The influence of epoxy-functionalized acrylonitrile-butadiene-styrene on the properties of PC/ABS alloy

The influence of epoxy-functionalized acrylonitrile-butadiene-styrene on the properties of PC/ABS alloy | 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 The influence of epoxy-functionalized acrylonitrile-butadiene-styrene on the properties of PC/ABS alloy Chao Xu, Shulai Lu, Dai Jingfu, Enzheng Zhou, Ning Kang, Xiaokun Ma This is a preprint; it has not been peer reviewed by a journal. https://doi.org/ 10.21203/rs.3.rs-9042941/v1 This work is licensed under a CC BY 4.0 License Status: Under Revision Version 1 posted 7 You are reading this latest preprint version Abstract In this study, glycidyl methacrylate (GMA) was introduced as the third monomer via emulsion polymerization to modify polybutadiene-styrene-acrylonitrile terpolymer latex, which enabled the grafting of epoxy groups—capable of forming chemical bonds with polycarbonate (PC) resin—onto the modified ABS resin latex. The comprehensive performance of PC/ABS alloys prepared using the modified core-shell structured ABS-g-GMA copolymer was systematically investigated. Fourier transform infrared (FTIR) spectroscopy confirmed the successful grafting of GMA onto the PBSAN latex, while scanning electron microscopy (SEM) revealed that GMA reduced the size of the ABS dispersed phase and enhanced the interfacial compatibility between PC and ABS. Mechanical property analysis demonstrated that when 10 g of GMA was incorporated into the polymerization system, the resulting PC/ABS alloy exhibited a notched impact strength of 60.86 kJ/m² (a 25.43% increase), along with a tensile strength of 59 MPa, a bending strength of 83.531 MPa, and favorable processability. Additionally, the effect of varying ABS proportions in the PC/ABS alloy was explored, and the optimal comprehensive mechanical properties were achieved at a PC/ABS mass ratio of 70:30. Notably, this epoxy-functionalized ABS latex eliminates the need for additional compatibilizers during PC/ABS alloy preparation, providing a simple and feasible approach for fabricating high-performance PC/ABS alloys. Emulsion polymerization epoxy-functionalized ABS PC/ABS Figures Figure 1 Figure 2 Figure 3 Figure 4 Figure 5 Figure 6 Figure 7 Figure 8 Figure 9 1 Introduction Acrylonitrile-butadiene-styrene copolymer (ABS) is a widely utilized engineering plastic, whose molecular structure comprises chemically resistant acrylonitrile, tough butadiene, and easily processable styrene segments [ 1 – 5 ]. Despite its excellent moldability, ABS suffers from low notched impact strength, which restricts its application as a typically notch-sensitive material [ 6 ]. To enhance the impact strength of ABS, blending it with other resins is a common strategy. However, most elastomers incompatible with ABS exhibit poor interfacial compatibility, leading to uneven dispersion of ABS in the matrix and insufficient phase stability—ultimately limiting ABS’s ability to exert an effective toughening effect.PC/ABS composites are a typical example of such blends [ 7 , 8 ]. Owing to the poor compatibility between PC and the polybutadiene (PB) component in ABS, additional compatibilizers are usually required to improve their interfacial adhesion [ 9 – 11 ]. Nevertheless, most commercially available compatibilizers are general-purpose products with relatively high costs, and some show limited efficacy in enhancing the performance of PC/ABS alloys. Compared with simply adding compatibilizers, directly introducing components that improve interfacial bonding into ABS via emulsion polymerization facilitates better dispersion of ABS in PC resin and significantly strengthens the interfacial bonding between the two phases. In this work, glycidyl methacrylate (GMA) was employed as the third grafting monomer to synthesize modified ABS via emulsion polymerization, and this modified ABS was used to prepare PC/ABS alloys without the addition of any external compatibilizers. GMA possesses two functional groups in its molecular structure: a reactive unsaturated double bond and an epoxy group. The unsaturated double bond readily undergoes copolymerization, while the epoxy group tends to undergo ring-opening addition reactions with functional groups (e.g., hydroxyl, carboxyl, amino), enabling the formation of functionalized polymers [ 12 – 17 ]. GMA is relatively easy to prepare, with characteristics of high boiling point, low toxicity, low volatility, and minimal corrosiveness to equipment.Consequently, GMA serves as a versatile functional monomer for the graft modification of polyolefins; it can also react with acrylates, ABS, ACR, and other polymers to produce functionalized materials. Additionally, GMA acts as a compatibilizer to enhance the compatibility of polymer blend systems and as a toughening agent for engineering plastics. GMA-based functionalized toughening agents are primarily used for the toughening modification of esters (e.g., PC, PET, PBT). Compared with commonly used maleic anhydride copolymers, the epoxy groups in GMA more easily react with the terminal carboxyl or hydroxyl groups of polyesters, thereby enhancing compatibility with PC, PET, and PBT and achieving a more significant toughening effect. The toughening modification of ABS has long been a research focus [ 18 – 20 ]. Several studies have investigated the effects of styrene-butadiene-glycidyl methacrylate (SBG) and polybutadiene-grafted methyl methacrylate copolymer (MB) on the toughening of PC/ABS blends.For example, Wang et al. [ 21 ] used SBG (styrene-butadiene-glycidyl methacrylate copolymer) as a reactive compatibilizer. By reacting its epoxy groups with the carboxyl/hydroxyl groups of PC/ABS degradation products, they effectively repaired the polar groups generated during PC/ABS degradation while significantly improving the interfacial compatibility between the PC and ABS phases. This modification increased the impact strength to 9 kJ/m² (2.2 times that of the unmodified sample).However, the addition of SBG requires precise control, with 6 wt% being the optimal dosage. Excessive addition results in phase separation.This modification method not only simultaneously enhances the tensile strength and impact toughness of the recycled PC/ABS (R-PC/ABS), but also notably improves the melt fluidity and processing stability of the material.Zhang et al. [ 22 ] investigated the effect of ABS-g-MAH on the properties of ABS/PC alloys and found that the maleic anhydride groups reacted with the terminal hydroxyl groups of PC to form PC-g-ABS copolymers.Interfacial adhesion was enhanced via molecular chain entanglement, thereby improving the material’s toughness.Experiments demonstrated that adding 10 wt% ABS-g-MAH significantly increased the notched impact strength, while maintaining tensile strength, flexural strength, and Vicat softening temperature (VST) essentially unchanged.However, if the grafting degree (DG) exceeds 1.74 wt% or the addition amount is excessively high, the toughening effect weakens due to increased brittleness.Differential scanning calorimetry (DSC) and scanning electron microscopy (SEM) analyses confirmed that ABS-g-MAH refines and homogenizes the dispersed phase by improving the compatibility of the two phases.Ma et al. [ 23 ] reported that styrene-maleic anhydride copolymer (SMA) can form SMA-g-PC copolymers via in-situ reactions, effectively improving the compatibility of PC/ABS blends and thus significantly enhancing their tensile strength, impact strength, and fatigue performance.Additionally, via cyclic tensile tests and fracture morphology analysis, they found that the fatigue failure of PC/ABS blends is primarily caused by interfacial peeling between the two phases, and the introduction of SMA significantly delays this process by enhancing interfacial bonding.Zuo et al. [ 24 ] proposed an alternative approach that avoids external compatibilizers: they synthesized core-shell structured polybutadiene-grafted methyl methacrylate copolymer (MB) via emulsion polymerization.Transesterification reactions and hydrogen bonding between the PMMA shell and PC significantly enhance the compatibility of PC/ABS blends.When the addition amount of MB is 12 phr, the notched impact strength of the composite reaches 430 J/m², and optimization of the melt flow rate (MFR) enhances processability.Compared with SBG modification, MB directly achieves compatibility between PC and ABS via its core-shell structure, eliminating the sensitivity issue associated with compatibilizer dosage.However, high MB content may still result in rubber phase agglomeration. In this study, glycidyl methacrylate (GMA) was introduced as the third grafting monomer in a redox initiation system via emulsion polymerization. By regulating the stage of GMA addition and investigating its dosage, a modified ABS resin tailored for PC/ABS alloys was prepared; subsequently, PC/modified ABS composites were fabricated via melt blending extrusion without the involvement of other compatibilizers, yielding alloy materials with excellent mechanical properties. Additionally, the effects of GMA introduction on the particle size distribution and residual monomer content of the ABS emulsion were systematically investigated, while the regulatory effects of GMA content in the ABS graft copolymer on the mechanical and thermal properties of PC/modified ABS composites were thoroughly analyzed. Finally, the cross-sectional morphology and microstructure of the deformation zone in the toughened PC/ABS alloy were characterized via scanning electron microscopy (SEM), and the toughening mechanism of the GMA-modified latex during alloy preparation was discussed. 2 Experiment 2.1 Main raw materials Acrylonitrile (AN), polybutadiene latex (PBL), styrene (St), and styrene-acrylonitrile binary copolymer (SAN) were all of industrial grade, supplied by the Synthetic Resin Plant of Jilin Petrochemical Branch, China National Petroleum Corporation. Polycarbonate (PC, grade: 2805) was purchased from Covestro via Shanghai Yilun Plastic Chemical Co., Ltd. Glycidyl methacrylate (GMA, analytical grade) was provided by Suzhou Anli Chemical Co., Ltd.; sodium pyrophosphate (SPP, analytical grade) by Shanghai Bohua Biological Co., Ltd.; glucose (DX, analytical grade) and ferrous sulfate (FeSO₄, analytical grade) by Tianjin Fuchen Chemical Reagent Factory; tertiary dodecyl mercaptan (TDDM, analytical grade) by Shanghai Chemical Reagent Co., Ltd. of Sinopharm Group; and cumene hydroperoxide (CHP, analytical grade) by Fushun Qingyuan Additive Factory. Concentrated sulfuric acid (98.0% w/w purity), deionized water, disproportionated rosin acid soap solution, and antioxidant were all commercially available. 2.2 Instruments and equipment ABS emulsion polymerization unit :3L polymerization kettle, agitator, reflux condenser, constant temperature water bath, temperature control system, peristaltic pump, TOKYORIKA Company, Japan; 30L autoclave: Steam heating, cooling water, temperature control system, electric mixer, NICHIGOENG Company, Japan; dehydrator :SS600-N, Liaoyang Pharmaceutical Machinery Co., LTD. Fluidized bed dryer :NFOD-15, TOKYORIKA, Japan; Twin-screw extruder: TB-35, Nanjing Bosch Company; Electric heating blower drying oven: DHG9070A, Shanghai Yiheng Scientific Instrument Co., LTD. Twin-screw extruder: TB-36, Jiangsu Chengmeng Equipment Co., LTD. Injection molding machine :Victory110, Engel Injection Molding Machinery Co., LTD. Electronic universal testing machine :34TM-10, Instron (Shanghai) Testing Equipment Trading Co., LTD. CEAST9050 impact testing machine High-speed kneader :SHR-100A, Shatong Plastic Machinery Factory, Zhangjiagang City, Jiangsu Province; Scanning electron microscope :JSM-7610FPlus model, Japan Electronics Corporation; Fourier Transform Infrared Instrument :Nicolet6700 model, Thermoelectric Instruments, USA. Thermogravimetric analyzer: TGA4000 model, PE Company, USA 2.3 Preparation of ABS-g-GMA The ABS-g-GMA core-shell emulsion was synthesized via emulsion polymerization in a 3 L three-necked flask equipped with a reflux condenser and a mechanical stirrer. In the initial stage, polybutadiene latex (PBL) was charged into the flask and maintained at 43 ℃ in a water bath. Then, water, acrylonitrile (AN), styrene (St), tertiary dodecyl mercaptan (TDDM), cumene hydroperoxide (CHP), and an activator were successively added. The temperature was then raised to 55 ℃, and the polymerization was allowed to proceed for 1 h.For the incremental feeding stage, a monomer mixture containing AN, St, TDDM, CHP, disproportionated rosin acid soap, and water was prepared. This mixture was heated to 60 ℃ and subsequently added to the reactor continuously over 2 h. In the final stage, the temperature was elevated to 70 ℃, and an antioxidant was introduced to terminate the reaction, affording the target ABS-g-GMA core-shell emulsion.The resulting emulsion was coagulated by adding it to 3 kg of an aqueous sulfuric acid solution (0.33% w/w) at 75 ℃ under stirring. The temperature of the coagulation reactor was then raised to 90 ℃ to complete the process. The coagulum was collected, rinsed three times with distilled water, and separated by centrifugation. The product was finally dried under vacuum at 60 ℃ for 12 h to obtain the ABS-g-GMA graft copolymer powder. The detailed dosages of all reactants are provided in Table 1 . Table 1 Formula of ABS-g-GMA graft Copolymer Types of raw materials Initial stage /g Incremental stage /g Later stage of grafting /g AN 22.467 68.124 — St 57.715 172.425 — Water 374.164 204.771 — PBL 829.016 — — Activator 46.400 — 23.200 TDDM 1.432 0.968 — CHP 0.550 2.200 0.850 Pine soap — 6.400 — 2.4 Preparation of PC/ABS alloy To ensure the processability of the PC/ABS alloy, a SAN resin with high melt flowability was selected. Prior to blending, both the GMA-modified ternary graft copolymer (ABS-g-GMA) and the SAN resin were dried at 80 ℃ for 4 h. The dried components were then blended at a mass ratio of ABS-g-GMA to SAN of 23:77. Specific amounts of ethylene-bis-stearamide (EBA), magnesium stearate (MAGST), and the antioxidant distearyl pentaerythritol diphosphite (SPEP) were added to the mixture.The composition was subsequently mixed using a high-speed mixer for 5 minutes and fed into the hopper of a co-rotating twin-screw extruder for melt compounding and granulation. The temperature profile along the extruder barrel (conveying, plasticizing, and metering sections) and the die was set between 190 ℃ and 210 ℃. The extrudate was cooled in a water bath and cut into cylindrical pellets with dimensions of 3 mm × 3 mm.The resulting GMA-modified ABS resin pellets were dried again at 80 ℃ for 4 h before injection molding. The injection molding process was conducted with a barrel temperature profile of 180, 200, 210, and 220 ℃, an injection pressure of 90 MPa, and a cooling time of 25 seconds to prepare specimens for property testing. Prior to melt processing, both PC and ABS resins were dried to prevent bubble formation during extrusion, which can compromise alloy properties due to moisture absorption from prolonged air exposure. The PC resin was dried at 100 ℃ for 4 hours, and the ABS resin was dried at 80 ℃ for 4 hours in a forced-air convection oven. Subsequently, the pre-dried GMA-modified ABS, PC resin, and additives were blended in a high-speed mixer at a predetermined ratio. The mixture was then melt-compounded using a co-rotating twin-screw extruder. The temperature settings for the extruder's conveying, plasticizing, metering sections, and die were maintained between 220 ℃ and 250 ℃. The resulting PC/ABS alloy was dried again at 100 ℃ for 4 hours before injection molding. The injection molding process was carried out with barrel zone temperatures set at 180 ℃, 245 ℃, 250 ℃, and 255 ℃, an injection pressure of 90 MPa, and a cooling time of 25 seconds. Finally, all test specimens were conditioned at constant temperature away from light for 2 hours before mechanical property analysis. 