The Curing Kinetics of Multiscale [Ni(EDTA)]-2 Intercalated Zn-Al Layered Double Hydroxides: Glass Fiber–Epoxy Composite Prepreg
In the present research, the effect of Zn2Al layered double hydroxides (LDH) and nickel (II)-EDTA complex intercalated LDH (LDH-[Ni(EDTA)]-2) on the cure kinetics of glass fiber/epoxy prepreg (GEP) was explored using nonisothermal differential scanning calorimetry (DSC). The results showed that LDH caused a shift in the cure temperature toward lower temperatures while accelerating the curing of epoxy prepregs. The use of LDH-[Ni(EDTA)]-2 more profoundly influenced the acceleration of the curing process. The curing kinetics of prepregs was assessed through the differential isoconversional Friedman (FR) technique and the integration method of Flynn–Wall–Ozawa (FWO) and Kissinger–Akahira–Sunose (KAS). A decrease was detected in the value of glass fiber/LDH-[Ni(EDTA)]-2/epoxy (GELP) and glass fiber/LDH-[Ni(EDTA)]-2/epoxy (GELNiP) prepregs at small cure degrees relative to GEP, suggesting the catalytic effect of LDH or LDH-[Ni(EDTA)]-2 on the initial epoxy/amine reaction. Furthermore, LDH-[Ni(EDTA)]-2 performed better due to the catalyst role of nickel (II). Moreover, the activation energy exhibited lower reliance on the degree of conversion in the cases of GELP and GELNiP rather than pure epoxy prepregs. An autocatalytic model was used to evaluate the curing behavior of the system. Based on the results, the curing reaction of the epoxy prepreg can be described by the autocatalytic Šesták-Berggren model even after the incorporation of LDH or LDH-[Ni(EDTA)]-2. The kinetic parameters of the autocatalytic model (such as , , , ) and the equations explaining the curing behavior of prepregs were introduced as well whose predictions were in line with the experimental findings.
Glass fiber/epoxy prepregs have been extensively utilized in the structures of automobiles as well as aerospace and space industries owing to their excellent strength-to-weight ratios and proper thermal and electrical features [1–3]. The ongoing works in the field of composites show that further modification of the systems with nanomaterials could improve their other characteristics such as the interlaminar strength of laminated composites through prepregs. Recently, the nanosized fillers have been incorporated in the prepregs [4–9]. The nanoengineered hybrid epoxy composite laminates include three components: regular reinforcing fibers/fabrics, nanofillers, and epoxy resins. These structures can be fabricated by two general methods; incorporation of nanofillers in the epoxy resin and using the resultant modified epoxy resin to prepare the composite laminate or the introduction of nanofillers on the reinforcing fabric and/or into the interlaminar zone prior to preparing the composite laminate [10, 11]. The layered double hydroxides (LDHs) belong to a class of nanofillers in which positively charged metal hydroxide layers are rested on the brucite structures with intercalated hydrated anions. LDHs are also regarded as hydrotalcite-like compounds or anionic clays with the general formula of [MII1-xMIIIx (OH)2] (An-x/n.mH2O), in which MII and MIII refer to divalent and trivalent metal cations, respectively, occupying the octahedral positions within the hydroxide layers. An− also denotes an interlayer hydrated anion compensating for the layer charge . LDHs can serve as molecular sieves, adsorbents, and catalysts in diverse chemical reactions . Based on their degree of intercalation, exfoliation, and dispersion, the nanosized inorganic LDHs can make a remarkable improvement in thermal stability , mechanical features , flame retardancy behavior , and UV absorption  of neat polymeric matrix/composites, even at relatively small amounts. The organic intercalation of LDH seems to be an efficient approach to improve their compatibility with epoxy and augment their dispersion within the epoxy matrix . As documented, the characteristics of the epoxy-based composites strongly depend on the curing reactions and the extent of 3D network formation during the curing process [2, 16–19]. Curing dramatically alters the thermal, physical, and mechanical features of the system depending on the kinetics of the curing process [1, 20, 21]. The curing process includes a series of complex reactions whose complete investigation requires considering the reactants, curing agent, crosslinkers, catalysts, and products. Regarding the potential impact of the original and organically intercalated on curing kinetics, study of the curing process at their presence could provide valuable information on the chemical reactions and hence deeper understanding of structure-related characteristics of such composites . In the course of thermosetting matrix composite preparation, the reinforcing fibers and nanoparticles restrain the molecular movements of the resin matrix. Despite no changes in the curing mechanism of the resin, some heat released from the resin will be absorbed by the fibers and nonoparticles, leading to a drastic difference in the kinetic parameters of the prepreg and neat resin. Precise curing kinetic parameters are required for