Xu Luo,
Yu Li*,
Zhaoyi Sun,
Guorong Wang and
Jie Xin
Department of Basic, Naval University of Engineering, Wuhan 430033, China. E-mail: luoxu19980504@163.com
First published on 15th July 2022
In this study, carboxyl-terminated polybutylene adipate (CTPBA) was used to modify epoxy resin, and the modified epoxy resin was cured by a room temperature rapid curing agent (T-31). The effects of CTPBA modification on bonding properties and mechanical properties of epoxy resin adhesive at room temperature were carefully studied. Epoxy-terminated prepolymer was synthesized by pre-polymerization and its structure was characterized. Compared with the addition method of direct blending, the bonding properties and mechanical properties of pre-polymerized epoxy resin adhesive were significantly better. Compared with unmodified epoxy resin, CTPBA modification significantly improved the bonding strength. Furthermore, with the increase of CTPBA content, the shear strength of the material increased first and then decreased, and reached the maximum when the addition amount was 40 phr. This shows that the tensile strength of the material decreased with the increase of CTPBA content, and the elongation at break increased with the increase of CTPBA content. Dynamic mechanical analyzer (DMA) test results showed that the addition of CTPBA reduced the glass transition temperature, but broadened the damping temperature range. TG analysis showed that the thermal stability of the modified epoxy resin was good, and compared with pure epoxy resin, the initial temperature of thermal weight loss and the maximum thermal decomposition rate decreased, but the overall thermal stability was not significantly different. In summary, CTPBA modification of epoxy resin is expected to improve the comprehensive mechanical properties at room temperature.
A large number of studies have shown that the addition of toughening agent can effectively improve the toughness of epoxy resin, and the active end groups (such as carboxyl, hydroxyl, isocyanate, amino, etc.) can react with epoxy resin to improve the compatibility with resin matrix and improve the mechanical properties.16,17 Up to now, the active end-group toughening agents mainly include carboxyl-terminated liquid nitrile rubber (CTBN), amino-terminated liquid nitrile rubber (ATBN), polysulfide rubber and so on.18–21 In general, rubber toughened epoxy resin is achieved by modulus loss and glass transition temperature reduction, but the glass transition temperature can be increased by adding other fillers.22,23 The mechanism of action is generally that it reacts with the active groups in epoxy resin such as epoxy group and hydroxyl group to form block polymers. During the curing process, the rubber chain is separated from the system to form a two-phase structure. When the resin matrix is subjected to external force, the rubber disperse the force, so as to achieve the purpose of toughening.24 Substances with similar solubility parameters can dissolve each other, and rubber functionalization can improve the cohesive energy of substances and increase the compatibility between rubber and epoxy resin. Macroscopically, the impact strength or tensile shear strength increases, and the comprehensive performance is effectively improved.25
However, the double bonds in nitrile rubber chains may be oxidized during curing, and the application of nitrile rubber chains is limited due to the presence of a trace carcinogen acrylonitrile.26 Compared with CTBN, the linear carboxyl-terminated polyester has better oxidation stability because it does not contain unsaturated structure, and the polyester material is generally nontoxic, which is in line with the concept of green development. The reports on polyester modified epoxy resin mainly focus on unsaturated polyester and hyperbranched polyester,27–29 while the reports on linear saturated polyester are less. Achary et al.30 modified epoxy resin by carboxyl-terminated poly (propylene adipate) glycol ester (CTPPGA), found that the modified epoxy resin adhesive strength depends on the molecular weight and content, and the epoxy resin adhesive can be used at 120 °C. Ratna et al.26 used carboxyl-terminated polyethylene glycol adipate (CTPEGA) as toughening agent, reacted with epoxy resin to form epoxy-terminated prepolymer. It was found that the addition of CTPEGA greatly improved the impact strength and toughness of epoxy resin. However, these studies did not consider the effects of modification methods and pre-reaction ratio on the properties of epoxy resin modified by carboxyl-terminated polyester.
In this work, carboxyl-terminated poly (butylene adipate) (CTPBA) modified epoxy resin was mainly studied. The epoxy-terminated polybutylene adipate (E-CTPBA) was synthesized by controlling the molar ratio of CTPBA to epoxy resin, and then added to E-51 epoxy resin to improve the bonding performance and mechanical properties of epoxy resin. The effects of molecular weight, modification method and pre-reaction ratio of CTPBA on the properties of epoxy resin adhesive were studied in detail. The chemical structures of CTPBA and E-CTPBA were characterized and analyzed by Fourier transform infrared spectroscopy (FTIR), nuclear magnetic resonance (NMR) and matrix-assisted laser desorption time-of-flight mass spectrometry (MALDI-TOF MS). The thermal stability of modified epoxy resin was studied by thermogravimetric analyzer. The glass transition temperature of modified epoxy resin was studied by DMA. The impact section of cured epoxy resin was observed by scanning electron microscope (SEM).