2.5 Testing and Characterization Grafting rate test: Accurately weigh approximately 1g of ABS powder sample into a already weighed centrifuge tube, add about 20mL of acetone, and shake for 24 hours to ensure it is fully dissolved. Then, centrifuge for 8 minutes at 3℃ ~4℃ and 18,000 RPM /min, transfer the supernatant, and repeat the washing operation twice. The remaining insoluble substances and centrifuge tubes were dried at 50℃ under normal pressure for 24 hours, then transferred to an 80℃ vacuum oven for drying for 24 hours. After cooling, they were weighed. Notch impact strength test: It is carried out in accordance with GB/T 1843–2008. Firstly, the standard impact spline formed by injection molding is processed. A standard V-shaped notch is milled in the middle part of one side of it, and it is ensured that the depth of this notch is 2mm. All the prepared splines were adjusted at room temperature for 24 hours and then tested using a pendulum at 2.75J. Tensile properties (including tensile strength and elongation at break) test: conducted in accordance with GB/T 1040.2–2022: Firstly, clamp the standard dumbbell-shaped spline formed by injection molding and stretch it at a test rate of 50 mm/min until the spline breaks; All splines were adjusted at room temperature for 24 hours and then tested using a universal testing machine equipped with an extensometer. Bending strength test: It is carried out in accordance with GB/T 9341 − 2008. The standard sample formed by injection molding is placed on two supports. A three-point bending loading method is adopted, and pressure is applied to the sample at a test rate of 2 mm/min until the specified deflection is reached or fracture occurs. All splines were tested after being adjusted at room temperature for 24 hours. Infrared testing: Samples are tested using Fourier Transform infrared spectroscopy (FTIR) equipped with attenuated total reflection (ATR) accessories. Before the test, place a small amount of dry sample directly on the detection surface of the ATR crystal, and apply appropriate pressure through the pressure rod to ensure that the powder is in close contact with the crystal surface. Spectra were collected directly in transmission mode, with a scanning wavenumber range of 4000 to 400 cm⁻¹ and a resolution of 4 cm⁻¹. A total of 32 scans were conducted to eliminate background noise. When testing the infrared of ABS-g-GMA powder, the powder needs to be separated for testing. The separation method is as follows: Take 2 g of the dried ABS-g-GMA powder and put it into a hard centrifuge tube. Dissolve the free chain segments in it with 35 mL of acetone solution. Place the centrifuge tubes on a constant temperature shaker at 25 ℃ and shake for 12 hours. Then, put the tubes on an ultracentrifuge for centrifugal separation at a speed of 10,000 r /min for 30 minutes. After centrifugation, pour out the supernatant. Repeat the above operation three times. All the supernatant obtained from the three times was placed in a beaker and dried to a constant weight to obtain the free chain segments dissolved in acetone, which were named SAN-g-GMA. The remaining part was placed in an oven at 65 ℃ and dried to a constant weight to obtain ABS-g-GMA after the free chains were removed. Vicat softening temperature test: Conducted in accordance with GB/T 1633–2000: Place the flat sample with a thickness exceeding 3mm horizontally on the support, press the flat-head needle with a cross-sectional area of 1mm ² vertically into the surface of the sample under a load of 50N, and heat it at a uniform rate of 50 ℃/h; All samples were tested after being adjusted at room temperature for 24 hours. The temperature at which the needle was pressed into the sample to a depth of 1 mm was recorded, which was the Vicat softening temperature. Scanning electron microscopy test: Select appropriate fracture spline, cut a 10mm thick sample along the cross-section, spray gold on the cross-section, and observe and take photos on the JSM-6610LV scanning electron microscope (SEM). When determining the compatibility of PC/ABS alloys, the ABS in the blend needs to be etched off. The cross-sectional treatment is as follows: At a constant temperature of 80℃, the sample piece is gently rotated in chromic acid wash solution with a sub-clamp for 8 minutes, and then ultrasonically cleaned for 15 minutes. After that, it is taken out and dried. Epoxy value test: The epoxy value test method is carried out in accordance with the national standard GB1677 test standard for hydrochloric acid and acetone method. Accurately weigh 2-4mg of epoxy equivalent epoxy resin sample and place it in a 250mL sealed flask. Add 20mL of 0.2mo/ L hydrochloric-acetone solution with a pipette, shake well to ensure complete dissolution of the sample. After standing at room temperature for 15 minutes, add 25mL of neutral ethanol. Then titrate the excess hydrochloric acid with a 0.1mol/L sodium oxide standard solution. The end point of titration is when the cresol red indicator in ethanol-acetone solution changes from pink to yellow first and then gradually to purple. Make a blank sample again. Thermogravimetric test: The thermal stability of the sample is tested using a thermogravimetric analyzer. Before the test, cut the sample into a solid state and accurately weigh 5mg of the sample and place it in an alumina crucible. The test was conducted in a nitrogen atmosphere with a nitrogen flow rate of 20mL/min. The heating range was from room temperature to 600℃, and the heating rate was 10℃/min. By recording the variation of sample mass with temperature, the parameters related to thermal stability such as thermal decomposition temperature and weight loss rate were analyzed. DSC test: The thermal performance of the sample is analyzed using a differential scanning calorimeter. Take 5mg of the sample and seal it in an aluminum sample cell, using an empty aluminum cell as the reference. The test was conducted under nitrogen protection with a nitrogen flow rate of 50 ml /min. The test procedure was as follows: First, the temperature was raised from room temperature to 250℃ and maintained for 5 minutes to eliminate the thermal history of the sample. Then, the temperature was reduced to -50 ℃ at a rate of 10℃/min, and the temperature was raised to 250℃ at the same rate. Record parameters such as the glass transition temperature, melting temperature, crystallization temperature of the sample and the corresponding enthalpy changes. 3 Results and Discussion 3.1 Performance analysis of modified latex Table 2 The emulsion properties of ABS-g-GMA Raw material type GMA /g Solid /% Grafting rate/% pH Particle size /um Stability None GMA 0 40.59 85.97 11.2 320.3 Stable GMA was added at the initial stage 10 \ \ \ \ Massive sedimentation GMA was added at the incremental stage 10 34.92 81.31 10.71 345.4 Granular sedimentation GMA was added at the later stage of grafting 10 42.64 86.37 10.1 362.7 Stable The emulsion polymerization process of GMA grafted modified ABS can be divided into three stages: the initial stage of emulsion polymerization, the increment stage and the later stage of curing. Table 2 lists the performance data of GMA and unmodified emulsion added in the three stages. The results show that when 10g of GMA is added at the initial stage of polymerization, due to the presence of a large amount of butadiene latex at this stage, GMA undergoes rapid copolymerization with it, generating a large number of short-chain and structurally disordered polymers, which will destroy the stability of the emulsion and lead to solid precipitation and demulsification. When GMA is added in the incremental stage, the polymerization reaction rate is relatively stable. The ternary copolymer latex has grown to a certain chain segment, and the system has a certain buffering capacity. Some granular precipitates are produced, which will not lead to demulsification of the polymerization system. In the later stage of the polymerization reaction's maturation, the addition of GMA can more stably graft with PB latex. At the same time, it can also react the unreacted styrene and acrylonitrile monomers in the system, thereby improving the residual monomer content of PB latex. The mechanism of GMA grafting modification was further explored based on the solid content, grafting rate and particle size data listed in Table 2 , as shown in Fig. 1 . As shown in Fig. 1 , at the initial stage of emulsion polymerization, when AN and St monomers are just added to the PBL latex, the grafting reaction is incomplete in the initial stage of the reaction. If GMA monomers are added at this time, the double bonds in the GMA molecules will compete with AN and St for the opportunity to polymerize with the PBL latex, resulting in cross-linking reactions and preventing the latex from fully forming stable polymer segments. The formation of blocky precipitates that disrupt the stability of the latex subsequently leads to demulsification. During the incremental reaction stage, some AN and St monomers have been grafted onto the surface of butadiene latex, forming a certain latex grafting layer. At this point, the introduction of GMA monomers can achieve a grafting rate of 81.31%, which is lower than the grafting rate of 85.97% of the unmodified ABS latex. This is because GMA will form a large number of by-products with AN and St, but does not form a good modified grafting. A large number of by-products will inevitably affect the improvement of the grafting rate. Meanwhile, the solid content of the system also decreased from 40.59% to 34.92%, which confirmed that the small-molecule by-products reduced the grafting rate of PB latex. The corresponding reaction equations are listed in Fig. 2 . A large amount of by-products of GMA grafted monomers were generated during the polymerization process, which not only led to incomplete ABS emulsion polymerization reaction but also further affected the impact performance of the subsequent PC/ ABS alloy, reducing it from 48.52 to 35.27 KJ/m 2 . In the later stage of polymerization and curing, most of the AN and St monomers have been grafted onto the PB latex. The grafting reaction generates high-molecular chains, and the particle size of the emulsion gradually increases, forming a stable emulsion system with a core-shell structure. At this point, the introduction of GMA monomers cannot react with AN and St to form by-products. The epoxy groups in GMA will first undergo hydrolysis under alkaline conditions, as shown in Fig. 3 Recation 1. This conclusion can be proved by the determination results of the epoxy values of the emulsion in Fig. 3 (d). The epoxy values in the emulsions with GMA added are all close to 1 PPM, indicating that most of the epoxy groups have been hydrolyzed. At this point, the GMA molecule breaks the acrylate double bond and can be grafted onto the surface of the core-shell structure of the PBL latex, further increasing the particle size to 362.7 µ m and forming the ABS-g-GMA grafted polymer, as shown in Reaction 3. The latex ABS-g-GMA modified by GMA grafting can effectively improve the compatibility between PC and ABS, and the impact strength of PC/ABS alloy is increased from 48.52 to 60.86KJ/m 2 . Figure 3 (a) shows the particle size distribution of the ABS-g-GMA emulsion prepared by graft polymerization with different amounts of GMA added to the ABS emulsion in the later stage of curing. As can be seen from the figure, with the increase of GMA dosage, the particle size of the emulsion gradually increases, confirming that in the later stage of curing, the addition of GAM can graft onto the latex particles, so the particle size will increase significantly. An appropriate amount of GMA can improve the uniformity of particle size in emulsions. However, when GMA is in excess, the particle size distribution becomes wider instead, indicating an uneven grafting phenomenon. Therefore, excessive GMA cannot provide good stability for the polymerization system. Figures 3 (b) and 3(c) respectively show the changing trends of pH value, grafting rate and solid content of the emulsion. As shown in Fig. 3 (b), the pH value gradually decreases as the amount of GMA added increases. The continuous decline in pH value also stems from the fact that after GMA is added to the system, under alkaline conditions, the ring-opening of epoxy groups consumes OH- in the emulsion system. As shown in Fig. 3 (c), when the GMA concentration is low, the grafting rate drops from the initial 85.97% to 84.17%. This is because the active GMA monomers in the system react with the unreacted AN and St, resulting in the formation of excessive small molecule polymer segments. These small molecules dissolve in acetone during the grafting test, thus causing the grafting rate to decrease. However, as the concentration of GMA increases, more GMA will be grafted onto the ternary copolymer latex particles to form the modified ABS-g-GMA grafted copolymer. The enhanced grafting reaction promotes the growth and cross-linking of the polymer molecular chain, forming a larger-sized molecular structure. This chemically grafted polymer will not dissolve in acetone, so the grafting rate will show an upward trend. Figure 3 (d) shows the results of the determination of acrylonitrile, butadiene and styrene residual monomers in the emulsion by chromatography. When GMA is not added, the residual amounts of acrylonitrile and butadiene in ABS emulsion are relatively high, at 48.4367ppm and 584.1975ppm respectively. This is due to the incomplete reaction of AN and St monomers during the polymerization process and is also one of the main sources of industrial wastewater pollution. After the introduction of GMA, the residual amounts of acrylonitrile and butadiene were significantly reduced to below 1ppm. This is mainly because, in addition to participating in the graft modification reaction, GMA can also react with unreacted acrylonitrile, styrene and other monomers in the system, effectively capturing the residual monomers and generating oligomolymer small molecules, which has a positive significance for reducing wastewater discharge. 