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Journal of Nanomaterials
Volume 2014 (2014), Article ID 631069, 6 pages
Research Article

Characterization of Carbon Nanofibers Treated with Thermal Nitrogen as a Catalyst Support Using Point-of-Zero Charge Analysis

1Chemical Engineering Department, Universiti Teknologi Petronas, 31750 Tronoh, Perak Darul Ridzuan, Malaysia
2Fundamental and Applied Science Department, Universiti Teknologi Petronas, 31750 Tronoh, Perak Darul Ridzuan, Malaysia

Received 5 July 2014; Accepted 27 August 2014; Published 14 September 2014

Academic Editor: Yongchun Hong

Copyright © 2014 Thien Duc Nguyen Van et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.


The chemical and physical purification of carbon nanofiber exposes more anchoring sites between meal precursors and carbon surface but thermal N2 gas flow maintains the crystal’s structure as well as its defect and edge sites, referred to as active sites or anchoring sites. After calcination in nitrogen at 450°C, samples were characterized by Raman spectra X-ray diffraction, as well as thermogravimetric and nitrogen physisorption analyses. Results showed a relatively lower fraction of amorphous carbon to graphite, indicating a greater removal of amorphous carbon. Moreover, the disorder intensity of carbon nanofibers that were treated in N2 flow rate of 1 L/min and 3 hours, called 1Gcom-3h sample, achieved far more defect sites compared with unmodified carbon nanofiber. In addition, the surface areas of mesoporous carbon nanofibers decreased over prolonged residence time. The carbon nanofiber support-metal cation interaction therefore improved the deposition of iron when the point-of-zero charge reading was greater than four.

1. Introduction

A heterogeneous catalyst should possess active sites on its solid surface as a key property. In order to maximize the number of active sites, researchers typically distribute active sites on carbon supports rather than these on oxidic supports because of carbon surface inertness property in activity and selectivity of any chemical reactions [1]. Carbon nanofiber (CNF) which is one kind of carbon support has unique advantageous properties including chemical inertia as well as electrical and thermal stability [1, 2]. Carbon’s hydrogen adsorption and activation may be the reason for its catalytic activity [3].

It is different from CNF structure, morphology, and chemistry surface that impact on metallic particles deposition [46]. CNFs consisting of strong tangled agglomeration structures establish an open pore volume and mesopore structure which reduce diffusion limited transfers that have a key role in heterogeneous catalysis [7]. CNF aggregates also display a high surface area of 100–250 m2/g. As synthesized, CNF exists in types of impurities (amorphous carbon) and graphite (graphene and defect structure) as well as metal based catalyst (metal carbide). Most scientists have successfully explored to modify graphite structure and remove amorphous carbon and metal carbide. They used refluxing acid, peroxide, or oxygen thermal treatment to attach more functional groups which become active sites or anchoring centers for the metal precursors [817], at preferred defect sites. Also, Mawhinney et al., 2000, suggested O3 method for titrating surface defect site density on carbon nanofilaments [18]. Barranco et al., 2010, and Sadezky et al., 2005, suggested that Raman analysis can determine the degree of graphitization or defect ( or , resp.) from CNF surface [19, 20].

Furthermore, there are many types of morphology as fishbone (f-), platelet (p-), ribbon (r-), and irregular CNF but fishbone and platelet CNF have high edge sites that are good position for adsorption or modification CNF structure surface [21]. Ochoa-Fernández et al. in 2005 said that f-CNF strongly influences metallic catalyst deposition more than other morphologies because of more curvature [22]. Based on treatments above, CNF structures of different morphology types such as f-CNFs, p-CNFs, r-CNFs, and irregular CNFs [2326] may become damaged and pose difficulty when attempting to control the number of active sites. This, in turn, limits electron transfer between active sites of metal catalyst. Also, point-of-zero charge (PZC) analysis plays an important role in the evaluation of surface chemistry support as it influences the predictability of interactions between metal ions and the carbon support structure in suspended solutions of varied pH. Therefore, the interaction of CNF and deposited metal ion depends on the anion and cation balance [27] whilst carbon surface modification techniques have become essential for efficient deposition of metal precursors. However, using nitrogen treatment is different from common approaches using chemical reacting such as KMnO4, H2O2, and HNO3 oxidation. It has been limited in modifying CNF surface structure.

This research utilized calcination in nitrogen gas flow to detach acidic and basic groups from the surface of as-synthesized CNF and remove the amorphous carbon phase because functional oxygen groups and the amorphous carbon phase inhibit the supported catalyst during nitrogen hydrogenation [28, 29]. As negative charges on the support surface affect interactions between iron colloids and the CNF support, the aim of this research was to explore CNF purification with thermal N2 gas flow and CNF surface properties for purposes of supported catalyst preparation.

