# Functionalization of Carbon Nanofibres Obtained by Floating Catalyst Method

Authors: Adolfo Fernández; Pavel Peretyagin; Washington Solís; Ramón Torrecillas; Amparo Borrell
Journal: Journal of Nanomaterials
 (2015)

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## Abstract

The excellent physicochemical and electrical properties of carbon nanofibres (CNF) combined with the possibility of being produced at industrial scale at reasonable costs have promoted the interest in their use in very diverse areas. However, there are still some drawbacks that must be solved in order to optimize their set of properties such as the presence of impurities or the imperfections in the crystalline structure. In this work, different modification treatments of CNFs produced by the floating catalyst method have been studied. Three types of modification processes have been explored that can be grouped as mechanical, thermal, and chemical functionalization processes. Mechanical processing has allowed solving the agglomeration problem related to CNFs produced by floating catalyst method and the resulting modified product ensures the secure handling of carbon nanofibres. Thermal and chemical treatments lead to purer and more crystalline products by removing catalyst impurities and amorphous carbon. Functionalization processes explored in this work open the possibility of customized posttreatment of carbon nanofibres according to the desired requirements.


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## Body

## 1. Introduction

The study of carbon nanomaterials such as carbon nanotubes, carbon nanofibres, and graphene has emerged during the last years due to their excellent physicochemical properties and their huge potential applications [1–4]. Carbon nanofilaments are produced since more than two decades by using different catalysers with hydrocarbon sources in gaseous phase [5–7]. However, the interest in this type of materials clearly increased after the discovery of multiwall nanotubes (MWNT) by Iijima [8] in 1991, single wall nanotubes (SWNT) by Iijima and Ichihashi [9] and Bethune et al. [10] in 1993, and more recently graphene [11]. Nowadays, the research on carbon nanomaterials is one of the most active research topics in the nanoscience and nanotechnology fields.Carbon nanofibres (CNFs) are a very attractive material from the economic point of view. CNFs combine very interesting mechanical and electrical properties with reduced production costs in comparison with carbon nanotubes (CNTs), what could facilitate their incorporation to different mass production industrial sectors such as reinforcing phases in thermostable or thermoplastic polymers, supercapacitors, ion-lithium batteries, gas storage, catalyzer supports, and electroconductive ceramics. CNFs are dimensionally similar to CNTs but they differ in the structure. Thus, CNFs show nonconcentric graphene planes and they are classified in different types according to their structure [12], such as “platelet,” “fishbone,” “ribbon,” or “stacked cup.”From a general point of view, CNFs growth in gaseous phase can be described as a solid material with length: diameter ratio higher than 10 : 1, a diameter <100 nm, and a carbon content >90%. The synthesis takes place by the catalytic decomposition of a carbon source (hydrocarbons or CO) at a temperature ranging from 500 to 1200°C and using a transition metal such as Fe, Co, Ni, or Cu as catalyzer. Among the different methods of production in gaseous phase, the floating catalyst method is especially interesting as it allows the continuous production of CNFs enabling the industrial use of this product. In this work, they are used CNFs produced by floating catalyst method. Nickel was used as catalyzer [13]. Briefly, the solution of nickel catalyzer is injected in the reactor and a sulfur source is added [14] while from the upper part of the reactor it incorporated natural gas as carbon source and hydrogen gas as carrier keeping a reductive atmosphere during the process. Synthesis temperature is controlled around 1100°C. The importance of the sulfur role during CNFs synthesis has been previously described [15–18], which must be added independently from the catalyzer used.Despite the economic advantages related to CNFs production, their lower properties in comparison with CNTs are limiting their incorporation as a mass product in the market. The main features that must be improved in the case of CNFs are three, chemical purity, structural order, and surface properties. The objective of this work is to functionalize the as synthesized CNFs by different treatments. The purpose is to enhance their final properties in order to increase their interest as advanced material. In particular, different mechanical, chemical, and thermal treatments were studied and the evolution of the CNFs properties was evaluated in comparison with raw CNFs.


## 2. Materials and Methods

### 2.1. Starting Materials

In Table1, the properties of the starting carbon nanofibres used in this work are described.Table 1
Properties of starting nanofibers.
Nanofibre average diameter
20–80 nm
Nanofibre average length
>30μm
Density
>1.97 g/cm3
Specific surface
150–200 m2/g
Graphitization degree
~70%
Electrical resistivity
10−2 Ω·cm
Metallic particles content (Ni)
6–8 wt%


### 2.2. Description of Posttreatment Procedures

Functionalization processes studied in this work can be divided in three subcategories, mechanical, thermal, and chemical posttreatments.


#### 2.2.1. Mechanical Modification

Mechanical treatments were carried out with a high energy attrition mill (Union Process, USA). The attrition mill has a central axis equipped with perpendicular ceramic bars that is placed into a container filled with alumina media of 2 mm diameter and the material (CNFs) using anhydrous 99.97% ethanol as solvent. Then, 350 rpm rotation speed was applied for 1 hour. After this time, rotation speed was reduced to 50 rpm and the slurry was extracted through the exit at the bottom of the container. This slurry was firstly dried at 60°C and the resulting cake was finally dried at 120°C. Finally, the dried powder was passed through a 63μm sieve.


