Startseite Experimental evaluation on compression-after-impact behavior of perforated sandwich panel comprised of foam core and glass fiber reinforced epoxy hybrid facesheets
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Experimental evaluation on compression-after-impact behavior of perforated sandwich panel comprised of foam core and glass fiber reinforced epoxy hybrid facesheets

  • Yilin Tu , Xu Li , Hongyuan Huang EMAIL logo , Chen Chen , Gang Liu , Youping Liu und Ye Wu EMAIL logo
Veröffentlicht/Copyright: 19. März 2024
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Abstract

To study the impact response and compression-after-impact (CAI) behavior of perforated sandwich panels comprised of foam core and glass fiber-reinforced epoxy hybrid facesheets, the hole diameter of specimens is changed in the fabrication via vacuum-assisted resin infusion. Furthermore, low-velocity-impact tests with various impact distances between the impact point and hole are carried out. With the help of the digital image correlation technique, CAI testing is conducted, and the strain evolution of specimens is monitored carefully. The mechanical response history, damage morphology, and compressive process are discussed in detail. The results show that the impact and CAI performance of specimens are weakened because of open holes. Compared with the non-perforated specimen, the maximum force of the specimen with a 6-mm hole and the 5-mm impact distance decreases by 41.21%, and its maximum displacement increases by 38.60%. During the CAI process, in comparison with the impact damage, more significant stress concentration and buckling around the hole are found.

Keywords: perforated sandwich panels; low-velocity impact; CAI behavior; damage mode

1 Introduction

Fiber-reinforced polymer composites have been widely used in aerospace, civil engineering, automobiles, and ships in recent years due to their advantages of light weight, high strength, good corrosion resistance, and strong durability (1,2,3,4,5,6). As a new type of composite structure, the sandwich structure has higher specific stiffness and specific strength than traditional composite materials, can meet the needs of lightweight design, and has attracted extensive attention in recent years (7,8,9,10,11). As with most composite structures, impact loading will cause damage on the surface of the sandwich structure that is difficult to observe with the naked eye, and these damages are not easy to find and generally produce defects such as matrix cracking and interlayer delamination inside the structure, which seriously weakens the compressive strength and stiffness of the composite structure and poses a serious threat to the safety of the sandwich panel (12,13,14,15,16). The study on impact damage mechanism of composite sandwich panels is a hot issue in the research field of composite sandwich structures.

Because the composite material is still in service after being damaged, it is beneficial to protect the structural safety by studying the damage mode and failure mechanism of compression after impact (CAI). Extensive scholarly investigations have been dedicated to the examination of the impact resistance and CAI characteristics of composite sandwich structures. Research by Yang et al. (17) indicates that specimens with more severe damage exhibit a significant reduction in residual strength compared to specimens with minor impact damage. Gilioli et al. (18) investigated the residual strength of different laminate sandwich structures after impact. The results indicate that both types of laminate sandwich structures experience a degradation in compression performance after impact. Yang et al. (19) conducted a study on the compression strength of hybrid panel sandwich structures after impact. The research revealed that, following the occurrence of an impact event, the compressive strength can decrease by up to 50%. The research conducted by Wu and Wan (20) on shape memory alloy composite material foam sandwich panels after impact indicates that the sandwich panel experiences initial delamination in the impact zone. As the delamination extends along the interface between the face and core layers, the sandwich panel progressively loses its ability to bear loads. Gordon et al. (21) investigated the compression strength of glass fiber composite foam sandwich panels at varying impact energy levels. The results indicate a nearly linear decline in CAI strength with increasing impact energy. Notably, under higher energy impacts, the sandwich panel experienced a substantial reduction of up to 40% in residual strength. In their study, Elamin et al. (22) explored the impact and CAI characteristics of carbon fiber composite foam sandwich panels under low-temperature conditions. The findings indicate that with decreasing temperature, the compressive strength of non-impacted sandwich panels shows an increase. Conversely, for sandwich panels exposed to higher energy impacts, there is a notable decline in residual strength.

