{"paper_id":"302d5200-69e3-4d30-aa7a-9b8e1af7718a","body_text":"Study on Preparation and Mechanical Properties for Graphene Oxide/Epoxy Resins Adhesives | 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 Study on Preparation and Mechanical Properties for Graphene Oxide/Epoxy Resins Adhesives Xueyue Lyu, Baozheng Cui, Xinjia Yang, Dongyu Zhao This is a preprint; it has not been peer reviewed by a journal. https://doi.org/ 10.21203/rs.3.rs-6538480/v1 This work is licensed under a CC BY 4.0 License Status: Under Review Version 1 posted 5 You are reading this latest preprint version Abstract In this study, graphene oxide (GO) was synthesized via Hummer’s method and subsequently integrated into an epoxy resin (EP) matrix using two distinct dispersion approaches: ultrasonic and emulsification dispersion to develop high-performance GO/EP adhesives (GO/EP-AD). At GO loading of 2 wt%, the adhesives exhibited shear strength of 31.94 MPa, demonstrating a 56% enhancement over pure EP. The storage modulus ( E' ) of the GO/EP composites (GO/EP-SH) prepared by emulsion dispersion reached 1.718 GPa, the glass transition temperature ( T g ) is 127 ℃. Compared with that of ultrasonic dispersion, T g has increased by 4 ℃. The tensile strength (58.9 MPa), elastic modulus (1.928 GPa), and impact strength (8.27 kJ/m²) of the composites increased by 42%, 58%, and 92% respectively compared with pure EP. The above experimental results confirm that the introduction of GO can effectively construct a three-dimensional reinforcing network and simultaneously improve the thermal stability and mechanical properties of the EP matrix because of the interface strengthening mechanism. Epoxy resin Graphene oxide Adhesives Emulsion dispersion Thermal stability Mechanical properties Figures Figure 1 Figure 2 Figure 3 Figure 4 Figure 5 Figure 6 Figure 7 Figure 8 Figure 9 Figure 10 1. Introduction Epoxy resin (EP) is extensively used as an adhesive and polymer composite matrix in aerospace, electronics, construction, and packaging due to its exceptional adhesion, thermal stability, mechanical performance, and processability [1]. However, the growing demand for adhesives with enhanced durability and strength in industrial applications cannot be fully satisfied by unmodified EP [2,3]. Graphene oxide (GO), a two-dimensional nanomaterial derived from graphene through strong oxidation, possesses a layered structure modified by oxygen-containing functional groups. The abundant surface hydroxyl and epoxy groups endow GO with excellent hydrophilicity, dispersibility, and chemically tunable interfacial properties [4]. GO is a new type of two-dimensional nanomaterial with a unique oxygen-containing functional group-modified layered structure formed by graphene after undergoing strong oxidation treatment. Due to the abundance of hydroxyl groups, epoxy groups, and other oxygen-containing groups on the surface, graphene oxide possesses good hydrophilicity, dispersibility, and tunable interfacial properties. As a nanoscale filler, GO demonstrates significant potential for improving the mechanical and thermal properties of composites when incorporated into polymer matrices. GO exhibits exceptional mechanical characteristics, with a tensile strength exceeding 130 GPa, making it an effective reinforcement phase [5]. Furthermore, its high thermal conductivity enables substantial enhancement of composite thermal conductivity, which makes it an ideal choice for a variety of applications where efficient heat dissipation is required. However, the interlayer forces of GO tend to result in their uneven distribution in the matrix, hindering their industrial applications. This agglomeration induces localized stress concentration and deteriorates the composite's mechanical properties [6,7]. Additionally, weak interfacial bonding between GO and the EP matrix may restrict mechanical load transfer, compromising the overall composite performance [8]. In this study, a novel GO/EP adhesive was prepared with EP as the matrix and GO as the reinforcing phase GO was synthesized via Hummer's method, and hydroxyl, carboxyl and epoxy groups were introduced on its surface and edges. These functional groups facilitated interfacial interactions with the EP matrix, enhancing the composite's mechanical performance. In addition, we explored two dispersion methods, ultrasonic and emulsion dispersion, to optimize GO distribution within the EP matrix. The homogeneous dispersion of GO promoted the formation of a three-dimensional reinforcement network, consequently improving thermal stability and mechanical properties. To sum up, this study provides a new idea for preparation polymer-based composites with excellent bonding performance, thermal stability, and mechanical properties, promoting the wide application of EP adhesives. 2. Experimental Section 2.1 Materials Graphene was obtained from Qingdao Dongkai Graphite Co., Ltd in China. EP was produced by the Bluestar New Material Wuxi Resin Factory, and the Beijing Xiangshan Joint Additive Factory produced the polyamide resin 651 (PA651). H 2 SO 4 , NaNO 3 , and H 2 O 2 , all of which were of analytical pure grade, were sourced from Tianjin Fuyu Fine Chemical Co., Ltd. Aqueous solutions were prepared using distilled water. 2.2 Pretreatment of GO The graphene and concentrated H 2 SO 4 were mixed in a round-bottom flask at a mass ratio 1:50 under continuous stirring to achieve homogeneous dispersion. Subsequently, 10 g of KMnO 4 and 1.5 g of NaNO 3 were gradually added to the mixture, which was then kept in an ice-water bath with constant stirring for 2 h. The reaction system was then permitted to proceed at room temperature for 24 h. To terminate the reaction and eliminate residual KMnO 4 , an appropriate amount of H 2 O 2 was introduced into the mixture. The GO dispersion was thoroughly washed 3 times with anhydrous ethanol, followed by vacuum drying to obtain the final GO product. 2.3 Preparation of GO/EP adhesives Two equal masses of GO are placed into two different ethanol solution beakers for ultrasonic dispersion, and then add the solution to the EP matrix. The ethanol solution is removed through two-phase extraction to obtain GO/EP mixtures called A mix and B mix . A mix was ultrasonically treated at 40°C for 2 h, and B mix was emulsified in the emulsifying machine at 8000 r/min for 30 min. The curing agent polyamide 651 (PA651) was added to A mix and B mix , stirred for 10 min, and then degassed under vacuum for 30 min to remove bubbles generated during the mixing process. The resulting GO/EP adhesive was designated as GO/EP-AD. The GO/EP adhesive cured sheets were prepared by pouring the GO/EP-AD into a pre-treated polytetrafluoroethylene mold and curing it in stages (70°C for 2 h, 125°C for 2 h, 150°C for 1h) is named GO/EP-SH. 2.4 Characterization X-ray diffraction (XRD) measurements were conducted using a Japan D/MAX-IIIB diffractometer. Fourier Transform Infrared Spectroscopy (FT-IR) testing was carried out using an MB-100 spectrophotometer from Bomem, Canada, covering a spectral acquisition range of 4000 − 500 cm − 1 . A scanning electron microscopy (SEM) analysis was done using a FEI Sirion microscope from the Netherlands. The shear strength test was completed using the YHS-229WJ electronic universal tensile testing machine of Yihuan Instrument Technology (Shanghai) Co., Ltd., According to the GB/T 7124 − 2008 standard, lap joint specimens of aluminum sheets with the size of 100 mm × 25 mm × 1.6 mm were adopted, with the bonding length of 12.5 mm. And the morphology of the sheared section was analyzed by using the 9XB-PC metallographic microscope produced by Shanghai Optical Instrument. The material's thermal stability was analyzed using the Perkin Elmer TGA-7 thermogravimetric analyzer from the United States. The GO/EP-SH were cut into 50 mm × 7 mm × 2 mm specimens. The thermodynamic properties were tested using the DMS6100 dynamic thermomechanical analyzer manufactured by Seiko Instruments Inc. The tensile strength and elastic modulus were tested using the YHS-229WJ-500kN microcomputer-controlled universal material testing machine of Shanghai Yihuan Instrument Technology Co., Ltd. The GO/EP-SH were cut into specimens of 63.5 mm × 12.7 mm × 3 mm. The impact strength was tested using an XJU-2.75J cantilever-beam impact testing machine manufactured by Chengde Testing Machine Co., Ltd., China. 3. Results and Discussion 3.1 Characterization of GO/EP-SH Figure 2 (a) presents the XRD patterns of the samples. From the XRD curve of graphene, there is a diffraction peak with a smaller peak and larger peak width at 2θ = 26.1°, the (002) crystallographic characteristic diffraction peak of graphene. The diminished intensity of the diffraction peaks is due to the complete exfoliation of graphene during the synthesis process. In the diffraction curve of GO, there is a sharp diffraction peak at 2θ = 9.8°, the diffraction peak of GO (001) [9,10]. According to the Bragg equation, the interlayer spacing of graphene is 0.78 nm, where n is one and λ is the wavelength of X-rays GO from the Cu target of 1.54 Å. This result follows the grain spacing of 0.71–0.82 nm reported in the literature for GO [11]. This interlayer spacing results from introducing oxygen-containing groups, such as carboxyl groups, hydroxyl groups, etc., to the surface and edges of graphene during the oxidation process, increasing the interlayer distance between the layers of graphene sheets. The XRD curves of the GO/EP-SH with different mass fractions of GO are shown in Fig. 2 (b). The XRD curves of GO/EP-SH showed diffraction peaks with smaller peaks and larger peak widths at 2θ of 15° to 25°, exhibiting epoxy resin characteristic peaks. The characteristic diffraction peaks of GO at 2θ = 9.8° and graphene at 2θ = 26.1° do not appear in Fig. 2 (b), which is attributed to the fact that GO is neither reduced nor agglomerated during the curing process of GO/EP-SH but dispersed uniformly in the EP matrix. Figure 3 (a) shows the infrared spectra of GO, EP, and Graphene. The absorption peak at 3364.22 cm − 1 corresponds to the stretching vibration of N-H in amid and O-H in alcohol. The peak at 2928.41 cm − 1 is attributed to the stretching vibration of C-H in methylene. Peaks at 1607.98 cm − 1 and 1509.93 cm − 1 represent the stretching vibration of the carbon skeleton in the benzene ring. The absorption peak at 1462.05 cm − 1 is associated with the deformation vibration of C-H. At 1301.09 cm − 1 , the absorption peak indicates the deformation vibration of C-N. The peak at 1253.63 cm − 1 corresponds to the deformation vibration of aromatic ether. Peaks at 1180.85 cm − 1 and 1033.67 cm − 1 arise from the deformation vibration of aliphatic ether. Peaks at 827.01 cm − 1 represent characteristic absorption bands for the benzene ring's in-plane and out-of-plane deformation vibrations. From the graph, the disappearance of the epoxy group absorption peak at 910–920 cm − 1 indicates the ring-opening of epoxy groups and complete epoxy resin curing [12]. Figure 3 (b) shows the FT-IR absorption spectra of GO/EP-SH with different GO content. From this Fig., with the increase of GO content, the vibration peak of the characteristic functional group of the EP matrix shows a red shift phenomenon, which indicates the uniform dispersion of GO nanosheets in the EP matrix and the interfacial interaction between the oxygen-containing functional groups on the surface and the epoxy molecular chain. Figure 4 shows SEM micrographs of fracture surfaces of GO/EP-SH with different GO contents. The pure EP fractured surface (Fig. 4 (a)) displays smooth and highly oriented deformation lines, demonstrating typical characteristics of brittle fracture behavior. This feature suggests that rapid crack propagation during the tensile process is accompanied by easy propagation [13,14]. When the GO content is lower than 2wt%, as shown in Fig. 4 (b-j), GO has decent dispersibility in the EP matrix and forms excellent interfacial interaction. Compared with pure EP, the number of cracks increased significantly. When the GO content increases to 2wt%, as shown in Fig. 4 (k), the fracture surface becomes rough, a typical ductile fracture feature. The GO is uniformly dispersed in the EP matrix to form a strong interfacial effect [15]. It effectively enhanced the mechanical properties of the GO/EP-SH. With the continuous increase of the GO content, agglomeration phenomena occur in the EP matrix, as shown in Fig. 4 (l). When the agglomeration size of GO is too large, it not only fails to fill the voids in the EP matrix but also causes the reduction of mechanical properties due to its stress concentration. 