International Journal of Corrosion

International Journal of Corrosion / 2019 / Article

Research Article | Open Access

Volume 2019 |Article ID 5470646 |

Wenrui Bian, Zhongchang Wang, Mo Zhang, "Epoxy Resin’s Influence in Metakaolin-Based Geopolymer’s Antiseawater Corrosion Performance", International Journal of Corrosion, vol. 2019, Article ID 5470646, 7 pages, 2019.

Epoxy Resin’s Influence in Metakaolin-Based Geopolymer’s Antiseawater Corrosion Performance

Academic Editor: Yuxin Wang
Received24 Feb 2019
Revised27 May 2019
Accepted12 Jun 2019
Published03 Jul 2019


To obtain the influence mechanism of epoxy resin content, curing time, and other external factors on the compressive strength and seawater corrosion resistance of geopolymer, the NaOH and Na2SiO3 were used as activators; the effect of epoxy resin concentration on the corrosion resistance of metakaolin-based geopolymer was investigated by experiments. The mechanism of epoxy resin concentration affecting the polymerization process and the properties of geopolymer was analyzed by X-ray diffraction, scanning electron microscopy-energy spectrum, and Fourier transform infrared spectroscopy. It was shown that the epoxy resin slowed down the polymerization. The presence of epoxy resin had a beneficial effect on compact structure. Furthermore, compared with the noncorrosive specimen, mixed with 30% specimen’s average compressive strength increased by 4.77MPa and 4.24MPa after curing for 1d and 3d and soaking for 56d.

1. Introduction

With the economic development of the Yangtze River Delta, the Pearl River Delta and the Bohai Bay region, more and more coastal infrastructures were built. However, the concrete structures are prone to be corroded in marine environment. The repair costs are high [1]. Improving corrosion resistance of offshore concrete structures is becoming more and more important. Current methods to prevent corrosion are mainly considered in the design stage, material selection, concrete mix design, adequate compaction, curing and anticorrosion coatings [2]. The traditional anticorrosive coatings such as epoxy anticorrosive coatings, rubber anticorrosive coatings, and polyurethane anticorrosive coatings had large solvent pollution, short antiseptic life, and poor weather resistance. The modified coatings did not change the internal structure and could not have excellent properties [37].

Geopolymers were an inorganic polymer formed by and first used by J. Davidovits in the late 1970s [8]. As emerging cementations materials, geopolymers have their great mechanical properties with low CO2 emission and low energy consumption. The reaction of synthetic geopolymers requires metakaolin or raw silico-aluminates. The CO2 emission can be reduced by 20% [9, 10]. Some industrial waste with amorphous silicon aluminum structure can be used to synthesize geopolymers, for example, metakaolin, fly ash, red mud, and granulated blast furnace slag [11]. The metakaolin has become the best aluminosilicate material owing to its high rate of dissolution in the reactant solution [1214]. Geopolymer based materials have excellent mechanical properties, high early strength, freeze-thaw resistance, low chloride diffusion rate, abrasion resistance, and thermal stability [9, 15, 16]. Geopolymer has lower calcium content and stronger acid corrosion resistance than traditional cement [17]. Geopolymers as anticorrosive coatings are seldom studied. Ana María Aguirre-Guerrero et al. used impressed voltage and wetting/drying (w/d) cycles in the presence of a 3.5% NaCl solution to investigate the MK based geopolymer had better corrosion resistance [18]. Zhang et al. obtained good corrosion resistance by using a liquid-solid ratio of 90% metakaolin and 10% blast furnace slag at a liquid-solid ratio of 0.6 ml/g. It was necessary to add polypropylene (PP) fiber and MgO expansion agent to improve dry shrinkage properties of geopolymers. The geopolymer could be a new type of green anticorrosion coating. Its development in anticorrosion coating is limited due to its drawbacks of large shrinkage and easy cracking [19].

In order to solve the issues previously described and to improve the geopolymers’ technologic properties, in the paper geopolymers containing epoxy resins with different mass ratio had been produced. Moreover, in order to investigate the morphology and the interface interactions between the geopolymers and the epoxy resins, a detailed microstructural analysis was performed.

