- Nano Express
- Open Access
Sensitivity of Dielectric Properties to Wear Process on Carbon Nanofiber/High-Density Polyethylene Composites
© Liu et al. 2010
Received: 25 June 2010
Accepted: 6 August 2010
Published: 21 August 2010
We examined the correlation of wear effects with dielectric properties of carbon nanofibers (CNFs; untreated and organosilane-treated)-reinforced high-density polyethylene (HDPE) composites. Wear testing for the nanocomposites over up to 120 h was carried out, and then, dielectric permittivity and dielectric loss factor of the polymer composites with the increased wear time were studied. Scanning electron microscope and optical microscope observations were made to analyze the microstructure features of the nanocomposites. The results reveal that there exist approximate linear relationships of permittivity with wear coefficient for the nanocomposites. Composites containing silanized CNFs with the sufficiently thick coating exhibited high wear resistance. The change in permittivity was more sensitive to the increased wear coefficient for the nanocomposites with lower wear resistance. This work provides potential for further research on the application of dielectric signals to detect the effects of wear process on lifetime of polymeric materials.
Making polymers into nanocomposites with the addition of appropriate nanofillers has been shown to be an effective way to obtain a multitude of enhanced properties and even extend to multi-functionalities not normally considered possible for polymeric materials. A variety of properties, such as physical, thermal, mechanical and others, as well as combinations of them, have been investigated for numerous nanocomposites in order to meet the burgeoning demands of industry. For example, carbon nanofillers, such as carbon nanotubes (CNTs) and carbon nanofibers (CNFs), not only improve electrical conductivity and dielectric properties, but also show enhanced tribological performance for polymers [1–8]. In addition, it has been widely reported in many studies that effective treatments for these nanofillers, including purifications, and/or chemical or non-chemical functionalization, are necessary in order to develop high-performance nanocomposites [9–13].
Among various nanoscale fillers, owing to high aspect ratios and potential for multi-functionality, CNTs and CNFs are commonly used as the reinforced materials for polymer composites [14–17]. For bulk and large volume inexpensive polymers, CNFs are attractive due to the excellent stability and quality of the commercial products. For example, the purity of Pyrograf® nanofibers, which have been widely used, is >98%, and thus, the use of CNFs will not require time/energy-consuming purification processes. In addition, CNFs have graphene-layered structures, which provide vast numbers of active edges on the surface for functionalization purposes. The enormous amount of edges on CNFs enable these nanofillers to be functionalized easily compared to CNTs, which have stable and smooth tube structures, requiring much more dramatic methods of functionalization, typically using strong acids . Therefore, not only the low cost of the raw CNF materials, but also the easy treatments of the nanofibers make this type of nanofiller more attractive and practical for bulk nanocomposite manufacturing and industrial applications.
Numerous attempts of using functionalized CNFs as the reinforcement in nanocomposites have been investigated to accomplish the purpose of improving interaction and adhesion between the nanofillers and polymers [18–24]. For composite systems with non-polar polymer matrices, to dramatically improve the interactions between nanofibers and non-polar polymer matrices is challenging due to limited and weak van der Waals forces. It has been reported that much stronger physical entanglement interactions can be realized through thicker coating layers on the nanofibers that function as bridges, or transition zones, to enhance entanglements between the nanofibers and non-polar polymers, e.g. polyethylene [15–17]. In our previous studies, we successfully synthesized silanized CNFs with thick silane coatings (~46 nm) . Dynamic mechanical analysis and wear-testing results indicated that CNFs treated with such thick silane coatings are effective nanofillers for enhancing mechanical and tribological properties for polyethylene. Our current studies suggested a great potential of this type of silanized CNFs in improving wear resistance and mechanical properties for high-performance polyethylene, i.e. ultra-high molecular polyethylene, so that the resulting nanocomposites will be conceivably be attractive for applications to joint replacement systems with lifetimes significantly extended over the pure polyethylene material [26–30].
However, there is dearth of information on how mechanical behavior such as wear/friction processes (during the usage of the artificial joint) affects structures and properties of nanocomposites used in biosystems. Therefore, there are many concerns that need to be addressed on the application of nanomodified polymers to joint replacements. One of the most critical issues is related to the effects of the wear process on the stability of nanocomposites, both physically and chemically. Even though in the resulting nanocomposites, silanization provides non-polar coatings on the nanofiber surface and polyethylene is also a non-polar polymer, it is not known whether the continuous wear process can create polar groups in the nanocomposites and what relationship would be between the wear rate/wear period and the potential polar group created by the wear process. Such polar groups inside the polymer matrix may directly influence the chemical stability of the polymer and thus affect the practical lifetime of the joint replacements. Moreover, if the wear process creates polar groups in the polymer matrix, such groups can also be maintained in the debris, which has been proved to have a relationship with bone loss.
