Epoxy Coatings Containing Modified Graphene for Electromagnetic Shielding

This study presents the functionalization and characterization of graphene and electromagnetic interference (EMI) attenuation capacity in epoxy-nanocomposites. The modification of graphene involved both small molecules and polymers for compatibilization with epoxy resin components to provide EMI shielding. The TGA and RAMAN analyses confirmed the synthesis of graphene with a different layer thickness of the graphene sheets. Graphene samples with different layer thicknesses (monolayer, few layers, and multilayer) were selected and further employed for epoxy coating formulation. The obtained nanocomposites were characterized in terms of EMI shielding effectiveness, SEM, micro-CT, magnetic properties, and stress-strain resistance. The EMI shielding effectiveness results indicated that the unmodified graphene and hexamethylene diamine (HMDA) modified graphene displayed the best EMI shielding properties at 11 GHz. However, the epoxy nanocomposites based on HMDA modified graphene displayed better flexibility with an identical EMI shielding effectiveness compared to the unmodified graphene despite the formation of aggregates. The improved flexibility of the epoxy nanocomposites and EMI shielding characteristics of HMDA functionalized graphene offers a practical solution for textile coatings with microwave absorbing (MA) capacity.


(a) Functionalization of Graphene with small molecules
Graphene oxide was prepared according to a modified method. Briefly, 1 g of graphene was dispersed in 30 mL of H 2 SO 4 (95-98%), then 10 mL of HNO 3 (68%) was slowly added and the reaction mixture was stirred for an additional 2 h. After, 100 mL H 2 O was added dropwise, and the reaction mixture was let to cool down under stirring before the addition of another 200 mL H 2 O. The reaction mixture was then neutralized using NaOH until pH 7 was achieved and the obtained GO was separated by filtration and washed thoroughly with water.
Synthesis of Graphene-G-BP. In a round bottom flask, 1 g of graphene was dispersed in 60 mL of DMF using an ultrasonic processor (Hielscher, Teltow, Germany, UP50H) followed by the addition of 0.5 g benzoyl peroxide. The reaction mixture was heated to 80 • C under nitrogen and kept under stirring for 4 h. The product was separated by vacuum filtration and washed thoroughly with methanol and acetone.
Synthesis of G-HMDA. In a round bottom flask, 1 g of graphene was dispersed in 60 mL of DMF using an ultrasonic processor (Hielscher, UP50H) followed by the addition of 10 g HMDA. The reaction mixture was heated to 80 • C under nitrogen and kept under stirring for 4 h. The product was separated by vacuum filtration and washed thoroughly with water, methanol, and acetone before being dried.

(b) Functionalization of Graphene with polymer chains
Synthesis of G-PAM. In a round bottom flask, 1 g of graphene was dispersed in 60 mL of DMF using an ultrasonic processor (Hielscher, UP50H) followed by the addition of 10 g acrylamide and 0.1 g of LP. The reaction mixture was heated to 80 • C under nitrogen and kept under stirring for 4 h. The product was separated by vacuum filtration and washed thoroughly with DMF, water, and acetone before being dried.
Synthesis of G-PGMA. In a round bottom flask, 1 g of graphene was dispersed in 60 mL of DMF using an ultrasonic processor (Hielscher, UP50H) followed by the addition of 10 mL GMA and 0.1 g of LP. The reaction mixture was heated to 80 • C under nitrogen and kept under stirring for 4 h. The product was separated by vacuum filtration and washed thoroughly with DMF, water, and acetone before being dried.
Synthesis of G-PHexylMA. In a round bottom flask, 1 g of graphene was dispersed in 60 mL of DMF using an ultrasonic processor (Hielscher, UP50H) followed by the addition of 10 mL hexylMA and 0.1 g of LP. The reaction mixture was heated to 80 • C under nitrogen and kept under stirring for 4 h. The product was separated by vacuum filtration and washed thoroughly with DMF, water, and acetone before being dried.

