# Effects of E-Beam Irradiation on the Chemical, Physical, and Electrochemical Properties of Activated Carbons for Electric Double-Layer Capacitors

Authors: Min-Jung Jung; Mi-Seon Park; Young-Seak Lee
Journal: Journal of Nanomaterials
 (2015)

---

## Abstract

Activated carbons (ACs) were modified via e-beam irradiation at various doses for use as an electrode material in electric double-layer capacitors (EDLCs). The chemical compositions of the AC surfaces were largely unchanged by the e-beam irradiation. The ACs treated with the e-beam at radiation doses of 200 kGy exhibited higher nanocrystallinity than the untreated ACs. The specific surface areas and pore volumes of the e-beam irradiated ACs were also higher than those of the untreated ACs. These results were attributed to the transformation and degradation of the nanocrystallinity of the AC surfaces due to the e-beam irradiation. The specific capacitance of the ACs treated with the e-beam at radiation doses of 200 kGy increased by 24% compared with the untreated ACs, and the charge transfer resistance of the ACs was decreased by the e-beam irradiation. The enhancement of the electrochemical properties of the e-beam irradiated ACs can be attributed to an increase in their specific surface area and surface crystallinity.


---

## Body

## 1. Introduction

Electron-beam (e-beam) irradiation has been of interest in many research fields, such as polymerization and the modification of polymers, lithography, and food science [1–5]. Electron-beam irradiation changes the structures of polymer chains, which induce chain scission, cross-linking, or radical formation [6–8]. Recently, some researchers have attempted to apply e-beam irradiation to various carbon materials (sp3 or sp2 materials), such as carbon nanotubes, graphene, and diamond [9–11]. It is usually intended to study a damage or deposition of carbon materials during analyzing by equipment using the e-beam including scanning electron microscopy (SEM), transmission electron microscopy (TEM), focused ion beam (FIB), and atomic force microscopy (AFM) [12–14]. Generally, e-beam irradiation causes the hemolytic cleavage of C-C and C-H bonds on polymer surfaces. The resulting alkyl radicals are not stable and undergo a complex series of reactions that lead to cross-linking, chain scissions, oxidation, and the formation of C=C bonds [15]. E-beam irradiation is a simple, solvent-free, and ambient-temperature electron-beam-based modification method [16]. Therefore, it is expected that e-beam irradiation is a viable technology for the modification of carbon material surfaces for electrochemical applications, such as electrical double-layer capacitors (EDLCs).In this study, e-beam irradiation was applied to modify activated carbons (ACs) for use as electrode materials in EDLCs. The changes in the physical and chemical properties of the AC surfaces after modification were characterized and analyzed, and the effects of e-beam irradiation on the electrochemical performance of the ACs were also investigated. Through this study, the potential use of the electron-beam irradiation was evaluated.


## 2. Materials and Methods

### 2.1. E-Beam Irradiation of Activated Carbons

In this study, phenol-based AC (MSP-20, Kansai Coke and Chemicals Co., Ltd., Japan) was used. For the e-beam treatment, 2 g of the AC was poured into sample bottles. The sample bottles were placed on a tray for e-beam radiation. E-beam irradiation was performed at 100, 200, 300, and 500 kGy. The prepared samples were named according to the e-beam radiation dose as E100-AC, E200-AC, E300-AC, and E500-AC, and the untreated AC was named R-AC.


### 2.2. Physicochemical Characterization

To investigate the changes in the functional groups on the surfaces of the untreated and e-beam irradiated ACs, X-ray photoelectron spectroscopy (XPS, VG Multilab 2000, Thermo VG Scientific, UK) analysis was performed using Al Kα radiation. XPS elemental analysis was used to determine the average elemental contents in the sample. The C1s peaks were deconvoluted into several pseudo-Voigt functions (sums of a Gaussian-Lorentzian function) using a peak analysis program obtained from Unipress Co., USA. The pseudo-Voigt function is given by [17](1)FE=H1-Sexp⁡⁡-ln⁡⁡2E-E0RFWHM2+S1+E-E0/RFWHM2,where F(E) is the intensity at energy E, H is the peak height, E0 is the peak center, RFWHM is the full width at half-maximum (FWHM), and S is the shape function related to the symmetry and the Gaussian-Lorentzian mixing ratio. The FWHM of the C1s peak was 1.3 eV.To characterize the crystalline structure of the ACs, the Raman spectra were recorded using a HORIBA Jobin-Yvon LabRam Aramis spectrometer (HORIBA Jobin-Yvon, Edison, NJ). The 514 nm arrow of an Ar-ion laser was used as the excitation source. The G and D peak positions and theID/IG intensity ratio are widely used for identifying the type of carbon and characterizing the carbon structure. The resulting Raman spectra were deconvoluted into G and D bands using Gaussian functions.The pore structures of the samples were assessed using N2 adsorption at 77 K (ASAP2020, Micromeritics, USA). The specific surface areas of the samples were evaluated using the Brunauer-Emmett-Teller (BET) equation. In addition, the pore size distributions of the samples were determined using density functional theory (DFT).


