[go: up one dir, main page]

 
 
Sign in to use this feature.

Years

Between: -

Subjects

remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline

Journals

remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline

Article Types

Countries / Regions

remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline
remove_circle_outline

Search Results (1,651)

Search Parameters:
Keywords = elastomer

Order results
Result details
Results per page
Select all
Export citation of selected articles as:
18 pages, 8956 KiB  
Article
Development and Experimental Study of a Mixed-Mode Vibration Isolator Using Magnetorheological Elastomer
by Qianjie Liu, Zhirong Guo, Wei Liu, Gang Li, Shengzhi Jin, Lei Yu and Guoliang Hu
Actuators 2024, 13(9), 352; https://doi.org/10.3390/act13090352 - 11 Sep 2024
Viewed by 205
Abstract
This paper proposes a mixed-mode (combining shear and squeeze working modes) vibration isolator using magnetorheological elastomer (MRE), which enables the isolator to have a larger working area and better isolation performance by combining the working modes of the MRE. Firstly, based on the [...] Read more.
This paper proposes a mixed-mode (combining shear and squeeze working modes) vibration isolator using magnetorheological elastomer (MRE), which enables the isolator to have a larger working area and better isolation performance by combining the working modes of the MRE. Firstly, based on the magnetorheological effect working principle of the MRE, the material selection and dimensional parameters of each component are determined through structural design and magnetic circuit calculation. On this basis, magnetic field simulation is conducted using Maxwell 16.0 software to analyze the distribution of magnetic field lines and magnetic induction in the working area. Simultaneously, equivalent stiffness and equivalent damping models are established to explore the variation of vibration response with external current and excitation frequency conditions. Finally, a vibration isolation experimental platform is built to test the mixed-mode MRE isolator. The experimental results are basically consistent with the simulation modeling results. The experimental results showed that when the external excitation is in the frequency range of 16 Hz, effective semi-active vibration isolation control could be achieved by applying different current inputs. The isolation effect of the system is difficult to effectively control using current input when the external excitation is at high frequency. These results validate the rationality and feasibility of the mixed-mode MRE isolator structure, which provides a good reference for the design of MRE isolators. Full article
(This article belongs to the Special Issue Magnetorheological Actuators and Dampers)
Show Figures