3.2 Shear strength of GO/EP-AD In Fig. 5 , the shear strength of GO/EP-AD shows a trend of increasing first and then decreasing. The shear strength of pure EP is 20.42 MPa. With the increase of GO content, the shear strength of GO/EP-AD also rises. When the GO content reaches 2wt%, the shear strength reaches a maximum value of 31.94 MPa, increasing by 56% compared to pure EP. As the GO content continues to rise, the shear strength of GO/EP-AD begins to decrease. This is because the appropriate amount of GO addition can effectively reduce the exothermic heat and shrinkage in the curing process of EP, thus reducing the defects produced by the adhesives layer in the adhesives bonding process. It not only significantly improves the overall quality of the adhesive joints, but also improves the adhesive bond strength through the enhancement of interfacial bonding [16,17]. GO as a nano-filler can effectively bear the external stress and improve the compressive strength by hindering the crack propagation when the load reaches the critical value. When the bonded part bears the external load, the stress transfer effect of GO can effectively share the interfacial stress and further enhance the shear strength. However, when the GO content exceeds the optimal threshold, the system's viscosity rises significantly, causing insufficient interfacial bonding [18]. This will give rise to defects in the bonding process, trigger the phenomenon of stress concentration, and ultimately lower the shear strength of the adhesive. To investigate the influence of GO content on the fracture mechanism of GO/EP -AD, this study employed metallurgical microscopy to conduct morphological analysis on the shear cross-sections of bonded specimens with aluminum substrates. Figure 6 displays the metallurgical microstructure characteristics of GO/EP-AD with varying GO contents. As shown in Fig. 6 (a), the shear fracture interface of the pure EP adhesives presents a clear boundary between the substrate and the adhesives layer, and shows typical brittle fracture characteristics. The incorporation of GO filler (Fig. 6 (b,c)) induced a marked increase in fractured surfaces of GO/EP-AD compared to those of pure EP. With the continuous augmentation of GO content (Fig.s 6(d-k)), the density of the fracture surface increases, the fracture surface becomes rough, and the crack distribution is disorderly. This is because a strong interfacial force is constructed between GO and the EP matrix. As the GO content in the EP matrix increases, the chemical bonds formed at the two-phase interface also increase accordingly [19]. Therefore, compared with the pure EP, the GO/EP-AD can absorb further impact energy, withstand greater shear force, and enhance the bonding strength of the adhesives. When the GO content exceeds 2.0 wt% (Fig. 6 (l)), distinct GO agglomeration phenomena emerge in the EP matrix accompanied by the formation of numerous bubbles. This is attributed to the excessive GO content leading to uneven distribution within the matrix, with a significant increase in system viscosity hinders effective bubble expulsion during the bonding process. These factors collectively contribute to increased defects in the shear fracture surface, ultimately resulting in a decline in the material's shear strength. 3.3 Thermal Properties of GO/EP-SH Thermal stability is a key indicator for assessing a polymer's resistance to thermal degradation or aging. When the polymers are heated, they may undergo physical state modifications such as softening and melting and chemical changes such as hydrolysis, decomposition, degradation, cyclization, and cross-linking [20,21]. Figure 7 demonstrates the effect of GO content on the thermal degradation of GO/EP-SH. By observation, we can see that the decomposition of pure EP starts at about 280 ℃ and is finished by 650 ℃. It is worth noting that the degradation of the samples before the temperature reaches 250 ℃ is mainly due to the volatilization of water, the initial decomposition of small amounts of EP, and the volatilization of low-molecular-weight substances in EP. When the temperature ranges from 280 ℃ to 650 ℃, the decomposition of EP molecules becomes the main cause of thermal weight loss. At lower temperatures, the thermal degradation of the GO/EP-SH exhibits minimal variation, with a lower thermal degradation mass loss compared to pure EP. However, as the temperature continues to rise, under identical decomposition temperatures, the residual amount of the GO/EP-SH after thermal decomposition becomes significantly lower than that of pure EP. Moreover, higher GO content correlates with reduced residual quantities. The reason for this phenomenon lies in the fact that the thermal decomposition temperature of the GO/EP-SH is lower than that of pure EP [22]. Therefore, under high-temperature conditions, when the masses of the two are the same, the GO/EP-SH absorb relatively less heat, eventually causing a more significant mass loss. Dynamic mechanical analysis (DMA) refers to the mechanical properties of polymers and their variation with temperature at a fixed frequency. The energy stored during the elastic deformation of a material is called the energy storage modulus ( E' ), a higher value of which indicates a more rigid material, the percentage of energy loss is expressed by the ratio of the loss modulus to the energy storage modulus ( tanδ ) [23,24]. The E'-T curves of GO/EP-SH with varying GO contents are presented in Fig. 8 (a). It can be observed from Fig. 8 (a) that the E' of the GO/EP-SH demonstrates a progressive enhancement with increasing GO content in the lower temperature region. This enhancement is ascribed to the hydroxyl and epoxy group functionalities on GO surfaces, which undergo crosslinking reactions with the EP matrix during processing. The formed covalent bonding network strengthens the GO and EP interfacial adhesion, thereby directly increasing the storage modulus through effective stress transfer mechanisms. When the temperature reached 40°C, the E' of the 2.0 wt% GO/EP-SH was 1.718 GPa, an increase of 45% compared to pure EP (950 MPa). As the temperature continued to increase, the E' value displayed a gradual downward trend, demonstrating the transition of the GO/EP-SH from the glassy state to the rubbery state. Furthermore, the interfacial interactions between GO and the EP matrix enable effective stress transfer from the polymer matrix to the rigid GO nanosheets [25]. This reinforcement mechanism significantly enhances the resistance to deformation in the GO/EP-SH. The maximum value of tanδ corresponds to the glass transition temperature ( T g ). The tanδ-T curves of GO/EP with varying GO contents are presented in Fig. 8 (b). The experimental data indicate that the energy loss of GO/EP-SH starts to show at 73°C when the GO addition is 0.5 wt%, and the onset temperature of this loss shows a significant high-temperature shift trend with the increase of GO content. The peak of tanδ continuously shifts towards higher temperatures with increasing GO content. The T g of pure EP is 106 ℃, compared with pure EP, the T g of 2.0 wt% GO/EP-SH is 127 ℃, which has increased by 21 ℃. This phenomenon can be attributed to two synergistic mechanisms. The abundant active group on GO surfaces forms strong chemical bonds with the EP matrix, establishing a stable chemical crosslinking network [26,27]. As rigid nanofillers in the polymer system, GO induces physical crosslinking effects through its lamellar structure that restricts polymer chain segment movement via steric hindrance effects. With the increase of GO content, the cross-linking density of the system increases, leading to a decrease in free volume and the mobility of the chain segments, and ultimately, the enhancement of T g is achieved [28]. The results of this study confirm that the introduction of GO can effectively improve the thermal stability of the EP matrix. Figure 9 displays the tanδ-T curves of GO/EP-SH with different dispersion processes. The tanδ peak of the GO/EP-SH containing 2wt% GO in the emulsification dispersion process appears at 127 ℃. In contrast, the tanδ peak of the sample prepared by ultrasonic dispersion appears at 123 ℃. The increase in T g indicates that the emulsification dispersion can enable GO to be effectively and uniformly distributed in the EP matrix. During the dispersion process, oxygen-containing functional groups on the surface of GO nanosheets undergo interfacial chemical interactions with epoxy molecular chains, forming a stable three-dimensional crosslinked network structure. The uniformly dispersed GO nanosheets become embedded within the intermolecular spaces of epoxy chains, where their steric hindrance effect significantly suppresses the thermal motion of polymer segments thereby enhancing the mechanical properties of the GO/EP-SH [29]. In contrast, ultrasonic dispersion demonstrates inferior dispersion efficacy, as evidenced by the stacking phenomena of GO nanosheets. These structural defects hinder sufficient crosslinking between the epoxy resin and curing agents, resulting in reduced crosslinking network density and, consequently, constrained performance enhancement of the composite. 