Improving Fracture Toughness of Tetrafunctional Epoxy with Functionalized 2D Molybdenum Disulfide Nanosheets

In this work, improved fracture toughness of tetra-functional epoxy polymer was obtained using two-dimensional (2H polytype) molybdenum disulfide (MoS2) nano-platelets as a filler. Simultaneous in-situ exfoliation and functionalization of MoS2 were achieved in the presence of cetyltrimethylammonium bromide (CTAB) via sonication. The aim was to improve the dispersion of MoS2 nanoplatelets in epoxy and enhance the interfacial interaction between nanoplatelets and epoxy matrix. Epoxy nanocomposites with CTAB functionalized MoS2 (f-MoS2) nanoplatelets, ranging in content from 0.1 wt% up to 1 wt%, were fabricated. Modified MoS2 improved the fracture properties (81%) of tetrafunctional epoxy nanocomposites. The flexural strength and compressive strength improved by 64% and 47%, respectively, with 0.25 wt% loading of f-MoS2 nanoplatelets compared to neat epoxy. The addition of f-MoS2 nanoplatelets enhanced the thermomechanical properties of epoxy. This work demonstrated the potential of organically modified MoS2 nanoplatelets for improving the fracture and thermal behavior of tetrafunctional epoxy nanocomposites.


Introduction
Tetrafunctional epoxy resins are among the most critical high-performance thermosetting polymers. These epoxy resins offer excellent strength and heat resistance for advanced structural and high-temperature applications in aerospace industries. The last decade has seen the increasing use of epoxy-based composites in the aerospace industry, especially in the Boeing 787 and Airbus A350. In these aircrafts, the fuselage, wings, and empennage, which are major structural parts, are manufactured using epoxy-based fiber reinforced composites. Due to their excellent resistance to fatigue and corrosion as well as enabling of a reduction in the number of components, more and more structural parts in aircraft are being designed using epoxy-based composites. However, the high crosslink density of epoxy polymers is low, which leads to decreased resistance to crack propagation. To address this problem, toughening agents that enhance the fracture properties of tetrafunctional epoxy without compromising modulus and thermal properties are required. There is little work reported on improving the fracture properties of tetrafunctional epoxy polymer. Most of the published work is on bifunctional epoxy polymers for low-temperature applications. Graphene and its derivatives provide excellent reinforcement for epoxy polymers and enhance their thermal properties at low concentrations [1,2]. However, because of the highly conducting nature of graphene [3], its usage as a filler is restricted when polymer composites with unaltered insulating properties are required [4], e.g., the structures which come in contact with the metal foil used for lightning strike protection. The presence of a conducting composite near metal foil may lead to corrosion. Hence, it is important to preserve the insulating characteristic of epoxy resin for these structures.
Apart from graphene, two-dimensional (2D) transition metal chalcogenides (TMD) [5][6][7][8][9][10] and boron nitride [11][12][13][14][15][16] nanosheets have attracted considerable interest due to their properties similar to graphene. Among these 2D TMD materials, molybdenum disulfide (MoS 2 ) has gained special interest due to its applications in the field of electronics [17][18][19], catalysis [20][21][22][23][24], biomedicine [25][26][27], environment [28], and polymer composites [29,30]. Few layered 2D MoS 2 nanosheets exhibit excellent mechanical properties, such as extremely high Young's modulus of 0.3 TPa [31] and breaking strength of 15 N m −1 (23 GPa) [32], which are comparable to those of graphene oxide, thus making them potential reinforcing agents for polymer nanocomposites. Another advantage of 2D MoS 2 nanosheets is their high bandgap that does not impart conductivity to the insulating polymer matrices. These properties make the 2H polytype of MoS 2 nanosheets an ideal complementary filler to graphene. MoS 2 has been explored by many researchers for improving the thermal and fire-retardant properties of thermoplastic polymers, such as polypropylene [33,34], polystyrene, and polymethylmethacrylate [29]. To overcome the issue of aggregation nanoplatelets, researchers have tried functionalizing TMDs. There are two main strategies for the functionalization of TMDs, covalent and noncovalent. The covalent modification of graphene oxide (GO) and its derivatives is relatively much easier, unlike TMDs, owing to the presence of various functional groups, such as hydroxyl, epoxy, and carboxylic acid groups on its basal plane. Hence, various methods for covalent modification exist using the coupling reaction between oxygen functionalities and functional groups on the modifier [1,[35][36][37][38]. However, for TMDs and specially MoS 2 , covalent functionalization is achieved by the intercalation method. One of the most used methods involves the Li-ion intercalation step followed by treatment with functional molecules [16,39,40]. However, it is to be noted that most of the covalent methods follow two or more steps for functionalization [40].
A few studies have reported using functionalized MoS 2 for thermosetting polymers such as epoxy [41]. Chhetri et al. used the hydrothermal method for synthesizing CTAB functionalized MoS 2 platelets leading to the formation of microparticles by self-assembly of nanosheets. The use of these functionalized MoS 2 demonstrated a 23% increase in the tensile strength [42] of bifunctional epoxy. Zhao et al. showed improvement in corrosionresistance of epoxy coating on steel by incorporating functionalized MoS 2 nanosheets [40]. However, this study did not evaluate the bulk properties of the epoxy nanocomposites. Zhao et al. focused on improving the tensile properties of low-temperature bifunctional epoxy using 3-mercaptopropyltriethoxysilane functionalized MoS 2 nanosheets [41]. The three-step method of intercalation, exfoliation followed by chemical modification using silane functional molecules was employed. The results showed that tensile properties show maximum improvement with the inclusion of 0.7 weight percent of covalently functionalized MoS 2 nanosheets. Chen et al. covalently modified MoS 2 using amine-containing melamine for improving the chemical interaction of filler with epoxy for improved tensile properties [43]. Similar to a study by Zhao et al. [41], covalently modified MoS 2 showed a maximum improvement in properties at 0.8 wt% of filler. The literature available focusing on the effect of MoS 2 nanosheets on the fracture, compression, and flexural properties of high-performance tetrafunctional epoxy polymers is still inadequate. Eksik et al. [44] reported a 60% improvement in fracture properties of bifunctional epoxy at low loading level (0.2 wt%) of pristine MoS 2 nanosheets. They concluded that the surface modification of MoS 2 is required to improve the interaction of the filler with the epoxy matrix. We have reported the effect of surface-functionalized tungsten disulfide (WS 2 ) on the fracture, compression, flexural properties, and thermal behavior of epoxy in our previous study. This study explores MoS 2 as an economically favorable alternative to WS 2 for enhanced mechanical andthermal properties of epoxy nanocomposites [45].
In this work, we report the effect of surface modified MoS 2 nanosheets on the fracture, compression, flexural, and thermal behavior of tetrafunctional epoxy polymers. The work involves the one-pot exfoliation and modification of MoS 2 nanoplatelets at room temperature using cetyltrimethylammonium bromide (CTAB) by bath sonication. The f-MoS 2 has been incorporated in the range 0.1 wt% to 1 wt% to study and compare the properties of epoxy nanocomposites with neat epoxy polymers.