(c) Epoxy coating formulation
The epoxy coating formulation involved the use of EPOTEC YD 011X75 (Epoxy Technology, Billerica, MA, USA) (a bisphenol-A based epoxy resin), dioctyl adipate (BASF) (as plasticizer), EPAMINE PC13 (PO.INT.ER) (as hardener), BP-183-B (Zhejiang Huate Group, Huzhou, China) (organic bentonite as rheology modifier), and IOX B-03 (LANXESS) (synthetic iron oxide-Fe 3 O 4 ). The resin: hardener ratio was set at 5:1; a 1:1 toluene: acetone solvent mixture was used to facilitate the dispersion of the graphene and modified graphene either in the resin (G, GO, G-PGMA) or in the hardener component (G-HDMA) and other fillers (BP-183-B and IOX B-03). The concentration of the EMI active fillers is presented in Error! Reference source not found. The coating was applied on polyester woven material (used for EMI shielding efficiency) and on polyethylene sheets from which the epoxy films were recovered and used for the characterization of the mechanical properties. The deposition was performed by doctor blade technique to ensure a reproducible film thickness.

Characterization Methods
The polymer nanocomposite films were investigated by optical microscopy using an Olympus BX41 light microscope (Olympus Corporation, Tokyo, Japan) equipped with live view E330 7.5 MP Digital SLR Camera and QuickPhoto Micro 2.3 software (PROMICRA, Prague, Czech Republic). The images were collected in transmission mode.
The morphology of the nanocomposite films was also investigated by SEM (scanning electron microscopy) using a Tescan Vega II LMU SEM instrument (TESCAN, Brno, Czech Republic) at 10 keV acceleration voltage.
The distribution of the graphene and iron oxide particles inside the epoxy matrix was examined via micro-CT technique. The SkyScan micro-CT attachment allowed for converting the Tescan Vega II LMU SEM to an X-ray microtomograph for non-destructive imaging and for measuring of the object's internal microstructure of specimens. Analysis parameters: Exposure time-4 s per projection at electron beam currents of 100 nA; accelerating voltage-30 KeV; step size −1 • ; scanning time-24 min. Reconstruction was performed by the NRecon program, which used float-point data values for internal calculations during reconstruction and afterward allowed the operator to define the density window as a range of the reconstructed values. The full set of reconstruction results was visualized by the program DataViewer ® 2D/3D Micro-CT Slice Visualization (Micro Photonics Inc., Allentown, PA, USA).
Raman spectra of the functionalized graphene were recorded on a DXR Raman Microscope (Thermo Scientific, Waltham, MA, USA) by 473 nm laser line.
Stress-strain curves were obtained using an Instron 3382 testing machine (Instron, Norwood, MA, USA). The samples were prepared for the tensile tests by cutting the nanocomposite films (without woven polyester). The tests were carried out according to the international standard ASTM D3039/D3039M-08. For each specimen, the rate of the extension was set at 500 mm/min, and the separation of the initial jaws was set at 50 mm (plain jaw faces). For each type of nanocomposite film, five tensile tests were carried out and the average of the measured values and the standard deviation for each point was registered. A comparative multigraph containing all the true stress/true strain values characteristic for each synthesized material was plotted to evaluate the influence of the nanofiller on their mechanical properties. This multigraph was designed to show only the curves with the closest parameters to the mean values from each set of specimens.
Hysteresis loops at 300 K were measured using a SQUID magnetometer (Magnetic Properties Measurement System, QD-MPMS-XL-7AC, manufactured by Quantum Design, San Diego, CA, USA) running under the RSO (Reciprocating Sample Option) mode. This apparatus allows performing measurements with a magnetic moment resolution up to 10 −7 emu. For magnetic measurements, the epoxy thin film strips used were closed in small sample holders.