3.4 Mechanical Properties of GO/EP-SH When subjected to externally applied stress, crazes initially form within the composite material. With continued application of the stress load, these crazes gradually evolve into cracks. After the graphene is oxidized, the functional groups on its surface can interact with the functional groups on the EP molecular chain, forming connection nodes and a three-dimensional network, which can effectively disperse stress, consume the fracture energy, and inhibit the further expansion of cracks, thereby improving the mechanical properties of the composite material [30–32]. Figure 10 (a-c) shows the tensile strength, elastic modulus and impact strength of GO/EP-SH with different GO contents. The Fig. shows that the mechanical properties of the GO/EP-SH prepared by emulsification dispersion are always higher than those prepared by ultrasonic dispersion, indicating that compared with ultrasonic dispersion, emulsification dispersion can disperse GO more uniformly in the EP matrix and significantly improve the mechanical properties of GO/EP-SH. The tensile strength and elastic modulus are key mechanical parameters that characterize a material's ability to resist external forces and deformation [33]. As shown in Fig. 10 (a, b) the tensile strength and elastic modulus of pure EP are 34 MPa and 8.07 GPa, respectively. With the increase of GO content, the mechanical properties of GO/EP-SH have been significantly improved. When the GO content reaches 2.0 wt%, the tensile strength and elastic modulus of the GO/EP-SH rise to 58.9 MPa and 1.928 GPa, respectively, representing 42% and 58% enhancements compared to pure EP. This enhancement effect is mainly attributed to the effectiveness of the emulsification dispersion process. The network structure formed by the uniformly dispersed GO in the EP matrix effectively enhances the mechanical properties of the GO/EP-SH [34]. As shown in Fig.s 10(c), the impact strength of GO/EP-SH also exhibited a trend of first increasing and then decreasing. When the GO content reached 2.0 wt%, the impact strength achieved maximum values of 8.27 kJ/m², representing 92% enhancements compared to pure EP. When the material is subjected to external forces, the strong interfacial bonding between GO and the EP matrix enabled effective energy transfer through the interface to GO layers, inducing localized yielding and deformation of the matrix that effectively absorbed impact energy. When the GO content exceeds 2.0 wt%, the reduced interlayer spacing of GO nanosheets induces GO agglomeration within the EP matrix. The microcracks generated under the stress expand and eventually form a macroscopic crack network, resulting in the decline of mechanical properties. 4. Conclusion In this study, GO was synthesized via Hummer’s method, GO/EP-SH adhesives were fabricated by incorporating GO into the epoxy matrix by ultrasonic and emulsification dispersion methodologies. The results showed that when the GO content reaches 2wt%, the shear strength of the GO/EP-AD 31.94 MPa, which is 56% higher than that of pure EP. At the same thermal degradation temperature, the thermal degradation rate of GO/EP-SH is higher than that of pure EP, and the higher the GO content, the more significant the thermal degradation. The GO/EP-SH exhibited a glass transition temperature ( T g ) of 127°C at 2 wt% GO loading, demonstrating a 22°C elevation compared to the pure EP matrix. When the temperature reached 40°C, the storage modulus ( E' ) of the GO/EP-SH reached 1.718 GPa, increasing by 45% compared with 950 MPa of pure EP. By comparing the two dispersion processes, it was found that the T g value of the sample prepared by the emulsification dispersion method was 4 ℃ higher than that of the sample prepared by the ultrasonic dispersion, which indicated that emulsion dispersion could better disperse GO uniformly in the EP matrix. The tensile strength of the GO/EP-SH loaded with 2 wt% GO was 58.9 MPa, the modulus of elasticity was 1.928 GPa, and the impact strength was 8.27 kJ/m². These values increased by 42, 58, and 92%, respectively, compared with pure EP. Declarations Acknowledgments This work is supported by the National Natural Science Foundation of China (No.51772061). Funding Access funding enabled by the National Natural Science Foundation of China. Declaration of interest statement The authors have no relevant financial or non-financial interests to disclose. Authors contribution Xueyue Lyu: Investigation, Software, Data curation, Writing–original draft. Baozheng Cui: material preparation. Xinjia Yang:Analyzing data, Writing. Dongyu Zhao: Methodology, Writing–review & editing. Data availability The data that support the findings of this study are available from the corresponding author upon. References Chu XC, Wang GQ, Ding QJ, Zhao G, Li HF (2023) Molecular dynamics simulation of epoxy resin modified by polyimide grafted graphene oxide. Polym. Eng. Sci. 63(11): 3798-3808. https://doi.org/10.1002/pen.26485. Hou WX, Gao Y, Wang J, Blackwood DJ, Teo S (2020) Recent advances and future perspectives for graphene oxide reinforced epoxy resins. Mater. Today Commun. 23: 100883. https://doi.org/10.1016/j.mtcomm.2019.100883. Chen J, Kinloch AJ, Sprenger S, Taylor AC (2022) The mechanical properties and toughening mechanisms of an epoxy polymer modified with polysiloxane-based core-shell particles. Polym. 54(16): 4276-4289. https://doi.org/10.1016/j.polymer.2013.06.009. Biranje PM, Patwardhan AW, Joshi JB, Dasgupta K (2022) Exfoliated graphene and its derivatives from liquid phase and their role in performance enhancement of epoxy matrix composite. Composites, Part A. 156: 106886. https://doi.org/10.1016/j.compositesa.2022.106886. Nuncira J, Seara LM, Sinisterra RD, Caliman V, Silva GG (2019) Long-term colloidal stability of graphene oxide aqueous nanofluids. Fullerenes, Nanotubes Carbon Nanostruct. 28(5): 407-417. https://doi.org/10.1080/1536383X.2019. 1695250. Amirbeygi H, Khosravi H, Tohidlou E (2019) Reinforcing effects of aminosilane-functionalized graphene on the tribological and mechanical behaviors of epoxy nanocomposites. J. Appl. Polym. Sci. 136: 18. https://doi.org/10.1002/app.47410. Hu CX, Zhang HN, Neate N, Hou XH, Grant D, Xu F (2022) Highly Aligned Ni-Decorated GO-CNT Nanostructures in Epoxy with Enhanced Thermal and Electrical Properties. Polym. 14: 13. https://doi.org/10.3390/polym14132583. Liu L, Liang S, Zheng CS, Wang DP (2023) Preparation and interfacial properties of functionalised graphene oxide modified carbon fibre/epoxy resin matrix composites. Plast., Rubber Compos. 52(6): 346-355. https://doi.org/10.1080/ 14658011. 2023.2207059. Wang N, Gao HY, Zhang J, Qin Y, Wang DY (2019) Phytic Acid Intercalated Graphene Oxide for Anticorrosive Reinforcement of Waterborne Epoxy Resin Coating. Polym. 11: 12. https://doi.org/10.3390/polym11121950. Azimi R, Roghani-Mamaqani H, Gholipour-Mahmoudalilou M (2017) Grafting poly (amidoamine) dendrimer-modified silica nanoparticles to graphene oxide for preparation of a composite and curing agent for epoxy resin. Polym. 126: 152-161. https://doi.org/10.1016/j.polymer.2017.08.037. Yuan M, Zhang Y, Xie F, Yang H, Bittencourt C, Snyders R, Li WJ (2025) Nano copper-modified GO and CNTs for enhanced the epoxy resin composite thermal properties. Appl. Surf. Sci. 690:162616. https://doi.org/10.1016/j.apsusc.2025. 162616. Xu H, Zhang XR, Hu GK, Weng L, Liu LH (2020) High thermal conductivity EP adhesive based on the GO/EP interface optimized by TDI. Polym. Adv. Technol. 31(6):1356-1364. https://doi.org/10.1002/pat.4865. Chen L, Chen WS, Li BH (2023) Investigation of shape memory and heat transfer properties of graphene oxide reinforced shape memory epoxy resin composites. Mater. Today Commun. 34: 105170. https://doi.org/10.1016/j. mtcomm.2022.105170. Fang F, Song PG, Ran SY, Guo ZH, Wang H, Fang ZP (2018) A facile way to prepare phosphorus-nitrogen-functionalized graphene oxide for enhancing the flame retardancy of epoxy resin. Adhes. Commun. 10:97-102. https://doi.org/10.1016/j.coco.2018.08.001. Yang XJ, Song KR, Zhao DY (2024) Preparation and mechanical properties of Ni/RGO reinforced epoxy resin composites. High Perform. Polym. 36(3): 163-172. https://doi.org/10.1177/09540083231225284. Beggs KM, Servinis L, Gengenbach TR, Huson MG, Fox BL (2015) Henderson, L.C. A systematic study of carbon fibre surface grafting via in situ diazonium generation for improved interfacial shear strength in epoxy matrix composites. Compos. Sci. Technol. 118: 31-38. https://doi.org/10.1016/j.compscitech. 2015.08.001. Reis Taiza, MC, Castro VG (2023) Amurin, L.G.; Silva, G.G. Graphene oxide dispersion in epoxy resin prepared by direct phase transfer from ethanol: Rheology and aging. Compos. Part C: Open Access. 10: 100340, https://doi.org/10.1016/j.jcomc.2022.100340. Liu ZJ, Wang D Cheng QK, Wang JP, Sun HT (2024) Outstanding interlaminar strength of carbon fiber reinforced epoxy resin via graphene oxide chemical bridge bonding. Appl. Surf. Sci. 670: https://doi.org/10.1016/j.apsusc.2024. 160658. Guo SY, Lu Y, Wan XM, Wu F, Zhao TJ, Shen Cn (2020) Preparation, characterization of highly dispersed reduced graphene oxide/epoxy resin and its application in alkali-activated slag composites. Cem. Concr. Compos. 105: https://doi.org/10.1016/j.cemconcomp.2019.103424. Fu BJ, Wang Y, Ding WY, Tian JF, Han ST (2024) Simultaneous improvement of mechanical, adhesive and ablative properties of phenolic epoxy modified PDMS. Polymer. 311: 127522. https://doi.org/10.1016/j.polymer.2024.127522. Chen J, Yao BW, Li C, Shi GQ (2013) An improved Hummers method for eco-friendly synthesis of graphene oxide. Carbon. 64: 225-229. https://doi.org/10.1016/j.carbon. 2013.07.055. Yang W, Wang NN, Ping P, Yuen AC, Li A, Zhu SE, Wang LL (2018) Novel 3D Network Architectured Hybrid Aerogel Comprising Epoxy, Graphene, and Hydroxylated Boron Nitride Nanosheets. ACS Appl. Mater. Interfaces. 10(46): 40032-40043. https://doi.org/10.1021/acsami.8b15301. Xiao WW, Liu Y, Guo SW (2016) Composites of graphene oxide and epoxy resin assuming a uniform 3D graphene oxide network structure. RSC Adv. 6(90): 86904-86908. https://doi.org/10.1039/c6ra16335a. Lavoratti A, Zattera AJ, Amico SC (2021) Effect of carbonaceous nanofillers and triblock copolymers on the toughness of epoxy resin. Polym. Bull. 78(10): 5467-5480. https://doi.org/10.1007/s00289-020-03375-1. Ghanbaralizadeh R, Bouhendi H, Kabiri K, Vafayan M (2016) A novel method for toughening epoxy resin through CO 2 fixation reaction. J. CO2 Util. 16: 225-235. https://doi.org/10.1016/j.jcou.2016.06.006. Bortz DR, Heras E, Martin-Gullon I (2012) Impressive Fatigue Life and Fracture Toughness Improvements in Graphene Oxide/Epoxy Composites. Macromol. 45(1): 238-245. https://doi.org/10.1021/ma201563k. Kim J, Yim BS, Kim JM, Kim J (2012) The effects of functionalized graphene nanosheets on the thermal and mechanical properties of epoxy composites for anisotropic conductive adhesives (ACAs). Microelectron. Reliab. 52(3): 595-602. https://doi.org/10.1016/j.microrel.2011.11.002. Liang X, Li XJ, Tang Y, Zhang XY, Wei W, Liu XY (2022) Hyperbranched epoxy resin-grafted graphene oxide for efficient and all-purpose epoxy resin modification. J. Colloid Interface Sci. 611: 105-117. https://doi.org/10.1016/j.jcis. 2021.12.068. Zhang JX, Liang YX, Wang XJ, Zhou HJ, Li SY, Zhang J, Feng YN, Lu N, Wang Q, Guo ZH (2018) Strengthened epoxy resin with hyperbranched polyamine-ester anchored graphene oxide via novel phase transfer approach. Adv. Compos. Hybrid Mater. 1(2): 300-309. https://doi.org/10.1007/s42114-017-0007-0. Chandrasekaran S, Sato N, Tolle F, Mulhaupt R, Fiedler B, Schulte K (2014) Fracture toughness and failure mechanism of graphene-based epoxy composites. Compos. Sci. Technol. 97: 90-99. https://doi.org/10.1016/j.compscitech. Lu C, Lin FB, Shao HQ, Chen NL, Shao GW, Jiang JH (2022) Carboxylated Carbon Nanotube/Polyimide Films with Low Thermal Expansion Coefficient and Excellent Mechanical Properties. Polym. 