The energy shortage problem has gained great importance in recent years. Thermal energy storage is a favorable way to improve efficient energy management and utilization. One of favored methods to store thermal energy is latent heat storage, because of its high storage density and small temperature variation from storage to retrieval (1). Phase change materials (PCMs) can absorb and release large capacity of latent energy during the phase change process when the ambient temperature is changed within a certain range (2). Thence, PCMs have a wide application prospect in the field of energy conservation, such as energy efficient buildings, solar energy storage, and thermo-regulated fibers (3, 4, 5, 6, 7, 8, 9, 10).
The most widely applied organic solid-liquid PCMs are paraffin, polyether, polyester, and fatty acids. A container was used to prevent leakage of melted PCMs; however, it could result in extra thermal resistance and cost (11). Microencapsulated phase change materials (MicroPCMs), which are tiny particles with core materials of PCMs surrounded with organic or inorganic materials, are used for many applications. Straight-chain paraffin and fatty acids are widely used as core materials due to their different phase-transition temperatures, and the most often used shell materials are polymers. Microcapsules and nanocapsules were prepared by in situ polymerization, in which n-alkanes (n-octadecane, n-nonadecane, and n-eicosane) were used as core materials with melamine-formaldehyde, poly(vinyl alcohol), urea-melamine-formaldehyde and polyurethane as shells (12, 13, 14, 15, 16, 17). Also, poly(methyl methacrylate) (18), expanded perlite composite (19), silica fume composite (20) and cellulose acetate (21) were selected as shell materials for thermal energy storage. Furthermore, polyaniline/phase-change nanocapsule composite, which is infrared sensitive, was synthesized by in situ polymerization (22).
However, there is still a little information available for electric conductive MicroPCMs. In recent years, conductive polymer composites have become a new hot spot in the study of conductive composite materials. Not only can composite materials with conductive properties be prepared, but also some new properties such as light, magnetism, antistatic and anticorrosion can be imparted, so this will expand application of
MicroPCMs. The composite material prepared by in-situ polymerization method can make the conductive layer and the matrix better composite, and obtain a conductive composite material with regular morphology and stable performance.
In the present work, we fabricated and investigated the properties of a core-shell microcapsule of PPy/n-octadecane via in situ chemical oxidative polymerization of pyrrole. PPy has high thermal stability and electrochromic (23). Yang et al. prepared carbon/polycarbazole nanocomposite black powder by in-situ polymerization at 0°C with ammonium persulfate as oxidant (24). Chao et al. used in-situ polymerization method with APS as the initiator and poly(2-hydroxy-3-(methacryloyloxy) propane-1-sulfonate) as surfactant and dopant on the surface of CB nanoparticles. The CB/PPy nanocomposite had a core-shell structure and the thickness of polypyrrole layer was from 30 to 100 nm (25). However, there are few studies on the preparation of conductive polypyrrole phase change composites with core-shell structure by in-situ polymerization. So we expect the PCM microcapsules coated with PPy can exhibit electrical conductivity and phase change properties, which will be possible to widen the application of PCMs in camouflage technology and electronic cooling. The results show that PPy/MicroPCMs have higher latent heat and the conductivity of the PPy/MicroPCMs increases from 0.1 S‧cm–1 to 0.33 S‧cm–1 as the PPy concentration increases from 3 to 10 wt% and it reached the design goals.
Pyrrole (Py) monomer (98 wt%, Sigma-Aldrich) was used after vacuum distillation. N-octadecane (purity 99 wt%, Union Lab Supplies, Hong Kong) was used as core material. Melamine (98 wt%, Tianjin Resins Material Factory) and formaldehyde (37 wt% aqueous, A.R., Tianjin Chem. Co.) were used as monomers. Anionic surfactant, SMA (sodium salt of styrenemaleic anhydride copolymer, 19 wt% aqueous solution, Shanghai Leather Chemical Works) was employed as an emulsifier. Acetic acid (36 wt%), triethanolamine (95 wt%), and sodium hydroxide (A.R.), as pH regulators, were from Tianjin Chemical Reagents. CuCl2·2H2O (99 wt%, Guangfu Fine Chemical Research Institute, Tianjin) was used as oxidant.
