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Search Results (9,830)

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Keywords = thermal and mechanical properties

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14 pages, 3629 KiB  
Article
Correlation of Solidification Thermal Variables with Microstructure and Hardness in CuMn11Al8Fe3Ni3 Manganese–Aluminum–Bronze Alloy
by Ricardo de Luca, Paulo Henrique Tedardi do Nascimento, Vinicius Torres dos Santos, Marcio Rodrigues da Silva, Flavia Gonçalves Lobo, Rogerio Teram, Mauricio Silva Nascimento, Antonio Augusto Couto, Anibal de Andrade Mendes Filho and Givanildo Alves dos Santos
Materials 2025, 18(2), 234; https://doi.org/10.3390/ma18020234 (registering DOI) - 8 Jan 2025
Abstract
The mechanical properties of a final product are directly influenced by the solidification process, chemical composition heterogeneity, and the thermal variables during solidification. This study aims to analyze the influence of solidification thermal variables on the microstructure, hardness, and phase distribution of the [...] Read more.
The mechanical properties of a final product are directly influenced by the solidification process, chemical composition heterogeneity, and the thermal variables during solidification. This study aims to analyze the influence of solidification thermal variables on the microstructure, hardness, and phase distribution of the CuMn11Al8Fe3Ni3. The alloy was directionally and upward solidified from a temperature of 1250 °C. Heat extraction occurred through a water-cooled AISI 1020 steel interface. The thermal variables were recorded using a data acquisition system, with temperature monitored at seven different positions, where cooling rates varied from 13.03 °C/s at the closest position to 0.23 °C/s at the farthest. The Brinell hardness decreased from 199 HB at the highest cooling rate position to 184 HB at the slowest cooling rate position. This indicates that higher cooling rates increase the hardness of the alloy, which can be attributed to the stabilization of the metastable β phase with refined and equiaxial grains due to iron addition. Vickers microhardness was observed in regions subjected to slower cooling (244 HV) compared to faster cooling regions (222 HV). Therefore, the correlation between solidification thermal variables and alloy properties provides valuable insights into the relationship between microstructure and the properties of the CuMn11Al8Fe3Ni3 alloy. Full article
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Figure 1

Figure 1
<p>Pseudo-binary diagram of Cu-Al-11Mn [<a href="#B12-materials-18-00234" class="html-bibr">12</a>].</p>
Full article ">Figure 2
<p>Schematic representation of the unidirectional solidification apparatus used to measure the thermal variables of the CuMn11Al8Fe3Ni3 alloy [<a href="#B13-materials-18-00234" class="html-bibr">13</a>,<a href="#B33-materials-18-00234" class="html-bibr">33</a>].</p>
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<p>Schematic sequence used for sample cut and preparation.</p>
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<p>CuMn11Al8Fe3Ni3 during directional solidification. In (<b>a</b>), liquidus temperature (t<sub>L</sub>) is observed in each thermocouple; in (<b>b</b>), growth rate (V<sub>L</sub>) is evaluated for each thermocouple; in (<b>c</b>), the cooling rate (T<sub>R</sub>) is evaluated for each thermocouple; and in (<b>d</b>), the thermal gradient (G<sub>L</sub>) is evaluated for each thermocouple.</p>
Full article ">Figure 5
<p>(<b>left</b>) Brinell hardness vs. position. (<b>right</b>) Vickers microhardness HV1 vs. position.</p>
Full article ">Figure 6
<p>Correlation between the fraction of precipitates, the grain size, the shape of the precipitates, and the distance from the heat extraction surface.</p>
Full article ">Figure 7
<p>Optical microstructural analysis and phase identification via SE-SEM.</p>
Full article ">
22 pages, 6110 KiB  
Article
Air–Ice–Water Temperature and Radiation Transfer Via Different Surface Coverings in Ice-Covered Qinghai Lake of the Tibetan Plateau
by Ruijia Niu, Lijuan Wen, Chan Wang, Hong Tang and Matti Leppäranta
Water 2025, 17(2), 142; https://doi.org/10.3390/w17020142 (registering DOI) - 8 Jan 2025
Abstract
There are numerous lakes in the Tibetan Plateau (TP) that significantly impact regional climate and aquatic ecosystems, which often freeze seasonally owing to the high altitude. However, the special warming mechanisms of lake water under ice during the frozen period are poorly understood, [...] Read more.
There are numerous lakes in the Tibetan Plateau (TP) that significantly impact regional climate and aquatic ecosystems, which often freeze seasonally owing to the high altitude. However, the special warming mechanisms of lake water under ice during the frozen period are poorly understood, particularly in terms of solar radiation penetration through lake ice. The limited understanding of these processes has posed challenges to advancing lake models and improving the understanding of air–lake energy exchange during the ice-covered period. To address this, a field experiment was conducted at Qinghai Lake, the largest lake in China, in February 2022 to systematically examine thermal conditions and radiation transfer across air–ice–water interfaces. High-resolution remote sensing technologies (ultrasonic instrument and acoustic Doppler devices) were used to observe the lake surface changes, and MODIS imagery was also used to validate differences in lake surface conditions. Results showed that the water temperature under the ice warmed steadily before the ice melted. The observation period was divided into three stages based on surface condition: snow stage, sand stage, and bare ice stage. In the snow and sand stages, the lake water temperature was lower due to reduced solar radiation penetration caused by high surface reflectance (61% for 2 cm of snow) and strong absorption by 8 cm of sand (absorption-to-transmission ratio of 0.96). In contrast, during the bare ice stage, a low reflectance rate (17%) and medium absorption-to-transmission ratio (0.86) allowed 11% of solar radiation to penetrate the ice, reaching 11.70 W·m−2, which increased the water temperature across the under-ice layer, with an extinction coefficient for lake water of 0.39 (±0.03) m−1. Surface coverings also significantly influenced ice temperature. During the bare ice stage, the ice exhibited the lowest average temperature and the greatest diurnal variations. This was attributed to the highest daytime radiation absorption, as indicated by a light extinction coefficient of 5.36 (±0.17) m−1, combined with the absence of insulation properties at night. This study enhances understanding of the characteristics of water/ice temperature and air–ice–water solar radiation transfer through effects of different ice coverings (snow, sand, and ice) in Qinghai Lake and provides key optical radiation parameters and in situ observations for the refinement of TP lake models, especially in the ice-covered period. Full article
(This article belongs to the Special Issue Ice and Snow Properties and Their Applications)
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Figure 1

Figure 1
<p>(<b>a</b>) Overview of Qinghai Lake, with the observation location marked by a red pentagram. (<b>b</b>) Layout of the observational instrumentation. (<b>c</b>–<b>f</b>) Instrument setup, manual snow thickness measurements, and lake ice thickness measurements via drilling.</p>
Full article ">Figure 2