3.2 Mechanical properties of alloys In order to further explore the influence of GMA-modified latex on PC/ABS alloys, the variation laws of mechanical properties of the alloys under different PC/ABS ratios and different GMA modification amounts were systematically investigated. Four compound ratios of PC to ABS, namely 50:50, 60:40, 70:30 and 80:20, were selected. Under each ratio condition, the GMA addition amount of the modified ABS powder was changed. The mechanical property analysis diagram is shown in Fig. 4 . Figure 4 (a) shows the impact strength curves of alloys with different proportions varying with the amount of modified GMA. With the increase of GMA addition, the impact strength curves all show a trend of first increasing and then decreasing. When the PC/ABS ratio is 70/30 and the GMA addition amount is 10g, the increase in impact strength is the most significant, reaching 25.43%. The impact strength has increased from 48.52 kJ/m² to 60.86 kJ/m². Except for the maximum impact value of the PC: ABS = 50:50 ratio when the GMA addition amount is 7.5g, the highest impact strength values of other alloy ratios are all when the GMA addition amount is 10g. When the addition amount of GMA is too high, in addition to the effective grafting rate of ABS-g-GMA modified latex, small molecules of styrene and acrylonitrile grafted with GMA will also be formed, thereby reducing the interface compatibility between PC and ABS, and thus the impact performance of the alloy will also decrease. The changing trends of tensile and bending properties also show a trend of first increasing and then decreasing, as shown in Figs. 4 (b) and (c). For the PC/ABS = 80/20 system, 10g GMA enables the tensile strength to reach a peak of 59.8 MPa and the flexural strength to reach a peak of 84.303 MPa. Except for the PC/ABS = 60/40 system where the tensile strength reached the peak of 57.3 MPa at 7.5g GMA, the tensile peaks of other proportions all occurred when the addition amount of GMA was 10g. Because the increase in PC resin content is beneficial to the processing performance of PC/ABS alloy, both tensile properties and bending properties gradually increase with the increase of PC content. As shown in Fig. 4 (d) from the elongation at break curve, the peak values of all proportion alloys occur when the GMA addition amount is 10g. The elongation at break and impact strength are more sensitive to the interfacial bonding between PC and ABS resins. The modified grafted ABS elastomer in the alloy will enhance the flexibility of the molecular chain. Therefore, only under the optimal grafting rate of ABS-g-GMA modified latex can the highest impact strength and elongation at break be obtained. Based on the above mechanical properties, when the addition amount of GMA is 10g, the alloy prepared from the modified grafted ABS resin has more superior performance. Moreover, under the alloy ratio of PC/ABS = 70/30, the comprehensive performance of the obtained alloy can all meet the application requirements of PC/ABS alloy in the automotive field. 3.3 Analysis of thermal properties of alloys Vicat softening point is suitable for controlling the quality of polymers and as an indicator for identifying the thermal performance of new varieties. It is tested under constant heating conditions and is a method for evaluating the high-temperature deformation trend of thermoplastics. The Vicat softening point trends of alloy resins with different PC/ABS ratios varying with the addition amount of GMA are shown in Fig. 5 . Firstly, the heat distortion temperature of PC/ABS alloy increases with the increase of PC content in the blend, from 104.7℃ when PC:ABS = 50:50 to 124.5℃ when PC:ABS = 80:20. The thermal decomposition temperature of PC resin is 480℃, which is significantly higher than that of ABS resin at 360℃. Therefore, an increase in the proportion of PC resin will significantly improve the thermal performance of PC/ABS alloy resin. No matter what proportion is used, the appropriate addition of GMA only slightly enhances the heat resistance of the alloy. This might be because GMA-modified latex can effectively improve the compatibility between PC and ABS, enhance the interfacial bonding force of plastic materials, and make the molecules at the interface more compact. The significant difference in the melting temperatures of PC and ABS resins makes the variation trend of the influence of GMA-modified latex on the thermal properties of PC/ABS alloys through interface modification not obvious. Figure 6 (a) shows the thermogravimetric curves of different PC/ABS ratios when the GMA addition amount is 10g. As the proportion of PC increases, the weight loss rate of the alloy at the same temperature varies. As the temperature rises, the residual mass fraction of PC/ABS alloy after decomposition increases with the increase of PC proportion. This result is consistent with the above-mentioned variation trend of PC/ABS alloy at the microcard softening point. This is because PC resin has higher heat resistance, so when ABS resin thermally decomposes, the residual mass with a higher PC content is higher. At around 600℃, the residual mass fraction of PC/ABS = 50/50 is approximately 7.37%, while that of PC/ABS = 80/20 is about 14.18%. Figure 6 (b) shows the influence of different GMA addition amounts on the thermal stability of the alloy at the alloy ratio of PC: ABS = 70:30. The weight loss rate of the alloy prepared from GMA-modified ABS latex in the range of 400–500℃ is significantly lower than that of the system without GMA added. At 500℃, the residual mass fraction of the unmodified alloy is approximately 21%, while the residual amounts of the alloy obtained when the GMA addition amounts are 5g, 10g, and 15g are approximately 27%, 31%, and 23% respectively. This confirms that the addition of GMA-modified ABS powder can improve the thermal stability of PC/ABS alloy in the medium-temperature range. Within the range of 400–500℃, when the addition amount of GMA is 15g, the thermal weight loss rate of the alloy is faster than that when the addition amount of GMA is 10g. This thermal performance analysis result also confirms that in the 3L latex system, when the addition amount of GMA is 10g, the grafting effect of ABS-g-GMA modified latex is the best, and it is the best for improving the interfacial bonding of PC/ABS alloy. 3.4 Infrared spectroscopy analysis The verification of grafting between GMA and the ternary copolymer PB latex was based on their differential solubility in acetone. The GMA-modified latex was centrifuged with acetone to dissolve away any ungraf ted linear macromolecules. Because the grafted PB latex is cross-linked into a three-dimensional network, it is only swollen by acetone and remains undissolved. Hence, the characteristic peaks observed in the FTIR spectrum of this insoluble material thus provide direct evidence for the success of the ABS-g-GMA grafting modification, as shown in Fig. 7 . The FTIR spectra in Fig. 7 compare unmodified ABS with GMA-grafted ABS. The appearance of a new absorption peak at 1730 cm⁻¹ in the modified sample is attributed to the carbonyl group (C = O) of GMA, confirming the successful grafting of GMA onto the ABS backbone. Furthermore, the intensity of this peak increases with the GMA loading, which is associated with the presence of free (ungrafted) GMA homopolymer. The incorporation of GMA is expected to enhance the compatibility between PC and ABS during melt blending, as the epoxy groups in GMA can react with the end groups of PC. This improved compatibility ultimately leads to superior physical properties of the PC/ABS alloy. 3.5 Analysis of alloy interface (a) No GMA; (b) 5g GMA; (c) 10gGMA; (d) 15gGMA; Table 3 The surface hole characteristic data of PC/ABS alloy SEM images under different GMA addition amounts GMA /g Number of holes Average area/um 2 0-0.2um 2 0.2-0.4um 2 0.4-0.6um 2 0.6-0.8um 2 0.8-1.0um 2 1.0-1.2um 2 0 421 0.79 62.5% 15.2% 7.3% 7.0% 4.2% 3.7% 5 988 0.17 69.1% 22.7% 5.3% 2.4% 0 0.4% 10 1292 0.09 89.9% 7.3% 2.2% 0.5% 0 0 15 1136 0.10 87.3% 10.6% 1.4% 0.7% 0 0 The microscopic morphology of the compatible interface of the PC/ABS blend system with different GMA addition amounts was observed by scanning electron microscopy. As shown in Fig. 8 , it is the impact cross-section diagram of the PC/ABS composite material obtained by adding different GMA in the later stage of ABS emulsion polymerization and curing. The ratio of PC to ABS is 70:30. The sample is immersed in chromic acid solution to etch away the ABS dispersed phase in the alloy, allowing for a more intuitive observation of the distribution state of ABS in the PC resin. Table 3 shows the specific data of ABS holes statistically analyzed by Image J. The pore structure on the surface of PC/ABS alloy reflects the dispersion state of the ABS phase. As shown in Fig. 8 (a), in the absence of additives, the ABS phase in the impact section of the PC/ABS alloy forms various types of unevenly sized strip holes (with an average area of 0.79 µm² and holes greater than 0.4 µm² accounting for 22.3%), indicating that the ungrafted modified ABS has poor dispersion and compatibility with PC. Figures 8 (b) and (c) respectively show the impact cross-sections of PC/ABS composites after adding 5g and 10g GMA. From the SEM images, it can be seen that the GMA-modified ABS resin is more evenly dispersed in the PC phase, and the large-sized pores are significantly reduced. When 10gGMA was added, the number of holes larger than 0.8um ² was 0, and the total number of holes increased from 421 to 1292. This fully confirmed that the ABS-g-GMA modified latex has a good effect on improving the compatibilization of the PC/ABS alloy system. However, when the addition amount of GMA increased to 15g as shown in Fig. 8 (d), both the PC phase and the ABS phase presented large-area continuous phases, and the proportion of large holes in the pore distribution also increased compared to Fig. 8 (c). This is consistent with the test results of the effective GMA-modified grafting rate when the addition amount of GMA is different, indicating that only when GMA is effectively grafted onto the ABS ternary polymer latex can a better interface grafting effect be provided in the preparation process of PC/ABS alloy. Simply adding too much GMA modified monomer will only be beneficial in capturing the unpolymerized AN and St monomers. Therefore, the optimal addition amount of GMA in a 3L latex polymerization system is 10g. 3.6 Principle analysis Based on the above analysis and experimental results of GMA-modified latex, the mechanism of the compatibilization effect of GMA-grafted modified ABS-g-GMA latex on PC/ABS alloy is shown in Fig. 9 . Firstly, it was confirmed that after GMA was added in the later stage of the emulsion polymerization reaction, it could be grafted onto the ternary copolymer latex, and its unsaturated double bond would undergo a polymerization reaction with the PBL latex. Meanwhile, in the polymerization system with a pH value of 10, the epoxy groups of GMA will react to open the ring and form -OH, as shown in reaction (1) of Fig. 2 . The carboxyl and hydroxyl groups carried in PC resin can react with the epoxy groups interrupted by ABS-g-GMA, as shown in reactions (1) and (2) of Fig. 9 . It is worth mentioning that this type of reaction can generate PC-co-ABS copolymers with special structures in situ at the interface of the two phases. This in-situ generated copolymer can be regarded as an efficient compatibilizer, significantly improving the compatibility of the blend system through the following dual mechanism of action. This PC-co-ABS copolymer promotes the refinement of dispersed phase particles by reducing the interphase interface free energy. At the same time, the agglomeration of dispersed phase particles can also be effectively inhibited through the steric hindrance effect. The synergistic effect of these two mechanisms eventually led to the formation of a microstructure with smaller dispersed phase size and more uniform distribution in the PC/ABS-g-GMA blend, thereby obtaining significantly optimized morphological characteristics. Reaction 3 and Reaction 4 are two types of cross-linking reactions with significantly different characteristics in the blend system. Reaction 3 originates from the self-crosslinking of hydroxyl groups at the interface of PC-co-ABS copolymer, mainly occurring within the dispersed phase. Reaction 4, on the other hand, is based on the bifunctional properties of the PC matrix and is achieved through interfacial cross-linking reactions with the disconnected epoxy groups. When the GMA content is too high, the excessive cross-linking reaction leads to an increase in the viscosity of the system, thereby interfering with the formation of phase morphology, ultimately intensifying phase separation and increasing the size of the dispersed phase. However, reaction 4 is more difficult to occur than Reaction 3, mainly due to the following two reasons. First, Reaction 4 relies on the interaction at the interface of the two phases, while Reaction 3 occurs directly within the dispersed phase. Therefore, ABS-g-GMA is more likely to diffuse in the dispersed phase and promote the occurrence of reaction 3. Secondly, the volume increase reactions 1 and 2 will reduce the concentrations of carboxyl groups, hydroxyl groups on PC and the broken epoxy groups on ABS-g-GMA, thereby inhibiting the rate of reaction 4. However, for reaction 3, although the broken epoxy groups decrease, the hydroxyl group concentration on the PC-CO-ABS copolymer increases instead due to the volume increase reaction, allowing reaction 3 to still proceed at a relatively high rate. Therefore, when GMA is in excess, reaction 3 becomes the dominant crosslinking reaction in the PC/ABS-g-GMA blend, and its influence on the phase morphology is more significant. This changing trend is mainly attributed to the bifunctional characteristics of GMA. Its acrylate double bond can undergo graft copolymerization with the ABS component, while the epoxy group can react with the carbonate group of PC. Therefore, appropriate GMA graft polymerization has a significant effect on improving the two-phase compatibility of PC and ABS resins. 