Preparation of CTAB Exfoliated MoS 2
In a typical experiment, 900 mg of 2H polytype-MoS 2 powder was added to 90 mL of 1% aqueous solution of CTAB and subjected to bath sonication for 8 h. The suspension was centrifuged at 15,000 RPM (REMI Instruments, Mumbai, India) for 10 min. The supernatant containing f-MoS 2 (CTAB functionalized MoS 2 ) was separated, further washed (15,000 RPM in a centrifuge) with ethanol and water several times, and dried for a duration of 24 h at 50 • C.

Preparation Epoxy/f-MoS 2 Nanocomposites
Dried f-MoS 2 nanoplatelets were dispersed in acetone (10 mg/mL) using a bath sonicator for 2 h. Epoxy was heated to 80 • C, and the required amount of f-MoS 2 nanoplatelets suspension was added and stirred for 2 h using an overhead stirrer (IKA, Staufen, Germany) followed by mixing using a homogenizer for 10 min. Post mixing, the modified epoxy resin was degassed in a vacuum oven for 12 h at 90 • C to remove the residual solvent molecules. A stoichiometric amount of hardener was added to the mixture at 120 • C assisted with stirring at high speed for 20 min to ensure complete mixing of the epoxy and the hardener. The mixture was again degassed for 2 h at 90 • C to remove the bubbles introduced during the mixing process. Finally, the mixture was cast in a mold (preheated to avoid gas entrapment) and cured at 150 • C for 2 h followed by 180 • C for 2 h followed by 200 • C for 2 h. Nanocomposites containing 0.1, 0.25, 0.5, and 1 wt% of f-MoS 2 nanoplatelets were fabricated, and for comparison, neat epoxy composites were also fabricated using similar processing conditions.