The tensile properties were measured at 25 °C according to GB/T 2567-2008 standard and the experimental speed was 10 mm min−1. According to GB/T 2567-2008 standard, the impact performance test was carried out by using the plastic pendulum impact tester (PTM1000) without notch impact. And the sample size was 120 mm × 15 mm × 10 mm.
According to GB/T 7124-2008 standard, the tensile shear strength of 100 mm × 25 mm × 1.6 mm SUS321 stainless steel sheet was selected. After grinding, the surface was cleaned with acetone, cleaned and dried for backup use. The length of the bonding surface was 12.5 ± 0.25 mm, the width was 25 ± 0.25 mm, and the thickness of the adhesive layer was about 0.2 mm. The overflow was cleaned in time. After complete curing, the universal tensile testing machine was used to test at 25 °C, and the test speed was 2 mm min−1. T-stripping strength reference GB/T 2791-1995, flexible materials are selected stainless steel, length 200 mm, width 25 mm, thickness 0.15 mm, coating length 150 mm, and running at 100 mm min−1. The gel time test was referred to GB/T 16995-1997. The modified epoxy resin and curing agent were added to the plastic cup to quickly stir and start timing. When the viscosity is increasing, stop stirring and start drawing. When the drawing becomes brittle to fracture and cannot be drawn into silk, stop timing.
According to HG/T 2708-95 chemical industry standard, acid value was measured by end-base titration method. Toluene–ethanol solution (volume ratio 2:
1), 10 g L−1 phenolphthalein solution was used as indicator, and 0.1 mol L−1 potassium hydroxide ethanol standard titration solution was used to titrate to the solution. The solution was peach red and did not fade within 30 s. The calculation formula was as follows:
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Fig. 2 (a) FTIR spectra of E-51, CTPBA and E-CTPBA; (b) synthetic infrared spectra of E-CTPBA varying with time. |
As shown in Fig. 2(b), the infrared spectrum of synthetic E-CTPBA changes with time. It can be seen from the figure that there was no obvious O–H stretching vibration absorption peak at 3489 cm−1 in the initial stage. With the progress of the reaction, the absorption peak gradually appeared, and the intensity of the absorption peak was increasing. This is because CTPBA reacts with E-51 to generate hydroxyl. With the progress of the reaction, the reaction degree is increasing, and the hydroxyl content is increasing, resulting in the increase of the intensity of the absorption peak.
In order to further confirm the chemical structures of the synthesized CTPBA and E-CTPBA, they were characterized by 1H-NMR. Fig. 3(a) and (b) were the 1H-NMR spectra of CTPBA and E-CTPBA, respectively. In the spectrum (a), δ = 4.07 (c) and 1.67(d) belong to the characteristic absorption peaks of H on α carbon and β carbon in the unit structure of 1,4-butanediol, respectively. δ = 2.31(a) and 1.57(b) belong to the characteristic absorption peaks of H on α carbon and β carbon in the unit structure of adipic acid, respectively. A single peak appears at δ = 3.66(m), which belongs to the characteristic absorption peak of methylene connected with –COOH. Together with the infrared spectrum, CTPBA is successfully synthesized.
Fig. 3(b) was the nuclear magnetic resonance hydrogen spectrum of E-CTPBA. It can be seen that the characteristic absorption peaks of epoxy resin appear, δ = 2.73(e), 2.88(e) and 3.32(f) belong to the absorption peaks of protons on epoxy groups, δ = 6.80(h) and 7.11(i) belong to the absorption peaks of protons on benzene rings, δ = 3.98(g) and 4.17(g) belong to the absorption peaks of methylene protons (–CH2O). Most of the absorption peaks in CTPBA appeared in the spectrum, while the peaks at δ = 3.66(m) disappeared, and δ = 4.28(l) and 4.69(k) were attributed to the absorption peaks of methylene and methylene connected with hydroxyl, respectively. This indicated that –COOH reacted with epoxy group to generate –OH, which was proved by infrared spectroscopy to synthesize E-CTPBA. Since the hydrogen proton in –COOH and the hydroxyl generated by the reaction were active hydrogen, there was no absorption peak in the 1H-NMR spectrum.
