Ionic Liquids as Alternative Curing Agents for Conductive Epoxy/CNT Nanocomposites with Improved Adhesive Properties

Good dispersion of carbon nanotubes (CNTs) together with effective curing were obtained in epoxy/CNT nanocomposites (NCs) using three different ionic liquids (ILs). Compared to conventional amine-cured epoxy systems, lower electrical percolation thresholds were obtained in some of the IL-based epoxy systems. For example, the percolation threshold of the trihexyltetradecylphosphonium dicyanamide (IL-P-DCA)-based system was 0.001 wt.%. The addition of CNTs was not found to have any significant effect on the thermal or low-strain mechanical properties of the nanocomposites, but it did improve their adhesive properties considerably compared to the unfilled systems. This study demonstrates that ILs can be used to successfully replace traditional amine-based curing agents for the production of electrically conductive epoxy/CNT NCs and adhesives, as a similar or better balance of properties was achieved. This represents a step towards greater sustainability given that the vapor pressure of ILs is low, and the amount needed to effectively cure epoxy resins is significantly lower than any of their counterparts.


Introduction
Epoxy resins are widely used due to their excellent mechanical and adhesive properties. One way to further improve these properties and acquire others-such as electrical conductivity-is by adding carbon-based nanofillers such as carbon nanotubes (CNTs). CNTs are an allotropic form of carbon made up of one (SWCNT) or multiple (MWCNT) one-atom-thick graphene sheets that are rolled into hollow cylinders with a nanometric diameter. They present outstanding mechanical and electrical properties. However, the nanofiller must be properly dispersed for the nanocomposites (NCs) to obtain a good balance of properties.
In fact, the strong propensity of CNTs to form bundles and aggregates (due to π-π stacking and Van der Waals forces of attraction) is one of their main drawbacks, as it limits their potential for improving mechanical and adhesive properties. In recent years, the use of ionic liquids (ILs) has been reported to enhance the dispersion of CNTs, thereby improving the properties of NCs based on different thermoplastic [12][13][14] and thermosetting [15][16][17][18] polymers as a result. This is because ILs interact with CNTs through cation-π Gholami et al. [7] also analyzed the dispersion efficiency of different choline chloridebased ILs in epoxy systems containing 0.3 wt% MWCNTs and cured with commercial hardeners. They observed that the addition of the glycerol and choline chloride-based ILs improved the electrical conductivity of the epoxy/CNT system by three orders of magnitude (from 10 −8 S/cm to 10 −5 S/cm). They attributed this to the ability of the IL to arrange the electrically conductive CNTs in the matrix and form a more complete conductive network. The enhanced dispersion of the CNTs also led to a 12% improvement in the tensile strength (from 64 MPa to 72 MPa) of the epoxy/CNT NCs.
However, while the dispersive effect of ILs in epoxy/CNT systems has been discussed quite widely in the literature, the role of ILs as effective curing agents has received less attention. Moreover, to the best of our knowledge, no studies have been conducted on the effect of different ILs and CNT concentrations on the final mechanical, electrical, and adhesive properties of epoxy NCs. Therefore, in this study, three different ionic liquids were selected (based on a previous study [46]) and used as curing/dispersing agents for epoxy/CNT NCs, with the objective of optimizing the performance of epoxy NCs without using traditional, volatile curing agents. With this aim in mind, the nanostructure and the thermal, electrical, mechanical, and adhesive properties of the NCs were determined and compared.

Abbreviation
Structure Properties of the IL led to an improvement, which the authors attributed to the improved adhesion between the CNTs and the epoxy resin. Finally, the tensile moduli of the epoxy resin and of the epoxy/CNT and epoxy/CNT/IL nanocomposites were all similar. Gholami et al. [7] also analyzed the dispersion efficiency of different choline chloridebased ILs in epoxy systems containing 0.3 wt% MWCNTs and cured with commercial hardeners. They observed that the addition of the glycerol and choline chloride-based ILs improved the electrical conductivity of the epoxy/CNT system by three orders of magnitude (from 10 −8 S/cm to 10 −5 S/cm). They attributed this to the ability of the IL to arrange the electrically conductive CNTs in the matrix and form a more complete conductive network. The enhanced dispersion of the CNTs also led to a 12% improvement in the tensile strength (from 64 MPa to 72 MPa) of the epoxy/CNT NCs.