Characterization
Surface morphology of bulk exfoliated MoS 2 and fractured epoxy nanocomposites were analyzed by scanning electron microscopy (FEI Sirion XL30, Eindhoven, The Netherlands) Bulk MoS 2 and f-MoS 2 nanoplatelets suspensions were prepared in an aqueous medium. Suspensions were diluted and drop cast on a freshly cleaned silicon substrate. Each sample was sputtered to build a 10 nm thick Au layer to prevent charge accumulation during analysis.
The structure and morphology of f-MoS 2 nanoplatelets were analyzed by transmission electron microscopy (JEOL 2000 FX-II, Akishima, Tokyo, Japan). Nanoplatelets were sonicated in an aqueous medium for 30 min, drop-cast on a Cu grid (carbon-coated), dried and analyzed.
Atomic force microscopy was performed in tapping mode using a NanoWizard 3 AFM (JPK Instruments, Berlin, Germany) to determine the thickness of f-MoS 2 nanoplatelets. Samples were prepared by sonicating f-MoS 2 nanoplatelets in deionized water for 30 min, followed by drop-casting on a freshly cleaned silica wafer. Samples were dried and desiccated before conducting AFM analysis.
The photoluminescence properties of the bulk and exfoliated f-MoS 2 nanoplatelets were evaluated by confocal microscopy (Zeiss LSM 710, Oberkochen, Germany). The powdered samples of the bulk and exfoliated f-MoS 2 nanoplatelets were mounted on a glass slide and imaged, covering the wavelength from 400 to 700 nm.
FTIR analysis of pure CTAB, bulk MoS 2 and f-MoS 2 nanoplatelets were performed on Thermo-Nicolet 6700 Fourier transform infrared spectrophotometer (Thermo Fisher Scientific, Waltham, MA, USA) in the 400-4000 cm −1 spectral range. Thermogravimetric analysis was performed on NETZSCH-STA-409 (NETZSCH-Gerätebau GmbH, Selb, Germany) in the range of 30 • C to 800 • C with a heating rate of 10 • C per minute. X-ray powder diffraction was performed for 2θ angles from 8 • to 60 • using X'Pert PRO (PANalytical, Almelo, The Netherlands).
Dynamic mechanical (DMA) study of nanocomposites was performed on Gabo Eplexor 500N (NETZSCH-Gerätebau GmbH, Selb, Germany) using samples of three-point bend geometry with measurements 5 × 2 × 45 mm 3 . The temperature was gradually changed from 30 to 330 • C at 3 • C min −1 with a frequency of 1 Hz.
Compression tests were performed using a Zwick/Rowell Z100 (ZwickRoell, Ulm, Germany) per ASTM D695. Five parallels of each sample with a cylindrical geometry (diameter 6.9 mm, length 10.4 mm) were tested, and the average value is reported here. The cross-sectional area of samples was polished using P4000 grade emery paper to ensure no friction exists between the sample surface and the compression clamps.
The fracture toughness of epoxy nanocomposites was calculated by conducting single edge notch bend tests per ASTM D5045, using a Zwick/Rowell Z100 machine. Samples with dimensions 6 × 12 × 48 mm 3 were cast molded. A sharp natural crack was induced in the samples by applying sawing motion using a razor blade dipped in liquid N 2 over the machined notch. The fracture toughness K IC was calculated using the below-mentioned formula: where P max represents the max load on the load-displacement graph, W is the width of the flexural sample, B is the depth of the sample, and a is the length of pre-crack. The geometry dependent function, f (a/W), is calculated using the following equation: Tests were conducted on six replicas per composition, and the average of the obtained values is reported here. The samples were loaded until a complete fracture occurred.
The flexural strength of neat epoxy and modified nanocomposites were determined using a Zwick/Rowell Z100 according to ASTM D790. Five replicas per composition were tested at a strain rate of 2 mm min −1 , and the average of the values is reported here. Samples with span length 48 mm, thickness 3 mm, and width 12 mm were employed.

Noncovalent Functionalization of MoS 2 and Characterization of f-MoS 2 Nanoplatelets
MoS 2 flakes were exfoliated by sonication in an aqueous solution containing CTAB. The long hydrocarbon chains of the surfactant help in exfoliating the stacked layers of MoS 2 when subjected to bath sonication. The presence of the surfactant molecules also provides the appropriate surface tension to overcome the van der Waals forces between the exfoliated layers. A schematic of the process for the simultaneous noncovalent modification of MoS 2 with CTAB and exfoliation of f-MoS 2 nanoplatelets followed by the fabrication of f-MoS 2 modified epoxy nanocomposites is shown in Figure 1. The CTAB modified MoS 2 nanoplatelets disperse quickly in a weakly polar solvent such as acetone due to the polar nature of the CTAB molecules.

