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Materials Research

Print version ISSN 1516-1439

Mat. Res. vol.16 no.1 São Carlos Jan./Feb. 2013  Epub Nov 22, 2012

http://dx.doi.org/10.1590/S1516-14392012005000165 

Influence of thermal treatment on porosity formation on carbon fiber from textile PAN

 

 

Jossano Saldanha MarcuzzoI,*; Choyu OtaniI; Heitor Aguiar PolidoroII, III; Satika OtaniII

IInstituto Tecnológico Aeroespacial – ITA, São José dos Campos, SP, Brazil
IIMultivácuo Indústria e Comércio Ltda, São José dos Campos, SP, Brazil
IIICentro de Tecnologia e Ciência – CETEC, São José dos Campos, SP, Brazil

 

 


ABSTRACT

Activated carbon fibers (ACFs) are known as an excellent adsorbent material due to their particular characteristics such as their high speed adsorption rate and for being easy to handle. The ACFs are commercially manufactured from carbon fibers (CF) which receive an additional activation process and can be produced from celluloses, phenolic resin, pitch and Polyacrylonitrile (PAN). In the present work, the oxidized 5.0 dtex textile PAN fiber was carbonized to CFs formation. During the carbonization process in different heating rates, the topographic features changes on fibers were monitored in order to determine the best carbonization condition for CFs production to be used as raw material for ACF. Different heating rates and maximum temperature of treatment were tested and the results indicated that it is possible to produce poorly activated carbon fiber, directly from oxidized textile PAN fiber, by one single step production process.

Keywords: carbon fiber, activated carbom fiber, activated carbon, adorption materials, carbonization


 

 

1. Introduction

Activated Carbons (AC) (granular, powdered or molded forms) are one of the most widely used adsorbent materials due to their ability to act over a wide range of adsorbates. Normally, ACs are used for drinkable and waste water treatment and in many other applications where the removal of generally dispersed contaminated molecules is desired1.

Activated carbon fibers (ACFs) have special characteristics when compared with common activated carbons (granular or powder), allowing their transformation into fabric, woven or yarn forms what give them self-sustainable characteristics. In addition, ACFs show well defined pore structures on their surface which provide a high and fast adsorption capacity for specific components2,3. In spite of all advantages of ACFs application, their use has been limited due to their relatively high cost.

One of the most important characteristics, which make ACFs a very special adsorbent material, is their pore size distribution. The architecture of the pores presented by common AC is a ladder-like structure. In this structure, micropores are located inside mesopores, which in turn are inserted into the macropores structures. The main mechanism by which the molecules are adsorbed can be summarized by a sieving process, where molecules first cross the macropore, secondly the mesopores and subsequently find these micropores where they are adsorbed. In the ACFs case, a large amount of micropores can be found directly on their surface leading to a faster and less energetic adsorption mechanism, especially for gases4.

The common methods used to produce ACFs from a carbon fiber (CF) are not far from those used for AC production. The process can be simply described as a thermal treatment oxidant atmosphere at temperatures between 700 and 1000 ºC2,3,5.

An efficient activation process can be performed by using a suitable feed gas, which reacts not only with the carbon surface, but also with the bulk atoms6. If the reactions are carried out only on their surface, the CF loses all atoms on its surface and does not develop porosity, but if the oxidation takes place on bulky carbon atoms, a rapid damage in the mechanical property of fiber can be promoted. The pore distribution characteristics and all physical characteristics of ACFs are strongly dependent on activation process parameters and on the raw material (carbon fiber) quality5,6.

All the results presented in this paper are focused on carbon fiber surface feature, considering the influence of the carbonization process parameter, and they are an integrant part of a main research project "the study of technical and financial aspects of activated carbon fiber production based on commercial textile PAN fiber".

 

2. Experimental

The 5.0 dtex textile PAN fibers were specially spun in 50 ktex tow by Radicifibras. They were oxidized in a laboratory scale oven set by Multivácuo Ind. Com. Ltda/PIPE FAPESP Nº 07/51606-5, aiming an experimental production of flame resistant fibers. The sample for carbonization, weighting 6 g and 400 mm length, was prepared by means of adequate subtraction and control of filament quantities, for carbonization experiments. Then, the sample was fixed into a holder showed in Figure 1 (detail) in which a 3 N force is applied by a spring. The set of such sample holder with fibers was introduced in a quartz tube, and finally this quartz tube was introduced in an electrical furnace (Figure 1). Both ends of the quartz tube were closed by special flanges, which allow the insertion and the purge of argon gas to provide an inert atmosphere condition necessary for carbonization.