2. Materials and Methods

2.1. Materials

The metakaolin (MK) from Jiaozuo Yu Kun Mining Co., Ltd. in Henan province was used as the raw material for geopolymer synthesis. The composition of MK was listed in Table 1. The Na2SiO3 (SiO2/Na2O molar ratio 2.0) was from a chemical plant in Hebei province, and the NaOH was from Dalian. The epoxy resin was from a chemical plant in Zhejiang province. The seawater was taken from the offshore waters of Dalian Heishijiao Park.



2.2. Specimen Preparation

The mixture of 50% NaOH and Na2SiO3 solution with SiO2/Na2O molar ratio 2.0 was used as the activator. The mass ratio of epoxy resin was 0%, 10%, 20%, and 30%, respectively.

The activator and metakaolin were mixed and stirred for 10min. Then, epoxy resin was added and continued to mix for 5 minutes. The slurry was poured into cylindrical molds and vibrated for 30 seconds for preparing φ37mm×750mm cylinder samples. Then, the slurry was sealed in zip bags and curing under room temperature until unconfined compression tests. Based on the ratios of epoxy resin (0%, 10%, 20%, and 30%), EGP0, EGP10, EGP20, and EGP30 were used.

2.3. Mechanical and Microstructural Characterization
2.3.1. Anticorrosion Performance Test

The anticorrosion performance was mainly determined by the compressive strength under different curing time and corrosion time under different resin dosages. To investigate the compression strength of the Epoxy Geopolymer (EGP), the unconfined compression test was conducted on a universal testing machine. The constant loading rate was 0.0788 in./min. To reduce the effect of uneven surface formed during curing, the top surface of sample was covered with a cardboard.

2.3.2. Microstructural Characterization

To observe the microscopic morphological changes of epoxy resin geopolymer samples after seawater corrosion, SEM scanning of selected samples was performed by JSM-6360LV scanning electron microscope. The 5×5×5mm cubic specimen was trimmed off from the center of the destroyed specimen. After drying, the sample was placed on the alumina stud with conductive adhesive for coating with gold-palladium alloy.

2.3.3. Mineralogy Characterization

The mineralogical changes of the epoxy resin geopolymer samples after seawater corrosion were analyzed using an Empyrean X-ray diffractometer. The main purpose of the XRD test was to determine whether the geopolymer precursor and the epoxy resin had undergone a chemical reaction and whether the geopolymer had reacted with seawater. This can be done by observing whether a new peak (new mineral) was produced on the map. CuKα radiation was used and analyzed by MDI Jade 5.0 (see Table 2).

SymbolMineral nameChemical formula

bSodium aluminosilicateNa2O Al2O3 SiO2
cSodium feldsparNaAlSi3O8
dHydrate sodium aluminosilicateNaSiAlO4 H2O
fCubiciteNa(Si2Al)O6 H2O

3. Results and Discussion

3.1. Mechanical Properties of Different Resin-Doped Geopolymers

The compressive strength data of the resin blends at 0%, 10%, 20%, and 30% for 1d, 3d, and 28d was shown in Figure 1. The compressive strength of EGP0-EGP30 after curing for 1d was 15.32MPa, 11.376MPa, 10.04MPa, and 7.90MPa, respectively. The strength of EGP0 was 7.42MPa higher than the strength of EGP30, and the compressive strength of EGP0 was 4.17MPa higher than the strength of EGP30 after curing for 28d. The compressive strength growth rate of EGP0-EGP30 group after curing for 28 days compared with curing for 3d was 18.52%, 49.12%, 57.04%, and 65.34%, respectively.

The effect of resin on the compressive strength of geopolymer was as follows. With the increase of resin content, the compressive strength of geopolymer decreased gradually. This may be because there were a large number of small bubbles in the resin, but the bubbles were not completely discharged after mixing and vibration exhaust. With the increase of resin content, the number of bubbles increased, and the internal structure of geopolymer was more loose. The effect of curing time on the compressive strength of geopolymer was as follows. With the increase of the curing time, the compressive strength of geopolymer increased gradually, but with the increase of resin content after 3 days of curing, the increase rate of the compressive strength of geopolymer increased gradually.

The geopolymer without epoxy resin will achieve high compressive strength after 1d of curing, which was due to the rapid reaction of the metakaolin base precursor. In the early stage of curing, the polycondensation reaction was completed, so that the strength was increased, and the epoxy resin will be doped into the alkali excitation solution to hinder the reaction. So the compressive strength of geopolymer which mixed epoxy resin would be improved in the later curing times.