In practical engineering applications, there is often a need for complex structural configurations. Due to the requirements of structural connections and subsequent maintenance (23,24,25,26,27), it is often necessary to introduce perforations in composite sandwich panels in practical engineering applications. However, this practice can lead to structural damage as it disrupts the continuous fiber arrangement. Stress concentration at the hole edges is a common consequence, making the structure susceptible to failure and risking overall structural integrity. This poses a serious threat to the safety of its engineering applications (28,29,30,31). With the help of commercial software ABAQUS, Liu et al. (32) conducted progressive damage analysis and experiments of open-hole composite laminates subjected to compression loads. As mentioned above, most investigations focus on the open-hole compressive strength of laminates rather than that of sandwich structures. On the other hand, current research primarily emphasizes the impact resistance and CAI characteristics of defect-free composite sandwich structures with diverse fiber types. However, there is a paucity of studies addressing the specific challenges posed by sandwich structures containing perforations or voids.

To investigate the influence of holes on the impact resistance and CAI performance of foam-filled sandwich panels with glass fiber-reinforced epoxy hybrid facesheets, the vacuum-assisted resin infusion (VARI) process is employed to fabricate the specimens with both no-hole and perforated configurations. Furthermore, low-velocity-impact (LVI) and CAI tests are conducted, and their mechanical response is analyzed carefully. Finally, some important conclusions are obtained.

2 Materials and methods

2.1 Raw materials and fabrication

As shown in Figure 1, the sandwich composites composed of two facesheets of 8 GFRP layers (300 g·m−2 of areal density) and a polyamine form (8 mm of thickness, 75 kg·m−3 of density) are manufactured via conventional process of VARI, in which the vinyl ester resin (purchased from Xinxin Plastic Industry, Hebei, China) can fill the room among the woven glass fiber well. With a proper proportion of the hardening agent (methyl ethyl ketone peroxide) and accelerating agent (Dimethylaniline) at a mass ratio of 100:1:0.1, it can be cured at room temperature. All sandwich plates, 10 mm thickness in total, are cut into rectangular samples of 150 mm × 100 mm via a low-speed diamond saw blade cutting machine, and drilled at the center with a penetrable hole of 4/6/8/10 mm diameter. Before the CAI testing, the specimens are cut into a rectangular of 150 mm × 60 mm (Figure 2).

Figure 1 Fabrication of specimens.
Figure 1

Fabrication of specimens.

Figure 2 Experimental setup: (a) the LVI and (b) CAI tests.
Figure 2

Experimental setup: (a) the LVI and (b) CAI tests.

2.2 LVI and post-impact compressive test

Instron CEAST 9340, meeting ASTM D7136, is employed to implement the LVI testing, in which the history including absorbed energy, displacement as well as contact force on the surface of the impactor, 4.5 kg of mass and nose of 16 mm diameter, is recorded. It is worth noting that, to investigate the effect of the distance from the impact point and hole center, the specimens are fixed by four toggle clamps on the impact support fixture base and are subjected to 32-J LVI loading (a speed of 3.77 m·s−1) at various distances of 5/10/15/20/25/30 mm around the hole.

To study the effect of the impact location and hole size, CAI testing is conducted at a speed of 0.5 mm·min−1 on the universal testing machine. During the compressive test, in addition to the history of force and displacement, the strain-contour evolution of post-impact samples is presented with the help of 3-D Digital image correlation (DIC).

3 Results and discussion

3.1 LVI behavior

3.1.1 Comparison of unperforated and perforated specimens

The damage morphology of unperforated sandwich panel specimens and perforated specimens under the LVI test is shown in Figure 3, which includes delamination and fiber breaking on the surface, form cracking, and form debonding in the foam core.

Figure 3 Damage morphology of unperforated/perforated sandwich panels under LVI test.
Figure 3

Damage morphology of unperforated/perforated sandwich panels under LVI test.

In Figure 4, the specimens with the same distances between the edge of the hole and the impact point of 15 mm and four kinds of hole diameters of 4/6/8/10 mm are defined as the hole diameter group. In Figure 5, The specimens with the same hole diameter of 6 mm and five distances between the edge of the hole and the impact point of 5/10/15/20/30 mm are defined as the impact distance group. The specimen is identified as A–B–C, where A is the hole diameter, as well as B represents the distance between the impact point and hole. C stands for impact energy.

Figure 4 Damage morphology of the hole diameter group under the LVI test.
Figure 4

Damage morphology of the hole diameter group under the LVI test.

Figure 5 The typical results of the hole diameter group under LVI tests: (a) contact force–time, (b) contact force–displacement, (c) absorbed energy–time curves, and (d) comparison of both the maximum force and maximum displacement.
Figure 5

The typical results of the hole diameter group under LVI tests: (a) contact force–time, (b) contact force–displacement, (c) absorbed energy–time curves, and (d) comparison of both the maximum force and maximum displacement.

