Effects of silanization and hybrid nanofillers of multiwalled carbon nanotubes and graphene oxide on the mechanical properties of epoxy/dicyandiamide/carbon fiber composites

Effects of silanization and hybrid nanofillers of multiwalled carbon nanotubes and graphene oxide on the mechanical properties of epoxy/dicyandiamide/carbon fiber composites | Research Square window.SnipcartSettings = { analytics: { enabled: false } }; (function() { var accessVector = localStorage.getItem('access_vector') || ''; window.dataLayer = window.dataLayer || []; if (accessVector) { window.dataLayer.push({ user: { profile: { profileInfo: { snid: accessVector } } } }); } })(); (function(w,d,s,l,i){w[l]=w[l]||[];w[l].push({'gtm.start':new Date().getTime(),event:'gtm.js'});var f=d.getElementsByTagName(s)[0],j=d.createElement(s),dl=l!='dataLayer'?'&l='+l:'';j.async=true;j.src='https://www.googletagmanager.com/gtm.js?id='+i+dl;f.parentNode.insertBefore(j,f);})(window,document,'script','dataLayer','GTM-K279D39R'); Browse Preprints In Review Journals COVID-19 Preprints AJE Video Bytes Research Tools Research Promotion AJE Professional Editing AJE Rubriq About Preprint Platform In Review Editorial Policies Our Team Advisory Board Help Center Sign In Submit a Preprint Cite Share Download PDF Research Article Effects of silanization and hybrid nanofillers of multiwalled carbon nanotubes and graphene oxide on the mechanical properties of epoxy/dicyandiamide/carbon fiber composites Nahid Jamali, Mohammad Hosain Beheshty This is a preprint; it has not been peer reviewed by a journal. https://doi.org/ 10.21203/rs.3.rs-7164361/v1 This work is licensed under a CC BY 4.0 License Status: Posted Version 1 posted You are reading this latest preprint version Abstract This study was conducted to evaluate the effects of the silanization of multiwall carbon nanotube (CNT) and graphene oxide (GO) nanoplates and their hybrid on the mechanical properties of epoxy/dicyandiamide (DICY)/carbon fiber (CF) composites. The silanized CNT (S-CNT) and GO (S-GO) were synthesized by refluxing (3-glycidyloxypropyl) trimethoxysilane in 97% ethanol. The silane grafting on CNT and GO was characterized by Fourier transform infrared spectroscopy, energy-dispersive X-ray spectroscopy, and thermogravimetric analysis. The nanocomposites' transverse tensile, flexural, and interlaminar shear strength (ILSS) were characterized. The transverse tensile and flexural strengths of the S-CNT0.5/epoxy/DICY/CF composite were 18% and 27% greater than those of the neat composite. Moreover, enhancements of approximately 34% and 39% were observed in the flexural moduli of the 0.5 wt.% S-CNT and S-GO filled samples, respectively. The tensile and flexural moduli of CF nanocomposite containing the hybrid of S-CNT-GO0.5 was enhanced by 31% and 45%, respectively. The evaluation of the tensile fracture surface of the samples revealed that the incorporation of GO and S-GO improved the CF‒epoxy interfacial bonding. The transverse interlaminar shear strength of the 0.5wt% S-CNT, S-GO, and S-CNT-GO hybrid-filled composites were enhanced by 18%, 10%, and 25%, respectively. Carbon nanotubes graphene oxide carbon fiber epoxy silane Figures Figure 1 Figure 2 Figure 3 Figure 4 Figure 5 Figure 6 Figure 7 Figure 8 Figure 9 Figure 10 Figure 11 Introduction Owing to their attractive properties, epoxy resins have been widely used as a matrix for carbon fiber-reinforced composites. The anisotropy between carbon fibers (CFs) and the polymer matrix results in poor interfacial properties and low stiffness of the composite [ 1 , 2 ]. Generally, in composite materials with epoxy matrix, the fracture is caused by, transverse and longitudinal rupture of the matrix or by the fiber-matrix interface debonding. These observations lead us to pay more attention to the event of deformation of epoxy composites by knowing the process of rupture and damage of both the matrix and the composites and the archiving method for improving the fiber and matrix reactions [ 3 , 4 ]. The use of carbon-derived nanofillers such as carbon nanotubes (CNTs) and graphene oxide (GO) with an epoxy matrix is one of the most investigated approaches to improve current polymer matrix properties [ 3 – 5 ]. The incorporation of nanofillers can affect the interaction of the polymer matrix with fiber reinforcements and the resin curing process [ 6 ]. Bahari et al. [ 7 ] investigated the synergetic effect of hybrid fillers, including surface-modified montmorillonite (MMT) nanoclusters and graphene nanoplatelets (GNPs), on the dispersion quality and mechanical characteristics of epoxy-based nanocomposites. The results revealed that the maximum tensile and flexural strengths were obtained for the samples containing 0.15 wt.% GNPs and 1 wt.% MMT, which were 19% and 17.4% greater than those of the neat epoxy, respectively. Jen et al. [ 8 ] studied the synergistic effect of hybrid nanofillers of multiwalled carbon nanotube (MWCNT)/graphene nanoplatelets (GNPs) on the mechanical and fatigue properties of epoxy composites. The experimental results show that the composites with a MWCNT:GNP ratio of 1:9 have greater monotonic and fatigue properties than those with other filler ratios. Yang et al. [ 9 ] investigated the effects of multigraphene platelets (MGPs) and multiwalled carbon nanotubes (MWCNTs) on improving the mechanical properties and thermal conductivity of epoxy composites. They reported 35.4% and 146.9% enhancements in tensile strength and thermal conductivity, respectively, for GD400-MWCNT/MGP/epoxy composites compared with nonderivatized epoxy. Li et al. [ 10 ] studied the effect of hybrid fillers composed of carbon nanotubes (CNTs) grown on graphene nanoplatelets (GNPs) in an epoxy matrix. For the 0.5 wt.% hybrid filler loading, the tensile modulus increased by 40%, and the tensile strength was increased by 36% concerning that of the neat epoxy. However, van der Waals forces between nanofillers can lead to agglomeration and result in inhomogeneous dispersion in a polymer matrix. The dispersibility and interfacial strength of fillers can be improved by functionalization of nanofillers with organosilane coupling agents. On the other hand, the functional groups of the silane coupling agents could be chemically attached to the polymer matrix and improve the adhesion of fillers to the polymer matrix. The silane coupling agent reacts with the nanofiller on one hand and reacts with the epoxy matrix on the end hand [ 11 – 14 ]. Recent curing systems based on dicyandiamide (DICY), a solid powder with limited solubility in epoxides at room temperature, can dedicate epoxy prepolymers with excellent processing ability, room temperature stability, and cured products with phenomenal mechanical and electrical properties. For these reasons, the epoxy/DICY-based resin widely used as a matrix for carbon fiber prepregs would allow long-term storage at room temperature, reduce storage costs, and simplify logistics. The adhesion between the matrix and fibers and the mechanical properties of the final composite products are strongly dependent on the curing reactions of the epoxy/DICY systems [ 15 – 18 ]. This work aims to investigate the curing behavior of the epoxy/DICY system and the mechanical behavior of its carbon fiber-reinforced composites by silanizing GO and CNT individually and the GO/CNT hybrid by combining one-dimensional multiwalled carbon nanotubes (1D CNTs) and 2D GO. The incorporation of hybrid nanofillers has the capacity to acquire the synergistic effects and properties of each nanofiller. Therefore, the appearance of different types of nanoparticles contains CNT and GO with tube and plate structures respectively, could improve the reaction between nanofiller, epoxy matrix and carbon fibers and enhance the mechanical properties of composites. To the best of our knowledge, no comprehensive study has focused on the effects of both the silanization and hybridization of CNTs and GO on the transverse tensile, flexural, and interlaminar shear properties of CF/DICY/epoxy composites. This was the motivation for choosing this method. Materials Epoxy resin (Epikote-828, diglycidyl ether of bisphenol-A) with epoxide equivalent weights of 185–190 and viscosity of 12 Pa.s to 14 Pa.s at room temperature was obtained from Momentive Co. (Columbus, OH, USA). The latent curing agent dicyandiamide (DICY, melting point of 208–211°C and average particle size of 10 µm), supplied by Alzchem (Germany, Trostberg) and 2,4,6-tris (diethylaminomethyl) phenol or DMP-30 accelerator was supplied by Mokarar Co. (Tehran, Iran). Unidirectional carbon fiber fabric (T300-6K) with an aerial weight of 240 g/m 2 and a thickness of 0.2 mm was obtained from Iranian Navid Company (Tehran, Iran). Hydroxylated GO (UGRAY-OH) with a thickness of 2 µm to 3 µm, 6–10 layers and a purity of 97% was obtained from United Nanotech Innovations, India. The multiwalled carbon nanotubes with thicknesses of 10 nm to 20 nm, lengths of 20 µm and purities of 97% were procured from Parse Company (Tehran, Iran). Silanization of GO and CNTs 500 mg of GO was dissolved in 100 mL of 97% ethanol, followed by ultrasonication for 1 h. Then, 5 ml of (3-glycidyloxypropyl) trimethoxysilane (3-GPTMS) was added to the black homogeneous mixture, and the pH of the solution was adjusted to 4. The resulting mixture was refluxed at 80°C for 12 h. Afterward, the resulting mixture was centrifuged, and the modified nanosheets were washed with ethanol and then dried at 80°C for 8 h. The silanized graphene oxide will be called further S-GO. The above steps were also conducted for silanization of the CNTs, and will be called further S-CNT. Sample preparation Different weight fractions of S-GO (0.1, 0.5, 3 wt%) were poured into the epoxy resin and initially distributed within the pre-weighted quantities of epoxy resin at 2000 rpm for 20 min via a mechanical stirrer and then dispersed properly by sonication for 20 min. Afterward, the DICY powder was added to the mixture and mixed for 30 min via a mechanical stirrer at 2000 rpm. DMP (4.69 g) was added, and a pasty compound was ultimately produced. To prepare the prepregs, the required amount of unidirectional carbon fibers (CF) was weighed. The prepregs with different matrix compositions were then prepared manually and the matrix was distributed over the fibers using a specific tool. The resin content of all the prepregs was about 40 ± 1 wt.