Effect of Composition Ratios on the Performance of Graphene/Carbon Nanotube/Manganese Oxide Composites toward Supercapacitor Applications.

Herein, we describe the preparation and characterization of graphene/carbon nanotube (CNT)/MnO v composites and the effects of chemical composition and phase transformation on the properties of the corresponding electrode film. In general, the effect of graphene-to-CNT ratio (G/C ratio) and the manganese (Mn) content on the morphology, chemical state, crystallization properties, and microstructure of the composite material was examined by scanning electron microscopy, X-ray photoelectron spectroscopy, X-ray diffraction, and selected area electron diffraction. The bonding mechanism between MnO v and graphite-based materials, that is, graphene and CNTs, is discussed. The influence of the composition of the composites on the performance of the electrode was investigated using charge-discharge curves. The faradically active MnO v also functioned as a considerable cobinder and allowed for a reduced amount of polymeric binder, which enhanced the conductivity and capacitance of the electrode. The optimized electrode composition was obtained based on our present graphene and CNT specifications. In summary, the results discussed in this article provide significant background information for future applications of graphene/CNT/MnO v composite electrodes.

Introduction

With the rapidly increasing demand for energy technologies in recent years, electroactive materials for various kinds of energy conversion and storage devices such as fuel cells, batteries, solar/thermoelectric/piezoelectric generators, and supercapacitors are being widely studied.[1−8] Among them, supercapacitors have attracted unique research attention because of their intrinsic features such as, high power density and excellent durability.[7,9,10]

Considering the charge–discharge mechanism, supercapacitors can be classified into three major categories: electrochemical double-layer capacitors (EDLCs), pseudocapacitors, and hybrid capacitors.[9,11−13] In general, carbon-based materials such as activated carbon, carbon nanotubes (CNTs), graphene, mesoporous carbon, and carbon-fiber-based materials are frequently employed as the electrode material in EDLCs.[6,9,11,14−19] Each of these has its specific advantages and disadvantages. Among them, multiwall CNTs and single-layered graphene have attracted most research attention because of the corresponding long-term conductivity and high specific surface area (SSA), respectively.[18,19] However, in practice, the contact resistance is huge between CNT–CNT, CNT–graphene, and graphene–graphene owing to the large interface between the polymer binder and the nanoparticles. Moreover, CNT and graphene-based electrodes also suffer from winding into a group and piling up in stacks, respectively.[10,11,20,21] Integrating them together mitigates those problem to a certain extent.[7,10,11,20,22,23]

Furthermore, when transition-metal oxides or electrically active polymers are involved in the electrodes, faradic redox reactions take place at the interface between them and the surrounding electrolytes during the charge–discharge process; these types of electrodes are known as pseudocapacitors.[9−11,22,24,25] Thus, EDLCs and pseudocapacitors are widely known for their higher power density and higher energy density compared to each other, respectively. Modification with these faradically active materials also helps to avoid the stacking of graphene.[26−28] Among various pseudocapacitive materials, manganese oxides (hereafter denoted as MnO), including MnO, MnO2, Mn2O3, Mn3O4, and Mn2O7 are promising candidates for active electrode materials for supercapacitors[9−11,22,23,25,26,29−36] due to their notable electrochemical capacity, wide potential range, low cost, and environmental friendliness.

For hybrid electrodes, graphene and CNT composites have been widely studied as EDLC materials. Recently many efforts have been made to blend manganese oxide with graphene and/or CNTs to obtain composites such as CNT/MnO, graphene/MnO, and graphene/CNT/MnO, and the results show that they exhibit higher specific capacitance and better cycle life compared to pure MnO.[10,30−32,34] Generally, graphene and CNTs are expected to be ideal supporting materials, as this combination provides remarkable surface area, good mechanical stiffness, excellent conductivity, and the ability to form a three-dimensional conducting matrix. However, there are very few studies in the literature on how these carbon materials bond to metal oxides. In general, it was well-accepted that −COOH groups on the carbon fiber and graphene oxide can aid in the extraction of heavy metals from water, because the −COOH group on the carbon support captures metal cations such as Fe2+, Cu2+, Fe3+, Cd2+, and Pb2+ and form −COOM, (M = metal).[17] According to this anion adsorption mechanism, MnO is considered to be coordinated with CNTs through the COO–Mn linkage.[9,10,22,37] However, from the viewpoint of metallurgy, manganese also has a chemical affinity to carbon, and thus it is known to form phases of manganese carbides such as, MnC, Mn3C, Mn5C2, Mn7C3, and Mn23C6.[38] This suggests that other than COO–Mn linkage, there are other possibilities for linkages between the metal oxide and graphite-based materials (Gbased).