3.2. Mineralogy Characterization

The X-ray diffraction (XRD) spectrum of the epoxy resin metakaolin geopolymer curing 28 d was shown in Figure 2. It can be seen that the composition of metakaolin was mainly an amorphous structure. Compared with the metakaolin, the geopolymers’ peaks at 2θ 25° and 30° were gradually weakened, and the phase corresponding to the e peak was quartz phase, indicating that the quartz phase was decreasing. However, two peaks c and d appeared in EGP10-EGP30, which may be caused by incomplete reaction; the aluminosilicate dissolved in an alkaline solution and formed a hydroxylated chain product without proceeding. The water molecules were decomposed between the chain products to form a three-dimensional network structure. This also explains why the strength of the geopolymer increased as the soaking time increases. There was no significant change in the pattern after the addition of epoxy resin (no new minerals were formed), so the compressive strength was largely determined by the geopolymer gel.

3.3. Score FTIR Spectra of Epoxy Resin, Metakaolin, and Geopolymer with Different Epoxy Resin Concentrations

According to the existing research, the functional groups represented by the infrared vibration peak are shown in Table 3 [20, 21].


3700-3600Stretching vibration (OH)
3600-2200Stretching vibration(OH,HOH)
1700-1600Bending vibration(HOH)
1430-1410Stretching vibration(O C O)
1200-950Non-symmetric stretching vibration (T O Si, T= Si, Al)
1100Non-symmetric stretching vibration(Si O Si)
800-780Symmetric stretching vibration(Si O Si)
424-470Bending vibration(Si O Si and O Si O)

Compared to the metakaolin, it can be seen from Figures 3 and 4 that the geopolymer has 4 more obvious peaks: a (1000 cm−1), b (1050 cm−1), c (1590 cm−1), and d (3400 cm−1). As shown in Figure 5 with the metakaolin, there was no e (811 cm−1) peak, and e represented Al-O, so it indicated that metakaolin had been dissolved in the solution. The peaks a and b represented the vibration of the asymmetric functional group T-O-Si (T was Si or Al) since the energy contained in the Si atom was larger than the energy contained in the Al atom. The vibration moves in the direction of the low wave number as the Al atom composition in the structure increases. Compared with the metakaolin, geopolymers’ T-O-Si (T:Sior Al) shifted to the a peak, and it indicated all groups formed geopolymer gel. However it could be seen from Figure 5 that the EGP20 vibrated most obviously at a, so it had more Si-O-Al, because of the Si-O-Si chemical bond had higher strength, so the EGP20’s had the lowest compressive strength. The c peak belongs to the bending vibration of HOH. The vibration peak showed the bound water and interlayer water entrained inside the geopolymer after the reaction, and it could be seen that the peak vibration was weakened as the amount of the resin was increased. This could be inferred that the resin slowed down the evaporation of water molecules after the geopolymerization. The -OH stretching vibration of the peak d reflected a hydroxyl group-containing gel in which the inside of the geopolymer did not undergo a polycondensation reaction after dissolution [22, 23].

3.4. SEM Image and Energy Spectrum Analysis of Geopolymers

The microscopic morphology of the fracture surface of different resin-doped geopolymers after curing 28d was shown in Figure 6. It can be seen from Figure 6 that the white matter was a nonconducting material, the spherical one was epoxy resin, and the other irregular ones were metakaolin or other impurities. The EGP0 geopolymer’s microstructure was dense, and the gel formed a homogeneous whole. After adding epoxy resin, geopolymer’s microstructure was loose; therefore, the compressive strength decreased after adding the resin. But the epoxy resin was embedded in the gel and formed a whole.

Table 4 shows the ratio of silicon to aluminum of the polymer in different resin dosages. When the ratio of silicon to aluminum was in the range of 2-3, it was very close to the pure geopolymer gel, which indicated that the epoxy resin only inhibited the progress of the reaction.