14: 21. https://doi.org/10.3390/polym 14214565. Bao CL, Guo YQ, Song L, Kan YC, Qian XD, Hu Y (2011) In situ preparation of functionalized graphene oxide/epoxy nanocomposites with effective reinforcements. J. Mater. Chem. 21(35): 13290-13298. https://doi.org/10.1039/ c1jm11434d. Lv XY, Wu SB, Zhao DY (2024) Preparation and Performance of MWNTs/ Epoxy Resins Composites. J. Inorg. Organomet. Polym. Mater. 34(10): 4558-4567. https://doi.org/10.1007/s10904-024-03122-3. Zhao XR, Li Y, Chen W, Li S, Zhao Y, Du SY (2019) Improved fracture toughness of epoxy resin reinforced with polyamide 6/graphene oxide nanocomposites prepared via in situ polymerization. Compos. Sci. Technol. 171: 180-189. https://doi.org/10.1016/j.compscitech.2018.12.023. Cite Share Download PDF Status: Under Review Version 1 posted Reviewers agreed at journal 06 May, 2025 Reviewers invited by journal 06 May, 2025 Editor invited by journal 01 May, 2025 Editor assigned by journal 28 Apr, 2025 First submitted to journal 27 Apr, 2025 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-6538480\",\"acceptedTermsAndConditions\":true,\"allowDirectSubmit\":false,\"archivedVersions\":[],\"articleType\":\"Research Article\",\"associatedPublications\":[],\"authors\":[{\"id\":452399316,\"identity\":\"19bd53df-3ed1-45da-b69e-a64ea66551df\",\"order_by\":0,\"name\":\"Xueyue Lyu\",\"email\":\"\",\"orcid\":\"\",\"institution\":\"\",\"correspondingAuthor\":false,\"prefix\":\"\",\"firstName\":\"Xueyue\",\"middleName\":\"\",\"lastName\":\"Lyu\",\"suffix\":\"\"},{\"id\":452399317,\"identity\":\"46cd7e70-379f-4d30-8e31-56ca4e7ad1fb\",\"order_by\":1,\"name\":\"Baozheng Cui\",\"email\":\"\",\"orcid\":\"\",\"institution\":\"\",\"correspondingAuthor\":false,\"prefix\":\"\",\"firstName\":\"Baozheng\",\"middleName\":\"\",\"lastName\":\"Cui\",\"suffix\":\"\"},{\"id\":452399318,\"identity\":\"80005ce5-4764-4a08-a15c-ec20e2669401\",\"order_by\":2,\"name\":\"Xinjia Yang\",\"email\":\"\",\"orcid\":\"\",\"institution\":\"\",\"correspondingAuthor\":false,\"prefix\":\"\",\"firstName\":\"Xinjia\",\"middleName\":\"\",\"lastName\":\"Yang\",\"suffix\":\"\"},{\"id\":452399319,\"identity\":\"c4190c13-031d-4d5d-a330-cd57c92c151d\",\"order_by\":3,\"name\":\"Dongyu Zhao\",\"email\":\"data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAZAAAAAyAQMAAABI0h/eAAAABlBMVEX///8AAABVwtN+AAAACXBIWXMAAA7EAAAOxAGVKw4bAAAA2klEQVRIiWNgGAWjYDACCSDmYWCQM2BnSAAymYnXYmzATKqWxA0QxURokZ/d/PDB27bD6duZGZ5JMFRYJzawnz2AVwvjnGPGhnPbDufubGZIk2A4k57YwJOXgFcLs0SCmTQvUMuGw0AtjG2HExskeAzwamGTSP8G0pJuANbyjwgtPBI5YFsSIFoaiNAiIZFTbDjnXLoh0GHJFgnH0o3beHLwa5Gfkb7xwZsya3mD4z2JNz7UWMv2s5/BrwUMGNnAbkwARyYbYfUg8AdEsB8gTvEoGAWjYBSMOAAAMKlA1MraiN4AAAAASUVORK5CYII=\",\"orcid\":\"\",\"institution\":\"Heilongjiang University\",\"correspondingAuthor\":true,\"prefix\":\"\",\"firstName\":\"Dongyu\",\"middleName\":\"\",\"lastName\":\"Zhao\",\"suffix\":\"\"}],\"badges\":[],\"createdAt\":\"2025-04-27 06:47:07\",\"currentVersionCode\":1,\"declarations\":\"\",\"doi\":\"10.21203/rs.3.rs-6538480/v1\",\"doiUrl\":\"https://doi.org/10.21203/rs.3.rs-6538480/v1\",\"draftVersion\":[],\"editorialEvents\":[],\"editorialNote\":\"\",\"failedWorkflow\":false,\"files\":[{\"id\":82387303,\"identity\":\"6711d101-8478-4995-aadf-e308d1b9bd9b\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 16:54:19\",\"extension\":\"png\",\"order_by\":1,\"title\":\"Figure 1\",\"display\":\"\",\"copyAsset\":false,\"role\":\"figure\",\"size\":284443,\"visible\":true,\"origin\":\"\",\"legend\":\"\\u003cp\\u003eSchematic showing synthesis routes of GO/EP-SH.\\u003c/p\\u003e\",\"description\":\"\",\"filename\":\"image1.png\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/e478bc3e0484b6692c91757b.png\"},{\"id\":82386700,\"identity\":\"61754559-b8ba-48e8-a946-8e3dd2918d69\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 16:46:20\",\"extension\":\"png\",\"order_by\":2,\"title\":\"Figure 2\",\"display\":\"\",\"copyAsset\":false,\"role\":\"figure\",\"size\":339245,\"visible\":true,\"origin\":\"\",\"legend\":\"\\u003cp\\u003eXRD of (a) GO, EP, Graphene, and (b) GO/EP-SH with different GO content.\\u003c/p\\u003e\",\"description\":\"\",\"filename\":\"image2.png\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/d4130a4cbe59dc245f5ca5df.png\"},{\"id\":82386691,\"identity\":\"d2898421-6264-4075-bb05-2d1d39757fe6\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 16:46:19\",\"extension\":\"png\",\"order_by\":3,\"title\":\"Figure 3\",\"display\":\"\",\"copyAsset\":false,\"role\":\"figure\",\"size\":393644,\"visible\":true,\"origin\":\"\",\"legend\":\"\\u003cp\\u003eFT-IR spectra of the (a) GO, EP, Graphene, and (b) GO/EP-SH with different GO content.\\u003c/p\\u003e\",\"description\":\"\",\"filename\":\"image3.png\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/9a1e5fac655a2dd6a1711a64.png\"},{\"id\":82386688,\"identity\":\"508ada5e-75d7-4fd7-88cd-4bef33136a7c\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 16:46:19\",\"extension\":\"png\",\"order_by\":4,\"title\":\"Figure 4\",\"display\":\"\",\"copyAsset\":false,\"role\":\"figure\",\"size\":779792,\"visible\":true,\"origin\":\"\",\"legend\":\"\\u003cp\\u003eSEM images of the (a) EP and GO/EP-SH composites with (b) 0.2 wt%, (c) 0.4 wt%, (d) 0.6 wt%, (e) 0.8 wt%, (f) 1.0 wt%, (g) 1.2 wt%, (h) 1.4 wt%, (i) 1.6 wt%, (j) 1.8 wt%, (k) 2.0 wt%, (l) 2.2 wt% GO.\\u003c/p\\u003e\",\"description\":\"\",\"filename\":\"image4.png\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/3fc8dbb10c3e640edd0f0902.png\"},{\"id\":82386689,\"identity\":\"b5d43c3a-94c6-4534-8fc5-9267d513aba5\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 16:46:19\",\"extension\":\"png\",\"order_by\":5,\"title\":\"Figure 5\",\"display\":\"\",\"copyAsset\":false,\"role\":\"figure\",\"size\":27774,\"visible\":true,\"origin\":\"\",\"legend\":\"\\u003cp\\u003eShear strength test of GO/EP-AD.\\u003c/p\\u003e\",\"description\":\"\",\"filename\":\"image5.png\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/bf1f2a0a57146a74c5729e66.png\"},{\"id\":82387650,\"identity\":\"331e01a8-442b-4754-95d8-735eb7abc09d\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 17:02:19\",\"extension\":\"png\",\"order_by\":6,\"title\":\"Figure 6\",\"display\":\"\",\"copyAsset\":false,\"role\":\"figure\",\"size\":1203647,\"visible\":true,\"origin\":\"\",\"legend\":\"\\u003cp\\u003eMetallographic microscopy pictures of the (a) EP and GO/EP-AD with (b) 0.2 wt%, (c) 0.4 wt%, (d) 0.6 wt%, (e) 0.8 wt%, (f) 1.0 wt%, (g) 1.2 wt%, (h) 1.4 wt%, (i) 1.6 wt%, (j) 1.8 wt%, (k) 2.0 wt%, (l) 2.2 wt% GO.\\u003c/p\\u003e\",\"description\":\"\",\"filename\":\"image6.png\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/51654a4aed90dec3be4a1100.png\"},{\"id\":82386695,\"identity\":\"1d4851d1-f5d6-4ade-888f-2f97c9d85a5f\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 16:46:19\",\"extension\":\"png\",\"order_by\":7,\"title\":\"Figure 7\",\"display\":\"\",\"copyAsset\":false,\"role\":\"figure\",\"size\":178474,\"visible\":true,\"origin\":\"\",\"legend\":\"\\u003cp\\u003eEffect of GO content on thermal degradationof GO/EP-SH.\\u003c/p\\u003e\",\"description\":\"\",\"filename\":\"image7.png\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/dc9dfa053b64a992a9a365f8.png\"},{\"id\":82387304,\"identity\":\"a7b495fc-7697-4abb-864c-5270843b96e5\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 16:54:19\",\"extension\":\"png\",\"order_by\":8,\"title\":\"Figure 8\",\"display\":\"\",\"copyAsset\":false,\"role\":\"figure\",\"size\":176167,\"visible\":true,\"origin\":\"\",\"legend\":\"\\u003cp\\u003eEffect of GO content on (a) \\u003cem\\u003eE'\\u003c/em\\u003e and (b) \\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003e\\u003cem\\u003eg\\u003c/em\\u003e\\u003c/sub\\u003e of GO/EP-SH.\\u003c/p\\u003e\",\"description\":\"\",\"filename\":\"image8.png\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/5262df5f0509dffefecd8640.png\"},{\"id\":82386693,\"identity\":\"2cd5139d-954d-47f3-b7a8-55b401947758\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 16:46:19\",\"extension\":\"jpeg\",\"order_by\":9,\"title\":\"Figure 9\",\"display\":\"\",\"copyAsset\":false,\"role\":\"figure\",\"size\":66471,\"visible\":true,\"origin\":\"\",\"legend\":\"\\u003cp\\u003eEffect of the dispersion process on the \\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003e\\u003cem\\u003eg\\u003c/em\\u003e\\u003c/sub\\u003e of the GO/EP-SH.\\u003c/p\\u003e\",\"description\":\"\",\"filename\":\"image9.jpeg\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/4ad4294749b2f44245b96d4a.jpeg\"},{\"id\":82387307,\"identity\":\"d8802770-d93e-48bc-a02a-3169eeb9a8d5\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 16:54:20\",\"extension\":\"png\",\"order_by\":10,\"title\":\"Figure 10\",\"display\":\"\",\"copyAsset\":false,\"role\":\"figure\",\"size\":219697,\"visible\":true,\"origin\":\"\",\"legend\":\"\\u003cp\\u003e(a) Tensile strength, (b) Elastic modulus, and (c) Impact strength of the GO/EP-SH with different GO content.\\u003c/p\\u003e\",\"description\":\"\",\"filename\":\"image10.png\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/09825eff956a84dee56572ad.png\"},{\"id\":82388081,\"identity\":\"f3fa1ef3-e38d-43e1-b0f3-a988d1cb76b2\",\"added_by\":\"auto\",\"created_at\":\"2025-05-09 17:10:22\",\"extension\":\"pdf\",\"order_by\":0,\"title\":\"\",\"display\":\"\",\"copyAsset\":false,\"role\":\"manuscript-pdf\",\"size\":4755953,\"visible\":true,\"origin\":\"\",\"legend\":\"\",\"description\":\"\",\"filename\":\"manuscript.pdf\",\"url\":\"https://assets-eu.researchsquare.com/files/rs-6538480/v1/8c0acb22-7fba-4280-835c-037155607326.pdf\"}],\"financialInterests\":\"\",\"formattedTitle\":\"Study on Preparation and Mechanical Properties for Graphene Oxide/Epoxy Resins Adhesives\",\"fulltext\":[{\"header\":\"1. Introduction\",\"content\":\"\\u003cp\\u003eEpoxy resin (EP) is extensively used as an adhesive and polymer composite matrix in aerospace, electronics, construction, and packaging due to its exceptional adhesion, thermal stability, mechanical performance, and processability [1]. However, the growing demand for adhesives with enhanced durability and strength in industrial applications cannot be fully satisfied by unmodified EP [2,3]. Graphene oxide (GO), a two-dimensional nanomaterial derived from graphene through strong oxidation, possesses a layered structure modified by oxygen-containing functional groups. The abundant surface hydroxyl and epoxy groups endow GO with excellent hydrophilicity, dispersibility, and chemically tunable interfacial properties [4]. GO is a new type of two-dimensional nanomaterial with a unique oxygen-containing functional group-modified layered structure formed by graphene after undergoing strong oxidation treatment. Due to the abundance of hydroxyl groups, epoxy groups, and other oxygen-containing groups on the surface, graphene oxide possesses good hydrophilicity, dispersibility, and tunable interfacial properties. As a nanoscale filler, GO demonstrates significant potential for improving the mechanical and thermal properties of composites when incorporated into polymer matrices. GO exhibits exceptional mechanical characteristics, with a tensile strength exceeding 130 GPa, making it an effective reinforcement phase [5]. Furthermore, its high thermal conductivity enables substantial enhancement of composite thermal conductivity, which makes it an ideal choice for a variety of applications where efficient heat dissipation is required. However, the interlayer forces of GO tend to result in their uneven distribution in the matrix, hindering their industrial applications. This agglomeration induces localized stress concentration and deteriorates the composite's mechanical properties [6,7]. Additionally, weak interfacial bonding between GO and the EP matrix may restrict mechanical load transfer, compromising the overall composite performance [8].