Therefore, to optimize the properties of EDLCs, tremendous attempts have been made to match, mix, and integrate multiple carbon materials together through a variety of methods. Moreover, various oxides or hydroxides of metals or bimetals, such as Ru, Co, Ni, Fe, Ce, Ni, Mn, V, Bi, Mo, and Ti, have been investigated to make various possible permutations and combinations.[13] Recently Saeed et al., reported a novel 3-dimensional graphene/CNTs/MoO3 hybrid film as an advance electrode material for asymmetric supercapacitors.[39] In addition, the manufacturing technology of supercapacitors has matured. Furthermore, the capacitance and performance also depend on the packaging technology and equipment; therefore, it is more valuable to work systematically toward a specific purpose rather than to compete for the highest capacitance. For instance, methods have been specifically devised to increase the conductivity, energy density, cost performance, decrease the binder content, and to better understand the mechanism of electron or ion transfer.

In this study, MnO was used as the faradic active material as well as a binder, allowing for the exclusion of the insulating polymer binder. The effects of graphene-to-CNT ratio (G/C ratio) on the morphology, Mn content on crystallization, and polyvinylidene fluoride (PVDF) content on resistance were analyzed to study the effect of all these on the capacitive behavior. Moreover, this article confirms the bonding between amorphous MnO2 and Gbased materials and explains its potential for significantly reducing polymer binder content. The optimized condition was determined based on the adopted graphene and CNT specifications. Finally, the results presented here provide valuable building blocks for the future development of composite electrodes for supercapacitors.

Results and Discussion

Integration and Characterization of Materials

MnO as a Binder and the Effect of Graphene-to-CNTs Ratio (G/C Ratio) on the Morphology of the Composite

The dispersion and morphology of graphene and CNT mixtures were analyzed via scanning electron microscopy (SEM) observations. Figure a shows the SEM images of a graphene and CNT mixture (Spec.#: G8C2). It is clear that CNTs tend to entangle each other, and that there are four groups of tangled CNTs, as marked with dotted circles in Figure a. The corresponding magnified images are shown in Figure a(i–iv). In contrast, when integrated with Mn (Spec. #: G8C2-M25), the graphene/CNT/MnO composites dispersed well without piling up or entangling each other (Figures b and S1c–f). These results strongly suggest that MnOv is not only a faradically active material, but it could also significantly act as a cobinder, providing better adhesion between graphene and CNTs.

Figure 1

SEM images of composites: (a) mixture of graphene and CNTs (Spec. #: G8C2) and (b,c) a mixture of graphene, CNTs, and MnO (Spec. #: G8C2-M25).

Furthermore, considering the effect of the G/C ratio on the morphology of the composite, SEM images of graphene/CNT/MnO composites with a constant Mn content (25 wt %) were obtained. Figure S1c–f shows that, upon using 25 wt % MnO as the binder, graphene (Figure S1a) and CNTs (Figure S1b) mixed well and were dispersed easily at the G/C ratios of 9/1, 8/2, 7/3, and 5/5. Even at a G/C ratio of 2/8 (Figure S1g), it is obvious that each graphene sheet is isolated in the CNT framework. This result illustrates that graphene and CNTs are dispersed well at all G/C ratios when using MnO as a binder, which is potentially useful for a wide range of electrode applications. In brief, the optimized graphene/CNT mixing condition with minimum stacking of graphene can be obtained with the method reported herein.

Effect of Mn Content on the Morphology of the Composite

As the capacitance of the material may be influenced by the variation in morphology caused by varying the Mn content, specimens with 10, 15, 20, 25, 30, 35, and 40 wt % of Mn (i.e., Spec. #: G8C2-M10, G8C2-M15, G8C2-M20, G8C2-M25, G8C2-M30, G8C2-M35, and G8C2-M40, respectively) were analyzed by SEM and transmission electron microscopy (TEM) (Figure S2a–g). The obtained SEM and TEM images agree with the conclusions drawn in the previous section, that is, graphene and CNT can be well dispersed by adding MnO. The Mn content of these composites was examined by SEM–energy-dispersive X-ray spectrometry (EDS) analysis, indicating 10.3, 15.9, 21.1, 24.4, 29.9, 35.6, and 40.6 wt % of Mn in G8C2-M10, G8C2-M15, G8C2-M20, G8C2-M25, G8C2-M30, G8C2-M35, and G8C2-M40, respectively. The SEM and TEM images of G8C2 and G8C2-M10 in Figures a and S2(a-1), respectively, indicate that in a composite with 10 wt % Mn, MnO was well dispersed and can be observed only by TEM (Figure S2(a-1)) and not by SEM (Figure S2a). The MnO particles with the average dimension of 10 × 40 nm are randomly dispersed on graphene and CNTs. Upon increasing their content to 15 wt %, the MnO particles start to agglomerate to form particles with a size of up to ca. 250 nm (as observed in Figure S2b). As the Mn content increased to 20, 25, 30, 35, and 40 wt %, the size of the MnO particle grew up to ca. 350, 600, 900, 1500, and 2000 nm, respectively. Because higher specific capacitance should be obtained with better dispersion,[8,40] optimized specific capacitance (F/g) was expected to be obtained with 10 wt % of MnO. However, phase transformation was also observed with particle agglomeration, which results in a positive effect on specific capacitance, which will be discussed in Section .