2.2.1 Fabrication of MicroPCMs
In 150 mL of distilled water, five and one fifth gram of SMA was dispersed, and heated to 60°C. N-octadecane was added to the micelles, the mixture was emulsified mechanically by the homomixer at a stirring rate of 3200 rpm for 30 min. The prepolymer was synthesized in a round bottomed flask equipped with a mechanical stirrer. Afterward, 13 mL formaldehyde, 7 g melamine, and 7 mL distilled water were added to the flask. The pH was adjusted to approximately 8-9 with triethanolamine. Then, 3 mL pyrrole was added into the mixture under vigorous stirring at 70°C in a nitrogen atmosphere until the mixture became transparent. After the pH of the emulsion was regulated to about 4-5, prepolymers were dropped at the rate of nearly 1 mL/min to the emulsion under vigorous stirring at 60°C for 2.5 h. After the reaction completed, MicroPCMs were obtained.
2.2.2 Fabrication of PPy/MicroPCMs
The composite of PPy/MicroPCMs was prepared by oxidative polymerization. A mixture of Py and CuCl2 was prepared. First, 3 mL pyrrole was added into the prepolymer. The molar ratio of Py/CuCl2 was 1:1 (26). Then, an aqueous solution (50 mL) of CuCl2·2H2O was added dropwise to the mixture. The mixture was mechanical stirring for 6 h under 60°C and the rotating speed should be 300 r/min. Then, the precipitates were filtered and washed with deionized water and ethanol. And were vacuum dried at 40°C for 24 h.
A drop of the colloidal solution was extracted and spread on a cover glass. The surface morphologies of vacuum dried MicroPCMs at 40°C for 24 h were examined using a field emission scanning electron microscope (FESEM, S-4800, Hitachi Co., Japan).
FTIR spectra of n-octadecane, composite shells and MicroPCMs were determined using a Fourier transformed infrared spectroscopy (FTIR, TENSOR37, Bruker Co., Germany) at room temperature.
Thermal properties were measured using differential scanning calorimetry (DSC, PERKIN-ELMER DSC-7) in the range of 0-80°C at a heating or cooling rate of 10°C/min in a nitrogen atmosphere. The content of n-octadecane was calculated (Eq. 1):(1)
where, η – the mass percentage of the PCM in the composites; ΔHMEPCM – the melting latent heat of the composites, and ΔHPCM – the melting latent heat of the n-octadecane as measured by the DSC.
Thermal stability of MicroPCMs and n-octadecane was examined by thermo gravimetric analysis (TGA, 409 PC/PG, Netzsch Co., Germany) in the range of 25-800°C at a heating rate of 10°C/min, in a nitrogen atmosphere.
The conductivity of MicroPCMs at room temperature was measured by a standard four-probe (Four-probe Technology Co., Guangzhou) method on pressed pellets of composites under 20 MPa.
3 Results and discussion
3.1 Morphology and structure
Figure 1 shows the SEM micrographs of PPy/MicroPCMs. It can be seen that most composites are spherical and have a rough surface. PPy is located on the shell of the PPy/MicroPCMs. The diameter of the PPy/MicroPCMs is approximately 20-30 μm. In addition, when the content of polypyrrole is 3 wt% (s-2), the surface of microcapsules cannot form a continuous distribution. When the content of polypyrrole is 10 wt% (s-5), the content of polypyrrole on the surface of microcapsules is high, and the surface aggregation is high. It is smooth.
As shown in Figure 2, the inner surface of PPy/MicroPCMs is extremely smooth. When the content of pyrrole monomer is 5 wt% (s-3), the outer surface of the polypyrrole composite microcapsules prepared is compact, smooth and uniform in thickness.