### 2.3. Electrochemical Characterization

EDLC electrodes were fabricated by mixing 80 wt% AC, 10 wt% carbon black (Super P, Timcal Ltd., Switzerland), and a 10 wt% solution of polyvinylidene fluoride (PVDF, Aldrich, USA) in N-methyl pyrrolidone (NMP, Aldrich, USA) to form a slurry, which was then painted onto a titanium plate. The AC-based electrodes were electrochemically characterized using a computer-controlled potentiostat/galvanostat (Ivium Technologies, Netherlands) equipped with a three-electrode assembly. The AC-based electrode was used as the working electrode, and Ag∣AgCl was used as the reference electrode. A platinum plate was used as the counter electrode. Cyclic voltammetry (CV) of the electrode materials was performed over a potential range of 0 to 1 V at scan rates of 5 and 50 mV s−1 in a 1 M H2SO4 electrolyte.An AC impedance spectrum analyzer was employed to measure and analyze the impedance behavior of the capacitors. In this work, the measurements were conducted at 0 V with an AC potential amplitude of 5 mV in the frequency range of 10 mHz to 100 kHz.


## 2.1. E-Beam Irradiation of Activated Carbons

In this study, phenol-based AC (MSP-20, Kansai Coke and Chemicals Co., Ltd., Japan) was used. For the e-beam treatment, 2 g of the AC was poured into sample bottles. The sample bottles were placed on a tray for e-beam radiation. E-beam irradiation was performed at 100, 200, 300, and 500 kGy. The prepared samples were named according to the e-beam radiation dose as E100-AC, E200-AC, E300-AC, and E500-AC, and the untreated AC was named R-AC.


## 2.2. Physicochemical Characterization

To investigate the changes in the functional groups on the surfaces of the untreated and e-beam irradiated ACs, X-ray photoelectron spectroscopy (XPS, VG Multilab 2000, Thermo VG Scientific, UK) analysis was performed using Al Kα radiation. XPS elemental analysis was used to determine the average elemental contents in the sample. The C1s peaks were deconvoluted into several pseudo-Voigt functions (sums of a Gaussian-Lorentzian function) using a peak analysis program obtained from Unipress Co., USA. The pseudo-Voigt function is given by [17](1)FE=H1-Sexp⁡⁡-ln⁡⁡2E-E0RFWHM2+S1+E-E0/RFWHM2,where F(E) is the intensity at energy E, H is the peak height, E0 is the peak center, RFWHM is the full width at half-maximum (FWHM), and S is the shape function related to the symmetry and the Gaussian-Lorentzian mixing ratio. The FWHM of the C1s peak was 1.3 eV.To characterize the crystalline structure of the ACs, the Raman spectra were recorded using a HORIBA Jobin-Yvon LabRam Aramis spectrometer (HORIBA Jobin-Yvon, Edison, NJ). The 514 nm arrow of an Ar-ion laser was used as the excitation source. The G and D peak positions and theID/IG intensity ratio are widely used for identifying the type of carbon and characterizing the carbon structure. The resulting Raman spectra were deconvoluted into G and D bands using Gaussian functions.The pore structures of the samples were assessed using N2 adsorption at 77 K (ASAP2020, Micromeritics, USA). The specific surface areas of the samples were evaluated using the Brunauer-Emmett-Teller (BET) equation. In addition, the pore size distributions of the samples were determined using density functional theory (DFT).