Figure 1

Figure 1
<p>The structure of the mixed-mode MRE isolator.</p>
Full article ">Figure 2
<p>Two commonly used magnetic circuits of the MRE devices. (<b>a</b>) Outside the coil; (<b>b</b>) Inside the coil.</p>
Full article ">Figure 3
<p>The magnetic circuit of the mixed-mode MRE isolator.</p>
Full article ">Figure 4
<p>The equivalent magnetic circuit.</p>
Full article ">Figure 5
<p>The magnetic field simulation results of the mixed-mode MRE isolator. (<b>a</b>) Magnetic field line; (<b>b</b>) Magnetic induction.</p>
Full article ">Figure 6
<p>The average magnetic induction of the MRE under different currents.</p>
Full article ">Figure 7
<p>The isolation system model of the MRE isolator.</p>
Full article ">Figure 8
<p>Rotational rheometer.</p>
Full article ">Figure 9
<p>The magnetic-induced modulus and loss factor of the MRE.</p>
Full article ">Figure 10
<p>The displacement response of spring-loaded mass under different currents. (<b>a</b>) 4 Hz; (<b>b</b>) 8 Hz; (<b>c</b>) 12 Hz; (<b>d</b>) 16 Hz; (<b>e</b>) 20 Hz; (<b>f</b>) 24 Hz.</p>
Full article ">Figure 10 Cont.
<p>The displacement response of spring-loaded mass under different currents. (<b>a</b>) 4 Hz; (<b>b</b>) 8 Hz; (<b>c</b>) 12 Hz; (<b>d</b>) 16 Hz; (<b>e</b>) 20 Hz; (<b>f</b>) 24 Hz.</p>
Full article ">Figure 11
<p>The acceleration response of spring-loaded mass under different currents. (<b>a</b>) 4 Hz; (<b>b</b>) 8 Hz; (<b>c</b>) 12 Hz; (<b>d</b>) 16 Hz; (<b>e</b>) 20 Hz; (<b>f</b>) 24 Hz.</p>
Full article ">Figure 12
<p>The prototype of the mixed-mode MRE isolator. (<b>a</b>) Components; (<b>b</b>) Prototype.</p>
Full article ">Figure 13
<p>The MRE isolator testing platform. (<b>a</b>) Experimental device; (<b>b</b>) Experimental principle.</p>
Full article ">Figure 14
<p>Comparison of test and simulation results. (<b>a</b>) 0.5 A; (<b>b</b>) 1 A; (<b>c</b>) 1.5 A; (<b>d</b>) 2 A.</p>
Full article ">Figure 15
<p>The acceleration response before vibration isolation is applied.</p>
Full article ">Figure 16
<p>The experimental acceleration response of spring-loaded mass under different currents. (<b>a</b>) 4 Hz; (<b>b</b>) 8 Hz; (<b>c</b>) 12 Hz; (<b>d</b>) 16 Hz; (<b>e</b>) 20 Hz; (<b>f</b>) 24 Hz.</p>
Full article ">Figure 17
<p>The vibration attenuation rate under different currents.</p>
Full article ">
18 pages, 5551 KiB  
Article
Use of Recycled Additive Materials to Promote Efficient Use of Resources While Acting as an Effective Toughness Modifier of Wood–Polymer Composites
by Luísa Rosenstock Völtz, Linn Berglund and Kristiina Oksman
Polymers 2024, 16(18), 2549; https://doi.org/10.3390/polym16182549 - 10 Sep 2024
Viewed by 319
Abstract
Wood–polymer composites (WPCs) with polypropylene (PP) matrix suffer from low toughness, and fossil-based impact modifiers are used to improve their performance. Material substitution of virgin fossil-based materials and material recycling are key aspects of sustainable development and therefore recycled denim fabric, and elastomer [...] Read more.
Wood–polymer composites (WPCs) with polypropylene (PP) matrix suffer from low toughness, and fossil-based impact modifiers are used to improve their performance. Material substitution of virgin fossil-based materials and material recycling are key aspects of sustainable development and therefore recycled denim fabric, and elastomer were evaluated to replace the virgin elastomer modifier commonly used in commercial WPCs. Microtomography images showed that the extrusion process fibrillated the denim fabric into long, thin fibers that were well dispersed within the WPC, while the recycled elastomer was found close to the wood fibers, acting as a soft interphase between the wood fibers and PP. The fracture toughness (KIC) of the WPC with recycled denim fabric matched the commercial WPC which was 1.4 MPa m1/2 and improved the composite tensile strength by 18% and E-modulus by 54%. Recycled elastomer resulted in slightly lower KIC, 1.1 MPa m1/2, as well as strength and modulus while increasing elongation and contributing to toughness. The results of this study showed that recycled materials can potentially be used to replace virgin fossil-based elastomeric modifiers in commercial WPCs, thereby reducing the CO2 footprint by 23% and contributing to more efficient use of resources. Full article
(This article belongs to the Special Issue Polymer Composites: Structure, Properties and Processing)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Used recycled materials in this study: (<b>a</b>) a strip of denim fabric; (<b>b</b>) two different types of yarns separated from the denim fabric, where the dark blue is dyed cotton and the white is polyester/elastane yarn; (<b>c</b>) polarized optical microscopy image showing the size difference of elastane, cotton, and polyester fibers separated from the yarns; and (<b>d</b>) image of the received recycled elastomer in granulated form.</p>
Full article ">Figure 2
<p>A schematic of the processing of textile masterbatch where the denim fabric was fed using a side extruder, the PP-rT masterbatch granulates, and the screw-configuration.</p>
Full article ">Figure 3
<p>Extrusion profile temperatures at different zones. Granulated PP-rT was compounded with WPC40 to produce WPC-rT, and rE was also compounded with WPC40 to form WPC-rE. The screw profile with different elements is shown on the bottom of the picture, with the high-shear zones highlighted.</p>
Full article ">Figure 4
<p>Fracture toughness test: (<b>a</b>) schematic of the used specimen’s shape; (<b>b</b>) stereomicroscope image of the notch and pre-crack; (<b>c</b>) specimen with speckle pattern for contrasting; and (<b>d</b>) fracture toughness test set-up in bending mode.</p>
Full article ">Figure 5
<p>Fracture cross-sections of the WPCs: (<b>a</b>) WPC-rT; (<b>b</b>) higher magnification of the rTF with a clean surface; (<b>c</b>) WPC-rE; (<b>d</b>) magnified view of recycled elastomer (rE) covering the wood fibers; (<b>e</b>) WPC-E with some broken wood fibers; and (<b>f</b>) magnified broken wood fiber.</p>
Full article ">Figure 6
<p>Three-dimensional reconstructions µ-CT of WPCs. Different colors represent different components in the composites. PP-matrix is black, fibers are purple, and elastomers are green; and bottom right figures show the same WPCs which are taken from the videos (available in <a href="#app1-polymers-16-02549" class="html-app">Supporting Information</a>).</p>
Full article ">Figure 7
<p>Load–time (continuous lines) and energy–time (dotted lines) curves from the drop-weight impact test, where crack initiation phases, total perforation of the impactor, and friction between impact and specimen are indicated with arrows.</p>
Full article ">Figure 8
<p>Load–displacement curves from fracture toughness with their respective DIC images (at the beginning of the test, and the end of the test); the color bar in DIC images represents the strain on the <span class="html-italic">x</span>-axis.</p>
Full article ">Figure 9
<p>WPC-rT: (<b>a</b>) micrograph of a detailed view of crack from fracture toughness specimen, where fiber pull-outs and fiber bridging are visible; (<b>b</b>) stereomicroscope image of the crack, where fiber pull-outs and microcracks are also visible, as well as stress-whitening zone around the crack; (<b>c</b>) fiber pullout and fiber bridging are suggested fracture toughness mechanisms. Textile fibers are visualized as blue and wood fibers as brown.</p>
Full article ">Figure 10
<p>WPC-rE: (<b>a</b>) micrograph of the crack from the fracture toughness test showing crack propagation in the matrix with crazing mechanism; (<b>b</b>) a stereo-microscopy image of the crack; and crazing; and (<b>c</b>) the suggested fracture toughness mechanism. Wood fibers are visualized as brown and recycled elastomer as green.</p>
Full article ">Figure 11
<p>WPC-E: (<b>a</b>) micrograph of a detailed view of a crack from fracture toughness test where few microcracks are visible; (<b>b</b>) stereomicroscope image of the crack where microcracks are visible, along with a stress-whitened area; and (<b>c</b>) suggested fracture toughness mechanism. Wood fibers are visualized as brown and elastomer as green.</p>
Full article ">Figure 12