prediction of the behavior of the multiscale nanoparticles/fiberglass/epoxy composite preprege during a particular curing cycle. Generally, the extent of improvement in the mechanical and thermal properties of the thermoset nanocomposites has a strong dependence on the curing state . The theoretical models can precisely describe the curing of composite prepreg using the experimental curing findings from differential scanning calorimetry (DSC) . As a thermoanalytical method, DSC correlates the heat flow variations with the resin reaction rates in the course of curing. Dynamic DSC measures the heat flow and total heat flow rates in terms of temperature to offer information with higher reliability compared to the isothermal modes [6, 22, 23]. The curing degree (α) is directly related to the ratio of the crosslinking released heat by to the total amount of heat produced throughout the reaction (i.e., ) .The curing heat can be determined through integration over the entire heat flow curve. and autocatalytic models with the respective curing conversion-dependence functions of and , as well as their combination, are among the various kinetic models of DSC cure analysis capable of predicting the characteristics of the cured system at a particular cure cycle [25, 26]. The and represent the symmetry and shape of the curve of the reaction rate, respectively. The kinetic analyses can be categorized to the model-fitting and model-free schemes. The former requires a proper model for determining the kinetic parameters (e.g., activation energy, conversion equation, and frequency factor) through mathematical optimization methods with the use of experimental from no-isothermal DSC assessments. In the model-free (isoconversional) methods, the curing reaction rate at a definite conversion (α) only relies on temperature. These methods can be classified into two groups; the differential methods such as Friedman (FR) and the integral techniques including Flynn–Wall–Ozawa (FWO) and Kissinger–Akahira–Sunose (KAS) [7, 18, 19]. The errors due to the improper models or parameters should be avoided to reach more accurate activation energies with no interference with the dynamic model functions. Similar kinetic parameters are attained by fitting under isothermal or nonisothermal evaluations; hence, the isothermal curing behavior can be described using nonisothermal data. The variation of the conversion temperature can be determined by 
Using the isoconversional differential methods, the FR model can be expressed as 
in which shows the heating rate (), represents the curing rate (), denotes a preexponential factor, and and are the gas constant (8.314 J/mol) and the absolute temperature (K). stands for the activation energy which alters by curing degree. does not depend on the heating cycle. The activation energy for various curing degrees (α) could be determined through linear regression of and T at different heating rates for diverse curing degrees .
The activation energy for different curing degrees can be determined through the linear fitting of the and the at different heating rates and curing degrees. With the help of isoconversional integral method, KAS can determine the kinetic equation by approximately solving the temperature integral function in equation (4) :
The activation energy for various curing degrees can be attained through linear regression of and at different heating rates.
Many studies have addressed the curing kinetics of glass fiber/epoxy [1, 9] and LDH/epoxy systems . However, the three-component multiscale LDH/fiberglass/epoxy composite prepreg systems have been rarely investigated. Karami et al.  examined the curing potential of the HA-functionalized LDH/epoxy nanocomposites and reported that the kinetics determined by the model-free methods are autocatalytic. Hayaty et al. [30, 31] and Gerami et al.  explored the curing reaction of glass/fiber prepreg and determined the autocatalytic model for the kinetics of both systems. Previous studies indicate that curing kinetic models of the glass/epoxy prepreg are mainly autocatalytic with constant activation energies. Nonetheless, the activation energy of LDH/epoxy systems showed drastic variations in the course of the curing reaction. To our knowledge, there are no studies investigating the curing kinetics of a multiscale LDH/glass/epoxy prepreg. In this context, the present study is aimed at evaluating the influence of Zn2/Al-LDH and [Ni(EDTA)]2- complex intercalated Zn2/Al-LDH (nano)particles on the cure kinetics of glass fiber epoxy in prepreg composites. To this end, three-phase multiscale prepreg was fabricated based on diglycidyl ether of bisphenol A (DGEBA), glass fiber, and LDH (nano)particles. The dynamic DSC was then employed to study the curing activities of the specimens. The variations in the activation energy of samples throughout the curing reactions were examined by isoconversional methods of Friedman (FR), Kissinger-Akahira-Sunose (KAS), and Flynn-Wall-Ozawa (FWO). Further kinetic evaluations were achieved by calculating activation energy (Eα), frequency factor, and the orders of autocatalytic reactions throughout the curing process.