Microstructure of the Composite

The microstructure of the specimens was investigated by TEM analyses to probe the contact between graphene/CNTs and MnO. The TEM images of functionalized CNTs (Spec.#: G0C10) and CNT/MnO (Spec.#: G0C10-M25) in Figure a,b, respectively, suggest that the functionalized CNTs can be fully covered with a MnO layer with a thickness of approximately 15–20 nm. Figure c,d shows the corresponding high-resolution TEM and selected area electron diffraction (SAED) images of specimen CNT/MnO, indicating that the whole MnO phase is in an amorphous state. In contrast, the TEM images of graphene and graphene/MnO (Spec.#: G10C0 and G10C0-M25) in Figure a,b, respectively, indicate that MnO is randomly attached to the graphene sheets. Figure c shows the corresponding high-resolution TEM image, in which most of the MnO phase is in an amorphous state with a few nanocrystals embedded in the amorphous phase. The diffraction spots reside along the rings in the SAED image (Figure d), thus proving the existence of both amorphous and nanocrystalline MnO on the graphene surface. These observations prove that our proposed MnO blending process helps MnO to bond well with the Gbased materials, as well as provide hints that MnO could also act as a binder for Gbased electrode materials, as reported.[41] Considering graphene/CNT/MnO ternary composites, for instance, Figure S2(a-1) evidently supports our speculation; it shows that MnO randomly binds graphene and CNTs together.

Figure 2

TEM images of (a) functionalized CNTs and (b) composite of CNTs and MnO (Spec. #: G0C10-M25); (c,d) show the high-resolution TEM and SAED images of (b), respectively.

Figure 3

TEM images of (a) graphene (Spec. #: G10C0) and (b) graphene with MnO (Spec. #: G10C0-M25); (c,d) are high-resolution TEM and SAED images of (b), respectively.

X-ray photoelectron spectroscopy (XPS) analyses were conducted to understand the mechanism of how amorphous MnO binds with both the CNTs and graphene. Figure shows the XPS C 1s spectrum of CNTs, graphene, and their composites with 25 wt % MnO (i.e., Spec.# G0C10, G0C10-M25, G10C0, G10C0-M25, and G8C2-M25). As reported earlier by Rosillo-Lopez and Salzmann, the binding energy of COOH (at ca. 289 eV) shifts to 288 eV, suggesting the formation of COO–M.[17] Considering the variation from CNT to CNT/MnO observed in the deconvoluted spectra (Figure ), the −COOH peak at ca. 288.85 (Spec.# G0C10) shifted to ca. 288.35 which corresponds to −COOMn (Spec.# G0C10-M25). This is in agreement with the previous reports that state that −COOMn bonding assists MnO bonding to CNT.[9,10,22,37] However, this explanation only partially supports our assumption regarding how Mn bonds with the Gbased materials. Consider that in single-layered graphene, only a trace amount of −COOH groups and −COOMn bonding can be identified in the XPS C 1s spectra of G10C0 and G8C2-M25, respectively (shown in deconvoluted spectra in Figure ). Furthermore, the amorphous MnO is randomly dispersed on the graphene surface (as seen in Figures and S2(a-1)). In other words, there may be another type of bonding that exists between the MnO and Gbased materials. After integrating with MnO, the XPS C 1s spectra shown in Figure shows an obvious peak shift, from C–OH bonding at 285.70 eV (CNT and graphene) to 285.35 eV, which is attributed to the formation of the C–OMn bond. These results suggest the possibility of C–OMn sharing a larger portion of the bonding between MnO and Gbased materials than C–OOMn.

Figure 4

XPS C 1s spectrum of CNTs, graphene, and their respective composites with MnO. (Spec. #: G0C10, G0C10-M25, G10C0, G10C0-M25, G8C2-M25).

