and epoxy resin. A thin and uniform TiO2 insulating layer was successfully deposited on the surface of Fe powder via a sol-gel process, employing titanium (IV) butoxide (TBOT) as the precursor. Scanning transmission electron microscopy and energy-dispersive X-ray spectroscopy analyses confirmed the formation of a core/shell Fe/TiO2 structure, with a coating thickness of several tens of nanometers. Increasing the TBOT concentration and coating duration time led to an improved quality factor (Q factor) and a shift of the maximum Q factor values to higher frequency regions. Notably, the permeability was decreased slightly from 14.2 to 13.4, but the core loss, measured at various AC frequencies under 20 mT and then separated into hysteresis loss and eddy current loss at 1 MHz, was significantly reduced from 573 to 435 kW/m3 when the Fe powder was coated with TiO2 using a 2.5 wt.% TBOT solution for 8 h. This reduction in core loss is attributed to the effective suppression of inter-particle eddy currents by the TiO2 insulation layer. Full article
Show Figures

Figure 1

Figure 1
<p>SEM micrographs of (<b>a</b>) uncoated powder and (<b>b</b>) TiO<sub>2</sub>-coated powder when the concentration of TBOT and the coating reaction time were 2.5 wt.% of Fe powder and 8 h, respectively.</p>
Full article ">Figure 2
<p>STEM micrographs of Fe powders coated with TiO<sub>2</sub> insulation layers when the concentrations of TBOT and the coating reaction times were (<b>a</b>) 1 wt.% and 1 h, (<b>b</b>) 2.5 wt.% and 1 h, and (<b>c</b>) 2.5 wt.% and 8 h.</p>
Full article ">Figure 3
<p>(<b>a</b>,<b>b</b>) STEM micrographs and (<b>c</b>) element mapping profiles of TiO<sub>2</sub>-coated Fe powder when the concentration of TBOT and the coating reaction time were 2.5 wt.% of Fe powder and 8 h, respectively.</p>
Full article ">Figure 4
<p>Plots of (<b>a</b>) effective permeability (μ<sub>e</sub>) and (<b>b</b>) Q factor values as a function of applied frequency.</p>
Full article ">Figure 5
<p>(<b>a</b>) Behavior of the loss per cycle and (<b>b</b>) total core loss, hysteresis loss, and eddy current loss at 1 MHz of SMCs of Fe and TiO<sub>2</sub>-coated Fe powders.</p>
Full article ">
10 pages, 2798 KiB  
Article
The Obtaining and Study of Composite Chromium-Containing Pigments from Technogenic Waste
by Bakyt Smailov, Bakhriddin Turakulov, Almagul Kadirbayeva, Nursulu Sarypbekova, Nurpeis Issabayev and Yerzhan Oralbay
J. Compos. Sci. 2024, 8(12), 520; https://doi.org/10.3390/jcs8120520 - 11 Dec 2024
Viewed by 391
Abstract
This article provides information on the processing of chromium-containing waste from the Aktobe ferroalloy compounds plant using chemical reagents followed by high-temperature heat treatment for the synthesis of a composite chromite pigment used in the textile industry. This technology was developed for the [...] Read more.
This article provides information on the processing of chromium-containing waste from the Aktobe ferroalloy compounds plant using chemical reagents followed by high-temperature heat treatment for the synthesis of a composite chromite pigment used in the textile industry. This technology was developed for the first time for the purpose of recycling industrial waste and rational use of natural resources. The obtained pigments were analyzed by the X-ray phase of a D878-PC75-17.0 incident beam monochromator and the phase composition of the composite chromite pigment was studied. The thermogravimetric analysis of the composite chromite pigments was performed using a TGA/DSC 1HT/319 analyzer to determine the change in mass with time and temperature. According to the TGA results, the mass loss was determined to be 0.18% of the total mass. The elemental composition of the composite chromite pigment was determined using a JEOL JSM-6490 LV SEM device and the content of chromium oxide (Cr2O3) was determined, which reached up to 50%. The thermodynamic patterns of the processes occurring during the production of chromite pigments were studied using the integrated Chemistry software pack HSC-6. The results of testing printed and processed cotton and composite fabrics by the proposed method showed that the color fastness to washing and wet and dry friction is 4 points and the wear resistance assessment is 4860 and 6485 cycles, respectively. Composite chromite pigment based on technogenic wastes is recommended for use in various coloring compositions, including those used for printing on cotton and composite fabrics. Full article
(This article belongs to the Special Issue Composites: A Sustainable Material Solution)
Show Figures

Figure 1

Figure 1
<p>The flow chart diagram of pigment synthesis.</p>
Full article ">Figure 2
<p>X-ray phase analysis of chromite pigments.</p>
Full article ">Figure 3
<p>Thermogravimetric analysis of chromite pigments.</p>
Full article ">Figure 4
<p>IR spectrum of chromite pigments.</p>
Full article ">Figure 5
<p>A micrograph of chromite pigments.</p>
Full article ">Figure 6
<p>Samples of fabrics with applied pigment from technogenic wastes. (<b>a</b>) Cotton fabric Alatau article 1001. (<b>b</b>) Composite fabric Arlan article 6005.</p>
Full article ">
10 pages, 2503 KiB  
Article
The Influence of Ultraviolet Irradiation on the Structure and Properties of Acrylonitrile Butadiene Styrene/Lignin Composites
by Ilya A. Grishanovich, Semen L. Shestakov, Alexander V. Potashev, Artyom V. Belesov and Aleksandr Yu. Kozhevnikov
J. Compos. Sci. 2024, 8(12), 519; https://doi.org/10.3390/jcs8120519 - 10 Dec 2024
Viewed by 355
Abstract
ABS plastic is an inexpensive material with attractive physical and chemical properties. Unfortunately, it is susceptible to degradation under UV radiation, so it limits the use of this material outdoors. In this paper, we demonstrate a low-cost approach to reduce the photodegradation of [...] Read more.
ABS plastic is an inexpensive material with attractive physical and chemical properties. Unfortunately, it is susceptible to degradation under UV radiation, so it limits the use of this material outdoors. In this paper, we demonstrate a low-cost approach to reduce the photodegradation of ABS plastic by using additives of kraft lignin and dioxane lignin as UV absorbers. Lignin is an abundant plant polymer, which is a waste product of the pulp and paper industry. Non-regular structure of lignin hampers its use in industry. However, there is possible use of lignin as an addition to enhance the properties of resulting materials. In this study, we obtained composites of ABS and lignin with the hot extrusion method. Adding up to 15% of lignin to ABS plastic does not have a significant negative impact on tensile properties. We irradiated the resulting composites with UV and studied the UV effects on their mechanical properties and chemical structure. Oxidative degradation was characterized by FTIR and 2D NMR methods. The results showed that small lignin additions reduced the photodegradation of ABS. The previously undescribed product of the degradation of the obtained composites was detected with the use of the set of 2D NMR spectra of the composites. We proposed a scheme for the formation of this photodegradation product based on the obtained data. Full article
(This article belongs to the Section Polymer Composites)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>FT-IR spectra before (blue) and after (red) UV treatment for pure ABS (<b>bottom</b>) and composites with 5 % (<b>middle</b>) and 10 % (<b>top</b>) Kraft lignin content.</p>
Full article ">Figure 2
<p>HSQC (blue and red cross-peaks) and HMBC (purple peaks) NMR spectra of ABS-KL with 10% of lignin content after UV treatment. The cross peak labels include the chemical shifts and numbers of atoms (in the brackets) in the detected structure. The found new structure is highlighted with green.</p>
Full article ">Figure 3
<p>Diagrams of tensile properties of obtaining composites: (<b>a</b>) tensile strength, (<b>b</b>) elongation at the break, and (<b>c</b>) Young’s modulus.</p>
Full article ">Figure 4
<p>Scheme of photodegradation product formation pathways. Arrows show the direction of chemical reactions: (<b>1</b>) Formation of O-radical and its product (<b>2</b>) Formation of C-radical and its product. (<b>3</b>) Formation of co-product of O- and C-radicals. (<b>4</b>) Esterification of co-product and lignin. hν—UV radiation. t°—thermal impact. Red frame—new found structure.</p>
Full article ">
15 pages, 6123 KiB  
Article
Impact of Moisture Absorption on Optical Fiber Sensors: New Bragg Law Formulation for Monitoring Composite Structures
by Pietro Aceti and Giuseppe Sala
J. Compos. Sci. 2024, 8(12), 518; https://doi.org/10.3390/jcs8120518 - 9 Dec 2024
Viewed by 435
Abstract
In recent decades, the aviation industry has increasingly adopted composite materials for various aircraft components, due to their high strength-to-weight ratio and durability. To ensure the safety and reliability of these structures, Health and Usage Monitoring Systems (HUMSs) based on fiber optics (FO), [...] Read more.
In recent decades, the aviation industry has increasingly adopted composite materials for various aircraft components, due to their high strength-to-weight ratio and durability. To ensure the safety and reliability of these structures, Health and Usage Monitoring Systems (HUMSs) based on fiber optics (FO), particularly Fiber Bragg Grating (FBG) sensors, have been developed. However, both composite materials and optical fibers are susceptible to environmental factors such as moisture, in addition to the well-known effects of mechanical stress and thermal loads. Moisture absorption can lead to the degradation of mechanical properties, posing a risk to the structural integrity of aircraft components. This research aims to quantify and monitor the impact of moisture on composite materials. A new formulation of the Bragg equation is introduced, incorporating mechanical strain, thermal expansion, and hygroscopic swelling to accurately measure Bragg wavelength variations. Experimental validation was performed using both uncoated and polyimide-coated optical fibers subjected to controlled hygrothermal conditions in a climate chamber. The results demonstrate that uncoated fibers are insensitive to humidity, whereas coated fibers exhibit measurable wavelength shifts due to moisture absorption. The proposed model effectively predicts these shifts, with errors consistently below 2.6%. This approach is crucial for improving the performance and reliability of HUMSs in monitoring composite structures, ensuring long-term safety in extreme environmental conditions. Full article
(This article belongs to the Section Composites Manufacturing and Processing)
Show Figures