%, and the fiber content was 60 ± 1 wt.% (51% by volume). The composite samples for tensile, flexural, and interlaminar shear tests were prepared by laying up eight layers of CF and epoxy/DICY/DMP-30/nanofiller mixture alternatively. After stacking, the prepregs were cured under a 15-ton hot press for 2 h at 130°C and a pressure of 50 bar and then post-cured at 150°C for 1 h. The codes and compositions of all the samples are summarized in Table 1 . Characterization Silane grafting on the graphene and carbon nanotube surfaces was evaluated via Perkin Elmer Fourier transform infrared (FTIR) spectrometer in the 400–4000 cm − 1 . The amount of grafted silane on the graphene and carbon nanotube surfaces was evaluated via thermogravimetric analysis. Thermogravimetric analysis was performed in the temperature range of 25–800°C via TGA-Rheometric Scientific Ltd. under a nitrogen atmosphere at a heating rate of 10°C/min. To characterize the silanized GO and CNTs, EDX analyses were conducted. An EDX analyzer (MIRA3TESCAN-XMU) was used to investigate the elemental analysis of silanized GO and CNTs. Curing kinetic evaluation of the epoxy/DICY/nano fillers was conducted via differential scanning calorimetry (DSC, Mettler Toledo, Switzerland). Approximately 6 mg of each resin mixture was encapsulated in hermetically sealed aluminum pans. The samples were heated from 25 to 300°C at a rate of 10°C min − 1 . Table 1 The codes and compositions of the samples Sample Code Epoxy resin Dicy (phr) DMP-30 (phr) ACNT AGO S-CNT S-GO Pure 100 7 0.6 - - - - ACNT0.5 1 100 7 0.6 0.5 - - - S-CNT0.1 2 100 7 0.6 - - 0.1 - S-CNT0.5 100 7 0.6 - - 0.5 - S-CNT1 100 7 0.6 - - 1 - S-CNT3 100 7 0.6 - - 3 - AGO0.5 3 100 7 0.6 - 0.5 - - S-GO0.1 4 100 7 0.6 - - - 0.1 S-GO0.5 100 7 0.6 - - - 0.5 S-GO1 100 7 0.6 - - - 1 S-GO3 100 7 0.6 - - - 3 S-GO-CNT0.5 100 7 0.6 - - 0.5 0.5 1 As-received CNTs 2 Silanized-CNTs 3 As-received GO 4 Silanized-GO Tensile, flexural (3-point bending), and interlaminar shear (ILS) tests were conducted at room temperature following ASTM D3039, ASTM D790, and ASTM D2344, respectively. The dimension of composites for the tensile test was 20 mm × 2 mm × 200 mm, for flexural was 13 mm × 2 mm × 62 mm and for ILSS was 12 mm × 2 mm × 20 mm for width, thickness and length, respectively. All the mechanical tests were carried out on STM-150 model of SANTAM universal testing machine. The crosshead rates for the tensile, flexural, and ILS tests were 2, 1.3, and 1 mm/min, respectively. Three samples were tested in each test, and the average value and its standard deviation were reported. Results and discussion Characterization of the Silanized CNTs and GO FTIR spectroscopy was conducted to reveal the interaction between the CNTs and GO nanoparticles with the 3-GPTMS coupling agent. Figure 1 a shows the FTIR spectra of the as-received CNTs and silanized CNTs (S-CNTs). Three new absorption bands in the infrared region of the S-CNT spectrum at 3400, 1080 and 773 cm − 1 are assigned to the deformation vibration (–Si–OH) and asymmetric stretching vibration modes of (–Si–OR) [ 19 , 20 ]. This spectral evidence indicates that 3-GPTMS is grafted on the surface of the CNTs. Figure 1 b displays the FTIR spectra of the as-received GO and silanized GO (S-GO). After modification with 3-GPTMS, a new peak appears at approximately 700 cm − 1 , which is related to Si–O–C bands and confirms the chemical bonding between 3-GPTMS and GO. The results of the thermal analysis are shown in Fig. 2. As shown in Fig. 2a, the very small weight loss in the thermal behavior of the CNT nanoparticles in the range of 25–180°C can be related to water removal from the surface [ 21 , 22 ]. The weight loss at 300–600°C, which is observed on the S-CNT graph, corresponds to the decomposition of 3-GPTMS on the CNT surface [ 23 , 24 ]. In the case of GO (Fig. 1 b), the peak at 180°C may be related to the removal of physically absorbed water on the surface of GO. Concerning the S-GO, in addition to the abovementioned weight loss peak, a new weight loss region in the range of 350–500°C also appeared due to the decomposition of the 3-GPTMS molecules [ 25 , 26 ]. The Energy-Dispersive X-ray spectra of silanized GO and CNTs are presented in Fig. 3 . The presence of silicon atoms originating from the organosilane compound in the EDX spectra of silanized GO and CNTs proved that the 3-GPTMS molecules were successfully grafted on the surfaces of the GO and CNTs. As seen from the EDX results, compared with the CNT filler, the GO possesses an eligible silane density on its surface. Therefore, the extent of aggregation caused by the intramolecular hydrogen bonding-type interactions between surface hydroxyl groups is expected to be greater. Weight ratios of S-CNT and S-GO from EDX analysis are shown in Table 2 . Table 2 Weight ratios of S-CNT and S-GO from EDX analysis S-CNT S-GO Atomic % of C 77.44 95.9 Atomic % of O 15.77 3.9 Atomic % of Si 6.79 0.2 Reaction mechanism The silanization reactions contain four steps including hydrolysis, condensation, hydrogen bonding, and bond formation. The R-O-CH3 groups of 3-GPTMS hydrolyze in acidic medium and the formed Si–OH reacts with the -OH functional group on the surface of GO and CNTs. During the refluxing, a covalent bond is formed between (GO, CNTs and 3-GPTMS) with losing of water. After dispersing the S-GO and S-CNTs in the epoxy resin, a chemical bonding forms between the functional groups of S-GO, S-CNTs nanofillers and epoxy matrix with functional groups of DMP-30 hardener. One end of the hardener reacts with epoxy matrix and another end of it react with the 3-GPTMS silane coupling agent. The molecular structure of 3-GPTMS is represented in Fig. 4 . As can be seen, the 3-GPTMS has two active sides for chemical reaction, which made it a good choice for improvement of epoxy matrix in fiber reinforced composites. Curing behavior Figure 5 presents the results of the DSC experiments in nonisothermal mode for the epoxy/DICY nanocomposites with different contents of S-CNT, S-GO, and their hybrid and a constant amount of 0.6 phr DMP accelerator from 25 to 300°C at a 10°C min − 1 heating rate. The DSC data of the pure and all the nanocomposites are presented in Table 3 . Compared with those of the pure sample, the maximum changes in the initial (T 0 ) and peak (T peak ) temperatures is 2°C. These results revealed that the incorporation of nanofillers has no significant effect on the curing behavior of the epoxy/DICY/nanofiller. This might be due to the solid nature of the DICY high temperature and latent curing agent. Table 3 Data from nonisothermal DSC thermograms at a heating rate of 10°C/min. Sample Pure ACNT0.5 S-CNT0.5 S-CNT3 AGO0.5 S-GO0.5 S-GO3 S-GO-CNT0.5 T O , ᵒC 128 145 462 129 144 474 128 144 476 130 146 427 127 145 463 127 143 469 127 144 469 129 145 458 T peak , ᵒC ΔH (mJ/mg) Mechanical properties The flexural, tensile, and shear properties of the epoxy/DICY/carbon fiber systems containing ACNT, AGO, S-CNTs, S-GO, and a hybrid of two nanoparticles were evaluated in the transverse direction of the fibers. The mechanical properties of composites in the transverse direction of fibers are controlled by the matrix, so these properties were measured in this direction. Typical transverse flexural stress-strain curves of carbon fiber/epoxy nanocomposites containing different amounts of S-CNT are presented in Fig. 6 . Similar behavior was observed for S-GO samples. Figure 7 displays the effects of silanization and hybrid nanoparticles on the tensile and flexural strengths of the ACNT/epoxy/DICY/CF and AGO/epoxy/DICY/CF composites. The tensile and flexural strengths of the S-CNT0.5/epoxy/DICY/CF composite are 18% and 27% greater than those of the neat ACNT0.5/epoxy/DICY/CF. This observation can be related to the enhanced matrix/fiber interaction due to S-CNT incorporation. In composites, the incongruity in the coefficient of thermal expansion (CTE) of the fiber and polymeric matrix caused residual stresses at the interface after the curing stage, which encouraged fiber/matrix debonding during mechanical testing [ 27 , 28 ]. In the presence of S-CNT in the matrix, the incongruity in the CTE between the CF and the matrix is reduced, which enhances the fiber/matrix bonding. On the other hand, the S-CNT nanofiller can convey a portion of the applied load, resulting in a reduction in the stress concentration on the CF. Therefore, the stress required for fiber breakage is increased. With further loading of S-CNT from 0.5 to 3 wt%, the tensile and flexural strengths decreased. In fact, at higher contents of S-CNT, agglomeration can occur, which acts as a stress concentration region within the matrix, resulting in reduced mechanical properties [ 29 , 30 ]. In the epoxy/CF composites containing GO nanoplates, as shown in Fig. 7 , the tensile and flexural strengths of the 0.5 wt.% S-GO/epoxy/DICY/CF composite are 21% and 16% greater than those of the neat AGO0.5/epoxy/DICY/CF composite. With greater loadings of 0.5 wt.