3.1.2 Effect of hole diameter

A comparison of the hole diameter group on damage morphology is shown in Figure 4. In general, fiber breaking between the edge of the holes and the impact points with foam cracking and debonding are observed on the perforated specimens, while delamination and foam debonding on the unperforated specimens. Differing from the upper surface of the perforated specimens, fiber breaking, and delamination areas are not observed on the bottom surface, which signifies that the impact hammer head fails to break through the sandwich panel specimens, indicating that specimens retain a certain amount of residual strength. Moreover, with the diameter of the hole increasing, dents, delamination areas, and fiber breakings are more noticeable. The final failure modes are the crushing of the upper panel matrix with foam core, fiber breakage, and delamination of the upper panel.

The response history, including force–time (F–t), force–displacement (F–d), and absorbed energy–time (E–t) curves, as well as a comparison of both the peak force and displacement of the impact distance group, is shown in detail in Figure 5. Overall, the double peak force and the oscillation after the twice peak can be observed in F–t and F–d curves. Notably, after achieving the initial peak force, the curves decline rapidly. Corresponding with the damage morphology, it indicates the delamination and fiber breaking of the upper surface which is insufficient to support the existing loads. When the foam core is compressed while being in contact with the bottom surface, the curve rises twice to form the second peak, and then oscillation appears. In Figure 5(c), the energy curves show a similar upward trend reaching the energy value set in the LVI test, which indicates that the foam sandwich panel specimens have an excellent energy absorption capability. As is shown in Figure 5(d), with the hole diameter increasing the maximum force declines, while the maximum displacement rises, up to 11.83%.

3.1.3 Effect of impact distance

Three views of the visual damage morphology of the impact distance group are pictured in Figure 6. Overall, in all types of cases, visual delamination area is observed in the contact face, but their bottom surfaces have no impact damage. Furthermore, different degrees of damage are found in the transverse fracture morphology of foam core sandwich panels. It is worth noting that the largest delamination area and fiber breaking at the hole edge are observed in 6-5-32 J, and its foam core bears severe foam cracking and debonding.

Figure 6 Damage morphology of the impact distance group under the LVI test.
Figure 6

Damage morphology of the impact distance group under the LVI test.

The response history, including F–t, F–d, and E–t curves, as well as the comparison of both the peak force and displacement of the impact distance group, is shown in detail in Figure 7, respectively. Overall, the double peak force and a similar trend are observed in F–t and F–d curves of all kinds of cases, but their different maximum force and maximum displacement are shown in Figure 7(d). It is interesting to see the sharp increment and decline around the first peak force, while the flat increment and decline around the second peak force. Combined with the three views of damage morphology, it is clearly indicating the penetration of glass fabric cloth skin. The second force peak is formed by the contact between the impactor and the inner foam core. Contrary to visual damage morphology, all cases suffer invisible fiber breaking because two peak forces are found in the F–t curves. Besides, the increase of maximum force and the decrease of maximum displacement with the increase of impact distance are shown in Figure 7(d). Therefore, the strength and stiffness are improved as the impact point is far away from the hole.

Figure 7 The typical results of the impact distance group under LVI tests: (a) contact force–time, (b) contact force–displacement, (c) absorbed energy–time curves, and (d) comparison on both the maximum force and maximum displacement.
Figure 7

The typical results of the impact distance group under LVI tests: (a) contact force–time, (b) contact force–displacement, (c) absorbed energy–time curves, and (d) comparison on both the maximum force and maximum displacement.

3.2 CAI behavior

3.2.1 Effect of hole diameter

The F–d curves and comparison on both maximum load and CAI strength of the hole diameter are pictured in Figure 8. Overall, a similar trend is observed in F–d curves of all kinds of cases, but there are different peak forces and their displacement at that time. The F–d curve usually shows the behavior in three stages. The first stage is the incomplete contact stage, which is characterized by a non-linear curve. This stage is relatively short because the fixture and the foam sandwich plate fail to contact fully, and the load slowly increases. The second stage is the axial compression, where the load increases linearly with displacement. The slope of the curve decreases as the load approaches the peak load, and then, the specimen buckles and fails. The last stage is the buckling failure stage, where the displacement continues to increase, and the load begins to decrease as the specimen buckles and incurs damage. It is worth noting to see the sharp increment and decline around the peak force, while a certain bearing capacity after peak force is observed. The maximum force and CAI strength increase with the increase in hole diameter are shown in Figure 8(b).