The ability of the synthesized materials to attenuate radar waves in the domain of 8-12 GHz was investigated as follows: A full-anechoic chamber (Figure 1), consisting of two distinct areas (command chamber and testing chamber) separated by a transition panel was utilized for performing the measurements. A Rohde & Schwarz SMB100A generator and a command equipment were placed in the command chamber. While in the testing chamber, we placed a metallic cube provided with a slot (A4 dimensions) in which the tested material was fixed. The transfer of the emitted signal was achieved through the transition panel situated between the two above mentioned chambers. Inside the metallic cube, we placed a Tektronix spectrum analyzer (RSA range) connected to a HF906 horn antenna for the reception of the signal to evaluate the shielding efficiency of the tested material. For the emission of the signal, in the testing chamber we also positioned a Horn SAS 571 antenna, which was placed outside the cube, in front of the slot where the tested material was fixed. The antennas have been chosen so that their working ranges cover the range of interest for these materials. The transfer of information from the spectrum analyzer to its control equipment located in the control chamber was done utilizing an optic fiber, the transition being made through a waveguide located between the two chambers. Given that in radar applications the range of interest is in the domain of 8 ÷ 12 GHz, the materials were tested in the range 7 ÷ 12.75 GHz by utilizing the above-described setup, schematically illustrated in Figure 1. To assess the shielding effect of the tested material fixed in the slot of the metallic cube, two measurements were performed: a reference measurement (when the slot provided for fixing the samples was empty, allowing the signal to pass untainted) and the measurement of the sample (when the slot provided was covered by the material subjected to this test and the signal passed through it). distinct areas (command chamber and testing chamber) separated by a transition pan was utilized for performing the measurements. A Rohde & Schwarz SMB100A generat and a command equipment were placed in the command chamber. While in the testin chamber, we placed a metallic cube provided with a slot (A4 dimensions) in which th tested material was fixed. The transfer of the emitted signal was achieved through th transition panel situated between the two above mentioned chambers. Inside the metall cube, we placed a Tektronix spectrum analyzer (RSA range) connected to a HF906 ho antenna for the reception of the signal to evaluate the shielding efficiency of the teste material. For the emission of the signal, in the testing chamber we also positioned a Ho SAS 571 antenna, which was placed outside the cube, in front of the slot where the teste material was fixed. The antennas have been chosen so that their working ranges cover th range of interest for these materials. The transfer of information from the spectrum an lyzer to its control equipment located in the control chamber was done utilizing an opt fiber, the transition being made through a waveguide located between the two chamber Given that in radar applications the range of interest is in the domain of 8 ÷ 12 GHz, th materials were tested in the range 7 ÷ 12.75 GHz by utilizing the above-described setu schematically illustrated in Figure 1. To assess the shielding effect of the tested materi fixed in the slot of the metallic cube, two measurements were performed: a referen measurement (when the slot provided for fixing the samples was empty, allowing th signal to pass untainted) and the measurement of the sample (when the slot provided w covered by the material subjected to this test and the signal passed through it).  The EMI shielding efficiency (SE) is the result of three mechanisms, reflection loss, absorption loss, and multiple reflections loss.
To calculate the SE total , Equation (2) was used where E i and E t are the incident and transmitted electric fields, respectively.

Results
The most utilized method to modify G involves obtaining GO, which was then mixed with epoxy resin and deposited on the textile material. This first stage can be used to highlight the physical compatibility between the textile and the modified epoxy resin. Thus, the textile material prior to and after the application of the modified epoxy resin coating was subjected to optical microscopy analysis.
From the comparative analysis of the images in Figure 2, it can be noticed that the resin coating adhered to almost the entire textile surface and filled the pores in the textile material. However, aggregates of different sizes can be observed, which indicates an improper dispersion of the GO in the epoxy resin matrix. The aggregates can be the result of the rapid reaction between the functional groups of GO and the amine component of the epoxy resin, leading to a reduction in the homogeneity of the deposited coating.

Results
The most utilized method to modify G involves obtaining GO, which was then mixed with epoxy resin and deposited on the textile material. This first stage can be used to highlight the physical compatibility between the textile and the modified epoxy resin. Thus, the textile material prior to and after the application of the modified epoxy resin coating was subjected to optical microscopy analysis.