Figure 5

Deconvoluted XPS spectra of C 1s region for CNTs, graphene, and their composite with 25 wt % MnO (Spec.# G0C10, G0C10-M25, G10C0, and G10C0-M25).

Figure shows the deconvoluted XPS O 1s spectra of functionalized CNTs, MnO, and CNT/MnOv composite (i.e., Spec.# G0C10, MnO, and G0C10-MnO). As can be seen, on one hand, the presence of oxygen on CNT can be attributed to the presence of −COOH, where the peaks at 531.2, 533.1, and 532.3 eV correspond to C=O, −COOH, and C–OH, respectively.[42] On the other hand, the peaks at 529.4, 530.8, and 532.05 eV represent Mn–O, M–OH, and H–O–H in MnO, respectively.[43] The peak corresponding to the binding energy at 529.4 eV represents Mn–O, whereas the peak at 531.3 eV denotes C–O–Mn, Mn–OH, and C=O (Figure ). These are the possible major bonding modes in the CNT/MnO composite. Furthermore, it is impossible to deconvolute the peak at 531.3 eV into separate C–O–Mn, Mn–OH, and C=O peaks, which makes it clear that the −COOH and C–OH peaks have almost disappeared in the O 1s region of the XPS spectrum of CNT/MnO (as indicated by the dotted line in Figure ). Instead, the C–O–Mn bond plays a major role in the binding of CNT and MnO, where C–O–Mn may represent the formation of bonding through both CNT–OMn and CNT–COOMn. This result agrees with the results drawn from the XPS analysis of the C 1s region. Figure S3 shows the XPS O 1s spectra of MnO, CNTs, MnO/CNTs, graphene, graphene/MnO, and graphene/CNT/MnO (i.e., Spec.# MnO, G0C10, G0C10-M25, G10C0, G10C0-M25, and G8C2-M25, respectively); the results show that the integration of graphene and MnO has the same trend (the variation of O 1s region of the XPS spectrum) as CNT to CNT/MnO. According to the above discussion, a scheme is proposed to illustrate how MnO binds to Gbased materials (shown in Figure S4). First, −COOH groups are formed accompanied with a greater number of −OH groups (Figure S4a). Consider that the red bond [in Figure S4 (a-left)] illustrates the bond that be reacted during the acid treatment, and Figure S4 (a-right) illustrates that after the acid treatment (the removal of red bonds), the carbon atom may connect the Gbased materials through one C–C bond (blue bond) or three C–C bonds (green bonds); in other words, it could be the C (red atoms) in −COOH group or could be the C (orange atoms) connecting to −OH group. This model suggests that the acid strength, reaction temperature, reaction time, and graphitization degree may affect the −OH/–COOH ratio. Figure S4b also demonstrates how the MnO can bind well with functionalized Gbased materials through the O–Mn and COO–Mn bonds.

Figure 6

XPS O 1s spectra of CNTs, MnO, and their composite (Spec. #: G0C10, MnO, G0C10-M25).

As discussed earlier, Mn also has a chemical affinity to carbon and MnC, Mn3C, Mn5C2, Mn7C3, and Mn23C6 are the possible manganese carbides.[38] However, there is a lack of literature reports discussing this mechanism. In the XPS analyses, it was known that the M–C (M = metal) binding energy in the metal carbide should be slightly lower than that of a sp3-hybridized carbon (C–C-sp3) in the C 1s region and lower than that of M0 in the Mn 2p region.[44,45] However, there is no noticeable manganese carbide peaks to be identified in the C 1s or Mn 2p regions (in Figures and S5), implying that there is not a considerable amount of manganese carbide in our composite. In brief, both CNT–OMn and CNT–COOMn are the only bonding possibilities, and CNT–COMn and CNT–Mn bonds are not possible between Gbased materials and MnO in the synthesized composite materials.

With regard to the chemical state of Mn in the composite, the XPS Mn 2p spectrum of pure MnO has examined and deconvoluted, as shown in Figure . The results suggest that approximately 25.3, 52.1, and 22.6% of Mn can be identified as Mn2+, Mn3+, and Mn4+, respectively. Other than pure MnO, the XPS Mn 2p spectra of CNT/MnO, graphene/MnO, and graphene/CNT/MnO (i.e., Spec.# MnO, G0C10-M25, G10C0-M25, and G8C2-M25) show no differences and thus have the same chemical states, as shown in Figure S5. Here, Mn4+ represents the existence of MnO2, and the Mn3+/Mn2+ ratio is consistent with the ratio of 2/1 in Mn3O4.[27] Thus, the XPS spectra revealed that there is approximately 77.4% Mn3O4 and 22.6% MnO2 in MnO in our materials, where subscript v equals to 1.4.