% S-GO, the tensile and flexural strengths considerably decrease. This may be related to the fact that at higher nanofiller contents, S-GO aggregates in the stress concentration region reduce the tensile and flexural strengths of the composites. Compared with ACNT0.5, the incorporation of the hybrid of S-CNT-GO0.5 increases the flexural and tensile strengths by 39.6% and 26%, respectively. It can be concluded that the contact geometry between nanofillers changes from 0D point contact to 1D linear contact, which considerably enhances the contact surface area in hybrid nanofillers, resulting in improved mechanical properties [ 9 ]. In one hand, the creation of a dual-network of GO-CNT and multiphase structure and proper dispersion of nanofillers and the other hand their synergetic effect on dispersion reinforce the interface with the epoxy, caused maximize load transfer from epoxy to nanofillers. The effects of silanization and hybrid nanoparticles on the transverse tensile and flexural moduli of the ACNT/epoxy/DICY/CF and AGO/epoxy/DICY/CF composites are shown in Fig. 8 . The tensile moduli of the S-CNT0.5- and S-GO0.5-filled epoxy/DICY/CF composites are 10% and 15% greater, respectively, than those of the nonfunctionalized samples. The mechanical properties of the matrix and matrix/fiber interactions improved because of the surface modification of the nanofillers with 3-GPTMS. In fact, the mobility of polymeric chains is restricted, which effectively enhances the interfacial interactions between fillers and the epoxy matrix. Moreover, approximately 34% and 39% increases in the flexural moduli of the 0.5 wt% S-CNT- and S-GO-filled samples, respectively, were observed. The tensile and flexural moduli of the hybrid S-CNT-GO-filled composites were enhanced by 31% and 45%, respectively, compared with those of the neat AGO0.5 composite. Morphology To interpret the observed mechanical properties, the fracture surfaces of the composites for the tensile test were evaluated by scanning electron microscopy. Weak interfacial bonding between the CF and the epoxy matrix for neat composites containing ACNT and AGO was observed from the clean surface of the CF and CF-matrix debonding in the SEM micrograph (Fig. 9 a, d). The good dispersion of S-CNT and S-GO in epoxy matrix results in S-CNT/epoxy and S-GO/epoxy matrix becoming progressively rough and making crack propagation more devious due to the crack deflection mechanism. Therefore, good adhesion between the CF and the epoxy matrix filled with S-CNT0.5 and S-GO0.5 is observable on the fracture surface of the composites (Fig. 9 . b, e). The agglomerates of 3 wt% SCNT and SGO can be seen on the fracture surface of the composites (Fig. 8 . c, f). These agglomerates act as stress concentration sites [ 31 , 32 ]. This observation confirms the reduced mechanical properties of the 3 wt% S-CNT- and S-GO-filled composite in comparison with those of the 0.5 wt% sample. An SEM image of the fracture surface of the hybrid S-CNT-S-GO/epoxy/DICY/CF composite is presented in Fig. 10 . As can be seen, the hybrid nanofillers improved the adhesion between the epoxy matrix and CF surface, resulting in enhanced matrix-fiber interfacial strength. Interlaminar shear strength Short beam shear testing (ASTM D2344) was conducted to measure the transverse interlaminar shear strength (ILSS) of each sample. The testing was carried out at room temperature. The ILSS results of the S-CNT/epoxy/DICY/CF, S-GO/epoxy/DICY/CF and S-CNT-GO0.5/epoxy/DICY/CF composites are presented in Fig. 11 . Compared with those of the ACNT0.5 and AGO0.5 composites, the ILSS of the 0.5 wt.% S-CNT and S-GO filled composites were 18% and 10% greater, respectively. This observation may be due to the interlocking and stress transfer capability of S-CNT and S-GO at the interface of the carbon fibers and the epoxy matrix [ 33 ]. The highest transverse ILSS 6.2 ± 0.6 MPa was observed for the 0.5 wt.% hybrids of S-CNT/S-GO because the better dispersion of the two nanofillers with different dimensions contained 1D CNTs and 2D GO in the epoxy. The ILSS is expected to increase because of the improvement in the matrix strength and fiber-matrix interface caused by nanofiller dispersion. A change in the thermal stability/residual stresses of the epoxy matrix creates pressure at the fiber surface, which results in strong adhesion between the fiber and the matrix [ 34 ]. The agglomeration of S-CNT and S-GO, beyond 0.5 wt.% loadings, causes stress concentration, which results in debonding of fibers from the matrix during loading and poor performance of the composite. Conclusion The silanization of CNTs and GO was done successfully, and the results of FTIR, TGA, and EDX analyses revealed that 3-GPTMS was grafted on the surface of the GO and CNT nanofillers. The effects of this modification on the transverse tensile, flexural, and ILSS properties of the epoxy/DICY/CF nanocomposites were evaluated. Tensile and flexural strengths of the 0.5 wt.% S-CNT-filled CF/DICY/epoxy composite were 18% and 27%, respectively, greater than those of the ACNT0.5/epoxy/DICY/CF composite. Compared with ACNT0.5, the nanocomposite containing the hybrid of S-CNT-GO0.5 presented 26% and 39.6% greater transverse tensile and flexural strengths, respectively. Compared with those of the control samples, the tensile moduli of the S-CNT0.5- and S-GO0.5-filled epoxy/DICY/CF composites were 10% and 15%, respectively, and the flexural moduli were 34% and 39% greater. The flexural modulus of the hybrid S-CNT-GO0.5-filled composites was enhanced by 31% and 45% compared with the S-CNT0.5 and S-GO0.5 samples, respectively. The good adhesion between the CF and the epoxy matrix filled with S-CNT0.5 and S-GO0.5 was observed on the fracture surface of the samples. Compared with those of the control composite, the transverse ILSS of 0.5 wt% S-CNT, S-GO, and their hybrid-filled composites were enhanced by 18%, 10%, and 25%, respectively. Declarations Funding This research was funded by the Iran National Science Foundation, grant number 98020833. Author Contributions Nahid Jamali: conceptualization, formal analysis, investigation, data curation and writing– original draft. 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Coatings 9:587 Vennerberg D, Rueger Z, Kessler MR (2014) Effect of silane structure on the properties of silanized multiwalled carbon nanotube-epoxy nanocomposites. Polymer 55:1854–1865 Anagnostopoulos G, Parthenios J, Galiotis C (2008) Thermal stress development in fibrous composites. Mater Lett 62:341–345 Gong LX, Hu LL, Zang J et al (2015) Improved Interfacial Properties between Glass Fibers and Tetra-functional Epoxy Resins Modified with Silica Nanoparticles. Fibers Polym 16:2056–2065 Wang E, Dong Y, Islam Z et al (2019) Effect of graphene oxide-carbon nanotube hybrid filler on the mechanical property and thermal response speed of shape memory epoxy composites. Comp Sci Tech 169:209–216 Jamali N, Khosravi H, Rezvani A et al (2021) Viscoelastic and dry-sliding wear properties of basalt fiber-reinforced composites based on a surface-modified graphene oxide/epoxy matrix. Indust Text 50:939–953 Kausar A, Ahmad I (2024) Nanocomposites of nanocarbon functionalized carbon fibers- Manufacturing to methodological applications. Adv Mat Sci 24:46–71 Fazeli M, Jayaprakash S, Baniasadi H et al (2024) Recycled carbon fiber reinforced composites: Enhancing mechanical properties through co-functionalization of carbon nanotube-bonded microfibrillated cellulose. Comp Part A: Appl Sci Manuf 180:108097 Hossain MK, Hossain ME, Dewan MW et al (2013) Effects of carbon nanofibers (CNFs) on thermal and interlaminar shear responses of E-glass/polyester composites. Comp Part B: Eng 44:313–320 Fan Z, Santare M-H, Advani SG (2008) Interlaminar shear strength of glass fiber reinforced epoxy composites enhanced with multiwalled carbon nanotubes. Comp Part A: Appl Sci Manuf 39:540–554 de Oliveira MM, Forsberg S, Selegard L, Carastan DJ (2021) The influence of sonication processing conditions on electrical and mechanical properties of single and hybrid epoxy nanocomposites filled with carbon nanoparticles. Polymers 13:4128 Cite Share Download PDF Status: Posted Version 1 posted You are reading this latest preprint version Research Square lets you share your work early, gain feedback from the community, and start making changes to your manuscript prior to peer review in a journal. As a division of Research Square Company, we’re committed to making research communication faster, fairer, and more useful. We do this by developing innovative software and high quality services for the global research community. Our growing team is made up of researchers and industry professionals working together to solve the most critical problems facing scientific publishing. Also discoverable on Platform About Our Team In Review Editorial Policies Advisory Board Help Center Resources Author Services Accessibility API Access RSS feed Manage Cookie Preferences © Research Square 2026 | ISSN 2693-5015 (online) Privacy Policy Terms of Service Do Not Sell My Personal Information {"props":{"pageProps":{"initialData":{"identity":"rs-7164361","acceptedTermsAndConditions":true,"allowDirectSubmit":true,"archivedVersions":[],"articleType":"Research Article","associatedPublications":[],"authors":[{"id":502955097,"identity":"f1fc71f3-cfff-4ecd-a543-e0270a29f80e","order_by":0,"name":"Nahid Jamali","email":"","orcid":"","institution":"","correspondingAuthor":false,"prefix":"","firstName":"Nahid","middleName":"","lastName":"Jamali","suffix":""},{"id":502955098,"identity":"b356257c-ba2a-418b-860a-1ebcb4308a95","order_by":1,"name":"Mohammad Hosain Beheshty","email":"data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAZAAAAAyAQMAAABI0h/eAAAABlBMVEX///8AAABVwtN+AAAACXBIWXMAAA7EAAAOxAGVKw4bAAAA6klEQVRIie3RsYrCMBzH8V8JOP2jjgFBX6FyUL3JV2npqqK4OEjp1C6661s4OqYEziUPcOOB4C6OB2IbEIWD2PGGfJdA4AP55w+4XP8wXxJYeYYAkxIQ5lbayOeDEBphPTJ6EvLrPSyQvDjNlsl0JMYXNT8M0cqlp5ZW0ow/tlotSEz2aqcFhA5RaCuhoMMzGa0rwrNylm+gSC2k/LHBL78lJRn/GNKrQQLGU1YRGOK/JaoZd+hLRWt99qtZqK+j1E6Om+JKqyTK8/h0nR+Sbveo1MVGzFJM7RDMS0GAZwUvtaQhLpfL5frTHcQRUuTXVx92AAAAAElFTkSuQmCC","orcid":"https://orcid.org/0000-0001-6417-7487","institution":"Iran Polymer and Petrochemical