Figure 1

Figure 1
<p>Accidents due to hygrothermal effects.</p>
Full article ">Figure 2
<p>Coated optical fiber scheme.</p>
Full article ">Figure 3
<p>Experimental setup.</p>
Full article ">Figure 4
<p>Wavelength trend in time for an uncoated fiber.</p>
Full article ">Figure 5
<p>Linear interpolation and sensitivities, uncoated fiber.</p>
Full article ">Figure 6
<p>Coated fiber response.</p>
Full article ">Figure 7
<p>Linear interpolation and sensitivities. (<b>a</b>) Linear interpolation for temperature sensitivities. (<b>b</b>) Linear interpolation for humidity sensitivities.</p>
Full article ">Figure 8
<p>Comparison between theoretical and experimental wavelengths at each constant temperature.</p>
Full article ">Figure 9
<p>Comparison between theoretical and experimental wavelengths at each constant temperature and relative humidity.</p>
Full article ">
21 pages, 8662 KiB  
Article
Effect of Alumina Proportion on the Microstructure and Technical and Mechanical Characteristics of Zirconia-Based Porous Ceramics
by Rusul Ahmed Shakir, Róbert Géber, Marwan T. Mezher, Tomasz Trzepieciński and Ferenc Móricz
J. Compos. Sci. 2024, 8(12), 517; https://doi.org/10.3390/jcs8120517 - 9 Dec 2024
Viewed by 416
Abstract
The current study investigates the process of preparing and analysing porous-structured ceramics made from zirconium, aluminium, and magnesium ceramic oxides. The starch consolidation casting (SCC) technique, with different types of starches (potato and tapioca), was used for this purpose. Our objective was to [...] Read more.
The current study investigates the process of preparing and analysing porous-structured ceramics made from zirconium, aluminium, and magnesium ceramic oxides. The starch consolidation casting (SCC) technique, with different types of starches (potato and tapioca), was used for this purpose. Our objective was to methodically examine the impact of different processing factors, such as the temperature at which pre-sintering and sintering occur, and the proportions of ceramic powders, on the microstructure, mechanical characteristics, and porosity of the resultant composites. Pre-sintering effectively reduced the rate of shrinkage during the final sintering stage; this resulted in more controlled and predictable shrinkage, leading to better dimensional stability and reduced risk of defects in the final product. A higher alumina content was associated with an increase in apparent porosity and a reduction in volume shrinkage and apparent densities. The mercury intrusion porosimetry (MIP) findings concluded that the prepared porous ceramics have a multi-modal pore structure. The highest calculated compressive strength was 76.89 MPa for a sample with a porous structure, which was manufactured using 20 wt.% tapioca starch and 30 wt.% alumina content. The main advantage of alumina is its ability to improve compressive strength by refining the grain structure and serving as a barrier against fracture development. Full article
(This article belongs to the Section Composites Modelling and Characterization)
Show Figures

Figure 1

Figure 1
<p>Particle size distribution of potato and tapioca starches.</p>
Full article ">Figure 2
<p>Swelling factor via mixing time for potato and tapioca starches.</p>
Full article ">Figure 3
<p>Apparent density via Al<sub>2</sub>O<sub>3</sub> content for porous ceramics: (<b>a</b>) after pre-sintering; (<b>b</b>) after sintering.</p>
Full article ">Figure 4
<p>Apparent porosity via Al<sub>2</sub>O<sub>3</sub> content for porous ceramics: (<b>a</b>) after pre-sintering; (<b>b</b>) after sintering.</p>
Full article ">Figure 5
<p>Volume shrinkage via Al<sub>2</sub>O<sub>3</sub> content for porous ceramics: (<b>a</b>) after pre-sintering; (<b>b</b>) after sintering.</p>
Full article ">Figure 6
<p>SEM micrographs of porous ceramics after pre-sintering (<b>a</b>) using potato starch, (<b>b</b>) using tapioca starch, and (<b>c</b>) using tapioca–potato starch at 50:50 wt.% ratio.</p>
Full article ">Figure 7
<p>SEM micrographs of porous ceramics after sintering (<b>a</b>) using potato starch, (<b>b</b>) using tapioca starch, and (<b>c</b>) using tapioca–potato starch at 50:50 wt.% ratio.</p>
Full article ">Figure 8
<p>SEM micrographs of porous ceramics after sintering: (<b>a</b>) using tapioca starch without pre-sintering; (<b>b</b>) using tapioca–potato starch at 50:50 wt.% ratio with pre-sintering.</p>
Full article ">Figure 9
<p>SEM micrographs of porous ceramics after pre-sintering (<b>a</b>) using potato starch, (<b>b</b>) using tapioca starch, and (<b>c</b>) using tapioca–potato starch at 50:50 wt.% ratio.</p>
Full article ">Figure 10
<p>SEM micrographs of porous ceramics after sintering (<b>a</b>) using potato starch, (<b>b</b>) using tapioca starch, and (<b>c</b>) using tapioca–potato starch at 50:50 wt.% ratio.</p>
Full article ">Figure 11
<p>The pore size distribution via relative pore volume.</p>
Full article ">Figure 12
<p>The total volume intrusion via applied pressure.</p>
Full article ">Figure 13
<p>XRD pattern for pre-sintered ceramic with 15 wt.% alumina.</p>
Full article ">Figure 14
<p>XRD pattern for pre-sintered ceramic with 30 wt.% alumina.</p>
Full article ">Figure 15
<p>XRD pattern for sintered ceramic with 15 wt.% alumina.</p>
Full article ">Figure 16
<p>XRD pattern for sintered ceramic with 30 wt.% alumina.</p>
Full article ">Figure 17
<p>Compressive strength vs. alumina content.</p>
Full article ">Figure 18
<p>Fracture mode for sintered ceramic with 15 wt.% alumina.</p>
Full article ">Figure 19
<p>SEM micrographs of sintered porous ceramics (<b>a</b>) with pre-sintering and (<b>b</b>) without pre-sintering.</p>
Full article ">
13 pages, 2808 KiB  
Article
Synthesis and Characterization of Thermosensitive Nanosupports with Core–Shell Structure (PSt-PNIPAM) and Their Application with Silver Nanoparticles
by Ana Cecilia Palos Zúñiga, Isabel Araceli Facundo Arzola, Ma. Gloria Rosales Sosa, Yadira Marlen Rangel Hernández, Claudia Verónica Reyes Guzmán, Manuel García Yregoi, Leonor Muñoz Ramirez and Hened Saade Caballero
J. Compos. Sci. 2024, 8(12), 516; https://doi.org/10.3390/jcs8120516 - 9 Dec 2024
Viewed by 302
Abstract
The present study synthesized silver nanoparticles supported on a thermosensitive polymer with a core–shell structure, formed by a polystyrene (PS) core and a poly(N-isopropylacrylamide) (PNIPAM)/Poly(N, N-methylenebisacrylamide) (MBA) shell. The PS core was synthesized via semicontinuous heterophase polymerization at a flow of 0.073 g/min, [...] Read more.
The present study synthesized silver nanoparticles supported on a thermosensitive polymer with a core–shell structure, formed by a polystyrene (PS) core and a poly(N-isopropylacrylamide) (PNIPAM)/Poly(N, N-methylenebisacrylamide) (MBA) shell. The PS core was synthesized via semicontinuous heterophase polymerization at a flow of 0.073 g/min, enabling polystyrene nanoparticles with an average size (Dz) of 35.2 nm to be obtained. In the next stage, the conditions required for polymerization synthesis were established in seeded microemulsion using PS nanoparticles as seed and semicontinuously adding the thermosensitive shell monomer (PNIPAM/MBA) under monomer-flooded conditions to favor shell formation. The non-homopolymerization of PNIPAM/MBA was demonstrated by obtaining nanoparticles with a core–shell structure, with average particle sizes of 41 nm and extremely low and narrow polydispersity index (PDI) values (1.1). The thermosensitive behavior was analyzed by QLS, revealing an average shrinkage of 4.03 nm and a percentage of shrinkage of 23.7%. Finally, silver nanoparticles were synthesized on the core–shell heat-sensitive nanoparticles in a colloidal solution containing the latices, while silver nanoparticles were anchored onto the cross-linked heat-sensitive network via the formation of complexes between the Ag+ ions and the nitrogen contained in the PNIPAM/MBA network, favoring anchorage around the network and maintaining a size of 5 nm. Full article
(This article belongs to the Special Issue Characterization of Polymer Nanocomposites)
Show Figures

Figure 1

Figure 1
<p>Micrographs and histogram of the final styrene latex sample prepared via semicontinuous microemulsion polymerization at an addition rate of 0.073 g/min.</p>
Full article ">Figure 2
<p>Micrographs and histogram of the final latex samples of the core–shell nanoparticles (PS-PNIPAM/MBA) prepared via seed polymerization at an addition flow rate of 0.11 g/min.</p>
Full article ">Figure 3
<p>(<b>a</b>) Histograms of the final latex samples obtained with the PS seed and (<b>b</b>) core–shell (PS-PNIPAM/MBA) particles.</p>
Full article ">Figure 4
<p>Change in particle size as a function of temperature, as measured by QLS for core–shell (PS-PNIPAM) nanoparticles (●) and compared to PS seed (♦). The dotted line indicates the temperature at which the change in Dz appears.</p>
Full article ">Figure 5
<p>Micrographs, obtained via STEM, of silver nanoparticles on core–shell (PS-PNIPAM/MBA) thermosensitive particles.</p>
Full article ">Figure 6
<p>Change in particle size as a function of temperature, as measured by QLS for core–shell (PS-PNIPAM/MBA) nanoparticles (●) and compared to PS- PNIPAM/MBA-Ag (♦).</p>
Full article ">
10 pages, 845 KiB  
Article
Application of a Multi-Component Composite Edible Coating for the Preservation of Strawberry Fruit
by Rafael González-Cuello, Aura Lucia Parada-Castro and Rodrigo Ortega-Toro
J. Compos. Sci. 2024, 8(12), 515; https://doi.org/10.3390/jcs8120515 - 6 Dec 2024
Viewed by 385
Abstract
The rapid perishability of strawberries due to factors such as fungal decay, mechanical damage, and respiration significantly limits their shelf life. In this study, a novel multi-component edible coating composed of bacterial cellulose, chitosan, and gellan gum (BChG) was developed to enhance the [...] Read more.
The rapid perishability of strawberries due to factors such as fungal decay, mechanical damage, and respiration significantly limits their shelf life. In this study, a novel multi-component edible coating composed of bacterial cellulose, chitosan, and gellan gum (BChG) was developed to enhance the postharvest quality and extend the shelf life of strawberries. The coated fruits were evaluated over a 15-day storage period for key parameters such as weight loss, total soluble solids (TSS), titratable acidity (TA), enzymatic activity, color retention, antioxidant activity, and microbiological analysis. The results demonstrated that coated strawberries exhibited significantly lower weight loss, reduced cellulase activity, and higher retention of TSS and TA compared to uncoated controls. The evaluation of microbial quality indicated that coatings, particularly those with higher concentrations of chitosan, control the growth of total mesophilic aerobic bacteria (TMAB) and molds and yeasts (MY), due to the antimicrobial properties of chitosan. This contributed to extending the shelf life of the fruit by preventing spoilage and reducing the risk of toxic compound formation. Additionally, the BChG coatings also preserved the characteristic red color of the fruit and maintained higher antioxidant activity, with BChG-4 being the most effective formulation. The inclusion of chitosan in the coatings was found to play a crucial role in reducing respiration, delaying ripening, and enhancing the fruit’s resistance to oxidative damage. Overall, multi-component coatings, particularly those with higher chitosan concentrations, offer a promising method for extending the shelf life of strawberries, reducing postharvest losses, and preserving fruit quality under ambient storage conditions. Full article
Show Figures