#### 2.2.2. Thermal Treatments

Different thermal treatments were used in order to study their influence on the purity and the crystallinity order of CNFs. Thermal treatments cover from relatively low temperature carbonization process to high temperature graphitization tests.Carbonization treatments were carried out in a tubular furnace (Agni, Germany), under continuous flow of 500 mL/min of high purity nitrogen (Alphagaz, Air Liquide) at temperature range 1100–1500°C for two hours. 2 g of CNFs introduced in a ceramic crucible was used in each test.On the other hand, graphitization test was carried out with 1 g of CNFs previously carbonized that was heated in a graphite crucible up to 2700°C in a graphite furnace, under argon flow, at a heating rate of 10°C/min. Sample was kept at this temperature for 1 h.


#### 2.2.3. Modification with Chemical Solvents

Different chemical reagents were used for exploring the surface modification of CNFs and the efficiency of removing impurities. HCl, HNO3, H2O2, H3PO4, and H2SO4 (Sigma-Aldrich) were used as chemical reagents. In a typical experiment, CNFs are mixed with the chemical solvent in 1 : 100 weight ratios and the mixture is heated under reflux at 80°C for 1 hour. Then, the slurry is filtered and washed with distilled water until no variation of the water pH is observed. Then, the solid is dried at 120°C for 48 hours.


### 2.3. Characterization Techniques

#### 2.3.1. Chemical Analysis

Carbon, hydrogen, nitrogen, and sulfur content was determined by combustion of 1 mg of sample in a LECO-CHNS-932 apparatus. Oxygen content was determined by direct measuring using a graphite furnace LECO-VTF-900 coupled with the apparatus previously described.Nickel content was determined by atomic absorption spectroscopy (apparatus AA-6300 Shimadzu) with background correction with deuterium lamp (BGD-D2). The procedure included the wet extraction of nickel with microwaves.


#### 2.3.2. Raman Spectroscopy

Raman spectroscopy was carried out with a Raman modular XY apparatus (DILOR), with CCD4 detector using a 532 nm excitation source (laser spectra-physics 265). The power was 20 mW and slit width was 200μm. Spectra were deconvoluted by Lorentzian/Gaussian adjustment.


#### 2.3.3. Scanning Electron Microscopy

Micrographs of synthesized and postmilled carbon nanofibres were obtained with scanning electron microscopy (SEM, Zeiss DSM 950).


#### 2.3.4. Differential Thermal Analysis and Thermogravimetry

DTA and TG analyses were carried out using TA INSTRUMENTS Model SDT 2960 and TGA/DSC1 METTLER TOLEDO GC 200 equipment, respectively. These apparatus analyzed both phenomena simultaneously either under inert atmosphere or air. They used Pt crucible for all the tests.


## 2.1. Starting Materials

In Table1, the properties of the starting carbon nanofibres used in this work are described.Table 1
Properties of starting nanofibers.
Nanofibre average diameter
20–80 nm
Nanofibre average length
>30μm
Density
>1.97 g/cm3
Specific surface
150–200 m2/g
Graphitization degree
~70%
Electrical resistivity
10−2 Ω·cm
Metallic particles content (Ni)
6–8 wt%


## 2.2. Description of Posttreatment Procedures

Functionalization processes studied in this work can be divided in three subcategories, mechanical, thermal, and chemical posttreatments.


### 2.2.1. Mechanical Modification

Mechanical treatments were carried out with a high energy attrition mill (Union Process, USA). The attrition mill has a central axis equipped with perpendicular ceramic bars that is placed into a container filled with alumina media of 2 mm diameter and the material (CNFs) using anhydrous 99.97% ethanol as solvent. Then, 350 rpm rotation speed was applied for 1 hour. After this time, rotation speed was reduced to 50 rpm and the slurry was extracted through the exit at the bottom of the container. This slurry was firstly dried at 60°C and the resulting cake was finally dried at 120°C. Finally, the dried powder was passed through a 63μm sieve.


### 2.2.2. Thermal Treatments

Different thermal treatments were used in order to study their influence on the purity and the crystallinity order of CNFs. Thermal treatments cover from relatively low temperature carbonization process to high temperature graphitization tests.Carbonization treatments were carried out in a tubular furnace (Agni, Germany), under continuous flow of 500 mL/min of high purity nitrogen (Alphagaz, Air Liquide) at temperature range 1100–1500°C for two hours. 2 g of CNFs introduced in a ceramic crucible was used in each test.On the other hand, graphitization test was carried out with 1 g of CNFs previously carbonized that was heated in a graphite crucible up to 2700°C in a graphite furnace, under argon flow, at a heating rate of 10°C/min. Sample was kept at this temperature for 1 h.