The carbonization was performed at final temperatures ranging from 600 ºC up to 1100 ºC, applying two different heating rates: 10 ºC/min (low heating rate) and 100 ºC/min (high heating rate). The process time for maximum temperature was set in 20 minutes for all carbonization experiments and at the end of the process the furnace was opened and the tube was removed to promote a condition of fast cooling to the room temperature.

The carbonization processes were analyzed by mass loss and shrinkage measurements of each sample. The densities were determined by the sink-float method (ASTMC 3800) and specific gravities were measured by helium ultra pycnometer. The microstructures of the fibers were analyzed using Scanning Electron Microscopy (SEM) NovaNanoSEM 400. The specific surface area and pore size distribution were determined by means of isotherm CO2 using the Micromeritics ASAP 2020 and the DA analysis method.

 

3. Results and Discussion

3.1. Oxidized PAN fiber analysis

The oxidized PAN fiber experimentally produced by Multivacuo (MV-OPAN), and commercial (PANOX® - 5.0 dtex) characterization results, are presented in Table 1. The MV-OPAN fiber presents higher density and similar mechanical properties in comparison with the PANOX®. Main differences between these two types of fibers are their filament cross section geometry and average moisture adsorption capability. Our fibers present a beam like cross section while the PANOX® one is circular, and the humidity content is 5% which is lesser than 9% of PANOX®, considered suitable for CF precursor oxidized PAN fiber7.

3.2. Mass loss and shrinkage of MV-OPAN fibers during their carbonization

The curves presented in Figure 2 show the mass loss evolution as a function of the carbonization temperature for MV-OPAN fiber for both heating rates used in this work (10 and 100 ºC/min). It can be observed that the volatile matters gradually evolved producing mass loss in the order of 50 to 60% for any type of tested treatments. Both curve profiles are similar until 1000 ºC, when a saturation behavior is observed for lower heating rate curve, not visible in the other one. This fact shows us that a lower heating rate promotes a higher molecular condensation reaction leading to a higher carbon yield process.

Figure 3 shows the fiber shrinkage rate as a function of carbonization temperature for both heating rates (10 and 100º C/min). In spite of the similarities observed in the mass loss analysis (Figure 2), the fibers shrank in a different way, showing a certain coherence only for treatments at temperatures between 900 and 1000 ºC. Out of this range of temperatures two heat treatments presented two samples with completely distinct shrinkage behavior, inferring that the physical variation of fibers are strongly affected by energy flux.

For a low heating rate condition, it was observed a gradual and monotonic increase in the shrinkage, with saturation at 9% for temperatures higher than 950 ºC. This curve profile can be correlated with the gradual mass loss observed (Figure 2) for this carbonization condition, while the fibers treated at higher heating rate showed a decrease in their shrinkage for treatment between 650 and 750 ºC, followed by a rapid increment region for higher temperatures (until 900 ºC). The shrinkage for both treatment conditions attained similar value in the temperature range of 900 to 1000 ºC, and finally at temperatures above 1000 ºC a new shrinkage is observed only for samples carbonized at a higher heating rate.

The correlated curves analysis presented in figures 2 and 3 leads to the conclusion that MV-OPAN fiber carbonization is strongly influenced by the heating rate in terms of mass loss (process yield) and shrinkage (fiber physical characteristics).

3.3. Specific gravity and density variation of fibers thermally treated

The sink-float density measurement results and helium ultra pycnometer specific gravity determination for samples treated by 10 ºC/min and 100 ºC/min are respectively shown in Figure 4a, b.

The sink-float method is based on the net volume, while in the helium ultra pycnometer, the volume is deducted by all its accessible pore volume generating higher density values for fibers. Consequently, the differences of values produced by these two methods for the same samples can be inferred to be due to the amount of pores which are not filled by solvent but accessed by He gas.

The analysis of the curves showed in Figure 4a reveals that the pycnometer density of samples, treated at low heating rate, increases with temperature until a maximum value of 1.90 g.cm –3 at 950 ºC, and above it is observed a decrease behavior. The sink-float density curve showed two maximum, first at 850 ºC and second at 1000 ºC, and a valley between them with minimum value (1.68 g.cm –3) at 900 ºC. Similar effects and shapes of curves are also observed for samples treated at higher heating rates (Figure 4b); however, three bands with maximum at 650, 850 and 950 ºC are observed in curves of both methods of density determination. It was verified two maximum differences, first at 900 ºC and second at 950 ºC, respectively for 10 ºC/min and 100 ºC/min. The differences observed can be attributed to a high volatilization reaction evolved in higher heating rate treatment, when compared with the lowest one, in which a polymerization reaction is more pronounced and leads to a lesser level of mass loss (Figure 2).