It is well known that dielectric response is a reflection of dipole movements in insulative materials under an electric field. There are many applications of dielectric measurements to polymeric materials, since dielectric response is very sensitive to polar groups in the polymers [31, 32]. For example, more than 25 years ago, there were studies on in situ monitoring of epoxy curing through continuous measurement of dielectric performance during curing processes [33–36], since with the increase in degree of cure, the molecular weight increases continuously, which has a direct impact on the movement of polar groups within the epoxy. In recent years, there have been many studies reporting on the effects of nanofillers, such as CNFs and CNTs, on the dielectric properties of various polymers including polyethylene [37, 38]. However, there has not been any reported investigation into the relationship between effects of a wear process on polymers and the dielectric characteristics.
In this study, we have investigated the dielectric property changes with wear time and the degree of wear for HDPE nanocomposites containing our previously silane-treated CNFs (thin and thick coatings). The silane coatings not only enhanced the interaction of HDPE matrix and the CNF reinforcement, but also provided a non-polar hydrocarbon layer to cover the nanofiber surface. We hypothesized that the wear process can create polar groups by cutting some polymer chains and causing separation of nanofibers with the polymer matrix, as well as causing damage to the nanofiber structure. Thus, it may be deduced that with the longer wear time, dielectric response can be stronger since more wear can result in more polar groups on the surface and near the surface (since wear on the micro scale is not uniform and successive wear broadens and fills in the affected area, asymptotically approaching totality). In addition, we postulate that the coating thickness can not only affect wear resistance of the resulting composites, but also impact the dielectric properties of the composites. In order to compare with a nanocomposite containing pre-existing polar groups, oxidized nanofibers (ox-CNFs) were used for this purpose. Subsequently, we prepared four types of nanocomposites including three types of composites with different thickness of silane coatings on the CNF surface. In order to gain both sufficient sensitivity of dielectric responses and relatively preferable wear resistance, a 3% wt concentration of carbon fibers was chosen. The experimental results remarkably revealed that approximate linear relationships of permittivity with wear coefficient for the nanocomposites. The change in permittivity was more sensitive to the increased wear coefficient for the nanocomposites with lower wear resistance.
The high-density polyethylene used as a matrix in this research was supplied by Equistar (LB010000) with density of 0.953 g cm-3. The pretreated ox-CNFs as the filler were obtained from Applied Sciences Inc., which are approximately 60 to 150 nm in diameter and 30 to 100 microns in length. Octadecyltrimethoxysilane (ODMS) (90% technical grade) was manufactured by Sigma–Aldrich. Acetone was obtained from J.T. Baker. Ethanol was purchased from Decon Laboratories Inc.
The ox-CNFs were modified under subsequent treatment in boiling ODMS–ethanol solution. Then, the condensation reaction of ox-CNFs and silane coupling agent can occur due to the reactive hydroxyl groups on the surface of organosilane after hydrolysis, forming a silane layer to cover ox-CNF surface. By changing the ratio of ODMS to ox-CNF added and the percentage of ethanol and water in this reaction, we can control the degree of hydrolysis and the thickness of silane coating. In the previous work, three calculated coating thicknesses were applied using TGA data, which is about 1.2 nm for silanized CNF-A, 2.8 nm for silanized CNF-B and 46 nm for silanized CNF-C .
The concentration of 3 wt% CNFs for both ox-CNFs (Nanocomposite-ox) and silanized CNFs (Nanocomposite-A with the thinnest coating, Nanocomposite-B with medium coating thickness and Nanocomposite-C with the thickest coating) were mixed with HDPE by a Haake Torque Rheometer for uniform dispersion. Mixing was set at 170°C with a rotator speed of 30 rpm. The order of adding the materials was as follows: half amount of HDPE, CNFs, and then another half amount of HDPE. The speed was then raised to 70 rpm for 15 min.