### 2.2.3. Modification with Chemical Solvents

Different chemical reagents were used for exploring the surface modification of CNFs and the efficiency of removing impurities. HCl, HNO3, H2O2, H3PO4, and H2SO4 (Sigma-Aldrich) were used as chemical reagents. In a typical experiment, CNFs are mixed with the chemical solvent in 1 : 100 weight ratios and the mixture is heated under reflux at 80°C for 1 hour. Then, the slurry is filtered and washed with distilled water until no variation of the water pH is observed. Then, the solid is dried at 120°C for 48 hours.


## 2.2.1. Mechanical Modification

Mechanical treatments were carried out with a high energy attrition mill (Union Process, USA). The attrition mill has a central axis equipped with perpendicular ceramic bars that is placed into a container filled with alumina media of 2 mm diameter and the material (CNFs) using anhydrous 99.97% ethanol as solvent. Then, 350 rpm rotation speed was applied for 1 hour. After this time, rotation speed was reduced to 50 rpm and the slurry was extracted through the exit at the bottom of the container. This slurry was firstly dried at 60°C and the resulting cake was finally dried at 120°C. Finally, the dried powder was passed through a 63μm sieve.


## 2.2.2. Thermal Treatments

Different thermal treatments were used in order to study their influence on the purity and the crystallinity order of CNFs. Thermal treatments cover from relatively low temperature carbonization process to high temperature graphitization tests.Carbonization treatments were carried out in a tubular furnace (Agni, Germany), under continuous flow of 500 mL/min of high purity nitrogen (Alphagaz, Air Liquide) at temperature range 1100–1500°C for two hours. 2 g of CNFs introduced in a ceramic crucible was used in each test.On the other hand, graphitization test was carried out with 1 g of CNFs previously carbonized that was heated in a graphite crucible up to 2700°C in a graphite furnace, under argon flow, at a heating rate of 10°C/min. Sample was kept at this temperature for 1 h.


## 2.2.3. Modification with Chemical Solvents

Different chemical reagents were used for exploring the surface modification of CNFs and the efficiency of removing impurities. HCl, HNO3, H2O2, H3PO4, and H2SO4 (Sigma-Aldrich) were used as chemical reagents. In a typical experiment, CNFs are mixed with the chemical solvent in 1 : 100 weight ratios and the mixture is heated under reflux at 80°C for 1 hour. Then, the slurry is filtered and washed with distilled water until no variation of the water pH is observed. Then, the solid is dried at 120°C for 48 hours.


## 2.3. Characterization Techniques

### 2.3.1. Chemical Analysis

Carbon, hydrogen, nitrogen, and sulfur content was determined by combustion of 1 mg of sample in a LECO-CHNS-932 apparatus. Oxygen content was determined by direct measuring using a graphite furnace LECO-VTF-900 coupled with the apparatus previously described.Nickel content was determined by atomic absorption spectroscopy (apparatus AA-6300 Shimadzu) with background correction with deuterium lamp (BGD-D2). The procedure included the wet extraction of nickel with microwaves.


### 2.3.2. Raman Spectroscopy

Raman spectroscopy was carried out with a Raman modular XY apparatus (DILOR), with CCD4 detector using a 532 nm excitation source (laser spectra-physics 265). The power was 20 mW and slit width was 200μm. Spectra were deconvoluted by Lorentzian/Gaussian adjustment.


### 2.3.3. Scanning Electron Microscopy

Micrographs of synthesized and postmilled carbon nanofibres were obtained with scanning electron microscopy (SEM, Zeiss DSM 950).


### 2.3.4. Differential Thermal Analysis and Thermogravimetry

DTA and TG analyses were carried out using TA INSTRUMENTS Model SDT 2960 and TGA/DSC1 METTLER TOLEDO GC 200 equipment, respectively. These apparatus analyzed both phenomena simultaneously either under inert atmosphere or air. They used Pt crucible for all the tests.


## 2.3.1. Chemical Analysis

Carbon, hydrogen, nitrogen, and sulfur content was determined by combustion of 1 mg of sample in a LECO-CHNS-932 apparatus. Oxygen content was determined by direct measuring using a graphite furnace LECO-VTF-900 coupled with the apparatus previously described.Nickel content was determined by atomic absorption spectroscopy (apparatus AA-6300 Shimadzu) with background correction with deuterium lamp (BGD-D2). The procedure included the wet extraction of nickel with microwaves.


## 2.3.2. Raman Spectroscopy

Raman spectroscopy was carried out with a Raman modular XY apparatus (DILOR), with CCD4 detector using a 532 nm excitation source (laser spectra-physics 265). The power was 20 mW and slit width was 200μm. Spectra were deconvoluted by Lorentzian/Gaussian adjustment.


## 2.3.3. Scanning Electron Microscopy

Micrographs of synthesized and postmilled carbon nanofibres were obtained with scanning electron microscopy (SEM, Zeiss DSM 950).