The composition and structure of the synthesized products were evaluated by 1H-NMR and MALDI-TOF MS. Fig. 4(a) was the MALDI-TOF MS spectra of CTPBA1000 samples under the reflected light mode. In order to identify the structure of CTPBA1000, the repeat unit is an important ‘judgment’ basis. According to the structural formula, the composition of the repeat unit is C10H16O4, and the adjacent peak spacing of each peak is 200, which is consistent with the mass number of the repeat unit of 200.12. All the peaks in this spectrum were consistent with n repeat units (200.12 × n) in CTPBA plus two terminal groups (–C6O3H9, M = 129.07 and –OH, M = 17.01) and Na+ and K+ (Na+ and K+ often appear in the MALDI spectrum of the sample). For example, the mass of the macromolecular chain containing four repeat units (n = 4) was 200.12 × 4 + 129.07 + 17.01 + 22.99 = 969.55, which was close to the peak of 970.77 Da in the spectrum. Together with the previous 1H-NMR and IR spectra, CTPBA was successfully synthesized.
Fig. 4(b) is the MALDI-TOF MS mass spectrum of E-CTPBA1000, its structure and synthesis process can be obtained from Fig. 1. We found that all peak shifts were consistent with the reaction. For example, when n = 4, the peak value of 1788.233 Da in E-CTPBA1000 can be expressed as 200.12 × 4 + 129.07 + 17.01 + 22.99 + 2 × 409 = 1787.55 Da, which was obtained by the peak value of 970.77 Da in CTPBA1000 plus the sum of two epoxy resins (E-51, M = 370–420).
Sample | Adipic acid![]() ![]() |
Acid value (mg KOH g−1) | Hydroxyl value (mg KOH g−1) | Molecular weight measured by end-group titration method | Mn | Mw | Mz | Mw/Mn |
---|---|---|---|---|---|---|---|---|
CTPBA1000 | 1.26![]() ![]() |
122 | Nil | 919 | 2445 | 3943 | 6156 | 1.61 |
CTPBA2000 | 1.12![]() ![]() |
51 | Nil | 2200 | 3838 | 8741 | 15850 | 2.28 |
CTPBA3000 | 1.08![]() ![]() |
41 | Nil | 2737 | 4294 | 10200 | 19645 | 2.38 |
Sample | Tensile shear strength (MPa) | T peel strength (kN m−1) | Tensile strength (MPa) | Elongation at break (%) | Impact strength (kJ m−2) |
---|---|---|---|---|---|
E-51 | 9.61 | 0.02 | 35.85 | 4.49 | 2.92 |
E-CTPBA1000-2-1 | 11.35 | 0.08 | 30.66 | 22.21 | 3.71 |
E-CTPBA2000-2-1 | 11.44 | 0.12 | 20.48 | 23.92 | 9.18 |
E-CTPBA3000-2-1 | 4.38 | 0.24 | 20.20 | 24.02 | 3.42 |
As shown in Table 2, when the addition amount was 20 phr, the tensile shear strength of E-CTPBA2000-2-1 was the largest, and the peel strength increased with the increase of molecular weight. The tensile strength decreased with the increase of molecular weight, but the elongation at break increased with the increase of molecular weight. This may be due to the linear polyester was a flexible chain segment, and the compatibility between epoxy resin and E-51 was relatively good after epoxy end sealing. With the curing reaction, the chain extension of epoxy resin and the increase of molecular weight, the compatibility between the two gradually deteriorates, and gradually formed the island structure, which produced obvious toughening effect. Macroscopically, the elongation at break increased gradually. However, with the increase of molecular weight, the distance between cross-linking points in the cross-linking network structure increased, resulting in the decrease of cross-linking density, the decrease of intermolecular chain force, and the decrease of tensile strength macroscopically.31
The impact strength of E-CTPBA was significantly improved compared with that of pure epoxy resin, and reached the maximum when the molecular weight was 2000. This may be because CTPBA had good compatibility with the resin matrix after being terminated by epoxy resin, and the epoxy group was involved in the curing reaction, which improved the crosslinking density and increased the stress point. When subjected to instantaneous force, the impact strength increased due to the increase of the stress point and the good dispersion effect of the flexible segment.