Figure 7

XPS Mn 2p3/2 spectrum of pristine MnO.

Factors Affecting the Capacitance

Effect of Graphene-to-CNT (G/C) Ratio

To determine the effect of the G/C ratio on the capacitance, electrodes made with different G/C ratios, that is, Spec. #: G10C0-M25-P10, G9C1-M25-P10, G8C2-M25-P10, G7C3-M25-P10, G5C5-M25-P10, G2C8-M25-P10, and G0C10-M25-P10, were examined with chronopotentiometric (CP) measurements under a current density of 1 A/g, as shown in Figure a. The trends are clearly illustrated in Figure b, and the parameters are collected in Table . These results indicate that when the G/C ratios are 10/0 and 0/10, the capacitances obtained are 102 and 83 F/g, respectively; this is due to the SSA of the adopted single-layered graphene (436.7 m2/g) being significantly greater than that of the multiwalled CNTs (31.9 m2/g). However, the graphene layers tend to pile up in stacks, which blocks most of the active surface, and hence it is impossible for G10C0 to perform to its potential capacity.[10,11,20,21] It also is clear that, with the addition of MnO, the specific capacity of G10C0-M25-P10 increased obviously. This improvement could be attributed to both the faradic capacitances of MnO and the decreased stacking of graphene layers.

Figure 8

(a) Galvanostatic charge–discharge curves of GC-M25P10; w and x represent the amount of graphene and CNTs and w/x ranges from 0/1 to 1/0; (b) variation of the capacitance as a function of the CNT content.

Table 1

Specimen Designation and Properties

	integration of materials				coating of electrode films
specimen designation	G/C ratio	Mn (wt %)	MnOv particle size (nm)	specimen designation	PVDF (wt %)	Super-P (wt %)	capacitance (F/g)	sheet resistance, Rs
p-CNT	0/10	0	N/A	p-CNT-P10	10	10	5	N/A
p-Ga	10/0	0	N/A	p-G-P10	10	10	102	N/A
f-Ca	0/10	0	N/A	f-C-P10	10	10	83	N/A
MnOv	N/A	71b		MnOv-P10	10	10	128	N/A
G10C0-M25	10/0	25		G10C0-M25-P10	10	10	102
G9C1-M25	9/1	25		G9C1-M25-P10	10	10	122
G8C2-M25	8/2	25		G8C2-M25-P10	10	10	146
G7C3-M25	7/3	25		G7C3-M25-P10	10	10	131
G5C5M25	5/5	25		G5C5M25P10	10	10	113
G2C8-M25	2/8	25		G2C8-M25-P10	10	10	95
G0C10-M25	0/10	25		G0C10-M25-P10	10	10	83
G8C2-M0	8/2	0	N/A	G8C2-M0-P10	10	10	30
G8C2-M10	8/2	10	10 × 40 nm2	G8C2-M10-P10	10	10	68
G8C2-M15	8/2	15	250 nm	G8C2-M15-P10	10	10	85
G8C2-M20	8/2	20	350 nm	G8C2-M20-P10	10	10	103
G8C2-M25	8/2	25	600 nm	G8C2-M25-P10	10	10	146
G8C2-M30a	8/2	30	900 nm	G8C2-M30-P10b	10	10	181	0.06355
G8C2-M35	8/2	35	1500 nm	G8C2-M35-P10	10	10	156
G8C2-M40	8/2	40	2000 nm	G8C2-M40-P10	10	10	128
G8C2-M30	8/2	30		G8C2-M30-P3	3	10	101	0.04897
G8C2-M30	8/2	30		G8C2-M30-P5	5	10	210	0.05447
G8C2-M30	8/2	30		G8C2-M30-P7	7	10	194	0.06044
G8C2-M30	8/2	30		G8C2-M30-P10	10	10	181	0.06355
G8C2-M30	8/2	30		G8C2-M30-P15	15	10	161	0.07113

Specific surface areas of graphene, CNT, and G8C2-M30 composite are 463.7, 31.9, and 158.3 m2/g, respectively.

71 wt % Mn in MnO was calculated considering the subscript v equals to 1.4, according to the XPS results discussed in Section .