Figure 1

Figure 1
<p>Quality characteristics of strawberry fruits. (<b>a</b>) Soluble solids; (<b>b</b>) acidity soluble; (<b>c</b>) weight loss; and (<b>d</b>) color change (ΔE). Vertical bars indicate the standard error of the means. (** significant difference in <span class="html-italic">p</span> &lt; 0.05 according to LSD test for the end of the storage time; NS: there was no significant difference in <span class="html-italic">p</span> &lt; 0.05). Vertical bars indicate the standard error of the means.</p>
Full article ">Figure 2
<p>Enzymatic and antioxidant activities of strawberry fruits. (<b>a</b>) cellulose activity; (<b>b</b>) antioxidant activity. Vertical bars indicate the standard error of the means (** significant difference in <span class="html-italic">p</span> &lt; 0.05 according to LSD test for the end of the storage time).</p>
Full article ">Figure 3
<p>Microbial count of control and coated strawberries during storage time. (<b>a</b>) Total mesophilic aerobic bacteria (TMAB); (<b>b</b>) Mold and yeast (MY). Values are given as means ± SD. (** significant difference in <span class="html-italic">p</span> &lt; 0.05 according to LSD test for the end of the storage time; NS: there was no significant difference in <span class="html-italic">p</span> &lt; 0.05). Vertical bars indicate the standard error of the means.</p>
Full article ">
14 pages, 8360 KiB  
Article
Investigation of the Impact of SmFeN Doping on the Anisotropic NdFeB/SmFeN Composite Magnets
by Wei Cai, Xinqi Zhang, Zhiping Shi, Haibo Chen, Qiaomin Zhu, Kun Jiang, Liang Qiao, Yao Ying, Wangchang Li, Jing Yu, Juan Li, Jingwu Zheng and Shenglei Che
J. Compos. Sci. 2024, 8(12), 514; https://doi.org/10.3390/jcs8120514 - 6 Dec 2024
Viewed by 361
Abstract
By incorporating various types of permanent magnetic powders, composite magnets with cost-effectiveness and a wide range of magnetic properties can be achieved. In this study, the anisotropic composite magnets were fabricated using the hot press forming method, which involved blending neodymium iron boron [...] Read more.
By incorporating various types of permanent magnetic powders, composite magnets with cost-effectiveness and a wide range of magnetic properties can be achieved. In this study, the anisotropic composite magnets were fabricated using the hot press forming method, which involved blending neodymium iron boron (NdFeB) powder and samarium iron nitrogen (SmFeN) powder. The experiment demonstrated that the magnet density reaches its maximum point when the doping level of SmFeN reaches 20 wt.%, aligning remarkably well with the corresponding theoretical value of 19.22 wt.% achieved through a cubic stacking arrangement. In the absence of an applied magnetic field or under a sufficiently high oriented magnetic field (3 T), the remanence variation pattern in composite magnets doped with different amounts of SmFeN aligns consistently with the density pattern, yielding a maximum value of 20%. However, in the actual solidification process, the orientation field is insufficient (e.g., 1.5 T), necessitating a doping amount that exceeds the value corresponding to peak density by 28% to achieve optimal remanence. This observation suggests that the incorporation of a higher proportion of small-sized and relatively low coercivity SmFeN magnetic powder can effectively facilitate the rotational alignment of neighboring large-sized NdFeB magnetic powder under weak magnetic fields, thereby inducing a synergistic effect. Full article
(This article belongs to the Special Issue Metal Composites, Volume II)
Show Figures

Figure 1

Figure 1
<p>Pressing principle of anisotropic NdFeB/SmFeN composite magnet: (1) orientation coil; (2) thermocouple; (3) composite magnet; (4) indenter; (5) press the mold.</p>
Full article ">Figure 2
<p>Characterization of morphology and corresponding particle size distribution in anisotropic NdFeB (<b>a</b>,<b>c</b>) and anisotropic SmFeN (<b>b</b>,<b>d</b>) magnetic powders.</p>
Full article ">Figure 3
<p>Different stacking modes of anisotropic Nd-Fe-B magnetic particles: (<b>a</b>) simple cubic stacking; (<b>b</b>) body-centered cubic packing; (<b>c</b>) hexagonal packing.</p>
Full article ">Figure 4
<p>Magnetic field distribution of anisotropic NdFeB magnetic particles under different stacking modes: (<b>a</b>) simple cubic stacking; (<b>b</b>) body-centred cubic packing; (<b>c</b>) hexagonal packing.</p>
Full article ">Figure 5
<p>Anisotropic Nd-Fe-B magnetic powder densest stacking: (<b>a</b>) physical model; (<b>b</b>) simplified model; (<b>c</b>) analytical model.</p>
Full article ">Figure 6
<p>The microscopic structure of NdFeB/SmFeN composite magnets with different SmFeN content: (<b>a</b>) 0%; (<b>b</b>) 20%; (<b>c</b>) 28%; (<b>d</b>) 40%; (<b>e</b>) 60%; (<b>f</b>) 80%; (<b>g</b>) 100%; and the density variation curves (<b>h</b>).</p>
Full article ">Figure 6 Cont.
<p>The microscopic structure of NdFeB/SmFeN composite magnets with different SmFeN content: (<b>a</b>) 0%; (<b>b</b>) 20%; (<b>c</b>) 28%; (<b>d</b>) 40%; (<b>e</b>) 60%; (<b>f</b>) 80%; (<b>g</b>) 100%; and the density variation curves (<b>h</b>).</p>
Full article ">Figure 7
<p>Magnetic properties of anisotropic NdFeB/SmFeN composite magnets at different proportions: (<b>a</b>,<b>b</b>) 3 T oriented magnetic field; (<b>c</b>,<b>d</b>) 1.5 T oriented magnetic field; (<b>e</b>,<b>f</b>) 0.8 T oriented magnetic field; (<b>g</b>,<b>h</b>) non-oriented magnetic field.</p>
Full article ">Figure 7 Cont.
<p>Magnetic properties of anisotropic NdFeB/SmFeN composite magnets at different proportions: (<b>a</b>,<b>b</b>) 3 T oriented magnetic field; (<b>c</b>,<b>d</b>) 1.5 T oriented magnetic field; (<b>e</b>,<b>f</b>) 0.8 T oriented magnetic field; (<b>g</b>,<b>h</b>) non-oriented magnetic field.</p>
Full article ">Figure 8
<p>The demagnetization curves (<b>a</b>) at 0.8 T orientation magnetic field and squareness ratio (<b>b</b>) of NdFeB/SmFeN composite magnets with varying SmFeN contents were analyzed, along with the demagnetization curves (<b>c</b>) and orientation degrees (<b>d</b>) under different orientation magnetic fields.</p>
Full article ">
17 pages, 3577 KiB  
Article
A Molecular Dynamics Study on Auxetic Behaviors of Origami Graphene/Cu Nanocomposites
by Bai-Wei Na, Hai-Ning Zhang, Yin Fan and Yeqing Wang
J. Compos. Sci. 2024, 8(12), 513; https://doi.org/10.3390/jcs8120513 - 6 Dec 2024
Viewed by 394
Abstract
Graphene is considered to be one of the most promising reinforcement phases for nanocomposites due to its unique two-dimensional planar structure with excellent mechanical properties. After the design of origami, the 2D material will obtain a negative Poisson’s ratio in the in-plane direction [...] Read more.
Graphene is considered to be one of the most promising reinforcement phases for nanocomposites due to its unique two-dimensional planar structure with excellent mechanical properties. After the design of origami, the 2D material will obtain a negative Poisson’s ratio in the in-plane direction and become a metamaterial with unusual mechanical properties. Inspired by this, an origami pattern is adopted for graphene at an atomic scale using a molecular dynamics (MD) approach, and then origami graphene is embedded into a single-crystal copper matrix to obtain origami graphene/copper nanocomposites with auxetic behaviors. In the modeling, the periodic boundary condition is chosen to exhibit the Poisson’s ratio of the whole system. Under the isothermal–isobaric ensemble, the interactions between C-C, Cu-Cu, and C-Cu atoms are, respectively, determined by three potential functions: AIREBO, EAM, and LJ. The effect of the origami graphene/copper interfacial gap on the critical strain of incremental Poisson’s ratio, critical strain of engineering Poisson’s ratio, and moduli of the origami graphene/copper nanocomposites is studied to determine the optimum distance between the two phases. The influences of the mass fraction of carbon atom and temperature on those properties are discussed in detail after the MD model is confirmed. Full article
(This article belongs to the Special Issue Mechanical Properties of Composite Materials and Joints)
Show Figures

Figure 1

Figure 1
<p>Schematic diagrams of (<b>a</b>) Miura origami and (<b>b</b>) Miura origami graphene, where the solid black line represents a fold outward from the paper, the dotted blue line represents a fold inward from the paper and carbon atoms in four regions are in different colors.</p>
Full article ">Figure 2
<p>Schematic diagrams of origami graphene/copper nanocomposite, Cu atoms are in blue and C atoms are in red.</p>
Full article ">Figure 3
<p>Schematic diagram of carbon/copper interfacial gap in origami graphene/copper nanocomposites, where Cu atoms are in blue and C atoms are in red.</p>
Full article ">Figure 4
<p>Strain curve between <span class="html-italic">x</span> direction and <span class="html-italic">y</span> direction.</p>
Full article ">Figure 5
<p>Relationship between the interfacial gap and the variation in elastic modulus in the <span class="html-italic">x</span> and <span class="html-italic">y</span> direction of the composite material.</p>
Full article ">Figure 6
<p>Relationship between bonding energy and interfacial gap of nanocomposites.</p>
Full article ">Figure 7
<p>(<b>a</b>) Relationship between bonding energy and basic parallelogram length. (<b>b</b>) Relationship between bonding energy and dihedral angle.</p>
Full article ">Figure 8
<p>Modulus of elasticity of origami graphene/copper nanocomposites in <span class="html-italic">x</span>, <span class="html-italic">y,</span> and <span class="html-italic">z</span> directions versus mass fraction of carbon in origami graphene/copper nanocomposites.</p>
Full article ">Figure 9
<p>(<b>a</b>) Engineering Poisson’s ratio versus thickness for <span class="html-italic">x</span>, <span class="html-italic">y</span> direction of nanocomposites. (<b>b</b>) Engineering Poisson’s ratio versus thickness for <span class="html-italic">x</span>, <span class="html-italic">z</span> direction of nanocomposites. (<b>c</b>) Engineering Poisson’s ratio versus thickness for <span class="html-italic">y</span>, <span class="html-italic">z</span> direction of nanocomposites.</p>
Full article ">
12 pages, 4508 KiB  
Article
Fabrication of PVTF Films with High Piezoelectric Properties Through Directional Heat Treatment
by Xin Xin, Aotian Yee, Zhiyuan Zhou, Xuzhao He, Wenjian Weng, Chengwei Wu and Kui Cheng
J. Compos. Sci. 2024, 8(12), 512; https://doi.org/10.3390/jcs8120512 - 6 Dec 2024
Viewed by 383
Abstract
Piezoelectric materials can realize the mutual conversion of mechanical energy and electric energy, so they have excellent application prospects in the fields of sensors, energy collectors and biological materials. The poly(vinylidene fluoride) (PVDF)-based polymers have the best piezoelectric properties in the piezoelectric polymer, [...] Read more.
Piezoelectric materials can realize the mutual conversion of mechanical energy and electric energy, so they have excellent application prospects in the fields of sensors, energy collectors and biological materials. The poly(vinylidene fluoride) (PVDF)-based polymers have the best piezoelectric properties in the piezoelectric polymer, but they still have a large room for improvement compared with the piezoelectric ceramics. Improving their content of the polar β phase has become a consensus to polish up the piezoelectric performance. Most available studies construct hydrogen bonds or coulomb interactions between the surface of the dopant and molecular chains by doping, which promotes the molecular chains arrangement and thus facilitates the formation of the polar β phase. Recent studies show that the ordered arrangement of molecular chains is also important for piezoelectric properties. At present, the main way to improve the piezoelectric performance of PVDF is through doping or complex heat treatment process. Here, the poly(vinylidene fluoride-co-trifluoroethylene) (P(VDF-TrFE)) film was treated by directional heat treatment which used a heating table. Compared with uniform heat treatment like muffle furnace heat treatment, this simple vertical temperature gradient has many advantages for the content of the β phase and the crystallinity of P(VDF-TrFE). The results of the experiment showed that the content of the β phase of films remained at about 88%. When the film thickness was limited to 100 μm and the heat treatment temperature was limited to 200 °C, its crystallinity could reach 75% and the highest piezoelectric coefficient could reach 33.5 ± 0.7 pC/N. P(VDF-TrFE) films based on the experimental methods described above that show great potential for future applications in electronic devices and biomedical applications. Full article
(This article belongs to the Special Issue Feature Papers in Journal of Composites Science in 2024)
Show Figures