4 Conclusion This study addresses the industrial application pain point of PC/ABS alloy, which is low impact strength and limited processing performance due to poor compatibility between PC and ABS. It proposes a method of preparing functionalized ABS (ABS-g-GMA) by in-situ grafting GMA through emulsion polymerization to achieve the preparation of self-reactive compatible groups and improve the mechanical properties of PC/ABS alloy. By regulating the stage and dosage of GMA addition, and combining FTIR, SEM, mechanical testing and thermal analysis, the correlation rules between key process parameters and alloy properties were clarified. Adding 10gGMA in the later stage of emulsion polymerization can ensure system stability and reduce residual single emissions. The ABS-g-GMA prepared under this condition can strengthen the PC/ABS interface through chemical grafting reaction, enabling the optimal comprehensive mechanical properties of the PC/ABS = 70/30 alloy with notched impact strength reaching 60.86kJ/m², tensile strength of 59MPa, and flexural strength of 83.531MPa. At the same time, the Vicat softening temperature and the thermal stability in the medium-temperature range were significantly improved. This method not only resolves the interfacial bonding issue of PC/ABS alloys, but also facilitates the reduction of industrial emissions through the side reactions of GMA with residual AN and St monomers, meeting the demand for high-performance PC/ABS alloys in fields such as electronics and electrical appliances, and automotive parts, and achieving convenient industrial production of PC/ABS alloys. Declarations Author Contribution X.C. and M.X. conceptualized the study. X.C. performed investigation and formal analysis, and wrote the original draft. L.S. contributed to methodology, validation, and project administration. D.J. conducted experiments and curated data. Z.E. analyzed data and prepared visualizations. K.N. provided resources and funding. M.X. supervised the work, reviewed and edited the manuscript, and acquired funding. 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J Polym Sci Part B Polym Phys 43:2170–2180. https://doi.org/10.1002/polb.20453 Sun S, Zhang M, Zhang H, Zhang X (2011) Polylactide toughening with epoxy-functionalized grafted acrylonitrile–butadiene–styrene particles. J Appl Polym Sci 122:2992–2999. https://doi.org/10.1002/app.34111 Additional Declarations No competing interests reported. Cite Share Download PDF Status: Under Revision Version 1 posted Editorial decision: Revision requested 29 Mar, 2026 Reviews received at journal 28 Mar, 2026 Reviewers agreed at journal 19 Mar, 2026 Reviewers invited by journal 13 Mar, 2026 Editor assigned by journal 12 Mar, 2026 Submission checks completed at journal 12 Mar, 2026 First submitted to journal 05 Mar, 2026 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. 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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-9042941","acceptedTermsAndConditions":true,"allowDirectSubmit":false,"archivedVersions":[],"articleType":"Research Article","associatedPublications":[],"authors":[{"id":605650586,"identity":"9b27bdee-32e6-43b0-a3e0-288b2fb15387","order_by":0,"name":"Chao Xu","email":"","orcid":"","institution":"Jilin University of Chemical Technology","correspondingAuthor":false,"prefix":"","firstName":"Chao","middleName":"","lastName":"Xu","suffix":""},{"id":605650587,"identity":"b4e6241b-d05b-4420-a897-98b609968cfe","order_by":1,"name":"Shulai Lu","email":"","orcid":"","institution":"Research Institute of Jilin Petrochemical 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07:58:08","extension":"png","order_by":5,"title":"Figure 5","display":"","copyAsset":false,"role":"figure","size":62592,"visible":true,"origin":"","legend":"\u003cp\u003e\u003cstrong\u003eThe influence of different GMA addition amounts and PC/ABS ratios on the Vicat softening temperature of PC/ABS alloys\u003c/strong\u003e\u003c/p\u003e","description":"","filename":"image5.png","url":"https://assets-eu.researchsquare.com/files/rs-9042941/v1/db601c333c5c6c57e95845e5.png"},{"id":104783147,"identity":"f4f6d163-789a-4999-b7c0-152b0548aa80","added_by":"auto","created_at":"2026-03-17 07:58:17","extension":"png","order_by":6,"title":"Figure 6","display":"","copyAsset":false,"role":"figure","size":117406,"visible":true,"origin":"","legend":"\u003cp\u003e\u003cstrong\u003eThermogravimetric curves of PC/ABS alloys prepared under different GMA addition amounts and PC/ABS ratios\u003c/strong\u003e\u003c/p\u003e","description":"","filename":"image6.png","url":"https://assets-eu.researchsquare.com/files/rs-9042941/v1/2d8b5c7ba1333eaa26658e86.png"},{"id":104737131,"identity":"35173a61-bcf1-4ec9-8287-033aa59521bf","added_by":"auto","created_at":"2026-03-16 15:35:24","extension":"png","order_by":7,"title":"Figure 7","display":"","copyAsset":false,"role":"figure","size":220446,"visible":true,"origin":"","legend":"\u003cp\u003e\u003cstrong\u003eFTIR spectra of GMA-modified ABS material\u003c/strong\u003e\u003c/p\u003e","description":"","filename":"image7.png","url":"https://assets-eu.researchsquare.com/files/rs-9042941/v1/c522407512728e72f526c60f.png"},{"id":104737132,"identity":"88fa2e7f-cd44-4099-b35d-2bea78c4ec8f","added_by":"auto","created_at":"2026-03-16 15:35:24","extension":"png","order_by":8,"title":"Figure 8","display":"","copyAsset":false,"role":"figure","size":719564,"visible":true,"origin":"","legend":"\u003cp\u003e\u003cstrong\u003eSEM images of the notched impact cross-section of PC/ABS alloy prepared with different GMA addition amounts at room temperature:\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003e(a) No GMA; (b) 5g GMA; (c) 10gGMA; (d) 15gGMA;\u003c/strong\u003e\u003c/p\u003e","description":"","filename":"image8.png","url":"https://assets-eu.researchsquare.com/files/rs-9042941/v1/0e62f492659207563d5b7599.png"},{"id":104783232,"identity":"640e7ba6-24b7-4f1d-8e5f-dda3be9e8cd2","added_by":"auto","created_at":"2026-03-17 07:58:26","extension":"png","order_by":9,"title":"Figure 9","display":"","copyAsset":false,"role":"figure","size":165140,"visible":true,"origin":"","legend":"\u003cp\u003e\u003cstrong\u003eThe mechanism diagram of the compatibilization effect of GMA graft-modified ABS-g-GMA latex on PC/ABS alloy\u003c/strong\u003e\u003c/p\u003e","description":"","filename":"image9.png","url":"https://assets-eu.researchsquare.com/files/rs-9042941/v1/afd62eb2f404902382e6dc45.png"},{"id":104810603,"identity":"f9687a1d-21f8-469e-8fa4-4041ef45bc0f","added_by":"auto","created_at":"2026-03-17 12:55:35","extension":"pdf","order_by":0,"title":"","display":"","copyAsset":false,"role":"manuscript-pdf","size":2831730,"visible":true,"origin":"","legend":"","description":"","filename":"manuscript.pdf","url":"https://assets-eu.researchsquare.com/files/rs-9042941/v1/65188f5b-e426-49bc-85d9-7ac714847f8d.pdf"}],"financialInterests":"No competing interests reported.","formattedTitle":"The influence of epoxy-functionalized acrylonitrile-butadiene-styrene on the properties of PC/ABS alloy","fulltext":[{"header":"1 Introduction","content":"\u003cp\u003eAcrylonitrile-butadiene-styrene copolymer (ABS) is a widely utilized engineering plastic, whose molecular structure comprises chemically resistant acrylonitrile, tough butadiene, and easily processable styrene segments [\u003cspan additionalcitationids=\"CR2 CR3 CR4\" citationid=\"CR1\" class=\"CitationRef\"\u003e1\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR5\" class=\"CitationRef\"\u003e5\u003c/span\u003e]. Despite its excellent moldability, ABS suffers from low notched impact strength, which restricts its application as a typically notch-sensitive material [\u003cspan citationid=\"CR6\" class=\"CitationRef\"\u003e6\u003c/span\u003e]. To enhance the impact strength of ABS, blending it with other resins is a common strategy. However, most elastomers incompatible with ABS exhibit poor interfacial compatibility, leading to uneven dispersion of ABS in the matrix and insufficient phase stability\u0026mdash;ultimately limiting ABS\u0026rsquo;s ability to exert an effective toughening effect.PC/ABS composites are a typical example of such blends [\u003cspan citationid=\"CR7\" class=\"CitationRef\"\u003e7\u003c/span\u003e, \u003cspan citationid=\"CR8\" class=\"CitationRef\"\u003e8\u003c/span\u003e]. Owing to the poor compatibility between PC and the polybutadiene (PB) component in ABS, additional compatibilizers are usually required to improve their interfacial adhesion [\u003cspan additionalcitationids=\"CR10\" citationid=\"CR9\" class=\"CitationRef\"\u003e9\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR11\" class=\"CitationRef\"\u003e11\u003c/span\u003e]. Nevertheless, most commercially available compatibilizers are general-purpose products with relatively high costs, and some show limited efficacy in enhancing the performance of PC/ABS alloys. Compared with simply adding compatibilizers, directly introducing components that improve interfacial bonding into ABS via emulsion polymerization facilitates better dispersion of ABS in PC resin and significantly strengthens the interfacial bonding between the two phases. In this work, glycidyl methacrylate (GMA) was employed as the third grafting monomer to synthesize modified ABS via emulsion polymerization, and this modified ABS was used to prepare PC/ABS alloys without the addition of any external compatibilizers.\u003c/p\u003e \u003cp\u003eGMA possesses two functional groups in its molecular structure: a reactive unsaturated double bond and an epoxy group. The unsaturated double bond readily undergoes copolymerization, while the epoxy group tends to undergo ring-opening addition reactions with functional groups (e.g., hydroxyl, carboxyl, amino), enabling the formation of functionalized polymers [\u003cspan additionalcitationids=\"CR13 CR14 CR15 CR16\" citationid=\"CR12\" class=\"CitationRef\"\u003e12\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR17\" class=\"CitationRef\"\u003e17\u003c/span\u003e]. GMA is relatively easy to prepare, with characteristics of high boiling point, low toxicity, low volatility, and minimal corrosiveness to equipment.Consequently, GMA serves as a versatile functional monomer for the graft modification of polyolefins; it can also react with acrylates, ABS, ACR, and other polymers to produce functionalized materials. Additionally, GMA acts as a compatibilizer to enhance the compatibility of polymer blend systems and as a toughening agent for engineering plastics. GMA-based functionalized toughening agents are primarily used for the toughening modification of esters (e.g., PC, PET, PBT). Compared with commonly used maleic anhydride copolymers, the epoxy groups in GMA more easily react with the terminal carboxyl or hydroxyl groups of polyesters, thereby enhancing compatibility with PC, PET, and PBT and achieving a more significant toughening effect.\u003c/p\u003e \u003cp\u003eThe toughening modification of ABS has long been a research focus [\u003cspan additionalcitationids=\"CR19\" citationid=\"CR18\" class=\"CitationRef\"\u003e18\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR20\" class=\"CitationRef\"\u003e20\u003c/span\u003e]. Several studies have investigated the effects of styrene-butadiene-glycidyl methacrylate (SBG) and polybutadiene-grafted methyl methacrylate copolymer (MB) on the toughening of PC/ABS blends.For example, Wang et al. [\u003cspan citationid=\"CR21\" class=\"CitationRef\"\u003e21\u003c/span\u003e] used SBG (styrene-butadiene-glycidyl methacrylate copolymer) as a reactive compatibilizer. By reacting its epoxy groups with the carboxyl/hydroxyl groups of PC/ABS degradation products, they effectively repaired the polar groups generated during PC/ABS degradation while significantly improving the interfacial compatibility between the PC and ABS phases. This modification increased the impact strength to 9 kJ/m\u0026sup2; (2.2 times that of the unmodified sample).However, the addition of SBG requires precise control, with 6 wt% being the optimal dosage. Excessive addition results in phase separation.This modification method not only simultaneously enhances the tensile strength and impact toughness of the recycled PC/ABS (R-PC/ABS), but also notably improves the melt fluidity and processing stability of the material.Zhang et al. [\u003cspan citationid=\"CR22\" class=\"CitationRef\"\u003e22\u003c/span\u003e] investigated the effect of ABS-g-MAH on the properties of ABS/PC alloys and found that the maleic anhydride groups reacted with the terminal hydroxyl groups of PC to form PC-g-ABS copolymers.Interfacial adhesion was enhanced via molecular chain entanglement, thereby improving the material\u0026rsquo;s toughness.Experiments demonstrated that adding 10 wt% ABS-g-MAH significantly increased the notched impact strength, while maintaining tensile strength, flexural strength, and Vicat softening temperature (VST) essentially unchanged.However, if the grafting degree (DG) exceeds 1.74 wt% or the addition amount is excessively high, the toughening effect weakens due to increased brittleness.Differential scanning calorimetry (DSC) and scanning electron microscopy (SEM) analyses confirmed that ABS-g-MAH refines and homogenizes the dispersed phase by improving the compatibility of the two phases.Ma et al. [\u003cspan citationid=\"CR23\" class=\"CitationRef\"\u003e23\u003c/span\u003e] reported that styrene-maleic anhydride copolymer (SMA) can form SMA-g-PC copolymers via in-situ reactions, effectively improving the compatibility of PC/ABS blends and thus significantly enhancing their tensile strength, impact strength, and fatigue performance.Additionally, via cyclic tensile tests and fracture morphology analysis, they found that the fatigue failure of PC/ABS blends is primarily caused by interfacial peeling between the two phases, and the introduction of SMA significantly delays this process by enhancing interfacial bonding.Zuo et al. [\u003cspan citationid=\"CR24\" class=\"CitationRef\"\u003e24\u003c/span\u003e] proposed an alternative approach that avoids external compatibilizers: they synthesized core-shell structured polybutadiene-grafted methyl methacrylate copolymer (MB) via emulsion polymerization.Transesterification reactions and hydrogen bonding between the PMMA shell and PC significantly enhance the compatibility of PC/ABS blends.When the addition amount of MB is 12 phr, the notched impact strength of the composite reaches 430 J/m\u0026sup2;, and optimization of the melt flow rate (MFR) enhances processability.Compared with SBG modification, MB directly achieves compatibility between PC and ABS via its core-shell structure, eliminating the sensitivity issue associated with compatibilizer dosage.However, high MB content may still result in rubber phase agglomeration.