<p>Representative stress–strain curves from tensile testing, where the area under the graph represents the toughness.</p>
Full article ">
15 pages, 7504 KiB  
Article
The Stability of UV-Defluorination-Driven Crosslinked Carbon Nanotubes: A Raman Study
by Yunxiang Gao, Mohammad Tarequl Islam, Promise Uzoamaka Otuokere, Merlyn Pulikkathara and Yuemin Liu
Nanomaterials 2024, 14(17), 1464; https://doi.org/10.3390/nano14171464 - 9 Sep 2024
Viewed by 350
Abstract
Carbon nanotubes (CNTs) are often regarded as semi-rigid, all-carbon polymers. However, unlike conventional polymers that can form 3D networks such as hydrogels or elastomers through crosslinking in solution, CNTs have long been considered non-crosslinkable under mild conditions. This perception changed with our recent [...] Read more.
Carbon nanotubes (CNTs) are often regarded as semi-rigid, all-carbon polymers. However, unlike conventional polymers that can form 3D networks such as hydrogels or elastomers through crosslinking in solution, CNTs have long been considered non-crosslinkable under mild conditions. This perception changed with our recent discovery of UV-defluorination-driven direct crosslinking of CNTs in solution. In this study, we further investigate the thermal stability of UV-defluorination-driven crosslinked CNTs, revealing that they are metastable and decompose more readily than either pristine or fluorinated CNTs under Raman laser irradiation. Using Raman spectroscopy under controlled laser power, we examined both single-walled and multi-walled fluorinated CNTs. The results demonstrate that UV-defluorinated CNTs exhibit reduced thermal stability compared to their pristine or untreated fluorinated counterparts. This instability is attributed to the strain on the intertube crosslinking bonds resulting from the curved carbon lattice of the linked CNTs. The metallic CNTs in the crosslinked CNT networks decompose and revert to their pristine state more readily than the semiconducting ones. The inherent instability of crosslinked CNTs leads to combustion at temperatures approximately 100 °C lower than those required for non-crosslinked fluorinated CNTs. This property positions crosslinked CNTs as promising candidates for applications where mechanically robust, lightweight materials are needed, along with feasible post-use removal options. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>(<b>A</b>) Generation and recombination of free radicals in F-SWNT bundles to form poly (CNTs), as described in our previous work [<a href="#B23-nanomaterials-14-01464" class="html-bibr">23</a>]. (<b>B</b>) Thermal stability of crosslinked CNTs studied in this work.</p>
Full article ">Figure 2
<p>(<b>A</b>) TEM images of untreated F-SWNTs and (<b>B</b>) UV-crosslinked F-SWNTs. (<b>C</b>) Raman spectra of untreated, UV-defluorinated, and hydrazine-defluorinated F-SWNTs, recorded using a 532 nm laser wavelength with a power density of 2.9 kW/mm<sup>2</sup>.</p>
Full article ">Figure 3
<p>Raman spectra of (<b>A</b>) untreated F-SWNTs and (<b>B</b>) UV-defluorinated crosslinked F-SWNTs. (<b>C</b>) D/G ratio of untreated F-SWNTs and UV-DeF-SWNTs as a function of the fraction of full Raman laser power density. The Raman laser wavelength is 532 nm, with a full laser power density of 2.9 kW/mm<sup>2</sup>. Insets in (<b>A</b>,<b>B</b>) show amplified RBM bands.</p>
Full article ">Figure 4
<p>Raman spectra of (<b>A</b>) untreated F-SWNTs and (<b>B</b>) crosslinked F-SWNTs via defluorination, using a 633 nm laser at varying power densities. (<b>C</b>) D/G ratio of untreated and crosslinked F-SWNTs as a function of the fraction of full laser power density. (<b>D</b>) Changes in RBM peak intensity in response to increasing laser power density. Full power density: 4.2 kW/mm<sup>2</sup>.</p>
Full article ">Figure 5
<p>Microscope images of the Raman laser-irradiated sample areas: (<b>A1</b>,<b>A2</b>) pristine SWNTs, (<b>B1</b>,<b>B2</b>) untreated F-SWNTs, and (<b>C1</b>,<b>C2</b>) crosslinked UV-DeF-SWNTs irradiated at 1/10 (Column 1) and full (Column 2) power density, respectively. Full power density: 2.9 kW/mm<sup>2</sup>.</p>
Full article ">Figure 6
<p>Raman spectra of (<b>A</b>) untreated F-MWNTs and (<b>B</b>) UV-DeF-MWNTs. Laser wavelength: 532 nm, with a full power density of 2.9 kW/mm<sup>2</sup>.</p>
Full article ">Figure 7
<p>Microscope images of various MWNTs irradiated with a 532 nm Raman laser at 1/10 full power density (Left, Column 1, <b>A1</b>,<b>B1</b>,<b>C1</b>) and full power density (Right, Column 2, <b>A2</b>,<b>B2</b>,<b>C2</b>). (<b>A1</b>,<b>A2</b>) Pristine MWNTs, (<b>B1</b>,<b>B2</b>) Untreated F-MWNTs, and (<b>C1</b>,<b>C2</b>) UV-defluorinated MWNTs (UV-DeF-MWNTs).</p>
Full article ">Figure 8
<p>(<b>A</b>) TGA curves of F-MWNTs and UV-DeF-MWNTs. (<b>B</b>) Enlarged view of the ignition and combustion region featured in (<b>A</b>).</p>
Full article ">
21 pages, 9076 KiB  
Article
Bioinspired Design of 3D-Printed Cellular Metamaterial Prosthetic Liners for Enhanced Comfort and Stability
by Vasja Plesec and Gregor Harih
Biomimetics 2024, 9(9), 540; https://doi.org/10.3390/biomimetics9090540 - 6 Sep 2024
Viewed by 642
Abstract
Traditional prosthetic liners are often limited in customization due to constraints in manufacturing processes and materials. Typically made from non-compressible elastomers, these liners can cause discomfort through uneven contact pressures and inadequate adaptation to the complex shape of the residual limb. This study [...] Read more.
Traditional prosthetic liners are often limited in customization due to constraints in manufacturing processes and materials. Typically made from non-compressible elastomers, these liners can cause discomfort through uneven contact pressures and inadequate adaptation to the complex shape of the residual limb. This study explores the development of bioinspired cellular metamaterial prosthetic liners, designed using additive manufacturing techniques to improve comfort by reducing contact pressure and redistributing deformation at the limb–prosthesis interface. The gyroid unit cell was selected due to its favorable isotropic properties, ease of manufacturing, and ability to distribute loads efficiently. Following the initial unit cell identification analysis, the results from the uniaxial compression test on the metamaterial cellular samples were used to develop a multilinear material model, approximating the response of the metamaterial structure. Finite Element Analysis (FEA) using a previously developed generic limb–liner–socket model was employed to simulate and compare the biomechanical behavior of these novel liners against conventional silicone liners, focusing on key parameters such as peak contact pressure and liner deformation during donning, heel strike, and the push-off phase of the gait cycle. The results showed that while silicone liners provide good overall contact pressure reduction, cellular liners offer superior customization and performance optimization. The soft cellular liner significantly reduced peak contact pressure during donning compared to silicone liners but exhibited higher deformation, making it more suitable for sedentary individuals. In contrast, medium and hard cellular liners outperformed silicone liners for active individuals by reducing both contact pressure and deformation during dynamic gait phases, thereby enhancing stability. Specifically, a medium-density liner (10% infill) balanced contact pressure reduction with low deformation, offering a balance of comfort and stability. The hard cellular liner, ideal for high-impact activities, provided superior shape retention and support with lower liner deformation and comparable contact pressures to silicone liners. The results show that customizable stiffness in cellular metamaterial liners enables personalized design to address individual needs, whether focusing on comfort, stability, or both. These findings suggest that 3D-printed metamaterial liners could be a promising alternative to traditional prosthetic materials, warranting further research and clinical validation. Full article
(This article belongs to the Special Issue Bionic Design & Lightweight Engineering)
Show Figures