<p>(<b>a</b>,<b>c</b>) Daily and (<b>b</b>,<b>d</b>) diurnal variations in (<b>a</b>,<b>b</b>) temperature and (<b>c</b>,<b>d</b>) wind speed at Qinghai Lake in 6–24 February 2022. The shaded areas in (<b>a</b>,<b>c</b>) correspond to the standard stages of lake cover: blue for snow, green for sand, and yellow for bare ice. Panels (<b>b</b>,<b>d</b>) display stage-averaged data for each variable. Note: Consistent with this article’s approach, the color coding in panels (<b>a</b>,<b>c</b>) is applied across all figures to represent the three distinct stages of the lake’s cover.</p>
Full article ">Figure 3
<p>Terra/MODIS images during the stable freezing period of Qinghai Lake in 6–24 February 2022, along with snapshots from the automatic weather station during the snow, sand, and bare ice stages. Two images from the automatic weather station are provided for each stage. The MODIS images are shown daily, except for 20 February, which has been removed due to distortion. Red corresponds to Band 3 (459–479 nm), green corresponds to Band 6 (1628–1652 nm), and blue corresponds to Band 7 (2105–2155 nm). Red areas represent ice and snow, cyan represents exposed soil, and white indicates small liquid water droplets in clouds. The lake surface is covered by a stable frozen ice layer.</p>
Full article ">Figure 4
<p>High-precision ultrasonic measurements of lake ice surface distances and thicknesses. The (<b>top</b>) graph depicts the distance from the sub-ice ultrasonic sensor to the underside of the ice, referred to as ’Under-ice’. The (<b>middle</b>) graph illustrates the distance from the ice surface ultrasonic sensor to the ice surface (or covering surface, if present), referred to as ’Surface-ice’. The (<b>bottom</b>) graph presents the combined thickness of the ice and any covering, measured from the top to the bottom surface, referred to as ’Ice and covering’.</p>
Full article ">Figure 5
<p>Temporal profiles of water temperature at various depths: (<b>a</b>) 12-hourly smoothed temperatures at 0.4 m, 0.5 m, 6.7 m, 8.7 m, and 12.7 m depths in February 2022; (<b>b</b>) 12-hourly smoothed temperatures at a depth of 2.1 m from February to April 2023, with the shaded area indicating the ice-covered period.</p>
Full article ">Figure 6
<p>(<b>a</b>) Thirty-minute average lake ice temperature and (<b>b</b>) vertical temperature profile.</p>
Full article ">Figure 7
<p>(<b>a</b>,<b>c</b>) Long-term trends and (<b>b</b>,<b>d</b>) daily variations in (<b>a</b>,<b>b</b>) solar shortwave radiation and (<b>c</b>,<b>d</b>) albedo. The lines in (<b>a</b>) denote downward (blue), upward (green), and net (yellow) shortwave radiation The shaded areas in (<b>b</b>,<b>d</b>) correspond to the snow (blue), sand (green), and bare ice (yellow) periods.</p>
Full article ">Figure 8
<p>(<b>a</b>) Long-term trend and (<b>b</b>–<b>d</b>) daily variations in underwater radiation at depths of 0.7 m, 2.1 m, and the ice bottom.</p>
Full article ">Figure 9
<p>Temporal variation in the attenuation coefficients of the lake water (blue) and lake ice (yellow). Dots represent values at 10-minute intervals, and lines represent the daily average.</p>
Full article ">Figure 10
<p>(<b>a</b>) Long-term trend and (<b>b</b>) daily variation in lake ice transmittance.</p>
Full article ">Figure 11
<p>Schematic diagram depicting radiation transfer within the air–ice–water system of Qinghai Lake. The blue dashed box shows the absorption-to-transmission ratio.</p>
Full article ">
19 pages, 15466 KiB  
Article
Development of Bio-Based and Recyclable Epoxy Adhesives by Modification with Thermoplastic Polymers
by Riccardo Miranda, Marco Luciano, Vincenzo Fiore and Antonino Valenza
Polymers 2025, 17(2), 131; https://doi.org/10.3390/polym17020131 (registering DOI) - 8 Jan 2025
Abstract
This paper deals with the design of novel epoxy adhesives by incorporating thermoplastic polymers such as polyetherimide (PEI) and poly(ε-caprolactone) (PCL) into a bio-based and recyclable epoxy resin, known as Polar Bear. The adhesives were characterized by their mechanical (quasi-static and dynamic) and [...] Read more.
This paper deals with the design of novel epoxy adhesives by incorporating thermoplastic polymers such as polyetherimide (PEI) and poly(ε-caprolactone) (PCL) into a bio-based and recyclable epoxy resin, known as Polar Bear. The adhesives were characterized by their mechanical (quasi-static and dynamic) and rheological properties, thermal stability, and adhesion properties in single-lap joints tested at three different temperatures (i.e., −55 °C, 23 °C, 80 °C). The experimental results indicated that low PEI content substantially improved the mechanical performance and toughness of the adhesive, while preserving good processability. Nonetheless, exceeding 3% weight percentage adversely affected the adhesives’ mechanical resistance and workability. Conversely, while PCL addition enhanced the adhesives’ viscosity, it also decreased mechanical performance. However, its eco-friendliness offers potential for sustainable adhesive applications. It is worth noting that regardless of temperature, the modified adhesives consistently outperformed the commercial epoxy adhesive (DP-460), used as reference, in single-lap shear joint tests. Additionally, both PEI- and PCL-modified epoxy adhesives have demonstrated recyclability through a simple acid-based process, enabling joint disassembly and recycling of the adhesive into a thermoplastic polymer. Overall, the modified adhesives represent a promising eco-friendly, high-performance alternative for structural applications, aligning with sustainable and circular practices. Full article
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Figure 1

Figure 1
<p>Schematic representation of the recycling process.</p>
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<p>FTIR spectra of neat Polar, neat PCL, and Polar-PCL blends with varying PCL content.</p>
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<p>FTIR of neat Polar, neat PEI, and Polar-PEI blends with varying PEI content spectra in the regions of (<b>a</b>) 650–1200 cm<sup>−1</sup> and (<b>b</b>) 1600–1900 cm<sup>−1</sup>.</p>
Full article ">Figure 4
<p>Complex viscosity values measured at the onset of the curing process for each polymeric system, varying thermoplastic content.</p>
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<p>Toughness values of the proposed epoxy adhesives compared to commercial adhesive DP-460.</p>
Full article ">Figure 6
<p>Toughness versus viscosity trends for (<b>a</b>) Polar-PCL and (<b>b</b>) Polar-PEI systems.</p>
Full article ">Figure 7
<p>Damping factor (tanδ) trends of (<b>a</b>) Polar-PEI and (<b>b</b>) Polar-PCL systems compared to neat epoxy and commercial adhesive DP-460.</p>
Full article ">Figure 8
<p>Fractured surfaces of Polar-PEI samples with varying thermoplastic content: (<b>a</b>) Polar; (<b>b</b>) Polar-PEI1; (<b>c</b>) Polar-PEI2; (<b>d</b>) Polar-PEI3; (<b>e</b>) Polar-PEI4; (<b>f</b>) Polar-PEI5 systems.</p>
Full article ">Figure 9
<p>Fractured surfaces of Polar-PCL samples with varying thermoplastic content: (<b>a</b>) Polar-PCL5; (<b>b</b>) Polar-PCL10; (<b>c</b>) Polar-PCL15; (<b>d</b>) Polar-PCL20 systems.</p>
Full article ">Figure 10
<p>Single-lap joints’ shear strength at varying temperature conditions.</p>
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<p>Metallic substrates separated after joint disassembly.</p>
Full article ">Figure 12
<p>Thermoplastic polymers extracted after the recycling process of (<b>a</b>) Polar-PCL5; (<b>b</b>) Polar-PCL10; (<b>c</b>) Polar-PEI1; (<b>d</b>) Polar-PEI2 epoxy systems.</p>
Full article ">Figure 12 Cont.