\u003c/p\u003e \u003cp\u003eIn this study, glycidyl methacrylate (GMA) was introduced as the third grafting monomer in a redox initiation system via emulsion polymerization. By regulating the stage of GMA addition and investigating its dosage, a modified ABS resin tailored for PC/ABS alloys was prepared; subsequently, PC/modified ABS composites were fabricated via melt blending extrusion without the involvement of other compatibilizers, yielding alloy materials with excellent mechanical properties. Additionally, the effects of GMA introduction on the particle size distribution and residual monomer content of the ABS emulsion were systematically investigated, while the regulatory effects of GMA content in the ABS graft copolymer on the mechanical and thermal properties of PC/modified ABS composites were thoroughly analyzed. Finally, the cross-sectional morphology and microstructure of the deformation zone in the toughened PC/ABS alloy were characterized via scanning electron microscopy (SEM), and the toughening mechanism of the GMA-modified latex during alloy preparation was discussed.\u003c/p\u003e"},{"header":"2 Experiment","content":"\u003cdiv id=\"Sec3\" class=\"Section2\"\u003e \u003ch2\u003e2.1 Main raw materials\u003c/h2\u003e \u003cp\u003eAcrylonitrile (AN), polybutadiene latex (PBL), styrene (St), and styrene-acrylonitrile binary copolymer (SAN) were all of industrial grade, supplied by the Synthetic Resin Plant of Jilin Petrochemical Branch, China National Petroleum Corporation. Polycarbonate (PC, grade: 2805) was purchased from Covestro via Shanghai Yilun Plastic Chemical Co., Ltd. Glycidyl methacrylate (GMA, analytical grade) was provided by Suzhou Anli Chemical Co., Ltd.; sodium pyrophosphate (SPP, analytical grade) by Shanghai Bohua Biological Co., Ltd.; glucose (DX, analytical grade) and ferrous sulfate (FeSO₄, analytical grade) by Tianjin Fuchen Chemical Reagent Factory; tertiary dodecyl mercaptan (TDDM, analytical grade) by Shanghai Chemical Reagent Co., Ltd. of Sinopharm Group; and cumene hydroperoxide (CHP, analytical grade) by Fushun Qingyuan Additive Factory. Concentrated sulfuric acid (98.0% w/w purity), deionized water, disproportionated rosin acid soap solution, and antioxidant were all commercially available.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec4\" class=\"Section2\"\u003e \u003ch2\u003e2.2 Instruments and equipment\u003c/h2\u003e \u003cp\u003eABS emulsion polymerization unit :3L polymerization kettle, agitator, reflux condenser, constant temperature water bath, temperature control system, peristaltic pump, TOKYORIKA Company, Japan; 30L autoclave: Steam heating, cooling water, temperature control system, electric mixer, NICHIGOENG Company, Japan; dehydrator :SS600-N, Liaoyang Pharmaceutical Machinery Co., LTD. Fluidized bed dryer :NFOD-15, TOKYORIKA, Japan; Twin-screw extruder: TB-35, Nanjing Bosch Company; Electric heating blower drying oven: DHG9070A, Shanghai Yiheng Scientific Instrument Co., LTD. Twin-screw extruder: TB-36, Jiangsu Chengmeng Equipment Co., LTD. Injection molding machine :Victory110, Engel Injection Molding Machinery Co., LTD. Electronic universal testing machine :34TM-10, Instron (Shanghai) Testing Equipment Trading Co., LTD. CEAST9050 impact testing machine High-speed kneader :SHR-100A, Shatong Plastic Machinery Factory, Zhangjiagang City, Jiangsu Province; Scanning electron microscope :JSM-7610FPlus model, Japan Electronics Corporation; Fourier Transform Infrared Instrument :Nicolet6700 model, Thermoelectric Instruments, USA. Thermogravimetric analyzer: TGA4000 model, PE Company, USA\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec5\" class=\"Section2\"\u003e \u003ch2\u003e2.3 Preparation of ABS-g-GMA\u003c/h2\u003e \u003cp\u003eThe ABS-g-GMA core-shell emulsion was synthesized via emulsion polymerization in a 3 L three-necked flask equipped with a reflux condenser and a mechanical stirrer. In the initial stage, polybutadiene latex (PBL) was charged into the flask and maintained at 43 ℃ in a water bath. Then, water, acrylonitrile (AN), styrene (St), tertiary dodecyl mercaptan (TDDM), cumene hydroperoxide (CHP), and an activator were successively added. The temperature was then raised to 55 ℃, and the polymerization was allowed to proceed for 1 h.For the incremental feeding stage, a monomer mixture containing AN, St, TDDM, CHP, disproportionated rosin acid soap, and water was prepared. This mixture was heated to 60 ℃ and subsequently added to the reactor continuously over 2 h. In the final stage, the temperature was elevated to 70 ℃, and an antioxidant was introduced to terminate the reaction, affording the target ABS-g-GMA core-shell emulsion.The resulting emulsion was coagulated by adding it to 3 kg of an aqueous sulfuric acid solution (0.33% w/w) at 75 ℃ under stirring. The temperature of the coagulation reactor was then raised to 90 ℃ to complete the process. The coagulum was collected, rinsed three times with distilled water, and separated by centrifugation. The product was finally dried under vacuum at 60 ℃ for 12 h to obtain the ABS-g-GMA graft copolymer powder. The detailed dosages of all reactants are provided in Table\u0026nbsp;\u003cspan refid=\"Tab1\" class=\"InternalRef\"\u003e1\u003c/span\u003e.\u003c/p\u003e \u003cp\u003e \u003cdiv class=\"gridtable\"\u003e\u003ctable float=\"Yes\" id=\"Tab1\" border=\"1\"\u003e \u003ccaption language=\"En\"\u003e \u003cdiv class=\"CaptionNumber\"\u003eTable 1\u003c/div\u003e \u003cdiv class=\"CaptionContent\"\u003e \u003cp\u003eFormula of ABS-g-GMA graft Copolymer\u003c/p\u003e \u003c/div\u003e \u003c/caption\u003e \u003ccolgroup cols=\"4\"\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c1\" colnum=\"1\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c2\" colnum=\"2\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c3\" colnum=\"3\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c4\" colnum=\"4\"\u003e\u003c/div\u003e \u003cthead\u003e \u003ctr\u003e \u003cth align=\"left\" colname=\"c1\"\u003e \u003cp\u003eTypes of raw materials\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c2\"\u003e \u003cp\u003eInitial stage /g\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c3\"\u003e \u003cp\u003eIncremental stage /g\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c4\"\u003e \u003cp\u003eLater stage of grafting /g\u003c/p\u003e \u003c/th\u003e \u003c/tr\u003e \u003c/thead\u003e \u003ctbody\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eAN\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e22.467\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e68.124\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e\u0026mdash;\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eSt\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e57.715\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e172.425\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e\u0026mdash;\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eWater\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e374.164\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e204.771\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e\u0026mdash;\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003ePBL\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e829.016\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e\u0026mdash;\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e\u0026mdash;\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eActivator\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e46.400\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e\u0026mdash;\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e23.200\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eTDDM\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e1.432\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e0.968\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e\u0026mdash;\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eCHP\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e0.550\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e2.200\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e0.850\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003ePine soap\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c2\"\u003e \u003cp\u003e\u0026mdash;\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e6.400\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e\u0026mdash;\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003c/tbody\u003e \u003c/colgroup\u003e \u003c/table\u003e\u003c/div\u003e \u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec6\" class=\"Section2\"\u003e \u003ch2\u003e2.4 Preparation of PC/ABS alloy\u003c/h2\u003e \u003cp\u003eTo ensure the processability of the PC/ABS alloy, a SAN resin with high melt flowability was selected. Prior to blending, both the GMA-modified ternary graft copolymer (ABS-g-GMA) and the SAN resin were dried at 80 ℃ for 4 h. The dried components were then blended at a mass ratio of ABS-g-GMA to SAN of 23:77. Specific amounts of ethylene-bis-stearamide (EBA), magnesium stearate (MAGST), and the antioxidant distearyl pentaerythritol diphosphite (SPEP) were added to the mixture.The composition was subsequently mixed using a high-speed mixer for 5 minutes and fed into the hopper of a co-rotating twin-screw extruder for melt compounding and granulation. The temperature profile along the extruder barrel (conveying, plasticizing, and metering sections) and the die was set between 190 ℃ and 210 ℃. The extrudate was cooled in a water bath and cut into cylindrical pellets with dimensions of 3 mm \u0026times; 3 mm.The resulting GMA-modified ABS resin pellets were dried again at 80 ℃ for 4 h before injection molding. The injection molding process was conducted with a barrel temperature profile of 180, 200, 210, and 220 ℃, an injection pressure of 90 MPa, and a cooling time of 25 seconds to prepare specimens for property testing.\u003c/p\u003e \u003cp\u003ePrior to melt processing, both PC and ABS resins were dried to prevent bubble formation during extrusion, which can compromise alloy properties due to moisture absorption from prolonged air exposure. The PC resin was dried at 100 ℃ for 4 hours, and the ABS resin was dried at 80 ℃ for 4 hours in a forced-air convection oven. Subsequently, the pre-dried GMA-modified ABS, PC resin, and additives were blended in a high-speed mixer at a predetermined ratio. The mixture was then melt-compounded using a co-rotating twin-screw extruder. The temperature settings for the extruder's conveying, plasticizing, metering sections, and die were maintained between 220 ℃ and 250 ℃. The resulting PC/ABS alloy was dried again at 100 ℃ for 4 hours before injection molding. The injection molding process was carried out with barrel zone temperatures set at 180 ℃, 245 ℃, 250 ℃, and 255 ℃, an injection pressure of 90 MPa, and a cooling time of 25 seconds. Finally, all test specimens were conditioned at constant temperature away from light for 2 hours before mechanical property analysis.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec7\" class=\"Section2\"\u003e \u003ch2\u003e2.5 Testing and Characterization\u003c/h2\u003e \u003cp\u003eGrafting rate test: Accurately weigh approximately 1g of ABS powder sample into a already weighed centrifuge tube, add about 20mL of acetone, and shake for 24 hours to ensure it is fully dissolved. Then, centrifuge for 8 minutes at 3℃ ~4℃ and 18,000 RPM /min, transfer the supernatant, and repeat the washing operation twice. The remaining insoluble substances and centrifuge tubes were dried at 50℃ under normal pressure for 24 hours, then transferred to an 80℃ vacuum oven for drying for 24 hours. After cooling, they were weighed.\u003c/p\u003e \u003cp\u003eNotch impact strength test: It is carried out in accordance with GB/T 1843\u0026ndash;2008. Firstly, the standard impact spline formed by injection molding is processed. A standard V-shaped notch is milled in the middle part of one side of it, and it is ensured that the depth of this notch is 2mm. All the prepared splines were adjusted at room temperature for 24 hours and then tested using a pendulum at 2.75J.\u003c/p\u003e \u003cp\u003eTensile properties (including tensile strength and elongation at break) test: conducted in accordance with GB/T 1040.2\u0026ndash;2022: Firstly, clamp the standard dumbbell-shaped spline formed by injection molding and stretch it at a test rate of 50 mm/min until the spline breaks; All splines were adjusted at room temperature for 24 hours and then tested using a universal testing machine equipped with an extensometer.\u003c/p\u003e \u003cp\u003eBending strength test: It is carried out in accordance with GB/T 9341\u0026thinsp;\u0026minus;\u0026thinsp;2008. The standard sample formed by injection molding is placed on two supports. A three-point bending loading method is adopted, and pressure is applied to the sample at a test rate of 2 mm/min until the specified deflection is reached or fracture occurs. All splines were tested after being adjusted at room temperature for 24 hours.\u003c/p\u003e \u003cp\u003eInfrared testing: Samples are tested using Fourier Transform infrared spectroscopy (FTIR) equipped with attenuated total reflection (ATR) accessories. Before the test, place a small amount of dry sample directly on the detection surface of the ATR crystal, and apply appropriate pressure through the pressure rod to ensure that the powder is in close contact with the crystal surface. Spectra were collected directly in transmission mode, with a scanning wavenumber range of 4000 to 400 cm⁻\u0026sup1; and a resolution of 4 cm⁻\u0026sup1;. A total of 32 scans were conducted to eliminate background noise. When testing the infrared of ABS-g-GMA powder, the powder needs to be separated for testing. The separation method is as follows: Take 2 g of the dried ABS-g-GMA powder and put it into a hard centrifuge tube. Dissolve the free chain segments in it with 35 mL of acetone solution. Place the centrifuge tubes on a constant temperature shaker at 25 ℃ and shake for 12 hours. Then, put the tubes on an ultracentrifuge for centrifugal separation at a speed of 10,000 r /min for 30 minutes. After centrifugation, pour out the supernatant. Repeat the above operation three times. All the supernatant obtained from the three times was placed in a beaker and dried to a constant weight to obtain the free chain segments dissolved in acetone, which were named SAN-g-GMA. The remaining part was placed in an oven at 65 ℃ and dried to a constant weight to obtain ABS-g-GMA after the free chains were removed.\u003c/p\u003e \u003cp\u003eVicat softening temperature test: Conducted in accordance with GB/T 1633\u0026ndash;2000: Place the flat sample with a thickness exceeding 3mm horizontally on the support, press the flat-head needle with a cross-sectional area of 1mm \u0026sup2; vertically into the surface of the sample under a load of 50N, and heat it at a uniform rate of 50 ℃/h; All samples were tested after being adjusted at room temperature for 24 hours. The temperature at which the needle was pressed into the sample to a depth of 1 mm was recorded, which was the Vicat softening temperature.