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The effect of different structural designs on impact resistance to carbon fiber foam sandwich structures

  • Kang Yang , Peng Gong EMAIL logo , Li Yang , Liguo Zhang , Ziao Zhang and Gang Ma
Published/Copyright: December 1, 2021
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e-Polymers
From the journal e-Polymers Volume 22 Issue 1

Abstract

The development of the composite materials in the past decades has made the composite materials more and more widely used in various engineering fields. The mechanical properties of the composite materials are gradually improved, especially the impact resistance. In this article, the damage of carbon fiber foam sandwich structure (material grade: W-3021FF/H60) under different sandwich thicknesses and impact energies was studied. Ultrasonic C-scan was used to measure the depth and area of impact damage area. Finally, the impact energy and foam core thickness on impact damage was analyzed by test results. The results show that the impact damage depth and area of foam sandwich structure were positively related to the impact energy, and with the increase in the impact energy, the growth rate of damage depth and damage area changes; the greater the thickness of the foam core was, the stronger the span-direction guiding energy for impact energy, the larger the damage area and the smaller the damage depth. Under the same energy, the more the layers of carbon fiber cloth with the foam sandwich structure, the larger the impact damage depth and the smaller the impact damage area. The proportion of ±45° ply in the foam sandwich structure can improve its impact resistance.

Keywords: composite; impact; ultrasonic C-scan; mechanical properties; sandwich structure

1 Introduction

With the continuous development of composite technology and its advantages of designability, high specific strength, high specific stiffness, fatigue resistance, corrosion resistance, etc., the demand for engineering application in various fields is getting higher and higher, especially in the aviation field (1,2,3). Compared with the ordinary composite laminates, the carbon fiber foam sandwich structure generally uses light material, so the stiffness and structural stability of the material can be greatly improved under the same quality (4,5). Therefore, carbon fiber foam sandwich composite materials are widely used in the production of general aircraft. In practical application, facing the complex working environment, in order to ensure the safety and reliability of the aircraft in flight, there are strict requirements on the mechanical properties of the carbon fiber composites, especially the damage caused by dynamic loads such as impact and vibration throughout the whole flight process from take-off, cruise to landing. Hence, many studies have been carried out on the impact damage of composite materials. Zhang et al. (6) studied the impact protection performance of different sandwich structures, and analyzed the influence of thickness, matrix content, impact energy, and other parameters. Dogan (7) has studied the investigation of the effects of different core types on the low velocity impact, three-point bending. and out-of-plane compression loading performance of sandwich composites. Three core materials were selected: Balsa wood, PVC foam, and Ayous wood. Anderson and Madenci (8) impacted the plates with different impact energy and summarized the relationship between plate damage and contact force rule. The impact test of different layers of skin, different thicknesses, and different densities of the foam sandwich plates was carried out. The test result showed that the damage degree of the foam core was only related to the pit depth of the upper skins, the increase in the density of the foam core and the thickness of the skin could increase the damage energy of the sandwich plates. Crupi et al. (9,10,11) prepared various types of composite sandwich structures and carried out a series of low-speed impact tests on sandwich specimens by using a falling hammer tester, and used the thermal imager and three-dimensional computer tomography system to conduct in-depth research on the damage mechanism of the sandwich structures.

The factors affecting the bearing capacity of the sandwich structures have not been systematically studied in the above literature (12,13,14,15,16,17,18). In this article, the carbon fiber foam sandwich structures with different thicknesses and different laying sequences were prepared, and the impact tests were carried out with different impact energies. After the test, the impact damage areas were analyzed by ultrasonic C-scan. Finally, the influence of impact energy, thickness of foam, and laying sequence of the carbon fiber on the impact damage of foam sandwich structures was studied. The test and analysis results have certain reference significance for engineering designers to carry out relevant structural design.

2 Experimental methods

2.1 Preparation of specimens

The specimens in this test are carbon fiber sandwich structure composed of composite panels and sandwich materials. The brand of the carbon fiber woven cloth of the specimen is W-3021FF (manufacturer: Weihai Guangwei Composite Material Co., Ltd.), the foam brand is H60 (manufacturer: Kunshan Daibo New Material Co., Ltd.). The specimens were made by hand lay-up vacuum bag pressing process, the foam thickness and laying sequence of each specimen are shown in Table 1. The formed specimens were cut into 150 mm × 100 mm standard specimens (Figure 1) by water cutting machine (LTJ1613, Shanghai Shimai Technology Co., Ltd.) for subsequent mechanical tests and inspection.