## 2.3.4. Differential Thermal Analysis and Thermogravimetry

DTA and TG analyses were carried out using TA INSTRUMENTS Model SDT 2960 and TGA/DSC1 METTLER TOLEDO GC 200 equipment, respectively. These apparatus analyzed both phenomena simultaneously either under inert atmosphere or air. They used Pt crucible for all the tests.


## 3. Results and Discussion

### 3.1. Modification by Attrition Milling

The CNFs used in this work were produced by the floating catalyst method; that is, a catalyst is injected at high temperature in presence of a hydrocarbon source. As consequence, the product is obtained while the current is passing the chamber in form of balls where the CNFs are intertwined [19]. A first negative consequence of this result is the difficulty for dispersing the CNFs in polymeric or ceramic matrices. Secondly, the low density of the CNFs balls due to the air occluded inside enhances the liberation to the environment during handling increasing the security risks that could be even more important in an industrial scale use. Then, the first posttreatment studied was the mechanical milling of CNFs balls by attrition milling in order to condition the raw material for more secure handling and in order to get a more easily dispersible product.In Figure1 the micrographs obtained by SEM corresponding to starting and milled CNFs are shown, respectively. In the low magnification micrographs ((a) and (c)) it is observed that the average sizes of microgranules are similar. Granule of starting CNFs corresponds to produced nanofibres while the granule size of milled CNFs can be adjusted depending on the sieve used. Then, the use of 63 μm sieve allows obtaining granule with similar average size as the original CNFs. Nevertheless, the comparison of high magnification micrographs ((b) and (d)) shows how the granules obtained after milling are significantly more compacted. They are formed by shorter nanofibres efficiently packed while the original granules are formed by larger and knotted nanofibres. This result has been quantified by measuring the tap density following the ISO 23145-1:2007 standard. Tap density of CNFs increased from 0.08 to 0.41 g/cm3 after the attrition milling process, that is, five times higher as consequence of the efficient compaction as it was observed by SEM. It has been also proved that milled CNFs handling is similar to conventional micrometer size powders. This result is very promising from the security point of view.Figure 1
SEM micrographs of original ((a) and (b)) and mechanically milled ((c) and (d)) CNFs.In Table2, the results of the chemical analysis of raw CNFs and the different products obtained after the functionalization posttreatments are shown. In the case of milled CNFs, as it could be expected, chemical composition is very similar to raw CNFs. A slightly simultaneous decrease of C content and increase of H and O are only observed. This result is due to the presence of low amounts of ethanol in milled CNFs. It has been quantified by TG/DTA that around 3 wt% of ethanol is absorbed in milled CNFs.Table 2
Chemical analysis of original, mechanical milled, and thermally and chemically treated CNFs.
%
Original CNFs
Milled CNFs
CNFs carbonized1100°C
CNFs carbonized1500°C
CNFs graphitized2700°C
CNFs H2O2
CNFs H3PO4
CNFs HCl
CNFs H2SO4
CNFs HNO3
C
88.33 ± 0.87
86.64 ± 0.77
88.64 ± 0.75
89.42 ± 0.66
98.92 ± 0.21
88.50 ± 0.26
90.14 ± 0.44
95.54 ± 0.76
94.13 ± 0.66
93.09 ± 0.32
H
0.43 ± 0.07
0.94 ± 0.09
0.20 ± 0.03
0.11 ± 0.02
0.05 ± 0.01
0.69 ± 0.12
0.63 ± 0.08
0.56 ± 0.10
0.34 ± 0.06
0.67 ± 0.07
N
0.20 ± 0.04
0.18 ± 0.02
0.50 ± 0.08
0.48 ± 0.11
0.04 ± 0.01
0.17 ± 0.03
0.16 ± 0.04
0.19 ± 0.06
1.95 ± 0.10
1.39 ± 0.12
S
0.69 ± 0.12
0.98 ± 0.11
0.47 ± 0.09
0.12 ± 0.03
0.01 ± 0.001
0.22 ± 0.08
0.74 ± 0.12
0.17 ± 0.03
0.59 ± 0.07
0.12 ± 0.01
O
2.11 ± 0.23
3.68 ± 0.19
0.38 ± 0.02
0.21 ± 0.02
0.51 ± 0.11
3.62 ± 0.24
2.58 ± 0.32
1.23 ± 0.09
1.41 ± 0.09
3.86 ± 0.14
Ni
8.00 ± 0.39
8.00 ± 0.35
10.00 ± 0.45
10.00 ± 0.53
0.55 ± 0.09
6.80 ± 0.34
5.70 ± 0.47
2.35 ± 0.32
2.04 ± 0.27
0.60 ± 0.08