\u003c/p\u003e \u003cp\u003eScanning electron microscopy test: Select appropriate fracture spline, cut a 10mm thick sample along the cross-section, spray gold on the cross-section, and observe and take photos on the JSM-6610LV scanning electron microscope (SEM). When determining the compatibility of PC/ABS alloys, the ABS in the blend needs to be etched off. The cross-sectional treatment is as follows: At a constant temperature of 80℃, the sample piece is gently rotated in chromic acid wash solution with a sub-clamp for 8 minutes, and then ultrasonically cleaned for 15 minutes. After that, it is taken out and dried.\u003c/p\u003e \u003cp\u003eEpoxy value test: The epoxy value test method is carried out in accordance with the national standard GB1677 test standard for hydrochloric acid and acetone method. Accurately weigh 2-4mg of epoxy equivalent epoxy resin sample and place it in a 250mL sealed flask. Add 20mL of 0.2mo/ L hydrochloric-acetone solution with a pipette, shake well to ensure complete dissolution of the sample. After standing at room temperature for 15 minutes, add 25mL of neutral ethanol. Then titrate the excess hydrochloric acid with a 0.1mol/L sodium oxide standard solution. The end point of titration is when the cresol red indicator in ethanol-acetone solution changes from pink to yellow first and then gradually to purple. Make a blank sample again.\u003c/p\u003e \u003cp\u003eThermogravimetric test: The thermal stability of the sample is tested using a thermogravimetric analyzer. Before the test, cut the sample into a solid state and accurately weigh 5mg of the sample and place it in an alumina crucible. The test was conducted in a nitrogen atmosphere with a nitrogen flow rate of 20mL/min. The heating range was from room temperature to 600℃, and the heating rate was 10℃/min. By recording the variation of sample mass with temperature, the parameters related to thermal stability such as thermal decomposition temperature and weight loss rate were analyzed.\u003c/p\u003e \u003cp\u003eDSC test: The thermal performance of the sample is analyzed using a differential scanning calorimeter. Take 5mg of the sample and seal it in an aluminum sample cell, using an empty aluminum cell as the reference. The test was conducted under nitrogen protection with a nitrogen flow rate of 50 ml /min. The test procedure was as follows: First, the temperature was raised from room temperature to 250℃ and maintained for 5 minutes to eliminate the thermal history of the sample. Then, the temperature was reduced to -50 ℃ at a rate of 10℃/min, and the temperature was raised to 250℃ at the same rate. Record parameters such as the glass transition temperature, melting temperature, crystallization temperature of the sample and the corresponding enthalpy changes.\u003c/p\u003e \u003c/div\u003e"},{"header":"3 Results and Discussion","content":"\u003cdiv id=\"Sec9\" class=\"Section2\"\u003e \u003ch2\u003e3.1 Performance analysis of modified latex\u003c/h2\u003e \u003cp\u003e \u003cdiv class=\"gridtable\"\u003e\u003ctable float=\"Yes\" id=\"Tab2\" border=\"1\"\u003e \u003ccaption language=\"En\"\u003e \u003cdiv class=\"CaptionNumber\"\u003eTable 2\u003c/div\u003e \u003cdiv class=\"CaptionContent\"\u003e \u003cp\u003eThe emulsion properties of ABS-g-GMA\u003c/p\u003e \u003c/div\u003e \u003c/caption\u003e \u003ccolgroup cols=\"7\"\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c1\" colnum=\"1\"\u003e\u003c/div\u003e \u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c2\" colnum=\"2\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c3\" colnum=\"3\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c4\" colnum=\"4\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c5\" colnum=\"5\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c6\" colnum=\"6\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c7\" colnum=\"7\"\u003e\u003c/div\u003e \u003cthead\u003e \u003ctr\u003e \u003cth align=\"left\" colname=\"c1\"\u003e \u003cp\u003eRaw material type\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c2\"\u003e \u003cp\u003eGMA /g\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c3\"\u003e \u003cp\u003eSolid /%\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c4\"\u003e \u003cp\u003eGrafting rate/%\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c5\"\u003e \u003cp\u003epH\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c6\"\u003e \u003cp\u003eParticle size /um\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c7\"\u003e \u003cp\u003eStability\u003c/p\u003e \u003c/th\u003e \u003c/tr\u003e \u003c/thead\u003e \u003ctbody\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eNone GMA\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e \u003cp\u003e0\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e40.59\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e85.97\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e11.2\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e320.3\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c7\"\u003e \u003cp\u003eStable\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eGMA was added at the initial stage\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e \u003cp\u003e10\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e\\\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e\\\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e\\\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e\\\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c7\"\u003e \u003cp\u003eMassive sedimentation\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eGMA was added at the incremental stage\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e \u003cp\u003e10\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e34.92\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e81.31\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e10.71\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e345.4\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c7\"\u003e \u003cp\u003eGranular sedimentation\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003eGMA was added at the later stage of grafting\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e \u003cp\u003e10\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c3\"\u003e \u003cp\u003e42.64\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c4\"\u003e \u003cp\u003e86.37\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c5\"\u003e \u003cp\u003e10.1\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c6\"\u003e \u003cp\u003e362.7\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c7\"\u003e \u003cp\u003eStable\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003c/tbody\u003e \u003c/colgroup\u003e \u003c/table\u003e\u003c/div\u003e \u003c/p\u003e \u003cp\u003eThe emulsion polymerization process of GMA grafted modified ABS can be divided into three stages: the initial stage of emulsion polymerization, the increment stage and the later stage of curing. Table\u0026nbsp;\u003cspan refid=\"Tab2\" class=\"InternalRef\"\u003e2\u003c/span\u003e lists the performance data of GMA and unmodified emulsion added in the three stages. The results show that when 10g of GMA is added at the initial stage of polymerization, due to the presence of a large amount of butadiene latex at this stage, GMA undergoes rapid copolymerization with it, generating a large number of short-chain and structurally disordered polymers, which will destroy the stability of the emulsion and lead to solid precipitation and demulsification. When GMA is added in the incremental stage, the polymerization reaction rate is relatively stable. The ternary copolymer latex has grown to a certain chain segment, and the system has a certain buffering capacity. Some granular precipitates are produced, which will not lead to demulsification of the polymerization system. In the later stage of the polymerization reaction's maturation, the addition of GMA can more stably graft with PB latex. At the same time, it can also react the unreacted styrene and acrylonitrile monomers in the system, thereby improving the residual monomer content of PB latex. The mechanism of GMA grafting modification was further explored based on the solid content, grafting rate and particle size data listed in Table\u0026nbsp;\u003cspan refid=\"Tab2\" class=\"InternalRef\"\u003e2\u003c/span\u003e, as shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eAs shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e, at the initial stage of emulsion polymerization, when AN and St monomers are just added to the PBL latex, the grafting reaction is incomplete in the initial stage of the reaction. If GMA monomers are added at this time, the double bonds in the GMA molecules will compete with AN and St for the opportunity to polymerize with the PBL latex, resulting in cross-linking reactions and preventing the latex from fully forming stable polymer segments. The formation of blocky precipitates that disrupt the stability of the latex subsequently leads to demulsification. During the incremental reaction stage, some AN and St monomers have been grafted onto the surface of butadiene latex, forming a certain latex grafting layer. At this point, the introduction of GMA monomers can achieve a grafting rate of 81.31%, which is lower than the grafting rate of 85.97% of the unmodified ABS latex. This is because GMA will form a large number of by-products with AN and St, but does not form a good modified grafting. A large number of by-products will inevitably affect the improvement of the grafting rate. Meanwhile, the solid content of the system also decreased from 40.59% to 34.92%, which confirmed that the small-molecule by-products reduced the grafting rate of PB latex. The corresponding reaction equations are listed in Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e. A large amount of by-products of GMA grafted monomers were generated during the polymerization process, which not only led to incomplete ABS emulsion polymerization reaction but also further affected the impact performance of the subsequent PC/ ABS alloy, reducing it from 48.52 to 35.27 KJ/m\u003csup\u003e2\u003c/sup\u003e.\u003c/p\u003e \u003cp\u003eIn the later stage of polymerization and curing, most of the AN and St monomers have been grafted onto the PB latex. The grafting reaction generates high-molecular chains, and the particle size of the emulsion gradually increases, forming a stable emulsion system with a core-shell structure. At this point, the introduction of GMA monomers cannot react with AN and St to form by-products. The epoxy groups in GMA will first undergo hydrolysis under alkaline conditions, as shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003eRecation 1. This conclusion can be proved by the determination results of the epoxy values of the emulsion in Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e (d). The epoxy values in the emulsions with GMA added are all close to 1 PPM, indicating that most of the epoxy groups have been hydrolyzed. At this point, the GMA molecule breaks the acrylate double bond and can be grafted onto the surface of the core-shell structure of the PBL latex, further increasing the particle size to 362.7 \u0026micro; m and forming the ABS-g-GMA grafted polymer, as shown in Reaction 3. The latex ABS-g-GMA modified by GMA grafting can effectively improve the compatibility between PC and ABS, and the impact strength of PC/ABS alloy is increased from 48.52 to 60.86KJ/m\u003csup\u003e2\u003c/sup\u003e.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eFigure \u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e(a) shows the particle size distribution of the ABS-g-GMA emulsion prepared by graft polymerization with different amounts of GMA added to the ABS emulsion in the later stage of curing. As can be seen from the figure, with the increase of GMA dosage, the particle size of the emulsion gradually increases, confirming that in the later stage of curing, the addition of GAM can graft onto the latex particles, so the particle size will increase significantly. An appropriate amount of GMA can improve the uniformity of particle size in emulsions. However, when GMA is in excess, the particle size distribution becomes wider instead, indicating an uneven grafting phenomenon. Therefore, excessive GMA cannot provide good stability for the polymerization system.\u003c/p\u003e \u003cp\u003eFigures \u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e(b) and 3(c) respectively show the changing trends of pH value, grafting rate and solid content of the emulsion. As shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e (b), the pH value gradually decreases as the amount of GMA added increases. The continuous decline in pH value also stems from the fact that after GMA is added to the system, under alkaline conditions, the ring-opening of epoxy groups consumes OH- in the emulsion system. As shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e (c), when the GMA concentration is low, the grafting rate drops from the initial 85.97% to 84.17%. This is because the active GMA monomers in the system react with the unreacted AN and St, resulting in the formation of excessive small molecule polymer segments. These small molecules dissolve in acetone during the grafting test, thus causing the grafting rate to decrease. However, as the concentration of GMA increases, more GMA will be grafted onto the ternary copolymer latex particles to form the modified ABS-g-GMA grafted copolymer. The enhanced grafting reaction promotes the growth and cross-linking of the polymer molecular chain, forming a larger-sized molecular structure. This chemically grafted polymer will not dissolve in acetone, so the grafting rate will show an upward trend.\u003c/p\u003e \u003cp\u003eFigure \u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e(d) shows the results of the determination of acrylonitrile, butadiene and styrene residual monomers in the emulsion by chromatography. When GMA is not added, the residual amounts of acrylonitrile and butadiene in ABS emulsion are relatively high, at 48.4367ppm and 584.1975ppm respectively. This is due to the incomplete reaction of AN and St monomers during the polymerization process and is also one of the main sources of industrial wastewater pollution. After the introduction of GMA, the residual amounts of acrylonitrile and butadiene were significantly reduced to below 1ppm. This is mainly because, in addition to participating in the graft modification reaction, GMA can also react with unreacted acrylonitrile, styrene and other monomers in the system, effectively capturing the residual monomers and generating oligomolymer small molecules, which has a positive significance for reducing wastewater discharge.