IL-P-TMPP
However, while the dispersive effect of ILs in epoxy/CNT systems has been discussed quite widely in the literature, the role of ILs as effective curing agents has received less attention. Moreover, to the best of our knowledge, no studies have been conducted on the effect of different ILs and CNT concentrations on the final mechanical, electrical, and adhesive properties of epoxy NCs. Therefore, in this study, three different ionic liquids were selected (based on a previous study [46]) and used as curing/dispersing agents for epoxy/CNT NCs, with the objective of optimizing the performance of epoxy NCs without using traditional, volatile curing agents. With this aim in mind, the nanostructure and the thermal, electrical, mechanical, and adhesive properties of the NCs were determined and compared.

Materials
The ionic liquids used in this study were as follows: (a) trihexyltetradecylphosphonium bis(2,4,4-trimethylpentyl)phosphinate (IL-P-TMPP), (b) 1-ethyl-3-methylimidazolium dicyanamide (IL-I-DCA) from Sigma Aldrich, and (c) trihexyltetradecylphosphonium dicyanamide (IL-P-DCA) from IoLiTec-Ionic Liquid Technologies GmbH. Table 1 shows the structures and properties of all three. The epoxy resin employed was a diglycidyl ether of bisphenol A (DGEBA) (Nazza, Eurotex) (epoxy equivalent: 186 g; density (at 20 °C): 1.17 g/cm 3 ; viscosity (at 25 °C): 11,500-13,500 mPa·s). A traditional amine-based curing agent, 2,2′-dimethyl-4,4′-methylenebis(cyclohexylamine) (Aradur) (Huntsman), was used as a reference. The carbon nanotubes used in this work were of the Nanocyl NC7000 series (L = 1.5 µm, D = 9.5 nm, 250-300 m 2 /g surface area, 90% purity) supplied by Nanocyl. of the IL led to an improvement, which the authors attributed to the improved adhesion between the CNTs and the epoxy resin. Finally, the tensile moduli of the epoxy resin and of the epoxy/CNT and epoxy/CNT/IL nanocomposites were all similar. Gholami et al. [7] also analyzed the dispersion efficiency of different choline chloridebased ILs in epoxy systems containing 0.3 wt% MWCNTs and cured with commercial hardeners. They observed that the addition of the glycerol and choline chloride-based ILs improved the electrical conductivity of the epoxy/CNT system by three orders of magnitude (from 10 −8 S/cm to 10 −5 S/cm). They attributed this to the ability of the IL to arrange the electrically conductive CNTs in the matrix and form a more complete conductive network. The enhanced dispersion of the CNTs also led to a 12% improvement in the tensile strength (from 64 MPa to 72 MPa) of the epoxy/CNT NCs.
However, while the dispersive effect of ILs in epoxy/CNT systems has been discussed quite widely in the literature, the role of ILs as effective curing agents has received less attention. Moreover, to the best of our knowledge, no studies have been conducted on the effect of different ILs and CNT concentrations on the final mechanical, electrical, and adhesive properties of epoxy NCs. Therefore, in this study, three different ionic liquids were selected (based on a previous study [46]) and used as curing/dispersing agents for epoxy/CNT NCs, with the objective of optimizing the performance of epoxy NCs without using traditional, volatile curing agents. With this aim in mind, the nanostructure and the thermal, electrical, mechanical, and adhesive properties of the NCs were determined and compared.

Preparation of Samples
The epoxy resin was previously degassed in a vacuum oven at 80 °C for one hour. For the reference unfilled epoxy/IL and epoxy/Aradur systems, 10 phr of IL (selected as the optimum content based on our previous work [46]) and the stoichiometric concentration of the amine, respectively, were added to the epoxy resin, and the resulting mixtures were mechanically mixed at 50 °C using a Heidolph RZR2000 digital rod stirrer until com-

Preparation of Samples
The epoxy resin was previously degassed in a vacuum oven at 80 • C for one hour. For the reference unfilled epoxy/IL and epoxy/Aradur systems, 10 phr of IL (selected as the optimum content based on our previous work [46]) and the stoichiometric concentration of the amine, respectively, were added to the epoxy resin, and the resulting mixtures were mechanically mixed at 50 • C using a Heidolph RZR2000 digital rod stirrer until completely homogeneous mixtures were obtained. They were then poured into the corresponding molds or between substrates and were cured according to the curing protocols shown in Table 2. Table 2. Curing protocol used for the epoxy/IL and the epoxy/Aradur systems.