## 2.3. Electrochemical Characterization

EDLC electrodes were fabricated by mixing 80 wt% AC, 10 wt% carbon black (Super P, Timcal Ltd., Switzerland), and a 10 wt% solution of polyvinylidene fluoride (PVDF, Aldrich, USA) in N-methyl pyrrolidone (NMP, Aldrich, USA) to form a slurry, which was then painted onto a titanium plate. The AC-based electrodes were electrochemically characterized using a computer-controlled potentiostat/galvanostat (Ivium Technologies, Netherlands) equipped with a three-electrode assembly. The AC-based electrode was used as the working electrode, and Ag∣AgCl was used as the reference electrode. A platinum plate was used as the counter electrode. Cyclic voltammetry (CV) of the electrode materials was performed over a potential range of 0 to 1 V at scan rates of 5 and 50 mV s−1 in a 1 M H2SO4 electrolyte.An AC impedance spectrum analyzer was employed to measure and analyze the impedance behavior of the capacitors. In this work, the measurements were conducted at 0 V with an AC potential amplitude of 5 mV in the frequency range of 10 mHz to 100 kHz.


## 3. Results and Discussion

### 3.1. Changes in the Surface Chemical Properties of the E-Beam Irradiated Activated Carbons

XPS elemental analysis was conducted to compare the surface chemical properties of the ACs before and after e-beam irradiation. As can be observed in Table1 and Figure 1, two main peaks are identified, marked C1s and O1s. The peaks at approximately 970–1 000 eV are the oxygen Auger peaks [18, 19]. As shown in Table 1, the samples are almost identical in terms of elemental composition. The oxygen content of R-AC was found to be approximately 7.3 at%, while the e-beam irradiated ACs had oxygen contents of 6.3–7.1 at%. Therefore, it is concluded that e-beam irradiation does not have a significant effect on the chemical composition of the AC surfaces.Table 1
XPS surface elemental analysis parameters of e-beam irradiated ACs.
Sample
Elemental contents (atomic percent)
O/C (%)
C
O
R-AC
92.7
7.3
7.87
E100-AC
93.4
6.6
7.07
E200-AC
92.9
7.1
7.64
E300-AC
93.3
6.7
7.18
E500-AC
93.7
6.3
6.72Figure 1
XPS wide scan spectra of e-beam irradiated ACs.In particular, to investigate the changes in the chemical bonds of the ACs due to e-beam irradiation, untreated and e-beam irradiated ACs were analyzed using C1s deconvolution. The deconvolution results of the C1s peaks are shown in Figure2. The C1s peaks of all samples were deconvoluted into four peaks at 284.5, 285.4, 286.4, and 287.4 eV, which correspond to C-C (sp2), C-C (sp3), C-O, and C=O, respectively [20]. The components, peak positions, and concentrations are also summarized in Table 2. In this study, E200-AC had the highest concentration of C-C sp2 bonds. The concentration of C-C sp2 bonds on the AC surfaces increased with e-beam irradiation up to 200 kGy, while the concentration of C-C sp3 bonds on the AC surfaces decreased. In contrast, when the e-beam irradiation was performed at above 200 kGy, the concentration of C-C sp2 bonds decreased and the C-C sp3 bonds increased. Thus, e-beam irradiation transformed and degraded the nanocrystals on the AC surfaces [21].Table 2
C1s peak parameters of e-beam irradiated ACs.
Component
Peak position (eV)
Concentration (%)
R-AC
E100-AC
E200-AC
E300-AC
E500-AC
C(1)
C–C (sp2)
284.5
64.1
73.2
74.6
70.3
66.3
C(2)
C–C (sp3)
285.4
19.9
16.5
11.9
18.4
23.9
C(3)
C–O
286.4
11.8
7.5
10.4
8.3
7.7
C(4)
C=O
287.4
4.2
2.8
3.1
3.0
2.1Figure 2
Deconvolution of the core level C1s spectra of (a) R-AC, (b) E100-AC, (c) E200-AC, (d) E300-AC, and (e) E500-AC.
(a)
(b)
(c)
(d)
(e)The Raman spectra were deconvoluted to acquire information about the changes in the carbon structure of the ACs due to e-beam irradiation and are shown in Figure3. The Raman spectra for the ACs were almost similar; therefore, only the Raman spectra of R-AC, E200-AC, and E500-AC are shown in Figure 3. Four peaks were observed at approximately 1605 cm−1 (G1), 1530 cm−1 (G2), 1340–1355 cm−1 (D1), and 1280 cm−1 (D2). The D-peaks (D1 and D2) correspond to the amorphous domains, while the G-peaks (G1 and G2) correspond to the graphite domains. The peak at 1605 cm−1 (G band) is attributed to the typical C-C stretching modes in graphite. The peak observed at approximately 1340–1355 cm−1 was assigned to the D band (related to the defects and disorder in the carbon material), which is typical for disordered carbon [22]. The Raman spectra of R-AC, E200-AC, and E500-AC were almost identical; however, the Raman spectra of E200-AC had a more intense G1 peak than R-AC and E500-AC.Figure 3
Raman spectra of (a) R-AC, (b) E200-AC, and (c) E500-AC.
(a)
(b)
(c)Table3 shows the peak intensity ratios of ID1/IG1,  ID2/IG2, IG2/IG1, and La in the investigated spectral range, which provides important information about the structures of the carbon materials [20]. Based on the following equation, the crystalline size (La) was calculated [23]:(2)La=4.4×ID1IG1-1.It is commonly known that a lower ID2/IG2 ratio indicates a lower amorphous phase content in the carbon material, whereas a lower IG2/IG1 ratio indicates decreasing of the carbon in forms of clusters [24]. According to the Raman results, E200-AC contained the smallest amount of amorphous phase.Table 3
Structure characteristics of e-beam irradiated ACs obtained by the Raman spectra deconvolution.
Intensity ratio
L
a
I
D1
/
I
G1
I
D2
/
I
G2
I
G2
/
I
G1
R-AC
1.86
1.16
2.48
2.36
E200-AC
1.54
0.96
2.36
2.85
E500-AC
1.75
1.24
1.85
2.51For the e-beam energies employed in this study, the primary effect of irradiation in graphitic or sp2 carbon materials is a result of the knock-on collisions of atoms with electrons, which generates vacancies and structural defects (or interstitials) [25]. In addition, the materials are far from thermal equilibrium, that is to say, nonequilibrium, and, under certain circumstances, they can fulfill the conditions for self-organized structure formation. Accordingly, the change in hybridization facilitates the structural transformation sp2+δ, sp3  ↔ sp2, sp2+δ (trigonal ↔ mixed trigonal, tetrahedral) [26]. Therefore, the nanocrystallinity of the AC surface could be increased by e-beam irradiation.