Figure 1

Figure 1
<p>Conventional definitive transtibial prosthesis including a socket, pylon, and prosthetic foot.</p>
Full article ">Figure 2
<p>Stress–strain chart illustrating the response of the cellular liner, soft tissue, and silicone liner, with the pain threshold level indicated.</p>
Full article ">Figure 3
<p>FEA of a unit cell performed in nTopology: (<b>a</b>) the meshed unit cell, (<b>b</b>) a spatial representation of the stiffness matrix, and (<b>c</b>) a representation of the deformation in all six directions.</p>
Full article ">Figure 4
<p>Unit cell structures used in the FEA along with the spatial representation of the stiffness matrix: (<b>a</b>) TPMS structures and (<b>b</b>) beam metamaterial structures. In the stiffness matrix, red represents higher stiffness, while blue indicates lower stiffness.</p>
Full article ">Figure 5
<p>Results of the uniaxial compression test with 6% (soft), 10% (medium), and 14% (hard) gyroid infill patterns. Solid lines represent the MELAS models used in numerical simulations to capture the hyperelastic behavior of the cellular structures. Diamond markers indicate the start and finish of the plateau regions for each structure.</p>
Full article ">Figure 6
<p>Geometry of the generic transtibial limb–prosthesis model: (<b>a</b>) bones, including the patella, tibia, fibula, and femur; (<b>b</b>) the soft tissue of the residual limb; and (<b>c</b>) the final model, including the transtibial limb, prosthetic liner, and socket.</p>
Full article ">Figure 7
<p>Color map illustrating rectification of PTB and TSB socket, where red denotes depressed areas and blue indicates domed areas.</p>
Full article ">Figure 8
<p>Loading conditions applied in the numerical analysis, comprising (<b>a</b>) socket donning and (<b>b</b>) normal gait, adhering to ISO 10328 guidelines.</p>
Full article ">Figure 9
<p>Maximum contact pressure during donning, heel strike, and push-off phases for all liner types, using (<b>a</b>) PTB socket and (<b>b</b>) TSB socket.</p>
Full article ">Figure 10
<p>Comparison of contact pressure distribution between a medium metamaterial liner and a traditional silicone liner during the heel strike and push-off phases for (<b>a</b>) the PTB socket and (<b>b</b>) TSB socket.</p>
Full article ">Figure 11
<p>Maximum deformation during donning, heel strike, and push-off phases for all liner types, using (<b>a</b>) PTB socket and (<b>b</b>) TSB socket.</p>
Full article ">Figure 12
<p>Comparison of deformation distribution between a medium metamaterial liner and a traditional silicone liner during the heel strike and push-off phases for (<b>a</b>) the PTB socket and (<b>b</b>) the TSB socket.</p>
Full article ">
12 pages, 23755 KiB  
Article
Estimation of the Structure of Hydrophobic Surfaces Using the Cassie–Baxter Equation
by Oleksiy Myronyuk, Egidijus Vanagas, Aleksej M. Rodin and Miroslaw Wesolowski
Materials 2024, 17(17), 4322; https://doi.org/10.3390/ma17174322 - 31 Aug 2024
Viewed by 581
Abstract
The effect of extreme water repellency, called the lotus effect, is caused by the formation of a Cassie–Baxter state in which only a small portion of the wetting liquid droplet is in contact with the surface. The rest of the bottom of the [...] Read more.
The effect of extreme water repellency, called the lotus effect, is caused by the formation of a Cassie–Baxter state in which only a small portion of the wetting liquid droplet is in contact with the surface. The rest of the bottom of the droplet is in contact with air pockets. Instrumental methods are often used to determine the textural features that cause this effect—scanning electron and atomic force microscopies, profilometry, etc. However, this result provides only an accurate texture model, not the actual information about the part of the surface that is wetted by the liquid. Here, we show a practical method for estimating the surface fraction of texture that has contact with liquid in a Cassie–Baxter wetting state. The method is performed using a set of ethanol–water mixtures to determine the contact angle of the textured and chemically equivalent flat surfaces of AlSI 304 steel, 7500 aluminum, and siloxane elastomer. We showed that the system of Cassie–Baxter equations can be solved graphically by the wetting diagrams introduced in this paper, returning a value for the texture surface fraction in contact with a liquid. We anticipate that the demonstrated method will be useful for a direct evaluation of the ability of textures to repel liquids, particularly superhydrophobic and superoleophobic materials, slippery liquid-infused porous surfaces, etc. Full article
Show Figures

Figure 1

Figure 1
<p>Surface structure of Al-46-16 sample (<b>a</b>) top view; (<b>b</b>) side view; and (<b>c</b>) surface of the asperity.</p>
Full article ">Figure 2
<p>Surface structure of St-60-45 sample (<b>a</b>) top view; (<b>b</b>) side view; and (<b>c</b>) groove border.</p>
Full article ">Figure 3
<p>Surface structure and asperities/groove borders of samples (<b>a</b>) St-100-30-L; (<b>b</b>) St-60-30-L; and (<b>c</b>) St-60-45-L.</p>
Full article ">Figure 4
<p>Wetting of the flat and textured anodized aluminum surfaces (treated with OCTEO) with different surface tension liquids: (<b>a</b>) the dependence between the contact angle for the flat and textured surfaces, (<b>b</b>) the wetting diagram.</p>
Full article ">Figure 5
<p>Wetting diagrams of samples: (<b>a</b>) St-60-45; (<b>b</b>) St-60-45; (<b>c</b>) St-60-30-L; and (<b>d</b>) St-100-30-L.</p>
Full article ">Figure 5 Cont.
<p>Wetting diagrams of samples: (<b>a</b>) St-60-45; (<b>b</b>) St-60-45; (<b>c</b>) St-60-30-L; and (<b>d</b>) St-100-30-L.</p>
Full article ">Figure 6
<p>Texture (<b>a</b>) and wetting diagram (<b>b</b>) of the PDMS sample surface formed by the templating technique.</p>
Full article ">Figure 7
<p>Schematic illustration of contact between the wetting liquid and the studied surfaces.</p>
Full article ">Figure 8
<p>Graphical solution description: (<b>a</b>) example of the wetting diagram; (<b>b</b>) results of linear fitting of Cassie state points.</p>
Full article ">
9 pages, 2073 KiB  
Article
Carbon Nanotube Sheets/Elastomer Bilayer Harvesting Electrode with Biaxially Generated Electrical Energy
by Seongjae Oh, Hyeon Ji Kim, Seon Lee, Keon Jung Kim and Shi Hyeong Kim
Polymers 2024, 16(17), 2477; https://doi.org/10.3390/polym16172477 - 30 Aug 2024
Viewed by 320
Abstract
Mechanical energy harvesters made from soft and flexible materials can be employed as energy sources for wearable and implantable devices. However, considering how human organs and joints expand and bend in many directions, the energy generated in response to a mechanical stimulus in [...] Read more.
Mechanical energy harvesters made from soft and flexible materials can be employed as energy sources for wearable and implantable devices. However, considering how human organs and joints expand and bend in many directions, the energy generated in response to a mechanical stimulus in only one direction limits the applicability of mechanical energy harvesters. Here, we report carbon nanotube (CNT) sheets/an elastomer bilayer harvesting electrode (CBHE) that converts two-axis mechanical stimulation into electrical energy. The novel microwinkled structure of the CBHE successfully demonstrates an electrochemical double-layer (EDL) capacitance change from biaxial mechanical stimulation, thereby generating electrical power (0.11 W kg−1). Additionally, the low modulus (0.16 MPa) and high deformability due to the elastomeric substrate suggest that the CBHE can be applied to the human body. Full article
(This article belongs to the Special Issue Advances in Natural Fiber Polymer Composites)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p><b>Fabrication process and stretchability of CBHE:</b> (<b>a</b>) illustration of the process for fabricating CBHE: (<b>a</b>)-(i) elastomer, (<b>a</b>)-(ii) omnidirectionally pre-stretched elastomer at 80 %, (<b>a</b>)-(iii) perpendicularly stacked CNT sheets on the pre-stretched elastomer, and (<b>a</b>)-(iv) released CNT sheets stacked on elastomer at 0% (The red arrow indicates the next step of progress). (<b>b</b>) Optical image of CBHE (scale bar: 1 cm). Optical images of CBHE before and after (<b>c</b>) twisting and (<b>d</b>) bending. Optical images of CBHE before and after stretching along (<b>e</b>) x-axis and (<b>f</b>) y-axis at 80%.</p>
Full article ">Figure 2
<p>The mechanical and electrical properties of the CBHE: (<b>a</b>) the strain–stress graph for the CBHE when stretching along the x-axis (black) and y-axis (red); (<b>b</b>) strain versus resistance retention when stretching the CBHE along the x-axis (black solid circle) and y-axis (red open circle).</p>
Full article ">Figure 3
<p>Surface structure analysis: (<b>a</b>–<b>c</b>) SEM images for CBHE: (<b>a</b>) surface SEM images (scale bar: 50 µm) and cross-sectional SEM images along (<b>b</b>) x-axis and (<b>c</b>) y-axis (scale bar: 40 µm). SEM images for CBHE stretching along (<b>d</b>) x-axis, (<b>e</b>) y-axis, and (<b>f</b>) both axes (scale bar: 50 µm).</p>
Full article ">Figure 4
<p>The electrical energy generation mechanism for the CBHE: (<b>a</b>) the configuration of the CBHE-based three-electrode system (reference electrode: Ag/AgCl; counter electrode: Pt mesh/CNT bucky paper); (<b>b</b>) a conceptual illustration showing the changes in EDL capacitance when stretching and releasing the CBHE; (<b>c</b>) the b-value is a function of voltage (inset showing the linear sweep voltammetry for calculating b-value); (<b>d</b>) PECS analysis using cyclic voltammetry with (black) and without (red) stretching the CBHE.</p>
Full article ">Figure 5
<p>Evaluating harvesting performance within 0.1 M HCl: (<b>a</b>) schematic illustrations of harvesting condition: (<b>a</b>)-(i) stretching CBHE along the x-axis, (<b>a</b>)-(ii) stretching CBHE along the y-axis; (<b>b</b>) CV curves before and after stretching CBHE along the x-axis; (<b>c</b>) real-time OCV and SCC graphs when sinusoidally stretching CBHE to 80% at 1 Hz along the x-axis; (<b>d</b>) CV curves before and after stretching CBHE along the y-axis; (<b>e</b>) real-time OCV and SCC graphs when sinusoidally stretching CBHE to 80% at 1 Hz along the y-axis; (<b>f</b>) gravimetric peak power and peak voltage of CBHE with load resistance; (<b>g</b>) gravimetric peak power of CBHE-based chemo-mechanical energy harvesters during 1000 cycles, when stretched to 80% at 1 Hz (inset showing the generated voltage on 10 cycles). SEM images of CBHE (<b>h</b>) before and (<b>i</b>) after the harvesting cycle test.</p>
Full article ">
17 pages, 3777 KiB  
Article
Three-Dimensionally Printed Microsystems to Facilitate Flow-Based Study of Cells from Neurovascular Barriers of the Retina
by Adam Leverant, Larissa Oprysk, Alexandra Dabrowski, Kelly Kyker-Snowman and Maribel Vazquez
Micromachines 2024, 15(9), 1103; https://doi.org/10.3390/mi15091103 - 30 Aug 2024
Viewed by 411
Abstract
Rapid prototyping has produced accessible manufacturing methods that offer faster and more cost-effective ways to develop microscale systems for cellular testing. Commercial 3D printers are now increasingly adapted for soft lithography, where elastomers are used in tandem with 3D-printed substrates to produce in [...] Read more.
Rapid prototyping has produced accessible manufacturing methods that offer faster and more cost-effective ways to develop microscale systems for cellular testing. Commercial 3D printers are now increasingly adapted for soft lithography, where elastomers are used in tandem with 3D-printed substrates to produce in vitro cell assays. Newfound abilities to prototype cellular systems have begun to expand fundamental bioengineering research in the visual system to complement tissue engineering studies reliant upon complex microtechnology. This project used 3D printing to develop elastomeric devices that examined the responses of retinal cells to flow. Our experiments fabricated molds for elastomers using metal milling, resin stereolithography, and fused deposition modeling via plastic 3D printing. The systems were connected to flow pumps to simulate different flow conditions and examined phenotypic responses of endothelial and neural cells significant to neurovascular barriers of the retina. The results indicated that microdevices produced using 3D-printed methods demonstrated differences in cell survival and morphology in response to external flow that are significant to barrier tissue function. Modern 3D printing technology shows great potential for the rapid production and testing of retinal cell responses that will contribute to both our understanding of fundamental cell response and the development of new therapies. Future studies will incorporate varied flow stimuli as well as different extracellular matrices and expanded subsets of retinal cells. Full article
Show Figures