Table 1

Foam thickness and laying sequence

Sample Foam thickness (mm) Laying direction
A01 2 [±45/(core)/±45]
B01 4 [±45/(core)/±45]
C01 6 [±45/(core)/±45]
B02 4 [±45/(0.90)/(core)/±45]
B03 4 [±45/(0.90)(core)/(0.90)/±45]
B04 4 [±45/±45/(core)/±45/±45]
Figure 1 Schematic diagram of standard test piece size and impact position: (a) schematic diagram of standard specimen dimensions and impact positions and (b) schematic diagram of the foam sandwich specimen (mm).
Figure 1

Schematic diagram of standard test piece size and impact position: (a) schematic diagram of standard specimen dimensions and impact positions and (b) schematic diagram of the foam sandwich specimen (mm).

2.2 Experimental procedure

ASTM D7136 Standard Test was used for the drop hammer impact test, and impact damage was introduced by drop hammer method. The support window size of the specimen was 125 mm × 75 mm, the impactor was a steel hemispherical punch with a diameter of 16 mm, the weight of the hammer was 5.5 kg, the impact energy was 6.67 J·mm−1, and the test environment temperature/humidity was 25°C/40% RH. Before the test, the specimens were visually inspected to ensure that there was no initial damage on the surface of the specimens. The specimens were clamped by the chuck on the edge, and the impact energy could reach 10.58, 21.17, 31.75, and 42.34 J by manually adjusting the height of the hammer head. Each group of test adopts multiple specimens to ensure the accuracy of test results. Ultrasonic C-scan (SAM300 Basic, PVA TePla company, Germany) was used to characterize the damage characteristics after impact, as shown in Figure 2.

Figure 2 Test equipment and process: (a) showed the ultrasonic C-scan equipment and (b) showed the impact test equipment.
Figure 2

Test equipment and process: (a) showed the ultrasonic C-scan equipment and (b) showed the impact test equipment.

3 Results and discussion

3.1 Influence of impact energy on impact damage

Figure 3 shows the typical damage of specimen. Table 2 shows the test results of the depth of impact damage area of each specimen under the impact energy of 10.58, 21.17, 31.75, and 42.34 J. When the impact energy was 42.34 J, the impact damage depth of three groups of specimens reaches the maximum value, which was 2.53, 2.11, and 1.91 mm. Table 3 shows the test results of impact damage area of each specimen under the impact energy of 10.58, 21.17, 31.75, and 42.34 J, when the impact energy was 42.34 J, the area diameter of impact damage area of three groups of specimens reached the maximum value, which was 10,700, 13,800, and 15,804 μm. It can be seen from Tables 2 and 3 that the change rules of depth and area of impact damage area of each group under different impact energy were the same. With the increase in impact energy, the depth and area of impact damage area of specimens gradually increase.

Figure 3 Typical damage of specimen.
Figure 3

Typical damage of specimen.

Table 2

Impact damage depth (mm)

Energy (J) A01 B01 C01 B02 B03 B04
10.58 1.2600 0.8100 0.6575 1.7500 2.3805 1.3025
21.17 1.5005 1.4105 1.3125 3.0405 3.7200 1.5705
31.75 1.8050 1.7125 1.6050 3.3605 — 1.6200
42.34 2.5300 2.1105 1.9100 — — —
Table 3

Impact damage area (μm)

Energy (J) A01 B01 C01 B02 B03 B04
10.58 4,900 6,200 9,000 10,800 7,303 5,500
21.17 7,400 9,000 9,901 15,700 8,101 6,600
31.75 8,501 11,400 12,600 16,400 11,500 8,300
42.34 10,700 13,800 15,804 16,801 12,302 11,300

Figure 4 shows the ultrasonic C-scan result of impact damage depth of A01 after impact. Figure 5 shows the ultrasonic C-scan result of impact damage area of A01 after impact. It can be seen from Figure 4 that the impact damage depth was 1.26, 1.50, 2.00, and 2.69 mm when the impact energy was 42.34 J, damage depth was the largest, and damage depth increases with the increase in the impact energy. It can be seen from Figure 5 that the area diameter of impact damage area was 4,900, 7,400, 8,501, and 10,700 μm when the impact energy was 42.34 J, damage area was the largest, and damage area increases with the increase in the impact energy.