Figure 1

Figure 1
<p>(<b>a</b>) Schematic diagram of P(VDF-TrFE) obtained by the heating table heat treatment and the SEM images of P(VDF-TrFE) of different thicknesses including (<b>b</b>) 50 μm, (<b>c</b>) 100 μm and (<b>d</b>) 150 μm.</p>
Full article ">Figure 2
<p>Composition and crystallization analysis of films of different thicknesses. (<b>a</b>) XRD image, (<b>b</b>) FTIR image, (<b>c</b>) DSC image, (<b>d</b>) schematic diagram of crystallization of films of different thicknesses.</p>
Full article ">Figure 3
<p>(<b>a</b>,<b>b</b>) d<sub>33</sub> analysis of films of different thicknesses and (<b>c</b>) contact angle images.</p>
Full article ">Figure 4
<p>SEM images of different temperature: (<b>a</b>) 160 °C, (<b>b</b>) 180 °C.</p>
Full article ">Figure 5
<p>Composition and crystallization analysis of films of different temperature. (<b>a</b>) XRD image, (<b>b</b>) FTIR image, (<b>c</b>) DSC image (the sample data for the heat treatment temperature of 200 °C here is the same as above), (<b>d</b>) schematic diagram of crystallization of films of different temperature.</p>
Full article ">Figure 6
<p>(<b>a</b>,<b>b</b>) d<sub>33</sub> analysis of films of different annealing temperatures and (<b>c</b>) contact angle images (the sample data for the heat treatment temperature of 200 °C here are the same as above).</p>
Full article ">Figure 7
<p>(<b>a</b>) FTIR image and (<b>b</b>) DSC image of a 100 μm film obtained by the muffle furnace, (<b>c</b>) melting point between the upper and lower surfaces of a 100 μm film obtained by heating table treatment, KPFM images of (<b>d</b>) 100 μm film obtained by the muffle furnace, (<b>e</b>) the worst-performing sample made from a heating table and (<b>f</b>) the best-performing sample made from a heating table; (<b>g</b>) schematic diagram of crystallization of films obtained from muffle furnace and heating table.</p>
Full article ">
14 pages, 25634 KiB  
Article
Effect of Extreme Environments on Adhesive Joint Performance
by Martin Kadlec, Bohuslav Cabrnoch and Robin Hron
J. Compos. Sci. 2024, 8(12), 511; https://doi.org/10.3390/jcs8120511 - 6 Dec 2024
Viewed by 346
Abstract
The presented research on adhesives was conducted with the aim of supporting the design of composite repairs for composite aircraft structures that can withstand specific environmental conditions. Double-sided strap joint specimens of epoxy-based CFRP adherents and straps were bonded by two types of [...] Read more.
The presented research on adhesives was conducted with the aim of supporting the design of composite repairs for composite aircraft structures that can withstand specific environmental conditions. Double-sided strap joint specimens of epoxy-based CFRP adherents and straps were bonded by two types of adhesives. Room-temperature curing epoxy adhesives EC-9323 and EA-9395 were used for bonding. The specimens’ shear strength and failure modes were evaluated under four different environmental conditions from −72 °C up to 70 °C unconditioned and at 70 °C after humidity conditioning. The results show that EC-9323 performed excellently at room temperature, but very poorly at elevated temperatures after hot–wet conditioning. Adhesive EA-9395 performed consistently well across all tested conditions. The failure mode analysis explained the performance trends and the effect of the environment on the fractured surface. This study will support proper repair design and verification of numerical simulations. The novelty of this article lies in its combined analysis of multiple environmental factors, providing a more realistic assessment of joint performance. Full article
(This article belongs to the Section Polymer Composites)
Show Figures

Figure 1

Figure 1
<p>Double-sided strap joint specimen geometry.</p>
Full article ">Figure 2
<p>Detail of double-sided strap joint bonded by (<b>a</b>) EC-9323 and (<b>b</b>) EA-9395.</p>
Full article ">Figure 3
<p>Measured adhesive thickness: (<b>a</b>) average values were 138 μm and 275 μm for EC-9323 and EA-9395, respectively; (<b>b</b>) details of adhesive layer.</p>
Full article ">Figure 4
<p>Shear strength results for (<b>a</b>) EC-9323 and (<b>b</b>) EA-9395.</p>
Full article ">Figure 5
<p>The typical failure mechanism for double-sided strap joints. One of the laps remains intact as the opposite lap initiates the failure.</p>
Full article ">Figure 6
<p>Observed failure modes: (<b>a</b>) schematic diagram; (<b>b</b>) actual fracture surface.</p>
Full article ">Figure 7
<p>Observed failure modes: (<b>a</b>) fracture surface of delamination (interlaminar failure) region was dominated by shear cusps (white) in between fibre tracks (black); (<b>b</b>) fracture surface of fibre tear (intralaminar failure) region was dominated by fibres and fibre tracks with less resin/adhesive deformation.</p>
Full article ">Figure 8
<p>Observed failure mode transition: (<b>a</b>) from debonding to fibre tear; (<b>b</b>) from cohesive failure to fibre tear; (<b>c</b>) from fibre tear to delamination. Propagation from left to right.</p>
Full article ">Figure 9
<p>Failure mode analysis of EC-9323 at various test temperatures: (<b>a</b>) −72 °C; (<b>b</b>) 21 °C; (<b>c</b>) 70 °C; and (<b>d</b>) 70 °C after wet conditioning. Initiation occurred on top side of imaged surfaces.</p>
Full article ">Figure 10
<p>Failure mode analysis of EA-9395 at various test temperatures: (<b>a</b>) −72 °C; (<b>b</b>) 21 °C; (<b>c</b>) 70 °C; and (<b>d</b>) 70 °C after wet conditioning. Initiation occurred on top side of imaged surfaces.</p>
Full article ">Figure 11
<p>Differences in fracture surfaces at low and high temperatures for delamination and fibre tear: (<b>a</b>,<b>c</b>) relatively smooth surface at −72 °C, and (<b>b</b>,<b>d</b>) significant fibre pull-out at 70 °C. Propagation from left to right.</p>
Full article ">Figure 12
<p>Failure mode analysis of EC-9323 adhesive joints. The significant impact of adhesive failure on shear strength is apparent.</p>
Full article ">Figure 13
<p>Failure mode analysis of EA-9395 adhesive joints. Wet environment degradation caused an increase in the adhesive failure ratio.</p>
Full article ">Figure 14
<p>Delamination failure ratio relationship with shear strength. Linear increase in strength with delamination ratio observed for both adhesives.</p>
Full article ">
17 pages, 9905 KiB  
Article
The Study of the Three-Parameter Normal Distribution Characteristics of the Pore Structure in C80 High-Performance Self-Compacting Concrete (HPSCC)
by Lixin Bao, Guihong Xu, Hui Li, Chunhong Xin, Hejun Li, Mingwei He and Ciqi Liu
J. Compos. Sci. 2024, 8(12), 510; https://doi.org/10.3390/jcs8120510 - 5 Dec 2024
Viewed by 533
Abstract
To investigate the distribution characteristics of the micropore structure in high-performance self-compacting concrete (C80), high-resolution X-ray computed tomography, AVIZO software (version 2024.1), and scanning electron microscopy were employed to observe and analyze the internal pore structure of C80 self-compacting concrete specimens. The main [...] Read more.
To investigate the distribution characteristics of the micropore structure in high-performance self-compacting concrete (C80), high-resolution X-ray computed tomography, AVIZO software (version 2024.1), and scanning electron microscopy were employed to observe and analyze the internal pore structure of C80 self-compacting concrete specimens. The main conclusions are as follows: There is a large number of pore structures within the carbonate rock-based high-performance self-compacting concrete. At a testing precision range of 10 μm, the micropores exhibit a circular feature with good overall circularity. Observations through SEM, scanning electron microscopy, reveal that there are micro-cracks or interconnected crack structures within the high-performance concrete, with widths ranging from 0.5 to 2 μm, and the sample contains tiny voids of 3 to 10 μm. A statistical analysis of the micropores within the carbonate rock-based self-compacting concrete indicates that the pore diameter follows a three-parameter normal distribution. Due to the limitations of experimental observation and precision, the experimental statistical results show a positively skewed (high peak and left-skewed) phenomenon. This paper proposes a “correction of skewed peak” method for the analysis and discussion of the calculation of the “third parameter C” in the statistical results. The results show that the method proposed in this paper can quickly, objectively, and optimally determine the third parameter, compensating for the missing data not accounted for below 10 μm and the limitations of the finite number of experimental samples, providing a reference for examining the distribution of pores within concrete. Full article
(This article belongs to the Section Composites Applications)
Show Figures