Institute","correspondingAuthor":true,"prefix":"","firstName":"Mohammad","middleName":"Hosain","lastName":"Beheshty","suffix":""}],"badges":[],"createdAt":"2025-07-19 12:13:46","currentVersionCode":1,"declarations":"","doi":"10.21203/rs.3.rs-7164361/v1","doiUrl":"https://doi.org/10.21203/rs.3.rs-7164361/v1","draftVersion":[],"editorialEvents":[],"editorialNote":"","failedWorkflow":false,"files":[{"id":90121599,"identity":"2dc37c6e-a557-4b2c-af28-ef6f376d915f","added_by":"auto","created_at":"2025-08-28 17:47:36","extension":"png","order_by":1,"title":"Figure 1","display":"","copyAsset":false,"role":"figure","size":50583,"visible":true,"origin":"","legend":"\u003cp\u003eFTIR spectra of a) as received CNT, S-CNT, and b) as received GOH, S-GO\u003c/p\u003e","description":"","filename":"1.png","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/5a6188897277d45b6454d5a9.png"},{"id":90121600,"identity":"225729a5-81b9-4a6b-b276-64d31044493a","added_by":"auto","created_at":"2025-08-28 17:47:36","extension":"png","order_by":2,"title":"Figure 2","display":"","copyAsset":false,"role":"figure","size":71269,"visible":true,"origin":"","legend":"\u003cp\u003eThermal gravimetry analysis of a) as received CNT, S-CNT, and b) as received GO, S-GO\u003c/p\u003e","description":"","filename":"2.png","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/17096e7a83ab101a60b38872.png"},{"id":90121610,"identity":"2492f747-f505-4a05-b905-73dd53ff9d6c","added_by":"auto","created_at":"2025-08-28 17:47:36","extension":"png","order_by":3,"title":"Figure 3","display":"","copyAsset":false,"role":"figure","size":116805,"visible":true,"origin":"","legend":"\u003cp\u003eEDX spectra of (a) S-CNT and (b) S-GO.\u003c/p\u003e","description":"","filename":"3.png","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/7dd0e2ca79a91a78c6ca383a.png"},{"id":90122181,"identity":"300b6551-e088-49f3-9830-9c8c37cdb1d7","added_by":"auto","created_at":"2025-08-28 17:55:36","extension":"png","order_by":4,"title":"Figure 4","display":"","copyAsset":false,"role":"figure","size":13064,"visible":true,"origin":"","legend":"\u003cp\u003eThe molecular structure of GPTMS\u003cstrong\u003e.\u003c/strong\u003e\u003c/p\u003e","description":"","filename":"4.png","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/0c68569982decd1787154009.png"},{"id":90122338,"identity":"3ee1bd00-72de-490c-9c0c-48f1849ae65f","added_by":"auto","created_at":"2025-08-28 18:03:36","extension":"png","order_by":5,"title":"Figure 5","display":"","copyAsset":false,"role":"figure","size":139930,"visible":true,"origin":"","legend":"\u003cp\u003eDSC heat flow curves for different contents of a) as received and silanized CNTs, b) as received and silanized GO and GO-CNT\u003c/p\u003e","description":"","filename":"5.png","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/895288aa251d5cd7cc3ad657.png"},{"id":90121607,"identity":"0c8a2159-cffa-4d07-8bd9-80c99466c668","added_by":"auto","created_at":"2025-08-28 17:47:36","extension":"png","order_by":6,"title":"Figure 6","display":"","copyAsset":false,"role":"figure","size":36840,"visible":true,"origin":"","legend":"\u003cp\u003eTypical transverse flexural stress-strain curves of carbon fiber/epoxy nanocomposites containing ACNT and different amounts of S-CNT.\u003c/p\u003e","description":"","filename":"6.png","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/4d035589a5464bdfa624b2a1.png"},{"id":90122339,"identity":"be03f303-581f-44cb-be8f-815a500eb8a9","added_by":"auto","created_at":"2025-08-28 18:03:36","extension":"png","order_by":7,"title":"Figure 7","display":"","copyAsset":false,"role":"figure","size":23035,"visible":true,"origin":"","legend":"\u003cp\u003eTransverse tensile and flexural strengths of the carbon fiber epoxy nanocomposites with different content of S-CNT, S-GO, and hybrid S-CNT/GO0.5.\u003c/p\u003e","description":"","filename":"7.png","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/f893558e347b7a7ce8e58c6a.png"},{"id":90121611,"identity":"f7688546-a2d6-4906-a417-4af0c926e04d","added_by":"auto","created_at":"2025-08-28 17:47:36","extension":"png","order_by":8,"title":"Figure 8","display":"","copyAsset":false,"role":"figure","size":22818,"visible":true,"origin":"","legend":"\u003cp\u003eTransverse tensile and flexural moduli of the epoxy/DICY/carbon fiber nanocomposites with different S-CNT, S-GO, and hybrid S-CNT-GO contents.\u003c/p\u003e","description":"","filename":"8.png","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/04709dee2891f7f3a9edfe1e.png"},{"id":90122189,"identity":"0c9245da-f63f-452d-bbcc-4da3ecc2dc49","added_by":"auto","created_at":"2025-08-28 17:55:37","extension":"png","order_by":9,"title":"Figure 9","display":"","copyAsset":false,"role":"figure","size":296443,"visible":true,"origin":"","legend":"\u003cp\u003eSEM micrographs of the tensile fracture surfaces of the (a) ACNT0.5 and (b) S-CNT0.5 (c) S-CNT3 (d) AGO0.5 (e) S-GO0.5 and (f) S-GO3 composites.\u003c/p\u003e","description":"","filename":"9.png","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/baebe54953abb4b35f067ce3.png"},{"id":90121603,"identity":"6b0c5d74-18a7-4cd2-93cf-9e3990e2ee93","added_by":"auto","created_at":"2025-08-28 17:47:36","extension":"jpg","order_by":10,"title":"Figure 10","display":"","copyAsset":false,"role":"figure","size":54810,"visible":true,"origin":"","legend":"\u003cp\u003eSEM micrograph of the tensile fracture surface of the S-CNT-GO0.5/epoxy/DICY/CF sample.\u003c/p\u003e","description":"","filename":"10.jpg","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/2961627818180a06be6620e5.jpg"},{"id":90122188,"identity":"7f0d888c-087f-4fa5-8963-e8176b6e0930","added_by":"auto","created_at":"2025-08-28 17:55:37","extension":"png","order_by":11,"title":"Figure 11","display":"","copyAsset":false,"role":"figure","size":18533,"visible":true,"origin":"","legend":"\u003cp\u003eTransverse ILSS results of the epoxy/DICY/carbon fiber composites in the presence of S-CNT, S-GO, and hybrid S-CNT/S-GO.\u003c/p\u003e","description":"","filename":"11.png","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/47dfa678796f5473e93eefdb.png"},{"id":99311942,"identity":"63abef8b-865d-43fa-aaeb-1eca1e49e051","added_by":"auto","created_at":"2025-12-31 16:17:29","extension":"pdf","order_by":0,"title":"","display":"","copyAsset":false,"role":"manuscript-pdf","size":1474778,"visible":true,"origin":"","legend":"","description":"","filename":"manuscript.pdf","url":"https://assets-eu.researchsquare.com/files/rs-7164361/v1/c6abd518-3ed8-462a-ba8c-801329515dbe.pdf"}],"financialInterests":"","formattedTitle":"Effects of silanization and hybrid nanofillers of multiwalled carbon nanotubes and graphene oxide on the mechanical properties of epoxy/dicyandiamide/carbon fiber composites","fulltext":[{"header":"Introduction","content":"\u003cp\u003eOwing to their attractive properties, epoxy resins have been widely used as a matrix for carbon fiber-reinforced composites. The anisotropy between carbon fibers (CFs) and the polymer matrix results in poor interfacial properties and low stiffness of the composite [\u003cspan citationid=\"CR1\" class=\"CitationRef\"\u003e1\u003c/span\u003e, \u003cspan citationid=\"CR2\" class=\"CitationRef\"\u003e2\u003c/span\u003e]. Generally, in composite materials with epoxy matrix, the fracture is caused by, transverse and longitudinal rupture of the matrix or by the fiber-matrix interface debonding. These observations lead us to pay more attention to the event of deformation of epoxy composites by knowing the process of rupture and damage of both the matrix and the composites and the archiving method for improving the fiber and matrix reactions [\u003cspan citationid=\"CR3\" class=\"CitationRef\"\u003e3\u003c/span\u003e, \u003cspan citationid=\"CR4\" class=\"CitationRef\"\u003e4\u003c/span\u003e]. The use of carbon-derived nanofillers such as carbon nanotubes (CNTs) and graphene oxide (GO) with an epoxy matrix is one of the most investigated approaches to improve current polymer matrix properties [\u003cspan additionalcitationids=\"CR4\" citationid=\"CR3\" class=\"CitationRef\"\u003e3\u003c/span\u003e–\u003cspan citationid=\"CR5\" class=\"CitationRef\"\u003e5\u003c/span\u003e]. The incorporation of nanofillers can affect the interaction of the polymer matrix with fiber reinforcements and the resin curing process [\u003cspan citationid=\"CR6\" class=\"CitationRef\"\u003e6\u003c/span\u003e]. Bahari et al. [\u003cspan citationid=\"CR7\" class=\"CitationRef\"\u003e7\u003c/span\u003e] investigated the synergetic effect of hybrid fillers, including surface-modified montmorillonite (MMT) nanoclusters and graphene nanoplatelets (GNPs), on the dispersion quality and mechanical characteristics of epoxy-based nanocomposites. The results revealed that the maximum tensile and flexural strengths were obtained for the samples containing 0.15 wt.% GNPs and 1 wt.% MMT, which were 19% and 17.4% greater than those of the neat epoxy, respectively. Jen et al. [\u003cspan citationid=\"CR8\" class=\"CitationRef\"\u003e8\u003c/span\u003e] studied the synergistic effect of hybrid nanofillers of multiwalled carbon nanotube (MWCNT)/graphene nanoplatelets (GNPs) on the mechanical and fatigue properties of epoxy composites. The experimental results show that the composites with a MWCNT:GNP ratio of 1:9 have greater monotonic and fatigue properties than those with other filler ratios. Yang et al. [\u003cspan citationid=\"CR9\" class=\"CitationRef\"\u003e9\u003c/span\u003e] investigated the effects of multigraphene platelets (MGPs) and multiwalled carbon nanotubes (MWCNTs) on improving the mechanical properties and thermal conductivity of epoxy composites. They reported 35.4% and 146.9% enhancements in tensile strength and thermal conductivity, respectively, for GD400-MWCNT/MGP/epoxy composites compared with nonderivatized epoxy. Li et al. [\u003cspan citationid=\"CR10\" class=\"CitationRef\"\u003e10\u003c/span\u003e] studied the effect of hybrid fillers composed of carbon nanotubes (CNTs) grown on graphene nanoplatelets (GNPs) in an epoxy matrix. For the 0.5 wt.