Figure 1

Figure 1
<p>Schematic of key cellular and structural features of the inner blood–retinal barrier (BRB). (<b>A</b>) This neurovascular barrier tissue is primarily composed of endothelial cells and pericytes within retinal capillaries, as well as astrocytes and Muller glia that reside within neural tissue. (<b>B</b>) Side view of circulating blood flow that exerts continuous shear stress upon endothelial cells that line the lumen (<b>top</b>). Also shown is a side view of cognate neuroglia exposed to shear stress from interstitial flow of neural tissue (<b>bottom</b>).</p>
Full article ">Figure 2
<p>Summary of the glial line system, known as the gLL. (<b>A</b>) Schematic of the gLL used as 3D model for manufacturing. A PDMS elastomer is bonded to a glass microscope slide to produce a closed microchannel in between two volumetric reservoirs, as previously described by our group. (<b>B</b>) The mold used to cure the elastomers needed to produce gLL devices was fabricated using metal milling via computer numerical control (CNC) in the three parts shown. (<b>C</b>) A top view of the final gLL system produced by curing PDMS within the metal molds.</p>
Full article ">Figure 3
<p>Summary of key steps in the rapid prototyping of 3D molds used for elastomeric soft lithography. (<b>A</b>) Fused deposition modeling (FDM) was used to manufacture plastic molds of polyethylene terephthalate glycol (PETG), wherein the 3D device model was converted to gcode for melted plastic extrusion and printed layer by layer. (<b>B</b>) Stereolithography (SLA) was used to develop resin molds of polylactic acid (PLA) via digital upload of the 3D device model, UV curing of layered resin, and two rounds of post processing in isopropyl alcohol.</p>
Full article ">Figure 4
<p>Graphical summary of the flow system used to examine behavior of retinal endothelial and retinal neural cells from the inner blood–retinal barrier. (<b>A</b>) Schematic of pump-driven flow applied within the microdevice and collection of cell media. (<b>B</b>) Images of experimental flow system and representative microdevice.</p>
Full article ">Figure 5
<p>Surface roughness of inner channels of elastomeric microdevices manufactured using 3D molds made of metal, resin, and plastic. (<b>A</b>) Data illustrate measurements from the channel center as determined via optical microscopy for inner channel surfaces coated with (+) and without (−) laminin. Representative images of the microfluidic channel manufactured using molds of (<b>B</b>) metal, (<b>C</b>) resin, and (<b>D</b>) plastic, with (+) and without (−) laminin coating (Scale bar = 200 μm). An average of n = 25 measurements were gathered per device, using 5–7 devices per mold type and laminin coating condition. Statistical significance is denoted by <span class="html-italic">p</span> &lt; 0.05 (**) and <span class="html-italic">p</span> &lt; 0.01 (***).</p>
Full article ">Figure 6
<p>Measurement of particle flow within 3D-printed microsystems alongside analytical flow model. (<b>A</b>) Measured velocity of individual microbeads (*) plotted against one-dimensional analytical solutions to Poiseuille Flow with low (QL) and high (QH) volume flow rates. (<b>B</b>) Analytical solution to imposed shear stress and QL and QH in the same system.</p>
Full article ">Figure 7
<p>Measurement of cell survival within 3D-printed microdevices after induced flow at low (QL =1 μL/min) and high (QH =3 μL/min) volume flow rates. Retinal endothelial cells (RECs) are shown in red and retinal neural cells (RNCs) are shown in blue. An average of n = 25 measurements were gathered per device, using 5–7 devices per mold. Statistical significance is denoted by <span class="html-italic">p</span> &lt; 0.01 (*). # indicates that only trace numbers of cells were observed.</p>
Full article ">Figure 8
<p>Flow-induced morphology changes of retinal endothelial cells (RECs) and retinal neural cells (RNCs) within 3D-printed microdevices. Representative images of RECs cultured in (<b>A</b>) low volume flow rate (QL) and (<b>B</b>) high volume flow rate (QH) alongside representative images of RNCs cultured in (<b>C</b>) control and (<b>D</b>) low volume flow rate (Scale bar = 100 μm). (<b>E</b>) Changes in cell morphology measured via cell shape index (CSI) shown after respective induced flow rates. A total of n = 25 cells were used within 3–5 different devices. Statistical significance of * denotes <span class="html-italic">p</span> &lt; 0.01. # indicates that only trace numbers of cells were observed.</p>
Full article ">
17 pages, 60359 KiB  
Article
Novel Design of Eco-Friendly High-Performance Thermoplastic Elastomer Based on Polyurethane and Ground Tire Rubber toward Upcycling of Waste Tires
by Maoyong He, Ruiping Li, Mingzheng Hao, Ying Tao, Peng Wang, Xiangcheng Bian, Haichun Dang, Yulong Wang, Zhenzhong Li and Tao Zhang
Polymers 2024, 16(17), 2448; https://doi.org/10.3390/polym16172448 - 29 Aug 2024
Viewed by 369
Abstract
Waste rubber tires are an area of global concern in relation to reducing the consumption of petrochemical products and environmental pollution. Herein, eco-friendly high-performance thermoplastic polyurethane (PU) elastomers were successfully in-situ synthesized through the incorporation of ground tire rubber (GTR). The excellent wet-skid [...] Read more.
Waste rubber tires are an area of global concern in relation to reducing the consumption of petrochemical products and environmental pollution. Herein, eco-friendly high-performance thermoplastic polyurethane (PU) elastomers were successfully in-situ synthesized through the incorporation of ground tire rubber (GTR). The excellent wet-skid resistance of PU/GTR elastomer was achieved by using mixed polycaprolactone polyols with Mn = 1000 g/mol (PCL-1K) and PCL-2K as soft segments. More importantly, an efficient solution to balance the contradiction between dynamic heat build-up and wet-skid resistance in PU/GTR elastomers was that low heat build-up was realized through the limited friction between PU molecular chains, which was achieved with the help of the network structure formed from GTR particles uniformly distributed in the PU matrix. Impressively, the tanδ at 60 °C and the DIN abrasion volume (Δrel) of the optimal PU/GTR elastomer with 59.5% of PCL-1K and 5.0% of GTR were 0.03 and 38.5 mm3, respectively, which are significantly lower than the 0.12 and 158.32 mm3 for pure PU elastomer, indicating that the PU/GTR elastomer possesses extremely low rolling resistance and excellent wear resistance. Meanwhile, the tanδ at 0 °C of the above-mentioned PU/GTR elastomer was 0.92, which is higher than the 0.80 of pure PU elastomer, evidencing the high wet-skid resistance. To some extent, the as-prepared PU/GTR elastomer has effectively solved the “magic triangle” problem in the tire industry. Moreover, this novel research will be expected to make contributions in the upcycling of waste tires. Full article
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>tanδ versus temperature curves (<b>a</b>), E′ versus temperature curves (<b>b</b>), DIN abrasion volume (<b>c</b>) and representative stress–strain curves (<b>d</b>) for PU/GTR thermoplastic elastomers.</p>
Full article ">Figure 2
<p>XPS survey spectrum of GTR (<b>a</b>), N1s XPS spectra of GTR (<b>b</b>), atomic ratio of different elements of GTR (<b>c</b>), C1s XPS spectra of pure GTR (<b>d</b>), C1s XPS spectra of GTR in PU-4 (<b>e</b>), the relative area obtained from the deconvoluted C1s XPS spectra of GTR (<b>f</b>).</p>
Full article ">Figure 3
<p>FTIR spectra of PU/GTR thermoplastic elastomers (<b>a</b>), Gaussian fitting curves of PU-1 (<b>b</b>), Gaussian fitting curves of PU-2 (<b>c</b>), Gaussian fitting curves of PU-3 (<b>d</b>), Gaussian fitting curves of PU-4 (<b>e</b>), Gaussian fitting curves of PU-5 (<b>f</b>), Gaussian fitting curves of PU-6 (<b>g</b>), Gaussian fitting curves of PU-7 (<b>h</b>).</p>
Full article ">Figure 4
<p>2D-SAXS patterns of PU-1, PU-4, PU-6 and PU-7 at different temperatures.</p>
Full article ">Figure 5
<p>Lorentz-corrected SAXS scattering curves at 25 °C (<b>a</b>), Lorentz-corrected SAXS scattering curves during heating process (<b>b</b>), and DSC curves (<b>c</b>) of PU/GTR thermoplastic elastomers.</p>
Full article ">Figure 6
<p>Cole–Cole plots for PU-7 (<b>a</b>) and PU-4 (<b>b</b>).</p>
Full article ">Figure 7
<p>Modeling of experimental stress relaxation curves (<b>a</b>) and relaxation times (<math display="inline"><semantics> <mrow> <msub> <mrow> <mi>τ</mi> </mrow> <mrow> <mn>3</mn> </mrow> </msub> </mrow> </semantics></math>) (<b>b</b>) for PU/GTR thermoplastic elastomers.</p>
Full article ">Scheme 1
<p>The synthesis process of PU/GTR thermoplastic elastomers.</p>
Full article ">
16 pages, 8399 KiB  
Article
The Hydrogen Bonding in the Hard Domains of the Siloxane Polyurea Copolymer Elastomers
by Ming Bao, Tianyu Liu, Ying Tao and Xiuyuan Ni
Polymers 2024, 16(17), 2438; https://doi.org/10.3390/polym16172438 - 28 Aug 2024
Viewed by 355
Abstract
For probing the structure–property relationships of the polyurea elastomers, we synthesize the siloxane polyurea copolymer elastomer by using two aminopropyl-terminated polysiloxane monomers with low and high number-average molecular weight (Mn), i.e., L-30D and H-130D. To study the influence of the [...] Read more.
For probing the structure–property relationships of the polyurea elastomers, we synthesize the siloxane polyurea copolymer elastomer by using two aminopropyl-terminated polysiloxane monomers with low and high number-average molecular weight (Mn), i.e., L-30D and H-130D. To study the influence of the copolymer structures on the film properties, these films are analyzed to obtain the tensile performance, UV-vis spectra, cross-sectional topographies, and glass transition temperature (Tg). The two synthetic thermoplastic elastomer films are characterized by transparency, ductility, and the Tg of the hard domains, depending on the reacting compositions. Furthermore, the film elasticity behavior is studied by the strain recovery and cyclic tensile test, and then, the linear fitting of the tensile data is used to describe the film elasticity based on the Mooney–Rivlin model. Moreover, the temperature-dependent infrared (IR) spectra during heating and cooling are conducted to study the strength and recovery rate of the hydrogen bonding, respectively, and their influence on the film performance is further analyzed; the calculated Mn of the hard segment chains is correlated to the macroscopic recovery rate of the hydrogen bonding. These results can add deep insight to the structure–property relationships of the siloxane polyurea copolymer. Full article
(This article belongs to the Special Issue Advances in Functional Rubber and Elastomer Composites II)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>The FTIR spectra of the siloxane polyurea copolymer using L-30D (<b>a</b>) and H-130D (<b>b</b>).</p>
Full article ">Figure 2
<p>The tensile stress–strain curves of the copolymer films using L-30D (<b>a</b>) and H-130D (<b>b</b>).</p>
Full article ">Figure 3
<p>The loss factor (tan δ) versus temperature of the films using L-30D (<b>a</b>) and H-130D (<b>b</b>).</p>
Full article ">Figure 4
<p>The UV-vis absorption spectra and photos of the films using L-30D (<b>a</b>) and H-130D (<b>b</b>). The characters covered by the films mean Fuand University in Chinese.</p>
Full article ">Figure 5
<p>The cross-sectional topography of SEM for the films using L-30D, the IPDI contents: (<b>a</b>) 11%, (<b>b</b>) 13%, (<b>c</b>) 18%.</p>
Full article ">Figure 6
<p>The cross-sectional topography of SEM for the films using H-130D, the IPDI contents: (<b>a</b>) 11%, (<b>b</b>) 13%, (<b>c</b>) 18%.</p>
Full article ">Figure 7
<p>The cyclic tensile curves of the samples: (<b>a</b>) L-30D-11%, (<b>b</b>) L-30D-18%, (<b>c</b>) H-130D-11%, and (<b>d</b>) H-130D-18%.</p>
Full article ">Figure 8
<p>The scatters and fitted lines (dashes) of [<span class="html-italic">f</span><sup>∗</sup>] versus <span class="html-italic">λ</span><sup>−1</sup> for the copolymer films using H-130D (<b>a</b>) and the films by the oligomers of different <span class="html-italic">M<sub>n</sub></span> (<b>b</b>).</p>
Full article ">Figure 9
<p>The FTIR spectra of the carbonyl during heating for the films using H-130D (<b>a</b>) and L-30D (<b>b</b>) at the IPDI content of 18%. (<b>c</b>) The fitting example of carbonyl peaks in IR spectra for the films. (<b>d</b>) The area percentage of free carbonyl peaks at rising temperatures for these samples.</p>
Full article ">Figure 10
<p>The FTIR spectra of the carbonyls during cooling for the films using H-130D, the IPDI contents: (<b>a</b>) 11%; (<b>b</b>) 13%. The recovery percentage curves (<b>c</b>) and the recovery rate (<b>d</b>) of the carbonyl peaks for the films using various IPDI contents.</p>
Full article ">Figure 11
<p>The FTIR spectra of the carbonyls during cooling for the films using L-30D (<b>a</b>) and H-130D (<b>b</b>). The recovery percentage curves (<b>c</b>) and the recovery rate (<b>d</b>) for the carbonyl peaks of these films.</p>
Full article ">Scheme 1
<p>The schematic representation of the synthesis of siloxane polyurea copolymers using aminopropyl-terminated PDMS.</p>
Full article ">
15 pages, 2239 KiB  
Article
Elastomeric Compositions of Ethylene–Norbornene Copolymer Containing Biofillers Based on Coffee and Tea Waste
by Aneta Malicka, Kamila Rułka, Malgorzata Latos-Brozio and Anna Masek
Materials 2024, 17(16), 4160; https://doi.org/10.3390/ma17164160 - 22 Aug 2024
Viewed by 562
Abstract
The development of eco-friendly elastomeric materials has become an important issue in recent years. In this work, thermoplastic elastomer samples of an ethylene–norbornene copolymer (EN) with coffee and tea biofillers mixed with typical fillers such as montmorillonite (MMT), silica (SiO2), and [...] Read more.
The development of eco-friendly elastomeric materials has become an important issue in recent years. In this work, thermoplastic elastomer samples of an ethylene–norbornene copolymer (EN) with coffee and tea biofillers mixed with typical fillers such as montmorillonite (MMT), silica (SiO2), and cellulose were investigated. The aim of this research was to determine the effect of fillers on the properties of the materials and to assess their degradability after two ultraviolet (UV) aging cycles (200, 400 h). The scientific novelty of this work is the assessment of the anti-aging effect of simultaneous biofillers–stabilizers based on coffee and tea waste. The surfaces of the obtained polymer compositions were examined using infrared spectroscopy (FTIR-ATR). Contact angles were determined, and surface energy was calculated. The mechanical properties were tested, and the influence of plant fillers and aging on the color change in the materials was analyzed. The combination of coffee with silica, MMT, and cellulose fillers limited the migration of fatty acids and other compounds from the biofiller to the EN surface (FTIR analysis). Based on the aging coefficients K, it was shown that all coffee- and tea-based fillers stabilized the polymer compositions during UV aging (400 h). The results allowed the authors to determine the importance and impact of waste plant fillers on the degradability of the synthetic EN. Full article
(This article belongs to the Special Issue New Advances in Elastomer Materials and Its Composites)
Show Figures