Curing Agent
Curing Protocol For the epoxy/CNT/IL systems, after degassing the DGEBA, the CNTs were added at concentrations ranging from 0 to 0.25% and mechanically mixed at 2000 rpm for 20 min using a EUROSTAR power control-visc digital stirrer. They were then ultrasonicated in a Hielscher UP400s at an amplitude of 100% for 20 min. Next, the IL (10 phr) was added and mechanically mixed at 50 • C for 5 min using a Heidolph RZR2000 digital rod stirrer. Finally, the mixture was poured into molds or placed between lap shear test substrates and the appropriate curing protocol was applied ( Table 2). Figure 1 shows the experimental flowchart.

Preparation of Samples
The epoxy resin was previously degassed in a vacuum oven at 80 °C for one hour. For the reference unfilled epoxy/IL and epoxy/Aradur systems, 10 phr of IL (selected as the optimum content based on our previous work [46]) and the stoichiometric concentration of the amine, respectively, were added to the epoxy resin, and the resulting mixtures were mechanically mixed at 50 °C using a Heidolph RZR2000 digital rod stirrer until completely homogeneous mixtures were obtained. They were then poured into the corresponding molds or between substrates and were cured according to the curing protocols shown in Table 2. For the epoxy/CNT/IL systems, after degassing the DGEBA, the CNTs were added at concentrations ranging from 0 to 0.25% and mechanically mixed at 2000 rpm for 20 min using a EUROSTAR power control-visc digital stirrer. They were then ultrasonicated in a Hielscher UP400s at an amplitude of 100% for 20 min. Next, the IL (10 phr) was added and mechanically mixed at 50 °C for 5 min using a Heidolph RZR2000 digital rod stirrer. Finally, the mixture was poured into molds or placed between lap shear test substrates and the appropriate curing protocol was applied ( Table 2). Figure 1 shows the experimental flowchart.

Thermal Properties
Dynamic mechanical analysis (DMA) was used to determine the glass transition temperature and to calculate the crosslinking density of the systems. Rectangular, nominally sized specimens measuring 17.5 × 6.0 × 2.0 mm 3 were tested using a TA Q800 viscoelastometer in single-cantilever bending mode, with a frequency of 1 Hz and an amplitude of

Characterization 2.3.1. Thermal Properties
Dynamic mechanical analysis (DMA) was used to determine the glass transition temperature and to calculate the crosslinking density of the systems. Rectangular, nominally sized specimens measuring 17.5 × 6.0 × 2.0 mm 3 were tested using a TA Q800 viscoelastometer in single-cantilever bending mode, with a frequency of 1 Hz and an amplitude of 15 µm. The heating rate was set at 4 • C/min and the temperature interval ranged from −100 • C to 250 • C. One specimen was tested per composition. The elasticity theory (Equation (1)) was used to calculate the crosslinking density (ν e ): where E r is the storage modulus in the rubbery state at a reference temperature (T r = 245 • C) and R is the ideal gas constant (8.314 J/mol·K).

Nanostructure
The nanostructure and the dispersion level of the CNTs were analyzed by transmission electron microscopy (TEM). A Tecnai G2 20 Twin microscope was used at an accelerating voltage of 200 kV. The samples were cut at a 45 • angle using a Leica EM UCG ultramicrotome with a diamond blade.

Electrical Properties
The electrical conductivity through the sample was measured using a digital Keithley 6487 picoammeter on circular samples (Ø70 mm × 2 mm thick), to which 1 V was applied for 1 min. The electrical conductivity (σ) was calculated using Equation (2): where ρ is the resistivity, V is the voltage applied, I is the intensity of the current, and 22.9 is the geometrical constant (specific area between electrodes). Three measurements were made for each reported value. The percolation threshold was calculated using Equation (3): where σ(p) is the conductivity, B is a constant, t is the critical exponent, p is the nanofiller concentration, and p c is the percolation concentration. The experimental data were fitted by plotting log(σ) vs. log(p − p c ) and increasing p c until the best linear fit was obtained.