From the comparative analysis of the images in Figure 2, it can be noticed that the resin coating adhered to almost the entire textile surface and filled the pores in the textile material. However, aggregates of different sizes can be observed, which indicates an improper dispersion of the GO in the epoxy resin matrix. The aggregates can be the result of the rapid reaction between the functional groups of GO and the amine component of the epoxy resin, leading to a reduction in the homogeneity of the deposited coating. SEM analysis was performed on the two samples for a more precise analysis. From the images in Figures 2 and 3 good compatibility between the textile material and the epoxy resin can be observed, however, there are some areas with a non-uniform coating which can be explained by the deposition process. SEM analysis was performed on the two samples for a more precise analysis. From the images in Figures 2 and 3 good compatibility between the textile material and the epoxy resin can be observed, however, there are some areas with a non-uniform coating which can be explained by the deposition process. SEM analysis was performed on the two samples for a more precise analysis. From the images in Figures 2 and 3 good compatibility between the textile material and the epoxy resin can be observed, however, there are some areas with a non-uniform coating which can be explained by the deposition process. Addressing the filler capacity to disperse in the resin matrix is a viable solution to further improve the coating quality. For this reason, several methods for graphene functionalization by the introduction of functional groups or polymer grafting were explored. The efficient dispersion and filler compatibility with the epoxy resin are critical aspects that affect the mechanical and microwave absorbing characteristics of the coating. The introduction of functional groups involved the oxidation of graphene, grafting of radical species obtained by the degradation of benzoyl peroxide, and the addition of hexamethylenediamine units to the graphene backbone. The polymer grafting assumed the polymerization in the presence of graphene. The selected monomers were methyl methacrylate (PMMA), glycidyl methacrylate (PGMA), hexyl methacrylate (PhexylMA), and acrylamide (PAM).
Thermogravimetric analyses (TGA) were performed to confirm the functionalization of the graphene (Figure 4). Addressing the filler capacity to disperse in the resin matrix is a viable solution to further improve the coating quality. For this reason, several methods for graphene functionalization by the introduction of functional groups or polymer grafting were explored. The efficient dispersion and filler compatibility with the epoxy resin are critical aspects that affect the mechanical and microwave absorbing characteristics of the coating. The introduction of functional groups involved the oxidation of graphene, grafting of radical species obtained by the degradation of benzoyl peroxide, and the addition of hexamethylenediamine units to the graphene backbone. The polymer grafting assumed the polymerization in the presence of graphene. The selected monomers were methyl methacrylate (PMMA), glycidyl methacrylate (PGMA), hexyl methacrylate (PhexylMA), and acrylamide (PAM).
Thermogravimetric analyses (TGA) were performed to confirm the functionalization of the graphene (Figure 4). Thermogravimetric analyses (TGA) were performed to confirm the functionalization of the graphene (Figure 4). In Figure 4 are presented the comparative TGA analyses for the modified graphene with small molecules/functional groups (A) and with polymers (B). Both types of functionalization aim for the facilitation of graphene dispersion in the epoxy resin, and they can permit a chemical interaction. The analysis of the spectra reveals that the highest thermal resistance was registered for the initial graphene. Considering the first modification approach, small molecules or functional groups, the introduction of new functionality on the graphene backbone results in a decrease of thermal stability. Both HMDA and PB In Figure 4 are presented the comparative TGA analyses for the modified graphene with small molecules/functional groups (A) and with polymers (B). Both types of functionalization aim for the facilitation of graphene dispersion in the epoxy resin, and they can permit a chemical interaction. The analysis of the spectra reveals that the highest thermal resistance was registered for the initial graphene. Considering the first modification approach, small molecules or functional groups, the introduction of new functionality on the graphene backbone results in a decrease of thermal stability. Both HMDA and PB afforded similar results with a residual mass of over 65% at 900 • C. As expected, the oxidation of graphene resulted in the introduction of functional groups hydroxyl [34,35], carboxyl [34,36,37], and oxirane [38], but the registered weight loss is lower than that afforded by the graphene functionalized by the radical grafting of benzoyl peroxide radicals and HMDA addition. The TGA results for polymer functionalized graphene indicate a relatively low polymer to graphene ratio in the case of methyl methacrylate and hexyl methacrylate. Nevertheless, in the case of glycidyl methacrylate and acrylamide this ratio increases. This observation can be explained by the difference in reactivity between the monomers and the competition between the radical trapping action of graphene and the homopolymerization process of the monomer.