As shown in Figure , the capacitance of GC-M25P10 is enhanced with an increase in the CNT content, and reaches the maximum value of 146 F/g, at a G/C ratio of 8/2. Further increase in the CNT content leads to a linear decrease in the capacitance, which suggested that minimized graphene stacking can be reached at a G/C ratio equal to or smaller than 8/2. However, the capacitance decline with a further increase in the CNT content, for Spec. #: G7C3-M25-P10 and Spec. #: G5C5-M25-P10, can be attributed to the lower specific capacitance (SSA) of CNTs. In brief, because graphene tends to pile up in stacks during the electrode drying process, adding lower content of CNTs helps to avoid this detrimental stacking. The optimized G/C ratio that delivers a higher capacity value was found to be 8/2.

Effect of Mn-to-Carbon Ratio

To examine the effects of the Mn content on the capacitance of the materials, CP measurements were conducted with specimens G8C2-M-P10 (where y = 0, 10, 15, 20, 25, 30, 35, and 40), based on the G/C ratio of 8/2 discussed in the previous section. As shown in Figure , the results indicate that all CP curves are pseudo-triangular. Without MnO, G8C2-M0-P10 has a capacitance of only 30 F/g. With the addition of MnO, even the MnO phase started to agglomerate into particles ranging from several tens of nm to 900 nm in size, the capacitance increased from 68 to 181 F/g as the Mn content increased from 10 to 30 wt %. It is worth noting that the specimen with only 25 wt % Mn (i.e., G8C2-M25-P10; capacitance: 146 F/g) displayed higher capacitance than pure MnO (i.e., MnO-P10; capacitance: 128 F/g), as depicted in Table . Upon increasing the Mn content further from 30 to 40 wt %, the size of the agglomerated MnO grew quickly to 2000 nm and caused declining capacitance.

Figure 9

(a) Galvanostatic charge–discharge curves of G8C2-M-P10 and (b) variation of the capacitance as a function of Mn content in G8C2-M-P10 composite, where y represents the Mn content in the electrode film, which ranges from 0 to 40 wt %.

Phase transformation of MnO, as the particle agglomeration takes place, could have some effect on the specific capacitance. As summarized in the previous section, MnO on one hand consists of ∼77.4% Mn3O4 and 22.6% MnO2. On the other hand, according to the observed X-ray diffraction (XRD) patterns of graphene/CNT/MnO composites (shown in Figure ; Spec. #: G8C2-M-P10, where y ranges from 10 to 35), while adding 10–25 wt % of Mn, it is hard to identify any crystalline peaks of Mn3O4 and MnO2. Subsequently, increasing the Mn content to 30 wt %, the obvious characteristic peaks correspond to Mn3O4 appeared, which matched the standard data card of Mn3O4 (JCPDS 08-0017). The existence of Mn3O4 is consistent with our prediction from the XPS analyses. Besides the crystalline phase has higher conductivity, and it has been reported that normal spinel-structured Mn3O4 with Mn2+ in tetrahedral units and Mn3+ in octahedral units exhibits higher capacity than MnO2.[33,35] However, no such characteristic peaks corresponding to MnO2 was seen in any of the XRD patterns, which suggests that 22.6 wt % of MnO2 tends to be in the amorphous state, whereas aggregation takes place during our experimental conditions. Therefore, the amorphous MnO2 phase is considered to bind to graphene and CNTs (Figure S4). In brief, the phase transformation from amorphous to spinel Mn3O4 confers G8C2-M-P10 for higher capacitance, whereas the MnO2 phase remains in the amorphous phase and binds with the Gbased materials.

Figure 10

XRD patterns of G8C2-M composite materials, where “y” ranges from 10 to 35.

Other than phase transformation, the particles agglomerated to an average diameter of 900 nm (in Figure S2e) were also examined by EDS mapping (shown in Figure S6). The EDS map shows that the particle consists of 43, 37, and 20 at. % of carbon, oxygen, and manganese, respectively, suggesting that the agglomerated particles are actually a mixture of carbon (43 wt %) and MnO. In other words, the nanostructure of the carbon/MnO mixture may also contribute to a certain extent to the capacitance and reduce the effect of agglomeration on the total specific capacitance.

In summary, as the Mn content increases to 30 wt %, the capacitance found increased to 181 F/g and is accompanied both by the crystallization of Mn3O4 and the agglomeration of the carbon/MnO mixture. On extending this limit, serious agglomeration of particles is the primary cause of declining capacitance.