<p>Thermoplastic polymers extracted after the recycling process of (<b>a</b>) Polar-PCL5; (<b>b</b>) Polar-PCL10; (<b>c</b>) Polar-PEI1; (<b>d</b>) Polar-PEI2 epoxy systems.</p>
Full article ">Figure 13
<p>FTIR spectra of recycled thermoplastic polymers.</p>
Full article ">
17 pages, 3867 KiB  
Article
First-Principles Study on the Mechanical Properties of Ni3Sn4-Based Intermetallic Compounds with Ce Doping
by Ruisheng Zhao, Yan Cao, Jinhu He, Jianjun Chen, Shiyuan Liu, Zhiqiang Yang, Jinbao Lin and Chao Chang
Coatings 2025, 15(1), 59; https://doi.org/10.3390/coatings15010059 - 7 Jan 2025
Abstract
Ni3Sn4 intermetallic compound (IMC) is a critical material in modern electronic packaging and soldering technology. Although Ni3Sn4 enhances the strength of solder joints, its brittleness and anisotropy make it prone to crack formation under mechanical stress, such [...] Read more.
Ni3Sn4 intermetallic compound (IMC) is a critical material in modern electronic packaging and soldering technology. Although Ni3Sn4 enhances the strength of solder joints, its brittleness and anisotropy make it prone to crack formation under mechanical stress, such as thermal cycling or vibration. To improve the plasticity of Ni3Sn4 and mitigate its anisotropy, this study employs first-principles calculations to investigate the mechanical properties and electronic structure of the doped compounds Cex Ni3−xSn4 (x = 0, 0.5, 1, 1.5, 2) by adding the rare earth element Ce. The results indicate that the structure Ce0.5 Ni2.5Sn4 has a lower formation enthalpy (Hf) compared to other doped structures, suggesting enhanced stability. It was found that all structures exhibit improved plasticity with Ce doping, while the Ce0.5 Ni2.5Sn4 structure shows relatively minor changes in hardness (H) and elastic modulus, along with the lowest anisotropy value (AU). Analysis of the total density of states (TDOS) and partial density of states (PDOS) reveals that the electronic properties are primarily influenced by the Ni-d and Ce-f orbitals. At the Fermi level, all Cex Ni3−xSn4 (x = 0, 0.5, 1, 1.5, 2) structures exhibit metallic characteristics and distinct electrical conductivity. Notably, the TDOS value at the Fermi level for Ce0.5 Ni2.5Sn4 lies between those of Ni3Sn4 and other doped structures, indicating good metallicity and conductivity, as well as relative stability. Further PDOS analysis suggests that Ce doping enhances the plasticity of Ni3Sn4. This study provides valuable insights for the further application of rare earth elements in electronic packaging materials. Full article
(This article belongs to the Special Issue Coatings for Advanced Devices)
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Figure 1

Figure 1
<p>Crystal structures of (<b>a</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>3</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>0.5</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>2.5</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> <mfenced open="(" close=")" separators="|"> <mrow> <mn>4</mn> <mi mathvariant="normal">i</mi> </mrow> </mfenced> <mo>,</mo> </mrow> </semantics></math> (<b>c</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>0.5</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>2.5</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>(2a), (<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>1</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, (<b>e</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>1.5</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>1.5</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, and (<b>f</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>1</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>.</p>
Full article ">Figure 2
<p>Changes in lattice constants a (Å), b (Å), and c (Å) with varying Ce content.</p>
Full article ">Figure 3
<p>The variation in bulk modulus, shear modulus, and Young modulus with the Ce atom.</p>
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<p>The variation of <math display="inline"><semantics> <mrow> <msup> <mrow> <mi>A</mi> </mrow> <mrow> <mi>U</mi> </mrow> </msup> </mrow> </semantics></math> with the Ce atom fraction.</p>
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<p>The surface constructions of bulk modulus for (<b>a</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>3</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>0.5</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>2.5</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, (<b>c</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>1</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, (<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>1.5</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>1.5</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, and (<b>e</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>1</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>.</p>
Full article ">Figure 6
<p>The 3D surface plots of Young’s modulus for (<b>a</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>3</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>0.5</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>2.5</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, (<b>c</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>1</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, (<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>1.5</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>1.5</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>, and (<b>e</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>1</mn> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math>.</p>
Full article ">Figure 7
<p>Comparison of total density of states (TDOS) in <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>e</mi> </mrow> <mrow> <mi>x</mi> </mrow> </msub> <msub> <mrow> <mi>N</mi> <mi>i</mi> </mrow> <mrow> <mn>3</mn> <mo>−</mo> <mi>x</mi> </mrow> </msub> <msub> <mrow> <mi>S</mi> <mi>n</mi> </mrow> <mrow> <mn>4</mn> </mrow> </msub> </mrow> </semantics></math> (<span class="html-italic">x</span> = 0, 0.5, 1, 1.5, 2).</p>
Full article ">Figure 8
<p>Total and partial density of states (TPDOS).</p>
Full article ">
25 pages, 4060 KiB  
Article
Impact of Microwave Time on the Structure and Functional Properties of Glycosylated Soy 7S Globulins
by Jixin Zhang, Tao Cui, Lan Zhang, Huiqing Xu, Jingguo Xu and Jun Wang
Foods 2025, 14(2), 151; https://doi.org/10.3390/foods14020151 - 7 Jan 2025
Abstract
This study examined the effects of varying microwave treatment durations (0–120 s) on the structural and functional properties of glycosylated soybean 7S protein. The results indicated that microwaving for 60 s significantly altered the structure of 7S, resulting in a more ordered protein [...] Read more.
This study examined the effects of varying microwave treatment durations (0–120 s) on the structural and functional properties of glycosylated soybean 7S protein. The results indicated that microwaving for 60 s significantly altered the structure of 7S, resulting in a more ordered protein configuration. The treated protein exhibited the largest particle size (152.3 nm), lowest polydispersity index (0.248), highest α-helix content (47.86%), and lowest β-sheet, β-turn, and random coil contents (12.33%, 16.07%, and 22.41%, respectively). It also showed the lowest endogenous fluorescence and surface hydrophobicity, and the highest thermal denaturation temperature (76.8 °C). Additionally, microwaving for ≤90 s led to increased peptide modifications, with carbamylation and deamidation being the most prevalent. A microwave treatment time of 60 s also notably enhanced the functional properties of glycosylated soybean 7S protein, optimizing water-holding capacity (6.060 g/g), emulsification activity, and stability (45.191 m2/g and 33.63 min). The foaming capacity was second only to the 120 s treatment (32% at 60 s versus 34% at 120 s), though the oil-holding capacity (22.73 g/g) and foaming stability (33.42%) were significantly lower than those of the controls. Microwave treatment durations exceeding or below 60 s led to the structural disintegration of the protein, diminishing most of its functional properties. This study explores the mechanism of how microwave processing time affects the structure and functional properties of glycosylated soybean 7S protein and identifies 60 s as the optimal microwave processing time. It meets the demands for healthy and delicious food in home cooking, providing scientific evidence for using microwave processing technology to enhance the nutritional value and quality of food. Full article
(This article belongs to the Topic Food Security and Healthy Nutrition)
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<p>The effect of varying microwave treatment times on the microstructure of glycosylated soybean 7S proteins is illustrated in images (<b>A</b>–<b>E</b>), which correspond to treatment durations of 0, 30, 60, 90, and 120 s, respectively.</p>
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<p>The effect of varying microwave treatment times on the particle size and polydispersity index (PDI) of glycosylated soybean 7S proteins is shown; The different letters in the figure indicate significant differences between the groups (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>The effect of varying microwave treatment durations on the secondary structure (<b>a</b>) and percentage composition (<b>b</b>) of glycosylated 7S protein.</p>
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<p>Analysis of far-ultraviolet CD spectra of glycosylated soybean 7S protein subjected to varying durations of microwave treatment.</p>
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<p>The impact of varying microwave exposure durations on the tryptophan fluorescence spectra of glycosylated soybean 7S protein.</p>
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<p>Exogenous fluorescence of glycosylated soybean 7S proteins subjected to varying microwave treatment durations.</p>
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<p>Effect of various microwave durations on the DSC curves of glycosylated soybean 7S proteins.</p>
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<p>Relative quantification of amino acid residue-modified peptides in glycosylated soybean 7S protein under varying microwave treatment durations.</p>
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<p>Major types of modifications in glycosylated soybean 7S proteins, both major and minor, at varying microwave durations.</p>
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<p>Water-holding (<b>a</b>) and oil-holding (<b>b</b>) properties of glycosylated soybean 7S at different microwave times; the different letters in the figure indicate significant differences between the groups (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>Emulsifiability and emulsion stability of glycosylated soybean 7S under varying microwave treatment durations; the different letters in the figure indicate significant differences between the groups (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>Foamability and stability of glycosylated soybean 7S proteins under varying microwave durations; the different letters in the figure indicate significant differences between the groups (<span class="html-italic">p</span> &lt; 0.05).</p>
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21 pages, 7145 KiB  
Article
Studying the Size-Dependence of Graphene Nanoplatelets (GNPs) in the Final Properties of Polyurethane Aerogels: Thermal Insulation and Mechanical Strength
by Jaime Lledó, Judith Martín-de León, Tomás E. Gómez Álvarez-Arenas, Miguel Ángel Rodríguez-Pérez and Beatriz Merillas
Gels 2025, 11(1), 44; https://doi.org/10.3390/gels11010044 - 7 Jan 2025
Abstract
In the present work, the influence of the addition of graphene nanoplatelets presenting different dimensions on polyurethane–polyisocyanurate aerogel structure and properties has been studied. The obtained aerogels synthesized through a sol–gel method have been fully characterized in terms of density, porosity, specific surface [...] Read more.