Noncovalent Functionalization of MoS2 and Characterization of f-MoS2Nanoplatelets
MoS2 flakes were exfoliated by sonication in an aqueous solution containing CTAB. The long hydrocarbon chains of the surfactant help in exfoliating the stacked layers of MoS2 when subjected to bath sonication. The presence of the surfactant molecules also provides the appropriate surface tension to overcome the van der Waals forces between the exfoliated layers. A schematic of the process for the simultaneous noncovalent modification of MoS2 with CTAB and exfoliation of f-MoS2 nanoplatelets followed by the fabrication of f-MoS2 modified epoxy nanocomposites is shown in Figure 1. The CTAB modified MoS2 nanoplatelets disperse quickly in a weakly polar solvent such as acetone due to the polar nature of the CTAB molecules.   [32]. The thickness of nanoplatelets obtained is almost five times the thickness of the monolayer. Therefore, exfoliation using CTAB, and sonication offers a simple approach to produce thinner sheets of MoS2.   [32]. The thickness of nanoplatelets obtained is almost five times the thickness of the monolayer. Therefore, exfoliation using CTAB, and sonication offers a simple approach to produce thinner sheets of MoS 2 .
Confocal microscopy images of the bulk and exfoliated MoS 2 flakes ( Figure 3) demonstrated that exfoliated MoS 2 exhibits excitation-dependent emission photoluminescence, which is not observed in the bulk MoS 2 . The photoluminescence properties of the exfoliated f-MoS 2 nanoplatelets are mainly due to the intrinsic electronic properties of the monolayer material and Eda et al. [46] have reported similar results. The absence of photoluminescence in the bulk material is mainly due to the indirect bandgap of the electronic transition and its higher refractive index that causes a decrease in the local electric field. The transition of bulk MoS 2 to exfoliated MoS 2 nanoplatelets shifts the photoluminescence properties due to a change in the direct gap electronic transition of MoS 2 . It also increases the local electric field due to a decrease in the refractive index [47].The excitation-dependent emission photoluminescence property from the blue region to the far-red region can be attributed to the polydispersity of the 2D layers and quantum size effect, which is not observed in the bulk material [48,49]. Polymers 2021, 13, 4440 6 of 16 Confocal microscopy images of the bulk and exfoliated MoS2 flakes ( Figure 3) demonstrated that exfoliated MoS2 exhibits excitation-dependent emission photoluminescence, which is not observed in the bulk MoS2. The photoluminescence properties of the exfoliated f-MoS2 nanoplatelets are mainly due to the intrinsic electronic properties of the monolayer material and Eda et al. [46] have reported similar results. The absence of photoluminescence in the bulk material is mainly due to the indirect bandgap of the electronic transition and its higher refractive index that causes a decrease in the local electric field. The transition of bulk MoS2 to exfoliated MoS2 nanoplatelets shifts the photoluminescence properties due to a change in the direct gap electronic transition of MoS2. It also increases the local electric field due to a decrease in the refractive index [47].The excitation-dependent emission photoluminescence property from the blue region to the far-red region can be attributed to the polydispersity of the 2D layers and quantum size effect, which is not observed in the bulk material [48,49].  FTIR spectroscopy was used to confirm the successful noncovalent organic modification of MoS2 nanoplatelets layers with CTAB ( Figure 4a). In addition to the peaks observed for bulk MoS2, the absorption peaks at 2847 cm −1 and 2930 cm −1 in the spectrum of f-MoS2 can be ascribed to CH3 and CH2 groups of CTAB molecules, respectively. The strong peaks at 1642 cm −1 and 1445 cm −1 can be attributed to the presence of CH3-N + symmetric vibration of CTAB. FTIR spectroscopy was used to confirm the successful noncovalent organic modification of MoS 2 nanoplatelets layers with CTAB ( Figure 4a). In addition to the peaks observed for bulk MoS 2 , the absorption peaks at 2847 cm −1 and 2930 cm −1 in the spectrum of f-MoS 2 can be ascribed to CH 3 and CH 2 groups of CTAB molecules, respectively. The strong peaks at 1642 cm −1 and 1445 cm −1 can be attributed to the presence of CH 3 -N + symmetric vibration of CTAB. FTIR spectroscopy was used to confirm the successful noncovalent organic modification of MoS2 nanoplatelets layers with CTAB ( Figure 4a). In addition to the peaks observed for bulk MoS2, the absorption peaks at 2847 cm −1 and 2930 cm −1 in the spectrum of f-MoS2 can be ascribed to CH3 and CH2 groups of CTAB molecules, respectively. The strong peaks at 1642 cm −1 and 1445 cm −1 can be attributed to the presence of CH3-N + symmetric vibration of CTAB. Thermogravimetric analysis was performed to further confirm the noncovalent functionalization of CTAB molecules on MoS2 nanoplatelets. The thermal decomposition curves are shown in Figure 4b. Bulk MoS2 lost 9% of the total weight, similar to the weight percent of SO2(10 wt%) [50]. Hence the observation suggests that in air, bulk MoS2 transforms to molybdenum oxide. In the case of f-MoS2, the observed weight loss was much higher in the temperature range of 100-700 °C when compared to bulk MoS2. For example, the temperature for 5 percent weight loss (T-5%) was 114 °C for f-MoS2, whereas T-5% was much higher at 497 °C for bulk MoS2 due to the absence of organic moieties. The residual mass for bulk MoS2 was 95 wt%, whereas f-MoS2 showed 27 wt% residual mass at 700 °C. The increased weight loss can be ascribed to the increased diffusion of heat in exfoliated layers and decomposition of CTAB moieties, thus confirming the successful functionalization of MoS2 nanoplatelets. Thermogravimetric analysis was performed to further confirm the noncovalent functionalization of CTAB molecules on MoS 2 nanoplatelets. The thermal decomposition curves are shown in Figure 4b. Bulk MoS 2 lost 9% of the total weight, similar to the weight percent of SO 2 (10 wt%) [50]. Hence the observation suggests that in air, bulk MoS 2 transforms to molybdenum oxide. In the case of f-MoS 2 , the observed weight loss was much higher in the temperature range of 100-700 • C when compared to bulk MoS 2 . For example, the temperature for 5 percent weight loss (T −5% ) was 114 • C for f-MoS 2 , whereas T −5% was much higher at 497 • C for bulk MoS 2 due to the absence of organic moieties. The residual mass for bulk MoS 2 was 95 wt%, whereas f-MoS 2 showed 27 wt% residual mass at 700 • C. The increased weight loss can be ascribed to the increased diffusion of heat in exfoliated layers and decomposition of CTAB moieties, thus confirming the successful functionalization of MoS 2 nanoplatelets.
The effect of exfoliation and surface functionalization on the crystalline structure of MoS 2 was studied by X-ray diffraction (XRD) analysis. Figure  the bulk MoS2(card no. 24-0513). In the case of f-MoS2, the diffraction peaks for the planes (104), (106), and (108) disappeared. The intensity of peak (002) of exfoliated MoS2 reduced dramatically compared to the bulk MoS2. This might be attributed to the reduced crystallite size, which reduces the probability of several (002) planes to satisfy Bragg's condition. Additionally, peaks representing (004), (100), (101), (103), (006), and (105) also showed a drastic reduction in intensity compared to bulk MoS2. The reduced intensity of the peak (002) indicates the successful exfoliation of MoS2.

