Research Article | Open Access
Dongyan Tang, Xiaohong Zhang, Lili Liu, Liangsheng Qiang, "Simultaneous and Gradient IPN of Polyurethane/Vinyl Ester Resin: Morphology and Mechanical Properties", Journal of Nanomaterials, vol. 2009, Article ID 514124, 6 pages, 2009. https://doi.org/10.1155/2009/514124
Simultaneous and Gradient IPN of Polyurethane/Vinyl Ester Resin: Morphology and Mechanical Properties
A series of polyurethane (PU) and vinyl ester resin (VER) simultaneous and gradient interpenetrating polymer networks (represented as s-IPN and g-IPN, resp.) curing at room temperature were prepared by changing the component ratios of PU or VER in s-IPN, time intervals, and component ratio sequences of s-IPN in g-IPN. The microstructures of s-IPN and g-IPN were detected by atomic force microscope (AFM), dynamic mechanical analyzer (DMA), and surface constitution scanning of nitrogen element of energy dispersive X-ray spectrum (EDX), respectively. The mechanical properties of s-IPN and g-IPN were studied by values in strain-stress curves detected by electronic multipurpose tester. The results indicated that the morphology and mechanical properties are both affected by PU/VER component ratios in s-IPN, gradient time intervals, and gradient component ratio sequences. Furthermore, the morphology detection by EDX and mechanical properties study both proved the formation of gradient structures in transition regions of g-IPN.
Interpenetrating polymer networks (IPNs) are a special class of polymer alloys synthesized with two or more distinct crosslinked polymer networks held together by permanent entanglement [1, 2]. They can exhibit much higher mechanical properties than that of the constituent polymers and that of ordinary multicomponent systems [3, 4] due to their interpenetrating structures created between two networks. And gradient IPN (g-IPN) is mixture of crosslinked polymers in which the concentration of one network of IPN changes across the section of a sample, and thus the physical or chemical properties also change across the section of a sample. They can be obtained by changing the concentration of one network of simultaneous IPN (s-IPN) across the section of a sample gradually and continuously. Thus, g-IPN [5, 6] can be regarded as a combination of an infinite number of layers of simultaneous IPN and show much more interpenetrating structures, resulting in different properties from the individual networks and IPN [7–10]. Enormous efforts have been focused, in both academic and industrial laboratories, on the preparation of g-IPN with excellent physical and chemical properties, and, however, reports on its properties of g-IPN are still limited  due to the complexity of preparation for multicomposition system and room temperature curing system of gradient IPN. Moreover, there are few reports on the control, verify, and estimate  of the gradient structures in multicomponent and multiphase IPN systems which exhibit great importance for the design of novel materials with unexpected improvements in mechanical and/or other properties.
In our present papers, a series of polyurethane/vinyl ester resin (PU/VER) simultaneous and gradient IPN curing at room temperature are successfully synthesized by changing the component ratios of PU or VER in IPN and casting the mixture with different component ratios in a mold at various times and by different component ratio sequences. The relationships of morphology of IPN and g-IPN with mechanical properties are studied by the results obtained by strain-stress curves and microstructure observation and detections. The gradient structures formed in system are proved by the results of energy dispersive X-ray spectrum and nitrogen element surface scanning.
2.1. Preparation of Simultaneous IPN and Gradient IPN
A weight amount of trimethylol propane (TMP, as crosslinker of PU) was dissolved in dyhydrated ethyl acetate (EAc) first and then 1,4-butylene glycol (1,4-BD, as chain-extender of PU), epoxy acrylate (supplied by Shanghai Xinhua Resin Plant, the main structure is formed by the chain extention of linear acrylate resin with bisphenol A and chloroepoxy propane and then is crosslinked by aromatic diisocyanate), PU prepolymer (toluene diisocyanate precursor, self prepared by using toluene diisocyanate and polyoxypropylene glyco (PPG, WM: about 3000; the hydroxyl value: about 52.0.), and benzoyl peroxide-N,N’-dimentylaniline (BPO-DMA, as redox initiators of epoxy acrylate) were sequentially added into the above system. After the mixture was thoroughly stirred and degassed under vacuum for 5–10 minutes, a transparent sample was prepared by curing in a mold. A series of simultaneous IPN (s-IPN, represented as , which refers to PU component, to VER component) were synthesized by varying the component ratios of PU and VER in the system. The g-IPN was prepared by casting the mixture of different component ratios in a mold sequentially. A series of g-IPN were obtained by changing the time intervals and component sequences (represented as , each represents each component ratio of s-IPN in g-IPN) during the curing process of s-IPN.