In the present work, the influence of the addition of graphene nanoplatelets presenting different dimensions on polyurethane–polyisocyanurate aerogel structure and properties has been studied. The obtained aerogels synthesized through a sol–gel method have been fully characterized in terms of density, porosity, specific surface area, mechanical stiffness, thermal conductivity, and speed of sound. Opacified aerogels showing high porosity (>92%) and low densities (78–98 kg/m3) have been produced, and the effect of the size and content of graphene nanoplatelets has been studied. It has been observed that formulations with less than 5 wt.% of graphene nanoplatelets larger than 2 microns can effectively reduce the total thermal conductivity by absorption and scattering of the infrared radiation, reducing the heat transfer by this mechanism. The resulting opacified samples are highly insulating materials, with thermal conductivities less than 18 mW/m·K. Moreover, it has been observed that smaller particles with ca. 200 nm of average length can promote an increase in the elastic modulus, therefore obtaining stiffer aerogels, combined with thermal conductivities lower than 20 mW/m·K. Results have been studied in detail, providing a further understanding of the mechanisms for improving the final properties of these materials, making them more suitable for industrial applications. Full article
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<p>SEM micrographs of the GNPs used in the present work.</p>
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<p>Photo of all the synthesized aerogels in this work. Aerogels with the same type of GNP are placed in the same row, while in the same column are sorted by GNP content. The dashed yellow line indicates when the particle aggregates start to be visible.</p>
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<p>(<b>a</b>) Densities of the opacified samples and the reference one and (<b>b</b>) volumetric shrinkage (S<sub>v</sub>) for all the produced materials.</p>
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<p>(<b>a</b>) SEM micrograph of the 5 L opacified aerogel. L-GNP particles are marked in blue color, surrounded by the pearl-necklace aerogel structure. (<b>b</b>) Magnification of the aerogel nanostructure.</p>
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<p>(<b>a</b>) pore size and (<b>b</b>) particle size of the opacified samples and the reference one. The dotted lines and the axis-break are visual guides to improve the visualization of data.</p>
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<p>Stress–strain curves for the opacified aerogels and the reference one obtained by compression-decompression tests up to a 10% deformation.</p>
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<p>Energy loss coefficients for each GNP size and content.</p>
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<p>Comparison of the ELC for samples with different GNPs with the same content (1 wt.%).</p>
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<p>Raw values of elastic modulus of all the samples.</p>
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<p>Elastic modulus vs. relative density of all the samples. L-GNP series in blue, M-GNP series in green, and S-GNP series in yellow.</p>
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<p>Stress–strain curves until a deformation of at least 80% of all the samples, separated by GNP type. In the three graphs, the dashed line represents the reference aerogel curve.</p>
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<p>Thermal conductivity of the studied aerogels at 20 °C. The gray bar represents the reference aerogel (non-opacified). For the sake of clarity, the dashed line represents the thermal conductivity of the reference aerogel.</p>
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<p>Contributions to the total thermal conductivity of opacified aerogels.</p>
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<p>Diagram of the scattering mechanism in opacified aerogels with large GNPs (L-GNPs and M-GNPs).</p>
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<p>Diagram of five of the most important parameters of aerogels from the reference, 5 L, 1 M, and 0.5 S samples.</p>
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17 pages, 5952 KiB  
Article
Enhancement of Biopolymer Film Properties Using Spermidine, Zinc Oxide, and Graphene Oxide Nanoparticles: A Study of Physical, Thermal, and Mechanical Characteristics
by Esmaeil Vafaei, Maryam Hasani, Nasrin Salehi, Farzaneh Sabbagh and Shirin Hasani
Materials 2025, 18(2), 225; https://doi.org/10.3390/ma18020225 - 7 Jan 2025
Abstract
One of the main limitations of biopolymers compared to petroleum-based polymers is their weak mechanical and physical properties. Recent improvements focused on surmounting these constraints by integrating nanoparticles into biopolymer films to improve their efficacy. This study aimed to improve the properties of [...] Read more.