Figure 1

Figure 1
<p>Carbonyl indices (CIs) of EN samples with fillers after 200 h and 400 h of UV aging.</p>
Full article ">Figure 2
<p>Polar (<b>A</b>) and dispersive (<b>B</b>) components, and surface free energy (<b>C</b>) of the EN composition with fillers before and after 200 h and 400 h of UV aging.</p>
Full article ">Figure 3
<p>Tensile strength (TS) (<b>A</b>) and elongation at break (Eb) (<b>B</b>) of samples before and after UV aging, and aging coefficients K (<b>C</b>) of EN materials.</p>
Full article ">Figure 4
<p>Change in color parameters after 200 h and 400 h of UV aging: color change coefficient ΔE (<b>A</b>), whiteness index (<b>B</b>), saturation (<b>C</b>), and hue angle (<b>D</b>).</p>
Full article ">Figure 5
<p>Photos of EN samples using a camera before and after 200 h and 400 h of UV aging.</p>
Full article ">
15 pages, 4010 KiB  
Article
Synthesis of High-Molecular-Weight Polypropylene Elastomer by Propylene Polymerization Using α-Diimine Nickel Catalysts
by Lujie Gao, Hegang Ren, Yanhui Hou, Linlin Ye, Hao Meng, Binyuan Liu and Min Yang
Polymers 2024, 16(16), 2376; https://doi.org/10.3390/polym16162376 - 22 Aug 2024
Viewed by 503
Abstract
The α-diimine late transition metal catalyst represents a new strategy for the synthesis of atactic polypropylene elastomer. Taking into account the properties of the material, enhancing the molecular weight of polypropylene at an elevated temperature through modifying the catalyst structure, and further increasing [...] Read more.
The α-diimine late transition metal catalyst represents a new strategy for the synthesis of atactic polypropylene elastomer. Taking into account the properties of the material, enhancing the molecular weight of polypropylene at an elevated temperature through modifying the catalyst structure, and further increasing the activity of α-diimine catalyst for propylene polymerization, are urgent problems to be solved. In this work, two α-diimine nickel(II) catalysts with multiple hydroxymethyl phenyl substituents were synthesized and used for propylene homopolymerization. The maximum catalytic activity was 5.40 × 105 gPP/molNi·h, and the activity was still maintained above 105 gPP/molNi·h at 50 °C. The large steric hindrance of catalysts inhibited the chain-walking and chain-transfer reactions, resulting in polypropylene with high molecular weights (407~1101 kg/mol) and low 1,3-enchainment content (3.57~16.96%) in toluene. The low tensile strength (0.3~1.0 MPa), high elongation at break (218~403%) and strain recovery properties (S.R. ~50%, 10 tension cycles) of the resulting polypropylenes, as well as the visible light transmittance of approximately 90%, indicate the characteristics of the transparent elastomer. Full article
(This article belongs to the Special Issue Polyolefin: Synthesis, Properties, and Characterization)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>GPC curves of resultant polypropylenes: (<b>a</b>) Entries 2, 4, 5, 6; (<b>b</b>) Entries 12, 14, 15, 16.</p>
Full article ">Figure 2
<p><sup>13</sup>C NMR spectra of polypropylenes (Entries 2, 4, 5, 6, 12).</p>
Full article ">Figure 3
<p>DSC curves of polypropylenes: (<b>a</b>) Entries 2, 12; (<b>b</b>) Entries 2, 4, 5, 6; (<b>c</b>) Entries 12, 14, 15, 16.</p>
Full article ">Figure 4
<p>(<b>a</b>) Stress–strain curves for polypropylenes (Entries 2, 5, 6); (<b>b</b>) Plots of hysteresis experiments of 10 cycles at a strain of 100% for polypropylene (Entry 2).</p>
Full article ">Figure 5
<p>UV-vis transmittance curves for polypropylenes (Entries 2, 5, 6).</p>
Full article ">Scheme 1
<p>α-Diimine nickel(II) catalysts in this work.</p>
Full article ">Scheme 2
<p>Synthesis process of complexes <b>C1</b> and <b>C2</b>.</p>
Full article ">
20 pages, 4725 KiB  
Article
A Light-Powered Self-Circling Slider on an Elliptical Track with a Liquid Crystal Elastomer Fiber
by Lu Wei, Yanan Chen, Junjie Hu, Xueao Hu, Jiale Wang and Kai Li
Polymers 2024, 16(16), 2375; https://doi.org/10.3390/polym16162375 - 22 Aug 2024
Viewed by 501
Abstract
In this paper, we propose an innovative light-powered LCE-slider system that enables continuous self-circling on an elliptical track and is comprised of a light-powered LCE string, slider, and rigid elliptical track. By formulating and solving dimensionless dynamic equations, we explain static and self-circling [...] Read more.
In this paper, we propose an innovative light-powered LCE-slider system that enables continuous self-circling on an elliptical track and is comprised of a light-powered LCE string, slider, and rigid elliptical track. By formulating and solving dimensionless dynamic equations, we explain static and self-circling states, emphasizing self-circling dynamics and energy balance. Quantitative analysis reveals that the self-circling frequency of LCE-slider systems is independent of the initial tangential velocity but sensitive to light intensity, contraction coefficients, elastic coefficients, the elliptical axis ratio, and damping coefficients. Notably, elliptical motion outperforms circular motion in angular velocity and frequency, indicating greater efficiency. Reliable self-circling under constant light suggests applications in periodic motion fields, especially celestial mechanics. Additionally, the system’s remarkable adaptability to a wide range of curved trajectories exemplifies its flexibility and versatility, while its energy absorption and conversion capabilities position it as a highly potential candidate for applications in robotics, construction, and transportation. Full article
(This article belongs to the Special Issue Polymer Materials for Sensors and Actuators)
Show Figures

Figure 1

Figure 1
<p>Diagram of a light-powered self-circling device on a plane including the LCE fiber, sliding element, and fixed elliptical track: (<b>a</b>) Initial state; (<b>b</b>) Current state; and (<b>c</b>) Force analysis. Under constant light exposure, the slider equipped with the LCE fiber achieves autonomous, sustained, and periodic movement along the elliptical track.</p>
Full article ">Figure 2
<p>Two motion regimes of the system under continuous light exposure: static state and self-circling state. (<b>a</b>,<b>b</b>) Time-dependent diagram of angular displacement at <math display="inline"><semantics> <mrow> <mover> <mi>I</mi> <mo>-</mo> </mover> <mo>=</mo> <mn>0.1</mn> </mrow> </semantics></math>; (<b>c</b>) Angular velocity dependence on angular displacement at <math display="inline"><semantics> <mrow> <mover> <mi>I</mi> <mo>-</mo> </mover> <mo>=</mo> <mn>0.1</mn> </mrow> </semantics></math>; (<b>d</b>,<b>e</b>) Time-dependent diagram of angular displacement at <math display="inline"><semantics> <mrow> <mover> <mi>I</mi> <mo>-</mo> </mover> <mo>=</mo> <mn>0.3</mn> </mrow> </semantics></math>; (<b>f</b>) Angular velocity dependence on angular displacement <math display="inline"><semantics> <mrow> <mover> <mi>I</mi> <mo>-</mo> </mover> <mo>=</mo> <mn>0.3</mn> </mrow> </semantics></math>.</p>
Full article ">Figure 3
<p>Self-circling mechanism of the system. (<b>a</b>) Time-dependent curve of angular displacement; (<b>b</b>) Time-dependent curve of the number fraction of <span class="html-italic">cis</span>-<span class="html-italic">isomers</span> in the LCE fiber; (<b>c</b>) Time-dependent curve of tangential tension in the LCE fiber; (<b>d</b>) Time-dependent curve of damping force; (<b>e</b>) Variation of tangential tension in the LCE fiber with respect to the angular displacement; (<b>f</b>) Variation of damping force with respect to angular displacement. The yellow squares in the figure denote illuminated region.</p>
Full article ">Figure 4
<p>The effect of light intensity on the self-circling frequency. (<b>a</b>) Depictions of limit cycles at <math display="inline"><semantics> <mrow> <mover> <mi>I</mi> <mo>-</mo> </mover> <mo>=</mo> <mn>0.3</mn> </mrow> </semantics></math>,<math display="inline"><semantics> <mrow> <mo> </mo> <mn>0.45</mn> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <mn>0.6</mn> </mrow> </semantics></math>. (<b>b</b>) Self-circling frequency variations with light intensities.</p>
Full article ">Figure 5
<p>The effect of the contraction coefficient on the self-circling frequency. (<b>a</b>) Depictions of limit cycles at <math display="inline"><semantics> <mrow> <mi>C</mi> <mo>=</mo> <mn>0.3</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <mn>0.35</mn> <mo>,</mo> <mo> </mo> </mrow> </semantics></math>and <math display="inline"><semantics> <mrow> <mn>0.4</mn> </mrow> </semantics></math>. (<b>b</b>) Self-circling frequency variations with the contraction coefficient.</p>
Full article ">Figure 6
<p>The effect of the elastic coefficient on the self-circling frequency. (<b>a</b>) Depictions of limit cycles at <math display="inline"><semantics> <mrow> <mover accent="true"> <mi>K</mi> <mo>¯</mo> </mover> <mo>=</mo> <mn>0.7</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <mn>1.0</mn> <mo>,</mo> <mo> </mo> </mrow> </semantics></math>and <math display="inline"><semantics> <mrow> <mn>1.3</mn> </mrow> </semantics></math>. (<b>b</b>) Self-circling frequency variations with the elastic coefficient.</p>
Full article ">Figure 7
<p>The effect of the initial tangential velocity on the self-circling frequency. (<b>a</b>) Depictions of limit cycles at <math display="inline"><semantics> <mrow> <mover accent="true"> <mrow> <msub> <mi>v</mi> <mn>0</mn> </msub> </mrow> <mo stretchy="true">¯</mo> </mover> <mo>=</mo> <mn>0.9</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <mn>1.2</mn> <mo> </mo> </mrow> </semantics></math>and <math display="inline"><semantics> <mrow> <mn>1.5</mn> </mrow> </semantics></math>. (<b>b</b>) Self-circling frequency variations with initial tangential velocity.</p>
Full article ">Figure 8
<p>The effect of damping coefficients on the self-circling frequency. (<b>a</b>) Depictions of limit cycles at <math display="inline"><semantics> <mrow> <mover accent="true"> <mrow> <msub> <mi>β</mi> <mn>1</mn> </msub> </mrow> <mo stretchy="true">¯</mo> </mover> <mo>=</mo> <mn>0.006</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <mn>0.007</mn> <mo>,</mo> <mo> </mo> </mrow> </semantics></math>and <math display="inline"><semantics> <mrow> <mn>0.008</mn> </mrow> </semantics></math>. (<b>b</b>) Self-circling frequency variations with the first-order damping coefficient <math display="inline"><semantics> <mrow> <msub> <mi>β</mi> <mn>1</mn> </msub> </mrow> </semantics></math>. (<b>c</b>) Depictions of limit cycles at <math display="inline"><semantics> <mrow> <mover accent="true"> <mrow> <msub> <mi>β</mi> <mn>2</mn> </msub> </mrow> <mo stretchy="true">¯</mo> </mover> <mo>=</mo> <mn>0.0003</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <mn>0.0006</mn> <mo>,</mo> <mo> </mo> </mrow> </semantics></math>and <math display="inline"><semantics> <mrow> <mn>0.0009</mn> </mrow> </semantics></math>. (<b>d</b>) Self-circling frequency variations with the second-order damping coefficient <math display="inline"><semantics> <mrow> <msub> <mi>β</mi> <mn>2</mn> </msub> </mrow> </semantics></math>.</p>
Full article ">Figure 9
<p>The effect of the elliptical semi-major axis on the self-circling frequency. (<b>a</b>) Depictions of limit cycles at <math display="inline"><semantics> <mrow> <mover accent="true"> <mi>a</mi> <mo>¯</mo> </mover> <mo>=</mo> <mn>1.92</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <mn>2.00</mn> <mo>,</mo> <mo> </mo> </mrow> </semantics></math>and <math display="inline"><semantics> <mrow> <mn>2.08</mn> </mrow> </semantics></math>. (<b>b</b>) Self-circling frequency variations with elliptical semi-major axis.</p>
Full article ">Figure 10
<p>The effect of the elliptical semi-minor axis on the self-circling frequency. (<b>a</b>) Depictions of limit cycles at <math display="inline"><semantics> <mrow> <mover accent="true"> <mi>b</mi> <mo>¯</mo> </mover> <mo>=</mo> <mn>1.84</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <mn>1.90</mn> <mo>,</mo> <mo> </mo> </mrow> </semantics></math>and <math display="inline"><semantics> <mrow> <mn>1.96</mn> </mrow> </semantics></math>. (<b>b</b>) Self-circling frequency variations with elliptical semi-minor axis.</p>
Full article ">
17 pages, 8054 KiB  
Article
Soft Gripping Fingers Made of Multi-Stacked Dielectric Elastomer Actuators with Backbone Strategy
by Armin Jamali, Robert Knoerlein, Dushyant Bhagwan Mishra, Seyed Alireza Sheikholeslami, Peter Woias and Frank Goldschmidtboeing
Biomimetics 2024, 9(8), 505; https://doi.org/10.3390/biomimetics9080505 - 21 Aug 2024
Viewed by 544
Abstract
Soft grippers, a rapidly growing subfield of soft robotics, utilize compliant and flexible materials capable of conforming to various shapes. This feature enables them to exert gentle yet, if required, strong gripping forces. In this study, we elaborate on the material selection and [...] Read more.
Soft grippers, a rapidly growing subfield of soft robotics, utilize compliant and flexible materials capable of conforming to various shapes. This feature enables them to exert gentle yet, if required, strong gripping forces. In this study, we elaborate on the material selection and fabrication process of gripping fingers based on the dielectric elastomer actuation technique. We study the effects of mixing the silicone elastomer with a silicone thinner on the performance of the actuators. Inspired by nature, where the motion of end-effectors such as soft limbs or fingers is, in many cases, directed by a stiff skeleton, we utilize backbones for translating the planar actuation into a bending motion. Thus, the finger does not need any rigid frame or pre-stretch, as in many other DEA approaches. The idea and function of the backbone strategy are demonstrated by finite element method simulations with COMSOL Multiphysics® 6.5. The paper describes the full methodology from material choice and characterization, design, and simulation to characterization to enable future developments based on our approach. Finally, we present the performance of these actuators in a gripper demonstrator setup. The developed actuators bend up to 68.3° against gravity, and the gripper fingers hold up to 10.3 g against gravity under an actuation voltage of 8 kV. Full article
(This article belongs to the Special Issue Bioinspired Structures for Soft Actuators: 2nd Edition)
Show Figures