Effect of the PVDF Content on the Capacitance

In addition to the effect of each active component, such as manganese, graphene, and CNTs, the effect of binder (PVDF) content on our proposed materials was also examined by the CP and electrochemical impedance spectra (EIS) analyses. The charge–discharge curves and capacitance variation trends are shown in Figure a. Figure b shows the capacitance variation trends with increasing PVDF content. Upon decreasing the PVDF content from 15 to 5 wt %, the capacitance increases linearly from 161 to 210 F/g, which is reasonable because less isolated PVDF would block less of the active area, and the material would have better conductivity. As shown in Figure a, IR drop can be clearly observed upon adding 15, 10, and 7 wt % PVDF (Spec. #: G8C2-M30-P15, G8C2-M30-P10, and G8C2-M30-P7). Upon decreasing the PVDF content to 5 wt %, the IR drop is greatly mitigated (Spec. #: G8C2-M30-P5). These results suggest that the conductivity can be significantly improved by reducing the PVDF content to 5 wt %.

Figure 11

(a) Galvanostatic charge–discharge curves of G8C2-M30-P and (b) variation of the capacitance with the PVDF content in G8C2-M30-P composite, where z represents the PVDF content in the electrode film, which ranges from 3 to 15 wt %.

Figure shows the EIS spectrum of the electrodes with different binder (PVDF) contents ranging from 15 to 3 wt %, that is, for Spec. #: G8C2-M30-P15, G8C2-M30-P10, G8C2-M30-P5, and G8C2-M30-P3. The corresponding sheet resistance (Rs) was found to be linear with respect to the PVDF content as shown in Table . Even the electrode specimen G8C2-M30-P3 with 3 wt % PVDF shows the lowest resistance, the capacitance of which is lower than that of the G8C2-M30-P5 electrode with 5 wt % PVDF. This is because the G8C2-M30-P3 electrode is not as stable as the G8C2-M30-P5, and it exhibited some peeling during the charge–discharge process. It is worth mentioning that our proposed graphene/CNT/MnO composite can reduce the PVDF binder content to 5 wt %, whereas for most active materials, optimized PVDF contents are reported between the range of 10–25 wt %.[9−11,20,21,24,25,35] The reduction in the PVDF content for our graphene/CNT/MnO composites can be attributed to two reasons: (1) CNTs provide longer range connections and (2) MnO tends to adhere to the surface of CNT and graphene, which helps them bind together. These reasons also lead to the reduction of interface resistance between the graphene and CNTs. In brief, the addition of MnO to graphene/CNTs reduced the PVDF content and the electrode resistance, and thus capacitance was increased. With regard to the cycle stability, a cycling charge–discharge test was done to examine the durability of our proposed composite. As shown in Figure S9, our graphene/CNTs/MnO performs at 91.0% of its original capacity after 1000 cycles long-term operation, which is compatible with recent MnO2-based reports.[46,47] Finally, a Ragone plot of our proposed graphene/CNTs/MnO composite material was derived from the CP curves (in Figure S10); it illustrated the relationship between the power and energy densities. Revealing that a maximum power density of 8619 W/Kg (at the energy density of 3.1 W h/Kg) and maximum energy density of 51.5 W h/Kg (at the power density of 50.3 W/Kg) can be achieved. These results demonstrated the potential of the graphene/CNTs/MnO ternary composite electrode for further applications in supercapacitors.

Figure 12

EIS spectra of G8C2-M30-P. The subscript z represents the PVDF content in the electrode film, which ranges from 3 to 15 wt %.

Conclusions

We have successfully demonstrated that MnO particles can bind and disperse well with CNTs and graphene to form graphene/CNT/MnO ternary composite electrodes. With the addition of MnO (as a binder), the graphene and CNTs were dispersed well, which helped avoid the piling up and the entanglement of graphene and CNTs. The optimized G/C ratio is found to be 8/2. The proposed graphene/CNTs/MnO composite materials can be obtained with the addition of 30 wt % of Mn. According to the results obtained from XPS analyses, a scheme was proposed to explain how MnO binds with functionalized Gbased materials. The −COOH functionalization is accompanied by a greater amount of −OH groups, which would be converted to COO–Mn and O–Mn bonds that connect the Gbased materials and MnO. Moreover, the manganese oxide (MnO) used in this study is found to be composed of 77.4% crystallized Mn3O4 and 22.6% amorphous MnO2. MnO has proved to serve as both a faradic material and a cobinder, which improved the capacitance and reduced the content of the PVDF binder. Finally, the optimized electrode material (i.e. G8C2-M30-P5) showed a high capacitance of 210 F/g with only 5 wt % PVDF, performed a high cycle stability of 91.0% after 1000 cycles, and achieved a maximum power density of 8619 W/Kg and energy density of 51.5 W h/Kg.