3.4. Microstructure evolution during the heat treatment analyzed by SEM

Figure 5 shows the commercial oxidized PAN fiber micrographs, and figure 6 shows the longitudinal surface (a) and the cross section (b) SEM micrographs of MV-OPAN. The analysis of these micrographs shows that the PANOX® fiber has both a circular cross section and a lamellar type internal structure aligned with external longitudinal fissures. While, the MV-OPAN (Figure 6) shows a bean-like cross section and smoother internal structure. Along the longitudinal surface of the MV-OPAN a similar pattern with slightly rough and irregular surface can be observed. These different morphology aspects can be indebted to the different polymer composition of the fiber precursor and also to the different oxidation conditions performed on the fibers.

 

 

Figure 7a, b show the SEM micrographs obtained for samples treated at 600 ºC with 10º C/min and 100º C/min, respectively. The comparative analysis of these micrographs with those obtained from MV-OPAN fiber (Figure 6b) shows that the surface of 600 ºC treated fiber is quite similar to the former one, presenting a smoother area with no holes, damages, pits or any other surface disconformities. There are some "powdered" materials on the surface (Figure 7a), but these are assigned as dust particles deposited on the fibers without any consequence to their structure and any other fiber properties.

Increasing the heat treatment temperature up to 1100 ºC a general smoothing on the fibers surface can be observed for both heating rate conditions. This fact is shown by micrographs presented in Figure 8a, b, for samples treated at 10 and 100 ºC/min conditions at 1100 ºC.

A gradual smoothing of the fiber external texture is a result of a carbon structure ordering process which gives rise to a better compacted structure, observed on the surfaces of both samples treated at 1100 ºC. Fibers produced on these conditions display a relatively smooth surface without holes, damages, pits or any other discontinuities.

Representative micrographs from the samples treated at 900 ºC-10 ºC/min, and 950 ºC-100 ºC/min are respectively shown in Figure 9a, b. These treatment conditions are those which provided the highest differences between density values obtained by two distinct measurement methods (Figure 4a, b).

The lower heating rate produces a material with microstructure of nooks at 900 ºC and apparently deep grooves leading to the rough comparison of this texture to a "tree bark" (Figure 9b). Moreover, the sample treated at higher heating rates produces a drastically damaged surface by homogeneously distributed polidispersive macro and mesopores (Figure 9b).

3.5. Specific surface area and pores size distribution for samples treated at 900 ºC-10ºC/min and 950 ºC-100 ºC/min.

For the specific objective to study micropores formation the CO2 isotherm at 273 K was performed by Micromeritics ASAP 2020, these isotherms are showed in Figure 10. The DA (Dubinin-Astakhov) method8 was applied to determine total micropores volume, pores size distribution and micropore surface area. The results are summarized on Table 2.

 

 

Quantitative analyses show that faster heating at 950 ºC is the treatment condition that produces more micropores volume fraction. The specific micropres surface area of this sample was about 8% higher than that produced by lower heating rate condition.

The surface structures and larger pores dimensions for both heating treatment can be observed by micrographs. The 950 ºC-100 ºC/min (Figure 9b) shows deeper grooves between well developed carbon fibrils and circular pores which can be classified as meso and macro pores, being both absent in 900 ºC-100 ºC/min sample (Figure 9b).

Figure 11 shows the pore size distribution curves for both samples. The pore size distribution has a very similar shape for both cases, but for the highest heating rate, the total pore volume is about 5% higher than that presented by the lower heating rate sample. Considering the IUPAC9 and Brunauer/Dubinin10,11, micropore definition (Table 3) all pores found in these samples can be classified as micropore.

 

 

4. Conclusion

Carbonization at temperature from 900 to 950 ºC is considered suitable for weakly activated carbon fibers production in a single step, independently of the heating rate (10 ºC/min or 100 ºC/min).

The density determination by two distinct methods can clearly show the presence of micropores on carbon fiber surface.

The open pores produced on Carbon Fibers surface by 950 ºC-100 ºC/min are polydispersive type, with diameter ranging from 1.3 to 3.5 nm (DA) and also larger pores were observed by SEM micrographs. But it is possible to observe narrow pick below 2 nm pores size

The micropores structure on produced Carbon Fibers gives a Specific Surface Area for micropores of 348 to 469 m2/g (DA), which are both relatively poorly valuable to classify these fibers as highly activated materials, but there can be considered as a positive signal to perform a subsequent activation process, which can probably transform them into an interesting material to apply as adsorption or sieving media.

 

Acknowledgement

The authors thank Alessandro Coelho of Radicifibras Ind. e Com. Ltda for providing fiber samples and equipment for fiber analysis. Ricardo Bicudo for the oxidized PAN fiber analyses. Maria Lucia of INPE and Adair J. Moreira of LSI-USP for SEM analyses. FAPESP for the financial support what made this work possible.

 

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Received: May 6, 2012
Revised: August 20, 2012

 

 

* e-mail: jossano@gmail.com

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