Mechanical Properties
Three-point bending tests were carried out in an Instron 5569 universal testing machine. The span was set at 64 mm with a crosshead speed of 2 mm/min. At least 5 specimens were tested for each composition.
The flexural modulus (E f ), the flexural strength (σ F ), and the deformation at break (ε F ) were calculated according to the ISO 178 standard, using Equations (4), (5) and (6), respectively: where F is the load, F max is the maximum load, L is the span, s is the degree of deflection, and b and h are the width and thickness of the specimen, respectively. Notched Charpy impact tests were carried out using a Ceast 6548/000 pendulum with an impactor of 2 J. Notched specimens with a radius of 0.25 mm and a depth of 2.54 mm were used. At least 8 specimens were tested for each composition.

Adhesive Properties
The adhesive properties were studied by performing lap shear strength tests according to the ASTM D-1002 standard. The substrates-aluminum 2021-T351 alloy sheets measuring 100 mm × 25 mm × 1.6 mm-were purchased from Rocholl GmbH, and the tested adhesion area measured 12.5 mm × 25 mm. An Instron 5569 universal testing machine in tensile mode was used, employing a constant speed of 1 mm/min. The lap shear strength was calculated by dividing the maximum force by the adhesion area. For each reported value, 10 specimens were tested. Figure 2 shows the tanδ and the storage modulus vs temperature curves of the samples cured with the different ILs at different CNT concentrations. The main peak of the tanδ curves, which appears at high temperatures (shown in the inset), indicates the glass transition temperature (T g ). The maximums of the peaks for the IL-based systems, along with the calculated crosslinking density values, are summarized in Table 3.

Nanostructure
The nanostructures of the epoxy/IL systems were analyzed by transmission electron microscopy (TEM).   As Figure 2 and Table 3 show, neither the glass transition temperature nor the crosslinking density changed significantly upon the addition of the CNTs. In fact, both higher [49][50][51] and lower [52][53][54] T g values have been reported when CNTs were added to epoxy resins, so there is no general consensus in the literature regarding the impact of CNTs on the T g of conventionally cured epoxy/CNT systems. Decreases in T g are generally attributed to the steric hindrance of the CNTs towards the curing reaction [54,55], which gives rise to samples with less cross-linkage. By contrast, increases in T g are usually linked to decreases in the mobility of the macromolecular chains caused by the presence of CNTs. This effect is more pronounced the greater the degree of dispersion or adhesion, i.e., the two parameters reported to most heavily impact the T g [51]. Regarding amine-cured epoxy systems with ILs as dispersing agents, both increases [9] and decreases [17,48,56] in the T g have been reported. The effect of the presence of ILs is not completely clear in these cases because they are also known to act as effective plasticizers. Both decreases [36] and increases [15,37] in T g have also been reported for epoxy/CNT NCs where the ILs acted as both curing and dispersing agents. The behavior of the epoxy/Aradur system in this study was similar to that of the epoxy/IL systems; the addition of CNTs did not significantly affect the T g or the crosslinking density of the unfilled system (the T g and crosslinking density of the 0.2 wt.% CNT composition were 191 • C and 3090 mol/m 3 , respectively).