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Fig. 5 The curves of (a) impact strength (b) tensile shear strength (c) tensile strength and (d) elongation at break under different modification methods. |
Method 1: metric CTPBA was reacted with E-51 at 96 °C for 3 h, and 0.3 wt% catalyst triphenylphosphine was added.
Method 2: the measured CTPBA was directly blended with E-51.
Method 3: the CTPBA with molar ratio of 1:
2 was reacted with E-51 at 96 °C to obtain the epoxy-terminated E-CTPBA-2-1, which was then added into the epoxy resin in proportion.
It can be seen from Fig. 5 that different modification methods had a great influence on the adhesive properties of the system. When CTPBA was directly blended with E-51, it showed the characteristics of ordinary liquid rubber toughening, and the peeling strength was enhanced, but it was significantly worse than that of the other two addition methods. The tensile shear strength was lower than that of pure epoxy resin system, and decreased with the increase of addition amount. Relatively speaking, the bonding performance of controlled molecular weight synthesis was the best, which may be due to the poor compatibility between CTPBA and E-51 by direct blending, showing the toughening characteristics of ordinary liquid rubber, while the compatibility between E-CTPBA and E-51 formed by epoxy end sealing was better, and it was easy to form island structure in the curing process.
The tensile strength decreased with the increase of CTPBA, and the tensile strength after modification according to molecular weight design was greater than that of the other two methods. The elongation at break increased with the increase of CTPBA, which was greatly improved compared with pure epoxy resin. The impact strength of molecular weight design modification and pre-reaction both increased first and then decreased. The impact strength reached the maximum when the addition amount was 40 phr, which was 324.7% higher than that of pure epoxy. Relatively speaking, the way of controlling molecular weight design and modification is method 3, which has the best comprehensive performance.
It can be seen from Table 3 that the peel strength, tensile shear strength and gel time increase with the increase of the feed ratio, which may be due to the larger the feed ratio, the lower the epoxy group content, and the increase of gel time. With the increase of the feed ratio, the tensile strength decreased gradually, but the elongation at break increased. This may be due to the rigid structure of the benzene ring in bisphenol A epoxy resin, which can improve the tensile strength. With the increase of the feed ratio, the content of the rigid structure of the benzene ring in the same mass of the copolymer decreased, which reduced the tensile strength and increased the elongation at break. Overall, the tensile strength of modified epoxy resin was lower than that of pure epoxy resin, and the elongation at break increased. The impact strength had little change, but it was significantly higher than that of pure epoxy resin.
Sample | Molar ratio | Tensile shear strength (MPa) | T peel strength (kN m−1) | Gel time (min) | Tensile strength (MPa) | Elongation at break (%) | Impact strength (kJ m−2) |
---|---|---|---|---|---|---|---|
E-CTPBA1000-2-1 | 1![]() ![]() |
11.35 | 0.08 | 75 | 30.66 | 18.22 | 3.71 |
E-CTPBA1000-3-2 | 2![]() ![]() |
12.18 | 0.11 | 80 | 22.81 | 19.38 | 3.15 |
E-CTPBA1000-4-3 | 3![]() ![]() |
12.50 | 0.12 | 93 | 18.82 | 28.96 | 3.58 |
The failure mode of stainless steel sheet after tensile shear test of carboxyl-terminated polyester modified epoxy resin adhesive was analyzed. When the amount of carboxyl-terminated polyester modified epoxy resin adhesive was 80 phr and 100 phr, the adhesive on the bonding interface was peeled off from the whole fracture, one bonding surface was smooth, and the other bonding surface was attached to the whole adhesive, which belonged to the form of interface failure. When the addition amount was less than 80 phr, the bonding surface was rough, and adhesive was distributed on both steel sheets. At this time, interface failure and cohesion failure occurred simultaneously. The main reason for the interfacial failure may be that the content of polyester as a flexible segment is too high, resulting in low strength, which cannot be well bonded with the steel sheet, and it is easy to fall off from the steel sheet as a whole. When the polyester content is low, the epoxy resin modified by carboxyl terminated polyester and the epoxy resin E-51 form a close winding and crosslinking, forming a network structure, and the stress can be better dispersed. At this time, it is easy to cause the damage of the resin matrix itself, namely, the cohesive failure. Compared with the interfacial failure, more energy was needed to absorb, so that the tensile shear strength was increased.1,32
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Fig. 7 Effect curves of the E-CTPBA1000 addition on (a) tensile strength and elongation at break; (b) impact strength. |
The effect of E-CTPBA1000-2-1 addition on the impact strength of the system was shown in Fig. 7(b). It can be seen that with the increase of the addition amount, the impact strength increased first, then decreased and then increased. When the addition amount reached 100%, the impact strength reached the maximum, which was 343.5% higher than that of pure epoxy resin system. In similar studies on toughening, Shiai Xu used liquid carboxyl terminated nitrile rubber (CTBN) as a toughening agent. When the addition amount of CTBN was 15 phr, the toughness was the largest, and the impact strength was 1.95 kJ m−2. The toughening effect was not obvious.25 Akbari used CTBN as toughening agent, and its impact strength of pure epoxy resin was 7.19 kJ m−2. When the addition amount of CTBN was 15 phr, the impact strength reached 19.20 kJ m−2, increasing by 167.04%.24 As reported by D. Ratna, when the addition amount of CTPEGA was 20 phr, the maximum value was 32.0 J m−1, which was 73.0% higher than that of pure matrix, and the toughening effect was poor. The impact strength of the material mainly depended on the toughness of the material. The linear polyester was a kind of flexible material with great elasticity, while the epoxy resin E-51 contained phenyl functional groups and had great brittleness. As a flexible chain, polyester was interspersed in the cross-linked network structure. When subjected to impact, it can well disperse the stress and increase the fracture energy of the material, and increase the impact strength after adding an appropriate amount of CTPBA.