### 3.2. Changes in the Textural Properties of E-Beam Irradiated Activated Carbons

Nitrogen adsorption analysis was performed at 77 K to examine the changes in the pore texture of the ACs after e-beam irradiation at different radiation doses. Table4 provides detailed information about the textural properties of the e-beam irradiated ACs. It was observed that the specific surface area and total pore volume were higher for the e-beam irradiated ACs than for R-AC, except for E500-AC. E200-AC exhibited the highest specific surface area and total pore volume (2339 m2/g and 1.02 cc/g, resp.). These changes in textural properties indicated that the nanocrystallinity of the AC surface was transformed and degraded by the e-beam irradiation. As Raman results in Section 3.2, IG2/IG1 ratio of ACs which indicated reduction of carbon in form of clusters was decreased as increase of e-beam irradiation dose. As mentioned above, the smaller IG2/IG1 ratio led to decreasing of the carbon in forms of clusters [24]. It was expected that specific surface area of e-beam irradiated ACs could be changed by degradation of AC surface. The specific surface area of ACs was increased by appropriate e-beam irradiation dose; however, excessive irradiation dose could reduce the specific surface area of ACs due to collapse of the AC surface.Table 4
Textual properties of e-beam irradiated ACs.
Sample
Specific surface area (m2/g)
Total pore volume (cm3/g)
Micropore volume (cm3/g)
Mesopore volume (cm3/g)
R-AC
1924
0.87
0.76
0.11
E100-AC
2300
0.92
0.88
0.04
E200-AC
2339
1.02
0.99
0.03
E300-AC
2310
0.97
0.96
0.01
E500-AC
1902
0.82
0.79
0.03Figure4 depicts the nitrogen adsorption isotherms of untreated and e-beam irradiated ACs. The isotherms of all samples were observed to be type I according to the IUPAC classification [27]. However, e-beam irradiated ACs seem to be more microporous than R-AC; the adsorption of R-AC gradually increased above a P/P0 ratio of 0.1. Figure 5 shows the DFT pore size distribution, and it can clearly be observed that all of the samples were microporous. In addition, E100-AC exhibited a larger pore volume than the other samples, with pore diameters of 1.5 to 2.0 nm. In general, the performances of the AC-based EDLCs were determined by the textural properties of the ACs [28]. Changes in the specific surface areas, pore volumes, and pore size distributions of the ACs after e-beam irradiation were expected to improve the performances of the prepared AC-based EDLCs.Figure 4
Nitrogen adsorption isotherms of e-beam irradiated ACs.Figure 5
DFT pore size distribution of e-beam irradiated ACs.