Thermogravimetric Analysis
The inorganic layered nanofillers are expected to affect the thermal performance of nanocomposites to a significant extent due to their excellent thermal resistance. The thermal performance of nanocomposites was measured by thermogravimetric analysis. Figure 6 shows the curves from the thermogravimetric analysis of neat epoxy and Epoxy/f-MoS2 nanocomposites, and the crucial data are shown in Table 1. For all the fabricated nanocomposites, thermal decomposition happens in one step. The most significant weight loss (~60%) occurred in the temperature range of 300-450 °C due to the gradual degradation of the epoxy crosslinked network. The addition of f-MoS2 nanoplatelets increased the T-5% of the epoxy nanocomposites by 20-30 °C. For example, the nanocomposite with 0.25 wt.% of f-MoS2 shows T-5% at 332°C, which is greater than T-5% of neat epoxy at 302 °C. This improvement in thermal properties can be ascribed to the barrier effect of well dispersed and exfoliated f-MoS2 nanoplatelets, which restrict the mobility of the volatile products across the matrix. The presence of CTAB molecules enhances the affinity of the MoS2 nanoplatelets towards the epoxy resulting in better dispersion of the f-MoS2 nanoplatelets in the epoxy matrix. The large surface area of MoS2 nanoplatelets, along with CTAB assisted dispersion, paves the way for the improved interlocking of filler with epoxy matrix.

Thermogravimetric Analysis
The inorganic layered nanofillers are expected to affect the thermal performance of nanocomposites to a significant extent due to their excellent thermal resistance. The thermal performance of nanocomposites was measured by thermogravimetric analysis. Figure 6 shows the curves from the thermogravimetric analysis of neat epoxy and Epoxy/f-MoS 2 nanocomposites, and the crucial data are shown in Table 1. For all the fabricated nanocomposites, thermal decomposition happens in one step. The most significant weight loss (~60%) occurred in the temperature range of 300-450 • C due to the gradual degradation of the epoxy crosslinked network. The addition of f-MoS 2 nanoplatelets increased the T −5% of the epoxy nanocomposites by 20-30 • C. For example, the nanocomposite with 0.25 wt.% of f-MoS 2 shows T −5% at 332 • C, which is greater than T −5% of neat epoxy at 302 • C. This improvement in thermal properties can be ascribed to the barrier effect of well dispersed and exfoliated f-MoS 2 nanoplatelets, which restrict the mobility of the volatile products across the matrix. The presence of CTAB molecules enhances the affinity of the MoS 2 nanoplatelets towards the epoxy resulting in better dispersion of the f-MoS 2 nanoplatelets in the epoxy matrix. The large surface area of MoS 2 nanoplatelets, along with CTAB assisted dispersion, paves the way for the improved interlocking of filler with epoxy matrix.    Hence, the f-MoS 2 nanoplatelets delay the degradation process by restricting the diffusion of degradation products and heat due to enhanced interface. The char yield is an essential factor for assessing the thermal stability of the polymer nanocomposite as the char residue resists heat flow during combustion and helps improve thermal stability. Hence, the higher the char yield, the better the thermal stability of nanocomposites [33,51]. The char yields of all the modified nanocomposites also shows significant improvement. Hence, it can be concluded that f-MoS 2 nanoplatelets enhance the thermal stability of epoxy nanocomposites. For example, the nanocomposite with 0.5 wt% filler yielded 29% char, which is much larger than the char yield of 12% for the neat epoxy. It can be noted that epoxy nanocomposites with 1.0 wt% show the least improvement in thermal stability that can be ascribed to the poor dispersion of f-MoS 2 nanosheets at high weight % loading. The presence of agglomerates also hinders the nanofiller from forming a stronger interface and imparting improved thermal properties.