\\u003c/p\\u003e \\u003cp\\u003eIn this study, a novel GO/EP adhesive was prepared with EP as the matrix and GO as the reinforcing phase GO was synthesized via Hummer's method, and hydroxyl, carboxyl and epoxy groups were introduced on its surface and edges. These functional groups facilitated interfacial interactions with the EP matrix, enhancing the composite's mechanical performance. In addition, we explored two dispersion methods, ultrasonic and emulsion dispersion, to optimize GO distribution within the EP matrix. The homogeneous dispersion of GO promoted the formation of a three-dimensional reinforcement network, consequently improving thermal stability and mechanical properties. To sum up, this study provides a new idea for preparation polymer-based composites with excellent bonding performance, thermal stability, and mechanical properties, promoting the wide application of EP adhesives.\\u003c/p\\u003e\"},{\"header\":\"2. Experimental Section\",\"content\":\"\\u003cdiv id=\\\"Sec3\\\" class=\\\"Section2\\\"\\u003e \\u003ch2\\u003e2.1 Materials\\u003c/h2\\u003e \\u003cp\\u003eGraphene was obtained from Qingdao Dongkai Graphite Co., Ltd in China. EP was produced by the Bluestar New Material Wuxi Resin Factory, and the Beijing Xiangshan Joint Additive Factory produced the polyamide resin 651 (PA651). H\\u003csub\\u003e2\\u003c/sub\\u003eSO\\u003csub\\u003e4\\u003c/sub\\u003e, NaNO\\u003csub\\u003e3\\u003c/sub\\u003e, and H\\u003csub\\u003e2\\u003c/sub\\u003eO\\u003csub\\u003e2\\u003c/sub\\u003e, all of which were of analytical pure grade, were sourced from Tianjin Fuyu Fine Chemical Co., Ltd. Aqueous solutions were prepared using distilled water.\\u003c/p\\u003e \\u003c/div\\u003e \\u003cdiv id=\\\"Sec4\\\" class=\\\"Section2\\\"\\u003e \\u003ch2\\u003e2.2 Pretreatment of GO\\u003c/h2\\u003e \\u003cp\\u003eThe graphene and concentrated H\\u003csub\\u003e2\\u003c/sub\\u003eSO\\u003csub\\u003e4\\u003c/sub\\u003e were mixed in a round-bottom flask at a mass ratio 1:50 under continuous stirring to achieve homogeneous dispersion. Subsequently, 10 g of KMnO\\u003csub\\u003e4\\u003c/sub\\u003e and 1.5 g of NaNO\\u003csub\\u003e3\\u003c/sub\\u003e were gradually added to the mixture, which was then kept in an ice-water bath with constant stirring for 2 h. The reaction system was then permitted to proceed at room temperature for 24 h. To terminate the reaction and eliminate residual KMnO\\u003csub\\u003e4\\u003c/sub\\u003e, an appropriate amount of H\\u003csub\\u003e2\\u003c/sub\\u003eO\\u003csub\\u003e2\\u003c/sub\\u003e was introduced into the mixture. The GO dispersion was thoroughly washed 3 times with anhydrous ethanol, followed by vacuum drying to obtain the final GO product.\\u003c/p\\u003e \\u003c/div\\u003e \\u003cdiv id=\\\"Sec5\\\" class=\\\"Section2\\\"\\u003e \\u003ch2\\u003e2.3 Preparation of GO/EP adhesives\\u003c/h2\\u003e \\u003cp\\u003eTwo equal masses of GO are placed into two different ethanol solution beakers for ultrasonic dispersion, and then add the solution to the EP matrix. The ethanol solution is removed through two-phase extraction to obtain GO/EP mixtures called A\\u003csub\\u003emix\\u003c/sub\\u003e and B\\u003csub\\u003emix\\u003c/sub\\u003e. A\\u003csub\\u003emix\\u003c/sub\\u003e was ultrasonically treated at 40\\u0026deg;C for 2 h, and B\\u003csub\\u003emix\\u003c/sub\\u003e was emulsified in the emulsifying machine at 8000 r/min for 30 min. The curing agent polyamide 651 (PA651) was added to A\\u003csub\\u003emix\\u003c/sub\\u003e and B\\u003csub\\u003emix\\u003c/sub\\u003e, stirred for 10 min, and then degassed under vacuum for 30 min to remove bubbles generated during the mixing process. The resulting GO/EP adhesive was designated as GO/EP-AD. The GO/EP adhesive cured sheets were prepared by pouring the GO/EP-AD into a pre-treated polytetrafluoroethylene mold and curing it in stages (70\\u0026deg;C for 2 h, 125\\u0026deg;C for 2 h, 150\\u0026deg;C for 1h) is named GO/EP-SH.\\u003c/p\\u003e \\u003c/div\\u003e \\u003cdiv id=\\\"Sec6\\\" class=\\\"Section2\\\"\\u003e \\u003ch2\\u003e2.4 Characterization\\u003c/h2\\u003e \\u003cp\\u003eX-ray diffraction (XRD) measurements were conducted using a Japan D/MAX-IIIB diffractometer. Fourier Transform Infrared Spectroscopy (FT-IR) testing was carried out using an MB-100 spectrophotometer from Bomem, Canada, covering a spectral acquisition range of 4000\\u0026thinsp;\\u0026minus;\\u0026thinsp;500 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e. A scanning electron microscopy (SEM) analysis was done using a FEI Sirion microscope from the Netherlands. The shear strength test was completed using the YHS-229WJ electronic universal tensile testing machine of Yihuan Instrument Technology (Shanghai) Co., Ltd., According to the GB/T 7124\\u0026thinsp;\\u0026minus;\\u0026thinsp;2008 standard, lap joint specimens of aluminum sheets with the size of 100 mm \\u0026times; 25 mm \\u0026times; 1.6 mm were adopted, with the bonding length of 12.5 mm. And the morphology of the sheared section was analyzed by using the 9XB-PC metallographic microscope produced by Shanghai Optical Instrument. The material's thermal stability was analyzed using the Perkin Elmer TGA-7 thermogravimetric analyzer from the United States. The GO/EP-SH were cut into 50 mm \\u0026times; 7 mm \\u0026times; 2 mm specimens. The thermodynamic properties were tested using the DMS6100 dynamic thermomechanical analyzer manufactured by Seiko Instruments Inc. The tensile strength and elastic modulus were tested using the YHS-229WJ-500kN microcomputer-controlled universal material testing machine of Shanghai Yihuan Instrument Technology Co., Ltd. The GO/EP-SH were cut into specimens of 63.5 mm \\u0026times; 12.7 mm \\u0026times; 3 mm. The impact strength was tested using an XJU-2.75J cantilever-beam impact testing machine manufactured by Chengde Testing Machine Co., Ltd., China.\\u003c/p\\u003e \\u003cp\\u003e \\u003c/p\\u003e \\u003c/div\\u003e\"},{\"header\":\"3. Results and Discussion\",\"content\":\"\\u003cdiv id=\\\"Sec8\\\" class=\\\"Section2\\\"\\u003e \\u003ch2\\u003e3.1 Characterization of GO/EP-SH\\u003c/h2\\u003e \\u003cp\\u003eFigure\\u0026nbsp;\\u003cspan refid=\\\"Fig2\\\" class=\\\"InternalRef\\\"\\u003e2\\u003c/span\\u003e(a) presents the XRD patterns of the samples. From the XRD curve of graphene, there is a diffraction peak with a smaller peak and larger peak width at 2θ\\u0026thinsp;=\\u0026thinsp;26.1\\u0026deg;, the (002) crystallographic characteristic diffraction peak of graphene. The diminished intensity of the diffraction peaks is due to the complete exfoliation of graphene during the synthesis process. In the diffraction curve of GO, there is a sharp diffraction peak at 2θ\\u0026thinsp;=\\u0026thinsp;9.8\\u0026deg;, the diffraction peak of GO (001) [9,10]. According to the Bragg equation, the interlayer spacing of graphene is 0.78 nm, where n is one and λ is the wavelength of X-rays GO from the Cu target of 1.54 \\u0026Aring;. This result follows the grain spacing of 0.71\\u0026ndash;0.82 nm reported in the literature for GO [11]. This interlayer spacing results from introducing oxygen-containing groups, such as carboxyl groups, hydroxyl groups, etc., to the surface and edges of graphene during the oxidation process, increasing the interlayer distance between the layers of graphene sheets. The XRD curves of the GO/EP-SH with different mass fractions of GO are shown in Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig2\\\" class=\\\"InternalRef\\\"\\u003e2\\u003c/span\\u003e(b). The XRD curves of GO/EP-SH showed diffraction peaks with smaller peaks and larger peak widths at 2θ of 15\\u0026deg; to 25\\u0026deg;, exhibiting epoxy resin characteristic peaks. The characteristic diffraction peaks of GO at 2θ\\u0026thinsp;=\\u0026thinsp;9.8\\u0026deg; and graphene at 2θ\\u0026thinsp;=\\u0026thinsp;26.1\\u0026deg; do not appear in Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig2\\\" class=\\\"InternalRef\\\"\\u003e2\\u003c/span\\u003e(b), which is attributed to the fact that GO is neither reduced nor agglomerated during the curing process of GO/EP-SH but dispersed uniformly in the EP matrix.\\u003c/p\\u003e \\u003cp\\u003e \\u003c/p\\u003e \\u003cp\\u003eFigure\\u0026nbsp;\\u003cspan refid=\\\"Fig3\\\" class=\\\"InternalRef\\\"\\u003e3\\u003c/span\\u003e(a) shows the infrared spectra of GO, EP, and Graphene. The absorption peak at 3364.22 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e corresponds to the stretching vibration of N-H in amid and O-H in alcohol. The peak at 2928.41 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e is attributed to the stretching vibration of C-H in methylene. Peaks at 1607.98 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e and 1509.93 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e represent the stretching vibration of the carbon skeleton in the benzene ring. The absorption peak at 1462.05 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e is associated with the deformation vibration of C-H. At 1301.09 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e, the absorption peak indicates the deformation vibration of C-N. The peak at 1253.63 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e corresponds to the deformation vibration of aromatic ether. Peaks at 1180.85 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e and 1033.67 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e arise from the deformation vibration of aliphatic ether. Peaks at 827.01 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e represent characteristic absorption bands for the benzene ring's in-plane and out-of-plane deformation vibrations. From the graph, the disappearance of the epoxy group absorption peak at 910\\u0026ndash;920 cm\\u003csup\\u003e\\u0026minus;\\u0026thinsp;1\\u003c/sup\\u003e indicates the ring-opening of epoxy groups and complete epoxy resin curing [12]. Figure\\u0026nbsp;\\u003cspan refid=\\\"Fig3\\\" class=\\\"InternalRef\\\"\\u003e3\\u003c/span\\u003e(b) shows the FT-IR absorption spectra of GO/EP-SH with different GO content. From this Fig., with the increase of GO content, the vibration peak of the characteristic functional group of the EP matrix shows a red shift phenomenon, which indicates the uniform dispersion of GO nanosheets in the EP matrix and the interfacial interaction between the oxygen-containing functional groups on the surface and the epoxy molecular chain.