### 3.2. Purification by Thermal Treatments

Production of CNFs by the floating catalyst procedure is a very efficient method from the point of view of industrial scaling-up but the short times of contact among the catalyst particles and the carbon sources lead to incomplete transformation of hydrocarbon into graphitic products. Thus, from the chemical analysis of produced CNFs it can be observed that the C content is ~88 wt% (~95 wt% excluding Ni) including amorphous carbon. Then, this section explores the possibility of increasing CNFs purity by applying different thermal treatments from carbonization processes for removing volatile compounds to high temperature graphitization treatments for improving the crystallinity degree of CNFs.It is known that thermal treatments at temperatures higher than the melting point of condensed product are efficient for increasing the purity of the carbon material [20–22]. Thus, two carbonization treatments were studied, the final temperatures being 1100 and 1500°C, respectively, and the stay at the maximum temperature 2 h. In Table 2 the results from the chemical analysis can be seen. It is observed how the sulfur content is reduced to 85% after heating at 1500°C. It is expected that residual sulfur is forming nickel sulfide in the catalyst particles [19]. The reduction in oxygen content is also noticeable, even for the lower temperature treatment (1100°C). These results together with the progressive reduction in hydrogen content are proving the removal of volatile compounds enriched in O, S, and H and, therefore, an increase in the C content. The increase in the relative content of Ni due to the removal of the volatile compounds hinders the increase in C content in CNFs. Thus, if the relative content in C is recalculated excluding the Ni content, it is observed how the C content is increased from 95% for the original CNFs to 98% and 99% when the sample is carbonized at 1100 and 1500°C, respectively.Removal of volatile compounds can also modify the thermal stability of CNFs. The resistance to burn of original and carbonized CNFs by TG/DTA analysis under air atmosphere was studied. The resulting curves are shown in Figure2. A significant delay in the starting burning temperature in the case of carbonized CNFs is observed. Whereas original CNFs burn from 510°C, CNFs carbonized at 1100 and 1500°C start at 570 and 600°C, respectively. Then, stability against oxidation has been significantly improved (~100°C) which is especially interesting for those applications in which the final component can be submitted to high temperatures such as ceramic-CNFs composites.Figure 2
TG curves under air atmosphere of original and carbonized CNFs.Following the strategy of purification by thermal treatments, the effect of a graphitization treatment at 2700°C was also studied. Graphitization of CNFs has been previously studied in order to evaluate the morphological changes in their graphitic structure [23–25]. From the data shown in Table 2, the effectivity of the graphitization treatment from the purification point of view can be clearly observed. Thus, the C content is 99% and only residual O and Ni contents are detected. In concordance with the results previously discussed for carbonized CNFs, the resistance to oxidation is further improved in the case of graphitized CNFs and the starting burning temperature is delayed until 650°C.The second objective of the thermal treatments is to improve the CNFs crystallographic degree. This effect was studied by Raman spectroscopy. Figure3 shows the Raman spectra corresponding to original CNFs and CNFs thermal-treated at 1100, 1500, and 2700°C. First order spectra (1200–1700 cm−1) only show two peaks, G~1580 cm−1 related with graphitic material and D~1350 cm−1 related with imperfections in the crystalline structure. In the second order spectra (2500–2900 cm−1), G′ appears as the only well-defined band ~2700 cm−1. These bands allow comparing the crystalline order of carbon materials [26]. A significant increase in the relative intensity of G and G′ bands is observed accompanied with a decrease in the band width when the temperature of the thermal treatment is increased, especially in the case of graphitization process at 2700°C. Table 3 shows the relative intensity of D band and the position of G band in order to compare the results quantitatively. The decrease of relative D band intensity when the CNFs are thermal-treated is observed, especially in the case of graphitized nanofibres as well as the displacement of G band to higher wavenumber. Both results are related with an increase in the structural order.Table 3
Parameters calculated from first order Raman spectra for original and thermally treated CNFs.
Material
υ
G
I
D
/
I
T
CNFs
1572.9
55
CNFs 1100°C
1573.2
49
CNFs 1500°C
1575.3
50
CNFs 2700°C
1582.2
35
υ
G corresponds to G band position (cm−1 ± 1) and ID/IT relative intensity ratio IT=(ID+IG).Figure 3
Raman spectra of original and thermally treated CNFs.