Figure 8 (a) Contact force–displacement curves and (b) comparison of both the maximum load and CAI strength of the hole diameter group in the CAI test.
Figure 8

(a) Contact force–displacement curves and (b) comparison of both the maximum load and CAI strength of the hole diameter group in the CAI test.

When the peak force is reached, the compression morphology of the side surface of the hole diameter group is recorded as shown in Figure 9. For 0-15-32 J, 4-15-32 J, and 8-15-32 J, out-of-plane buckling occurs at two positions, buckling to both sides at the hole and impact point, respectively, and their buckling morphology is S-shaped. However, for 6-15-32 J and 10-15-32 J, only one out-of-plane buckling is observed around the hole and the impact point.

Figure 9 Lateral failure morphology of the hole diameter group.
Figure 9

Lateral failure morphology of the hole diameter group.

3.2.2 Effect of impact distance

As is shown in Figure 10, the F–d curves and comparison of both maximum load and CAI strength of the impact distance group are similar to those of the hole diameter group. It is easy to find the maximum force, CAI strength, and displacement at peak force increase with the impact distance. Furthermore, for the specimens subjected to the impact with an impact distance larger than 15 mm, their CAI strength drop is very small as shown in Figure 8(b). Therefore, if the impact position is too close to the hole, the CAI strength will be greatly reduced, such as in the specimen with a 6 mm hole and a 5 mm impact distance.

Figure 10 (a) Contact force–displacement curves and (b) comparison of both the maximum load and CAI strength of the impact distance group in the CAI test.
Figure 10

(a) Contact force–displacement curves and (b) comparison of both the maximum load and CAI strength of the impact distance group in the CAI test.

In conjunction with Figures 10 and 11, as the load increases, the foam sandwich panel specimens initially compress axially. At peak load, the middle of the specimens experiences local buckling in an S-shape. Moreover, the larger strains occur at the edge of the hole and the point of impact. For 6-10-32 J, out-of-plane buckling at two positions, including the hole and impact point, is found clearly. However, for the last specimens, only one out-of-plane buckling is observed around the hole and the impact point.

Figure 11 Lateral failure morphology of the impact distance group.
Figure 11

Lateral failure morphology of the impact distance group.

3.2.3 Comparison of all cases of strain contour

The damage evolution of the virgin specimen and the impacted and open-hole specimen in compression tests, including A–E stages corresponding to their curves, are compared with strain contour in 0° direction in Figure 12. For non-perforated and non-impact specimens, the compressive strain concentration is first in the middle, and then, the specimen is stretched on the upper part and compressed on the lower part. For 6-15-32 J, from moment C to moment E in the F–d curve, the strain around the hole and impact damage changes compressive strain to tensile stress, and finally, the double ends are compressed.

Figure 12 Typical comparison of (a) unperforated; (b) perforated specimens with strain contour.
Figure 12

Typical comparison of (a) unperforated; (b) perforated specimens with strain contour.

Figure 13 shows the comparison of all kinds of cases on failure contour in 0° direction. Whether the impact distance or the hole diameter groups, the cases with a hole diameter less than 6 mm are compression at the lower end as well as tension around the hole and impact damage. Especially, for 8-15-32 J and 10-15-32 J, the failure mode changes to compression around the hole and tension at the impact damage. The reason is the larger diameter of the hole and the weaker the cross section, as well as the compressive stress concentration is more likely to occur at the hole.

Figure 13 Comparison of all cases of strain contour: (a) the hole diameter group and (b) the impact distance group.
Figure 13

Comparison of all cases of strain contour: (a) the hole diameter group and (b) the impact distance group.

4 Conclusion

The damage mechanism and failure mode of perforated sandwich panels under LVI and CAI loading are investigated based on the typical response history, damage morphology, and strain contour. Therefore, the following conclusions can be drawn:

  1. Open holes and impact distance significantly weaken the impact property. Under the same incident energy of 32 J, compared with the non-perforated specimen, the maximum force of the specimen with a 6 mm hole and the 5 mm impact distance decreases by 41.21%, and its maximum displacement increases by 38.60%.