Epoxy resin (EEW: 174 g/eq) and m-phenylenediamine (MPD, 99%) were supplied by Sigma-Aldrich. Aceton (Merck Co.) was utilized as the solvent. The commercial glass fiber fabric (SAERTEX; and weight of 301 g/m2) included two layers of E-glass fibers laid at ±45° upon each other.
2.2. Differential Scanning Calorimetry (DSC)
The curing features of the prepregs were assessed by a DSC (Netsch, 200-F3 Maia, Germany) at the heating rates of 5, 10, 15, and 20 K/min under N2 atmosphere. An empty cell was used as a reference in the temperature range of 25 to 320. The heat flow was normalized to the weight of the samples (4–5 mg). Nitrogen was purged at the rate of 40 mL min−1 to minimize the oxygen accessibility.
2.3. Synthesis of LDH
2.3.1. Synthesis of Zn2/Al-NO3-LDH
The initial LDHs, [Zn2/Al-NO3] which was employed in the anion-exchange reaction, was prepared through the following stages: 12.1 g Al(NO3)3·9H2O and 19.1 g Zn(NO3)2. 6H2O was dissolved in 100 mL deionized and decarbonated water to reach the total Zn: Al ratio of 2. The obtained solution was then dropwise added to 50 mL aqueous solution of 12.5% wt NaOH and 18.2% wt NaNO3 under stirring. The reaction mixture underwent stirring at 60°C until full precipitation. The pH was kept at 8-9 using NaOH solution. The obtained gel-like slurry underwent aging at 60°C for 24 h which was then collected by vacuum filtration after cooling down followed by washing with hot DD water and drying at 65°C for minimum 12 hours, obtained LDH.
2.3.2. Synthesis of Ni2+ Intercalation in [Zn2/Al–EDTA]
The ethylenediaminetetraacetate (EDTA) intercalated LDHs were synthesized through the coprecipitation approach as mentioned elsewhere . In a typical procedure, a solution containing 1.8 g Al(NO3)3·9H2O and 3.5 g Zn(NO3)2·6H2O was made in 150 mL of deionized (DI) water. Afterward, the pH of EDTA aqueous solution (0.1 M) was set to ~7 using NaOH solution which was dropwise added to 150 mL of a metal solution under stirring to maintain the pH at the optimum level (8 to 9). The obtained gel-like slurry underwent overnight aging at 70°C, followed by filtration and several times washing with DI water and air drying at 65°C for 12 h. In the next step, 2 g coprecipitated [Zn2/Al– EDTA] was dispersed in 50 mL of the Ni2+nitrate salt solution. The solution concentration was set at 0.05 M. The suspensions were occasionally shaken at room temperature for 24 h. The obtained solids were filtered, washed with DI water, and air-dried at room temperature. The resulting powder product was named as LDH-[Ni (EDTA)]-2.
2.4. LDH and LDH-[Ni (EDTA)]-2 Characterization
The powder X-ray diffraction (XRD) analysis was carried out using Shimadzu X-ray Diffractometer XRD-7000, with monochromatic Cu Kα radiation () at 40 kV and 30 mA and the dwell time of 1° min−1. Fourier transform infrared (FTIR) spectroscopy (Perkin Elmer; Spectrume GX) was also applied using the KBr pellet technique. The data were recorded at resolution of 2 cm over a wavenumber region of 400–4000 cm−1.