\\u003c/p\\u003e \\u003cp\\u003e \\u003c/p\\u003e \\u003cp\\u003eFigure\\u0026nbsp;\\u003cspan refid=\\\"Fig4\\\" class=\\\"InternalRef\\\"\\u003e4\\u003c/span\\u003e shows SEM micrographs of fracture surfaces of GO/EP-SH with different GO contents. The pure EP fractured surface (Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig4\\\" class=\\\"InternalRef\\\"\\u003e4\\u003c/span\\u003e(a)) displays smooth and highly oriented deformation lines, demonstrating typical characteristics of brittle fracture behavior. This feature suggests that rapid crack propagation during the tensile process is accompanied by easy propagation [13,14]. When the GO content is lower than 2wt%, as shown in Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig4\\\" class=\\\"InternalRef\\\"\\u003e4\\u003c/span\\u003e(b-j), GO has decent dispersibility in the EP matrix and forms excellent interfacial interaction. Compared with pure EP, the number of cracks increased significantly. When the GO content increases to 2wt%, as shown in Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig4\\\" class=\\\"InternalRef\\\"\\u003e4\\u003c/span\\u003e(k), the fracture surface becomes rough, a typical ductile fracture feature. The GO is uniformly dispersed in the EP matrix to form a strong interfacial effect [15]. It effectively enhanced the mechanical properties of the GO/EP-SH. With the continuous increase of the GO content, agglomeration phenomena occur in the EP matrix, as shown in Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig4\\\" class=\\\"InternalRef\\\"\\u003e4\\u003c/span\\u003e(l). When the agglomeration size of GO is too large, it not only fails to fill the voids in the EP matrix but also causes the reduction of mechanical properties due to its stress concentration.\\u003c/p\\u003e \\u003cp\\u003e \\u003c/p\\u003e \\u003c/div\\u003e \\u003cdiv id=\\\"Sec9\\\" class=\\\"Section2\\\"\\u003e \\u003ch2\\u003e3.2 Shear strength of GO/EP-AD\\u003c/h2\\u003e \\u003cp\\u003eIn Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig5\\\" class=\\\"InternalRef\\\"\\u003e5\\u003c/span\\u003e, the shear strength of GO/EP-AD shows a trend of increasing first and then decreasing. The shear strength of pure EP is 20.42 MPa. With the increase of GO content, the shear strength of GO/EP-AD also rises. When the GO content reaches 2wt%, the shear strength reaches a maximum value of 31.94 MPa, increasing by 56% compared to pure EP. As the GO content continues to rise, the shear strength of GO/EP-AD begins to decrease. This is because the appropriate amount of GO addition can effectively reduce the exothermic heat and shrinkage in the curing process of EP, thus reducing the defects produced by the adhesives layer in the adhesives bonding process. It not only significantly improves the overall quality of the adhesive joints, but also improves the adhesive bond strength through the enhancement of interfacial bonding [16,17]. GO as a nano-filler can effectively bear the external stress and improve the compressive strength by hindering the crack propagation when the load reaches the critical value. When the bonded part bears the external load, the stress transfer effect of GO can effectively share the interfacial stress and further enhance the shear strength. However, when the GO content exceeds the optimal threshold, the system's viscosity rises significantly, causing insufficient interfacial bonding [18]. This will give rise to defects in the bonding process, trigger the phenomenon of stress concentration, and ultimately lower the shear strength of the adhesive.\\u003c/p\\u003e \\u003cp\\u003e \\u003c/p\\u003e \\u003cp\\u003eTo investigate the influence of GO content on the fracture mechanism of GO/EP -AD, this study employed metallurgical microscopy to conduct morphological analysis on the shear cross-sections of bonded specimens with aluminum substrates. Figure\\u0026nbsp;\\u003cspan refid=\\\"Fig6\\\" class=\\\"InternalRef\\\"\\u003e6\\u003c/span\\u003e displays the metallurgical microstructure characteristics of GO/EP-AD with varying GO contents. As shown in Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig6\\\" class=\\\"InternalRef\\\"\\u003e6\\u003c/span\\u003e(a), the shear fracture interface of the pure EP adhesives presents a clear boundary between the substrate and the adhesives layer, and shows typical brittle fracture characteristics. The incorporation of GO filler (Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig6\\\" class=\\\"InternalRef\\\"\\u003e6\\u003c/span\\u003e(b,c)) induced a marked increase in fractured surfaces of GO/EP-AD compared to those of pure EP. With the continuous augmentation of GO content (Fig.s 6(d-k)), the density of the fracture surface increases, the fracture surface becomes rough, and the crack distribution is disorderly. This is because a strong interfacial force is constructed between GO and the EP matrix. As the GO content in the EP matrix increases, the chemical bonds formed at the two-phase interface also increase accordingly [19]. Therefore, compared with the pure EP, the GO/EP-AD can absorb further impact energy, withstand greater shear force, and enhance the bonding strength of the adhesives. When the GO content exceeds 2.0 wt% (Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig6\\\" class=\\\"InternalRef\\\"\\u003e6\\u003c/span\\u003e(l)), distinct GO agglomeration phenomena emerge in the EP matrix accompanied by the formation of numerous bubbles. This is attributed to the excessive GO content leading to uneven distribution within the matrix, with a significant increase in system viscosity hinders effective bubble expulsion during the bonding process. These factors collectively contribute to increased defects in the shear fracture surface, ultimately resulting in a decline in the material's shear strength.\\u003c/p\\u003e \\u003cp\\u003e \\u003c/p\\u003e \\u003c/div\\u003e \\u003cdiv id=\\\"Sec10\\\" class=\\\"Section2\\\"\\u003e \\u003ch2\\u003e3.3 Thermal Properties of GO/EP-SH\\u003c/h2\\u003e \\u003cp\\u003eThermal stability is a key indicator for assessing a polymer's resistance to thermal degradation or aging. When the polymers are heated, they may undergo physical state modifications such as softening and melting and chemical changes such as hydrolysis, decomposition, degradation, cyclization, and cross-linking [20,21]. Figure\\u0026nbsp;\\u003cspan refid=\\\"Fig7\\\" class=\\\"InternalRef\\\"\\u003e7\\u003c/span\\u003e demonstrates the effect of GO content on the thermal degradation of GO/EP-SH. By observation, we can see that the decomposition of pure EP starts at about 280 ℃ and is finished by 650 ℃. It is worth noting that the degradation of the samples before the temperature reaches 250 ℃ is mainly due to the volatilization of water, the initial decomposition of small amounts of EP, and the volatilization of low-molecular-weight substances in EP. When the temperature ranges from 280 ℃ to 650 ℃, the decomposition of EP molecules becomes the main cause of thermal weight loss. At lower temperatures, the thermal degradation of the GO/EP-SH exhibits minimal variation, with a lower thermal degradation mass loss compared to pure EP. However, as the temperature continues to rise, under identical decomposition temperatures, the residual amount of the GO/EP-SH after thermal decomposition becomes significantly lower than that of pure EP. Moreover, higher GO content correlates with reduced residual quantities. The reason for this phenomenon lies in the fact that the thermal decomposition temperature of the GO/EP-SH is lower than that of pure EP [22]. Therefore, under high-temperature conditions, when the masses of the two are the same, the GO/EP-SH absorb relatively less heat, eventually causing a more significant mass loss.\\u003c/p\\u003e \\u003cp\\u003e \\u003c/p\\u003e \\u003cp\\u003eDynamic mechanical analysis (DMA) refers to the mechanical properties of polymers and their variation with temperature at a fixed frequency. The energy stored during the elastic deformation of a material is called the energy storage modulus (\\u003cem\\u003eE'\\u003c/em\\u003e), a higher value of which indicates a more rigid material, the percentage of energy loss is expressed by the ratio of the loss modulus to the energy storage modulus (\\u003cem\\u003etanδ\\u003c/em\\u003e) [23,24]. The \\u003cem\\u003eE'-T\\u003c/em\\u003e curves of GO/EP-SH with varying GO contents are presented in Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig8\\\" class=\\\"InternalRef\\\"\\u003e8\\u003c/span\\u003e(a). It can be observed from Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig8\\\" class=\\\"InternalRef\\\"\\u003e8\\u003c/span\\u003e(a) that the \\u003cem\\u003eE'\\u003c/em\\u003e of the GO/EP-SH demonstrates a progressive enhancement with increasing GO content in the lower temperature region. This enhancement is ascribed to the hydroxyl and epoxy group functionalities on GO surfaces, which undergo crosslinking reactions with the EP matrix during processing. The formed covalent bonding network strengthens the GO and EP interfacial adhesion, thereby directly increasing the storage modulus through effective stress transfer mechanisms. When the temperature reached 40\\u0026deg;C, the \\u003cem\\u003eE'\\u003c/em\\u003e of the 2.0 wt% GO/EP-SH was 1.718 GPa, an increase of 45% compared to pure EP (950 MPa). As the temperature continued to increase, the \\u003cem\\u003eE'\\u003c/em\\u003e value displayed a gradual downward trend, demonstrating the transition of the GO/EP-SH from the glassy state to the rubbery state. Furthermore, the interfacial interactions between GO and the EP matrix enable effective stress transfer from the polymer matrix to the rigid GO nanosheets [25]. This reinforcement mechanism significantly enhances the resistance to deformation in the GO/EP-SH.\\u003c/p\\u003e \\u003cp\\u003e \\u003c/p\\u003e \\u003cp\\u003eThe maximum value of \\u003cem\\u003etanδ\\u003c/em\\u003e corresponds to the glass transition temperature (\\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003eg\\u003c/sub\\u003e). The \\u003cem\\u003etanδ-T\\u003c/em\\u003e curves of GO/EP with varying GO contents are presented in Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig8\\\" class=\\\"InternalRef\\\"\\u003e8\\u003c/span\\u003e(b). The experimental data indicate that the energy loss of GO/EP-SH starts to show at 73\\u0026deg;C when the GO addition is 0.5 wt%, and the onset temperature of this loss shows a significant high-temperature shift trend with the increase of GO content. The peak of \\u003cem\\u003etanδ\\u003c/em\\u003e continuously shifts towards higher temperatures with increasing GO content. The \\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003e\\u003cem\\u003eg\\u003c/em\\u003e\\u003c/sub\\u003e of pure EP is 106 ℃, compared with pure EP, the \\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003e\\u003cem\\u003eg\\u003c/em\\u003e\\u003c/sub\\u003e of 2.0 wt% GO/EP-SH is 127 ℃, which has increased by 21 ℃. This phenomenon can be attributed to two synergistic mechanisms. The abundant active group on GO surfaces forms strong chemical bonds with the EP matrix, establishing a stable chemical crosslinking network [26,27]. As rigid nanofillers in the polymer system, GO induces physical crosslinking effects through its lamellar structure that restricts polymer chain segment movement via steric hindrance effects. With the increase of GO content, the cross-linking density of the system increases, leading to a decrease in free volume and the mobility of the chain segments, and ultimately, the enhancement of \\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003e\\u003cem\\u003eg\\u003c/em\\u003e\\u003c/sub\\u003e is achieved [28]. The results of this study confirm that the introduction of GO can effectively improve the thermal stability of the EP matrix.