### 3.3. Purification by Chemical Treatments

Finally, the chemical purification of synthesized CNFs has been studied. CNFs contain Ni nanoparticles from the synthesis and removal of these metal impurities can be interesting for specific applications. Moreover, the surface functionalization with chemical groups can enhance the dispersion of CNFs in ceramic and polymeric matrices which is a great challenge. Taking into account both objectives simultaneously, treatment with chemical reagents appears as a very promising method. Thus, chloride acid is recognized as a very suitable reagent for dissolving metals while nitric and sulfuric acids have more oxidant power [27, 28].In this work, the effect of using five different chemical reagents has been studied, HCl, HNO3, H2O2, H3PO4, and H2SO4. Table 2 shows the results of the chemical analysis of resulting CNFs. Concerning Ni removal, the most efficient chemical reagent was HNO3 that reduced the Ni content to <1%. The high oxidant power of nitric acid which can facilitate the partial oxidation of CNFs [29] allowing the extraction of Ni occluded inside the CNFs is known. On the other side, H2O2 leads to the lowest Ni removal rate. H2O2 has partially oxidized the nanofibre as it can be concluded from the oxygen content similar to the corresponding HNO3 treated CNFs but without effective Ni dissolution. Concerning HCl, H2SO4, and H3PO4 treatments, they lead to partial reduction of Ni content. The result obtained after H3PO4 treatment is remarkable in which a slight reduction of Ni content is observed but S content remains similar to original CNFs. Catalyst particles are formed by Ni/Ni sulfide [19]. Then, it can be deduced that H3PO4 treatment dissolves selectively the metallic particles. This result has been corroborated by XRD where nickel sulfide (NiS) peaks are easily detected.The resistance to oxidation of resulting CNFs after chemical modification has been studied. Burning profile is similar but significant differences can be observed from a more detailed analysis of the data shown in Table4, where temperatures of initial weight loss, final weight loss, and maximum weight loosing rate are described. Starting burning temperature slightly decreases after chemical modification especially in the case of HNO3 treatment. The presence of more oxygenated groups facilitates the starting of material removal. However, the final temperature is similar for all the samples with a maximum difference of <20°C. Despite the lower temperature to CNFs burning after chemical treatments, the maximum rate of weight losses is delayed and, therefore, the average stability of the nanofibres is increased. During the chemical treatments, impurities and low crystallinity components adhered to CNFs are removed. Although the partial oxidation of carbon nanofibres allows an early starting of material removal, after the elimination of the generated oxygenated groups, the remaining material is more stable as it is mainly formed by high crystallinity material.Table 4
TG analysis under air atmosphere of original and chemically treated CNFs.
Sample
T
i
a
T
f
b
T
max
⁡
c
CNFs
480
710
550
CNFs H2O2
480
715
578
CNFs H3PO4
470
704
580
CNFs HCl
473
700
606
CNFs H2SO4
473
700
603
CNFs HNO3
440
697
585
aStarting temperature of weight loss (°C).
bFinal temperature of weight loss (°C).
cTemperature for maximum rate of weight loss.


## 3.1. Modification by Attrition Milling

The CNFs used in this work were produced by the floating catalyst method; that is, a catalyst is injected at high temperature in presence of a hydrocarbon source. As consequence, the product is obtained while the current is passing the chamber in form of balls where the CNFs are intertwined [19]. A first negative consequence of this result is the difficulty for dispersing the CNFs in polymeric or ceramic matrices. Secondly, the low density of the CNFs balls due to the air occluded inside enhances the liberation to the environment during handling increasing the security risks that could be even more important in an industrial scale use. Then, the first posttreatment studied was the mechanical milling of CNFs balls by attrition milling in order to condition the raw material for more secure handling and in order to get a more easily dispersible product.In Figure1 the micrographs obtained by SEM corresponding to starting and milled CNFs are shown, respectively. In the low magnification micrographs ((a) and (c)) it is observed that the average sizes of microgranules are similar. Granule of starting CNFs corresponds to produced nanofibres while the granule size of milled CNFs can be adjusted depending on the sieve used. Then, the use of 63 μm sieve allows obtaining granule with similar average size as the original CNFs. Nevertheless, the comparison of high magnification micrographs ((b) and (d)) shows how the granules obtained after milling are significantly more compacted. They are formed by shorter nanofibres efficiently packed while the original granules are formed by larger and knotted nanofibres. This result has been quantified by measuring the tap density following the ISO 23145-1:2007 standard. Tap density of CNFs increased from 0.08 to 0.41 g/cm3 after the attrition milling process, that is, five times higher as consequence of the efficient compaction as it was observed by SEM. It has been also proved that milled CNFs handling is similar to conventional micrometer size powders. This result is very promising from the security point of view.Figure 1
SEM micrographs of original ((a) and (b)) and mechanically milled ((c) and (d)) CNFs.In Table2, the results of the chemical analysis of raw CNFs and the different products obtained after the functionalization posttreatments are shown. In the case of milled CNFs, as it could be expected, chemical composition is very similar to raw CNFs. A slightly simultaneous decrease of C content and increase of H and O are only observed. This result is due to the presence of low amounts of ethanol in milled CNFs. It has been quantified by TG/DTA that around 3 wt% of ethanol is absorbed in milled CNFs.Table 2
Chemical analysis of original, mechanical milled, and thermally and chemically treated CNFs.
%
Original CNFs
Milled CNFs
CNFs carbonized1100°C
CNFs carbonized1500°C
CNFs graphitized2700°C
CNFs H2O2
CNFs H3PO4
CNFs HCl
CNFs H2SO4
CNFs HNO3
C
88.33 ± 0.87
86.64 ± 0.77
88.64 ± 0.75
89.42 ± 0.66
98.92 ± 0.21
88.50 ± 0.26
90.14 ± 0.44
95.54 ± 0.76
94.13 ± 0.66
93.09 ± 0.32
H
0.43 ± 0.07
0.94 ± 0.09
0.20 ± 0.03
0.11 ± 0.02
0.05 ± 0.01
0.69 ± 0.12
0.63 ± 0.08
0.56 ± 0.10
0.34 ± 0.06
0.67 ± 0.07
N
0.20 ± 0.04
0.18 ± 0.02
0.50 ± 0.08
0.48 ± 0.11
0.04 ± 0.01
0.17 ± 0.03
0.16 ± 0.04
0.19 ± 0.06
1.95 ± 0.10
1.39 ± 0.12
S
0.69 ± 0.12
0.98 ± 0.11
0.47 ± 0.09
0.12 ± 0.03
0.01 ± 0.001
0.22 ± 0.08
0.74 ± 0.12
0.17 ± 0.03
0.59 ± 0.07
0.12 ± 0.01
O
2.11 ± 0.23
3.68 ± 0.19
0.38 ± 0.02
0.21 ± 0.02
0.51 ± 0.11
3.62 ± 0.24
2.58 ± 0.32
1.23 ± 0.09
1.41 ± 0.09
3.86 ± 0.14
Ni
8.00 ± 0.39
8.00 ± 0.35
10.00 ± 0.45
10.00 ± 0.53
0.55 ± 0.09
6.80 ± 0.34
5.70 ± 0.47
2.35 ± 0.32
2.04 ± 0.27
0.60 ± 0.08