Figure 1

Figure 1
<p>Actuation mechanism of a DEA. The Maxwell stress caused by the high voltage compresses the dielectric in thickness and expands its area.</p>
Full article ">Figure 2
<p>Dog-bone sample molded with Ecoflex™ elastomers for the stress–strain test. The height of the samples is 3 mm.</p>
Full article ">Figure 3
<p>Mechanical behavior of the elastomers: (<b>a</b>) the stress–strain curves for Ecoflex 10T and Ecoflex 30 over compressive and tensile strains, and (<b>b</b>) comparing the elastic modulus of the silicones to study the effect of silicone thinner on Ecoflex 10.</p>
Full article ">Figure 4
<p>Housing used for molding, curing, and measuring the capacitance of the elastomers: (<b>a</b>) the 3D model of the housing, and (<b>b</b>) a drawing of the cross-section of the housing illustrating the dimensions of the cured specimen and the measurement electrodes.</p>
Full article ">Figure 5
<p>Relative permittivity of the elastomers for frequencies up to 100 kHz.</p>
Full article ">Figure 6
<p>Cross-section of a sample fabricated to compare the electrode layer made of dry-brushed carbon black versus the electrode layer made of a mixture of Ecoflex 10 and carbon black.</p>
Full article ">Figure 7
<p>Bending mechanism of a DEA bending finger: (<b>a</b>) initial state, and (<b>b</b>) final state.</p>
Full article ">Figure 8
<p>The structured mesh used for simulating the DEA bending fingers. The dimensions of the finger are 45 mm × 25 mm with layer thicknesses of 800 µm for the passive layer (Ecoflex 30), 500 µm for the PMMA backbones, 50 µm for each passive layer (Ecoflex 30), and 550 µm for each active layer (Ecoflex 10T). The electrodes cover the full area excluding the bearing with a 200 µm isolation frame to avoid spark discharge.</p>
Full article ">Figure 9
<p>Simulation results for DEA fingers with one to five active layers: (<b>a</b>) simulated DEA fingers at 8 kV with maximum strains of 9.7%, 17.7%, 24.1%, 29.3%, and 33.2% from left to right, and (<b>b</b>) bending angle <span class="html-italic">β</span> vs. electrical field strength.</p>
Full article ">Figure 10
<p>Layer-by-layer fabrication step for manufacturing DEA bending fingers with one active layer: (a) PMMA substrate, (b) first passive elastomer layer, (c) first patterned dry-brushed carbon black electrode layer (25 mm × 20 mm), (d) active elastomer layer, (e) second patterned dry-brushed carbon black electrode layer (25 mm × 20 mm), (f) second passive electrode layer, (g) PMMA backbone structure, and (h) final passive elastomer layer that holds the backbone structure in place.</p>
Full article ">Figure 11
<p>Photographs of DEA bending finger actuators: (<b>a</b>) top view indicating the area where the transparent PMMA backbone sheets are placed, and (<b>b</b>) side view to compare the actuators with one versus five active layers.</p>
Full article ">Figure 12
<p>A hanging DEA bending finger with 2 active layers: (<b>a</b>) under no actuation voltage, (<b>b</b>) bending under 8 kV, and (<b>c</b>) bending angle of DEA bending fingers with one to five active layers.</p>
Full article ">Figure 13
<p>Gripping setup: (<b>a</b>) two DEA finger actuators bending towards each other hanging from a linear stage, where d = 11 mm, D = 55 mm, and h = 14 mm, (<b>b</b>) DEA gripping fingers grabbing, and (<b>c</b>) lifting a basket.</p>
Full article ">Figure 14
<p>Increasing the number of active elastomer layers without increasing the overall thickness of the gripping finger: (<b>a</b>) a gripping finger with one thick (550 µm) active layer driven by 8 kV, and (<b>b</b>) a gripping finger with ten thin (55 µm) active layers with the same overall thickness but driven with only 800 V. The bending behavior of both actuators is theoretically the same.</p>
Full article ">Figure 15
<p>Experimental and simulated bending angles versus electrical field (<b>a</b>) for one and two layers, and (<b>b</b>) for three to five layers.</p>
Full article ">
24 pages, 8062 KiB  
Review
Research Status of Lignin-Based Polyurethane and Its Application in Flexible Electronics
by Jingbo Hu, Mengmeng Huang, Xing Zhou, Rubai Luo, Lu Li and Xiaoning Li
Polymers 2024, 16(16), 2340; https://doi.org/10.3390/polym16162340 - 19 Aug 2024
Viewed by 958
Abstract
Polyurethanes (PU) have drawn great attention due to their excellent mechanical properties and self-healing and recyclable abilities. Lignin is a natural and renewable raw material in nature, composed of a large number of hydroxyl groups, and has a great potential to replace petroleum [...] Read more.
Polyurethanes (PU) have drawn great attention due to their excellent mechanical properties and self-healing and recyclable abilities. Lignin is a natural and renewable raw material in nature, composed of a large number of hydroxyl groups, and has a great potential to replace petroleum polyols in PU synthesis. This review summarizes the recent advances in modification methods such as the liquefaction, alkylation, and demethylation of lignin, and a systematic analysis of how to improve the reactivity and monomer substitution of lignin during polyurethane synthesis for the green manufacturing of high-performance polyurethanes was conducted. Polyurethane can be used in the form of films, foams, and elastomers instead of conventional materials as a dielectric or substrate material to improve the reliability and durability of flexible sensors; this review summarizes the green synthesis of polyurethanes and their applications in flexible electronics, which are expected to provide inspiration for the wearable electronics sector. Full article
(This article belongs to the Section Biobased and Biodegradable Polymers)
Show Figures