2.5. Preparation of Prepregs
LDH and LDH-[Ni (EDTA)]2- were initially dispersed in acetone followed by 30 minutes of sonication. Subsequently, the (nano)particle suspension was mixed with the epoxy solution in acetone. m-Phenylenediamine (MPD) underwent 20 minutes of premelting at 115°C followed by 30 minutes of high-shear mixing with epoxy/(nano)particle suspension (100 : 15) to reach proper homogeneity. The final content of (nano)particles in the epoxy/MPD matrix was 0.2%wt. Afterward, square patches of commercial glass fiber fabric () were successively put on a flat glass panel and uniformly brushed with the (nano)particle-containing epoxy/MPD/acetone blend. The prepregs were then placed in an oven at 50°C for 30 min to enhance their wettability and eliminate any residual solvent. The specimens were labeled as GEP (glass fiber/epoxy prepreg), GELP (glass fiber/epoxy/LDH prepreg), and GELNiP (glass fiber/epoxy/LDH-[Ni(EDTA)]-2 prepreg). The prepregs were kept at -10°C until further evaluations.
3. Result and Discussion
3.1. LDH Characterization
Figure 1 depicts the FTIR results of LDH and LDH-[Ni(EDTA)]2-.
In the case of LDH, the peak at 3400 cm−1 can be assigned to the O-H vibrations in the hydroxyl groups and H2O. A weak absorption at 1630 cm−1in the FTIR spectra can be ascribed to the H2O bending vibration of the interlayer water. The peaks at 460, 550, and 790 cm−1 are related to the Al-O condensed groups, Zn/Al-OH translation, and the Al-OH deformation, respectively . A strong signal at about 1380 cm−1 also signifies the antisymmetric stretching mode (ʋ3) of the nitrate anion in the LDH intercalated with NO3.Considering LDH-[Ni(EDTA)]-2, the new signals at 1120 cm−1 can be ascribed to the bending vibrations as a consequence of EDTA and Ni2+coordination. The peaks at 1750 and 1629 cm−1 also reflect the stretching vibrations of carbonyl and the Ni-capped carboxylic groups in EDTA, respectively . The new peaks at 1400 cm−1 can be assigned to the stretching vibration of the amine group.
The XRD patterns of Zn2Al-LDH-NO3 (LDH) and the [Ni(EDTA)]-2 intercalated LDH (LDH-[Ni(EDTA)]-2) are presented in Figure 2.
The sharp peaks indicate the highly ordered and regular stacking of the LDH layers. In the case of LDH, the peaks can be well assigned to hexagonal the structure planes of (003), (006), and (009) , with the basal spacing of 0.890 nm for (003). An increment can be detected in the basal distance of LDH-[Ni(EDTA)]-2 (Figure 2(b)) which can be attributed to the complex [Ni(EDTA)]-2 intercalation. A basal spacing shift can be observed from 0.89 nm for LDH to 2.55 nm for LDH-[Ni(EDTA)]-2complex implying the [Ni(EDTA)]-2 intercalation in the galleries.
3.2. Curing Characteristics for the GEP, GELP, and GELNiP
Figure 3 shows the DSC curves of the GEP, GELP, and GELNiP at various heating rates. The conversion can be observed in terms of temperature for GEP, GELP, and GELNiP for various heating rates.
The obtained diagrams can be exploited to calculate the kinetic parameters of the curing process. Due to its aromatic primary amines, curing of epoxy is a highly complex polyaddition procedure which may involve secondary amine addition. At advanced stages or higher temperatures, side reactions (e.g., etherification or homopolymerization) are also probable. The differences in the DSC curves of the epoxy prepregs indicate the profound impact of LDH or LDH-[Ni (EDTA)]-2 on the curing procedure. The LDH altered the onset (), peak (), and end () temperatures toward smaller values implying the accelerating role of LDH incorporation in the GEP curing reaction. This trend can be well described by the catalyst impact of LDH on opening the epoxy rings. Moreover, the variations in the shape of thermograms reveal the involvement of various curing mechanisms and kinetic parameters at the presence of LDH (Figure 4).