## 3.2. Purification by Thermal Treatments

Production of CNFs by the floating catalyst procedure is a very efficient method from the point of view of industrial scaling-up but the short times of contact among the catalyst particles and the carbon sources lead to incomplete transformation of hydrocarbon into graphitic products. Thus, from the chemical analysis of produced CNFs it can be observed that the C content is ~88 wt% (~95 wt% excluding Ni) including amorphous carbon. Then, this section explores the possibility of increasing CNFs purity by applying different thermal treatments from carbonization processes for removing volatile compounds to high temperature graphitization treatments for improving the crystallinity degree of CNFs.It is known that thermal treatments at temperatures higher than the melting point of condensed product are efficient for increasing the purity of the carbon material [20–22]. Thus, two carbonization treatments were studied, the final temperatures being 1100 and 1500°C, respectively, and the stay at the maximum temperature 2 h. In Table 2 the results from the chemical analysis can be seen. It is observed how the sulfur content is reduced to 85% after heating at 1500°C. It is expected that residual sulfur is forming nickel sulfide in the catalyst particles [19]. The reduction in oxygen content is also noticeable, even for the lower temperature treatment (1100°C). These results together with the progressive reduction in hydrogen content are proving the removal of volatile compounds enriched in O, S, and H and, therefore, an increase in the C content. The increase in the relative content of Ni due to the removal of the volatile compounds hinders the increase in C content in CNFs. Thus, if the relative content in C is recalculated excluding the Ni content, it is observed how the C content is increased from 95% for the original CNFs to 98% and 99% when the sample is carbonized at 1100 and 1500°C, respectively.Removal of volatile compounds can also modify the thermal stability of CNFs. The resistance to burn of original and carbonized CNFs by TG/DTA analysis under air atmosphere was studied. The resulting curves are shown in Figure2. A significant delay in the starting burning temperature in the case of carbonized CNFs is observed. Whereas original CNFs burn from 510°C, CNFs carbonized at 1100 and 1500°C start at 570 and 600°C, respectively. Then, stability against oxidation has been significantly improved (~100°C) which is especially interesting for those applications in which the final component can be submitted to high temperatures such as ceramic-CNFs composites.Figure 2
TG curves under air atmosphere of original and carbonized CNFs.Following the strategy of purification by thermal treatments, the effect of a graphitization treatment at 2700°C was also studied. Graphitization of CNFs has been previously studied in order to evaluate the morphological changes in their graphitic structure [23–25]. From the data shown in Table 2, the effectivity of the graphitization treatment from the purification point of view can be clearly observed. Thus, the C content is 99% and only residual O and Ni contents are detected. In concordance with the results previously discussed for carbonized CNFs, the resistance to oxidation is further improved in the case of graphitized CNFs and the starting burning temperature is delayed until 650°C.The second objective of the thermal treatments is to improve the CNFs crystallographic degree. This effect was studied by Raman spectroscopy. Figure3 shows the Raman spectra corresponding to original CNFs and CNFs thermal-treated at 1100, 1500, and 2700°C. First order spectra (1200–1700 cm−1) only show two peaks, G~1580 cm−1 related with graphitic material and D~1350 cm−1 related with imperfections in the crystalline structure. In the second order spectra (2500–2900 cm−1), G′ appears as the only well-defined band ~2700 cm−1. These bands allow comparing the crystalline order of carbon materials [26]. A significant increase in the relative intensity of G and G′ bands is observed accompanied with a decrease in the band width when the temperature of the thermal treatment is increased, especially in the case of graphitization process at 2700°C. Table 3 shows the relative intensity of D band and the position of G band in order to compare the results quantitatively. The decrease of relative D band intensity when the CNFs are thermal-treated is observed, especially in the case of graphitized nanofibres as well as the displacement of G band to higher wavenumber. Both results are related with an increase in the structural order.Table 3
Parameters calculated from first order Raman spectra for original and thermally treated CNFs.
Material
υ
G
I
D
/
I
T
CNFs
1572.9
55
CNFs 1100°C
1573.2
49
CNFs 1500°C
1575.3
50
CNFs 2700°C
1582.2
35
υ
G corresponds to G band position (cm−1 ± 1) and ID/IT relative intensity ratio IT=(ID+IG).Figure 3
Raman spectra of original and thermally treated CNFs.