  2. The impact and CAI performance are obviously decreased as the hole diameter increases. Under the same incident energy of 32 J, compared with the non-perforated specimen, the maximum force and CAI strength of the specimen with a 10 mm hole diameter and 15 mm impact distance decreased by 27.3% and 12.4%, respectively.

  3. The main forms of impact damage are fiber breaking, matrix cracking, interlaminar delamination, and crushing of foam core. In the CAI test, compared with the impact damage, more significant stress concentration and buckling around the hole are found. However, owing to the good capability for elastic deformation of sandwich panels, significant face-core delamination is not observed.

Acknowledgments

This work was sponsored by the Foundation of Jiangxi Province of China Educational Committee (GJJ201907, GJJ2201503) and the Innovative Projects of NIT(YC2023-S997, YC2023-S1004).

  1. Funding information: This work was sponsored by the Foundation of Jiangxi Province of China Educational Committee (GJJ201907, GJJ2201503) and the Innovative Projects of NIT(YC2023-S997, YC2023-S1004).

  2. Conflict of interest: Authors state no conflict of interest.

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Received: 2024-02-01
Revised: 2024-02-15
Accepted: 2024-02-15
Published Online: 2024-03-19

© 2024 the author(s), published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 International License.

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  47. Research on microscopic structure–activity relationship of AP particle–matrix interface in HTPB propellant
  48. Three-layered films enable efficient passive radiation cooling of buildings
  49. Electrospun nanofibers membranes of La(OH)3/PAN as a versatile adsorbent for fluoride remediation: Performance and mechanisms
  50. Preparation and characterization of biodegradable polyester fibers enhanced with antibacterial and antiviral organic composites
  51. Preparation of hydrophobic silicone rubber composite insulators and the research of anti-aging performance
  52. Surface modification of sepiolite and its application in one-component silicone potting adhesive
  53. Study on hydrophobicity and aging characteristics of epoxy resin modified with nano-MgO
  54. Optimization of baffle’s height in an asymmetric twin-screw extruder using the response surface model
  55. Effect of surface treatment of nickel-coated graphite on conductive rubber
  56. Experimental investigation on low-velocity impact and compression after impact behaviors of GFRP laminates with steel mesh reinforced
  57. Development and characterization of acetylated and acetylated surface-modified tapioca starches as a carrier material for linalool
  58. Investigation of the compaction density of electromagnetic moulding of poly(ether-ketone-ketone) polymer powder
  59. Experimental investigation on low-velocity-impact and post-impact-tension behaviors of GFRP T-joints after hydrothermal aging
  60. The repeated low-velocity impact response and damage accumulation of shape memory alloy hybrid composite laminates
  61. Exploring a new method for high-performance TPSiV preparation through innovative Si–H/Pt curing system in VSR/TPU blends
  62. Large-scale production of highly responsive, stretchable, and conductive wrapped yarns for wearable strain sensors
  63. Preparation of natural raw rubber and silica/NR composites with low generation heat through aqueous silane flocculation
  64. Molecular dynamics simulation of the interaction between polybutylene terephthalate and A3 during thermal-oxidative aging
  65. Crashworthiness of GFRP/aluminum hybrid square tubes under quasi-static compression and single/repeated impact
  66. Review Articles
  67. Recent advancements in multinuclear early transition metal catalysts for olefin polymerization through cooperative effects
  68. Impact of ionic liquids on the thermal properties of polymer composites
  69. Recent progress in properties and application of antibacterial food packaging materials based on polyvinyl alcohol
  70. Additive manufacturing (3D printing) technologies for fiber-reinforced polymer composite materials: A review on fabrication methods and process parameters
  71. Rapid Communication
  72. Design, synthesis, characterization, and adsorption capacities of novel superabsorbent polymers derived from poly (potato starch xanthate-graft-acrylamide)
  73. Special Issue: Biodegradable and bio-based polymers: Green approaches (Guest Editors: Kumaran Subramanian, A. Wilson Santhosh Kumar, and Venkatajothi Ramarao)
  74. Development of smart core–shell nanoparticles-based sensors for diagnostics of salivary alpha-amylase in biomedical and forensics
  75. Thermoplastic-polymer matrix composite of banana/betel nut husk fiber reinforcement: Physico-mechanical properties evaluation
  76. Special Issue: Electrospun Functional Materials
  77. Electrospun polyacrylonitrile/regenerated cellulose/citral nanofibers as active food packagings
https://doi.org/10.1515/epoly-2024-0021
Schlagwörter für diesen Artikel
perforated sandwich panels; low-velocity impact; CAI behavior; damage mode
Creative Commons
BY 4.0