Figure 4 Impact damage depth of A01 under different impact energies: (a) under 10.58 J impact, (b) under 21.17 J impact, (c) under 31.75 J impact, and (d) under 42.34 J impact.
Figure 4

Impact damage depth of A01 under different impact energies: (a) under 10.58 J impact, (b) under 21.17 J impact, (c) under 31.75 J impact, and (d) under 42.34 J impact.

Figure 5 Impact damage area of A01 after different impact energies: (a) under 10.58 J impact, (b) under 21.17 J impact, (c) under 31.75 J impact, and (d) under 42.34 J impact.
Figure 5

Impact damage area of A01 after different impact energies: (a) under 10.58 J impact, (b) under 21.17 J impact, (c) under 31.75 J impact, and (d) under 42.34 J impact.

3.2 Influence of foam thickness on impact damage

In this experiment, A01, B01, and C01 adopted the laying sequence of [±45/(core)/±45], and the foam thickness of A01, B01, and C01 was 2, 4, and 6 mm, respectively. Figure 6 shows the test results of impact damage depth of three kinds of specimens under different impact energies, the impact damage depth of A01 was the maximum for three kinds of specimens under four impact energies, and the impact damage depth of three kinds of specimens shows a downward trend under each impact energy. Figure 6 shows the test results of the impact damage area of three kinds of specimens under different impact energies, the impact damage area of C01 was the maximum for three kinds of specimens under four impact energies, and the impact damage area of three kinds of specimens shows an upward trend under each impact energy.

Figure 6 Impact damage depth (a) and area (b) of the same laminate under different impact energies.
Figure 6

Impact damage depth (a) and area (b) of the same laminate under different impact energies.

It can be seen from Figure 6 that as the thickness of the foam increases, the pit depth of the specimen after impact decreases gradually, but the area diameter of damage area increases gradually, and there was no linear correspondence between the two sets of data. Under the same impact energy, the damage depth of A01 was the largest, followed by B01, and the damage depth of C01 was the smallest. When impacted by high energy, the damage depth of the former was 1.5 times that of the latter. The rule of damage area was different from that of damage depth. When the test piece have been at the low impact energy of 10.58 J, the damage area of C01 was the largest, followed by B01, and A01 had the smallest damage area. When the impact energy increases, the increase rate of damage area of C01 increases gradually. The reason was that when the thickness of the specimen was smaller, the impact energy extends along the thickness direction, and causes greater damage to the thickness direction; when the thickness of the specimen was larger, the impact energy gradually diffuses and was absorbed along the contact surface, resulting in larger damage area, but the penetration of impact energy into the thickness direction was weakened, and the damage depth decreases. When the specimen was impacted, the upper and lower panels bear the tensile and compressive stress in the thickness direction during the transmission of impact energy. Compared with the carbon fiber panel, the stronger energy absorption performance of the foam sandwich layer enables the energy to be transmitted in the spanwise direction. The foam sandwich layer mainly bears the shear stress in the spanwise direction to disperse the stress and improve the impact resistance of the whole structure.

3.3 Influence of laying sequence on impact damage

Figure 7 shows the influence of impact energy on the impact damage depth and area of specimens with different laying sequences. It can be seen from Figure 7a that under the same impact energy, the damage depth of B02 and B03 were larger, which was 3.04 and 3.72 mm at 21.17 J, and the damage depth of B01 and B04 were smaller, 1.51 and 1.57 mm at 21.17 J, respectively. The change rule of damage area was the same as damage depth. The impact damage area of B02 was the largest, which reached 10,800 μm at 10.58 J, the impact damage area of B04 and B05 were smaller, 5,500 and 4,000 μm at 10.58 J. With the increase in the impact energy, the increase rate of damage area of B01 increases gradually, which reached 138% higher than that at 10.58 J. Under the impact energy of 31.75 and 42.34 J, the damage area of B04 was the smallest, which was 11,300 and 6,700 μm, respectively. The damage area of B02 was the largest, which was 16,400 and 16,801 μm.