Figure 1

Figure 1
<p>Cement particle size distribution and particle size cumulative distribution diagram.</p>
Full article ">Figure 2
<p>Machine-made sand scored screen allowance and cumulative screen allowance.</p>
Full article ">Figure 3
<p>S95 Slag powder particle size distribution and particle size cumulative distribution diagram.</p>
Full article ">Figure 4
<p>Silica fume particle size distribution and particle size cumulative distribution diagram.</p>
Full article ">Figure 5
<p>Microsphere particle size distribution and particle size cumulative distribution diagram.</p>
Full article ">Figure 6
<p>Expansion agent particle size distribution and cumulative particle size distribution diagram.</p>
Full article ">Figure 7
<p>HPSCC experimental samples’ preparation process. (<b>a</b>) Expansion plate test: used to measure the fluidity of concrete paste. (<b>b</b>) J-ring test: used to test the ability of concrete slurry to move through a narrow space. (<b>c</b>) V-type funnel test: used to test the stickiness and anti-segregation of concrete slurry. (<b>d</b>) Mixing the concrete. (<b>e</b>) Sample casting. (<b>f</b>) Completed specimens.</p>
Full article ">Figure 7 Cont.
<p>HPSCC experimental samples’ preparation process. (<b>a</b>) Expansion plate test: used to measure the fluidity of concrete paste. (<b>b</b>) J-ring test: used to test the ability of concrete slurry to move through a narrow space. (<b>c</b>) V-type funnel test: used to test the stickiness and anti-segregation of concrete slurry. (<b>d</b>) Mixing the concrete. (<b>e</b>) Sample casting. (<b>f</b>) Completed specimens.</p>
Full article ">Figure 8
<p>Three-dimensional image of the reconstructed sample using VG Studio MAX.</p>
Full article ">Figure 9
<p>A circularity distribution chart of the pores.</p>
Full article ">Figure 10
<p>The micropores(<b>a</b>–<b>f</b>) were observed along the Z-axis (side view).</p>
Full article ">Figure 11
<p>HPSCC SEM observation results. (<b>a</b>) Magnification of point A by 5 × 10<sup>4</sup> times. (<b>b</b>) Magnification of point B by 1 × 10<sup>4</sup> times. (<b>c</b>) Magnification of point C by 2 × 10<sup>4</sup> times. (<b>d</b>) Magnification of point D by 1 × 10<sup>4</sup> times.</p>
Full article ">Figure 12
<p>Frequency distribution of pore size in C80 HPSCC.</p>
Full article ">Figure 13
<p>Fitted curve of pore size frequency distribution for C80 HPSCC.</p>
Full article ">Figure 14
<p>Schematic diagram of the determination method for <math display="inline"><semantics> <mrow> <msub> <mi>x</mi> <mrow> <mi>most</mi> </mrow> </msub> <mo> </mo> <mi>and</mi> <mo> </mo> <msub> <mi>x</mi> <mrow> <mi>max</mi> </mrow> </msub> </mrow> </semantics></math>.</p>
Full article ">Figure 15
<p>Corrected three-parameter log-normal distribution of micropores.</p>
Full article ">
17 pages, 5157 KiB  
Article
Iron-Doped Biochar from Hospital Sludge for Efficient Arsenic Removal from Groundwater
by Nhat-Thien Nguyen, Sy-Yuan Kang, Chang-Tang Chang and Gui-Bing Hong
J. Compos. Sci. 2024, 8(12), 509; https://doi.org/10.3390/jcs8120509 - 5 Dec 2024
Viewed by 383
Abstract
Arsenic contamination in groundwater poses serious health risks, as exemplified by the Blackfoot disease epidemic in Taiwan, which was caused by prolonged arsenic exposure. This study investigates the use of biochar derived from the wastewater treatment sludge of the Far Eastern Memorial Hospital [...] Read more.
Arsenic contamination in groundwater poses serious health risks, as exemplified by the Blackfoot disease epidemic in Taiwan, which was caused by prolonged arsenic exposure. This study investigates the use of biochar derived from the wastewater treatment sludge of the Far Eastern Memorial Hospital (New Taipei City, Taiwan) as an efficient adsorbent for arsenic removal. A novel iron-doped sludge biochar (Fe-SBC) was developed to enhance arsenic adsorption efficiency, facilitate adsorbent recovery, and reduce operational costs. The adsorption mechanism of arsenic on Fe-SBC, modified with iron hydroxide complexes, was examined through Density Functional Theory (DFT) simulations. The results demonstrate a high arsenic removal efficiency of approximately 90% using continuous adsorption systems. The DFT calculations revealed strong chemical interactions between arsenic and the biochar, evidenced by high adsorption energy (−156.8 kJ mol−1) and a short bond distance (1.48 Å), correlating with the high adsorption performance observed experimentally. Additionally, arsenic byproducts desorbed from the adsorbent were repurposed into antibacterial agents and pigments. Four distinct pigment colors—green, blue, gray, and orange—were produced through different preparation methods, with the antibacterial agents showing effective antimicrobial properties. This study highlights the potential of Fe-SBC for sustainable arsenic remediation and resource recovery. Full article
(This article belongs to the Section Composites Applications)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>The effect of different materials on arsenic adsorption [<a href="#B4-jcs-08-00509" class="html-bibr">4</a>,<a href="#B5-jcs-08-00509" class="html-bibr">5</a>,<a href="#B6-jcs-08-00509" class="html-bibr">6</a>,<a href="#B7-jcs-08-00509" class="html-bibr">7</a>,<a href="#B8-jcs-08-00509" class="html-bibr">8</a>,<a href="#B9-jcs-08-00509" class="html-bibr">9</a>,<a href="#B10-jcs-08-00509" class="html-bibr">10</a>,<a href="#B11-jcs-08-00509" class="html-bibr">11</a>,<a href="#B12-jcs-08-00509" class="html-bibr">12</a>,<a href="#B13-jcs-08-00509" class="html-bibr">13</a>,<a href="#B14-jcs-08-00509" class="html-bibr">14</a>,<a href="#B15-jcs-08-00509" class="html-bibr">15</a>,<a href="#B16-jcs-08-00509" class="html-bibr">16</a>,<a href="#B17-jcs-08-00509" class="html-bibr">17</a>,<a href="#B18-jcs-08-00509" class="html-bibr">18</a>,<a href="#B19-jcs-08-00509" class="html-bibr">19</a>,<a href="#B20-jcs-08-00509" class="html-bibr">20</a>,<a href="#B21-jcs-08-00509" class="html-bibr">21</a>,<a href="#B22-jcs-08-00509" class="html-bibr">22</a>,<a href="#B23-jcs-08-00509" class="html-bibr">23</a>,<a href="#B24-jcs-08-00509" class="html-bibr">24</a>,<a href="#B25-jcs-08-00509" class="html-bibr">25</a>,<a href="#B26-jcs-08-00509" class="html-bibr">26</a>,<a href="#B27-jcs-08-00509" class="html-bibr">27</a>,<a href="#B28-jcs-08-00509" class="html-bibr">28</a>].</p>
Full article ">Figure 2
<p>The mechanism of arsenic adsorption on sludge biochar and a metal oxide complex schematic diagram.</p>
Full article ">Figure 3
<p>Characterization of materials: (<b>a</b>) SEM of 8% Fe-SBC, (<b>b</b>) XRD of materials, (<b>c</b>) XPS of 8% Fe-SBC, and (<b>d</b>) XPS of the As3d state of arsenic present in 8% Fe-SBC.</p>
Full article ">Figure 4
<p>Effect of different conditions on the adsorption performance: (<b>a</b>) different Fe content, (<b>b</b>) different pH levels, (<b>c</b>) different pH<sub>pzc</sub> levels, and (<b>d</b>) different initial concentrations.</p>
Full article ">Figure 5
<p>Continuous adsorption test results: (<b>a</b>) 6% Mn-SBC [<a href="#B51-jcs-08-00509" class="html-bibr">51</a>], (<b>b</b>) 10% Ni-SBC [<a href="#B51-jcs-08-00509" class="html-bibr">51</a>], (<b>c</b>) 8% Fe-SBC, and (<b>d</b>) saturation time.</p>
Full article ">Figure 6
<p>The schematic diagram of (<b>a</b>) arsenic adsorption and (<b>b</b>) desorption on 8% Fe-SBC.</p>
Full article ">Figure 7
<p>The uptake of arsenic by 8% Fe-SBC in consecutive regeneration cycles.</p>
Full article ">Figure 8
<p>The potential As(III) adsorption configurations on Fe-SBC: (<b>a</b>) SBC, (<b>b</b>) Fe-SBC, (<b>c</b>) As<sub>1</sub>-O<sub>1</sub>-Fe-SBC, (<b>d</b>) As<sub>1</sub>-As<sub>2</sub>-O<sub>1</sub>-Fe-SBC, (<b>e</b>) As<sub>1</sub>-As<sub>2</sub>-O<sub>2</sub>-Fe-SBC, and (<b>f</b>) As<sub>1</sub>-As<sub>2</sub>-O<sub>1</sub>-O<sub>2</sub>-Fe-SBC.</p>
Full article ">Figure 9
<p>The inhibition zone tests for pure water (Ct) and commercial ampicillin (Amp) with arsenic-containing green (S1) and blue (S2) antibacterial agents for tested Staphylococcus aureus (SA) and <span class="html-italic">Escherichia coli</span> (<span class="html-italic">E. coli</span>).</p>
Full article ">Figure 10
<p>Different arsenic-containing pigments: (<b>a</b>) S-1, (<b>b</b>) S-2, (<b>c</b>) S-3, and (<b>d</b>) S-4.</p>
Full article ">Figure 11
<p>SEM micrograph of (<b>a</b>) S-1, (<b>b</b>) S-2, (<b>c</b>) S-3, and (<b>d</b>) S-4.</p>
Full article ">
12 pages, 6249 KiB  
Article
Microhardness and Compressive Strength of Bulk Fill Glass Hybrid Material and Other Direct Restorative Materials
by Ahmed J. Abuzinadah, Yasser M. A. Merdad, Reem S. Aldharrab, Wejdan A. Almutairi, Hanin E. Yeslam and Fatin A. Hasanain
J. Compos. Sci. 2024, 8(12), 508; https://doi.org/10.3390/jcs8120508 - 5 Dec 2024
Viewed by 439
Abstract
Background: This study aims to compare the compressive strength and microhardness of four tooth-colored restorative materials: bulk fill glass hybrid (GH), resin-modified glass ionomer (RMGIC), conventional glass ionomer (CGIC), and resin-based composite (RBC). Methods: Stainless steel molds were used to prepare 20 specimens [...] Read more.
Background: This study aims to compare the compressive strength and microhardness of four tooth-colored restorative materials: bulk fill glass hybrid (GH), resin-modified glass ionomer (RMGIC), conventional glass ionomer (CGIC), and resin-based composite (RBC). Methods: Stainless steel molds were used to prepare 20 specimens for each material. Half of the specimens were subjected to 10,000 thermal cycles; the materials were subjected to compressive strength and microhardness tests. Mean values were statistically compared using a one-way ANOVA Test and Bonferroni pairwise comparisons. Results: GH (147.03 ± 20.19 MPa) had lower compressive strength than RBC (264.82 ± 30.95 MPa) but showed no significant difference with CGIC (130.19 ± 30.38 MPa) and RMGIC (183.52 ± 18.45 MPa). RMGIC’s compressive strength also significantly fell short of RBC (p < 0.05), but it significantly increased after thermocycling (160.14 to 183.52 MPa). As for microhardness, no significant difference was found between the groups. Thermocycling significantly increased the microhardness of CGIC (from 24.27 to 31.8 ± 2.66). Conclusion: Resin-based materials outperformed the other materials. Glass hybrid restorative material performed as well as resin-modified glass ionomer regarding compressive strength; however, further studies are necessary before considering glass hybrids for use as a permanent restoration. Full article
Show Figures

Figure 1

Figure 1
<p>Specimen fabrication mold to produce specimens measuring 6 mm in thickness and 4 mm in diameter.</p>
Full article ">Figure 2
<p>Study design detailing group assignment of specimens.</p>
Full article ">Figure 3
<p>Compressive strength testing of specimens in the universal testing machine.</p>
Full article ">Figure 4
<p>Microhardness testing of the specimens.</p>
Full article ">Figure 5
<p>Compressive strength measurements in MPa of tested restorative materials, comparing their performance before and after aging by thermocycling. Bonferroni post hoc comparisons group results are reported with significance level set at <span class="html-italic">p</span> &lt; 0.05; different uppercase letters in mean column indicate significant differences. * represents significant difference after thermocycling at <span class="html-italic">p</span> &lt; 0.05.</p>
Full article ">Figure 6
<p>Microhardness measurements (Vicker’s) of the tested restorative materials, comparing their performance before and after aging. * represents a significant difference after thermocycling at <span class="html-italic">p</span> &lt; 0.05 using <span class="html-italic">t</span>-test.</p>
Full article ">
19 pages, 3280 KiB  
Article
Environmental Implications of Using Waste Glass as Aggregate in Concrete
by Robert Lopez and Charbel El-Fata
J. Compos. Sci. 2024, 8(12), 507; https://doi.org/10.3390/jcs8120507 - 5 Dec 2024
Viewed by 389
Abstract
Approximately 10 billion tons of fine and coarse aggregate are manufactured worldwide annually, solely to be used as concrete for constructed structures. With approximately 80% of conventional concrete comprising sand and stone, activities in their extraction and relocation harm the natural environment. Manufacturing [...] Read more.
Approximately 10 billion tons of fine and coarse aggregate are manufactured worldwide annually, solely to be used as concrete for constructed structures. With approximately 80% of conventional concrete comprising sand and stone, activities in their extraction and relocation harm the natural environment. Manufacturing concrete causes substantial amounts of ecological damage and energy consumption. The replacement of natural aggregate with waste glass, therefore, theoretically removes this environmental damage and energy consumption. The research presented in this paper tested the theory that waste glass concrete aggregate represents a potential solution to curtail the adverse impact of concrete on the natural environment. Testing this theory entailed the review of the existing literature and analyses of the findings from a survey of 107 organizations situated in five countries within the concrete manufacturing supply chain. The findings of this research demonstrate that environmental implications exist with the use of both natural aggregate and glass waste. Significant CO2 reductions can be achieved by using glass as aggregate in concrete. This is found to be up to 60% and 65% for fine and coarse aggregates, respectively. In addition, using glass in its aggregate can potentially improve the strength of concrete. With a concrete grade of 20, an improved compressive strength test of up to 10 could be possible. Similarly, with concrete grades of 25 and 30, an improved tensile strength test of up to 9 could be possible. This depends on differences in the percentage of natural aggregate that has been substituted with glass. Full article
(This article belongs to the Special Issue Novel Cement and Concrete Materials)
Show Figures