% hybrid filler loading, the tensile modulus increased by 40%, and the tensile strength was increased by 36% concerning that of the neat epoxy.\u003c/p\u003e\u003cp\u003eHowever, van der Waals forces between nanofillers can lead to agglomeration and result in inhomogeneous dispersion in a polymer matrix. The dispersibility and interfacial strength of fillers can be improved by functionalization of nanofillers with organosilane coupling agents. On the other hand, the functional groups of the silane coupling agents could be chemically attached to the polymer matrix and improve the adhesion of fillers to the polymer matrix. The silane coupling agent reacts with the nanofiller on one hand and reacts with the epoxy matrix on the end hand [\u003cspan additionalcitationids=\"CR12 CR13\" citationid=\"CR11\" class=\"CitationRef\"\u003e11\u003c/span\u003e–\u003cspan citationid=\"CR14\" class=\"CitationRef\"\u003e14\u003c/span\u003e]. Recent curing systems based on dicyandiamide (DICY), a solid powder with limited solubility in epoxides at room temperature, can dedicate epoxy prepolymers with excellent processing ability, room temperature stability, and cured products with phenomenal mechanical and electrical properties. For these reasons, the epoxy/DICY-based resin widely used as a matrix for carbon fiber prepregs would allow long-term storage at room temperature, reduce storage costs, and simplify logistics. The adhesion between the matrix and fibers and the mechanical properties of the final composite products are strongly dependent on the curing reactions of the epoxy/DICY systems [\u003cspan additionalcitationids=\"CR16 CR17\" citationid=\"CR15\" class=\"CitationRef\"\u003e15\u003c/span\u003e–\u003cspan citationid=\"CR18\" class=\"CitationRef\"\u003e18\u003c/span\u003e].\u003c/p\u003e\u003cp\u003eThis work aims to investigate the curing behavior of the epoxy/DICY system and the mechanical behavior of its carbon fiber-reinforced composites by silanizing GO and CNT individually and the GO/CNT hybrid by combining one-dimensional multiwalled carbon nanotubes (1D CNTs) and 2D GO. The incorporation of hybrid nanofillers has the capacity to acquire the synergistic effects and properties of each nanofiller. Therefore, the appearance of different types of nanoparticles contains CNT and GO with tube and plate structures respectively, could improve the reaction between nanofiller, epoxy matrix and carbon fibers and enhance the mechanical properties of composites. To the best of our knowledge, no comprehensive study has focused on the effects of both the silanization and hybridization of CNTs and GO on the transverse tensile, flexural, and interlaminar shear properties of CF/DICY/epoxy composites. This was the motivation for choosing this method.\u003c/p\u003e"},{"header":"Materials","content":"\u003cp\u003eEpoxy resin (Epikote-828, diglycidyl ether of bisphenol-A) with epoxide equivalent weights of 185–190 and viscosity of 12 Pa.s to 14 Pa.s at room temperature was obtained from Momentive Co. (Columbus, OH, USA). The latent curing agent dicyandiamide (DICY, melting point of 208–211°C and average particle size of 10 µm), supplied by Alzchem (Germany, Trostberg) and 2,4,6-tris (diethylaminomethyl) phenol or DMP-30 accelerator was supplied by Mokarar Co. (Tehran, Iran). Unidirectional carbon fiber fabric (T300-6K) with an aerial weight of 240 g/m\u003csup\u003e2\u003c/sup\u003e and a thickness of 0.2 mm was obtained from Iranian Navid Company (Tehran, Iran). Hydroxylated GO (UGRAY-OH) with a thickness of 2 µm to 3 µm, 6–10 layers and a purity of 97% was obtained from United Nanotech Innovations, India. The multiwalled carbon nanotubes with thicknesses of 10 nm to 20 nm, lengths of 20 µm and purities of 97% were procured from Parse Company (Tehran, Iran).\u003c/p\u003e\u003cp\u003e\u003cb\u003eSilanization of GO and CNTs\u003c/b\u003e\u003c/p\u003e\u003cp\u003e500 mg of GO was dissolved in 100 mL of 97% ethanol, followed by ultrasonication for 1 h. Then, 5 ml of (3-glycidyloxypropyl) trimethoxysilane (3-GPTMS) was added to the black homogeneous mixture, and the pH of the solution was adjusted to 4. The resulting mixture was refluxed at 80°C for 12 h. Afterward, the resulting mixture was centrifuged, and the modified nanosheets were washed with ethanol and then dried at 80°C for 8 h. The silanized graphene oxide will be called further S-GO. The above steps were also conducted for silanization of the CNTs, and will be called further S-CNT.\u003c/p\u003e\u003cp\u003e\u003cb\u003eSample preparation\u003c/b\u003e\u003c/p\u003e\u003cp\u003eDifferent weight fractions of S-GO (0.1, 0.5, 3 wt%) were poured into the epoxy resin and initially distributed within the pre-weighted quantities of epoxy resin at 2000 rpm for 20 min via a mechanical stirrer and then dispersed properly by sonication for 20 min. Afterward, the DICY powder was added to the mixture and mixed for 30 min via a mechanical stirrer at 2000 rpm. DMP (4.69 g) was added, and a pasty compound was ultimately produced.\u003c/p\u003e\u003cp\u003eTo prepare the prepregs, the required amount of unidirectional carbon fibers (CF) was weighed. The prepregs with different matrix compositions were then prepared manually and the matrix was distributed over the fibers using a specific tool. The resin content of all the prepregs was about 40 ± 1 wt.%, and the fiber content was 60 ± 1 wt.% (51% by volume). The composite samples for tensile, flexural, and interlaminar shear tests were prepared by laying up eight layers of CF and epoxy/DICY/DMP-30/nanofiller mixture alternatively. After stacking, the prepregs were cured under a 15-ton hot press for 2 h at 130°C and a pressure of 50 bar and then post-cured at 150°C for 1 h. The codes and compositions of all the samples are summarized in Table\u0026nbsp;\u003cspan refid=\"Tab1\" class=\"InternalRef\"\u003e1\u003c/span\u003e.\u003c/p\u003e\u003cp\u003e\u003cb\u003eCharacterization\u003c/b\u003e\u003c/p\u003e\u003cp\u003eSilane grafting on the graphene and carbon nanotube surfaces was evaluated via Perkin Elmer Fourier transform infrared (FTIR) spectrometer in the 400–4000 cm\u003csup\u003e− 1\u003c/sup\u003e. The amount of grafted silane on the graphene and carbon nanotube surfaces was evaluated via thermogravimetric analysis. Thermogravimetric analysis was performed in the temperature range of 25–800°C via TGA-Rheometric Scientific Ltd. under a nitrogen atmosphere at a heating rate of 10°C/min. To characterize the silanized GO and CNTs, EDX analyses were conducted. An EDX analyzer (MIRA3TESCAN-XMU) was used to investigate the elemental analysis of silanized GO and CNTs. Curing kinetic evaluation of the epoxy/DICY/nano fillers was conducted via differential scanning calorimetry (DSC, Mettler Toledo, Switzerland). Approximately 6 mg of each resin mixture was encapsulated in hermetically sealed aluminum pans. The samples were heated from 25 to 300°C at a rate of 10°C min\u003csup\u003e− 1\u003c/sup\u003e.\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cdiv class=\"gridtable\"\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c1\" colnum=\"1\"\u003e\u003c/div\u003e\u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c2\" colnum=\"2\"\u003e\u003c/div\u003e\u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c3\" colnum=\"3\"\u003e\u003c/div\u003e\u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c4\" colnum=\"4\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c5\" colnum=\"5\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c6\" colnum=\"6\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c7\" colnum=\"7\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c8\" colnum=\"8\"\u003e\u003c/div\u003e\u003ctable float=\"Yes\" id=\"Tab1\" border=\"1\"\u003e\u003ccaption language=\"En\"\u003e\u003cdiv class=\"CaptionNumber\"\u003eTable 1\u003c/div\u003e\u003cdiv class=\"CaptionContent\"\u003e\u003cp\u003eThe codes and compositions of the samples\u003c/p\u003e\u003c/div\u003e\u003c/caption\u003e\u003ccolgroup cols=\"8\"\u003e\u003c/colgroup\u003e\u003cthead\u003e\u003ctr\u003e\u003cth align=\"left\" colname=\"c1\"\u003e\u003cp\u003eSample Code\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c2\"\u003e\u003cp\u003eEpoxy resin\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c3\"\u003e\u003cp\u003eDicy\u003c/p\u003e\u003cp\u003e(phr)\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c4\"\u003e\u003cp\u003eDMP-30 (phr)\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c5\"\u003e\u003cp\u003eACNT\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c6\"\u003e\u003cp\u003eAGO\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c7\"\u003e\u003cp\u003eS-CNT\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c8\"\u003e\u003cp\u003eS-GO\u003c/p\u003e\u003c/th\u003e\u003c/tr\u003e\u003c/thead\u003e\u003ctbody\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003ePure\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eACNT0.5\u003csup\u003e1\u003c/sup\u003e\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e0.5\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eS-CNT0.1\u003csup\u003e2\u003c/sup\u003e\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e0.1\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eS-CNT0.5\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e0.5\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eS-CNT1\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e1\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eS-CNT3\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e3\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eAGO0.5\u003csup\u003e3\u003c/sup\u003e\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e0.5\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eS-GO0.1\u003csup\u003e4\u003c/sup\u003e\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e0.1\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eS-GO0.5\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e0.5\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eS-GO1\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e1\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eS-GO3\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e3\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eS-GO-CNT0.5\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e100\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e7\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e\u003cp\u003e0.6\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c5\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c6\"\u003e\u003cp\u003e-\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c7\"\u003e\u003cp\u003e0.5\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"left\" colname=\"c8\"\u003e\u003cp\u003e0.5\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003c/tbody\u003e\u003ctfoot\u003e\u003ctr\u003e\u003ctd