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec10\" class=\"Section2\"\u003e \u003ch2\u003e3.2 Mechanical properties of alloys\u003c/h2\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eIn order to further explore the influence of GMA-modified latex on PC/ABS alloys, the variation laws of mechanical properties of the alloys under different PC/ABS ratios and different GMA modification amounts were systematically investigated. Four compound ratios of PC to ABS, namely 50:50, 60:40, 70:30 and 80:20, were selected. Under each ratio condition, the GMA addition amount of the modified ABS powder was changed. The mechanical property analysis diagram is shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003e.\u003c/p\u003e \u003cp\u003eFigure \u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003e(a) shows the impact strength curves of alloys with different proportions varying with the amount of modified GMA. With the increase of GMA addition, the impact strength curves all show a trend of first increasing and then decreasing. When the PC/ABS ratio is 70/30 and the GMA addition amount is 10g, the increase in impact strength is the most significant, reaching 25.43%. The impact strength has increased from 48.52 kJ/m\u0026sup2; to 60.86 kJ/m\u0026sup2;. Except for the maximum impact value of the PC: ABS\u0026thinsp;=\u0026thinsp;50:50 ratio when the GMA addition amount is 7.5g, the highest impact strength values of other alloy ratios are all when the GMA addition amount is 10g. When the addition amount of GMA is too high, in addition to the effective grafting rate of ABS-g-GMA modified latex, small molecules of styrene and acrylonitrile grafted with GMA will also be formed, thereby reducing the interface compatibility between PC and ABS, and thus the impact performance of the alloy will also decrease.\u003c/p\u003e \u003cp\u003eThe changing trends of tensile and bending properties also show a trend of first increasing and then decreasing, as shown in Figs.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003e (b) and (c). For the PC/ABS\u0026thinsp;=\u0026thinsp;80/20 system, 10g GMA enables the tensile strength to reach a peak of 59.8 MPa and the flexural strength to reach a peak of 84.303 MPa. Except for the PC/ABS\u0026thinsp;=\u0026thinsp;60/40 system where the tensile strength reached the peak of 57.3 MPa at 7.5g GMA, the tensile peaks of other proportions all occurred when the addition amount of GMA was 10g. Because the increase in PC resin content is beneficial to the processing performance of PC/ABS alloy, both tensile properties and bending properties gradually increase with the increase of PC content. As shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003e (d) from the elongation at break curve, the peak values of all proportion alloys occur when the GMA addition amount is 10g. The elongation at break and impact strength are more sensitive to the interfacial bonding between PC and ABS resins. The modified grafted ABS elastomer in the alloy will enhance the flexibility of the molecular chain. Therefore, only under the optimal grafting rate of ABS-g-GMA modified latex can the highest impact strength and elongation at break be obtained. Based on the above mechanical properties, when the addition amount of GMA is 10g, the alloy prepared from the modified grafted ABS resin has more superior performance. Moreover, under the alloy ratio of PC/ABS\u0026thinsp;=\u0026thinsp;70/30, the comprehensive performance of the obtained alloy can all meet the application requirements of PC/ABS alloy in the automotive field.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec11\" class=\"Section2\"\u003e \u003ch2\u003e3.3 Analysis of thermal properties of alloys\u003c/h2\u003e \u003cp\u003eVicat softening point is suitable for controlling the quality of polymers and as an indicator for identifying the thermal performance of new varieties. It is tested under constant heating conditions and is a method for evaluating the high-temperature deformation trend of thermoplastics. The Vicat softening point trends of alloy resins with different PC/ABS ratios varying with the addition amount of GMA are shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig5\" class=\"InternalRef\"\u003e5\u003c/span\u003e. Firstly, the heat distortion temperature of PC/ABS alloy increases with the increase of PC content in the blend, from 104.7℃ when PC:ABS\u0026thinsp;=\u0026thinsp;50:50 to 124.5℃ when PC:ABS\u0026thinsp;=\u0026thinsp;80:20. The thermal decomposition temperature of PC resin is 480℃, which is significantly higher than that of ABS resin at 360℃. Therefore, an increase in the proportion of PC resin will significantly improve the thermal performance of PC/ABS alloy resin. No matter what proportion is used, the appropriate addition of GMA only slightly enhances the heat resistance of the alloy. This might be because GMA-modified latex can effectively improve the compatibility between PC and ABS, enhance the interfacial bonding force of plastic materials, and make the molecules at the interface more compact. The significant difference in the melting temperatures of PC and ABS resins makes the variation trend of the influence of GMA-modified latex on the thermal properties of PC/ABS alloys through interface modification not obvious.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eFigure \u003cspan refid=\"Fig6\" class=\"InternalRef\"\u003e6\u003c/span\u003e (a) shows the thermogravimetric curves of different PC/ABS ratios when the GMA addition amount is 10g. As the proportion of PC increases, the weight loss rate of the alloy at the same temperature varies. As the temperature rises, the residual mass fraction of PC/ABS alloy after decomposition increases with the increase of PC proportion. This result is consistent with the above-mentioned variation trend of PC/ABS alloy at the microcard softening point. This is because PC resin has higher heat resistance, so when ABS resin thermally decomposes, the residual mass with a higher PC content is higher. At around 600℃, the residual mass fraction of PC/ABS\u0026thinsp;=\u0026thinsp;50/50 is approximately 7.37%, while that of PC/ABS\u0026thinsp;=\u0026thinsp;80/20 is about 14.18%.\u003c/p\u003e \u003cp\u003eFigure \u003cspan refid=\"Fig6\" class=\"InternalRef\"\u003e6\u003c/span\u003e (b) shows the influence of different GMA addition amounts on the thermal stability of the alloy at the alloy ratio of PC: ABS\u0026thinsp;=\u0026thinsp;70:30. The weight loss rate of the alloy prepared from GMA-modified ABS latex in the range of 400\u0026ndash;500℃ is significantly lower than that of the system without GMA added. At 500℃, the residual mass fraction of the unmodified alloy is approximately 21%, while the residual amounts of the alloy obtained when the GMA addition amounts are 5g, 10g, and 15g are approximately 27%, 31%, and 23% respectively. This confirms that the addition of GMA-modified ABS powder can improve the thermal stability of PC/ABS alloy in the medium-temperature range. Within the range of 400\u0026ndash;500℃, when the addition amount of GMA is 15g, the thermal weight loss rate of the alloy is faster than that when the addition amount of GMA is 10g. This thermal performance analysis result also confirms that in the 3L latex system, when the addition amount of GMA is 10g, the grafting effect of ABS-g-GMA modified latex is the best, and it is the best for improving the interfacial bonding of PC/ABS alloy.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec12\" class=\"Section2\"\u003e \u003ch2\u003e3.4 Infrared spectroscopy analysis\u003c/h2\u003e \u003cp\u003eThe verification of grafting between GMA and the ternary copolymer PB latex was based on their differential solubility in acetone. The GMA-modified latex was centrifuged with acetone to dissolve away any ungraf ted linear macromolecules. Because the grafted PB latex is cross-linked into a three-dimensional network, it is only swollen by acetone and remains undissolved. Hence, the characteristic peaks observed in the FTIR spectrum of this insoluble material thus provide direct evidence for the success of the ABS-g-GMA grafting modification, as shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig7\" class=\"InternalRef\"\u003e7\u003c/span\u003e.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eThe FTIR spectra in Fig.\u0026nbsp;\u003cspan refid=\"Fig7\" class=\"InternalRef\"\u003e7\u003c/span\u003e compare unmodified ABS with GMA-grafted ABS. The appearance of a new absorption peak at 1730 cm⁻\u0026sup1; in the modified sample is attributed to the carbonyl group (C\u0026thinsp;=\u0026thinsp;O) of GMA, confirming the successful grafting of GMA onto the ABS backbone. Furthermore, the intensity of this peak increases with the GMA loading, which is associated with the presence of free (ungrafted) GMA homopolymer. The incorporation of GMA is expected to enhance the compatibility between PC and ABS during melt blending, as the epoxy groups in GMA can react with the end groups of PC. This improved compatibility ultimately leads to superior physical properties of the PC/ABS alloy.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec13\" class=\"Section2\"\u003e \u003ch2\u003e3.5 Analysis of alloy interface\u003c/h2\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003e \u003cb\u003e(a) No GMA; (b) 5g GMA; (c) 10gGMA; (d) 15gGMA;\u003c/b\u003e \u003c/p\u003e \u003cp\u003e \u003cdiv class=\"gridtable\"\u003e\u003ctable float=\"Yes\" id=\"Tab3\" border=\"1\"\u003e \u003ccaption language=\"En\"\u003e \u003cdiv class=\"CaptionNumber\"\u003eTable 3\u003c/div\u003e \u003cdiv class=\"CaptionContent\"\u003e \u003cp\u003eThe surface hole characteristic data of PC/ABS alloy SEM images under different GMA addition amounts\u003c/p\u003e \u003c/div\u003e \u003c/caption\u003e \u003ccolgroup cols=\"9\"\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c1\" colnum=\"1\"\u003e\u003c/div\u003e \u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c2\" colnum=\"2\"\u003e\u003c/div\u003e \u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c3\" colnum=\"3\"\u003e\u003c/div\u003e \u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c4\" colnum=\"4\"\u003e\u003c/div\u003e \u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c5\" colnum=\"5\"\u003e\u003c/div\u003e \u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c6\" colnum=\"6\"\u003e\u003c/div\u003e \u003cdiv align=\"char\" char=\".\" class=\"colspec\" colname=\"c7\" colnum=\"7\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c8\" colnum=\"8\"\u003e\u003c/div\u003e \u003cdiv align=\"left\" class=\"colspec\" colname=\"c9\" colnum=\"9\"\u003e\u003c/div\u003e \u003cthead\u003e \u003ctr\u003e \u003cth align=\"left\" colname=\"c1\"\u003e \u003cp\u003eGMA\u003c/p\u003e \u003cp\u003e/g\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c2\"\u003e \u003cp\u003eNumber of holes\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c3\"\u003e \u003cp\u003eAverage area/um\u003csup\u003e2\u003c/sup\u003e\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c4\"\u003e \u003cp\u003e0-0.2um\u003csup\u003e2\u003c/sup\u003e\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c5\"\u003e \u003cp\u003e0.2-0.4um\u003csup\u003e2\u003c/sup\u003e\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c6\"\u003e \u003cp\u003e0.4-0.6um\u003csup\u003e2\u003c/sup\u003e\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c7\"\u003e \u003cp\u003e0.6-0.8um\u003csup\u003e2\u003c/sup\u003e\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c8\"\u003e \u003cp\u003e0.8-1.0um\u003csup\u003e2\u003c/sup\u003e\u003c/p\u003e \u003c/th\u003e \u003cth align=\"left\" colname=\"c9\"\u003e \u003cp\u003e1.0-1.2um\u003csup\u003e2\u003c/sup\u003e\u003c/p\u003e \u003c/th\u003e \u003c/tr\u003e \u003c/thead\u003e \u003ctbody\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003e0\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e \u003cp\u003e421\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e \u003cp\u003e0.79\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e \u003cp\u003e62.5%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c5\"\u003e \u003cp\u003e15.2%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c6\"\u003e \u003cp\u003e7.3%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e7.0%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e4.2%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c9\"\u003e \u003cp\u003e3.7%\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003e5\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e \u003cp\u003e988\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e \u003cp\u003e0.17\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e \u003cp\u003e69.1%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c5\"\u003e \u003cp\u003e22.7%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c6\"\u003e \u003cp\u003e5.3%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e2.4%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e0\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c9\"\u003e \u003cp\u003e0.4%\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003e10\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e \u003cp\u003e1292\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e \u003cp\u003e0.09\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e \u003cp\u003e89.9%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c5\"\u003e \u003cp\u003e7.3%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c6\"\u003e \u003cp\u003e2.2%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e0.5%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e0\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c9\"\u003e \u003cp\u003e0\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003ctr\u003e \u003ctd align=\"left\" colname=\"c1\"\u003e \u003cp\u003e15\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c2\"\u003e \u003cp\u003e1136\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c3\"\u003e \u003cp\u003e0.10\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c4\"\u003e \u003cp\u003e87.3%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c5\"\u003e \u003cp\u003e10.6%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c6\"\u003e \u003cp\u003e1.4%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"char\" char=\".