Figure 1

Figure 1
<p>Survey respondent locations.</p>
Full article ">Figure 2
<p>Scree and Cut Off Point plot with factor numbers and eigenvalues.</p>
Full article ">Figure 3
<p>Production of fine aggregate and respondent numbers bar chart.</p>
Full article ">Figure 4
<p>Aggregate sources and respondent numbers bar chart.</p>
Full article ">Figure 5
<p>Production of coarse aggregate and respondent numbers bar chart.</p>
Full article ">Figure 6
<p>Loads of haulage (tons) and respondent numbers bar chart.</p>
Full article ">Figure 7
<p>Aggregate distribution (%) and respondent numbers bar chart.</p>
Full article ">Figure 8
<p>Distances of haulage (km) and respondent numbers bar chart.</p>
Full article ">
27 pages, 3521 KiB  
Review
Exploring the Impact of Nanoclay on Epoxy Nanocomposites: A Comprehensive Review
by Daksh Shelly, Varun Singhal, Surinder Singh, Tarun Nanda, Rajeev Mehta, Seul-Yi Lee and Soo-Jin Park
J. Compos. Sci. 2024, 8(12), 506; https://doi.org/10.3390/jcs8120506 - 2 Dec 2024
Viewed by 556
Abstract
This review provides a comprehensive exploration of the current research landscape surrounding nanoclay-reinforced epoxy composites. A primary challenge in developing these nanocomposites is the hydrophilic nature of pristine clay, which hinders its dispersion within the epoxy matrix. To address this issue, organic modifiers [...] Read more.
This review provides a comprehensive exploration of the current research landscape surrounding nanoclay-reinforced epoxy composites. A primary challenge in developing these nanocomposites is the hydrophilic nature of pristine clay, which hinders its dispersion within the epoxy matrix. To address this issue, organic modifiers are frequently employed to enhance clay compatibility and facilitate effective incorporation into the nanocomposite structure. The unique properties of nanoclay make it a particularly attractive reinforcement material. The performance of nanoclay/epoxy nanocomposites is largely determined by their morphology, which is influenced by various factors including processing methods, clay types, modifiers, and curing agents. A thorough understanding and control of these parameters are essential for optimizing nanocomposite performance. These advanced materials find extensive applications across multiple industries, including aerospace, defense, anti-corrosive coatings, automotive, and packaging. This review offers an in-depth analysis of the processing techniques, mechanical properties, barrier capabilities, and thermal characteristics of nanoclay-reinforced epoxy nanocomposites. Additionally, it explores their diverse industrial applications, providing a holistic view of their potential and current use. By examining the multifaceted landscape of epoxy/clay nanocomposites, this review illuminates the intricate relationships between fabrication methods, resulting properties, and potential industrial applications. It serves as a comprehensive resource for researchers and practitioners seeking to advance the development and application of these innovative materials. Full article
(This article belongs to the Section Nanocomposites)
Show Figures

Figure 1

Figure 1
<p>(<b>a</b>) Comparison of conventional composites and polymer nanocomposites, (<b>b</b>) schematic representation of thermoset polymer, (<b>c</b>) schematic representation of thermoplastic polymer, and (<b>d</b>) surface-to-volume ratios of frequently used particle reinforcements and shapes.</p>
Full article ">Figure 2
<p>A graphic representation of the elements of the 3-D phase transition between the fiber and matrix [<a href="#B30-jcs-08-00506" class="html-bibr">30</a>].</p>
Full article ">Figure 3
<p>(<b>a</b>) Structure of sodium montmorillonite [<a href="#B64-jcs-08-00506" class="html-bibr">64</a>] and (<b>b</b>) organic modification of nanoclay [<a href="#B2-jcs-08-00506" class="html-bibr">2</a>].</p>
Full article ">Figure 4
<p>Types of nanoclay dispersion in polymers and their associated TEM, XRD, and schematic micrographs (<b>a</b>–<b>c</b>) phase-separated/immiscible, (<b>d</b>–<b>f</b>) intercalated, and (<b>g</b>–<b>i</b>) exfoliated morphologies [<a href="#B64-jcs-08-00506" class="html-bibr">64</a>].</p>
Full article ">Figure 5
<p>(<b>a</b>) Classification of processing of clay–polymer nanocomposites, (<b>b</b>) melt intercalation synthesis of clay–polymer composites, (<b>c</b>) in situ template synthesis of clay–polymer composites, and (<b>d</b>) in situ polymerization synthesis of clay–polymer composites [<a href="#B83-jcs-08-00506" class="html-bibr">83</a>].</p>
Full article ">Figure 6
<p>(<b>a</b>) Diagram depicts the intercalated/exfoliation procedure, illustrating the forces exerted on a pair of nanoclay platelets, modified nanoclay, epoxy intercalated state, and the forces acting on two-particle tactoids, (<b>b</b>) figure illustrating the correlation between the energy of ionic bonding and the positioning of the clay platelets within the tactoids [<a href="#B103-jcs-08-00506" class="html-bibr">103</a>].</p>
Full article ">Figure 7
<p>(<b>a</b>,<b>b</b>) XRD patterns of pristine epoxy, nanoclay, and their nanocomposites [<a href="#B117-jcs-08-00506" class="html-bibr">117</a>,<a href="#B118-jcs-08-00506" class="html-bibr">118</a>]; (<b>c</b>) TEM micrographs of 3 wt.% nanoclay reinforced epoxy nanocomposite [<a href="#B102-jcs-08-00506" class="html-bibr">102</a>]; and (<b>d</b>) TEM micrographs of epoxy nanocomposite containing 5 wt.% and 10 wt.% nanoclay [<a href="#B116-jcs-08-00506" class="html-bibr">116</a>].</p>
Full article ">Figure 8
<p>(<b>a</b>,<b>b</b>) Influence of modified clay loading on tensile and impact strength at ambient and at 77 K temperature [<a href="#B123-jcs-08-00506" class="html-bibr">123</a>], (<b>c</b>,<b>d</b>) TGA curves of epoxy-containing various loading of hydrated/dehydrated sepiolite [<a href="#B138-jcs-08-00506" class="html-bibr">138</a>], (<b>e</b>) illustration of a zigzag pathway of a liquid/gas through clay–epoxy nanocomposites.</p>
Full article ">
18 pages, 3612 KiB  
Article
The Effect of Adhesive Quantity on Adhesion Quality and Mechanical Characteristics of Woven Kevlar Fabric-Reinforced Laminated Structures
by Feyi Adekunle and Abdel-Fattah M. Seyam
J. Compos. Sci. 2024, 8(12), 505; https://doi.org/10.3390/jcs8120505 - 2 Dec 2024
Viewed by 425
Abstract
This study investigated the adhesion and mechanical properties of woven fabric-reinforced laminates (FRLs) made with four distinct Kevlar fabrics of varying areal densities (36 g/m2, 60 g/m2, 140 g/m2, and 170 g/m2) under different fabric-to-adhesive [...] Read more.
This study investigated the adhesion and mechanical properties of woven fabric-reinforced laminates (FRLs) made with four distinct Kevlar fabrics of varying areal densities (36 g/m2, 60 g/m2, 140 g/m2, and 170 g/m2) under different fabric-to-adhesive weight ratios (1:0.5, 1:1, and 1:1.5) in both the warp and weft directions. A novel aspect of this research lies in our systematic study of the effect of adhesive quantity on FRLs, a topic that has received limited attention despite its critical role in laminate performance. Additionally, the application of a newly developed yarn pullout test alongside the standard T-peel test provides unique insights into the interfacial behavior of laminates. The results show that in lower areal density fabrics (36 g/m2 and 60 g/m2), adhesive quantity minimally affects the pullout and T-peel forces or tear strength, indicating that structural integrity can be maintained with reduced adhesive application. In contrast, higher areal density fabrics (140 g/m2 and 170 g/m2) benefit from an increased adhesive ratio, with a transition from 1:0.5 to 1:1 significantly enhancing the pullout resistance, while further increases to 1:1.5 yielded diminishing returns. Tensile strength remained consistent across all samples, highlighting that it is largely dictated by the inherent properties of the fibers and fabric structure rather than the adhesive. This study concludes that a 1:1 fiber-to-adhesive ratio offers an optimal balance of adhesion quality and mechanical performance for FRLs. By addressing the understudied impact of adhesive quantity on FRLs and introducing the yarn pullout test, this research provides novel and practical guidelines for optimizing FRLs in applications demanding high structural integrity and adaptability under challenging conditions. Full article
(This article belongs to the Special Issue Mechanical Properties of Composite Materials and Joints)
Show Figures