Figure 7 Impact damage depth (a) and area (b) of the same thickness under different impact energies.
Figure 7

Impact damage depth (a) and area (b) of the same thickness under different impact energies.

Under the same impact energy, the damage of B04 was smaller, and the damage behavior of two kinds of laying sequence of specimens would not be obvious when the impact energy did not exceed 21.71 J. When the impact energy reached 31.75 J, the load that B01 can bear decreases obviously, while B04 had greater bearing capacity and better impact resistance. The test results showed that increasing the proportion of ±45° ply can improve the impact resistance of foam sandwich structure. Under the condition of different layers of carbon fiber woven cloth, the comparison between B01, B03, and B04 showed that under the same impact energy the impact damage depth of B01 was smaller, and it was still not penetrated at 42.34 J, but the impact damage area of B01 was the largest among them, which was 14,800 μm. The test results showed that under the same energy, more layers of carbon fiber cloth are arranged, the greater the impact damage depth and smaller the damage area. Because the warp and weft fibers in each layer were interwoven with each other, and there were interwoven points, so the anti-delamination ability increases with the increase in the fiber arrangement direction. When the impact energy increased to a certain extent, although the impact damage depth of B04 and B05 were larger, and the upper panel was almost penetrated, because the fibers were interwoven with each other, the crack propagation to a larger area was effectively inhibited. Therefore, the impact energy was mainly concentrated near the impact point, leading to serious damage in the local area, causing a large number of fiber fractures, partial delamination cracks, and compression failure of the sandwich. The scope of damage caused by the impact was smaller, so the damage area was much smaller than other groups. On the contrary, B01 lacks more fiber arrangement directions, so the damage form was mainly delamination, and the fiber fracture along the thickness direction was less (17,18).

Comparing B02 with B01, B03, and B04, the damage area of symmetrical ply was smaller and more regular, and the damage area was mainly concentrated near the impact point. Under higher impact energy, the damage areas of B01, B03, and B04 are smaller than that of B02, asymmetric laying sequence will greatly reduce the impact resistance. Because the anisotropy of thermal expansion coefficient of material caused the mismatch of shrinkage between the layers when the temperature of the asymmetric layer drops to room temperature after high temperature curing, thermal stress was generated and maintained between the layers. Under the action of thermal stress, the square sandwich panel was deformed into an arch shape, and the impact damage area of the specimen was larger.

4 Conclusion

  1. Under the impact of low energy, the crushing damage of foam sandwich structure was the main failure mode, and the impact damage depth and damage area increase with the increase in the impact energy.

  2. The thicker the foam sandwich was, the stronger the ability to guide the spanwise extension of impact energy, and the larger the impact damage area, the smaller the damage depth.

  3. Under the condition of same layers of carbon fiber woven cloth, increasing the proportion of ±45° ply can improve the impact resistance of the foam sandwich structure.

  4. The asymmetric laying sequence of foam sandwich structure will greatly reduce the impact resistance.

  1. Funding information: This work was supported by a grant from the project of Liaoning Provincial Department of Education (JYT2020141) and the key research and service local project of Liaoning Provincial Department of Education (JYT2020156).

  2. Author contributions: Kang Yang: writing – original draft, writing – review and editing, resources, formal and analysis; Peng Gong: writing – original draft, formal analysis, visualization, and project administration; Li Yang: data curation; Liguo Zhang: supervision; Ziao Zhang: formal analysis; Gang Ma: investigation.

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

  4. Data availability statements: The datasets generated during and/or analyzed during the current study are available from the corresponding author on reasonable request.

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Received: 2021-09-07
Revised: 2021-10-12
Accepted: 2021-10-15
Published Online: 2021-12-01