In comparison with LDH, the incorporation of LDH-[Ni(EDTA)]2- shifted , , and toward lower temperatures suggesting further acceleration of curing reaction upon the presence of the Ni(EDTA) complex intercalation of LDH. The amine groups and Ni ions in the interlayers of LDH-[Ni (EDTA)]-2 further augmented the catalytic activities of LDH and promoted the primary amine–epoxide reaction.
3.3. Cure Analysis
Curing mechanisms and its kinetics modeling were addressed in this section for the epoxy prepregs containing 0.2 wt. % of LDH or LDH-[Ni (EDTA)]-2.
3.3.1. Calculation of the Kinetic Parameters
According to Figure 5, the curing trends of GEP, GELP, and GELNiP significantly differed. In the case of GEP, the apparent remained constant at ~55 kJ/mol up to and then increases sharply toward the maximum value of 94 kJ/mol at a conversion of 90%. Concerning the GELP, at all degrees of curing, the apparent was substantially lower than that of GEP. The showed a decrement from ~60 kJ/mol at to a minimum of ~40 kJ/mol at followed by a rise to ~58 kJ/mol at . In the case of the GELNiP system and for lower curing degrees (), a rise in the curing degree slightly declined E to ~35 Kj/mol at which then remained almost constant until . Here, was evidently lower than those of GEP and GELP. The variations in in the course of the curing process could be assigned to the following trend: temperature is lower at the early curing stages, and the reactions mainly occur between epoxy and amine groups. By the progression of the curing reaction, and hence at augmented temperatures, other reactions (mainly epoxy etherification, but hydroxyl are also probable) are expected to gain further importance [18, 35, 36]. The odd low activation energy of the nanocomposite at lower curing degrees confirmed the facilitating role of the LDH or LDH-[Ni(EDTA)]-2 incorporation in the curing process, especially the initial epoxy-amine reaction. The first stages of the dependency of GEP are the characteristic of epoxy-amine reactions. At the final stages of the reaction, a decline in values can be assigned to a transition from chemical control of the crosslinkers to the diffusive controls which had become evident in this system at the gelation stage. For GELP and GELNiP, the characteristic decrement of was milder guiding use to this conclusion that its contribution is lower in this case. Side reactions (etherifications/homopolymerizations) are anticipated at higher temperatures; thus, it can be hypothesized that these reactions are significant in the case of GELNiP. Two reasons can justify the smaller activation energy of the LDH-[Ni(EDTA)]-2 incorporated prepregs. First, the improvement in the dispersion of nanosheets in the epoxy matrix through galleries enlargement between LDH sheets due to the [Ni(EDTA)]-2 intercalation of LDH layers. Ni ions in the interlayers of LDH nanosheets can also serve as catalysts and accelerate the reaction between the epoxy resin and curing agent. At the presence of [Ni(EDTA)]-2 in the interlayers of LDH-[Ni(EDTA)]-2 nanosheets, lower energies are required to achieve the epoxy-amine reaction which was proved by a decline in of GELNiP in comparison with GELP. It was proposed that the main curing reaction mechanism is addition of primary amine to the epoxide groups, accompanied with catalytic polymerization reaction of epoxide groups with the complex cation at the lower temperatures. The reactions of metal-containing and complex compounds with epoxy oligomers are examined in several works as mentioned the introduction part. Being ionic compounds, metal salts react with epoxy oligomers through the coordination of the cations with epoxy groups and the formation of a transition complex. The oxirane ring opening is accompanied by the formation of an ionic associate that acts as the initiator of ion polymerization.