Figure 1

Figure 1
<p>Laminate structure.</p>
Full article ">Figure 2
<p>Film layer tearing during the T-peel test, affecting the adhesive strength measurement [<a href="#B7-jcs-08-00505" class="html-bibr">7</a>].</p>
Full article ">Figure 3
<p>Yarn pullout in laminate test results in warp and weft directions for various fabric areal densities: (<b>a</b>) 36 g/m<sup>2</sup> (<b>b</b>) 60 g/m<sup>2</sup> (<b>c</b>) 140 g/m<sup>2</sup>, and (<b>d</b>) 170 g/m<sup>2</sup>.</p>
Full article ">Figure 3 Cont.
<p>Yarn pullout in laminate test results in warp and weft directions for various fabric areal densities: (<b>a</b>) 36 g/m<sup>2</sup> (<b>b</b>) 60 g/m<sup>2</sup> (<b>c</b>) 140 g/m<sup>2</sup>, and (<b>d</b>) 170 g/m<sup>2</sup>.</p>
Full article ">Figure 4
<p>Microscopic images of 170 g/m<sup>2</sup> FRLs post yarn pullout test in (×20): (<b>a</b>) 1:0.5, (<b>b</b>) 1:1, (<b>c</b>) 1:1.5 and in (×40): (<b>d</b>) 1:0.5, (<b>e</b>) 1:1, and (<b>f</b>) 1:1.5.</p>
Full article ">Figure 4 Cont.
<p>Microscopic images of 170 g/m<sup>2</sup> FRLs post yarn pullout test in (×20): (<b>a</b>) 1:0.5, (<b>b</b>) 1:1, (<b>c</b>) 1:1.5 and in (×40): (<b>d</b>) 1:0.5, (<b>e</b>) 1:1, and (<b>f</b>) 1:1.5.</p>
Full article ">Figure 5
<p>Tear test results in the warp and weft directions for various fabric areal densities: (<b>a</b>) 36 g/m<sup>2</sup> (<b>b</b>) 60 g/m<sup>2</sup> (<b>c</b>) 140 g/m<sup>2</sup>, and (<b>d</b>) 170 g/m<sup>2</sup>.</p>
Full article ">Figure 5 Cont.
<p>Tear test results in the warp and weft directions for various fabric areal densities: (<b>a</b>) 36 g/m<sup>2</sup> (<b>b</b>) 60 g/m<sup>2</sup> (<b>c</b>) 140 g/m<sup>2</sup>, and (<b>d</b>) 170 g/m<sup>2</sup>.</p>
Full article ">Figure 6
<p>Tensile test results in the warp and weft directions for various fabric areal densities: (<b>a</b>) 36 g/m<sup>2</sup>, (<b>b</b>) 60 g/m<sup>2</sup>, (<b>c</b>) 140 g/m<sup>2</sup>, and (<b>d</b>) 140 g/m<sup>2</sup>.</p>
Full article ">Figure 6 Cont.
<p>Tensile test results in the warp and weft directions for various fabric areal densities: (<b>a</b>) 36 g/m<sup>2</sup>, (<b>b</b>) 60 g/m<sup>2</sup>, (<b>c</b>) 140 g/m<sup>2</sup>, and (<b>d</b>) 140 g/m<sup>2</sup>.</p>
Full article ">
25 pages, 18165 KiB  
Article
End-to-End Simulation of Linerless Composite Pressure Vessels Using 3D Continuum Damage Models
by Paulo Teixeira Gonçalves, Albertino Arteiro and Nuno Rocha
J. Compos. Sci. 2024, 8(12), 504; https://doi.org/10.3390/jcs8120504 - 2 Dec 2024
Viewed by 405
Abstract
Linerless composite pressure vessels, or type V pressure vessels, are gaining increased interest in the transportation industry because they offer improved storage volume and dry weight, especially for low-pressure cryogenic storage. Nevertheless, the design and manufacturing of this type of pressure vessel bring [...] Read more.
Linerless composite pressure vessels, or type V pressure vessels, are gaining increased interest in the transportation industry because they offer improved storage volume and dry weight, especially for low-pressure cryogenic storage. Nevertheless, the design and manufacturing of this type of pressure vessel bring several challenges due to the inherent difficulties in the manufacturing process implementation, assembly, and related analysis of structural integrity due to the severe operating conditions at cryogenic temperatures that should be taken into consideration. In this work, a novel analysis procedure using a finite element model is developed to perform an end-to-end simulation of a linerless pressure vessel, including the relevant features associated with automated fiber placement manufacturing processes regarding thickness and tape profiles, followed by an analysis of the structural response under service conditions. The results show that residual stresses from manufacturing achieve values near 50% of the composite ply transverse strength, which reduces the effective ply transverse load carrying capacity for pressure loading. Transverse damage is triggered and propagated across the vessel thickness before fiber breakage, indicating potential failure by leakage, which was confirmed by hydrostatic tests in the physical prototype at 26 bar. The cryogenic condition analysis revealed that the thermal stresses trigger transverse damage before pressure loading, reducing the estimated leak pressure by 40%. These results highlight the importance of considering the residual stresses that arise from the manufacturing process and the thermal stresses generated during cooling to cryogenic conditions, demonstrating the relevance of the presented methodology for designing linerless cryogenic composite pressure vessels. Full article
(This article belongs to the Special Issue Feature Papers in Journal of Composites Science in 2024)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Elastic–plastic hardening curves: (<b>a</b>) transverse tension, (<b>b</b>) longitudinal and transverse shear, and (<b>c</b>) transverse compression.</p>
Full article ">Figure 2
<p>COPV reduced-scale prototype dimensions: (<b>a</b>) external dimensions and (<b>b</b>) dome profile.</p>
Full article ">Figure 3
<p>Discretization of the COPV section.</p>
Full article ">Figure 4
<p>Tape trajectory schematic over the vessel head.</p>
Full article ">Figure 5
<p>Geometric modeling of the COPV: (<b>a</b>) representative layers and (<b>b</b>) vessel assembly.</p>
Full article ">Figure 6
<p>Thickness profile of the COPV (ply thickness was scaled for clarity).</p>
Full article ">Figure 7
<p>Local fiber orientations of the COPV.</p>
Full article ">Figure 8
<p>Boundary conditions in the 1/8 COPV model.</p>
Full article ">Figure 9
<p>Pressure vessel prototype: (<b>a</b>) Complete vessel. (<b>b</b>) Vessel cross-section without the dome.</p>
Full article ">Figure 10
<p>End-to-end simulation steps.</p>
Full article ">Figure 11
<p>Curing residual stresses (MPa) of the internal shell after the complete curing process of the vessel: (<b>a</b>) longitudinal direction and (<b>b</b>) transverse direction.</p>
Full article ">Figure 12
<p>Curing residual stresses (MPa) evolution during the second curing stage: (<b>a</b>) at cure initiation, time 0; (<b>b</b>) at 120 °C; and (<b>c</b>) at cure process end (after cooling from curing temperature).</p>
Full article ">Figure 13
<p>Stress distributions at design pressure of 8.5 bar: (<b>a</b>) longitudinal stress <math display="inline"><semantics> <mrow> <msub> <mi>σ</mi> <mrow> <mn>11</mn> </mrow> </msub> </mrow> </semantics></math> (MPa); (<b>b</b>) transverse stress <math display="inline"><semantics> <mrow> <msub> <mi>σ</mi> <mrow> <mn>22</mn> </mrow> </msub> </mrow> </semantics></math> (MPa); (<b>c</b>) transverse damage variable.</p>
Full article ">Figure 14
<p>Failure criteria comparison: (<b>a</b>) without curing residual stresses being accounted and (<b>b</b>) with curing residual stresses being accounted.</p>
Full article ">Figure 15
<p>Transverse damage evolution with internal pressure at RT.</p>
Full article ">Figure 16
<p>Leaking after completion of burst test.</p>
Full article ">Figure 17
<p>Stress distributions after cooling down to −196 °C (no damage evolution): (<b>a</b>) transverse stress <math display="inline"><semantics> <mrow> <msub> <mi>σ</mi> <mrow> <mn>22</mn> </mrow> </msub> </mrow> </semantics></math> (MPa) and (<b>b</b>) transverse failure criteria.</p>
Full article ">Figure 18
<p>Stress distributions after cooling down to −196 °C (considering damage evolution). (<b>a</b>) Transverse stress <math display="inline"><semantics> <mrow> <msub> <mi>σ</mi> <mrow> <mn>22</mn> </mrow> </msub> </mrow> </semantics></math> (MPa) and (<b>b</b>) transverse damage variable.</p>
Full article ">Figure 19
<p>Stress distributions after cooling and loading to 8.5 bar: (<b>a</b>) transverse stress <math display="inline"><semantics> <mrow> <msub> <mi>σ</mi> <mrow> <mn>22</mn> </mrow> </msub> </mrow> </semantics></math> (MPa) and (<b>b</b>) transverse damage variable.</p>
Full article ">Figure 20
<p>Stress distributions after cooling and loading to 15 bar: (<b>a</b>) transverse stress <math display="inline"><semantics> <mrow> <msub> <mi>σ</mi> <mrow> <mn>22</mn> </mrow> </msub> </mrow> </semantics></math> (MPa) and (<b>b</b>) transverse damage variable.</p>
Full article ">
17 pages, 949 KiB  
Review
Polymer Concretes Based on Various Resins: Modern Research and Modeling of Mechanical Properties
by Aleksandr Palamarchuk, Pavel Yudaev and Evgeniy Chistyakov
J. Compos. Sci. 2024, 8(12), 503; https://doi.org/10.3390/jcs8120503 - 2 Dec 2024
Viewed by 482
Abstract
This review is devoted to experimental studies and modeling in the field of mechanical and physical properties of polymer concretes and polymer-modified concretes. The review analyzes studies carried out over the past two years. The paper examines the properties of polymer concretes based [...] Read more.
This review is devoted to experimental studies and modeling in the field of mechanical and physical properties of polymer concretes and polymer-modified concretes. The review analyzes studies carried out over the past two years. The paper examines the properties of polymer concretes based on various polymer resins and presents the advantages and disadvantages of various models developed to predict the mechanical properties of materials. Based on data in the literature, the most promising polymers for use in the field of road surface repair are polymer concretes with poly(meth)acrylic resins. It was found that the most adequate and productive models are the deep machine learning model—using several hidden layers that perform calculations based on input parameters—and the extreme gradient boosting model. In particular, the extreme gradient boosting model showed high R2 values in forecasting (in the range of 0.916–0.981) when predicting damping coefficient and ultimate compressive strength. In turn, among the additives to Portland cement concrete, the most promising are natural polymers, such as mammalian gelatin and cold fish gelatin, and superabsorbent polymers. These additives allow for an improvement in compressive strength of 200% or more. The review may be of interest to engineers specializing in building construction, materials scientists involved in the development and implementation of new materials into production, as well as researchers in the interdisciplinary fields of chemistry and technology. Full article
(This article belongs to the Special Issue Research on Sustainable Cement-Based Composites)
Show Figures