The polymeric nanocomposites were hot-pressing at 178°C for 10 min via a hydraulic presser. Then, they were allowed to cool down to room temperature naturally after turning off the heat. All samples were cut for wear testing and dielectric testing with the same size of 20 mm × 20 mm and similar average thickness around 2.5 mm.
where w is the wear coefficient, △m is the weight loss, ρ is the density of composites, F is the normal force and d is the linear sliding distance. An Adventurer Pro analytic scale was used to determine mass loss, with a detectable range of 0.1 mg.
The frequency dependence of permittivity and dielectric loss under a constant temperature was determined by using an Alpha-N High Resolution Dielectric Analyzer equipped with Au parallel plate sensors, with frequencies from 10-3 to 107 Hz. Debris produced by friction was removed by nitrogen gas rather than a solvent to avoid any effects related to them, and then dielectric analysis testing was conducted. The change in dielectric properties was measured before and after each wear testing (24, 48, 72, 96 and 120 h, respectively). The frequency ranges were chosen from 101 to 106 Hz for both dielectric constant and loss factor.
The microstructure features on the fracture interface of both ox-CNF and silanized CNF nanocomposite specimens were observed by field-emission scanning electron microscopy (FESEM type Quanta 200F) in order to characterize the interaction and adhesion between fibers and matrix. FESEM images for fractured surfaces were prepared by freezing in liquid nitrogen for 10 min prior to fracturing. The surfaces of all samples were sputter-coated with gold for electrical conductivity. Additionally, the morphology of the composites was observed using optical microscope (Olympus BX51TRF) equipped with a camera (Olympus U-CMAD 3).
Results and Discussion
Morphology and Wear Resistance
Dispersion of the various CNFs (oxidized and silanized) in the HDPE matrix was observed through field-emission SEM (FESEM). The FESEM images in Figure 2e–l are typical fracture morphology of the nanocomposites before wear testing. It can be seen that there are no obvious agglomerates of nanofibers found in the composites, indicating dispersion and distribution of the nanofibers in the composites were uniform. For the nanocomposites with ox-CNFs, Nanocomp-ox, there was some fiber pullout (Figure 2e, i). Also, there were gaps between the nanofibers, and the matrix revealing the adhesion was poor. For the nanocomposites reinforced by silanized CNFs, Nanocomp-A (Figure 2f, j) and Nanocomp-B (Figure 2g, k), which have thinner coating layers on the CNF surface (1.2 nm and 2.8 nm, respectively), there were also fibers pulled out, especially for Nanocomp-A with the thinnest coating thickness. This phenomenon indicates that the poorer interaction and adhesion between nanofiller and HDPE due to a very thin coating likely result in insufficient entanglement of nanofibers with the polymer chains. The loose entanglement from the thin silane coatings cannot induce an increased strength between the fiber coating and matrix so that the fibers are easier to be pulled out. For Nanocomp-C (Figure 2h, l), there were no obvious long fibers exposed on the surface of matrix and few were pulled out, indicating good adhesion and interaction were obtained from Nanocomp-C with the thick coating. Also, there were few voids between the two phases. This clearly suggested that a thicker silane coating may allow for hydrophobic polymer chains to entangle onto the coating, thus attributing to an improved adhesion and interaction between the modified CNFs and HDPE matrix. Therefore, the higher wear coefficients were appeared from the nanocomposites with the lightly silane-treated CNFs (with thin coatings), especially for Nanocomp-A with the thinnest coating layer on the CNF surface, as revealed in below results.
Effect of silane-coating thickness of CNFs on permittivity of the nanocomposites before and after wear testing
Thickness of silane coating on CNF surface (nm)
Permittivity before wearing
Permittivity after 120-h wearing
Slope (from Fig. 4) × 10-3
Permittivity Versus wear Coefficient
Loss Factor Analysis
To postulate from these results further, the debris generated from nanocomposites with the thicker silane coatings on the CNFs may also have the lowest amount of polarized groups/segments, which will be extremely positive for the application of the polymeric materials to bone joint replacement.
Since there has never been any reported study indicating the effects of a mechanical process, such as wear, on dielectric properties of polymeric materials, this original study is purely an exploratory work. The results reveal that there exist relationships between wear effects and dielectric properties for polymeric nanocomposites. Composites containing silanized CNFs with sufficiently thick coatings exhibited high wear resistance. The permittivity of the nanocomposites decreased obviously for the nanocomposites with appropriate silane treatment for the nanofillers throughout the 120-h wear process. For all the nanocomposites prepared in this study, both ox-CNF/HDPE and silanized CNF/HDPE nanocomposites, dielectric constants were sensitive to the wear effects. It was revealed that approximate linear relationships of permittivity with wear coefficient existed for the nanocomposites. Also, the change in permittivity was more sensitive to the increased wear coefficient for the nanocomposites with lower wear resistance. Additionally, the silane-coating thickness played a significant role on the resistance of dielectric loss for the nanocomposites.