The cure of epoxy resin with an amine curing agent occurs through several steps. The primary amines react with an epoxied ring, at the end of epoxy resin chains to form secondary amines at the beginning of curing reaction. With increasing in the viscose system, the reactivity and accessibility to oxirane groups become less and therefore, the crosslinking reaction of epoxy with the hydrogen of secondary amine starts to be more pronounce. Meanwhile, some hydroxyl groups form during the opening reaction between oxirane ring and the primary and secondary amine. These OH groups can also act as a catalyst in promoting the oxirane ring opening reaction at higher temperatures. Moreover, the kinetic of epoxy ring opening can be changed by Ni(II) known as lewis acid catalysis. It is supposed that the hardening of epoxy oligomers with the various chelates of nickel proceeds both at the expense of the reactions of the epoxy and hydroxyl groups with the alkoxy groups included into the compositions of the nickel chelates and due to the reaction of the ligands with the epoxy groups. The curing reaction proceeded through a two-step polymerization mechanism. The formation of 1 : 1 adduct between the epoxy resin and Nickel(II)-EDTA complex (first step) was followed by chain growth polymerization reaction (second step). The complex curing agent dissociates to form active cation species during the first stage of reaction. With increasing in temperature, the complex cation is dissociated completely. The dissociation equilibrium of the complex curing agent dissolved in epoxy resin at high temperatures. It is clear that complex curing agent is not capable of having an interaction with the epoxy groups due to deactivation of the amine groups, steric hindrance, and coordination number restriction. This means that other active species must be created in the reaction media to start the curing reaction. With raising the temperature, the active cationic species are produced owing to dissociation of the complex, that is more Ni–N, donor–acceptor, linkages are broken and more active amine sites will be available. It is interesting to note that active species are able to commence effective interactions with the epoxy groups by the amine addition reactions, and/or catalytic polymerization reaction (due to reduction of the coordination number of nickel to 4). It seems that there is a competition between catalytic polymerization reaction and amine addition reactions at the initial step of the curing reaction. However, the complex cation (II) is dissociated completely at elevated temperatures, and the polymerization is preceded by the amine addition reactions.
(2) FWO Method. Using the FWO method, the activation energy can be calculated from the slope of ln() versus 1/, as depicted in Figure 7.
In this technique, the activation energy is independent of conversion. According to FWO, the values of activation energy were 65.4, 53.7, and 46.2 for the GEP, GELP, and GELNiP, respectively.
Similar to the Friedman model, the activation energy showed a reduction for the GEP system at the initial stages of curing. For epoxy/LDH and epoxy/LDH-[Ni(EDTA)]2-, however, the activation energy remained constant over conversion when the KAS model was employed (Figure 9). The of GELP and GELNiP was less than GEP which might be assigned to the improved reactivity of the system upon LDH and LDH-[Ni (EDTA)]-2 incorporation.
Although the FR-obtained average activation energies (61.24, 48.8, and 35.8 kJ.mol−1 for GEP, GELP, and GELNiP, respectively) were more than those determined by the KAS (56.9, 40.5, and 27.3 kJ mol−1 for GEP, GELP, and GELNiP, respectively), both approaches predicted the same trend of the apparent activation energy. Therefore, both approaches can be implemented.
3.3.2. Determination of the Reaction Model
Determination of the reaction model parameters considering the role of pristine and [Ni(EDTA)]-2 intercalated LDH in the curing mechanism is a prominent step in studies on the cure kinetics. Friedman and Malek methods were implemented to explore the reaction kinetics.
(1) Friedman Method. According to the Friedman method, the curing process of epoxy can be modeled by Eq. (5), assuming the -th order reaction:
The shape of ln [Af(α)] versus ln (1-α) indicates the deviation from the -th order reaction (Figure 10).
For the -th-order cure reaction, a straight line was observed when ln [Af(α)] was plotted against ln (1-α) whose slope is the reaction order (). Based on Figure 10, a maximum can be observed in the conversion between values of 0.1 and 0.5 which is typical for autocatalytic reactions.
(2) Malek Method. The following equations can be employed to determine the kinetic model based on the Malek method:
where π indicates the function of temperature integrals which can be sufficiently approximated with the following expression [(7)]:
In Eq. (8), E0 can be obtained using the FWO method in which the variations in the activation energy remain constant in terms of α. Both and functions were normalized within (0, 1) intervals:
Considering the shape and the maximum values of and , the best kinetic model can be selected. Then, the kinetic parameters such as and can be determined. Figure 11 depicts the changes in and with conversion α. and showed maximum values at and , respectively. Furthermore, can be determined using the DSC peak, as listed in Table 1.