Tensile strength (σ), elongation at break (ε), and elastic modulus () of s-IPN and g-IPN of small size dumb-bells were measured from strain-stress curves by Zwick Roell Z1010 testing machine at 2C with a crosshead speed of 2 mm/min according to GB4456-84. Data were taken as average of at least five measurements. Atomic force microscopy (AFM) imaging was performed on microtomed surfaces with a digital instrument nanoscope III scanning probe microscope with multimode head and J-scanner. The tapping mode was used at ambient conditions. The resonance frequencies of these probes were in the 300 KHz range. Phase images of two dimensions were recorded simultaneously. Dynamic mechanical analyzer (DMA) measurements were made at 100 Hz in the temperature range of 75 15C with a heating rate of 1C/min. Energy dispersive X-ray (EDX) analysis was performed using Oxford ISIS-300 spectrometer coupled to a JEOL JXA-scanning electron microscope on the cross-section of a sample.
3. Results and Discussion
3.1. Mechanical Properties Study
3.1.1. Mechanical Properties of s-IPN with Different Component Ratios
Generally, s-IPN shows better elongation at break and tensile strength than those of ordinary polymers and other types of multicomponent systems due to the mutual entanglement, forced compatibility, and synergism of the networks in s-IPN. In the s-IPN of PU/VER, VER is the hard segment contents. Thus, both the values of elongation at break and tensile strength are proportional to the VER content in s-IPN. Figure 1 shows the strain-stress curves of 70/30 s-IPN. As shown in Figure 1, the s-IPN shows the mechanical properties of PU mostly, because of the higher elastic properties of PU and more component ratios in s-IPN. It is suggested that the thermodynamic miscibility created by the amino group in VER and the isocyanate group in PU lead to approximate compatibility of s-IPN .
3.1.2. Mechanical Properties of g-IPN with Different Component Sequences and Time Intervals
Similar to the effects of VER in s-IPN to mechanical properties, higher modulus of VER in g-IPN also contributes better mechanical properties to g-IPN. Different component ratio of PU and VER results in the different modulus contributions of PU and VER networks in system. The different component sequence of PU to VER networks with different component ratio is another factor to affect mechanical properties of g-IPN. Figure 2 shows the strain-stress curves of g-IPN at different time intervals with different component sequences. Seen from the figure, two g-IPNs show approximate the same values of elongation at break. But more VER contents in s-IPN in each sequence give apparent higher tensile strengths values. Furthermore, the results listed in Table 1 are calculated from the stress-strain curves. The results listed in Table 1 indicate that the gradient techniques can do improve the elastic properties of IPN greatly. The g-IPN in different components sequences with higher content of VER exhibits the higher tensile strength values and lower elongation values. Especially for the g-IPN with components sequences, it shows higher elongation at break values without a dramatic decrease in the tensile strength, demonstrating the formation of gradient structures between different s-IPN. It provides a basis for the design of novel materials with unexpected improvements in elastic properties and appropriate tensile strength.
Figure 3 shows the strain-stress curves of g-IPN with different time intervals. It can be observed that the partially gradient structures in transitional regions between the layers for sample with 3.5-hour intervals can contribute better mechanical properties. The calculation results from the strain-stress curves are listed in Table 2. All g-IPN show higher elongation at break than those of s-IPN, proving the synergistic action of more interpenetrating effects of g-IPN.