This work provides potential for the in-depth research on the application of dielectric signals to detect the effects of wear process on lifetime of polymeric materials for the application to joint replacement systems. It may also be extended to the more general case of detecting damage to structural composites in many applications.
The authors gratefully acknowledge the support from NSF (CMMI 0856510). The authors are also grateful to Mr. Bin Li, Ms. Lili Sun, Ms. Jianying Ji, Mr. Brooks Lively and Mr. Sandeep Kumar for the helpful discussion and suggestions.
- Park SK, Kim SH, Hwang JT: J Appl Polym Sci. 2008,109(1):388–396. 10.1002/app.28137View ArticleGoogle Scholar
- Sui G, Zhong WH, Ren X, Wang XQ, Yang XP: Mater Chem Phys. 2009, 115: 404–412. 10.1016/j.matchemphys.2008.12.016View ArticleGoogle Scholar
- Park SJ, Lim ST, Cho MS, Kim HM, Joo J, Cho HJ: Electrical Curr Appl Phys. 2005, 5: 302–304. 10.1016/j.cap.2004.02.013View ArticleGoogle Scholar
- Clayton LM, Sikder AK, Kumar A, Cinke M, Meyyappan M, Gerasimov TG, Harmon JP: Adv Funct Mater. 2005, 15: 101–106. 10.1002/adfm.200305106View ArticleGoogle Scholar
- Sung JH, Kim HS, Jin HJ, Choi HJ, Chin IJ: Macromolecules. 2004, 37: 9899–9902. 10.1021/ma048355gView ArticleGoogle Scholar
- Du FM, Scogna RC, Zhou W, Brand S, Fischer JE, Winey KI: Macromolecules. 2004, 37: 9048–9055. 10.1021/ma049164gView ArticleGoogle Scholar
- Kymakis E, Alexandou I, Amaratunga GAJ: Synth Met. 2002, 127: 59–62. 10.1016/S0379-6779(01)00592-6View ArticleGoogle Scholar
- Tjong SC: Mater Sci Eng R. 2006, 53: 73–197. 10.1016/j.mser.2006.06.001View ArticleGoogle Scholar
- Nantao H, Hongwei Z, Guodong D, Xianhua R, Chunhai C, Wanjin Z: Polym Int. 2007, 5: 655.Google Scholar
- Penza M, Rossi R, Alvisi M, Cassano G, Serra E: Sens Actuators B Chem. 2009, 140: 176–184. 10.1016/j.snb.2009.04.008View ArticleGoogle Scholar
- Tan EPS, Lim CT: Compos Sci Technol. 2006, 66: 1102. 10.1016/j.compscitech.2005.10.003View ArticleGoogle Scholar
- Coleman JN, Khan U, Blau WJ, Gun'ko YK: Carbon. 2006, 44: 1624. 10.1016/j.carbon.2006.02.038View ArticleGoogle Scholar
- Ying D, Nantao H, Hongwei Z, Peng L, Peng Z, Xiaogang Z, Guodong D, Chunhai C: Polym Int. 2009, 58: 832. 10.1002/pi.2602View ArticleGoogle Scholar
- Kanagaraj S, Varanda FR, Zhiltsova TV, Oliveira MSA, Simoes JAO: Compos Sci Technol. 2007, 67: 3071. 10.1016/j.compscitech.2007.04.024View ArticleGoogle Scholar
- Shofner ML, Khabashesku VN, Barrera EV: Chem Mater. 2006, 18: 906. 10.1021/cm051475yView ArticleGoogle Scholar
- Yang S, Taha-Tijerina J, Serrato-Diaz V, Hernandez K, Lozano K: Compos Part B. 2007, 38: 228. 10.1016/j.compositesb.2006.04.003View ArticleGoogle Scholar
- Ren X, Wang XQ, Sui G, Zhong WH, Fuqua MA, Ulven CA: J Appl Polym Sci. 2008, 107: 2837. 10.1002/app.27354View ArticleGoogle Scholar
- Colom X, Carrasco F, Pages P, Canavate J: Compos Sci Technol. 2003, 63: 161–169. 10.1016/S0266-3538(02)00248-8View ArticleGoogle Scholar