Based on Figure 11 and Table 1, the curing process could be well described by a two-parameter autocatalytic kinetic model of Sesták–Berggren . The average αm, , was employed to determine the kinetic parameters. The general kinetic model can be rearranged in terms of the ratio of reaction order, as mentioned by Málek: where αMav shows the average αM values. The values of αp, αm, and αpinf obtained from DSC analysis based on the Malek model at various heating rates were shown in Table 2. The value of as degree of noncatalytic and as the degree of autocatalytic reactions as well as the preexponential factor () was calculated by plotting against .
The kinetic parameters (, , and ) and the mean of various conversions were applied in the Friedman and Malek methods as tabulated in Table 1.
Based on Table 1, the kinetic parameters (, , and LnA) offered by the Friedman method are properly in line with those of the KAS method. The kinetic parameters showed an increase in the autocatalytic reaction order () upon the incorporation of LDH and LDH-[Ni(EDTA)]2- indicating a shift in the mechanism from noncatalytic to autocatalytic. Furthermore, the use of LDH and LDH-[Ni(EDTA)]2- nanosheets enhanced the collisions between the reaction moieties, thus raising the pre-exponential factor.
3.3.3. Model Validation
The Málek method was validated by comparing the plots of dα/dT vs. for the data of Table 1 and experimental data. The results of the comparison are presented in Figure 12 for GEP, GELP, and GELNiP. Finally, the kinetic parameters were validated by comparing the plots of dα/dT against for the data of Table 1 and experimental values. Figure 12 presents the reliability of the analytical curing rate for neat epoxy, epoxy/LDH, and epoxy/LDH-[Ni (EDTA)]2- according to the Friedman and KAS methods, respectively.
As can be seen, both Friedman and KAS approaches well agreed with the experimental findings with some minor differences at the advanced stages of the curing reaction. At the initial crosslinking stages, the viscosity of the system was low, and the curing process was under the control of the chemical kinetics prior to the gelation. Before gelation and vitrification, the curing rate could be well described by Friedman and KAS techniques. Besides that, some deviation emerged between the empirical and predicted values when the curing reaction continued which can be assigned to the rise of viscosity. After gelation and vitrification, the mobility of curing reactant decreases and the crosslinking reaction becomes diffusion-controlled decreased and the crosslinking reaction was controlled.
The cure kinetics of GEP was evaluated with and without LDH or LDH-[Ni(EDTA)]-2 using nonisothermal DSC. The presence of LDH altered the cure temperature toward lower values and accelerated the GEP curing. The incorporation of LDH-[Ni(EDTA)]-2 played a more pronounced role in accelerating the GEP curing. Activation energies were determined by the differential isoconversional approach of FR and the integral techniques of FWO and KAS. The activation energy showed a declining trend upon the incorporation of LDH or LDH-[Ni(EDTA)]-2 at low curing degrees indicating the stronger influence of LDH on the curing process. LDH facilitated the curing reaction, especially in the initial epoxy/amine reaction. Furthermore, [Ni(EDTA)]-2 complex intercalated LDH manifested superior performance. The activation energy of the neat epoxy prepreg (GEP) exhibited a descending pattern against the conversion of the system. The average activation energy decreased from 58 kJ/mol for GEP to 42 kJ/mol for LDH-containing GELP which was further reduced to 32 kJ/mol upon the use of LDH-[Ni (EDTA)]-2. Such a further decrease in the LDH-[Ni (EDTA)]2--incorporated epoxy prepreg compared to the LDH-containing system can be explained by the contribution of Ni ions in the interlayer of LDH nanosheets to opening the epoxy rings which catalyzed the curing reaction. The autocatalytic model was employed to explain the cure kinetics of the investigated systems. Upon the incorporation of the LDH or LDH-[Ni (EDTA)]-2, the Sesták–Berggren model still managed to describe the cure kinetic of GEP composites, as its results were in line with the empirical data. Additionally, the Sesták–Berggren model was applied to propose the kinetic parameters and the equation of the curing process.
The data used to support the findings of this study are available from the corresponding author upon request.
Conflicts of Interest
The authors declare that they have no conflicts of interest.
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