One of the main limitations of biopolymers compared to petroleum-based polymers is their weak mechanical and physical properties. Recent improvements focused on surmounting these constraints by integrating nanoparticles into biopolymer films to improve their efficacy. This study aimed to improve the properties of gelatin–chitosan-based biopolymer layers using zinc oxide (ZnO) and graphene oxide (GO) nanoparticles combined with spermidine to enhance their mechanical, physical, and thermal properties. The results show that adding ZnO and GO nanoparticles increased the tensile strength of the layers from 9.203 MPa to 17.787 MPa in films containing graphene oxide and zinc oxide, although the elongation at break decreased. The incorporation of nanoparticles reduced the water vapor permeability from 0.164 to 0.149 (g.m−2.24 h−1). Moreover, the transparency of the layers ranged from 72.67% to 86.17%, decreasing with higher nanoparticle concentrations. The use of nanoparticles enhanced the light-blocking characteristics of the films, making them appropriate for the preservation of light-sensitive food items. The thermal properties improved with an increase in the melting temperature (Tm) up to 115.5 °C and enhanced the thermal stability in the nanoparticle-containing samples. FTIR analysis confirmed the successful integration of all components within the films. In general, the combination of gelatin and chitosan, along with ZnO, GO, and spermidine, significantly enhanced the properties of the layers, making them stronger and more suitable for biodegradable packaging applications. Full article
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<p>Stress–strain curves of CH/G films.</p>
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<p>Water vapor permeability of CH/G films.</p>
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<p>Swelling degree of CH/G films.</p>
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<p>XRD patterns of (<b>a</b>) CH/G film (control), (<b>b</b>) CH/G/SPD film, (<b>c</b>) CH/G/SPD/ZnO film, (<b>d</b>) CH/G/SPD/GO, (<b>e</b>) CH/G/SPD/ZnO/GO film.</p>
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<p>FTIR spectroscopy for (<b>a</b>) CH/G film (control), (<b>b</b>) CH/G/SPD film, (<b>c</b>) CH/G/SPD/ZnO film, (<b>d</b>) CH/G/SPD/GO, (<b>e</b>) CH/G/SPD/ZnO/GO film.</p>
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<p>Differential scanning calorimetry (DSC) for (<b>a</b>) CH/G film (control), (<b>b</b>) CH/G/SPD film, (<b>c</b>) CH/G/SPD/ZnO film, (<b>d</b>) CH/G/SPD/GO, (<b>e</b>) CH/G/SPD/ZnO/GO film.</p>
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<p>Differential scanning calorimetry (DSC) for (<b>a</b>) CH/G film (control), (<b>b</b>) CH/G/SPD film, (<b>c</b>) CH/G/SPD/ZnO film, (<b>d</b>) CH/G/SPD/GO, (<b>e</b>) CH/G/SPD/ZnO/GO film.</p>
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<p>SEM images for (<b>a</b>) CH/G film (control), (<b>b</b>) CH/G/SPD film, (<b>c</b>) CH/G/SPD/ZNO film, (<b>d</b>) CH/G/SPD/GO, (<b>e</b>) CH/G/SPD/ZNO/GO film.</p>
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8 pages, 2833 KiB  
Communication
Enhanced Peelability and Quality of Whiteleg Shrimp (Litopenaeus vannamei) Using Pulsed Electric Field (PEF) Treatment
by Gyeong-Seo Park, Hyeon Seo, Han-Baek Lee, Ji-Won Lee, Hafiz Muhammad Shahbaz, Se-Ho Jeong and Dong-Un Lee
Foods 2025, 14(2), 148; https://doi.org/10.3390/foods14020148 - 7 Jan 2025
Abstract
This study investigated the effects of pulsed electric field (PEF) treatment on the peeling efficiency and textural properties of whiteleg shrimp (Litopenaeus vannamei). Shrimp samples were treated at field strengths of 0, 1.0, 1.5, and 2.0 kV/cm to assess PEF impact [...] Read more.
This study investigated the effects of pulsed electric field (PEF) treatment on the peeling efficiency and textural properties of whiteleg shrimp (Litopenaeus vannamei). Shrimp samples were treated at field strengths of 0, 1.0, 1.5, and 2.0 kV/cm to assess PEF impact on peeling force, incomplete peeling percentage, and texture profile. The results showed that PEF treatment significantly reduced the peeling force from 50.88 N in controls to 42.99 N at 2.0 kV/cm, while the percentage of incompletely peeled shrimp decreased from 27.5% to 15.9%. Texture profile analysis indicated that PEF treatment had no impact on the key properties of hardness and chewiness (no significant difference), with a reduction in springiness observed at higher field strengths. Improvements in peelability are attributed to electroporation, which disrupts collagen in the connective tissue between the shrimp shell and muscle. These findings indicate that PEF treatment is an efficient, non-thermal method for enhancing shrimp peeling processes while preserving textural integrity. PEF technology offers a promising alternative to traditional mechanical and thermal methods in the seafood processing industry. Full article
(This article belongs to the Special Issue Optimization of Non-thermal Technology in Food Processing)
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<p>Peeling force (<b>a</b>) and incompletely peeled percentage (<b>b</b>) for shrimp after PEF treatment with different field strengths (n = 40). The error bar for the peeling force values (<b>a</b>) represents standard deviation, and letters (<b>a</b>,<b>b</b>) indicate significant differences for each sample (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>Appearance of PEF-treated shrimp before and after peeling. The scale bar of the images is 3 cm.</p>
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17 pages, 6537 KiB  
Article
Development of Acoustic Insulating Carpets from Milkweed Fibers Using Air-Laid Spike Process
by Deborah Lupescu, Mathieu Robert and Said Elkoun
Fibers 2025, 13(1), 4; https://doi.org/10.3390/fib13010004 - 7 Jan 2025
Viewed by 151
Abstract
Fibers from milkweed, which grows in Quebec (Canada), offer a distinct and outstanding advantage compared to other natural fibers: their ultra-lightweight hollow structure provides excellent acoustic and thermal insulation properties for the automobile industry. To highlight the properties of milkweed fibers and reduce [...] Read more.
Fibers from milkweed, which grows in Quebec (Canada), offer a distinct and outstanding advantage compared to other natural fibers: their ultra-lightweight hollow structure provides excellent acoustic and thermal insulation properties for the automobile industry. To highlight the properties of milkweed fibers and reduce the use of synthetic materials in vehicles, nonwoven carpeting made from a blend of milkweed fibers and polylactic acid (PLA) fibers was produced using the air-laid process. Some of the nonwovens were compressed to investigate the effects of increased mass per unit area on their thermal, acoustic, and mechanical properties. The nonwovens’ mass per unit area, thermal insulation, sound absorption coefficient, airflow resistivity, compression, and resistance to moisture were evaluated and compared to other carpets made of natural and synthetic fibers. The findings indicate that milkweed and PLA carpets have lower thermal conductivity values of 37.45 (mW/m·K), (mW/m·K) less than carpets made from cotton and polypropylene. At low frequencies, none of the carpets absorbed sound. At high frequencies, milkweed and PLA carpets showed sound absorption values of at least 0.6, which provide better acoustic insulation than nonwoven materials made from jute and polyethylene (PE) fibers. Milkweed and PLA carpets exhibited better compression values than polypropylene (PP) carpets. Full article
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<p>Milkweed fiber.</p>
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<p>The manufacturing process of nonwoven mats and carpets using the air-laid process.</p>
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<p>Carpets.</p>
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<p>Steps to calculate the compression resistance and recovery (ASTM D6571-22).</p>
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<p>SEM images of milkweed fibers from (<b>a</b>) UC nonwoven, (<b>b</b>) C1, (<b>c</b>) C2, (<b>d</b>) C3, (<b>e</b>) C4, and (<b>f</b>) C5.</p>
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<p>The sound absorption coefficient versus the frequency for the nonwoven and the carpets.</p>
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<p>Sound absorption coefficient values versus the frequency for the nonwoven and the carpets with and without a 30 mm deep cavity, (<b>a</b>) the UC nonwoven, (<b>b</b>) C1, (<b>c</b>) C2, (<b>d</b>) C3, (<b>e</b>) C4, (<b>f</b>) C5.</p>
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<p>Sound absorption coefficient values versus the frequency for carpets with the same thickness of 8.65 mm.</p>
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<p>Airflow resistivity values versus (<b>a</b>) density and (<b>b</b>) porosity.</p>
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41 pages, 8350 KiB  
Review
Structure and Properties of Al–CNT-Based Composites Manufactured by Different Methods: A Brief Review
by Marat Nurguzhin, Marat Janikeyev, Myrzakhan Omarbayev, Azira Yermakhanova, Mohammed Meiirbekov, Miras Zhumakhanov, Aruzhan Keneshbekova, Meiram Atamanov, Aigerim Akylbayeva, Aidos Lesbayev and Darkhan Yerezhep
Materials 2025, 18(1), 214; https://doi.org/10.3390/ma18010214 - 6 Jan 2025
Viewed by 247
Abstract
Aluminum–carbon nanotube (Al–CNT) composites represent a cutting-edge class of materials characterized by their exceptional mechanical, thermal, and electrical properties, making them highly promising for aerospace, automotive, electronics, and energy applications. This review systematically examines the impact of various fabrication methods, including conventional powder [...] Read more.