## 3.3. Purification by Chemical Treatments

Finally, the chemical purification of synthesized CNFs has been studied. CNFs contain Ni nanoparticles from the synthesis and removal of these metal impurities can be interesting for specific applications. Moreover, the surface functionalization with chemical groups can enhance the dispersion of CNFs in ceramic and polymeric matrices which is a great challenge. Taking into account both objectives simultaneously, treatment with chemical reagents appears as a very promising method. Thus, chloride acid is recognized as a very suitable reagent for dissolving metals while nitric and sulfuric acids have more oxidant power [27, 28].In this work, the effect of using five different chemical reagents has been studied, HCl, HNO3, H2O2, H3PO4, and H2SO4. Table 2 shows the results of the chemical analysis of resulting CNFs. Concerning Ni removal, the most efficient chemical reagent was HNO3 that reduced the Ni content to <1%. The high oxidant power of nitric acid which can facilitate the partial oxidation of CNFs [29] allowing the extraction of Ni occluded inside the CNFs is known. On the other side, H2O2 leads to the lowest Ni removal rate. H2O2 has partially oxidized the nanofibre as it can be concluded from the oxygen content similar to the corresponding HNO3 treated CNFs but without effective Ni dissolution. Concerning HCl, H2SO4, and H3PO4 treatments, they lead to partial reduction of Ni content. The result obtained after H3PO4 treatment is remarkable in which a slight reduction of Ni content is observed but S content remains similar to original CNFs. Catalyst particles are formed by Ni/Ni sulfide [19]. Then, it can be deduced that H3PO4 treatment dissolves selectively the metallic particles. This result has been corroborated by XRD where nickel sulfide (NiS) peaks are easily detected.The resistance to oxidation of resulting CNFs after chemical modification has been studied. Burning profile is similar but significant differences can be observed from a more detailed analysis of the data shown in Table4, where temperatures of initial weight loss, final weight loss, and maximum weight loosing rate are described. Starting burning temperature slightly decreases after chemical modification especially in the case of HNO3 treatment. The presence of more oxygenated groups facilitates the starting of material removal. However, the final temperature is similar for all the samples with a maximum difference of <20°C. Despite the lower temperature to CNFs burning after chemical treatments, the maximum rate of weight losses is delayed and, therefore, the average stability of the nanofibres is increased. During the chemical treatments, impurities and low crystallinity components adhered to CNFs are removed. Although the partial oxidation of carbon nanofibres allows an early starting of material removal, after the elimination of the generated oxygenated groups, the remaining material is more stable as it is mainly formed by high crystallinity material.Table 4
TG analysis under air atmosphere of original and chemically treated CNFs.
Sample
T
i
a
T
f
b
T
max
⁡
c
CNFs
480
710
550
CNFs H2O2
480
715
578
CNFs H3PO4
470
704
580
CNFs HCl
473
700
606
CNFs H2SO4
473
700
603
CNFs HNO3
440
697
585
aStarting temperature of weight loss (°C).
bFinal temperature of weight loss (°C).
cTemperature for maximum rate of weight loss.


## 4. Conclusions

Mechanical, thermal, and chemical functionalizations of carbon nanofibres are efficient treatments for improving different properties of nanofibres obtained by floating catalyst method.Original CNFs are knotted avoiding their efficient dispersion and increasing the health risk during handling due to their extremely low tap density. Mechanical milling allows partial nanofibre breaking eliminating knots and leading to compact and easy dispersible granules. Health risk during handling is minimized and the dispersion of milled product is noticeably improved.Evolution of crystalline order of CNFs with temperature used during thermal treatments was studied by Raman spectroscopy. The efficiency of the treatment is proportional to the final temperature. Partial removal of amorphous carbon can be obtained at relatively low temperature carbonization treatment (1100°C) while completely pure and high crystalline product is obtained after graphitization process.Finally, chemical treatment with different reagents has been explored. Removal of catalyst impurities can be completed by treatment with HNO3 at low temperature (80°C). Resistance to oxidation of resulting carbon nanofibres is improved thanks to the removal of impurities and amorphous carbon.The results obtained in this work open the possibility of designing specific posttreatments of CNFs depending on the desired final properties that would be defined by the final application requirements.



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*Source: 395014-2015-04-06.xml*