© 2022 Kang Yang et al., published by De Gruyter

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

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https://doi.org/10.1515/epoly-2022-0003
Keywords for this article
composite; impact; ultrasonic C-scan; mechanical properties; sandwich structure
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  8. Development, characterization, and in vitro evaluation of adhesive fibrous mat for mucosal propranolol delivery
  9. Fused deposition modeling of polypropylene-aluminium silicate dihydrate microcomposites
  10. Preparation of highly water-resistant wood adhesives using ECH as a crosslinking agent
  11. Chitosan-based antioxidant films incorporated with root extract of Aralia continentalis Kitagawa for active food packaging applications
  12. Molecular dynamics simulation of nonisothermal crystallization of a single polyethylene chain and short polyethylene chains based on OPLS force field
  13. Synthesis and properties of polyurethane acrylate oligomer based on polycaprolactone diol
  14. Preparation and electroactuation of water-based polyurethane-based polyaniline conductive composites
  15. Rapeseed oil gallate-amide-urethane coating material: Synthesis and evaluation of coating properties
  16. Synthesis and properties of tetrazole-containing polyelectrolytes based on chitosan, starch, and arabinogalactan
  17. Preparation and properties of natural rubber composite with CoFe2O4-immobilized biomass carbon
  18. A lightweight polyurethane-carbon microsphere composite foam for electromagnetic shielding
  19. Effects of chitosan and Tween 80 addition on the properties of nanofiber mat through the electrospinning
  20. Effects of grafting and long-chain branching structures on rheological behavior, crystallization properties, foaming performance, and mechanical properties of polyamide 6
  21. Study on the interfacial interaction between ammonium perchlorate and hydroxyl-terminated polybutadiene in solid propellants by molecular dynamics simulation
  22. Study on the self-assembly of aromatic antimicrobial peptides based on different PAF26 peptide sequences
  23. Effects of high polyamic acid content and curing process on properties of epoxy resins
  24. Experiment and analysis of mechanical properties of carbon fiber composite laminates under impact compression
  25. A machine learning investigation of low-density polylactide batch foams
  26. A comparison study of hyaluronic acid hydrogel exquisite micropatterns with photolithography and light-cured inkjet printing methods
  27. Multifunctional nanoparticles for targeted delivery of apoptin plasmid in cancer treatment
  28. Thermal stability, mechanical, and optical properties of novel RTV silicone rubbers using octa(dimethylethoxysiloxy)-POSS as a cross-linker
  29. Preparation and applications of hydrophilic quaternary ammonium salt type polymeric antistatic agents
  30. Coefficient of thermal expansion and mechanical properties of modified fiber-reinforced boron phenolic composites
  31. Synergistic effects of PEG middle-blocks and talcum on crystallizability and thermomechanical properties of flexible PLLA-b-PEG-b-PLLA bioplastic
  32. A poly(amidoxime)-modified MOF macroporous membrane for high-efficient uranium extraction from seawater
  33. Simultaneously enhance the fire safety and mechanical properties of PLA by incorporating a cyclophosphazene-based flame retardant
  34. Fabrication of two multifunctional phosphorus–nitrogen flame retardants toward improving the fire safety of epoxy resin
  35. The role of natural rubber endogenous proteins in promoting the formation of vulcanization networks
  36. The impact of viscoelastic nanofluids on the oil droplet remobilization in porous media: An experimental approach
  37. A wood-mimetic porous MXene/gelatin hydrogel for electric field/sunlight bi-enhanced uranium adsorption
  38. Fabrication of functional polyester fibers by sputter deposition with stainless steel
  39. Facile synthesis of core–shell structured magnetic Fe3O4@SiO2@Au molecularly imprinted polymers for high effective extraction and determination of 4-methylmethcathinone in human urine samples
  40. Interfacial structure and properties of isotactic polybutene-1/polyethylene blends
  41. Toward long-live ceramic on ceramic hip joints: In vitro investigation of squeaking of coated hip joint with layer-by-layer reinforced PVA coatings
  42. Effect of post-compaction heating on characteristics of microcrystalline cellulose compacts
  43. Polyurethane-based retanning agents with antimicrobial properties
  44. Preparation of polyamide 12 powder for additive manufacturing applications via thermally induced phase separation
  45. Polyvinyl alcohol/gum Arabic hydrogel preparation and cytotoxicity for wound healing improvement
  46. Synthesis and properties of PI composite films using carbon quantum dots as fillers
  47. Effect of phenyltrimethoxysilane coupling agent (A153) on simultaneously improving mechanical, electrical, and processing properties of ultra-high-filled polypropylene composites