Dynamic Mechanical Analysis
The dynamic mechanical study was employed to study the effect of f-MoS 2 nanoplatelets on the thermomechanical properties of nanocomposites. The storage modulus and tan δ curves of the nanocomposites and the neat epoxy are shown in Figure 7a,b. Since tetrafunctional epoxy polymers are the choice for high-temperature applications due to their high (>200 • C) glass transition temperature (T g ), the epoxy nanocomposites must retain enhanced mechanical properties at elevated temperatures. Figure 7a shows the storage modulus of epoxy nanocomposites at various temperatures, including temperatures below and above T g of the nanocomposites. The storage modulus is a measure of the stiffness of the nanocomposites. The storage modulus of the nanocomposite Epoxy/f-MoS 2 -0.25 wt% showed a maximum increase of 28% at 200 • C and 39% at 250 • C in comparison to neat epoxy. T g of the polymer nanocomposites is taken as the temperature at the maximum of the tan δ curve. Figure 7b shows the change in tan δ with temperature for the neat epoxy and epoxy modified with different loading of f-MoS 2 nanoplatelets. The epoxy nanocomposites modified with low levels (0.1 and 0.25 wt%) of f-MoS 2 nanoplatelets showed a higher T g than the neat epoxy (281.1 • C) with a higher value of storage modulus. The increase in T g suggests improvement in the thermo-mechanical properties of the final nanocomposites. The increase in storage modulus values and T g for epoxy with the loading of f-MoS 2 nanoplatelets should be attributed to the robust nature and high intrinsic stiffness of the MoS 2 nanoplatelets. The segmental motional is restricted by the large aspect ratio of f-MoS 2 platelets. The presence of CTAB molecules over the surface of the MoS 2 nanoplatelets provides enhanced compatibility with the epoxy matrix due to its long hydrocarbon chains. Better exfoliation and distribution of the f-MoS 2 in the epoxy matrix lead to enhanced effective volume of the filler, which is also one of the factors for the excellent reinforcing effect of f-MoS 2 nanoplatelets. the robust nature and high intrinsic stiffness of the MoS2 nanoplatelets. The segmental motional is restricted by the large aspect ratio of f-MoS2 platelets. The presence of CTAB molecules over the surface of the MoS2 nanoplatelets provides enhanced compatibility with the epoxy matrix due to its long hydrocarbon chains. Better exfoliation and distribution of the f-MoS2 in the epoxy matrix lead to enhanced effective volume of the filler, which is also one of the factors for the excellent reinforcing effect of f-MoS2 nanoplatelets.  Figure 8a shows the typical true stress vs. strain curves for compression tests for the neat epoxy and epoxy modified with f-MoS2 nanoplatelets with loading up to 1 wt%. All the samples showed similar deformation behavior under the applied load with an initial elastic region up to the diffused yield zone followed by the strain hardening region until the sample fractures. The strain hardening region is an indication of the energy absorbed by the sample before fracture. Unlike in instances of rubber toughened epoxy, a strain-softening region was not observed for any of the epoxy samples. Strain softening causes enhancement in the local cross-sectional area, which stabilizes further local strain [52]. The absence of strain-softening region is attributed to the high crosslink density of tetrafunctional epoxy & intrinsic strength of f-MoS2 nanoplatelets, which leads to stronger composites. It can be noted in Figure 8a that the strain hardening region increased for all the epoxy samples modified with f-MoS2 nanoplatelets. However, the extent of variation was different for different loading of filler. Nanocomposites with 0.25 wt% of f-MoS2 nanoplatelets showed the most significant increase in the strain hardening region and are, therefore, most effective in absorbing the stress during the compressive loading. Figure 8b shows the comparative plot of compressive strengths of neat epoxy and epoxy nanocomposites. The compressive strength increased as the content of f-MoS2 increased from 0.1 wt% to 0.25 wt%. The addition of 0.25 wt% of f-MoS2 nanoplatelets showed the maximum improvement in compressive strength compared to  Figure 8a shows the typical true stress vs. strain curves for compression tests for the neat epoxy and epoxy modified with f-MoS 2 nanoplatelets with loading up to 1 wt%. All the samples showed similar deformation behavior under the applied load with an initial elastic region up to the diffused yield zone followed by the strain hardening region until the sample fractures. The strain hardening region is an indication of the energy absorbed by the sample before fracture. Unlike in instances of rubber toughened epoxy, a strain-softening region was not observed for any of the epoxy samples. Strain softening causes enhancement in the local cross-sectional area, which stabilizes further local strain [52]. The absence of strain-softening region is attributed to the high crosslink density of tetrafunctional epoxy & intrinsic strength of f-MoS 2 nanoplatelets, which leads to stronger composites. It can be noted in Figure 8a that the strain hardening region increased for all the epoxy samples modified with f-MoS 2 nanoplatelets. However, the extent of variation was different for different loading of filler. Nanocomposites with 0.25 wt% of f-MoS 2 nanoplatelets showed the most significant increase in the strain hardening region and are, therefore, most effective in absorbing the stress during the compressive loading. Figure 8b shows the comparative plot of compressive strengths of neat epoxy and epoxy nanocomposites. The compressive strength increased as the content of f-MoS 2 increased from 0.1 wt% to 0.25 wt%. The addition of 0.25 wt% of f-MoS 2 nanoplatelets showed the maximum improvement in compressive strength compared to epoxy nanocomposites loaded with higher wt% of f-MoS 2 nanoplatelets (0.5 to 1.0 wt%). For example, the incorporation of 0.25 wt% of f-MoS 2 nanoplatelets in epoxy leads to a 46% improvement in compressive strength of the nanocomposite in comparison to the neat one. The enhancement in the compressive properties could be ascribed to the high intrinsic strength and good dispersion of f-MoS 2 nanoplatelets caused by organic CTAB moieties, which promote enhanced interaction with the epoxy network and reduce agglomeration. The effective concentration of f-MoS 2 improves due to uniform dispersion of the filler owing to organic modification of its surface. Uniform dispersion gives rise to better load transfer from epoxy matrix to f-MoS 2 nanoplatelets during the compressive loading. Nanocomposites with 1 wt% of f-MoS 2 nanoplatelets show a reduced level of improvement with 26% enhancement in the compressive properties. This reduction could be ascribed to the reduced degree of distribution of f-MoS 2 nanoplatelets at higher loading levels.