colspan=\"8\"\u003e\u003csup\u003e1\u003c/sup\u003e As-received CNTs\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd colspan=\"8\"\u003e\u003csup\u003e2\u003c/sup\u003e Silanized-CNTs\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd colspan=\"8\"\u003e\u003csup\u003e3\u003c/sup\u003e As-received GO\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd colspan=\"8\"\u003e\u003csup\u003e4\u003c/sup\u003e Silanized-GO\u003c/td\u003e\u003c/tr\u003e\u003c/tfoot\u003e\u003c/table\u003e\u003c/div\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003eTensile, flexural (3-point bending), and interlaminar shear (ILS) tests were conducted at room temperature following ASTM D3039, ASTM D790, and ASTM D2344, respectively. The dimension of composites for the tensile test was 20 mm × 2 mm × 200 mm, for flexural was 13 mm × 2 mm × 62 mm and for ILSS was 12 mm × 2 mm × 20 mm for width, thickness and length, respectively. All the mechanical tests were carried out on STM-150 model of SANTAM universal testing machine. The crosshead rates for the tensile, flexural, and ILS tests were 2, 1.3, and 1 mm/min, respectively. Three samples were tested in each test, and the average value and its standard deviation were reported.\u003c/p\u003e"},{"header":"Results and discussion","content":"\u003cp\u003e\u003cb\u003eCharacterization of the Silanized CNTs and GO\u003c/b\u003e\u003c/p\u003e\u003cp\u003eFTIR spectroscopy was conducted to reveal the interaction between the CNTs and GO nanoparticles with the 3-GPTMS coupling agent. Figure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003ea shows the FTIR spectra of the as-received CNTs and silanized CNTs (S-CNTs). Three new absorption bands in the infrared region of the S-CNT spectrum at 3400, 1080 and 773 cm\u003csup\u003e\u0026minus;\u0026thinsp;1\u003c/sup\u003e are assigned to the deformation vibration (\u0026ndash;Si\u0026ndash;OH) and asymmetric stretching vibration modes of (\u0026ndash;Si\u0026ndash;OR) [\u003cspan citationid=\"CR19\" class=\"CitationRef\"\u003e19\u003c/span\u003e, \u003cspan citationid=\"CR20\" class=\"CitationRef\"\u003e20\u003c/span\u003e]. This spectral evidence indicates that 3-GPTMS is grafted on the surface of the CNTs. Figure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003eb displays the FTIR spectra of the as-received GO and silanized GO (S-GO). After modification with 3-GPTMS, a new peak appears at approximately 700 cm\u003csup\u003e\u0026minus;\u0026thinsp;1\u003c/sup\u003e, which is related to Si\u0026ndash;O\u0026ndash;C bands and confirms the chemical bonding between 3-GPTMS and GO.\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003eThe results of the thermal analysis are shown in Fig.\u0026nbsp;2. As shown in Fig.\u0026nbsp;2a, the very small weight loss in the thermal behavior of the CNT nanoparticles in the range of 25\u0026ndash;180\u0026deg;C can be related to water removal from the surface [\u003cspan citationid=\"CR21\" class=\"CitationRef\"\u003e21\u003c/span\u003e, \u003cspan citationid=\"CR22\" class=\"CitationRef\"\u003e22\u003c/span\u003e]. The weight loss at 300\u0026ndash;600\u0026deg;C, which is observed on the S-CNT graph, corresponds to the decomposition of 3-GPTMS on the CNT surface [\u003cspan citationid=\"CR23\" class=\"CitationRef\"\u003e23\u003c/span\u003e, \u003cspan citationid=\"CR24\" class=\"CitationRef\"\u003e24\u003c/span\u003e]. In the case of GO (Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003eb), the peak at 180\u0026deg;C may be related to the removal of physically absorbed water on the surface of GO. Concerning the S-GO, in addition to the abovementioned weight loss peak, a new weight loss region in the range of 350\u0026ndash;500\u0026deg;C also appeared due to the decomposition of the 3-GPTMS molecules [\u003cspan citationid=\"CR25\" class=\"CitationRef\"\u003e25\u003c/span\u003e, \u003cspan citationid=\"CR26\" class=\"CitationRef\"\u003e26\u003c/span\u003e].\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003eThe Energy-Dispersive X-ray spectra of silanized GO and CNTs are presented in Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e3\u003c/span\u003e. The presence of silicon atoms originating from the organosilane compound in the EDX spectra of silanized GO and CNTs proved that the 3-GPTMS molecules were successfully grafted on the surfaces of the GO and CNTs. As seen from the EDX results, compared with the CNT filler, the GO possesses an eligible silane density on its surface. Therefore, the extent of aggregation caused by the intramolecular hydrogen bonding-type interactions between surface hydroxyl groups is expected to be greater. Weight ratios of S-CNT and S-GO from EDX analysis are shown in Table\u0026nbsp;\u003cspan refid=\"Tab2\" class=\"InternalRef\"\u003e2\u003c/span\u003e.\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003e\u003cdiv class=\"gridtable\"\u003e\u003ctable float=\"Yes\" id=\"Tab2\" border=\"1\"\u003e\u003ccaption language=\"En\"\u003e\u003cdiv class=\"CaptionNumber\"\u003eTable 2\u003c/div\u003e\u003cdiv class=\"CaptionContent\"\u003e\u003cp\u003eWeight ratios of S-CNT and S-GO from EDX analysis\u003c/p\u003e\u003c/div\u003e\u003c/caption\u003e\u003ccolgroup cols=\"3\"\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c1\" colnum=\"1\"\u003e\u003c/div\u003e\u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c2\" colnum=\"2\"\u003e\u003c/div\u003e\u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c3\" colnum=\"3\"\u003e\u003c/div\u003e\u003cthead\u003e\u003ctr\u003e\u003cth align=\"left\" colname=\"c1\"\u003e\u0026nbsp;\u003c/th\u003e\u003cth align=\"left\" colname=\"c2\"\u003e\u003cp\u003eS-CNT\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c3\"\u003e\u003cp\u003eS-GO\u003c/p\u003e\u003c/th\u003e\u003c/tr\u003e\u003c/thead\u003e\u003ctbody\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eAtomic % of C\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e77.44\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e95.9\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eAtomic % of O\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e15.77\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e3.9\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003eAtomic % of Si\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e\u003cp\u003e6.79\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e\u003cp\u003e0.2\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003c/tbody\u003e\u003c/colgroup\u003e\u003c/table\u003e\u003c/div\u003e\u003c/p\u003e\u003cp\u003e\u003cb\u003eReaction mechanism\u003c/b\u003e\u003c/p\u003e\u003cp\u003eThe silanization reactions contain four steps including hydrolysis, condensation, hydrogen bonding, and bond formation. The R-O-CH3 groups of 3-GPTMS hydrolyze in acidic medium and the formed Si\u0026ndash;OH reacts with the -OH functional group on the surface of GO and CNTs. During the refluxing, a covalent bond is formed between (GO, CNTs and 3-GPTMS) with losing of water.\u003c/p\u003e\u003cp\u003eAfter dispersing the S-GO and S-CNTs in the epoxy resin, a chemical bonding forms between the functional groups of S-GO, S-CNTs nanofillers and epoxy matrix with functional groups of DMP-30 hardener. One end of the hardener reacts with epoxy matrix and another end of it react with the 3-GPTMS silane coupling agent. The molecular structure of 3-GPTMS is represented in Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e4\u003c/span\u003e. As can be seen, the 3-GPTMS has two active sides for chemical reaction, which made it a good choice for improvement of epoxy matrix in fiber reinforced composites.\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003e\u003cb\u003eCuring behavior\u003c/b\u003e\u003c/p\u003e\u003cp\u003eFigure \u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e5\u003c/span\u003e presents the results of the DSC experiments in nonisothermal mode for the epoxy/DICY nanocomposites with different contents of S-CNT, S-GO, and their hybrid and a constant amount of 0.6 phr DMP accelerator from 25 to 300\u0026deg;C at a 10\u0026deg;C min\u003csup\u003e\u0026minus;\u0026thinsp;1\u003c/sup\u003e heating rate.\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003eThe DSC data of the pure and all the nanocomposites are presented in Table\u0026nbsp;\u003cspan refid=\"Tab3\" class=\"InternalRef\"\u003e3\u003c/span\u003e. Compared with those of the pure sample, the maximum changes in the initial (T\u003csub\u003e0\u003c/sub\u003e) and peak (T\u003csub\u003epeak\u003c/sub\u003e) temperatures is 2\u0026deg;C. These results revealed that the incorporation of nanofillers has no significant effect on the curing behavior of the epoxy/DICY/nanofiller. This might be due to the solid nature of the DICY high temperature and latent curing agent.