RAMAN spectroscopy was performed on the modified graphene to confirm the chemical modification of the graphene ( Figure 5).
tively low polymer to graphene ratio in the case of methyl methacrylate and hexyl methacrylate. Nevertheless, in the case of glycidyl methacrylate and acrylamide this ratio increases. This observation can be explained by the difference in reactivity between the monomers and the competition between the radical trapping action of graphene and the homopolymerization process of the monomer.
RAMAN spectroscopy was performed on the modified graphene to confirm the chemical modification of the graphene ( Figure 5). RAMAN spectra analysis of graphene can give valuable information regarding the degree of functionalization, or defect introduction, through the comparison of the intensity of the D (1360 cm −1 ) and G (1575 cm −1 ) bands. Thus, based on the ID/IG ratio ( Figure  5C,D) we can notice that the highest degree of functionalization was obtained in the case of HDMA and PAM. This observation coincides with the TGA results, confirming the covalent grafting of the small molecule and polymer units.
RAMAN spectra also offer information on the thickness of the graphene sheets and their variation induced by the functionalization technique can be ascertained using the ratio between the G and 2D (2680 cm −1 ) bands. Using the IG/I2D ratio ( Figure 5C RAMAN spectra analysis of graphene can give valuable information regarding the degree of functionalization, or defect introduction, through the comparison of the intensity of the D (1360 cm −1 ) and G (1575 cm −1 ) bands. Thus, based on the I D /I G ratio ( Figure 5C,D) we can notice that the highest degree of functionalization was obtained in the case of HDMA and PAM. This observation coincides with the TGA results, confirming the covalent grafting of the small molecule and polymer units.
RAMAN spectra also offer information on the thickness of the graphene sheets and their variation induced by the functionalization technique can be ascertained using the ratio between the G and 2D (2680 cm −1 ) bands. Using the I G /I 2D ratio ( Figure 5C,D) it can be noticed that in the case of PAM a high degree of functionalization also leads to the obtaining of thinner graphene structures. Thus, during the polymerization process the exfoliation of the graphene layers also takes place towards a monolayer structure (the I G /I 2D value being <0.5). Similarly, for the G-PHexylMA derivative, a similar process is observed, despite the lower functionalization degree. This can be explained by the steric effect of the hexyl unit. In contrast, in G-PGMA and G-PMMA a higher thickness of the graphene stacks was observed. Thus, although G-PMMA and G-PHexylMA display a similar functionalization degree, the thickness of the graphene sheets is different. Another explanation for this aspect resides in the competition during the functionalization process between the radical trapping by the graphene and the homopolymerization of the monomer units. Thus, MMA is more susceptible to homopolymerization compared to hexyl methacrylate and the radical species are more stable than in the case of acrylamide. Surprisingly, in the case of the HDMA, although a high degree of functionalization was obtained, from the I G /I 2D ratio a multilayer graphene structure was observed. This can be explained by the bifunctionality of the HMDA, which can be intercalated between the graphene sheets and react with both layers. A graphical representation of the obtained structures is presented in Scheme 1. effect of the hexyl unit. In contrast, in G-PGMA and G-PMMA a higher thickness of the graphene stacks was observed. Thus, although G-PMMA and G-PHexylMA display a similar functionalization degree, the thickness of the graphene sheets is different. Another explanation for this aspect resides in the competition during the functionalization process between the radical trapping by the graphene and the homopolymerization of the monomer units. Thus, MMA is more susceptible to homopolymerization compared to hexyl methacrylate and the radical species are more stable than in the case of acrylamide. Surprisingly, in the case of the HDMA, although a high degree of functionalization was obtained, from the IG/I2D ratio a multilayer graphene structure was observed. This can be explained by the bifunctionality of the HMDA, which can be intercalated between the graphene sheets and react with both layers. A graphical representation of the obtained structures is presented in Scheme 1.