Figure 1

Figure 1
<p>Areas of application of composites.</p>
Full article ">Figure 2
<p>Chemical structure of polyhedral oligomeric silsesquioxane.</p>
Full article ">Figure 3
<p>Crack propagation when a load is applied to the interface of the sample at a rate of 0.1 kN/s until the polymer–concrete sample fails. White arrow means the interlayer crack in the sample developed from top to bottom.</p>
Full article ">Figure 4
<p>Compressive strength values for concrete samples with additives of various natural polymers.</p>
Full article ">
17 pages, 11855 KiB  
Article
Preparation and Corrosion Resistance of Superhydrophobic Composite Coatings on Shot-Peened AA 7075-T6 Aluminum Alloy
by Ke Zhan, Ruiqing Ding, Ziliang Liu, Qingchao Yang and Vincent Ji
J. Compos. Sci. 2024, 8(12), 502; https://doi.org/10.3390/jcs8120502 - 2 Dec 2024
Viewed by 440
Abstract
In order to further improve the corrosion resistance of 7075-T6 aluminum alloy after shot peening, corrosion-resistant superhydrophobic coatings (EP-HDTMS@SiO2) containing epoxy resin (EP), cetyltrimethoxysilane (HDTMS), and nano-silica (SiO2) were prepared by a simple spraying method on the surface of [...] Read more.
In order to further improve the corrosion resistance of 7075-T6 aluminum alloy after shot peening, corrosion-resistant superhydrophobic coatings (EP-HDTMS@SiO2) containing epoxy resin (EP), cetyltrimethoxysilane (HDTMS), and nano-silica (SiO2) were prepared by a simple spraying method on the surface of shot-peened AA 7075-T6 aluminum alloy. The effects of different EP/SiO2 mass ratios on the micro-morphology, surface wettability, and corrosion resistance of the superhydrophobic composite coatings were analyzed. Due to the combination of microstructure and the modification of low surface energy organics, the contact angle of EP-HDTMS@SiO2 coatings reached the superhydrophobic level (152.6°). The electrochemical tests showed that the corrosion current densities (Icorr) of the EP-HDTMS@SiO2 composite coatings were both significantly lower than those of the EP-HDTMS coatings and matrix aluminum alloys. The addition of SiO2 nanoparticles could improve the hydrophobicity and corrosion resistance of epoxy-based composite coatings. Due to the increase in surface roughness and epoxy resin, the shot-peened AA 7075-T6 alloy coating had high adhesion after the peel test. The prepared coatings also showed excellent corrosion resistance in the neutral salt spray test. This study provides a simple method for preparing stable superhydrophobic coatings on metal surfaces, which is expected to expand the application of 7075 aluminum alloy in harsh environments. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Processing to prepare superhydrophobic EP-HDTMS@SiO<sub>2</sub> coatings on shot-peened 7075-T6 aluminum alloy. (1. Mechanism of Superhydrophobic EP-HDTMS@SiO<sub>2</sub> Coating Formation. 2. Processing of Superhydrophobic EP-HDTMS@SiO2 Coating.).</p>
Full article ">Figure 2
<p>Low and high magnification SEM images of EP/SiO<sub>2</sub> composite coatings with different ratios, (<b>a<sub>1</sub></b>,<b>a<sub>2</sub></b>) no SiO<sub>2</sub> was added; (<b>b<sub>1</sub></b>,<b>b<sub>2</sub></b>) 3:1; (<b>c<sub>1</sub></b>,<b>c<sub>2</sub></b>) 3:2; (<b>d<sub>1</sub></b>,<b>d<sub>2</sub></b>) 1:1; (<b>e<sub>1</sub></b>,<b>e</b><sub>2</sub>) 3:4.</p>
Full article ">Figure 3
<p>(<b>a</b>,<b>b</b>) EDS without nanosized SiO<sub>2</sub> and EP/SiO<sub>2</sub> mass ratio of 3:2; (<b>c</b>) mapping with an EP/SiO<sub>2</sub> ratio of 3:2.</p>
Full article ">Figure 4
<p>EP-HDTMS@SiO<sub>2</sub> FT-IR spectroscopy of superhydrophobic coatings.</p>
Full article ">Figure 5
<p>EP-HDTMS@SiO<sub>2</sub> XPS of superhydrophobic coatings: (<b>a</b>) full spectrum; (<b>b</b>) C 1s; (<b>c</b>) O 1s; (<b>d</b>) Si 2p.</p>
Full article ">Figure 6
<p>WAC data of aluminum alloy, pretreated aluminum alloy, and coated surface with different contents of SiO<sub>2</sub> nanoparticles.</p>
Full article ">Figure 7
<p>Wettability of EP-HDTMS@SiO<sub>2</sub> superhydrophobic coating with 3:2 mass ratio of EP to SiO<sub>2</sub> on different liquids: (<b>a</b>) different pH; (<b>b</b>) different solutions.</p>
Full article ">Figure 8
<p>(<b>a</b>) Bode impedance plots with different EP/SiO<sub>2</sub> ratios; (<b>b</b>) phase diagram; (<b>c</b>) freq Z diagram; (<b>d</b>) circuit fitting diagram.</p>
Full article ">Figure 9
<p>Tafel curves for the coatings and substrate.</p>
Full article ">Figure 10
<p>(<b>a<sub>1</sub></b>,<b>b<sub>1</sub></b>,<b>c<sub>1</sub></b>) EP-HDTMS@SiO<sub>2</sub> self-cleaning comparison between superhydrophobic coating with 3:2 mass ratio of EP to SiO<sub>2</sub> and substrate (<b>a<sub>2</sub></b>,<b>b<sub>2</sub></b>,<b>c<sub>2</sub></b>), blue powder is CuSO<sub>4</sub>. (<b>a<sub>3</sub></b>,<b>b<sub>3</sub></b>,<b>c<sub>3</sub></b>) Self-cleaning theory diagram.</p>
Full article ">Figure 11
<p>(<b>a<sub>1</sub></b>,<b>a<sub>2</sub></b>) Tape peeling test. (<b>b<sub>1</sub></b>,<b>b<sub>2</sub></b>) Knife scraping test. (<b>c<sub>1</sub></b>) Shot peening SEM image. (<b>c<sub>2</sub></b>) Schematic of coating–substrate bonding.</p>
Full article ">Figure 12
<p>(<b>a</b>) Macroscopic morphologies of EP-HDTMS@SiO<sub>2</sub> superhydrophobic coating and substrate in different days under salt spray test. (<b>b</b>,<b>c</b>) EP-HDTMS@SiO<sub>2</sub> XRD before and after salt spray test between superhydrophobic coating and substrate. (<b>d</b>) Weight change of EP-HDTMS@SiO<sub>2</sub> superhydrophobic coating and substrate.</p>
Full article ">Figure 13
<p>(<b>a</b>) Schematic diagram of aluminum alloy pitting corrosion. (<b>b</b>) Schematic diagram of non-added nano-silica coating. (<b>c</b>) EP-HDTMS@SiO<sub>2</sub> coating corrosion resistance schematic diagram.</p>
Full article ">
10 pages, 1647 KiB  
Article
Application of Olivine Powder as a Filler for Silicone Pressure-Sensitive Adhesives
by Adrian Krzysztof Antosik
J. Compos. Sci. 2024, 8(12), 501; https://doi.org/10.3390/jcs8120501 - 2 Dec 2024
Viewed by 386
Abstract
In this work, new self-adhesive materials were obtained based on cross-linked silicone self-adhesives obtained by modifying the composition with the addition of a silicon filler, olivine. Silicone pressure-sensitive resin DOWSIL 7358 was used as a basis and modified with various amounts of olivine. [...] Read more.
In this work, new self-adhesive materials were obtained based on cross-linked silicone self-adhesives obtained by modifying the composition with the addition of a silicon filler, olivine. Silicone pressure-sensitive resin DOWSIL 7358 was used as a basis and modified with various amounts of olivine. New materials (self-adhesive tape samples) were characterized in terms of peel adhesion, tack, cohesion at room and elevated temperatures, SAFT test (shear adhesion failure temperature), pot life (storage stability), and shrinkage (dimensional stability). During the tests, an increase in thermal resistance (>225 °C) and a drastic reduction in shrinkage values (below 0.5%) were noted for all modified samples tested. All tests were performed in compliance with international standards, e.g., FINAT FTM 1, FINAT FTM 8, FINAT FTM 9, FINAT FTM 14, and GTF 6001. This allows us to conclude that the new material has significant application potential due to the good performance results. The results of adhesion and tack were in ranges accepted in the PSA industry, cohesion was kept at an unchanged level (above 72 h), and a great increase in the thermal resistance was observed (from 147 °C for pure resin to high above 225 °C for even the smallest additions of the olivine powder. Moreover, the shrinkage of prepared adhesive films was reduced significantly. In the available literature, there are no references to the modification of adhesives using powdered silicon minerals of natural origin, which is a novelty due to their higher bulk density compared to commercial powdered silicon fillers. Full article
Show Figures

Figure 1

Figure 1
<p>Scheme of preparation of one-sided self-adhesive tape.</p>
Full article ">Figure 2
<p>TGA curve of olivine.</p>
Full article ">Figure 3
<p>DSC curves of the cross-linking process of PSA films with various amounts of olivine content.</p>
Full article ">Figure 4
<p>Effect of olivine content on the peel adhesion and tack of silicone pressure-sensitive adhesive.</p>
Full article ">
16 pages, 7589 KiB  
Article
Effect of Hybrid Addition of Boron Nitride and Vanadium Carbide on Microstructure, Tribological, and Mechanical Properties of the AA6061 Al-Based Composites Fabricated by FSP
by Ahmad H. Milyani, Ahmed O. Mosleh and Essam B. Moustafa
J. Compos. Sci. 2024, 8(12), 500; https://doi.org/10.3390/jcs8120500 - 1 Dec 2024
Viewed by 644
Abstract
This work investigates the impact of friction stir processing (FSP) on the microstructure and mechanical characteristics of AA 6061 alloy and its composites, which are strengthened with boron nitride nanoparticles and vanadium carbide microparticles. Composite samples were created using different proportions of reinforcing [...] Read more.
This work investigates the impact of friction stir processing (FSP) on the microstructure and mechanical characteristics of AA 6061 alloy and its composites, which are strengthened with boron nitride nanoparticles and vanadium carbide microparticles. Composite samples were created using different proportions of reinforcing particles, including mono and hybrid composites. The efficacy of FSP as a technological method for enhancing the grain size of AA 6061 alloy and its composites has been proven. Adding reinforcing particles led to enhanced grain refinement, especially when using VC particles, which demonstrated greater efficacy than BN particles; thus, mono composite AA6061/VC shows the highest percentage reduction (94.29%) in grain size. Hybrid composites with a higher concentration of VC particles exhibited a more symmetrical microhardness profile. The microhardness of hybrid composites with a larger concentration of VC particles (40 vol.%BN + 60 vol.%VC) shows the most significant enhancement, with an increase of 51.61%. The Young’s and shear modulus of all composite samples processed by (FSP) had greater values than the wrought AA 6061 alloy. The investigated composite samples, especially 60% BN and 40% VC, enhanced the tribological properties of AA6061 and reduced the wear rate by about 52%. The observed characteristics may be due to BN and VC particles in the hybrid compost. This is because these particles effectively prevent grain elongation and inconsistent movement. This is because reinforcing particles can be tailored to have specific properties for specific applications. Full article
(This article belongs to the Section Metal Composites)
Show Figures

Figure 1

Figure 1
<p>TEM images of the investigated reinforcement particles (<b>a</b>) BN, (<b>b</b>) VC.</p>
Full article ">Figure 2
<p>Friction stir process schematic drawing and design.</p>
Full article ">Figure 3
<p>Manufacturing the composite sheet using FSP: (<b>a</b>) typical FSP process using a milling machine, (<b>b</b>) a thermal image during the manufacturing process.</p>
Full article ">Figure 4
<p>Optical micrographs showing the grain structure of (<b>a</b>) AA 6061 base alloy and (<b>b</b>) the refined grain structure in the stirred zone after friction stir processing (FSP), (<b>b</b>) Al/BN, (<b>c</b>) Al/VC, and (<b>d</b>) hybrid Al/50%BN + 50%VC.</p>
Full article ">Figure 5
<p>Grain size distribution of the manufactured composites in the stirred zone: (<b>a</b>) Al/BN, (<b>b</b>) Al/VC, and (<b>c</b>) hybrid Al/50%BN + 50%VC.</p>
Full article ">Figure 6
<p>Percentage of grain refinement due to friction stir processing (FSP) in AA 6061 alloy and its composites.</p>
Full article ">Figure 7
<p>(SEM) images of hybrid composite samples containing (<b>a</b>) AA6061/BN mono composite, (<b>b</b>) AA6061/VC mono composite, and (<b>c</b>) hybrid composite AA6061/40%BN + 60%VC.</p>
Full article ">Figure 8
<p>(SEM) images of hybrid composite samples containing (<b>a</b>) 60% BN + 40%VC, (<b>b</b>) hybrid composite AA6061/50%BN + 50%VC.</p>
Full article ">Figure 9
<p>Bulk density values of the investigated samples.</p>
Full article ">Figure 10
<p>Microhardness behavior (<b>a</b>) AVG microhardness value in the stirred zone; mechanical properties: (<b>b</b>) profile of the base metal, mono composite, and hybrid composite samples fabricated through friction stir processing (FSP).</p>
Full article ">Figure 11
<p>Mechanical properties: (<b>a</b>) Young’s modulus of AA 6061 alloy and its composites with different reinforcement percentages, (<b>b</b>) influence of shear modulus on AA 6061 alloy and its composites.</p>
Full article ">Figure 12
<p>The wear rate behavior of the investigated sample using the weight loss method.</p>
Full article ">Figure 13
<p>The radar plot shows the comparative performance of AA6061 and its composites.</p>
Full article ">
Previous Issue
Back to TopTop