The ratio of silica to aluminum with different resin content was shown in Table 4. The gel can be divided into the PS, PSS, and PSDS gel according to the ratio of Si to Al. From the ratio of Si to Al, it was known that the PSS was the main type of gel when no epoxy resin was added, and with the increase of epoxy resin, the PSDS type was the main type of gel. It can be explained that the formation of polymer gel without hindering the addition of epoxy resin merely slowed down the reaction time.

3.5. Corrosion Resistance of Geopolymers

It can be seen from Figure 7 that the compressive strength of EGP 0 decreased, which is not related to the length of curing time. This is because alkali-exciting solution is basically completed when EGP 0 was curing 1d. The compressive strength also reached a higher level. The compressive strength of EGP10 and EGP20 did not change much with the soaking time after curing for 1d and 3d. The compressive strength of EGP10 and EGP20 decreased with the soaking time after curing for 28d. However, the strength of EGP 30 decreased by 4.94 MPa with the immersion time after curing for 28d, but the compressive strength increased with the immersion time during the curing time of 1d and 3d (the compressive strength was enhanced by 4.77 MPa and 4.24 MPa, respectively). This may be due to the fact that the structure becomes denser after the addition of the epoxy resin, the corrosion resistance can be excellent, or the seawater inhibited the polycondensation reaction, resulting in a slow increase in strength.

3.6. Mineralogy Characterization

The effect of seawater immersion on the compressive strength of geopolymers was as follows. After curing for 1d and 3d, as the soaking time increased, the compressive strength of the geopolymer gradually decreased. But with the addition of epoxy resin, the decreasing trend of compressive strength of geopolymers was alleviated, and even the compressive strength of EGP30 increased (the compressive strength increased by 4.77MPa and 4.24MPa, respectively). The reason for this phenomenon was that the reaction between metakaolin and alkali excited solution was basically completed when EGP 0 curing for 1d, and the compressive strength had reached a high level; however the EGP 10, 20, and 30 groups did not complete the polycondensation reaction due to the presence of epoxy resin, and the excessive water also slowed down the polycondensation reaction; therefore the amount of geopolymer gels decreased, so did the compressive strength. However, the mechanical strength of EGP30 was significantly improved after soaking for 56 days, which may be due to the formation of the geopolymer gels; it made the structure dense and offset the microcrack expansion caused by seawater corrosion. After 28 days of curing, the compressive strength of all groups decreased because the geopolymer had completed the polycondensation, but as the curing days are gone, microcracks occurred and seawater corrosion also increased the expansion of cracks, but these cracks did not influence the compressive strength in the early stage. Although the compressive strength of EGP 0-30 decreased by 8.55MPa, 5.66MPa, 4.76MPa, and 3.94MPa, respectively, with the addition of the epoxy resin, the seawater corrosion resistance of the geopolymer enhanced (see Table 5).

SymbolMineral nameChemical formula

aSodium aluminosilicateNa3Al3Si5O14
eCubiciteNa(Si2Al)O6 H2O

The X-ray diffraction pattern after seawater erosion for 56 days was shown in Figure 8. The metasilicate kaolin base polymer phase with epoxy resin was aluminosilicate, which indicated that seawater erosion had no obvious influence on the material phase structure of the test piece. Metakaolin base polymer had good seawater corrosion resistance

4. Conclusion

The effect of epoxy resin on the compressive strength of geopolymers was investigated by experiments. The mechanism of the impact resistance of epoxy resin on geopolymers and the antiseawater performance of geopolymer with different epoxy resin concentrations were studied.

(1) The metakaolin base geopolymer mainly consists of an amorphous phase and a quartz phase. As the epoxy resin was added, the geopolymer did not form other phases.

(2) The epoxy resin could inhibit the polymerization reaction, and the compressive strength of the metakaolin-based geopolymer increased slowly. Compared with curing for 3d, the compressive strength growth rate of EGP 30 group after curing for 28 days was 65.34%.

(3) The antiseawater performance of epoxy resin metakaolin geopolymer was better, and the compressive strength enhanced by 4.77 MPa when curing for 1d and soaking for 56d.

Data Availability

The data used to support the findings of this study are included within the article. No additional unpublished data are available.

Conflicts of Interest

The authors declare that they have no conflicts of interest.


This work was supported by The Key State Laboratory of Coastal and Offshore Engineering (No. LP1720) and Liaoning Province Natural Science Foundation of China (No. 20170540143).


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