Experimental Section

Pretreatment of CNTs

CNTs purchased from Hodogaya Chemical (NT-7, diameter of 65 nm, SSA = 139 m2/g) were pretreated with an acid solution containing 4.5 M nitric acid and 1.5 M sulfuric acid. Typically, 0.5 g of CNTs were dispersed and stirred in 100 mL of acid solution at 45 °C for 3 h. The functionalized CNTs were then filtered and collected using a Büchner funnel and washed with deionized (DI) water and dried. The functionalized CNT powder was then used for preparing the composite electrode.

Synthesis of Graphene/CNT/MnO Composites

Graphene/CNT, graphene/MnO, CNT/MnO, and graphene/CNT/MnO composite materials were prepared by dispersing the desired amounts of graphene, CNT, and MnO in acetone. Graphene powder [N002-PDR, Angstron Materials Inc. (AMI)] with less than 3-graphene layers, x–y dimensions of up to 10 × 10 μm2, and average SSA of 400–800 m2/g was used in this study. The solution was placed in a sealed glass bottle and sonicated for 30 min to obtain a uniform dispersion. Subsequently, 10 mL of ethylene glycol was added as a reducing agent, and the resulting mixture was sonicated for another 30 min. The mixture was then loaded into a Teflon-lined autoclave and heated at 150 °C for 2 h. The resulting composite material was washed with DI water and dried overnight at 60 °C.

Preparation of Electrodes

Carbon black Super-P, PVDF, and N-methyl-2-pyrrolidone (NMP) at a desired ratio were added together and stirred for 3 h at 100 °C. Super-P served as the conducting agent and PVDF as the binder. Each of the dried composite powder specimens listed in Table was then added to the Super-P/PVDF/NMP solution. Uniform slurries were then obtained after stirring for 1 h. The slurries were subsequently scraped onto 316L stainless steel sheets (20 mm × 40 mm × 0.1 mm) through a fixed template (10 mm × 20 mm × 0.1 mm). The obtained electrodes were then dried at 100 °C in a circulating oven.

Specimen Designation

A series of composites were designed for the active materials and investigated to understand the effects of graphene-to-CNT ratio (G/C ratio) and the Mn and PVDF contents on the properties of the composite electrode. As shown in Table , the materials such as pure CNT, functionalized CNT, pure graphene, and manganese oxides are denoted as p-CNT, f-C, p-G, and MnO, respectively. Graphene and CNT mixtures are referred to as GC; the corresponding specimens integrated with MnO are referred to as GC-M; the corresponding electrodes bound with the PVDF binder are denoted as GC-M-P. The suffixes “w” and “x” represent the G and C content in weight ratio; the suffix “v” represents the Mn content in the graphene/CNT/MnO composite material, and the suffix “z” stands for the PVDF content (wt %) of the electrodes.

Characterization

All composite electrode specimens listed in Table were analyzed ex situ and in situ. For ex situ experiments, SEM (JSM-7100F) was used to observe the surface morphology, TEM (JEOL JEM-2100, 200 keV) was used to examine the microstructure, and XRD analysis (PANalytical X’Pert PRO, Cu Kα radiation, λ = 0.1541 nm) was used to verify the crystal structure and phase. Nitrogen adsorption/desorption analysis was carried out under 77 K (Micromeritics, ASAP2020) and used to determine the SSA. EDS was employed to determine the electrode compositions and the XPS (ULVAC-PHI PHI 5000 VersaProbe) was used to determine the composition and chemical state of specimens shown in Table .

For in situ analyses, a CP technique was employed to determine the capacitance (C) of each specimen. Typically, the CPs were recorded with the response voltage (V) and time (s) under the desired charge–discharge current (mA) in the range of −0.2 to 0.8 V. As each electrode had a different weight, the current was normalized by mass (unit of A/g) for ease of comparing the results between different electrodes. In this study, half-cell test analyses were done to conclude the optimized electrode composition. The CP measurements were carried out in a three-electrode cell using 1 M Na2SO4 solution as the electrolyte, with Pt and Ag/AgCl as the counter and reference electrodes, respectively. Instead of using glassy carbon or graphite rods, a stainless-steel sheet, which provides a high electrode area (200 mm2) and thus excellent accuracy, was utilized as the support for the working electrode. The EIS were then measured with signals operating at a frequency range between 30 mHz and 1000 kHz.

The gravimetric capacitances were calculated according to eq , where I is the charge–discharge current, Δt stands for the time differential, m represents the mass of the active electrode material, and ΔV is the voltage range of scanning segments. The cell device capacitance Cs, energy density (De), and power density (Dp) were also calculated from the cyclic chronopotentiometric curves, according to eqs and 3.[7,22]