2. Materials and Methods

CNFs were purchased from Carbon Nanomaterial Co., LTD., and modified in a fixed-bed alumina reactor. Treatments were carried out under different conditions of residence time (1, 3, and 6 h) and nitrogen flow rate (0.5 and 1 L/min) at 450°C because CNF decomposes above 500°C (Figure 1). Degradation temperatures were determined by Pyris 1 thermogravimetric analysis (TGA) using the same gas at a heating rate of 20°C/min. Also, for instance, name code of sample is 1Gcom-1h. It means that 1 is symbol of 1 L/min; Gcom is name of CNF; and 1 h is calcination time.

Figure 1: Degradation behavior of CNF from TGA spectra.

Samples were prepared in isopropanol under sonication and resultant structures were observed under field emission transmission electron microscopy (FETEM; Zeiss Libra @200) for all CNF samples. Surface area and pore size ranges were analyzed by nitrogen ASAP 2020 physisorption where samples were degassed at 250°C over four hours prior to analysis. The degree of graphitization of samples and their relative amorphous values were assessed by (i) obtaining the Raman spectra with a Horiba HR 800 spectrometer operating at 514.53 nm at room temperature and (ii) Bruker AXS D8-advance X-ray diffraction (XRD) using copper Kα radiation (wavelength,  nm) and 2 theta from 2–80°. The zeta potential for CNFs as a function of pH 2–10 was also tested with a Malvern Nano-ZS Zetasizer (DKSH Technology Sdn. Bhd.) in solutions of 0.01 M NaCl mixed with carbon nanofiber powder with either 0.5 M NaOH or 0.5 M HCl to alter pH [30].

3. Results and Discussion

Commercial carbon nanofiber (G-com) and as-synthesized carbon nanofiber (G-syn) [23] weight losses are shown in Figure 1. Changes were rapid at the beginning (500°C). G-com had one inclination at 550°C but G-syn had two inclination change stages (600 and 800°C). Overall, the degradation level of G-com was higher than that of G-syn because of G-syn’s greater structural stability. The TGA curve shows three regions with the first between 50 and 200°C due to the loss of water. The second (200–500°C) shows a decomposition of light amorphous polycarbons from carbon dioxide that are easily vaporized [31]. The final region indicates the gradual destruction of the CNF’s structure above 500°C for both G-com and G-syn. All observed changes were due to amorphous carbon layers and differences in morphological structure [32, 33]. Thus, the purpose of thermal treatment in an inert environment is to eliminate amorphous carbon layers and increase defective sites on the carbon surface (as shown in Table 1). This may enhance the ability of metal adsorption on CNF surfaces. As discussed, G-com and G-syn samples were calcinated at 450°C to avoid CNF structural breakdown; however, CNF surface defects remained.

Table 1: X-Ray diffraction intensity of carbon nanofiber.

Table 1 illustrates how the X-ray diffraction intensity was amplified over one to three hours (1Gcom-1h; 1Gcom-3h). However, intensity changed slightly as residence time increased to six hours (1Gcom-6h) and also when a reduction in flow rate to 500 mL/min (0.5Gcom-3h) occurred. These findings were similar to Raman’s results for degrees of graphitization (see Table 2) as discussed below.

Table 2: Graphite nanofiber peak positions and the intensity ratio of Raman spectroscopy bands.

The CNF XRD pattern in Figure 2 shows more information of d-spacing interlayer of graphite and existence elements in samples. The data of iron, iron carbide, and carbon nanofiber were matched with reference data of 13-0534, 35-0772, and 75-2078 based on JCPDS, respectively. Figure 2 displays that no change occurred in the d-spacing interlayer of crystalline graphite in 2θ = 20–30°. The iron carbide changes did occur in 2θ = 40–48° [23]. The modified samples (1Gcom-1h, 1Gcom-3h, 1Gcom-6h, and 0.5Gcom-3h) each displayed iron peaks between 30 and 40° that were not present in the G-com sample [34]. This indicated that treatment abolished amorphous carbon layers and revealed encapsulated iron.

Figure 2: X-ray diffraction results for CNFs and modified CNFs.

We used Raman spectra analysis to explore intrinsic defects in the graphite lattice that were responsible for the symmetrical breakdown of the entire crystalline network [35]. Raman spectra of microcrystalline graphite showed a disordered band (D peak) between 1300 and 1400 cm−1 due to lattice defects and a loss of long-range in-plane symmetry. However, a G-band peak (1580–1600 cm−1) appeared due to in-plane bond stretching of carbon atom sp2 hybridization. Also, the intensity of the D peak (Table 2) was higher than that of the G peak, implying high disordered graphitic structures [20] and corrugation of the CNF [36]. The degree of graphitization was estimated by the intensity ratio: [37] or else is for defect degree. In addition, increased CNF graphitization results agreed with the sample (1Gcom-3h) because unstable carbon structures were removed via calcination. These findings also endorsed our XRD results as shown in Table 1, which, taken together, indicated that the majority of amorphous carbon was gradually eliminated. In Table 2 the graphitization degree value of modified samples decreases. It means that using N2 thermal treatment can improve the defect surface structure of CNF because of the defect or disordered degree value of modified samples increases.