### 3.3. Electrochemical Properties of the E-Beam Irradiated Activated Carbons

Cyclic voltammetry (CV) was used to assess the electrochemical properties of the e-beam irradiated AC-based electrodes. Figure6 shows the CV plots of each sample acquired at scan rates of 5 mV/s and 50 mV/s. At a scan rate of 5 mV/s (Figure 6(a)), the CV profiles of the ACs were approximately rectangular, and small redox peaks were observed at 0.3–0.4 V, which indicated the occurrence of a pseudo-Faradaic reaction caused by oxygen functional groups [29]. R-AC had the highest redox peaks in this study because the C=O bonds in the ACs were reduced by the e-beam irradiation. In the CV profiles of the ACs obtained at 50 mV/s (Figure 6(b)), the CVs also exhibited a rectangular shape with small redox peaks.Figure 6
Cyclic voltammograms of e-beam irradiated ACs obtained at 5 mV/s (a) and 50 mV/s (b).
(a)
(b)The discharge capacitances (C) of the electrodes in the EDLCs were calculated using [30](3)C=1wΔV∫01idt,where C is the specific capacitance of the cell in F/g, w is the mass of the active material, i is the current flowing for time dt, and ΔV is the potential window in which the current flows.The calculated specific capacitances of the AC-based electrodes are listed in Table5. In this study, E200-AC exhibited the highest specific capacitances (306 and 262 F/g at scan rates of 5 and 50 mV/s, resp.). The specific capacitances of the e-beam irradiated ACs increased with the e-beam irradiation dose up to 200 kGy and then decreased. These results were expected because the specific surface areas and pore volumes of the ACs were increased by the e-beam irradiation.Table 5
Specific capacitances of e-beam irradiated ACs.
Sample
Specific capacitance (F/g)
5 mV/s
50 mV/s
R-AC
247
157
E100-AC
277
257
E200-AC
306
262
E300-AC
250
229
E500-AC
169
161Figure7 depicts the results of the AC impedance measurements of the prepared AC-based electrodes. The charge transfer resistance (RC) values for R-AC, E100-AC, E200-AC, E300-AC, and E500-AC were calculated to be 1.80, 0.61, 0.56, 0.75, and 3.84 Ω, respectively. The impedance results directly showed that the e-beam irradiation contributed significantly to the reduction of the charge transfer resistance of the ACs, which is in agreement with the change in electrical conductivity [31]. As mentioned above, the nanocrystallinity of the AC surfaces was increased by the e-beam irradiation. Therefore, it can be concluded that the increased nanocrystallinity of the AC surface induced by the e-beam irradiation also decreased the charge transfer resistance. However, the charge transfer resistance of the ACs increased because the nanocrystallinity of the AC surfaces was destroyed by excessive e-beam irradiation (E500-AC). The increasing charge transfer resistance of the e-beam irradiated ACs was expected because of the decrease in the specific capacitance. The charge transfer resistance was generally related to the electroactive surface area of the electrode materials. The electroactive surface area was a combination of the specific surface area and electrical conductivity [32]. R-AC and E500-AC had similar specific surface area, but the charge transfer resistance of E500-AC is higher than R-AC. It was expected that electrical conductivity of E500-AC decreased which causes a reduction in the specific capacitance.Figure 7
Nyquist impedance plots of e-beam irradiated ACs in 1 M H2SO4 in the frequency range from 10 mHz to 100 kHz.