Nanostructure
The nanostructures of the epoxy/IL systems were analyzed by transmission electron microscopy (TEM). Figure 3a-c show representative micrographs of the IL-P-DCA, IL-P-TMPP, and IL-I-DCA epoxy/IL systems, respectively, each containing 0.2 wt.% of CNTs. As a reference, Figure 3d shows a representative TEM micrograph of the epoxy/Aradur NC with the same concentration of CNTs. As can be seen in Figure 3a-c, good dispersion of the nanofiller was achieved in the case of all three ILs, with mostly individually dispersed CNTs and far fewer small aggregates. When the different ILs are compared, it is evident that, in Figure 3a, there are fewer and smaller CNT aggregates than those appearing in Figure 3b,c, indicating that the CNTs were best dispersed in the epoxy/CNT/IL-P-DCA system, and more poorly dispersed in the epoxy/CNT/IL-P-TMPP and epoxy/CNT/IL-I-DCA systems. A similar nanostructure was observed in the reference epoxy/CNT/Aradur system (shown here in Figure 3d). As expected, these differences significantly affected the electrical properties of the NCs and are discussed below.
persed CNTs and far fewer small aggregates. When the different ILs are compared, it is evident that, in Figure 3a, there are fewer and smaller CNT aggregates than those appearing in Figure 3b,c, indicating that the CNTs were best dispersed in the epoxy/CNT/IL-P-DCA system, and more poorly dispersed in the epoxy/CNT/IL-P-TMPP and epoxy/CNT/IL-I-DCA systems. A similar nanostructure was observed in the reference epoxy/CNT/Aradur system (shown here in Figure 3d). As expected, these differences significantly affected the electrical properties of the NCs and are discussed below.  The achievement of good dispersion of CNTs is known to be complicated due to interactions between the sp 2 orbitals perpendicular to the layers, which lead to the reaggregation of the CNTs. ILs have been reported to be effective in terms of dispersing CNTs, although how they actually execute this is a controversial topic judging from the bibliography contained herein. In the case of imidazolium-based ILs, some authors indicate that the π-cation interaction [19,20] is likely responsible, while others believe the Van der Waals forces-based interactions [21] cause the rupture of the π-π attractive forces between the CNTs. With respect to the phosphonium-based ILs, in the absence of aromatic groups in their structures, π-cation interactions are preferred [57]. Moreover, as these ILs contain cations with long aliphatic chains, a surfactant effect has also been suggested as being responsible for the dispersive effect [15,36,37]. Figure 4 shows the electrical conductivity vs the CNT content of the different epoxy/IL systems. It can be clearly seen that the addition of CNTs led to a dramatic increase in conductivity in all the epoxy/IL systems. For example, the conductivity values of the 0.2 wt.% CNT composition were 1.13 × 10 −7 , 5.67 × 10 −8 , 1.96 × 10 −9 , and 9.99 × 10 −9 S/cm for the IL-P-TMPP, IL-P-DCA, IL-I-DCA, and Aradur-based systems, respectively. The percolation thresholds are shown in Table 4, and the fitting parameters B and t (Equation (3)) along with the conductivity values corresponding to the p c are presented in Table S1. As can be seen, the percolation threshold was reached at very low CNT fractions-0.025 wt.% or lower-in all cases. The IL-P-DCA-cured epoxy NC had the lowest p c at 0.001 wt.%. This is consistent with the best dispersion levels on the TEM micrographs. Table 4 also shows how the similar CNT dispersion levels of the other two IL-based systems (and for the reference amine-based one) also resulted in similar percolation threshold values. Thus, at low CNT shares, tiny changes in the degree of dispersion can affect the percolation threshold, i.e., the minimum concentration required to create the conductive path necessary for the transition from an insulator to semiconductor to take place. although how they actually execute this is a controversial topic judging from the bibliography contained herein. In the case of imidazolium-based ILs, some authors indicate that the π-cation interaction [19,20] is likely responsible, while others believe the Van der Waals forces-based interactions [21] cause the rupture of the π-π attractive forces between the CNTs. With respect to the phosphonium-based ILs, in the absence of aromatic groups in their structures, π-cation interactions are preferred [57]. Moreover, as these ILs contain cations with long aliphatic chains, a surfactant effect has also been suggested as being responsible for the dispersive effect [15,36,37]. Figure 4 shows the electrical conductivity vs the CNT content of the different epoxy/IL systems. It can be clearly seen that the addition of CNTs led to a dramatic increase in conductivity in all the epoxy/IL systems. For example, the conductivity values of the 0.2 wt.% CNT composition were 1.13 × 10 −7 , 5.67 × 10 −8 , 1.96 × 10 −9 , and 9.99 × 10 −9 S/cm for the IL-P-TMPP, IL-P-DCA, IL-I-DCA, and Aradur-based systems, respectively. The percolation thresholds are shown in Table 4, and the fitting parameters B and t (Equation (3)) along with the conductivity values corresponding to the pc are presented in Table  S1. As can be seen, the percolation threshold was reached at very low CNT fractions-0.025 wt.% or lower-in all cases. The IL-P-DCA-cured epoxy NC had the lowest pc at 0.001 wt.%. This is consistent with the best dispersion levels on the TEM micrographs. Table 4 also shows how the similar CNT dispersion levels of the other two IL-based systems (and for the reference amine-based one) also resulted in similar percolation threshold values. Thus, at low CNT shares, tiny changes in the degree of dispersion can affect the percolation threshold, i.e., the minimum concentration required to create the conductive path necessary for the transition from an insulator to semiconductor to take place.    At high CNT shares, the conductivity values of the systems cured with the phosphoniumbased ILs (i.e., IL-P-TMPP and IL-P-DCA) were two orders of magnitude higher than those cured with the imidazolium-based IL (i.e., IL-I-DCA), suggesting that the long chains in the structures of the former two are more effective at preventing the formation of CNT aggregates.