Scheme 1.
Graphical representation of the graphene stacks' thickness depending on the functionalization technique.
The practical aim of this study consisted in the synthesis, characterization, and utilization of nanocomposite materials with the capacity for EMI shielding. Therefore, four representative specimens G, GO, G-HDMA, and G-PGMA were selected from both the "few layers" and the "multilayer" examples. The selected specimens present the capacity to react with one of the epoxy resin components, while G was selected as the reference point. Iron oxide particles were also added in the nanocomposites to enhance their EMI shielding effectiveness properties. The samples coding is presented in Table 1 while the electromagnetic shielding efficiency is presented in Figure 6. The practical aim of this study consisted in the synthesis, characterization, and utilization of nanocomposite materials with the capacity for EMI shielding. Therefore, four representative specimens G, GO, G-HDMA, and G-PGMA were selected from both the "few layers" and the "multilayer" examples. The selected specimens present the capacity to react with one of the epoxy resin components, while G was selected as the reference point. Iron oxide particles were also added in the nanocomposites to enhance their EMI shielding effectiveness properties. The samples coding is presented in Table 1 while the electromagnetic shielding efficiency is presented in Figure 6.  The EMI shielding results present the highest values at 11 GHz and the order for shielding effectiveness is: MB017 ≈ MB013 > MB018 ≈ MB014 > MB015 > MB016. Table 2 compares the EMI shielding properties of different composite materials reported in the literature taking into account the matrix, filler and its content, thickness of  The EMI shielding results present the highest values at 11 GHz and the order for shielding effectiveness is: MB017 ≈ MB013 > MB018 ≈ MB014 > MB015 > MB016. Table 2 compares the EMI shielding properties of different composite materials reported in the literature taking into account the matrix, filler and its content, thickness of the sample, and microwave frequency range. Although the values obtained in our case are small, the advantage of a lightweight, cheap solution with good mechanical properties with the capacity of facile scale up can make the materials viable for commercial applications. The EMI shielding effectiveness depends on the electrical conductivity, permeability, and thickness of the materials [46]. Graphene is an attractive candidate because of its high electrical conductivity, low density, high specific surface area, large aspect ratios, excellent chemical and environmental stability, and mechanical flexibility.
The deposition technique permitted the obtaining of coatings with similar thicknesses of around 100 µm (Figure 7), but the difference between the samples consists in the permeability and the electrical conductivity. The EMI shielding effectiveness depends on the electrical conductivity, permeability, and thickness of the materials [46]. Graphene is an attractive candidate because of its high electrical conductivity, low density, high specific surface area, large aspect ratios, excellent chemical and environmental stability, and mechanical flexibility.