Aluminum–carbon nanotube (Al–CNT) composites represent a cutting-edge class of materials characterized by their exceptional mechanical, thermal, and electrical properties, making them highly promising for aerospace, automotive, electronics, and energy applications. This review systematically examines the impact of various fabrication methods, including conventional powder metallurgy, diffusion and reaction coupling, as well as adhesive and reaction bonding on the microstructure and performance of Al–CNT composites. The analysis emphasizes the critical role of CNT dispersion, interfacial bonding, and the formation of reinforcing phases, such as Al4C3 and Al2O3, in determining the mechanical strength, wear resistance, corrosion resistance, and thermal stability of these materials. The challenges of CNT agglomeration, high production costs, and difficulties in controlling interfacial interactions are highlighted alongside potential solutions, such as surface modifications and reinforcement strategies. The insights presented aim to guide future research and innovation in this rapidly evolving field. Full article
40 pages, 12985 KiB  
Article
Electrolytic Ni-P and Ni-P-Cu Coatings on PCM-Loaded Expanded Graphite for Enhanced Battery Thermal Management with Mechanical Properties
by Onur Güler and Mustafa Yusuf Yazıcı
Materials 2025, 18(1), 213; https://doi.org/10.3390/ma18010213 - 6 Jan 2025
Viewed by 210
Abstract
This study addresses the thermal management challenge in battery systems by enhancing phase change material composites with Ni-P and Ni-P-Cu coatings on phase change material/expanded graphite structures. Traditional phase change materials are limited by low thermal conductivity and mechanical stability, which restricts their [...] Read more.
This study addresses the thermal management challenge in battery systems by enhancing phase change material composites with Ni-P and Ni-P-Cu coatings on phase change material/expanded graphite structures. Traditional phase change materials are limited by low thermal conductivity and mechanical stability, which restricts their effectiveness in high-demand applications. Unlike previous studies, this work integrates Ni-P and Ni-P-Cu coatings to significantly improve both the thermal conductivity and mechanical strength of phase change material/expanded graphite composites, filling a crucial gap in battery thermal management solutions. The results reveal that Ni-P-Cu-coated phase change material/expanded graphite composites exhibit a superior thermal conductivity of 27.1 W/m·K, significantly outperforming both uncoated and Ni-P-coated counterparts. Mechanical testing showed that the Ni-P-Cu coating provided the highest compressive strength at 39.4 MPa and enhanced tensile strength due to the coating’s highly crystalline structure and smaller grain size. Additionally, the phase-change characteristics of the phase change material/expanded graphite composites, with phase transition temperatures between 38 °C and 43 °C, allowed effective heat absorption, stabilizing battery temperatures under 1.25C and 2.5C discharge rates. Voltage decay analysis indicated that Ni-P and Ni-P-Cu coatings reduced polarization effects, extending operational stability. These findings suggest that Ni-P-Cu-coated phase change material/expanded graphite composites are highly effective in thermal management applications, especially in battery systems where efficient heat dissipation and mechanical durability are critical for performance and safety. This study offers a promising approach to improving energy storage systems for applications such as electric vehicles, grid storage, and portable electronics. Full article
(This article belongs to the Section Energy Materials)
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<p>Particle size distribution graph of the expandable graphite particles.</p>
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<p>SEM images of the initial expandable graphite and obtained EG particles.</p>
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<p>SEM images of the microstructure of the bulk EG and PCM/EG composite packs.</p>
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<p>The curves of (<b>a</b>) TGA and (<b>b</b>) DSC of the EG, PCM, and PCM/EG composite packs.</p>
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<p>XRD patterns of the EG, PCM, and PCM/EG composites.</p>
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<p>Morphology of the Ni-P and Ni-P-Cu coatings obtained with different coating parameters.</p>
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<p>XRD patterns of the Ni-P- and Ni-P-Cu-coated PCM/EG composite packs.</p>
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<p>Crystallite size and crystallinity values of the PCM/EG composite packs with Ni-P and Ni-P-Cu coatings obtained under different parameters.</p>
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<p>Tensile stress–strain curves of the samples.</p>
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<p>Compressive stress–strain curves of the samples.</p>
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<p>Thermal conductivity of the samples.</p>
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<p>Local temperature variations for (<b>a</b>) PCM/EG, (<b>b</b>) Ni-P, and (<b>c</b>) Ni-P-Cu.</p>
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<p>Time-dependent variation in the potential value for (<b>a</b>) PCM/EG, (<b>b</b>) Ni-P, and (<b>c</b>) Ni-P-Cu.</p>
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<p>Discharge capacity and energy capacity variation for (<b>a</b>) PCM/EG, (<b>b</b>) Ni-P, and (<b>c</b>) Ni-P-Cu.</p>
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<p>Production of EG particles by expansion of expandable graphite particles.</p>
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<p>The mold and fabrication of different types of block or bulk samples.</p>
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<p>PCM impregnation into the EG blocks.</p>
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<p>Electrolytic (<b>a</b>) Ni-P and (<b>b</b>) Ni-P-Cu coating process of the PCM/EG composite packs.</p>
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<p>Thermal management test setup images; (<b>a</b>) test area, (<b>b</b>) assembly of the packs with LBs and placement of batteries in uncoated packs, (<b>c</b>) Ni-P-coated packs, and (<b>d</b>) Ni-P-Cu-coated packs.</p>
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<p>Illustration of thermocouple placement (<b>a</b>) locations with (<b>b</b>) dimensions on the LIBs.</p>
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12 pages, 3591 KiB  
Article
Multilayer Graphene Stacked with Silver Nanowire Networks for Transparent Conductor
by Jinsung Kwak
Materials 2025, 18(1), 208; https://doi.org/10.3390/ma18010208 - 6 Jan 2025
Viewed by 226
Abstract
A mechanically robust flexible transparent conductor with high thermal and chemical stability was fabricated from welded silver nanowire networks (w-Ag-NWs) sandwiched between multilayer graphene (MLG) and polyimide (PI) films. By modifying the gas flow dynamics and surface chemistry of the Cu surface during [...] Read more.