\u003c/p\u003e\u003cp\u003e\u003cdiv class=\"gridtable\"\u003e\u003ctable float=\"Yes\" id=\"Tab3\" border=\"1\"\u003e\u003ccaption language=\"En\"\u003e\u003cdiv class=\"CaptionNumber\"\u003eTable 3\u003c/div\u003e\u003cdiv class=\"CaptionContent\"\u003e\u003cp\u003eData from nonisothermal DSC thermograms at a heating rate of 10\u0026deg;C/min.\u003c/p\u003e\u003c/div\u003e\u003c/caption\u003e\u003ccolgroup cols=\"9\"\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c1\" colnum=\"1\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c2\" colnum=\"2\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c3\" colnum=\"3\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c4\" colnum=\"4\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c5\" colnum=\"5\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c6\" colnum=\"6\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c7\" colnum=\"7\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c8\" colnum=\"8\"\u003e\u003c/div\u003e\u003cdiv align=\"left\" class=\"colspec\" colname=\"c9\" colnum=\"9\"\u003e\u003c/div\u003e\u003cthead\u003e\u003ctr\u003e\u003cth align=\"left\" colname=\"c1\"\u003e\u003cp\u003eSample\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c2\"\u003e\u003cp\u003ePure\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c3\"\u003e\u003cp\u003eACNT0.5\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c4\"\u003e\u003cp\u003eS-CNT0.5\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c5\"\u003e\u003cp\u003eS-CNT3\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c6\"\u003e\u003cp\u003eAGO0.5\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c7\"\u003e\u003cp\u003eS-GO0.5\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c8\"\u003e\u003cp\u003eS-GO3\u003c/p\u003e\u003c/th\u003e\u003cth align=\"left\" colname=\"c9\"\u003e\u003cp\u003eS-GO-CNT0.5\u003c/p\u003e\u003c/th\u003e\u003c/tr\u003e\u003c/thead\u003e\u003ctbody\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003e\u003cb\u003eT\u003c/b\u003e\u003csub\u003e\u003cb\u003eO\u003c/b\u003e\u003c/sub\u003e, \u003cb\u003eᵒC\u003c/b\u003e\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c2\" morerows=\"2\" rowspan=\"3\"\u003e\u003cp\u003e128\u003c/p\u003e\u003cp\u003e145\u003c/p\u003e\u003cp\u003e462\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c3\" morerows=\"2\" rowspan=\"3\"\u003e\u003cp\u003e129\u003c/p\u003e\u003cp\u003e144\u003c/p\u003e\u003cp\u003e474\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c4\" morerows=\"2\" rowspan=\"3\"\u003e\u003cp\u003e128\u003c/p\u003e\u003cp\u003e144\u003c/p\u003e\u003cp\u003e476\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c5\" morerows=\"2\" rowspan=\"3\"\u003e\u003cp\u003e130\u003c/p\u003e\u003cp\u003e146\u003c/p\u003e\u003cp\u003e427\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c6\" morerows=\"2\" rowspan=\"3\"\u003e\u003cp\u003e127\u003c/p\u003e\u003cp\u003e145\u003c/p\u003e\u003cp\u003e463\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c7\" morerows=\"2\" rowspan=\"3\"\u003e\u003cp\u003e127\u003c/p\u003e\u003cp\u003e143\u003c/p\u003e\u003cp\u003e469\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c8\" morerows=\"2\" rowspan=\"3\"\u003e\u003cp\u003e127\u003c/p\u003e\u003cp\u003e144\u003c/p\u003e\u003cp\u003e469\u003c/p\u003e\u003c/td\u003e\u003ctd align=\"char\" char=\".\" colname=\"c9\" morerows=\"2\" rowspan=\"3\"\u003e\u003cp\u003e129\u003c/p\u003e\u003cp\u003e145\u003c/p\u003e\u003cp\u003e458\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003e\u003cb\u003eT\u003c/b\u003e\u003csub\u003e\u003cb\u003epeak\u003c/b\u003e\u003c/sub\u003e, \u003cb\u003eᵒC\u003c/b\u003e\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003ctr\u003e\u003ctd align=\"left\" colname=\"c1\"\u003e\u003cp\u003e\u003cb\u003eΔH (mJ/mg)\u003c/b\u003e\u003c/p\u003e\u003c/td\u003e\u003c/tr\u003e\u003c/tbody\u003e\u003c/colgroup\u003e\u003c/table\u003e\u003c/div\u003e\u003c/p\u003e\u003cp\u003e\u003cb\u003eMechanical properties\u003c/b\u003e\u003c/p\u003e\u003cp\u003eThe flexural, tensile, and shear properties of the epoxy/DICY/carbon fiber systems containing ACNT, AGO, S-CNTs, S-GO, and a hybrid of two nanoparticles were evaluated in the transverse direction of the fibers. The mechanical properties of composites in the transverse direction of fibers are controlled by the matrix, so these properties were measured in this direction. Typical transverse flexural stress-strain curves of carbon fiber/epoxy nanocomposites containing different amounts of S-CNT are presented in Fig.\u0026nbsp;\u003cspan refid=\"Fig5\" class=\"InternalRef\"\u003e6\u003c/span\u003e. Similar behavior was observed for S-GO samples. Figure\u0026nbsp;\u003cspan refid=\"Fig6\" class=\"InternalRef\"\u003e7\u003c/span\u003e displays the effects of silanization and hybrid nanoparticles on the tensile and flexural strengths of the ACNT/epoxy/DICY/CF and AGO/epoxy/DICY/CF composites. The tensile and flexural strengths of the S-CNT0.5/epoxy/DICY/CF composite are 18% and 27% greater than those of the neat ACNT0.5/epoxy/DICY/CF. This observation can be related to the enhanced matrix/fiber interaction due to S-CNT incorporation. In composites, the incongruity in the coefficient of thermal expansion (CTE) of the fiber and polymeric matrix caused residual stresses at the interface after the curing stage, which encouraged fiber/matrix debonding during mechanical testing [\u003cspan citationid=\"CR27\" class=\"CitationRef\"\u003e27\u003c/span\u003e, \u003cspan citationid=\"CR28\" class=\"CitationRef\"\u003e28\u003c/span\u003e]. In the presence of S-CNT in the matrix, the incongruity in the CTE between the CF and the matrix is reduced, which enhances the fiber/matrix bonding. On the other hand, the S-CNT nanofiller can convey a portion of the applied load, resulting in a reduction in the stress concentration on the CF. Therefore, the stress required for fiber breakage is increased. With further loading of S-CNT from 0.5 to 3 wt%, the tensile and flexural strengths decreased. In fact, at higher contents of S-CNT, agglomeration can occur, which acts as a stress concentration region within the matrix, resulting in reduced mechanical properties [\u003cspan citationid=\"CR29\" class=\"CitationRef\"\u003e29\u003c/span\u003e, \u003cspan citationid=\"CR30\" class=\"CitationRef\"\u003e30\u003c/span\u003e].\u003c/p\u003e\u003cp\u003eIn the epoxy/CF composites containing GO nanoplates, as shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig6\" class=\"InternalRef\"\u003e7\u003c/span\u003e, the tensile and flexural strengths of the 0.5 wt.% S-GO/epoxy/DICY/CF composite are 21% and 16% greater than those of the neat AGO0.5/epoxy/DICY/CF composite. With greater loadings of 0.5 wt.% S-GO, the tensile and flexural strengths considerably decrease. This may be related to the fact that at higher nanofiller contents, S-GO aggregates in the stress concentration region reduce the tensile and flexural strengths of the composites.\u003c/p\u003e\u003cp\u003eCompared with ACNT0.5, the incorporation of the hybrid of S-CNT-GO0.5 increases the flexural and tensile strengths by 39.6% and 26%, respectively. It can be concluded that the contact geometry between nanofillers changes from 0D point contact to 1D linear contact, which considerably enhances the contact surface area in hybrid nanofillers, resulting in improved mechanical properties [\u003cspan citationid=\"CR9\" class=\"CitationRef\"\u003e9\u003c/span\u003e]. In one hand, the creation of a dual-network of GO-CNT and multiphase structure and proper dispersion of nanofillers and the other hand their synergetic effect on dispersion reinforce the interface with the epoxy, caused maximize load transfer from epoxy to nanofillers.\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003eThe effects of silanization and hybrid nanoparticles on the transverse tensile and flexural moduli of the ACNT/epoxy/DICY/CF and AGO/epoxy/DICY/CF composites are shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig7\" class=\"InternalRef\"\u003e8\u003c/span\u003e. The tensile moduli of the S-CNT0.5- and S-GO0.5-filled epoxy/DICY/CF composites are 10% and 15% greater, respectively, than those of the nonfunctionalized samples. The mechanical properties of the matrix and matrix/fiber interactions improved because of the surface modification of the nanofillers with 3-GPTMS. In fact, the mobility of polymeric chains is restricted, which effectively enhances the interfacial interactions between fillers and the epoxy matrix. Moreover, approximately 34% and 39% increases in the flexural moduli of the 0.5 wt% S-CNT- and S-GO-filled samples, respectively, were observed.\u003c/p\u003e\u003cp\u003eThe tensile and flexural moduli of the hybrid S-CNT-GO-filled composites were enhanced by 31% and 45%, respectively, compared with those of the neat AGO0.5 composite.\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003e\u003cb\u003eMorphology\u003c/b\u003e\u003c/p\u003e\u003cp\u003eTo interpret the observed mechanical properties, the fracture surfaces of the composites for the tensile test were evaluated by scanning electron microscopy. Weak interfacial bonding between the CF and the epoxy matrix for neat composites containing ACNT and AGO was observed from the clean surface of the CF and CF-matrix debonding in the SEM micrograph (Fig.\u0026nbsp;\u003cspan refid=\"Fig8\" class=\"InternalRef\"\u003e9\u003c/span\u003ea, d). The good dispersion of S-CNT and S-GO in epoxy matrix results in S-CNT/epoxy and S-GO/epoxy matrix becoming progressively rough and making crack propagation more devious due to the crack deflection mechanism. Therefore, good adhesion between the CF and the epoxy matrix filled with S-CNT0.5 and S-GO0.5 is observable on the fracture surface of the composites (Fig.\u0026nbsp;\u003cspan refid=\"Fig8\" class=\"InternalRef\"\u003e9\u003c/span\u003e. b, e). The agglomerates of 3 wt% SCNT and SGO can be seen on the fracture surface of the composites (Fig.