Fig. 8 was the SEM images of the impact section of epoxy resin cured with different amounts of E-CTPBA1000-2-1. It can be clearly seen from the figure that the impact fracture surface of pure epoxy resin was smooth without obvious defects, showing typical brittle fracture characteristics. Compared with epoxy resin, the fracture surface of carboxyl-terminated polyester modified epoxy resin was rough, showing ductile fracture characteristics. When the addition amount was 40 phr, the branching pattern appears, the surface was smoother, and the corresponding impact strength was relatively large. When the addition amount was 60 phr, there was a more serious agglomeration phenomenon, which reduced the impact strength, when the addition amount continued to increase, the polyester became a continuous phase, and the epoxy resin was a dispersed phase. The dimples increased, showing typical ductile fracture characteristics.
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Fig. 9 Curve of E-CTPBA1000 addition to modified epoxy resin (a) tan![]() |
In China, the temperature range corresponding to the loss factor greater than or equal to 0.3 is called the effective damping temperature range DTR (Damping Temperature Range) of the damping material. The damping performance data were shown in Table 4. It can be seen that the damping temperature range gradually increased with the increase of the addition amount. When the addition was 100 phr, the glass transition temperature increased and the tanδ peak decreased.
Content | 0 phr | 20 phr | 40 phr | 60 phr | 80 phr | 100 phr |
---|---|---|---|---|---|---|
Tg/°C | 88.4 | 70.3 | 60.8 | 51.9 | 49.1 | 54.9 |
DTR/(tan![]() |
21 (79–100) | 26 (58–84) | 29 (47–76) | 30 (37–67) | 31 (34–65) | 37 (36–73) |
tan![]() |
0.81 | 0.78 | 0.92 | 0.97 | 1.01 | 0.84 |
The effects of different modification methods and molecular weight on the properties of epoxy resin were studied. When CTPBA with molecular weight of 1000 was used and the epoxy terminated polymer (E-CTPBA) was synthesized by controlling the molar ratio, the comprehensive mechanical properties of the modified epoxy resin were the best, which provided a screening method for other linear carboxyl-terminated polyesters (such as carboxyl-terminated poly adipic acid adipate, carboxyl-terminated polybutadiene glycol ester, etc.) to modify epoxy resin. In order to improve the adhesion and mechanical properties of epoxy resin, the modifier E-CTPBA was added to the E-51 resin matrix. The addition of E-CTPBA can improve the tensile shear strength, peel strength, elongation at break and impact strength, while the tensile strength decreases. When the addition amount was 40 phr, the adhesive property and toughness of the system were the best. Compared with pure epoxy resin, the tensile shear strength and toughness increased by 19.0% and 139.0%, respectively, but the tensile strength decreased by 43.6%. The thermal stability of the system was good. Compared with pure epoxy resin, the initial temperature and maximum thermal decomposition rate of the system were reduced, but the overall thermal stability is similar. Therefore, it is a promising method for modifying epoxy resin to control the end of epoxy resin by modification.
Footnote |
† Electronic supplementary information (ESI) available. See https://doi.org/10.1039/d2ra02915d |
This journal is © The Royal Society of Chemistry 2022 |