The deposition technique permitted the obtaining of coatings with similar thicknesses of around 100 µm (Figure 7), but the difference between the samples consists in the permeability and the electrical conductivity. An electromagnetic wave (such as light) has both an electric and a magnetic component. Magnetism is defined as the physical phenomena produced by the moving electric charge. A magnetic field can also induce the movement of the charged particles producing an electrical current, which is the proof of the dependence between magnetism and electric conductivity. The magnetic properties of the samples were assessed to explain their electromagnetic shielding capacity (Figure 8). The values of the coercive field, Hc, and the remanence (the ratio between the remanence magnetization, Mr, and the one of saturation Ms, namely Mr/Ms) are very close for all samples, but the small differences can be correlated as follows: MB014 > MB013 > MB017 > MB018 > MB015 > MB016. An electromagnetic wave (such as light) has both an electric and a magnetic component. Magnetism is defined as the physical phenomena produced by the moving electric charge. A magnetic field can also induce the movement of the charged particles producing an electrical current, which is the proof of the dependence between magnetism and electric conductivity. The magnetic properties of the samples were assessed to explain their electromagnetic shielding capacity (Figure 8). The values of the coercive field, Hc, and the remanence (the ratio between the remanence magnetization, Mr, and the one of saturation Ms, namely Mr/Ms) are very close for all samples, but the small differences can be correlated as follows: An electromagnetic wave (such as light) has both an electric and a magnetic component. Magnetism is defined as the physical phenomena produced by the moving electric charge. A magnetic field can also induce the movement of the charged particles producing an electrical current, which is the proof of the dependence between magnetism and electric conductivity. The magnetic properties of the samples were assessed to explain their electromagnetic shielding capacity (Figure 8). The values of the coercive field, Hc, and the remanence (the ratio between the remanence magnetization, Mr, and the one of saturation Ms, namely Mr/Ms) are very close for all samples, but the small differences can be correlated as follows: MB014 > MB013 > MB017 > MB018 > MB015 > MB016.  It can be easily noticed that the EMI shielding attenuation efficiency decrease does not follow the same trend as the magnetic properties. The last two samples, MB015 and MB016, respect the order for both magnetism and EMI attenuation. These low values could be explained by a higher amount of doping agent which leads to the formation of larger aggregates in the case of MB015, therefore larger "multilayer" structures by reaction of the amine group of HMDA with the oxirane of the epoxy component. In the case of MB016, although initially G-PGMA displays a "few layers" structure, the introduction in the epoxy resin could lead to aggregates by reaction of the oxirane present in PGMA with the amine component of the resin. The enhanced magnetic properties of MB014 can be explained by the increased amount of dopant presenting magnetic characteristics. Based on these explanations, a clear correlation about the determining factor for EMI shielding improvement cannot be made. Therefore, the next step consisted in the highlighting of aggregates formation by micro-CT analysis (Figure 9) for samples MB013, MB014, MB015, and MB017.
The largest aggregates can be observed for sample MB013, followed by MB015 and MB014, while the most uniform sample appears to be MB017, all utilizing the "multilayer" type of functionalized graphene. Even if in the case of MB013 large aggregates can be observed, the EMI shielding performance is similar to MB017. In the case of MB017, a very good dispersion of the doping agents can be observed (usually a determinant aspect for EMI), while in the case of MB013 the good results good be attributed to an improvement of the electrical conductivity. Therefore, the electroconductive properties of the fillers counterbalance the lack of uniformity of the sample leading to a good EMI shielding efficiency. Thus, it can be concluded that G-HMDA presents an enhanced electrical conductivity compared with the unmodified graphene which is confirmed by similar examples in the literature data [47]. of MB016, although initially G-PGMA displays a "few layers" structure, the introduction in the epoxy resin could lead to aggregates by reaction of the oxirane present in PGMA with the amine component of the resin. The enhanced magnetic properties of MB014 can be explained by the increased amount of dopant presenting magnetic characteristics. Based on these explanations, a clear correlation about the determining factor for EMI shielding improvement cannot be made. Therefore, the next step consisted in the highlighting of aggregates formation by micro-CT analysis (Figure 9) for samples MB013, MB014, MB015, and MB017. The largest aggregates can be observed for sample MB013, followed by MB015 and MB014, while