\" colname=\"c7\"\u003e \u003cp\u003e0.7%\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c8\"\u003e \u003cp\u003e0\u003c/p\u003e \u003c/td\u003e \u003ctd align=\"left\" colname=\"c9\"\u003e \u003cp\u003e0\u003c/p\u003e \u003c/td\u003e \u003c/tr\u003e \u003c/tbody\u003e \u003c/colgroup\u003e \u003c/table\u003e\u003c/div\u003e \u003c/p\u003e \u003cp\u003eThe microscopic morphology of the compatible interface of the PC/ABS blend system with different GMA addition amounts was observed by scanning electron microscopy. As shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig8\" class=\"InternalRef\"\u003e8\u003c/span\u003e, it is the impact cross-section diagram of the PC/ABS composite material obtained by adding different GMA in the later stage of ABS emulsion polymerization and curing. The ratio of PC to ABS is 70:30. The sample is immersed in chromic acid solution to etch away the ABS dispersed phase in the alloy, allowing for a more intuitive observation of the distribution state of ABS in the PC resin. Table\u0026nbsp;\u003cspan refid=\"Tab3\" class=\"InternalRef\"\u003e3\u003c/span\u003e shows the specific data of ABS holes statistically analyzed by Image J. The pore structure on the surface of PC/ABS alloy reflects the dispersion state of the ABS phase. As shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig8\" class=\"InternalRef\"\u003e8\u003c/span\u003e(a), in the absence of additives, the ABS phase in the impact section of the PC/ABS alloy forms various types of unevenly sized strip holes (with an average area of 0.79 \u0026micro;m\u0026sup2; and holes greater than 0.4 \u0026micro;m\u0026sup2; accounting for 22.3%), indicating that the ungrafted modified ABS has poor dispersion and compatibility with PC. Figures\u0026nbsp;\u003cspan refid=\"Fig8\" class=\"InternalRef\"\u003e8\u003c/span\u003e (b) and (c) respectively show the impact cross-sections of PC/ABS composites after adding 5g and 10g GMA. From the SEM images, it can be seen that the GMA-modified ABS resin is more evenly dispersed in the PC phase, and the large-sized pores are significantly reduced. When 10gGMA was added, the number of holes larger than 0.8um \u0026sup2; was 0, and the total number of holes increased from 421 to 1292. This fully confirmed that the ABS-g-GMA modified latex has a good effect on improving the compatibilization of the PC/ABS alloy system. However, when the addition amount of GMA increased to 15g as shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig8\" class=\"InternalRef\"\u003e8\u003c/span\u003e (d), both the PC phase and the ABS phase presented large-area continuous phases, and the proportion of large holes in the pore distribution also increased compared to Fig.\u0026nbsp;\u003cspan refid=\"Fig8\" class=\"InternalRef\"\u003e8\u003c/span\u003e (c). This is consistent with the test results of the effective GMA-modified grafting rate when the addition amount of GMA is different, indicating that only when GMA is effectively grafted onto the ABS ternary polymer latex can a better interface grafting effect be provided in the preparation process of PC/ABS alloy. Simply adding too much GMA modified monomer will only be beneficial in capturing the unpolymerized AN and St monomers. Therefore, the optimal addition amount of GMA in a 3L latex polymerization system is 10g.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec14\" class=\"Section2\"\u003e \u003ch2\u003e3.6 Principle analysis\u003c/h2\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eBased on the above analysis and experimental results of GMA-modified latex, the mechanism of the compatibilization effect of GMA-grafted modified ABS-g-GMA latex on PC/ABS alloy is shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig9\" class=\"InternalRef\"\u003e9\u003c/span\u003e. Firstly, it was confirmed that after GMA was added in the later stage of the emulsion polymerization reaction, it could be grafted onto the ternary copolymer latex, and its unsaturated double bond would undergo a polymerization reaction with the PBL latex. Meanwhile, in the polymerization system with a pH value of 10, the epoxy groups of GMA will react to open the ring and form -OH, as shown in reaction (1) of Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e. The carboxyl and hydroxyl groups carried in PC resin can react with the epoxy groups interrupted by ABS-g-GMA, as shown in reactions (1) and (2) of Fig.\u0026nbsp;\u003cspan refid=\"Fig9\" class=\"InternalRef\"\u003e9\u003c/span\u003e. It is worth mentioning that this type of reaction can generate PC-co-ABS copolymers with special structures in situ at the interface of the two phases. This in-situ generated copolymer can be regarded as an efficient compatibilizer, significantly improving the compatibility of the blend system through the following dual mechanism of action. This PC-co-ABS copolymer promotes the refinement of dispersed phase particles by reducing the interphase interface free energy. At the same time, the agglomeration of dispersed phase particles can also be effectively inhibited through the steric hindrance effect. The synergistic effect of these two mechanisms eventually led to the formation of a microstructure with smaller dispersed phase size and more uniform distribution in the PC/ABS-g-GMA blend, thereby obtaining significantly optimized morphological characteristics.\u003c/p\u003e \u003cp\u003eReaction 3 and Reaction 4 are two types of cross-linking reactions with significantly different characteristics in the blend system. Reaction 3 originates from the self-crosslinking of hydroxyl groups at the interface of PC-co-ABS copolymer, mainly occurring within the dispersed phase. Reaction 4, on the other hand, is based on the bifunctional properties of the PC matrix and is achieved through interfacial cross-linking reactions with the disconnected epoxy groups. When the GMA content is too high, the excessive cross-linking reaction leads to an increase in the viscosity of the system, thereby interfering with the formation of phase morphology, ultimately intensifying phase separation and increasing the size of the dispersed phase. However, reaction 4 is more difficult to occur than Reaction 3, mainly due to the following two reasons. First, Reaction 4 relies on the interaction at the interface of the two phases, while Reaction 3 occurs directly within the dispersed phase. Therefore, ABS-g-GMA is more likely to diffuse in the dispersed phase and promote the occurrence of reaction 3. Secondly, the volume increase reactions 1 and 2 will reduce the concentrations of carboxyl groups, hydroxyl groups on PC and the broken epoxy groups on ABS-g-GMA, thereby inhibiting the rate of reaction 4. However, for reaction 3, although the broken epoxy groups decrease, the hydroxyl group concentration on the PC-CO-ABS copolymer increases instead due to the volume increase reaction, allowing reaction 3 to still proceed at a relatively high rate. Therefore, when GMA is in excess, reaction 3 becomes the dominant crosslinking reaction in the PC/ABS-g-GMA blend, and its influence on the phase morphology is more significant. This changing trend is mainly attributed to the bifunctional characteristics of GMA. Its acrylate double bond can undergo graft copolymerization with the ABS component, while the epoxy group can react with the carbonate group of PC. Therefore, appropriate GMA graft polymerization has a significant effect on improving the two-phase compatibility of PC and ABS resins.\u003c/p\u003e \u003c/div\u003e"},{"header":"4 Conclusion","content":"\u003cp\u003eThis study addresses the industrial application pain point of PC/ABS alloy, which is low impact strength and limited processing performance due to poor compatibility between PC and ABS. It proposes a method of preparing functionalized ABS (ABS-g-GMA) by in-situ grafting GMA through emulsion polymerization to achieve the preparation of self-reactive compatible groups and improve the mechanical properties of PC/ABS alloy. By regulating the stage and dosage of GMA addition, and combining FTIR, SEM, mechanical testing and thermal analysis, the correlation rules between key process parameters and alloy properties were clarified. Adding 10gGMA in the later stage of emulsion polymerization can ensure system stability and reduce residual single emissions. The ABS-g-GMA prepared under this condition can strengthen the PC/ABS interface through chemical grafting reaction, enabling the optimal comprehensive mechanical properties of the PC/ABS\u0026thinsp;=\u0026thinsp;70/30 alloy with notched impact strength reaching 60.86kJ/m\u0026sup2;, tensile strength of 59MPa, and flexural strength of 83.531MPa. At the same time, the Vicat softening temperature and the thermal stability in the medium-temperature range were significantly improved. This method not only resolves the interfacial bonding issue of PC/ABS alloys, but also facilitates the reduction of industrial emissions through the side reactions of GMA with residual AN and St monomers, meeting the demand for high-performance PC/ABS alloys in fields such as electronics and electrical appliances, and automotive parts, and achieving convenient industrial production of PC/ABS alloys.\u003c/p\u003e"},{"header":"Declarations","content":"\u003ch2\u003eAuthor Contribution\u003c/h2\u003e\u003cp\u003eX.C. and M.X. conceptualized the study. X.C. performed investigation and formal analysis, and wrote the original draft. L.S. contributed to methodology, validation, and project administration. D.J. conducted experiments and curated data. Z.E. analyzed data and prepared visualizations. K.N. provided resources and funding. M.X. supervised the work, reviewed and edited the manuscript, and acquired funding. All authors reviewed the manuscript.\u003c/p\u003e\u003ch2\u003eAcknowledgement\u003c/h2\u003e \u003cp\u003eThis research was supported by the Jilin Petrochemical Company of China National Petroleum Corporation (Project No. :232022400002).\u003c/p\u003e"},{"header":"References","content":"\u003col\u003e\u003cli\u003e\u003cspan\u003eRodrigues PV, Ramoa B, Torres AR, Castro MCR, Machado AV (2023) Enhancing the interface behavior on polycarbonate/elastomeric blends: morphological, structural, and thermal characterization. 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J Appl Polym Sci 122:2992\u0026ndash;2999. \u003cspan class=\"ExternalRef\"\u003e\u003cspan class=\"RefSource\"\u003ehttps://doi.org/10.1002/app.34111\u003c/span\u003e\u003cspan address=\"10.1002/app.34111\" targettype=\"DOI\" class=\"RefTarget\"\u003e\u003c/span\u003e\u003c/span\u003e\u003c/span\u003e\u003c/li\u003e\u003c/ol\u003e"}],"fulltextSource":"","fullText":"","funders":[],"hasAdminPriorityOnWorkflow":false,"hasManuscriptDocX":true,"hasOptedInToPreprint":true,"hasPassedJournalQc":"","hasAnyPriority":false,"hideJournal":false,"highlight":"","institution":"","isAcceptedByJournal":false,"isAuthorSuppliedPdf":false,"isDeskRejected":"","isHiddenFromSearch":false,"isInQc":false,"isInWorkflow":false,"isPdf":false,"isPdfUpToDate":true,"isWithdrawnOrRetracted":false,"journal":{"display":true,"email":"[email protected]","identity":"colloid-and-polymer-science","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":false,"externalIdentity":"","sideBox":" Learn more about [Colloid and Polymer Science](https://www.springer.com/journal/396) ","snPcode":"396","submissionUrl":"https://mc.manuscriptcentral.com/cps","title":"Colloid and Polymer Science","twitterHandle":"","acdcEnabled":true,"dfaEnabled":true,"editorialSystem":"stoa","reportingPortfolio":"Springer Hybrid","inReviewEnabled":true,"inReviewRevisionsEnabled":false},"keywords":"Emulsion polymerization, epoxy-functionalized ABS, PC/ABS","lastPublishedDoi":"10.21203/rs.3.rs-9042941/v1","lastPublishedDoiUrl":"https://doi.org/10.21203/rs.3.rs-9042941/v1","license":{"name":"CC BY 4.0","url":"https://creativecommons.org/licenses/by/4.0/"},"manuscriptAbstract":"\u003cp\u003eIn this study, glycidyl methacrylate (GMA) was introduced as the third monomer via emulsion polymerization to modify polybutadiene-styrene-acrylonitrile terpolymer latex, which enabled the grafting of epoxy groups\u0026mdash;capable of forming chemical bonds with polycarbonate (PC) resin\u0026mdash;onto the modified ABS resin latex. The comprehensive performance of PC/ABS alloys prepared using the modified core-shell structured ABS-g-GMA copolymer was systematically investigated. Fourier transform infrared (FTIR) spectroscopy confirmed the successful grafting of GMA onto the PBSAN latex, while scanning electron microscopy (SEM) revealed that GMA reduced the size of the ABS dispersed phase and enhanced the interfacial compatibility between PC and ABS. Mechanical property analysis demonstrated that when 10 g of GMA was incorporated into the polymerization system, the resulting PC/ABS alloy exhibited a notched impact strength of 60.86 kJ/m\u0026sup2; (a 25.43% increase), along with a tensile strength of 59 MPa, a bending strength of 83.531 MPa, and favorable processability. Additionally, the effect of varying ABS proportions in the PC/ABS alloy was explored, and the optimal comprehensive mechanical properties were achieved at a PC/ABS mass ratio of 70:30. Notably, this epoxy-functionalized ABS latex eliminates the need for additional compatibilizers during PC/ABS alloy preparation, providing a simple and feasible approach for fabricating high-performance PC/ABS alloys.\u003c/p\u003e","manuscriptTitle":"The influence of epoxy-functionalized acrylonitrile-butadiene-styrene on the properties of PC/ABS alloy","msid":"","msnumber":"","nonDraftVersions":[{"code":1,"date":"2026-03-16 15:35:16","doi":"10.21203/rs.3.rs-9042941/v1","editorialEvents":[{"type":"communityComments","content":0},{"type":"decision","content":"Revision requested","date":"2026-03-29T22:09:35+00:00","index":"","fulltext":""},{"type":"editorInvitedReview","content":"","date":"2026-03-28T16:04:04+00:00","index":"hide","fulltext":""},{"type":"reviewerAgreed","content":"139731264948468983001148328743384041609","date":"2026-03-19T23:18:31+00:00","index":"hide","fulltext":""},{"type":"reviewersInvited","content":"","date":"2026-03-13T11:58:42+00:00","index":"","fulltext":""},{"type":"editorAssigned","content":"","date":"2026-03-12T05:33:18+00:00","index":"","fulltext":""},{"type":"checksComplete","content":"","date":"2026-03-12T05:32:29+00:00","index":"","fulltext":""},{"type":"submitted","content":"Colloid and Polymer Science","date":"2026-03-05T17:08:54+00:00","index":"","fulltext":""}],"status":"published","journal":{"display":true,"email":"[email protected]","identity":"colloid-and-polymer-science","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":false,"externalIdentity":"","sideBox":" Learn more about [Colloid and Polymer Science](https://www.springer.com/journal/396) ","snPcode":"396","submissionUrl":"https://mc.manuscriptcentral.com/cps","title":"Colloid and Polymer Science","twitterHandle":"","acdcEnabled":true,"dfaEnabled":true,"editorialSystem":"stoa","reportingPortfolio":"Springer Hybrid","inReviewEnabled":true,"inReviewRevisionsEnabled":false}}],"origin":"","ownerIdentity":"af09d485-4046-4f99-b95a-1e8f30a2a09d","owner":[],"postedDate":"March 16th, 2026","published":true,"recentEditorialEvents":[],"rejectedJournal":[],"revision":"","amendment":"","status":"in-revision","subjectAreas":[],"tags":[],"updatedAt":"2026-03-29T22:23:43+00:00","versionOfRecord":[],"versionCreatedAt":"2026-03-16 15:35:16","video":"","vorDoi":"","vorDoiUrl":"","workflowStages":[]},"version":"v1","identity":"rs-9042941","journalConfig":"researchsquare"},"__N_SSP":true},"page":"/article/[identity]/[[...version]]","query":{"redirect":"/article/rs-9042941","identity":"rs-9042941","version":["v1"]},"buildId":"XKTyCvWXoU3ODBz1xrDgd","isFallback":false,"isExperimentalCompile":false,"dynamicIds":[84888],"gssp":true,"scriptLoader":[]}