Artikel in diesem Heft

  1. Research Articles
  2. Flame-retardant thermoelectric responsive coating based on poly(3,4-ethylenedioxythiphene) modified metal–organic frameworks
  3. Highly stretchable, durable, and reversibly thermochromic wrapped yarns induced by Joule heating: With an emphasis on parametric study of elastane drafts
  4. Molecular dynamics simulation and experimental study on the mechanical properties of PET nanocomposites filled with CaCO3, SiO2, and POE-g-GMA
  5. Multifunctional hydrogel based on silk fibroin/thermosensitive polymers supporting implant biomaterials in osteomyelitis
  6. Marine antifouling coating based on fluorescent-modified poly(ethylene-co-tetrafluoroethylene) resin
  7. Preparation and application of profiled luminescent polyester fiber with reversible photochromism materials
  8. Determination of pesticide residue in soil samples by molecularly imprinted solid-phase extraction method
  9. The die swell eliminating mechanism of hot air assisted 3D printing of GF/PP and its influence on the product performance
  10. Rheological behavior of particle-filled polymer suspensions and its influence on surface structure of the coated electrodes
  11. The effects of property variation on the dripping behaviour of polymers during UL94 test simulated by particle finite element method
  12. Experimental evaluation on compression-after-impact behavior of perforated sandwich panel comprised of foam core and glass fiber reinforced epoxy hybrid facesheets
  13. Synthesis, characterization and evaluation of a pH-responsive molecular imprinted polymer for Matrine as an intelligent drug delivery system
  14. Twist-related parametric optimization of Joule heating-triggered highly stretchable thermochromic wrapped yarns using technique for order preference by similarity to ideal solution
  15. Comparative analysis of flow factors and crystallinity in conventional extrusion and gas-assisted extrusion
  16. Simulation approach to study kinetic heterogeneity of gadolinium catalytic system in the 1,4-cis-polyisoprene production
  17. Properties of kenaf fiber-reinforced polyamide 6 composites
  18. Cellulose acetate filter rods tuned by surface engineering modification for typical smoke components adsorption
  19. A blue fluorescent waterborne polyurethane-based Zn(ii) complex with antibacterial activity
  20. Experimental investigation on damage mechanism of GFRP laminates embedded with/without steel wire mesh under low-velocity-impact and post-impact tensile loading
  21. Preparation and application research of composites with low vacuum outgassing and excellent electromagnetic sealing performance
  22. Assessing the recycling potential of thermosetting polymer waste in high-density polyethylene composites for safety helmet applications
  23. Mesoscale mechanics investigation of multi-component solid propellant systems
  24. Preparation of HTV silicone rubber with hydrophobic–uvioresistant composite coating and the aging research
  25. Experimental investigation on tensile behavior of CFRP bolted joints subjected to hydrothermal aging
  26. Structure and transition behavior of crosslinked poly(2-(2-methoxyethoxy) ethylmethacrylate-co-(ethyleneglycol) methacrylate) gel film on cellulosic-based flat substrate
  27. Mechanical properties and thermal stability of high-temperature (cooking temperature)-resistant PP/HDPE/POE composites
  28. Preparation of itaconic acid-modified epoxy resins and comparative study on the properties of it and epoxy acrylates
  29. Synthesis and properties of novel degradable polyglycolide-based polyurethanes
  30. Fatigue life prediction method of carbon fiber-reinforced composites
  31. Thermal, morphological, and structural characterization of starch-based bio-polymers for melt spinnability
  32. Robust biaxially stretchable polylactic acid films based on the highly oriented chain network and “nano-walls” containing zinc phenylphosphonate and calcium sulfate whisker: Superior mechanical, barrier, and optical properties
  33. ARGET ATRP of styrene with low catalyst usage in bio-based solvent γ-valerolactone
  34. New PMMA-InP/ZnS nanohybrid coatings for improving the performance of c-Si photovoltaic cells
  35. Impacts of the calcinated clay on structure and gamma-ray shielding capacity of epoxy-based composites
  36. Preparation of cardanol-based curing agent for underwater drainage pipeline repairs
  37. Preparation of lightweight PBS foams with high ductility and impact toughness by foam injection molding
  38. Gamma-ray shielding investigation of nano- and microstructures of SnO on polyester resin composites: Experimental and theoretical study