A mechanically robust flexible transparent conductor with high thermal and chemical stability was fabricated from welded silver nanowire networks (w-Ag-NWs) sandwiched between multilayer graphene (MLG) and polyimide (PI) films. By modifying the gas flow dynamics and surface chemistry of the Cu surface during graphene growth, a highly crystalline and uniform MLG film was obtained on the Cu foil, which was then directly coated on the Ag-NW networks to serve as a barrier material. It was found that the highly crystalline layers in the MLG film compensate for structural defects, thus forming a perfect barrier film to shield Ag NWs from oxidation and sulfurization. MLG/w-Ag-NW composites were then embedded into the surface of a transparent and colorless PI thin film by spin-coating. This allowed the MLG/w-Ag-NW/PI composite to retain its original structural integrity due to the intrinsic physical and chemical properties of PI, which also served effectively as a binder. In view of its unique sandwich structure and the chemical welding of the Ag NWs, the flexible substrate-cum-electrode had an average sheet resistance of ≈34 Ω/sq and a transmittance of ≈91% in the visible range, and also showed excellent stability against high-temperature annealing and sulfurization. Full article
(This article belongs to the Section Advanced Nanomaterials and Nanotechnology)
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<p>(<b>a</b>) A sequential schematic diagram of fabricating MLG/Ag-NW/PI composites. First, using LPCVD in our oxidation protocols, a large-area MLG layer was grown on a Cu foil. Then, Ag-NW solution was spin-coated on an MLG/Cu foil. Followed by chemical welding of Ag-NW networks on an MLG/Cu foil, transparent soluble PI solution was spin-coated and cured for structural integrity. Finally, Cu was etched away and the MLG/w-Ag-NW/PI composite was obtained. (<b>b</b>) A photo of MLG/w-Ag-NW/PI held by tweezers. (<b>c</b>–<b>e</b>) Representative SEM images of MLG/w-Ag-NW/PI composite. Purple arrow in (<b>d</b>) indicates typical torn MLG and green arrow in (<b>e</b>) indicates a wrinkle of MLG right above Ag-NWs. (<b>f</b>) Representative Raman spectrum obtained from various locations in an MLG layer.</p>
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<p>(<b>a</b>,<b>b</b>) Schematic illustrations of layer-controlled CVD graphene synthesis by changing the position of a Cu foil loaded in the interior of a quartz tube (upper panels) and corresponding optical microscope images of as-synthesized graphene layers transferred onto a Si/SiO<sub>2</sub> substrate (lower panels). (<b>c</b>) A schematic illustration of an air-oxidized Cu foil loaded at the bottom of a quartz tube with MLG transferred onto a Si/SiO<sub>2</sub> substrate observed using an optical microscope. (<b>d</b>) MLG coverage data as a function of Cu foil oxidation method. (<b>e</b>) Data on graphene coverage on back side of Cu foil as a function of Cu foil oxidation method. (<b>f</b>) MLG coverage data as a function of growth time.</p>
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<p>(<b>a</b>) Sheet resistance and transmittance at 550 nm of Gr/PI composites according to the MLG portion. (<b>b</b>) Sheet resistance and transmittance at 550 nm of MLG/Ag-NW/PI films depending on the number of Ag coating cycles, in which MLG coverage is ~98%. (<b>c</b>) Comparison of sheet resistance values before and after chemical welding of Ag-NWs on the Ag-NW/MLG/Cu foil. (<b>d</b>) Comparison of optoelectronic properties (<span class="html-italic">R</span><sub>sh</sub> and transmittance at 550 nm) between our MLG/w-AgNW/PI composite and previously reported results. The performance of Ag-NW [<a href="#B40-materials-18-00208" class="html-bibr">40</a>], graphene [<a href="#B41-materials-18-00208" class="html-bibr">41</a>], SWCNT [<a href="#B42-materials-18-00208" class="html-bibr">42</a>], and SWCNT/graphene [<a href="#B43-materials-18-00208" class="html-bibr">43</a>] composites is shown for comparison. (<b>e</b>,<b>f</b>) Mechanical bending properties of TCEs upon continuous bending cycles and bending radii, respectively.</p>
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<p>Test for environmental stability of our MLG/w-Ag-NW/PI composite in air (<b>a</b>) at ~25 °C and (<b>b</b>) ~100 °C and (<b>c</b>) in an aqueous ammonium persulfate solution (0.1 M), in which a change in resistance is observed.</p>
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21 pages, 9244 KiB  
Review
Carbon Nanotube/Polymer Composites for Functional Applications
by Yoon-Ji Yim, Young-Hoon Yoon, Seong-Hwang Kim, Jeong-Hoon Lee, Dong-Chul Chung and Byung-Joo Kim
Polymers 2025, 17(1), 119; https://doi.org/10.3390/polym17010119 - 6 Jan 2025
Viewed by 290
Abstract
Carbon nanotubes (CNTs) have garnered significant interest in the field of nanotechnology owing to their unique structure and exceptional properties. These materials find applications across a diverse array of fields, including electronics, environmental science, energy, and biotechnology. CNTs serve as potent reinforcing agents [...] Read more.
Carbon nanotubes (CNTs) have garnered significant interest in the field of nanotechnology owing to their unique structure and exceptional properties. These materials find applications across a diverse array of fields, including electronics, environmental science, energy, and biotechnology. CNTs serve as potent reinforcing agents in polymer composites; even minimal additions can significantly improve the mechanical, electrical, and thermal properties of polymers. With the growing demand for polymer composites across various industries, there is an anticipation for CNT/polymer composites to evolve in increasingly diverse directions. This paper reviews recent advancements in the manufacturing techniques of various CNT/polymer composites and discusses the enhancements in their mechanical, electrical, and thermal properties. Furthermore, it explores the potential applications of these composites. Full article
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<p>Structural comparison: (<b>a</b>) single-walled carbon nanotubes (SWCNTs) and (<b>b</b>) multi-walled carbon nanotubes (MWCNTs) [<a href="#B38-polymers-17-00119" class="html-bibr">38</a>].</p>
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<p>Classification of CNT/polymer composites.</p>
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<p>Illustration of the solution mixing method for producing CNT/polymer composites.</p>
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<p>Manufacturing techniques for CNT/polymer composites: (<b>a</b>) melt-mixing processes [<a href="#B77-polymers-17-00119" class="html-bibr">77</a>] and (<b>b</b>) in situ polymerization [<a href="#B80-polymers-17-00119" class="html-bibr">80</a>].</p>
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<p>Manufacturing techniques for CNT/polymer composites: (<b>a</b>) melt-mixing processes [<a href="#B77-polymers-17-00119" class="html-bibr">77</a>] and (<b>b</b>) in situ polymerization [<a href="#B80-polymers-17-00119" class="html-bibr">80</a>].</p>
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<p>(<b>A</b>) Manufacturing method; (<b>a</b>) The ERE and rotor trajectory diagram based on elongational rheology technology, (<b>b</b>) The flow field distribution diagram of polymer melting plasticization in EFF and (<b>B</b>) mechanical properties of MWCNT/PLA/P (3HB-co-4HB); (<b>a</b>) Tensile strength (<b>b</b>) Elongation at break, (<b>c</b>) Young’s modulus (<b>d</b>) Impact strength [<a href="#B45-polymers-17-00119" class="html-bibr">45</a>].</p>
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<p>Scheme of the three-roll milling dispersion method for CNT/polymer composites according to process time: MWCNT (top) and SWCNT (bottom). The red box indicates the ideal dispersion state [<a href="#B52-polymers-17-00119" class="html-bibr">52</a>].</p>
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<p>(<b>A</b>) Electrical conductivity of SWCNT and MWCNT/PDMS composites with three-roll milling process time [<a href="#B52-polymers-17-00119" class="html-bibr">52</a>] and (<b>B</b>) SEM images of the cross-sectional specimens cut from the plated-shape cavity at the center position of microinjection-molded SWCNT/PC (<b>a</b>,<b>c</b>) before annealing and (<b>b</b>,<b>d</b>) after annealing at 250 °C for 1 h [<a href="#B56-polymers-17-00119" class="html-bibr">56</a>].</p>
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<p>Synthesis reaction of p-SWCNT-OH and p-SWCNT-O-APTS [<a href="#B60-polymers-17-00119" class="html-bibr">60</a>].</p>
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<p>Simulation model containing CNT/polymer and EMI SE of the composites [<a href="#B97-polymers-17-00119" class="html-bibr">97</a>].</p>
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<p>Room-temperature electrical conductivities, Seebeck coefficients, and power factors as a function of CNT loading composites, with schematic illustration of CNT/polymer composites [<a href="#B99-polymers-17-00119" class="html-bibr">99</a>].</p>
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<p>Schematic illustration of PMMA-based bone cement for CNT and cell attachment; positive (pathway 1) and negative effect (pathway 2) [<a href="#B102-polymers-17-00119" class="html-bibr">102</a>].</p>
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21 pages, 7149 KiB  
Article
Experimental Testing Results on Critical Components for Molten Salt-Based CSP Systems
by Valeria Russo, Giuseppe Petroni, Francesco Rovense, Mauro Giorgetti, Giuseppe Napoli, Gianremo Giorgi and Walter Gaggioli
Energies 2025, 18(1), 198; https://doi.org/10.3390/en18010198 - 5 Jan 2025
Viewed by 332
Abstract
Concentrated Solar Power (CSP) plants integrated with Thermal Energy Storage (TES) represent a promising renewable energy source for generating heat and power. Binary molten salt mixtures, commonly referred to as Solar Salts, are utilized as effective heat transfer fluids and storage media due [...] Read more.