## 3.1. Changes in the Surface Chemical Properties of the E-Beam Irradiated Activated Carbons

XPS elemental analysis was conducted to compare the surface chemical properties of the ACs before and after e-beam irradiation. As can be observed in Table1 and Figure 1, two main peaks are identified, marked C1s and O1s. The peaks at approximately 970–1 000 eV are the oxygen Auger peaks [18, 19]. As shown in Table 1, the samples are almost identical in terms of elemental composition. The oxygen content of R-AC was found to be approximately 7.3 at%, while the e-beam irradiated ACs had oxygen contents of 6.3–7.1 at%. Therefore, it is concluded that e-beam irradiation does not have a significant effect on the chemical composition of the AC surfaces.Table 1
XPS surface elemental analysis parameters of e-beam irradiated ACs.
Sample
Elemental contents (atomic percent)
O/C (%)
C
O
R-AC
92.7
7.3
7.87
E100-AC
93.4
6.6
7.07
E200-AC
92.9
7.1
7.64
E300-AC
93.3
6.7
7.18
E500-AC
93.7
6.3
6.72Figure 1
XPS wide scan spectra of e-beam irradiated ACs.In particular, to investigate the changes in the chemical bonds of the ACs due to e-beam irradiation, untreated and e-beam irradiated ACs were analyzed using C1s deconvolution. The deconvolution results of the C1s peaks are shown in Figure2. The C1s peaks of all samples were deconvoluted into four peaks at 284.5, 285.4, 286.4, and 287.4 eV, which correspond to C-C (sp2), C-C (sp3), C-O, and C=O, respectively [20]. The components, peak positions, and concentrations are also summarized in Table 2. In this study, E200-AC had the highest concentration of C-C sp2 bonds. The concentration of C-C sp2 bonds on the AC surfaces increased with e-beam irradiation up to 200 kGy, while the concentration of C-C sp3 bonds on the AC surfaces decreased. In contrast, when the e-beam irradiation was performed at above 200 kGy, the concentration of C-C sp2 bonds decreased and the C-C sp3 bonds increased. Thus, e-beam irradiation transformed and degraded the nanocrystals on the AC surfaces [21].Table 2
C1s peak parameters of e-beam irradiated ACs.
Component
Peak position (eV)
Concentration (%)
R-AC
E100-AC
E200-AC
E300-AC
E500-AC
C(1)
C–C (sp2)
284.5
64.1
73.2
74.6
70.3
66.3
C(2)
C–C (sp3)
285.4
19.9
16.5
11.9
18.4
23.9
C(3)
C–O
286.4
11.8
7.5
10.4
8.3
7.7
C(4)
C=O
287.4
4.2
2.8
3.1
3.0
2.1Figure 2
Deconvolution of the core level C1s spectra of (a) R-AC, (b) E100-AC, (c) E200-AC, (d) E300-AC, and (e) E500-AC.
(a)
(b)
(c)
(d)
(e)The Raman spectra were deconvoluted to acquire information about the changes in the carbon structure of the ACs due to e-beam irradiation and are shown in Figure3. The Raman spectra for the ACs were almost similar; therefore, only the Raman spectra of R-AC, E200-AC, and E500-AC are shown in Figure 3. Four peaks were observed at approximately 1605 cm−1 (G1), 1530 cm−1 (G2), 1340–1355 cm−1 (D1), and 1280 cm−1 (D2). The D-peaks (D1 and D2) correspond to the amorphous domains, while the G-peaks (G1 and G2) correspond to the graphite domains. The peak at 1605 cm−1 (G band) is attributed to the typical C-C stretching modes in graphite. The peak observed at approximately 1340–1355 cm−1 was assigned to the D band (related to the defects and disorder in the carbon material), which is typical for disordered carbon [22]. The Raman spectra of R-AC, E200-AC, and E500-AC were almost identical; however, the Raman spectra of E200-AC had a more intense G1 peak than R-AC and E500-AC.Figure 3
Raman spectra of (a) R-AC, (b) E200-AC, and (c) E500-AC.
(a)
(b)
(c)Table3 shows the peak intensity ratios of ID1/IG1,  ID2/IG2, IG2/IG1, and La in the investigated spectral range, which provides important information about the structures of the carbon materials [20]. Based on the following equation, the crystalline size (La) was calculated [23]:(2)La=4.4×ID1IG1-1.It is commonly known that a lower ID2/IG2 ratio indicates a lower amorphous phase content in the carbon material, whereas a lower IG2/IG1 ratio indicates decreasing of the carbon in forms of clusters [24]. According to the Raman results, E200-AC contained the smallest amount of amorphous phase.Table 3
Structure characteristics of e-beam irradiated ACs obtained by the Raman spectra deconvolution.
Intensity ratio
L
a
I
D1
/
I
G1
I
D2
/
I
G2
I
G2
/
I
G1
R-AC
1.86
1.16
2.48
2.36
E200-AC
1.54
0.96
2.36
2.85
E500-AC
1.75
1.24
1.85
2.51For the e-beam energies employed in this study, the primary effect of irradiation in graphitic or sp2 carbon materials is a result of the knock-on collisions of atoms with electrons, which generates vacancies and structural defects (or interstitials) [25]. In addition, the materials are far from thermal equilibrium, that is to say, nonequilibrium, and, under certain circumstances, they can fulfill the conditions for self-organized structure formation. Accordingly, the change in hybridization facilitates the structural transformation sp2+δ, sp3  ↔ sp2, sp2+δ (trigonal ↔ mixed trigonal, tetrahedral) [26]. Therefore, the nanocrystallinity of the AC surface could be increased by e-beam irradiation.