\u0026nbsp;\u003cspan refid=\"Fig7\" class=\"InternalRef\"\u003e8\u003c/span\u003e. c, f). These agglomerates act as stress concentration sites [\u003cspan citationid=\"CR31\" class=\"CitationRef\"\u003e31\u003c/span\u003e, \u003cspan citationid=\"CR32\" class=\"CitationRef\"\u003e32\u003c/span\u003e]. This observation confirms the reduced mechanical properties of the 3 wt% S-CNT- and S-GO-filled composite in comparison with those of the 0.5 wt% sample.\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003eAn SEM image of the fracture surface of the hybrid S-CNT-S-GO/epoxy/DICY/CF composite is presented in Fig.\u0026nbsp;\u003cspan refid=\"Fig9\" class=\"InternalRef\"\u003e10\u003c/span\u003e. As can be seen, the hybrid nanofillers improved the adhesion between the epoxy matrix and CF surface, resulting in enhanced matrix-fiber interfacial strength.\u003c/p\u003e\u003cp\u003e\u003c/p\u003e\u003cp\u003e\u003cb\u003eInterlaminar shear strength\u003c/b\u003e\u003c/p\u003e\u003cp\u003eShort beam shear testing (ASTM D2344) was conducted to measure the transverse interlaminar shear strength (ILSS) of each sample. The testing was carried out at room temperature. The ILSS results of the S-CNT/epoxy/DICY/CF, S-GO/epoxy/DICY/CF and S-CNT-GO0.5/epoxy/DICY/CF composites are presented in Fig.\u0026nbsp;\u003cspan refid=\"Fig10\" class=\"InternalRef\"\u003e11\u003c/span\u003e. Compared with those of the ACNT0.5 and AGO0.5 composites, the ILSS of the 0.5 wt.% S-CNT and S-GO filled composites were 18% and 10% greater, respectively. This observation may be due to the interlocking and stress transfer capability of S-CNT and S-GO at the interface of the carbon fibers and the epoxy matrix [\u003cspan citationid=\"CR33\" class=\"CitationRef\"\u003e33\u003c/span\u003e]. The highest transverse ILSS 6.2\u0026thinsp;\u0026plusmn;\u0026thinsp;0.6 MPa was observed for the 0.5 wt.% hybrids of S-CNT/S-GO because the better dispersion of the two nanofillers with different dimensions contained 1D CNTs and 2D GO in the epoxy. The ILSS is expected to increase because of the improvement in the matrix strength and fiber-matrix interface caused by nanofiller dispersion. A change in the thermal stability/residual stresses of the epoxy matrix creates pressure at the fiber surface, which results in strong adhesion between the fiber and the matrix [\u003cspan citationid=\"CR34\" class=\"CitationRef\"\u003e34\u003c/span\u003e]. The agglomeration of S-CNT and S-GO, beyond 0.5 wt.% loadings, causes stress concentration, which results in debonding of fibers from the matrix during loading and poor performance of the composite.\u003c/p\u003e\u003cp\u003e\u003c/p\u003e"},{"header":"Conclusion","content":"\u003cp\u003eThe silanization of CNTs and GO was done successfully, and the results of FTIR, TGA, and EDX analyses revealed that 3-GPTMS was grafted on the surface of the GO and CNT nanofillers. The effects of this modification on the transverse tensile, flexural, and ILSS properties of the epoxy/DICY/CF nanocomposites were evaluated. Tensile and flexural strengths of the 0.5 wt.% S-CNT-filled CF/DICY/epoxy composite were 18% and 27%, respectively, greater than those of the ACNT0.5/epoxy/DICY/CF composite. Compared with ACNT0.5, the nanocomposite containing the hybrid of S-CNT-GO0.5 presented 26% and 39.6% greater transverse tensile and flexural strengths, respectively. Compared with those of the control samples, the tensile moduli of the S-CNT0.5- and S-GO0.5-filled epoxy/DICY/CF composites were 10% and 15%, respectively, and the flexural moduli were 34% and 39% greater. The flexural modulus of the hybrid S-CNT-GO0.5-filled composites was enhanced by 31% and 45% compared with the S-CNT0.5 and S-GO0.5 samples, respectively. The good adhesion between the CF and the epoxy matrix filled with S-CNT0.5 and S-GO0.5 was observed on the fracture surface of the samples. Compared with those of the control composite, the transverse ILSS of 0.5 wt% S-CNT, S-GO, and their hybrid-filled composites were enhanced by 18%, 10%, and 25%, respectively.\u003c/p\u003e"},{"header":"Declarations","content":"\u003cp\u003e\u003cstrong\u003eFunding\u0026nbsp;\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThis research was funded by the Iran National Science Foundation, grant number 98020833.\u0026nbsp;\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eAuthor Contributions\u0026nbsp;\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eNahid Jamali:\u003c/strong\u003e conceptualization, formal analysis, investigation, data curation and writing– original draft. \u003cstrong\u003eMohammad Hosain Beheshty:\u003c/strong\u003e conceptualization, writing, review and editing, supervision, funding acquisition.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eDisclosure\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eGenerative AI has been used to improve the readability and language of this manuscript.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eConflicts of Interest\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThe authors declare no conflicts of interest.\u0026nbsp;\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eData Availability Statement\u0026nbsp;\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThe data that support the findings of this study are available from the corresponding author upon reasonable request.\u003c/p\u003e"},{"header":"References","content":"\u003col\u003e\u003cli\u003e\u003cspan\u003eEl-Aouni N, Dagdag O, Haldhar R et al (2024) One-pot synthesis of epoxy resin composite: thermal, rheological and Monte Carlo investigations. 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Polymers 13:4128\u003c/span\u003e\u003c/li\u003e\u003c/ol\u003e"}],"fulltextSource":"","fullText":"","funders":[],"hasAdminPriorityOnWorkflow":false,"hasManuscriptDocX":true,"hasOptedInToPreprint":true,"hasPassedJournalQc":"","hasAnyPriority":false,"hideJournal":true,"highlight":"","institution":"","isAcceptedByJournal":false,"isAuthorSuppliedPdf":false,"isDeskRejected":"","isHiddenFromSearch":false,"isInQc":false,"isInWorkflow":true,"isPdf":false,"isPdfUpToDate":true,"isWithdrawnOrRetracted":false,"journal":{"display":true,"email":"[email protected]","identity":"researchsquare","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":true,"externalIdentity":"","sideBox":"","snPcode":"","submissionUrl":"/submission","title":"Research Square","twitterHandle":"researchsquare","acdcEnabled":true,"dfaEnabled":false,"editorialSystem":"","reportingPortfolio":"","inReviewEnabled":false,"inReviewRevisionsEnabled":true},"keywords":"Carbon nanotubes, graphene oxide, carbon fiber, epoxy, silane","lastPublishedDoi":"10.21203/rs.3.rs-7164361/v1","lastPublishedDoiUrl":"https://doi.org/10.21203/rs.3.rs-7164361/v1","license":{"name":"CC BY 4.0","url":"https://creativecommons.org/licenses/by/4.0/"},"manuscriptAbstract":"\u003cp\u003eThis study was conducted to evaluate the effects of the silanization of multiwall carbon nanotube (CNT) and graphene oxide (GO) nanoplates and their hybrid on the mechanical properties of epoxy/dicyandiamide (DICY)/carbon fiber (CF) composites. The silanized CNT (S-CNT) and GO (S-GO) were synthesized by refluxing (3-glycidyloxypropyl) trimethoxysilane in 97% ethanol. The silane grafting on CNT and GO was characterized by Fourier transform infrared spectroscopy, energy-dispersive X-ray spectroscopy, and thermogravimetric analysis. The nanocomposites' transverse tensile, flexural, and interlaminar shear strength (ILSS) were characterized. The transverse tensile and flexural strengths of the S-CNT0.5/epoxy/DICY/CF composite were 18% and 27% greater than those of the neat composite. Moreover, enhancements of approximately 34% and 39% were observed in the flexural moduli of the 0.5 wt.% S-CNT and S-GO filled samples, respectively. The tensile and flexural moduli of CF nanocomposite containing the hybrid of S-CNT-GO0.5 was enhanced by 31% and 45%, respectively. The evaluation of the tensile fracture surface of the samples revealed that the incorporation of GO and S-GO improved the CF‒epoxy interfacial bonding. The transverse interlaminar shear strength of the 0.5wt% S-CNT, S-GO, and S-CNT-GO hybrid-filled composites were enhanced by 18%, 10%, and 25%, respectively.\u003c/p\u003e","manuscriptTitle":"Effects of silanization and hybrid nanofillers of multiwalled carbon nanotubes and graphene oxide on the mechanical properties of epoxy/dicyandiamide/carbon fiber composites","msid":"","msnumber":"","nonDraftVersions":[{"code":1,"date":"2025-08-28 17:47:32","doi":"10.21203/rs.3.rs-7164361/v1","editorialEvents":[{"type":"communityComments","content":0}],"status":"published","journal":{"display":true,"email":"[email protected]","identity":"researchsquare","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":true,"externalIdentity":"","sideBox":"","snPcode":"","submissionUrl":"/submission","title":"Research Square","twitterHandle":"researchsquare","acdcEnabled":true,"dfaEnabled":false,"editorialSystem":"","reportingPortfolio":"","inReviewEnabled":false,"inReviewRevisionsEnabled":true}}],"origin":"","ownerIdentity":"95296b1e-716f-434c-8f36-055d58ba33ea","owner":[],"postedDate":"August 28th, 2025","published":true,"recentEditorialEvents":[],"rejectedJournal":[],"revision":"","amendment":"","status":"posted","subjectAreas":[],"tags":[],"updatedAt":"2025-12-24T21:23:40+00:00","versionOfRecord":[],"versionCreatedAt":"2025-08-28 17:47:32","video":"","vorDoi":"","vorDoiUrl":"","workflowStages":[]},"version":"v1","identity":"rs-7164361","journalConfig":"researchsquare"},"__N_SSP":true},"page":"/article/[identity]/[[...version]]","query":{"redirect":"/article/rs-7164361","identity":"rs-7164361","version":["v1"]},"buildId":"8U1c8b4HqxoKbykW_rLl7","isFallback":false,"isExperimentalCompile":false,"dynamicIds":[84888],"gssp":true,"scriptLoader":[]}