Concentrated Solar Power (CSP) plants integrated with Thermal Energy Storage (TES) represent a promising renewable energy source for generating heat and power. Binary molten salt mixtures, commonly referred to as Solar Salts, are utilized as effective heat transfer fluids and storage media due to their thermal stability and favorable thermophysical properties. However, these mixtures pose significant challenges due to their high solidification temperatures, around 240 °C, which can compromise the longevity and reliability of critical system components such as pressure sensors and bellows seal globe valves. Thus, it is essential to characterize their performance, assess their reliability under various conditions, and understand their failure mechanisms, particularly in relation to temperature fluctuations affecting the fluid’s viscosity. This article discusses experimental tests conducted on a pressure sensor and a bellows seal globe valve, both designed for direct contact with molten salts in CSP environments, at the ENEA Casaccia Research Center laboratory in Rome. The methodology for conducting these experimental tests is detailed, and guidelines are outlined to optimize plant operation. The findings provide essential insights for improving component design and maintenance to minimize unplanned plant downtime. They also offer methodologies for installing measurement instruments and electrical heating systems on the components. Full article
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<p>(<b>a</b>) Comprehensive view of the MoSE laboratory-scale test loop; (<b>b</b>) view of the plant from the control room.</p>
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<p>Overview of process showing lines and main components of the plant. In red circles the Pressure Sensor and the Bellows Seal Globe Valve considered in this analysis.</p>
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<p>A detail view of the piping line containing the pressure sensor and the bellows seal globe valve considered in the study.</p>
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<p>(<b>a</b>) Preparation phase of the molten salt mixture before the tank filling; (<b>b</b>) a view inside the tank during the installation of some thermocouples on the electric heaters external casings.</p>
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<p>(<b>a</b>) A schematic section drawing of the bellows seal globe vale; (<b>b</b>) the valve during the electric cables assembly and the thermocouples welding on its casing; (<b>c</b>) the Bellows Seal Globe Valve after the final assembly.</p>
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<p>(<b>a</b>) schematic drawing of the pressure sensor; (<b>b</b>) view of the instrument during electric tracing assembly and thermocouples installation; (<b>c</b>) the instrument after the final assembly.</p>
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<p>(<b>a</b>) detail view of the bellows seal globe valve; (<b>b</b>) schematic drawing of the bellows seal globe valve with indication of the thermocouples position on its casing.</p>
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<p>(<b>a</b>) A detailed view of the pressure sensor; (<b>b</b>) a schematic drawing of the pressure sensor with indication of the thermocouples position on its casing.</p>
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<p>Measured temperature profiles of the salt in the piping line and on the bellows seal globe valve casing. Test I (<b>a</b>). Test II (<b>b</b>).</p>
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<p>Measured temperature profiles of the salt in the piping line and on the pressure sensor casing. Test III (<b>a</b>). Test IV (<b>b</b>).</p>
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<p>Temperature trends on the bellows seal globe valve body vs time. (<b>a</b>) Test V. (<b>b</b>) Test VI.</p>
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17 pages, 7807 KiB  
Article
Methodological Impact on Curing Kinetics of Bone Cement Based on Poly (Styrene-co-Methyl Methacrylate)–2D Nanofiller Nanocomposites
by Mohan Raj Krishnan and Edreese Housni Alsharaeh
Polymers 2025, 17(1), 116; https://doi.org/10.3390/polym17010116 - 5 Jan 2025
Viewed by 258
Abstract
Herein, we report the methodological impact on the curing kinetics of bone cement based on polymer nanocomposites prepared using different methods. Poly (styrene-co-methylmethacrylate)–2D nanofiller nanocomposites (P(S-MMA)–2D Nanofiller) were prepared using bulk and suspension polymerization methods to study the effect of the [...] Read more.
Herein, we report the methodological impact on the curing kinetics of bone cement based on polymer nanocomposites prepared using different methods. Poly (styrene-co-methylmethacrylate)–2D nanofiller nanocomposites (P(S-MMA)–2D Nanofiller) were prepared using bulk and suspension polymerization methods to study the effect of the different methods. The prepared nanocomposites were well-characterized for chemical, thermal, mechanical, and structural characteristics using Fourier Transform Infrared spectroscopy (FT-IR), differential scanning calorimetry (DSC), nano-indentation, and scanning electron microscopy (SEM) techniques, respectively. The FT-IR results confirmed the successful formation of the polymer nanocomposites. The DSC results showed that the prepared nanocomposites have higher thermal stabilities than their copolymer counterparts. The nano-indentation results revealed that the elastic modulus of the copolymer nanocomposites (bulk polymerization) was as high as 7.89 GPa, and the hardness was 0.219 GPa. Incorporating the 2D nanofiller in the copolymer matrix synergistically enhances the thermo-mechanical properties of the bone cement samples. The polymer nanocomposites prepared using the suspension polymerization method exhibit faster-curing kinetics (15 min) than those prepared using the bulk polymerization (120–240 min) method. Full article
(This article belongs to the Section Polymer Composites and Nanocomposites)
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<p>Preparation of P(S-MMA)–2D nanofiller nanocomposites.</p>
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<p>Room-temperature activation of BPO initiator with DMPT [<a href="#B64-polymers-17-00116" class="html-bibr">64</a>].</p>
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<p>Curing kinetics of bone cement. I is the initiator; A is the activator; M is the monomer; RM<sup>•</sup> is formed monomer radical by reacting with the initiator radical; k<sub>d</sub>, k<sub>i</sub>, k<sub>p</sub>, and k<sub>t</sub> are the respective rate constants of initiator decomposition, initiation, propagation, and termination reactions [<a href="#B64-polymers-17-00116" class="html-bibr">64</a>].</p>
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<p>SEM images of bone cement prepared by suspension polymerization. (<b>a</b>) P(S-MMA), (<b>b</b>) P(S-MMA)/CG, (<b>c</b>) P(S-MMA)/BN, and (<b>d</b>) P(S-MMA)/CG:BN.</p>
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<p>SEM images of bone cement prepared by bulk polymerization. (<b>a</b>) P(S-MMA), (<b>b</b>) P(S-MMA)/CG, (<b>c</b>) P(S-MMA)/BN, and (<b>d</b>) P(S-MMA)/CG:BN.</p>
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<p>FT−IR spectra of P(S-MMA)–2D nanofiller nanocomposite bone cement samples prepared using bulk and suspension polymerization methods.</p>
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<p>DSC curves of P(S-MMA)–2D nanofiller nanocomposite bone cement samples prepared using bulk and suspension polymerization methods.</p>
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<p>Nanomechanical of P(S-MMA) and P(S-MMA)–2D nanofiller nanocomposites that are prepared using (<b>a</b>) bulk and (<b>b</b>) suspension polymerization methods.</p>
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<p>Curing and dough times of bone cement samples using different methods. (<b>a</b>) Suspension polymerization and (<b>b</b>) bulk polymerization.</p>
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