## 3.2. Changes in the Textural Properties of E-Beam Irradiated Activated Carbons

Nitrogen adsorption analysis was performed at 77 K to examine the changes in the pore texture of the ACs after e-beam irradiation at different radiation doses. Table4 provides detailed information about the textural properties of the e-beam irradiated ACs. It was observed that the specific surface area and total pore volume were higher for the e-beam irradiated ACs than for R-AC, except for E500-AC. E200-AC exhibited the highest specific surface area and total pore volume (2339 m2/g and 1.02 cc/g, resp.). These changes in textural properties indicated that the nanocrystallinity of the AC surface was transformed and degraded by the e-beam irradiation. As Raman results in Section 3.2, IG2/IG1 ratio of ACs which indicated reduction of carbon in form of clusters was decreased as increase of e-beam irradiation dose. As mentioned above, the smaller IG2/IG1 ratio led to decreasing of the carbon in forms of clusters [24]. It was expected that specific surface area of e-beam irradiated ACs could be changed by degradation of AC surface. The specific surface area of ACs was increased by appropriate e-beam irradiation dose; however, excessive irradiation dose could reduce the specific surface area of ACs due to collapse of the AC surface.Table 4
Textual properties of e-beam irradiated ACs.
Sample
Specific surface area (m2/g)
Total pore volume (cm3/g)
Micropore volume (cm3/g)
Mesopore volume (cm3/g)
R-AC
1924
0.87
0.76
0.11
E100-AC
2300
0.92
0.88
0.04
E200-AC
2339
1.02
0.99
0.03
E300-AC
2310
0.97
0.96
0.01
E500-AC
1902
0.82
0.79
0.03Figure4 depicts the nitrogen adsorption isotherms of untreated and e-beam irradiated ACs. The isotherms of all samples were observed to be type I according to the IUPAC classification [27]. However, e-beam irradiated ACs seem to be more microporous than R-AC; the adsorption of R-AC gradually increased above a P/P0 ratio of 0.1. Figure 5 shows the DFT pore size distribution, and it can clearly be observed that all of the samples were microporous. In addition, E100-AC exhibited a larger pore volume than the other samples, with pore diameters of 1.5 to 2.0 nm. In general, the performances of the AC-based EDLCs were determined by the textural properties of the ACs [28]. Changes in the specific surface areas, pore volumes, and pore size distributions of the ACs after e-beam irradiation were expected to improve the performances of the prepared AC-based EDLCs.Figure 4
Nitrogen adsorption isotherms of e-beam irradiated ACs.Figure 5
DFT pore size distribution of e-beam irradiated ACs.