Electrical Properties
In the literature, a wide range of percolation threshold concentrations have been reported for epoxy/CNT NCs. This variation is probably due to the myriad factors that affect the formation of percolated networks, namely, the aspect ratio of the CNTs. Usually, the reported p c values do not exceed 1-2 wt.% [58], with most ranging from 0.1 to 1 wt.% [59][60][61]. However, figures as low as 0.04 wt.% [62,63] or 0.001 wt.% [64] have also been reported. Lopes Pereira et al. [48] studied the effect of adding ILs as nanofiller-dispersing agents and reported an increase of three orders of magnitude in electrical conductivity compared to the non-IL system. Regarding the conductivity of the Nanocyl NC7000 CNT-based percolated systems, a wide range of values (from 10 −7 to 10 −2 S/cm) can be found in our bibliography depending on the experimental technique or conditions used [15,36,37]. Figure 5 shows the flexural modulus, flexural strength, and deformation at break of the epoxy/IL NCs as a function of the CNT content. The data for the reference unfilled epoxy/Aradur system have also been included (the green, solid line shows the average value, while the shaded area shows the standard deviation).  As Figure 5a shows, overall, the flexural modulus of the epoxy resin was barely affected by the addition of the CNTs. Slight increases were only observed for the IL-I-DCA-based system at high CNT shares. These results suggest that neither the crosslinking density (Table 3) nor the degree of dispersion of the CNTs (Figure 3a-c) in these systems are directly related to their mechanical properties. Similar results were obtained in the reference epoxy/Aradur system, given that the addition of 0.2 wt.% CNTs did not lead to significant changes in the flexural modulus (2270 MPa) or in flexural strength (56.0 MPa). This is further discussed below.

Mechanical Properties
No significant trends in flexural strength were observed in any of the systems (Figure 5b). As with the flexural modulus, the IL-I-DCA-cured samples with a high concentration of CNTs scored highest. It is worth noting that the flexural modulus and strength data of some of the compositions are similar or better than those of the amine-cured reference system.
With respect to high-strain mechanical properties, the deformation at break (Figure 5c) and the impact strength ( Figure 6) both decreased when CNTs were added. This was to be expected because nanofillers in general-and CNTs in particular-are known to act as crack initiators and/or stress-concentration points, thus leading to decreases in ductility and toughness [1].   Epoxy resins that have been mechanically improved by adding CNTs have been extensively documented in the literature [1,2]. In amine-cured epoxy/CNT NCs with ILs as dispersing agents, the mechanical properties were further enhanced due to the enhanced levels of dispersion [6,7,9,10]. Nevertheless, the fact that ILs can also act as plasticizers also needs to be taken into account. Accordingly, depending on the amount of IL used, the plasticizing effect may be predominant, causing decreases in low-strain mechanical properties [7].
Few papers on the roles of ILs as both curing and dispersing agents in epoxy systems have examined their mechanical behavior. For those that have, organoclays [65], silica [47], core-shell particles [43], and CNTs [8] were used as nanofillers. In the epoxy/IL/CNT system [8], for example, the authors reported that Young's modulus increased with the CNT content with respect to the unfilled epoxy/IL-I-DCA system. However, this increase was not significant above 1 wt.% CNTs, which is probably due to the deficient dispersion associated with an excessive number of CNTs. Figure 7 shows the lap shear strength of the epoxy/IL NCs as a function of their CNT content. The corresponding result for the unfilled epoxy/Aradur system is also shown as a reference. As can be seen, regardless of the IL used, the addition of low concentrations of CNTs led to increases in the lap shear strength compared to the unfilled compositions. However, higher concentrations of CNTs did not lead to higher lap shear strength values. A maximum improvement in adhesive properties (30%) was attained with the IL-P-DCA-cured epoxy system containing 0.025 wt.% CNTs. Similar increases-close to 30% (from 6.8 to 8.8 MPa)-were also observed when 0.2% wt.% CNTs were added to the reference epoxy/Aradur system. Figure 7 shows the lap shear strength of the epoxy/IL NCs as a function of their CNT content. The corresponding result for the unfilled epoxy/Aradur system is also shown as a reference. As can be seen, regardless of the IL used, the addition of low concentrations of CNTs led to increases in the lap shear strength compared to the unfilled compositions. However, higher concentrations of CNTs did not lead to higher lap shear strength values. A maximum improvement in adhesive properties (30%) was attained with the IL-P-DCAcured epoxy system containing 0.025 wt.% CNTs. Similar increases-close to 30% (from 6.8 to 8.8 MPa)-were also observed when 0.2% wt.% CNTs were added to the reference epoxy/Aradur system. Our findings are consistent with the results reported in the literature for epoxy/CNT systems [4,5,11]. In an epoxy/CNT/amine system, Alves et al. [16] reported that the improvement in the dispersion of CNTs effected by a masterbatch led to enhanced adhesive properties. However, they also observed-in the same study-that even though the dispersion of the CNTs was enhanced when an IL was added, the lap shear strength decreased by over 50% due to the lubricating effect of the IL [13,66].