Compressive Properties
of the filler owing to organic modification of its surface. Uniform dispersion gives rise to better load transfer from epoxy matrix to f-MoS2 nanoplatelets during the compressive loading. Nanocomposites with 1 wt% of f-MoS2 nanoplatelets show a reduced level of improvement with 26% enhancement in the compressive properties. This reduction could be ascribed to the reduced degree of distribution of f-MoS2 nanoplatelets at higher loading levels.   Figure 8c. Figure 8d shows the base value of fracture toughness of neat epoxy to be 0.84 MPa m 1/2 . It is evident that the presence of f-MoS 2 nanoplatelets significantly improves the fracture properties of the nanocomposites. The maximum improvement in the fracture properties was observed with an f-MoS 2 nanoplatelets loading of 0.25 wt% as it shows K IC value of 1.52 MPa m 1/2 . This value corresponds to an improvement of 81% when compared to neat epoxy. The extremely high Young's modulus of MoS 2 nanoplatelets [31], which is higher than that of graphene oxide, is one of the primary reasons for the improved fracture properties of the f-MoS 2 modified epoxy nanocomposites. MoS 2 nanosheets are intrinsically stiff and provide excellent barrier properties for crack propagation. The toughening effect is further improved by the enhanced compatibility of organically modified MoS 2 nanoplatelets with the epoxy matrix. The long chains of CTAB cause hindrance between the layers due to its bulky nature, promoting exfoliation and avoiding the agglomeration of layers. CTAB modification also makes MoS 2 layers more compatible with the epoxy matrix. This enhanced affinity of the MoS 2 nanoplatelets leads to an even stronger interface which helps in better stress transfer from the epoxy matrix to f-MoS 2 nanoplatelets during mechanical loading. The large surface area of MoS 2 nanoplatelets enables interlocking of the MoS 2 nanoplatelets with epoxy over a much larger interfacial area. The modification of the nanoplatelets with the organic molecules of CTAB helps realize the full potential of the MoS 2 nanoplatelets as a toughening agent for epoxy.
As the content of f-MoS 2 nanoplatelets reaches 1 wt%, the degree of improvement dips to 56%. Thus, f-MoS 2 nanoplatelets provide maximum enhancement in fracture properties at lower loading levels of 0.25 wt%. The decrease in toughening effect with loading beyond 0.25 wt% could be ascribed to the increased agglomeration of nanoplatelets in the epoxy at a higher concentration level. Agglomeration leads to a reduction in the interfacial area, thus limiting the interaction of the f-MoS 2 nanoplatelets with the epoxy matrix. The presence of agglomerates also increases defects, which reduces the intrinsic cured properties of the epoxy composite. Further analysis of fractured samples obtained from the fracture toughness test was done by scanning electron microscopy.