  39. Experimental study on impact and flexural behaviors of CFRP/aluminum-honeycomb sandwich panel
  40. Normal-hexane treatment on PET-based waste fiber depolymerization process
  41. Effect of tannic acid chelating treatment on thermo-oxidative aging property of natural rubber
  42. Design, synthesis, and characterization of novel copolymer gel particles for water-plugging applications
  43. Influence of 1,1′-Azobis(cyclohexanezonitrile) on the thermo-oxidative aging performance of diolefin elastomers
  44. Characteristics of cellulose nanofibril films prepared by liquid- and gas-phase esterification processes
  45. Investigation on the biaxial stretching deformation mechanism of PA6 film based on finite element method
  46. Simultaneous effects of temperature and backbone length on static and dynamic properties of high-density polyethylene-1-butene copolymer melt: Equilibrium molecular dynamics approach
  47. Research on microscopic structure–activity relationship of AP particle–matrix interface in HTPB propellant
  48. Three-layered films enable efficient passive radiation cooling of buildings
  49. Electrospun nanofibers membranes of La(OH)3/PAN as a versatile adsorbent for fluoride remediation: Performance and mechanisms
  50. Preparation and characterization of biodegradable polyester fibers enhanced with antibacterial and antiviral organic composites
  51. Preparation of hydrophobic silicone rubber composite insulators and the research of anti-aging performance
  52. Surface modification of sepiolite and its application in one-component silicone potting adhesive
  53. Study on hydrophobicity and aging characteristics of epoxy resin modified with nano-MgO
  54. Optimization of baffle’s height in an asymmetric twin-screw extruder using the response surface model
  55. Effect of surface treatment of nickel-coated graphite on conductive rubber
  56. Experimental investigation on low-velocity impact and compression after impact behaviors of GFRP laminates with steel mesh reinforced
  57. Development and characterization of acetylated and acetylated surface-modified tapioca starches as a carrier material for linalool
  58. Investigation of the compaction density of electromagnetic moulding of poly(ether-ketone-ketone) polymer powder
  59. Experimental investigation on low-velocity-impact and post-impact-tension behaviors of GFRP T-joints after hydrothermal aging
  60. The repeated low-velocity impact response and damage accumulation of shape memory alloy hybrid composite laminates
  61. Exploring a new method for high-performance TPSiV preparation through innovative Si–H/Pt curing system in VSR/TPU blends
  62. Large-scale production of highly responsive, stretchable, and conductive wrapped yarns for wearable strain sensors
  63. Preparation of natural raw rubber and silica/NR composites with low generation heat through aqueous silane flocculation
  64. Molecular dynamics simulation of the interaction between polybutylene terephthalate and A3 during thermal-oxidative aging
  65. Crashworthiness of GFRP/aluminum hybrid square tubes under quasi-static compression and single/repeated impact
  66. Review Articles
  67. Recent advancements in multinuclear early transition metal catalysts for olefin polymerization through cooperative effects
  68. Impact of ionic liquids on the thermal properties of polymer composites
  69. Recent progress in properties and application of antibacterial food packaging materials based on polyvinyl alcohol
  70. Additive manufacturing (3D printing) technologies for fiber-reinforced polymer composite materials: A review on fabrication methods and process parameters
  71. Rapid Communication
  72. Design, synthesis, characterization, and adsorption capacities of novel superabsorbent polymers derived from poly (potato starch xanthate-graft-acrylamide)
  73. Special Issue: Biodegradable and bio-based polymers: Green approaches (Guest Editors: Kumaran Subramanian, A. Wilson Santhosh Kumar, and Venkatajothi Ramarao)
  74. Development of smart core–shell nanoparticles-based sensors for diagnostics of salivary alpha-amylase in biomedical and forensics
  75. Thermoplastic-polymer matrix composite of banana/betel nut husk fiber reinforcement: Physico-mechanical properties evaluation
  76. Special Issue: Electrospun Functional Materials
  77. Electrospun polyacrylonitrile/regenerated cellulose/citral nanofibers as active food packagings
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Heruntergeladen am 12.9.2025 von https://www.degruyterbrill.com/document/doi/10.1515/epoly-2024-0021/html
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