We determined that the CNF’s amorphous phase occurred at Raman shift 1550 cm−1 [35]. Table 2 describes results indicating that thermal treatment enhanced the CNF by the incineration of amorphous carbon. The relative value of the amorphous carbon filament was estimated by the integrated intensity ratio of [9], which decreased as residence time increased to 3 h with a nitrogen flow rate of 1 L per min (1Gcom-3h). However, the amorphous phase increased with diminishing nitrogen flow (500 mL per min) (0.5Gcom-3h). The relative value of amorphous carbon was lowest for sample 1Gcom-3h as shown in Figure 1. Amorphous carbon reflected a weight loss of approximately 15% (G-com) below 500°C. By reducing amorphous carbon, CNF pore size increased and could then be characterized as mesopores (Table 3) that allowed an easier internal diffusion of metal ions. Nevertheless, the defective surface of the CNF remained constant which also improved the adsorption of carbon filaments.

Table 3: Surface area and pore size of CNF.

Hence, it appeared that nitrogen physisorption (Table 3) established mesopores with diameters >2 nm [38]. With thermal N2 flow rates of 500 mL/min and 1000 mL/min and over residence intervals of 1, 3, and 6 hours, both surface area and pore size decreased compared to nonmodified samples (G-com) due to amorphous phase removal of CNF and increased rearrangement of the graphite structure. In addition, there was a wide distribution of pore width ranging from 1.8 to 1415.4 nm. The range of pore size for modified samples was larger than that of G-com, indicating that the majority of pores allowed for more efficient metal ion adsorption on deposition.

Typical CNF TEM images of two types are shown in Figure 3 based on angles between graphene layers and the growth axis. CNF graphene layers called platelet CNFs (p-CNF) are arranged perpendicular to the axis (see Figure 3(a)). The G-com structure showed angles of approximately 30° between graphene layers and the CNF axis, also known as fishbone CNF (f-CNF), seen in Figure 3(b). This phenomenon indicated the existence of more edge sites on p-CNF and f-CNF structures, in addition to defect sites as active sites, all of which aid metal ion adsorption on the CNF surface [39, 40].

Figure 3: CNF TEM images: p-CNF, 3(a); f-CNF, 3(b).

CNF zeta potential characterization is shown in Figure 4. Varied relative point-of-zero charges (PZC) for p-CNF and f-CNF ranged between pH 3 and 4 and were lower than those for argon gas modified CNFs as reported by Zhu et al. [30], most likely due to extant iron within the CNF. Except for the 1Gcom-1h sample, PZC for all other CNF samples varied between pH 3.5 and 4. Vinke et al. [41] and Solar et al. [42] suggested that the PZC of carbon was subject to total surface oxygen and the nature and distribution of surface oxygen sites. These results therefore implied that oxygen was removed by heat treatment.

Figure 4: CNF zeta potential (PZC) under different treatment conditions.

Furthermore, the PZC value aids our understanding of changes that occur in surface charges of the CNF support using impregnation of the supported catalyst preparation and consequently also for the dispersion of the metallic active phase as discussed by Regalbuto [43]. An electrostatic attraction between the CNF support and cation salt depends on the pH medium as formulated over or under PZC value. Figure 4 shows PZC values for a basic suspension (pH > 4) and for an acid medium (pH < 3). Rodríguez-Reinoso 1998 similarly reviewed that Pt complex salt can adsorb on surface of oxygen-free carbon by electrostatic force [1] and it belonged to precursor salt ion in acid or basic solution. Therefore, a deposition method can be developed for pH values greater than the CNF support’s PZC since cation salts can interact with negative charges of surface carbons. Also, the larger the interaction, the higher the potential difference between the CNF support and metal ion [4, 30, 44]. This approach controls both metal loading and particle size for interaction and adsorption characteristics during the process of deposition.

4. Conclusion

Using thermal purification in nitrogen gas, p-CNF and f-CNF structures were broken down to release impurities during the amorphous phase and still retain iron metal and defect sites. Amorphous carbon layers were efficiently eliminated to minimize the ratio of amorphous carbon to graphite. Furthermore, CNF defect structures increase after modification and get minimum amorphous carbon with sample of 1Gcom-3h. The surface area of the sample was 90.238 m2/g, and pore width ranged from micro- to macropore. These results clearly indicated easier metal ion diffusion. Finally, electrostatic attraction between negative CNF support and cation salt improves when the pH medium is greater than a PZC value of four.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.


The authors gratefully acknowledge MOE for its financial support (LRGS-One Baja Funder and FRGS), Universiti Teknologi PETRONAS for its generous Graduate Assistantship scheme and lab facilities, and also Mr. Albert Lim and Mr. Simon Choo from DKSH Technology Sdn. Bhd. for supporting this research with the Malvern Nano-ZS Zetasizer equipment.


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