Study of Fractured Surfaces
The homogeneous dispersion of the nano-reinforcements in the polymer composites provides a maximum enhancement in the mechanical properties of polymer composites.
The dispersion state of f-MoS 2 nanoplatelets in the epoxy matrix was analyzed using SEM. Figure 9 shows the SEM micrographs of the cross-sectional areas of the fractured surfaces of neat epoxy and Epoxy/f-MoS 2 nanocomposites of different compositions. The neat epoxy had a smoother and featureless surface (Figure 9a), while the modified epoxy nanocomposite with f-MoS 2 layers showed an irregular surface (Figure 9b-e). It can be seen in Figure 9b-d that f-MoS 2 nanoplatelets cause less agglomeration in the epoxy nanocomposites owing to the lower filler content. The improved dispersion of f-MoS 2 nanoplatelets leads to a stronger interface between filler and the matrix, thus enhancing the nanocomposites' mechanical properties. The enhanced interfacial characteristics of epoxy modified with 0.25 wt% of f-MoS 2 may also be attributed to the thin structure of exfoliated nanoplatelets resulting in wrinkled morphology, thus enabling better interlocking between the reinforcing agent and the epoxy polymer chains. The micrographs show that the filler has excellent adhesion to the matrix as no pullout or loose nanoplatelets were observed. The enhanced compatibility of the f-MoS 2 nanoplatelets could be ascribed to the presence of organic CTAB molecules on the surface of the MoS 2 nanoplatelets. However, as the f-MoS 2 content reached 1 wt%, it is observed that the distribution of the filler in the matrix becomes non-uniform (Figure 9e). The agglomeration and non-homogeneous distribution of the nanoplatelets in the epoxy matrix reduce the interfacial area and the degree of interaction between f-MoS 2 nanoplatelets and epoxy, reducing the efficiency of the filler as a reinforcing agent. The agglomerated MoS 2 also act as a defect hindering the crosslinking of epoxy and hardener. The agglomeration does not significantly improve the mechanical properties of epoxy nanocomposites with 1 wt% of the filler.

Flexural Properties
The flexural properties of neat epoxy and Epoxy/f-MoS2 nanocomposites are compared in Figure 10. F-MoS2 nanoplatelets improved the flexural properties of epoxy nanocomposites for the entire range of loading percentage, although the degree of improvement varied with the loading level. Like the trend observed in the compressive and the fracture properties, nanocomposites modified with 0.25 wt% of f-MoS2 nanoplatelets give rise to a maximum increase of 64% in flexural strength compared to the neat epoxy. The flexural strength of the Epoxy/f-MoS2-0.25 wt% corresponds to 143 MPa, which is significantly high compared to the flexural strength of 87 MPa observed for the the nanocomposites. The improvement in flexural properties is minimal beyond 0.25 wt% of platelets. The least improvement is observed with 1 wt% of f-MoS2 nanoplatelets, which can be attributed to the poor dispersion of the nanoplatelets in the matrix. The results confirm that f-MoS2 nanoplatelets show better improvement in the flexural properties at low loading levels because of the better dispersion and stronger interface facilitated by the presence of CTAB molecules.

Conclusions
In conclusion, 2D MoS2 nanoplatelets were successfully modified using a noncovalent method for the enhanced fracture and thermal properties of tetrafunctional epoxy nanocomposites. Organic modification supports better compatibility, dispersion, and interaction of the MoS2 nanoplatelets with the epoxy matrix. f-MoS2 nanoplatelets were prepared by the one-pot sonication method. The inclusion of f-MoS2 nanoplatelets in relatively low amounts induced an excellent improvement in fracture, flexural, compression, and thermal properties. The remarkable improvement in the mechanical properties was attributed to better interfacial adhesion between f-MoS2 nanoplatelets and the epoxy matrix and a better distribution of the layers due to the presence of the bulky organic groups on the nanoplatelets surface. The loading of f-MoS2 nanoplatelets beyond 0.25 wt% leads to a relatively non-homogeneous distribution of the nanoplatelets in the epoxy matrix, causing a reduction in the extent of interaction and the interfacial area between the filler and the matrix. This work demonstrates the potential of organically modified MoS2 nanosheets as a toughening agent for tetrafunctional epoxy nanocomposites.

Conclusions
In conclusion, 2D MoS 2 nanoplatelets were successfully modified using a noncovalent method for the enhanced fracture and thermal properties of tetrafunctional epoxy nanocomposites. Organic modification supports better compatibility, dispersion, and interaction of the MoS 2 nanoplatelets with the epoxy matrix. f-MoS 2 nanoplatelets were prepared by the one-pot sonication method. The inclusion of f-MoS 2 nanoplatelets in relatively low amounts induced an excellent improvement in fracture, flexural, compression, and thermal properties. The remarkable improvement in the mechanical properties was attributed to better interfacial adhesion between f-MoS 2 nanoplatelets and the epoxy matrix and a better distribution of the layers due to the presence of the bulky organic groups on the nanoplatelets surface. The loading of f-MoS 2 nanoplatelets beyond 0.25 wt% leads to a relatively non-homogeneous distribution of the nanoplatelets in the epoxy matrix, causing a reduction in the extent of interaction and the interfacial area between the filler and the matrix. This work demonstrates the potential of organically modified MoS 2 nanosheets as a toughening agent for tetrafunctional epoxy nanocomposites.
Author Contributions: M.S. and L.N. conceived, designed, performed experiments, analyzed the results, and wrote the manuscript; A.M.R. supervised and designed the research planning, experiments, and results, and provided a technical proofread of the manuscript; A.S., R.C.C., M.A. and N.L. analyzed the experiments, technical proof of results, and review of the manuscript. All authors have read and agreed to the published version of the manuscript.
Funding: This work was supported by a publications grant of the TUIASI, project number GI/P5/2021.

Data Availability Statement:
The datasets generated during and/or analyzed during the current study are available from the corresponding author on reasonable request.