Adhesive Properties
Considering the results in Figure 7, it is noteworthy that, regardless of the CNT content, all the epoxy/IL-I-DCA NCs showed significantly enhanced adhesive properties compared to both the reference unfilled epoxy/Aradur system and the CNT-filled epoxy/Aradur composition. So, in summary, electrically conductive epoxy adhesives with outstanding adhesive properties were obtained when ILs were used as both the curing and dispersing agents.

Conclusions
The dual role of ionic liquids (ILs) as effective curing and dispersing agents produced volatile-amine-free epoxy/CNT nanocomposites with a better balance of mechanical, electrical, and adhesive properties. Three different ILs were tested, and all three led to good dispersion of the nanofiller, featuring individually dispersed CNTs as well as some small aggregates. Overall, with a percolation threshold of 0.001 wt.%, the IL-P-DCA system was the most effective. Our findings are consistent with the results reported in the literature for epoxy/CNT systems [4,5,11]. In an epoxy/CNT/amine system, Alves et al. [16] reported that the improvement in the dispersion of CNTs effected by a masterbatch led to enhanced adhesive properties. However, they also observed-in the same study-that even though the dispersion of the CNTs was enhanced when an IL was added, the lap shear strength decreased by over 50% due to the lubricating effect of the IL [13,66].
Considering the results in Figure 7, it is noteworthy that, regardless of the CNT content, all the epoxy/IL-I-DCA NCs showed significantly enhanced adhesive properties compared to both the reference unfilled epoxy/Aradur system and the CNT-filled epoxy/Aradur composition. So, in summary, electrically conductive epoxy adhesives with outstanding adhesive properties were obtained when ILs were used as both the curing and dispersing agents.

Conclusions
The dual role of ionic liquids (ILs) as effective curing and dispersing agents produced volatile-amine-free epoxy/CNT nanocomposites with a better balance of mechanical, electrical, and adhesive properties. Three different ILs were tested, and all three led to good dispersion of the nanofiller, featuring individually dispersed CNTs as well as some small aggregates. Overall, with a percolation threshold of 0.001 wt.%, the IL-P-DCA system was the most effective.
The addition of CNTs had no effect on the thermal or low-strain mechanical properties of the epoxy/IL systems. However, it did improve the systems' adhesive properties. The epoxy/IL-P-DCA system containing 0.025 wt.% CNTs improved by 30% and was the best of the three. This work proves that, using very small amounts of CNTs, it is possible to obtain electrically conductive, amine-free epoxy adhesives with similar mechanical properties but greater lap shear strength than the reference amine-cured epoxy system. ILs have a lower vapor pressure, and a significantly lower amount is needed to effectively cure epoxy resins. Therefore, replacing conventional epoxy resin curing agents (amines, anhydrides, etc.) with ILs is a major step forward in the development of more sustainable materials.

Supplementary Materials:
The following are available online at https://www.mdpi.com/article/10 .3390/nano13040725/s1, Table S1: Fitting parameters (B and t) and conductivity values corresponding to the p c of the epoxy/CNT/IL NCs cured with IL-P-TMPP, IL-P-DCA and IL-I-DCA and of the reference epoxy/CNT/Aradur systems.