\\u003c/p\\u003e \\u003cp\\u003eFigure\\u0026nbsp;\\u003cspan refid=\\\"Fig9\\\" class=\\\"InternalRef\\\"\\u003e9\\u003c/span\\u003e displays the \\u003cem\\u003etanδ-T\\u003c/em\\u003e curves of GO/EP-SH with different dispersion processes. The \\u003cem\\u003etanδ\\u003c/em\\u003e peak of the GO/EP-SH containing 2wt% GO in the emulsification dispersion process appears at 127 ℃. In contrast, the \\u003cem\\u003etanδ\\u003c/em\\u003e peak of the sample prepared by ultrasonic dispersion appears at 123 ℃. The increase in \\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003e\\u003cem\\u003eg\\u003c/em\\u003e\\u003c/sub\\u003e indicates that the emulsification dispersion can enable GO to be effectively and uniformly distributed in the EP matrix. During the dispersion process, oxygen-containing functional groups on the surface of GO nanosheets undergo interfacial chemical interactions with epoxy molecular chains, forming a stable three-dimensional crosslinked network structure. The uniformly dispersed GO nanosheets become embedded within the intermolecular spaces of epoxy chains, where their steric hindrance effect significantly suppresses the thermal motion of polymer segments thereby enhancing the mechanical properties of the GO/EP-SH [29]. In contrast, ultrasonic dispersion demonstrates inferior dispersion efficacy, as evidenced by the stacking phenomena of GO nanosheets. These structural defects hinder sufficient crosslinking between the epoxy resin and curing agents, resulting in reduced crosslinking network density and, consequently, constrained performance enhancement of the composite.\\u003c/p\\u003e \\u003cp\\u003e \\u003c/p\\u003e \\u003c/div\\u003e \\u003cdiv id=\\\"Sec11\\\" class=\\\"Section2\\\"\\u003e \\u003ch2\\u003e3.4 Mechanical Properties of GO/EP-SH\\u003c/h2\\u003e \\u003cp\\u003eWhen subjected to externally applied stress, crazes initially form within the composite material. With continued application of the stress load, these crazes gradually evolve into cracks. After the graphene is oxidized, the functional groups on its surface can interact with the functional groups on the EP molecular chain, forming connection nodes and a three-dimensional network, which can effectively disperse stress, consume the fracture energy, and inhibit the further expansion of cracks, thereby improving the mechanical properties of the composite material [30\\u0026ndash;32]. Figure\\u0026nbsp;\\u003cspan refid=\\\"Fig10\\\" class=\\\"InternalRef\\\"\\u003e10\\u003c/span\\u003e(a-c) shows the tensile strength, elastic modulus and impact strength of GO/EP-SH with different GO contents. The Fig. shows that the mechanical properties of the GO/EP-SH prepared by emulsification dispersion are always higher than those prepared by ultrasonic dispersion, indicating that compared with ultrasonic dispersion, emulsification dispersion can disperse GO more uniformly in the EP matrix and significantly improve the mechanical properties of GO/EP-SH. The tensile strength and elastic modulus are key mechanical parameters that characterize a material's ability to resist external forces and deformation [33]. As shown in Fig.\\u0026nbsp;\\u003cspan refid=\\\"Fig10\\\" class=\\\"InternalRef\\\"\\u003e10\\u003c/span\\u003e(a, b) the tensile strength and elastic modulus of pure EP are 34 MPa and 8.07 GPa, respectively. With the increase of GO content, the mechanical properties of GO/EP-SH have been significantly improved. When the GO content reaches 2.0 wt%, the tensile strength and elastic modulus of the GO/EP-SH rise to 58.9 MPa and 1.928 GPa, respectively, representing 42% and 58% enhancements compared to pure EP. This enhancement effect is mainly attributed to the effectiveness of the emulsification dispersion process. The network structure formed by the uniformly dispersed GO in the EP matrix effectively enhances the mechanical properties of the GO/EP-SH [34]. As shown in Fig.s 10(c), the impact strength of GO/EP-SH also exhibited a trend of first increasing and then decreasing. When the GO content reached 2.0 wt%, the impact strength achieved maximum values of 8.27 kJ/m\\u0026sup2;, representing 92% enhancements compared to pure EP. When the material is subjected to external forces, the strong interfacial bonding between GO and the EP matrix enabled effective energy transfer through the interface to GO layers, inducing localized yielding and deformation of the matrix that effectively absorbed impact energy. When the GO content exceeds 2.0 wt%, the reduced interlayer spacing of GO nanosheets induces GO agglomeration within the EP matrix. The microcracks generated under the stress expand and eventually form a macroscopic crack network, resulting in the decline of mechanical properties.\\u003c/p\\u003e \\u003cp\\u003e \\u003c/p\\u003e \\u003c/div\\u003e\"},{\"header\":\"4. Conclusion\",\"content\":\"\\u003cp\\u003eIn this study, GO was synthesized via Hummer\\u0026rsquo;s method, GO/EP-SH adhesives were fabricated by incorporating GO into the epoxy matrix by ultrasonic and emulsification dispersion methodologies. The results showed that when the GO content reaches 2wt%, the shear strength of the GO/EP-AD 31.94 MPa, which is 56% higher than that of pure EP. At the same thermal degradation temperature, the thermal degradation rate of GO/EP-SH is higher than that of pure EP, and the higher the GO content, the more significant the thermal degradation. The GO/EP-SH exhibited a glass transition temperature (\\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003e\\u003cem\\u003eg\\u003c/em\\u003e\\u003c/sub\\u003e) of 127\\u0026deg;C at 2 wt% GO loading, demonstrating a 22\\u0026deg;C elevation compared to the pure EP matrix. When the temperature reached 40\\u0026deg;C, the storage modulus (\\u003cem\\u003eE'\\u003c/em\\u003e) of the GO/EP-SH reached 1.718 GPa, increasing by 45% compared with 950 MPa of pure EP. By comparing the two dispersion processes, it was found that the \\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003e\\u003cem\\u003eg\\u003c/em\\u003e\\u003c/sub\\u003e value of the sample prepared by the emulsification dispersion method was 4 ℃ higher than that of the sample prepared by the ultrasonic dispersion, which indicated that emulsion dispersion could better disperse GO uniformly in the EP matrix. The tensile strength of the GO/EP-SH loaded with 2 wt% GO was 58.9 MPa, the modulus of elasticity was 1.928 GPa, and the impact strength was 8.27 kJ/m\\u0026sup2;. These values increased by 42, 58, and 92%, respectively, compared with pure EP.\\u003c/p\\u003e\"},{\"header\":\"Declarations\",\"content\":\"\\u003cp\\u003e\\u003cstrong\\u003eAcknowledgments\\u003c/strong\\u003e\\u003c/p\\u003e\\n\\u003cp\\u003eThis work is supported by the National Natural Science Foundation of China (No.51772061).\\u003c/p\\u003e\\n\\u003cp\\u003e\\u003cstrong\\u003eFunding\\u003c/strong\\u003e\\u003c/p\\u003e\\n\\u003cp\\u003eAccess funding enabled by the National Natural Science Foundation of China.\\u003c/p\\u003e\\n\\u003cp\\u003e\\u003cstrong\\u003eDeclaration of interest statement\\u003c/strong\\u003e\\u003c/p\\u003e\\n\\u003cp\\u003eThe authors have no relevant financial or non-financial interests to disclose.\\u003c/p\\u003e\\n\\u003cp\\u003e\\u003cstrong\\u003eAuthors contribution\\u003c/strong\\u003e\\u003c/p\\u003e\\n\\u003cp\\u003eXueyue Lyu: Investigation, Software, Data curation, Writing\\u0026ndash;original draft. Baozheng Cui: material preparation. Xinjia Yang:Analyzing data, Writing. Dongyu Zhao: Methodology, Writing\\u0026ndash;review \\u0026amp; editing.\\u003c/p\\u003e\\n\\u003cp\\u003e\\u003cstrong\\u003eData availability\\u003c/strong\\u003e\\u003c/p\\u003e\\n\\u003cp\\u003eThe data that support the findings of this study are available from the corresponding author upon.\\u0026nbsp;\\u003c/p\\u003e\"},{\"header\":\"References\",\"content\":\"\\u003col\\u003e\\n\\u003cli\\u003eChu XC, Wang GQ, Ding QJ, Zhao G, Li HF (2023) Molecular dynamics simulation of epoxy resin modified by polyimide grafted graphene oxide. Polym. Eng. Sci. 63(11): 3798-3808. https://doi.org/10.1002/pen.26485.\\u003c/li\\u003e\\n\\u003cli\\u003eHou WX, Gao Y, Wang J, Blackwood DJ, Teo S (2020) Recent advances and future perspectives for graphene oxide reinforced epoxy resins. Mater. Today Commun. 23: 100883. https://doi.org/10.1016/j.mtcomm.2019.100883.\\u003c/li\\u003e\\n\\u003cli\\u003eChen J, Kinloch AJ, Sprenger S, Taylor AC (2022) The mechanical properties and toughening mechanisms of an epoxy polymer modified with polysiloxane-based core-shell particles. Polym. 54(16): 4276-4289. https://doi.org/10.1016/j.polymer.2013.06.009.\\u003c/li\\u003e\\n\\u003cli\\u003eBiranje PM, Patwardhan AW, Joshi JB, Dasgupta K (2022) Exfoliated graphene and its derivatives from liquid phase and their role in performance enhancement of epoxy matrix composite. Composites, Part A. 156: 106886. https://doi.org/10.1016/j.compositesa.2022.106886.\\u003c/li\\u003e\\n\\u003cli\\u003eNuncira J, Seara LM, Sinisterra RD, Caliman V, Silva GG (2019) Long-term colloidal stability of graphene oxide aqueous nanofluids. Fullerenes, Nanotubes Carbon Nanostruct. 28(5): 407-417. https://doi.org/10.1080/1536383X.2019. 1695250.\\u003c/li\\u003e\\n\\u003cli\\u003eAmirbeygi H, Khosravi H, Tohidlou E (2019) Reinforcing effects of aminosilane-functionalized graphene on the tribological and mechanical behaviors of epoxy nanocomposites. J. Appl. Polym. Sci. 136: 18. https://doi.org/10.1002/app.47410. \\u003c/li\\u003e\\n\\u003cli\\u003eHu CX, Zhang HN, Neate N, Hou XH, Grant D, Xu F (2022) Highly Aligned Ni-Decorated GO-CNT Nanostructures in Epoxy with Enhanced Thermal and Electrical Properties. Polym. 14: 13. https://doi.org/10.3390/polym14132583.\\u003c/li\\u003e\\n\\u003cli\\u003eLiu L, Liang S, Zheng CS, Wang DP (2023) Preparation and interfacial properties of functionalised graphene oxide modified carbon fibre/epoxy resin matrix composites. Plast., Rubber Compos. 52(6): 346-355. https://doi.org/10.1080/ 14658011. 2023.2207059.\\u003c/li\\u003e\\n\\u003cli\\u003eWang N, Gao HY, Zhang J, Qin Y, Wang DY (2019) Phytic Acid Intercalated Graphene Oxide for Anticorrosive Reinforcement of Waterborne Epoxy Resin Coating. Polym. 11: 12. https://doi.org/10.3390/polym11121950.\\u003c/li\\u003e\\n\\u003cli\\u003eAzimi R, Roghani-Mamaqani H, Gholipour-Mahmoudalilou M (2017) Grafting poly (amidoamine) dendrimer-modified silica nanoparticles to graphene oxide for preparation of a composite and curing agent for epoxy resin. Polym. 126: 152-161. https://doi.org/10.1016/j.polymer.2017.08.037.\\u003c/li\\u003e\\n\\u003cli\\u003eYuan M, Zhang Y, Xie F, Yang H, Bittencourt C, Snyders R, Li WJ (2025) Nano copper-modified GO and CNTs for enhanced the epoxy resin composite thermal properties. Appl. Surf. Sci. 690:162616. https://doi.org/10.1016/j.apsusc.2025. 162616.\\u003c/li\\u003e\\n\\u003cli\\u003eXu H, Zhang XR, Hu GK, Weng L, Liu LH (2020) High thermal conductivity EP adhesive based on the GO/EP interface optimized by TDI. Polym. Adv. Technol. 31(6):1356-1364. https://doi.org/10.1002/pat.4865.