  48. High-temperature behavior of silicone rubber composite with boron oxide/calcium silicate
  49. Lipid nanodiscs of poly(styrene-alt-maleic acid) to enhance plant antioxidant extraction
  50. Study on composting and seawater degradation properties of diethylene glycol-modified poly(butylene succinate) copolyesters
  51. A ternary hybrid nucleating agent for isotropic polypropylene: Preparation, characterization, and application
  52. Facile synthesis of a triazine-based porous organic polymer containing thiophene units for effective loading and releasing of temozolomide
  53. Preparation and performance of retention and drainage aid made of cationic spherical polyelectrolyte brushes
  54. Preparation and properties of nano-TiO2-modified photosensitive materials for 3D printing
  55. Mechanical properties and thermal analysis of graphene nanoplatelets reinforced polyimine composites
  56. Preparation and in vitro biocompatibility of PBAT and chitosan composites for novel biodegradable cardiac occluders
  57. Fabrication of biodegradable nanofibers via melt extrusion of immiscible blends
  58. Epoxy/melamine polyphosphate modified silicon carbide composites: Thermal conductivity and flame retardancy analyses
  59. Effect of dispersibility of graphene nanoplatelets on the properties of natural rubber latex composites using sodium dodecyl sulfate
  60. Preparation of PEEK-NH2/graphene network structured nanocomposites with high electrical conductivity
  61. Preparation and evaluation of high-performance modified alkyd resins based on 1,3,5-tris-(2-hydroxyethyl)cyanuric acid and study of their anticorrosive properties for surface coating applications
  62. A novel defect generation model based on two-stage GAN
  63. Thermally conductive h-BN/EHTPB/epoxy composites with enhanced toughness for on-board traction transformers
  64. Conformations and dynamic behaviors of confined wormlike chains in a pressure-driven flow
  65. Mechanical properties of epoxy resin toughened with cornstarch
  66. Optoelectronic investigation and spectroscopic characteristics of polyamide-66 polymer
  67. Novel bridged polysilsesquioxane aerogels with great mechanical properties and hydrophobicity
  68. Zeolitic imidazolate frameworks dispersed in waterborne epoxy resin to improve the anticorrosion performance of the coatings
  69. Fabrication of silver ions aramid fibers and polyethylene composites with excellent antibacterial and mechanical properties
  70. Thermal stability and optical properties of radiation-induced grafting of methyl methacrylate onto low-density polyethylene in a solvent system containing pyridine
  71. Preparation and permeation recognition mechanism of Cr(vi) ion-imprinted composite membranes
  72. Oxidized hyaluronic acid/adipic acid dihydrazide hydrogel as cell microcarriers for tissue regeneration applications
  73. Study of the phase-transition behavior of (AB)3 type star polystyrene-block-poly(n-butylacrylate) copolymers by the combination of rheology and SAXS
  74. A new insight into the reaction mechanism in preparation of poly(phenylene sulfide)
  75. Modified kaolin hydrogel for Cu2+ adsorption
  76. Thyme/garlic essential oils loaded chitosan–alginate nanocomposite: Characterization and antibacterial activities
  77. Thermal and mechanical properties of poly(lactic acid)/poly(butylene adipate-co-terephthalate)/calcium carbonate composite with single continuous morphology
  78. Review Articles
  79. The use of chitosan as a skin-regeneration agent in burns injuries: A review
  80. State of the art of geopolymers: A review
  81. Mechanical, thermal, and tribological characterization of bio-polymeric composites: A comprehensive review
  82. The influence of ionic liquid pretreatment on the physicomechanical properties of polymer biocomposites: A mini-review
  83. Influence of filler material on properties of fiber-reinforced polymer composites: A review
  84. Rapid Communications
  85. Pressure-induced flow processing behind the superior mechanical properties and heat-resistance performance of poly(butylene succinate)
  86. RAFT polymerization-induced self-assembly of semifluorinated liquid-crystalline block copolymers
  87. RAFT polymerization-induced self-assembly of poly(ionic liquids) in ethanol
  88. Topical Issue: Recent advances in smart polymers and their composites: Fundamentals and applications (Guest Editors: Shaohua Jiang and Chunxin Ma)
  89. Fabrication of PANI-modified PVDF nanofibrous yarn for pH sensor
  90. Shape memory polymer/graphene nanocomposites: State-of-the-art
  91. Recent advances in dynamic covalent bond-based shape memory polymers
  92. Construction of esterase-responsive hyperbranched polyprodrug micelles and their antitumor activity in vitro
  93. Regenerable bacterial killing–releasing ultrathin smart hydrogel surfaces modified with zwitterionic polymer brushes
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