3.2. Morphology Study
3.2.1. Morphology of s-IPN with Different Component Ratios
The mechanism of curing reactions for PU and VER is different, and thus the two networks could be formed simultaneously. In most cases of the formation of IPN, to improve the thermodynamic compatibility between two different components, researchers often introduce the graft structures between two networks. In this paper, the amino group in VER can react with the isocyanate group in PU to form the graft-IPN. Figure 4 gives the AFM (phase images of two dimensions) photographs of s-IPN with different component ratios.
The bright phase is the PU phase with lower modulus and the darker phase is the VER phase with higher modulus. As shown in Figure 4, the dispersed VER phase is also linked and the continuous degree increases with the PU component ratios in system. The results of AFM indicate that the phase ranges of PU/VER s-IPN obtained are all in nanometer scales owing to the possible graft structures formed. Similarly, the compatibility of 80/20 s-IPN is better than that of 70/30 and 90/10 s-IPN because of the smaller domain sizes in AFM photos.
The morphology of IPN also can be studied further by DMA detection. From the loss factor () versus temperature curve of DMA, the degree of inward shift of of s-IPN, compared with that of pure PU and pure VER, and the numbers of peaks in of both can indicate the degree of phase mixing in each component . Figure 5 shows the plots of loss factor () versus temperature of various PU/VER component ratios of s-IPN. As shown in the figure, the PU/VER component ratio affects morphology of IPN. The maximum value of shifts toward lower temperatures. These results can be attributed to the fact that PU phase in IPN polymerizes first and forms the continuous phase. The results also indicate that multicomponent system can broaden the effective range and move the range toward higher regions corresponding to higher VER content. All the s-IPNs show one expended peaks with maximum value higher than 0.4 in near 5C temperature ranges. These show better interpenetration and apparent entanglement effects led by better compatibility between two components of s-IPN. Meanwhile, there appear relatively expended ranges in curves. According to the Rouse-Bueche theory, such single broad peaks do not mean homogeneous system formed.
3.2.2. Morphology of g-IPN with Different Components Sequences
Figure 6 shows the plots of loss factor () versus temperature of the g-IPN with different components ratio sequences ( IPN and IPN). Compared with s-IPN, the broad damping plateaus with higher is the result of superposition of a great number of relaxation maxima in the layer and transition regions between layers with progressively varying compositions. The better ranges are higher than 0.4 in near 10C temperature ranges. The morphology study of g-IPN is consistent with the result of mechanical properties detections shown in Figures 2 and 3.
3.2.3. Verifying the Gradient Structures of g-IPN
In the present study, considering that g-IPNs contain nitrogen, and its content contributes by PU network, the detection of the content changing of N element along the samples in system can illustrate the changing of PU in g-IPN. Figure 7 gives the surface line scanning of element N on the cross section of g-IPN with the component ratios of . Figure 8 gives the surface constitution scanning of element N on the cross section of transitional regions of g-IPN. Both the EDX analysis of g-IPN in Figures 7 and 8 verify the gradient structures of g-IPN through the nitrogen element distribution detection in the layer ( m) and in the transition regions between layers ( m). The element N is homogeneously distributed in the layer, while the N distribution in the transition regions varies gradually from one layer to another layer.
A series of simultaneous and gradient IPN with different miscibility and mechanical properties are prepared by varying the component ratios of PU to VER in simultaneous IPN, time intervals, and component ratio sequences in gradient IPN. The elastic properties of IPN can be improved evidently by interpenetrating techniques and gradient structures formed in transitional regions. PU/VER component ratios in s-IPN, time intervals, and component ratio sequences in g-IPN all affect the morphology. The formation of gradient constructions in transition regions of g-IPN can be proved by morphology studies through EDX analysis and mechanical properties detections. The content of nitrogen in g-IPN changes with different trend along the direction of sample. And the morphology observation and detection results are both consistent with the results gained by mechanical detections.
The authors gratefully acknowledge the National Natural Science Foundation of China under Grant no. 50675045, the Program for New Century Excellent Talents in University (NCET-08-0165), and Youth Science and Technology Foundation of Heilongjiang Province, China (QC07C01).
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