- Xiang Y, Hou Z, Su R, Wang K, Fu Q: Polym Adv Technol. 2010, 21: 48–54. 10.1002/pat.1355View ArticleGoogle Scholar
- Smita M, Sanjay KN: J Reinforced Plastics Compos. 2010, 0: 00.Google Scholar
- Daniella RM, Herman JCV, Odila HC Maria, da Silva Maria Lucia CP, Sandra ML: Carbonhydrate Polymers. 2009, 75: 317–321. 10.1016/j.carbpol.2008.07.028View ArticleGoogle Scholar
- George JJ, Bhowmick AK: Nanoscale Res Lett. 2008, 3: 508–515. 10.1007/s11671-008-9188-3View ArticleGoogle Scholar
- Jimenez GA, Jana SC: Carbon. 2007, 45: 2079. 10.1016/j.carbon.2007.05.015View ArticleGoogle Scholar
- Abdelmouleh M, Boufi S, Belgacem MN, Dufresne A: Compos Sci Technol. 2007, 67: 1627. 10.1016/j.compscitech.2006.07.003View ArticleGoogle Scholar
- Wood Weston, Kumar Sandeep, Zhong Wei-Hong: Synthesis of organosilane-carbon nanofibers and influence of silane coating thickness on the performance of polyethylene nanocomposites. Accepted by Macromolecular Materials and Engineering.Google Scholar
- Price R, Haberstroh KM, Webster TJ: Nanotechnology. 2004, 15: 892. 10.1088/0957-4484/15/8/004View ArticleGoogle Scholar
- Vermes C, Roebuck KA, Chandrasekaran R, Dobai JG, Jacobs JJ, Glant TT: Miner J Bone Res. 2000, 15–1756.Google Scholar
- Goldman M, Pruitt L: J Biomed, Mater Res. 1998, 40–378.Google Scholar
- Bradford L, Baker D, Ries MD, Pruitt L: Orthop Clin, Relat Res. 2004, 429–468.Google Scholar
- Bradford L, Kurland R, Sankaran M, Kim H, Pruitt LA, Ries MD: Bone J Joint Surg [Am]. 2004, 86–1051.Google Scholar
- Ronald P, ed.: Dielectric and Electronic Properties of Biological Materials. Wiley, Chichester; 1979.Google Scholar
- Chen CK, Raimond L, eds.: Electrical Properties of Polymers. Hanser, New York; 1987.Google Scholar
- Butta E, Livi A, Levita G, Rolla PA: J Polym Sci, Polym Phys Ed. 1995, 33: 2253. 10.1002/polb.1995.090331610View ArticleGoogle Scholar
- Kortaberria G, Arruti P, Gabilondo N: Mondragon I Euro Polym J. 2004, 40: 129–136. 10.1016/j.eurpolymj.2003.09.009View ArticleGoogle Scholar
- Nixdorf K, Busse G: Compos Sci Technol. 2001, 61: 889–894. 10.1016/S0266-3538(00)00174-3View ArticleGoogle Scholar
- Farzana H, Jihua C, Mehdi H: Mater Sci Eng A. 2007, 445–446: 467–476.Google Scholar
- Ryan R Kohlmeyer, Javadi A, Pradhan B, Pilla S, Setyowat K, Chen J, Gong S: J Phys Chem C. 2009, 113: 17626–17629. 10.1021/jp901082cView ArticleGoogle Scholar
- Yang S, Benitez R, Fuentes A, Lozano K: Compos Sci Technol. 2007, 67: 1159–1166. 10.1016/j.compscitech.2006.05.022View ArticleGoogle Scholar
- Sichel EK, ed.: Carbon Black Polymer Composites. Marcel Dekker, New York; 1982.Google Scholar
- Gul VE: Structure and Properties of Conducting Polymer Composites. VSP BV-Utrecht, Tokyo; 1996.Google Scholar
- Kremer F, Schonhals A, eds.: A Broadband Dielectric Spectroscopy. Springer, Berlin; 2002.Google Scholar
- Stauffer D: Introduction to Percolation Theory. Taylor & Francis, London; 1985. 10.4324/9780203211595View ArticleGoogle Scholar
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