\\u003c/li\\u003e\\n\\u003cli\\u003eChen L, Chen WS, Li BH (2023) Investigation of shape memory and heat transfer properties of graphene oxide reinforced shape memory epoxy resin composites. Mater. Today Commun. 34: 105170. https://doi.org/10.1016/j. mtcomm.2022.105170. \\u003c/li\\u003e\\n\\u003cli\\u003eFang F, Song PG, Ran SY, Guo ZH, Wang H, Fang ZP (2018) A facile way to prepare phosphorus-nitrogen-functionalized graphene oxide for enhancing the flame retardancy of epoxy resin. Adhes. Commun. 10:97-102. https://doi.org/10.1016/j.coco.2018.08.001.\\u003c/li\\u003e\\n\\u003cli\\u003eYang XJ, Song KR, Zhao DY (2024) Preparation and mechanical properties of Ni/RGO reinforced epoxy resin composites. High Perform. Polym. 36(3): 163-172. https://doi.org/10.1177/09540083231225284.\\u003c/li\\u003e\\n\\u003cli\\u003eBeggs KM, Servinis L, Gengenbach TR, Huson MG, Fox BL (2015) Henderson, L.C. A systematic study of carbon fibre surface grafting via in situ diazonium generation for improved interfacial shear strength in epoxy matrix composites. Compos. Sci. Technol. 118: 31-38. https://doi.org/10.1016/j.compscitech. 2015.08.001.\\u003c/li\\u003e\\n\\u003cli\\u003eReis Taiza, MC, Castro VG (2023) Amurin, L.G.; Silva, G.G. Graphene oxide dispersion in epoxy resin prepared by direct phase transfer from ethanol: Rheology and aging. Compos. Part C: Open Access. 10: 100340, https://doi.org/10.1016/j.jcomc.2022.100340.\\u003c/li\\u003e\\n\\u003cli\\u003eLiu ZJ, Wang D Cheng QK, Wang JP, Sun HT (2024) Outstanding interlaminar strength of carbon fiber reinforced epoxy resin via graphene oxide chemical bridge bonding. Appl. Surf. Sci. 670: https://doi.org/10.1016/j.apsusc.2024. 160658. \\u003c/li\\u003e\\n\\u003cli\\u003eGuo SY, Lu Y, Wan XM, Wu F, Zhao TJ, Shen Cn (2020) Preparation, characterization of highly dispersed reduced graphene oxide/epoxy resin and its application in alkali-activated slag composites. Cem. Concr. Compos. 105: https://doi.org/10.1016/j.cemconcomp.2019.103424. \\u003c/li\\u003e\\n\\u003cli\\u003eFu BJ, Wang Y, Ding WY, Tian JF, Han ST (2024) Simultaneous improvement of mechanical, adhesive and ablative properties of phenolic epoxy modified PDMS. Polymer. 311: 127522. https://doi.org/10.1016/j.polymer.2024.127522.\\u003c/li\\u003e\\n\\u003cli\\u003eChen J, Yao BW, Li C, Shi GQ (2013) An improved Hummers method for eco-friendly synthesis of graphene oxide. Carbon. 64: 225-229. https://doi.org/10.1016/j.carbon. 2013.07.055. \\u003c/li\\u003e\\n\\u003cli\\u003eYang W, Wang NN, Ping P, Yuen AC, Li A, Zhu SE, Wang LL (2018) Novel 3D Network Architectured Hybrid Aerogel Comprising Epoxy, Graphene, and Hydroxylated Boron Nitride Nanosheets. ACS Appl. Mater. Interfaces. 10(46): 40032-40043. https://doi.org/10.1021/acsami.8b15301. \\u003c/li\\u003e\\n\\u003cli\\u003eXiao WW, Liu Y, Guo SW (2016) Composites of graphene oxide and epoxy resin assuming a uniform 3D graphene oxide network structure. RSC Adv. 6(90): 86904-86908. https://doi.org/10.1039/c6ra16335a.\\u003c/li\\u003e\\n\\u003cli\\u003eLavoratti A, Zattera AJ, Amico SC (2021) Effect of carbonaceous nanofillers and triblock copolymers on the toughness of epoxy resin. Polym. Bull. 78(10): 5467-5480. https://doi.org/10.1007/s00289-020-03375-1.\\u003c/li\\u003e\\n\\u003cli\\u003eGhanbaralizadeh R, Bouhendi H, Kabiri K, Vafayan M (2016) A novel method for toughening epoxy resin through CO\\u003csub\\u003e2\\u003c/sub\\u003e fixation reaction. J. CO2 Util. 16: 225-235. https://doi.org/10.1016/j.jcou.2016.06.006. \\u003c/li\\u003e\\n\\u003cli\\u003eBortz DR, Heras E, Martin-Gullon I (2012) Impressive Fatigue Life and Fracture Toughness Improvements in Graphene Oxide/Epoxy Composites. Macromol. 45(1): 238-245. https://doi.org/10.1021/ma201563k. \\u003c/li\\u003e\\n\\u003cli\\u003eKim J, Yim BS, Kim JM, Kim J (2012) The effects of functionalized graphene nanosheets on the thermal and mechanical properties of epoxy composites for anisotropic conductive adhesives (ACAs). Microelectron. Reliab. 52(3): 595-602. https://doi.org/10.1016/j.microrel.2011.11.002.\\u003c/li\\u003e\\n\\u003cli\\u003eLiang X, Li XJ, Tang Y, Zhang XY, Wei W, Liu XY (2022) Hyperbranched epoxy resin-grafted graphene oxide for efficient and all-purpose epoxy resin modification. J. Colloid Interface Sci. 611: 105-117. https://doi.org/10.1016/j.jcis. 2021.12.068. \\u003c/li\\u003e\\n\\u003cli\\u003eZhang JX, Liang YX, Wang XJ, Zhou HJ, Li SY, Zhang J, Feng YN, Lu N, Wang Q, Guo ZH (2018) Strengthened epoxy resin with hyperbranched polyamine-ester anchored graphene oxide via novel phase transfer approach. Adv. Compos. Hybrid Mater. 1(2): 300-309. https://doi.org/10.1007/s42114-017-0007-0.\\u003c/li\\u003e\\n\\u003cli\\u003eChandrasekaran S, Sato N, Tolle F, Mulhaupt R, Fiedler B, Schulte K (2014) Fracture toughness and failure mechanism of graphene-based epoxy composites. Compos. Sci. Technol. 97: 90-99. https://doi.org/10.1016/j.compscitech. \\u003c/li\\u003e\\n\\u003cli\\u003eLu C, Lin FB, Shao HQ, Chen NL, Shao GW, Jiang JH (2022) Carboxylated Carbon Nanotube/Polyimide Films with Low Thermal Expansion Coefficient and Excellent Mechanical Properties. Polym. 14: 21. https://doi.org/10.3390/polym 14214565. \\u003c/li\\u003e\\n\\u003cli\\u003eBao CL, Guo YQ, Song L, Kan YC, Qian XD, Hu Y (2011) In situ preparation of functionalized graphene oxide/epoxy nanocomposites with effective reinforcements. J. Mater. Chem. 21(35): 13290-13298. https://doi.org/10.1039/ c1jm11434d. \\u003c/li\\u003e\\n\\u003cli\\u003eLv XY, Wu SB, Zhao DY (2024) Preparation and Performance of MWNTs/ Epoxy Resins Composites. J. Inorg. Organomet. Polym. Mater. 34(10): 4558-4567. https://doi.org/10.1007/s10904-024-03122-3.\\u003c/li\\u003e\\n\\u003cli\\u003eZhao XR, Li Y, Chen W, Li S, Zhao Y, Du SY (2019) Improved fracture toughness of epoxy resin reinforced with polyamide 6/graphene oxide nanocomposites prepared via in situ polymerization. Compos. Sci. Technol. 171: 180-189. https://doi.org/10.1016/j.compscitech.2018.12.023. \\u003c/li\\u003e\\n\\u003c/ol\\u003e\"}],\"fulltextSource\":\"\",\"fullText\":\"\",\"funders\":[],\"hasAdminPriorityOnWorkflow\":false,\"hasManuscriptDocX\":true,\"hasOptedInToPreprint\":true,\"hasPassedJournalQc\":\"\",\"hasAnyPriority\":false,\"hideJournal\":false,\"highlight\":\"\",\"institution\":\"\",\"isAcceptedByJournal\":true,\"isAuthorSuppliedPdf\":false,\"isDeskRejected\":\"\",\"isHiddenFromSearch\":false,\"isInQc\":false,\"isInWorkflow\":false,\"isPdf\":false,\"isPdfUpToDate\":true,\"isWithdrawnOrRetracted\":false,\"journal\":{\"display\":true,\"email\":\"info@researchsquare.com\",\"identity\":\"journal-of-polymer-research\",\"isNatureJournal\":false,\"hasQc\":true,\"allowDirectSubmit\":false,\"externalIdentity\":\"jpol\",\"sideBox\":\"Learn more about [Journal of Polymer Research](https://www.springer.com/journal/10965)\",\"snPcode\":\"10965\",\"submissionUrl\":\"https://www.editorialmanager.com/jpol/\",\"title\":\"Journal of Polymer Research\",\"twitterHandle\":\"\",\"acdcEnabled\":true,\"dfaEnabled\":true,\"editorialSystem\":\"em\",\"reportingPortfolio\":\"Springer Hybrid\",\"inReviewEnabled\":true,\"inReviewRevisionsEnabled\":false},\"keywords\":\"Epoxy resin, Graphene oxide, Adhesives, Emulsion dispersion, Thermal stability, Mechanical properties\",\"lastPublishedDoi\":\"10.21203/rs.3.rs-6538480/v1\",\"lastPublishedDoiUrl\":\"https://doi.org/10.21203/rs.3.rs-6538480/v1\",\"license\":{\"name\":\"CC BY 4.0\",\"url\":\"https://creativecommons.org/licenses/by/4.0/\"},\"manuscriptAbstract\":\"\\u003cp\\u003eIn this study, graphene oxide (GO) was synthesized via Hummer\\u0026rsquo;s method and subsequently integrated into an epoxy resin (EP) matrix using two distinct dispersion approaches: ultrasonic and emulsification dispersion to develop high-performance GO/EP adhesives (GO/EP-AD). At GO loading of 2 wt%, the adhesives exhibited shear strength of 31.94 MPa, demonstrating a 56% enhancement over pure EP. The storage modulus (\\u003cem\\u003eE'\\u003c/em\\u003e) of the GO/EP composites (GO/EP-SH) prepared by emulsion dispersion reached 1.718 GPa, the glass transition temperature (\\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003e\\u003cem\\u003eg\\u003c/em\\u003e\\u003c/sub\\u003e) is 127 ℃. Compared with that of ultrasonic dispersion, \\u003cem\\u003eT\\u003c/em\\u003e\\u003csub\\u003e\\u003cem\\u003eg\\u003c/em\\u003e\\u003c/sub\\u003e has increased by 4 ℃. The tensile strength (58.9 MPa), elastic modulus (1.928 GPa), and impact strength (8.27 kJ/m\\u0026sup2;) of the composites increased by 42%, 58%, and 92% respectively compared with pure EP. The above experimental results confirm that the introduction of GO can effectively construct a three-dimensional reinforcing network and simultaneously improve the thermal stability and mechanical properties of the EP matrix because of the interface strengthening mechanism.\\u003c/p\\u003e\",\"manuscriptTitle\":\"Study on Preparation and Mechanical Properties for Graphene Oxide/Epoxy Resins Adhesives\",\"msid\":\"\",\"msnumber\":\"\",\"nonDraftVersions\":[{\"code\":1,\"date\":\"2025-05-09 16:46:14\",\"doi\":\"10.21203/rs.3.rs-6538480/v1\",\"editorialEvents\":[{\"type\":\"communityComments\",\"content\":0},{\"type\":\"reviewerAgreed\",\"content\":\"\",\"date\":\"2025-05-06T05:33:32+00:00\",\"index\":0,\"fulltext\":\"\"},{\"type\":\"reviewersInvited\",\"content\":\"\",\"date\":\"2025-05-06T05:02:54+00:00\",\"index\":\"\",\"fulltext\":\"\"},{\"type\":\"editorInvited\",\"content\":\"Journal of Polymer Research\",\"date\":\"2025-05-01T17:11:37+00:00\",\"index\":\"\",\"fulltext\":\"\"},{\"type\":\"editorAssigned\",\"content\":\"\",\"date\":\"2025-04-28T22:33:40+00:00\",\"index\":\"\",\"fulltext\":\"\"},{\"type\":\"submitted\",\"content\":\"Journal of Polymer Research\",\"date\":\"2025-04-28T02:41:32+00:00\",\"index\":\"\",\"fulltext\":\"\"}],\"status\":\"published\",\"journal\":{\"display\":true,\"email\":\"info@researchsquare.com\",\"identity\":\"journal-of-polymer-research\",\"isNatureJournal\":false,\"hasQc\":true,\"allowDirectSubmit\":false,\"externalIdentity\":\"jpol\",\"sideBox\":\"Learn more about [Journal of Polymer Research](https://www.springer.com/journal/10965)\",\"snPcode\":\"10965\",\"submissionUrl\":\"https://www.editorialmanager.com/jpol/\",\"title\":\"Journal of Polymer Research\",\"twitterHandle\":\"\",\"acdcEnabled\":true,\"dfaEnabled\":true,\"editorialSystem\":\"em\",\"reportingPortfolio\":\"Springer Hybrid\",\"inReviewEnabled\":true,\"inReviewRevisionsEnabled\":false}}],\"origin\":\"\",\"ownerIdentity\":\"4f7eb345-cead-4de7-ba29-0baf284d9f7d\",\"owner\":[],\"postedDate\":\"May 9th, 2025\",\"published\":true,\"recentEditorialEvents\":[],\"rejectedJournal\":[],\"revision\":\"\",\"amendment\":\"\",\"status\":\"under-review\",\"subjectAreas\":[],\"tags\":[],\"updatedAt\":\"2025-08-01T08:59:18+00:00\",\"versionOfRecord\":[],\"versionCreatedAt\":\"2025-05-09 16:46:14\",\"video\":\"\",\"vorDoi\":\"\",\"vorDoiUrl\":\"\",\"workflowStages\":[]},\"version\":\"v1\",\"identity\":\"rs-6538480\",\"journalConfig\":\"researchsquare\"},\"__N_SSP\":true},\"page\":\"/article/[identity]/[[...version]]\",\"query\":{\"redirect\":\"/article/rs-6538480\",\"identity\":\"rs-6538480\",\"version\":[\"v1\"]},\"buildId\":\"8U1c8b4HqxoKbykW_rLl7\",\"isFallback\":false,\"isExperimentalCompile\":false,\"dynamicIds\":[84888],\"gssp\":true,\"scriptLoader\":[]}","source_license":"CC-BY-4.0","license_restricted":false}