Figure 1

Figure 1
<p>PU synthesis path. (<b>A</b>) Overview of the main synthetic routes to Pus [<a href="#B35-polymers-16-02340" class="html-bibr">35</a>]. (<b>B</b>) Reaction mechanism of lignin and diisocyanate (diisocyanate takes TDI (Toluene-2,4-diisocyanate) as an example) [<a href="#B39-polymers-16-02340" class="html-bibr">39</a>].</p>
Full article ">Figure 2
<p>Preparation and properties of lignin-based polyurethane. (<b>A</b>) The preparation, scale-up, and degradation of the lignin-based polyurethane foams (the foam is about 30 cm in diameter) [<a href="#B31-polymers-16-02340" class="html-bibr">31</a>]. (<b>B</b>) The degradation of LPUF30-1 in 2 mol/L NaOH aqueous solution for 10 h at different temperatures, and the corresponding photos of the experiments [<a href="#B31-polymers-16-02340" class="html-bibr">31</a>]. (<b>C</b>) Illustration of the preparation of lignin and bio-polyols [<a href="#B53-polymers-16-02340" class="html-bibr">53</a>]. (<b>D</b>) Molecular weight distribution of the liquefied bio-polyols [<a href="#B41-polymers-16-02340" class="html-bibr">41</a>].</p>
Full article ">Figure 3
<p>Alkylation modification of lignin. (<b>A</b>) Hydromethylation of the phenolic ring of a lignin unit (guaiacol type) [<a href="#B44-polymers-16-02340" class="html-bibr">44</a>]. (<b>B</b>) 31<sup>P</sup> NMR spectra of OKL and KL in CDCl<sub>3</sub> with NHND as an internal standard. Polyalkylation condition of OKL: 60 wt.% PEG400, 20 wt.% lignin loading, 170 °C for 30 min [<a href="#B59-polymers-16-02340" class="html-bibr">59</a>]. (<b>C</b>) Tensile stress-strain curves of the obtained LPUs [<a href="#B61-polymers-16-02340" class="html-bibr">61</a>]. (<b>D</b>) Photos of the bare CS and LPU coatings after the short-term corrosion resistance test [<a href="#B61-polymers-16-02340" class="html-bibr">61</a>].</p>
Full article ">Figure 4
<p>Acetylation modification of lignin. (<b>A</b>) Kraft lignin partial acetylation reaction with acetic anhydride scheme [<a href="#B49-polymers-16-02340" class="html-bibr">49</a>]. (<b>B</b>) SEM images of KLPU foam with KL content of 10 wt.% at different magnifications [<a href="#B66-polymers-16-02340" class="html-bibr">66</a>]. (<b>C</b>) Recycle number and time, showing reusability and sorption kinetics of the sorbent, respectively [<a href="#B66-polymers-16-02340" class="html-bibr">66</a>].</p>
Full article ">Figure 5
<p>(<b>A</b>) ①: Bamboo lignin is demethylated. ②: The L2 lignin is modified by 6-bromo-1-hexene [<a href="#B69-polymers-16-02340" class="html-bibr">69</a>]. (<b>B</b>) Lap shear strength of PSAs [<a href="#B69-polymers-16-02340" class="html-bibr">69</a>]. (<b>C</b>) The comparison of tensile strength of PU adhesives among this paper and some studies [<a href="#B39-polymers-16-02340" class="html-bibr">39</a>]. (<b>D</b>) Steps for sequential solvent fractionation of lignin [<a href="#B29-polymers-16-02340" class="html-bibr">29</a>]. (<b>E</b>) Mechanical properties of the RPFs, the apparent density, and the compressive strength of the foams [<a href="#B74-polymers-16-02340" class="html-bibr">74</a>].</p>
Full article ">Figure 6
<p>(<b>A</b>) Schematic diagram of the spider silk spatial hierarchy [<a href="#B18-polymers-16-02340" class="html-bibr">18</a>]. (<b>B</b>) Optical images of MLPU-2 film at different repairing times at 80 °C [<a href="#B18-polymers-16-02340" class="html-bibr">18</a>].</p>
Full article ">Figure 7
<p>Application of tactile sensing based on the SFF-STENG in the Internet of Things by WLAN [<a href="#B83-polymers-16-02340" class="html-bibr">83</a>]. (<b>a</b>) Working diagram of a tactile sensing control system. A press signal trigged by tactile sensing can control the appliances by some electric modules. (<b>b</b>) Optical photographs of components of the tactile sensing control system for the drone movement control. (<b>c</b>) The SFF-STENG generates original triboelectric voltage input and output signal after rectification. (<b>d</b>) Voltage waveform diagram of a tactile sensor based on the SFF-STENG by fingertips touch. (<b>e</b>) Tactile sensing test based on SFF-STENG by fingertips press. (<b>f</b>) Tactile signal for the drone movement in (i) forward/backward/left/right direction, (ii) up/down direction, and (iii) right rotation. (<b>g</b>) Diagram of the drone movements.</p>
Full article ">Figure 8
<p>(<b>A</b>) Schematic representation of the preparation and degradation of superhydrophobic 0.04F-LPUF foam adsorbent and photograph of 0.04F-LPUF degradation over time in aqueous sodium hydroxide solution in methanol [<a href="#B88-polymers-16-02340" class="html-bibr">88</a>]. (<b>B</b>) Schematic illustration of the fabrication process of the MWCNTs @ LPUF sensor [<a href="#B93-polymers-16-02340" class="html-bibr">93</a>]. (<b>a</b>–<b>c</b>) Degradation of MWCNTs @ LPUF sensors at 0–3 h.</p>
Full article ">Figure 9
<p>(<b>A</b>) Shape memory effect based on the photothermal conversion capability of LPUs [<a href="#B95-polymers-16-02340" class="html-bibr">95</a>]. (<b>B</b>) Self-healing process of lignin self-healing polyurethane [<a href="#B96-polymers-16-02340" class="html-bibr">96</a>]. (<b>C</b>) Ultraviolet transmittance curve [<a href="#B98-polymers-16-02340" class="html-bibr">98</a>]. (<b>D</b>) Photographs showing the restoration of a closed conduction circuit containing an LED after PU-NM1-CNT3 cutting and healing (the illustration is a schematic diagram of the circuit) [<a href="#B100-polymers-16-02340" class="html-bibr">100</a>].</p>
Full article ">Figure 10
<p>Instantaneous output voltage signal of several wave periods obtained from the FFNG-based wave sensor and instantaneous wave height versus wave frequency and output peak voltage [<a href="#B102-polymers-16-02340" class="html-bibr">102</a>]. (<b>a</b>) Photograph of a 12-cm-long FFNG woven from three T40/L60 fibers (<b>b</b>) The output voltage generated by FFNG-1 and FFNG-3 with a contact length of 6 cm in 0.6molL-1 NaCl solution. (<b>c</b>) Plots of charged voltages across a 10 μF capacitor in FFNG-1 and FFNG-3. (<b>d</b>) Schematic diagram of the ocean wave monitoring device. (<b>e</b>) Instantaneous output voltage signal of several wave periods obtained from the FFNG-based wave sensor. (<b>f</b>) Instantaneous wave height versus wave frequency and output peak voltage.</p>
Full article ">Figure 11
<p>Lignin-based polyurethanes for wearable flexible electronics applications. (<b>A</b>) Detection of human physiological signals: frown; say Hahaha; pulse at relaxation and excitation; finger; elbow; knee [<a href="#B103-polymers-16-02340" class="html-bibr">103</a>]. (<b>B</b>) Peeling off the hydrogel film without any attached hair and without any pain [<a href="#B104-polymers-16-02340" class="html-bibr">104</a>].</p>
Full article ">
11 pages, 1506 KiB  
Article
Color Modifications of a Maxillofacial Silicone Elastomer under the Effect of Cigarette Smoke
by Anca Irina Gradinariu, Alexandru-Constantin Stoica, Alexandra Bargan, Carmen Racles, Carmen Gabriela Stelea and Victor Vlad Costan
Materials 2024, 17(16), 4089; https://doi.org/10.3390/ma17164089 - 17 Aug 2024
Viewed by 398
Abstract
Although it is known (from the observations of medical professionals) that cigarette smoke negatively affects maxillofacial prostheses, especially through staining/discoloration, systematic research in this regard is limited. Herein, the color modifications of M511 maxillofacial silicone, unpigmented and pigmented with red or skin tone [...] Read more.
Although it is known (from the observations of medical professionals) that cigarette smoke negatively affects maxillofacial prostheses, especially through staining/discoloration, systematic research in this regard is limited. Herein, the color modifications of M511 maxillofacial silicone, unpigmented and pigmented with red or skin tone pigments, covered with mattifiers, or with makeup and mattifiers, and directly exposed to cigarette smoke, were investigated by spectrophotometric measurements in the CIELab and RGB color systems. The changes in color parameters are comparatively discussed, showing that the base silicone material without pigmentation and coating undergoes the most significant modifications. Visible and clinically unacceptable changes occurred after direct exposure to only 20 cigarettes. By coating and application of makeup, the material is more resistant to color changes, which suggests that surface treatments provide increased protection to adsorption of the smoke components. The dynamic water vapor sorption (DVS) measurements indicate a decrease of the sorption capacity in pigmented versus unpigmented elastomers, in line with the changes in color parameters. Full article
(This article belongs to the Special Issue Advances in Biomaterials: Synthesis, Characteristics and Applications)
Show Figures

Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>Dynamic vapor sorption isotherms of uncoated samples (“s” stands for sorption and “d” for desorption branch).</p>
Full article ">Figure 2
<p>The modification of different color parameters of unpigmented and red samples after being exposed to the smoke of 20 cigarettes.</p>
Full article ">Figure 3
<p>The Pearson correlation matrix for: (<b>A</b>) the CIELab system and (<b>B</b>) RGB system.</p>
Full article ">Scheme 1
<p>Schematic representation of the addition cross-linking, the presumptive structures of the main silicone components in the maxillofacial elastomer, and sample coding.</p>
Full article ">
Back to TopTop