## 3.3. Electrochemical Properties of the E-Beam Irradiated Activated Carbons

Cyclic voltammetry (CV) was used to assess the electrochemical properties of the e-beam irradiated AC-based electrodes. Figure6 shows the CV plots of each sample acquired at scan rates of 5 mV/s and 50 mV/s. At a scan rate of 5 mV/s (Figure 6(a)), the CV profiles of the ACs were approximately rectangular, and small redox peaks were observed at 0.3–0.4 V, which indicated the occurrence of a pseudo-Faradaic reaction caused by oxygen functional groups [29]. R-AC had the highest redox peaks in this study because the C=O bonds in the ACs were reduced by the e-beam irradiation. In the CV profiles of the ACs obtained at 50 mV/s (Figure 6(b)), the CVs also exhibited a rectangular shape with small redox peaks.Figure 6
Cyclic voltammograms of e-beam irradiated ACs obtained at 5 mV/s (a) and 50 mV/s (b).
(a)
(b)The discharge capacitances (C) of the electrodes in the EDLCs were calculated using [30](3)C=1wΔV∫01idt,where C is the specific capacitance of the cell in F/g, w is the mass of the active material, i is the current flowing for time dt, and ΔV is the potential window in which the current flows.The calculated specific capacitances of the AC-based electrodes are listed in Table5. In this study, E200-AC exhibited the highest specific capacitances (306 and 262 F/g at scan rates of 5 and 50 mV/s, resp.). The specific capacitances of the e-beam irradiated ACs increased with the e-beam irradiation dose up to 200 kGy and then decreased. These results were expected because the specific surface areas and pore volumes of the ACs were increased by the e-beam irradiation.Table 5
Specific capacitances of e-beam irradiated ACs.
Sample
Specific capacitance (F/g)
5 mV/s
50 mV/s
R-AC
247
157
E100-AC
277
257
E200-AC
306
262
E300-AC
250
229
E500-AC
169
161Figure7 depicts the results of the AC impedance measurements of the prepared AC-based electrodes. The charge transfer resistance (RC) values for R-AC, E100-AC, E200-AC, E300-AC, and E500-AC were calculated to be 1.80, 0.61, 0.56, 0.75, and 3.84 Ω, respectively. The impedance results directly showed that the e-beam irradiation contributed significantly to the reduction of the charge transfer resistance of the ACs, which is in agreement with the change in electrical conductivity [31]. As mentioned above, the nanocrystallinity of the AC surfaces was increased by the e-beam irradiation. Therefore, it can be concluded that the increased nanocrystallinity of the AC surface induced by the e-beam irradiation also decreased the charge transfer resistance. However, the charge transfer resistance of the ACs increased because the nanocrystallinity of the AC surfaces was destroyed by excessive e-beam irradiation (E500-AC). The increasing charge transfer resistance of the e-beam irradiated ACs was expected because of the decrease in the specific capacitance. The charge transfer resistance was generally related to the electroactive surface area of the electrode materials. The electroactive surface area was a combination of the specific surface area and electrical conductivity [32]. R-AC and E500-AC had similar specific surface area, but the charge transfer resistance of E500-AC is higher than R-AC. It was expected that electrical conductivity of E500-AC decreased which causes a reduction in the specific capacitance.Figure 7
Nyquist impedance plots of e-beam irradiated ACs in 1 M H2SO4 in the frequency range from 10 mHz to 100 kHz.


## 4. Conclusions

To investigate the use of e-beam irradiation for the modification of AC surfaces, ACs were treated with e-beam irradiation. Based on the XPS results, the e-beam irradiation did not affect the chemical compositions of the AC surfaces; however, the C-C sp2 bonds on the AC surfaces increased as a result of the e-beam irradiation. According to the Raman results, the e-beam irradiated ACs contained lower amounts of amorphous material than the untreated AC. The specific surface areas and total pore volumes of the ACs increased after the e-beam irradiation. These changes in the chemical and textural properties indicated that the nanocrystallinity of the AC surfaces was transformed and degraded by the e-beam irradiation. Accordingly, the electrochemical properties of the ACs were enhanced by the e-beam irradiation. The specific capacitance of the AC subjected to e-beam irradiation at a dose of 200 kGy increased by 24% relative to the untreated AC. Furthermore, the charge transfer resistance of this sample decreased from 1.80 (untreated AC) to 0.56 upon irradiation. Therefore, e-beam irradiation could be used to modify AC surfaces for electrochemical applications.



---

*Source: 240264-2015-06-04.xml*