the most uniform sample appears to be MB017, all utilizing the "multilayer" type of functionalized graphene. Even if in the case of MB013 large aggregates can be observed, the EMI shielding performance is similar to MB017. In the case of MB017, a very good dispersion of the doping agents can be observed (usually a determinant aspect for EMI), while in the case of MB013 the good results good be attributed to an improvement of the electrical conductivity. Therefore, the electroconductive properties of the fillers counterbalance the lack of uniformity of the sample leading to a good EMI shielding efficiency. Thus, it can be concluded that G-HMDA presents an enhanced electrical conductivity compared with the unmodified graphene which is confirmed by similar examples in the literature data [47]. The analysis of the mechanical properties of the materials was also performed considering the application of the materials. Figure 10 illustrates a comparative stress-strain plot of epoxy thin films synthesized in this study. The analysis revealed that MB013 is the most elastic sample, but it also presents the lowest mechanical resistance. This could be explained by an improved load transfer due to the presence of amino-functionalized graphene [48,49]. The addition of a supplementary amount of iron oxide to this formulation led to higher mechanical resistance (MB014) probably due to a reinforcing effect of the filler. On the other hand, a minor influence on the improvement of the mechanical performances of these thin films was observed when doubling the concentration of G-HDMA (sample MB015). In contrast with these first three materials, the samples containing G-PGMA (MB016) displayed superior mechanical performances, reaching a maximum value of approximately 1.5 × 10 7 Pa tensile stress at 1.64% strain, probably due to the interactions established between the two polymers chain, the epoxy resin and the PGMA, grafted on the G surfaces, respectively. The samples containing neat G (MB017) resisted up to 1.4 × 10 7 Pa tensile stress, the value measured at 1% strain. The mechanical behavior of MB018 to tensile load is comparable to that of MB014. The analysis of the mechanical properties of the materials was also performed considering the application of the materials. Figure 10 illustrates a comparative stress-strain plot of epoxy thin films synthesized in this study. The analysis revealed that MB013 is the most elastic sample, but it also presents the lowest mechanical resistance. This could be explained by an improved load transfer due to the presence of amino-functionalized graphene [48,49]. The addition of a supplementary amount of iron oxide to this formulation led to higher mechanical resistance (MB014) probably due to a reinforcing effect of the filler. On the other hand, a minor influence on the improvement of the mechanical performances of these thin films was observed when doubling the concentration of G-HDMA (sample MB015). In contrast with these first three materials, the samples containing G-PGMA (MB016) displayed superior mechanical performances, reaching a maximum value of approximately 1.5 × 10 7 Pa tensile stress at 1.64% strain, probably due to the interactions established between the two polymers chain, the epoxy resin and the PGMA, grafted on the G surfaces, respectively. The samples containing neat G (MB017) resisted up to 1.4•× 10 7 Pa tensile stress, the value measured at 1% strain. The mechanical behavior of MB018 to tensile load is comparable to that of MB014. Figure 10. Comparative stress-strain plots of the thin films.

Conclusions
This study highlights the synthesis and characterization of epoxy-nanocomposites containing nanofillers of unmodified and functionalized graphene. The graphene modifi-

Conclusions
This study highlights the synthesis and characterization of epoxy-nanocomposites containing nanofillers of unmodified and functionalized graphene. The graphene modification involved both functional groups or small molecules and polymers for compatibilization with the epoxy resin components to provide electromagnetic interference (EMI) shielding effectiveness. The first part of the study was dedicated to the modification of graphene and its characterization by RAMAN and TGA. The results confirmed the obtaining of modified graphene with different thicknesses of the graphene sheets. Samples of graphene with different thicknesses (monolayer, few layers, and multilayer) were selected and further employed for epoxy coating formulation. The obtained nanocomposites were characterized in terms of EMI shielding effectiveness, SEM, micro-CT, magnetic properties, and stress-strain resistance. The interesting aspect is that the unmodified graphene and HMDA-modified graphene displayed the best EMI shielding properties, although the ununiformed characteristic of the nanocomposites was confirmed by the micro-CT. In addition, the epoxy nanocomposites based on HMDA-modified graphene displayed better flexibility with little difference in the EMI shielding effectiveness. The improved mechanical properties and EMI shielding characteristics make HMDA-graphene a good candidate for textile coatings with MA capacity.