As shown in Figure 3, when the reaction temperature is 40°C, it is hard to prepare the composite into a sphere, and there are many flaky impurities (s-6). When the reaction temperature is 50°C, the microspheres surface is smooth, the polypyrrole is less attached, and a large amount of smooth flaky material exists. When the reaction temperature is 60°C (s-3) and 70°C (s-8), a core-shell composite with polypyrrole on the surface can be formed, but the composite at 70°C is not a regular spherical shape and the surface layer is aggregated. The thickness of the pyrrole is not uniform.
It can be seen from the above analysis that when the reaction temperature is 60°C and the content of pyrrole monomer is 5 wt% (s-3) and 7 wt% (s-4), the prepared polypyrrole microcapsules are spherical in shape and the thickness of the surface polypyrrole is uniform.
The diameter of the PPy/MicroPCMs is approximately 20-30 μm. The inner surface of PPy/MicroPCMs is extremely smooth. (s-3) PPy/MicroPCMs tend to be dispersed without agglomeration. However, PPy does not fully coat the melamine resin layer and part of the Py monomer self-polymerized.
3.2 Thermal properties
The FT-IR spectra of n-octadecane, PPy, MicroPCMs, PPy/MicroPCMs are shown in Figure 4. The main characteristic absorption peaks of n-octadecane at 2857 cm–1, 2923 cm–1 and 2853 cm–1 are due to the aliphatic C–H stretching vibration. The peaks corresponding to C–H stretching vibration of composite shells are overlapped with n-octadecane in each spectrum of MicroPCMs (Figures 4b and 4c) The peaks at around 1470 cm–1, 1356 cm–1 and 720 cm–1 are assigned to the C–H bending vibration, which can be observed in the spectra of n-octadecane, MicroPCMs and PPy/MicroPCMs, and are the characteristic bands for n-octadecane (15). As shown in Figure 4d, the absorption peak at 3400 cm–1 is related to the N–H stretching vibration of pyrrole rings; and 1633 cm–1 is assigned to the stretching vibration of the conjugated C=C double bond of pyrrole rings; and 1400 cm–1 is attributed to the C–N stretching vibration, while 620 cm–1 is assigned to N–H out of plane vibration. The spectra of the PPy/MicroPCMs include all the characteristic peaks of PPy and n-octadecane; and the spectra of the MicroPCMs do not include the characteristic peaks of PPy. The characteristic peaks of PPy and n-octadecane are stronger than those of the MicroPCMs.
DSC heating and cooling curves of n-octadecane, MicroPCMs and PPy/MicroPCMs are shown in Figure 5. The data are listed in Table 2. It is obviously seen that the temperatures of MicroPCMs and PPy/MicroPCMs are very close to those of the n-octadecane. The melting and crystallizing peak temperature of PPy/MicroPCMs is 24.6°C and 17.9°C, respectively. The encapsulation ratio can be calculated with Eq. 1. The encapsulation ratio of MicroPCMs and PPy/MicroPCMs is 40.1% and 40.4%, respectively. The encapsulation ratio of MicroPCMs is higher than that of PPy/MicroPCMs, and could be attributed to two points: (1) the PPy has good thermal conductivity; (2) due to the fact that not entire n-octadecane is encapsulated in MicroPCMs, the pores which are formed in the polymerization process of the pyrrole monomer provide many places for some free n-octadecane.
Figure 6 shows the TGA curves of n-octadecane, MicroPCMs, PPy/MicroPCMs and PPy. The mass of all composites decreases with increasing temperature. The n-octadecane starts to lose mass at nearly 160°C and decomposes completely at approximately 200°C. The melamine resin shell protects n-octadecane from losing mass quickly, and the leakage of n-octadecane finishes at about 250°C. The temperature range of 250-430°C is caused by the further decomposition of melamine resin. The improvement of thermal stability of PPy/MicroPCMs is obviously seen in Figure 4b The first mass loss is due to n-octadecane leaking out of the shell materials, while the second mass loss starts at about 250°C. This could result from the decomposition of the degradation of melamine resin. The third mass loss starts at about 418°C, mainly due to the PPy chains. Owing to the PPy content in PPy/MicroPCMs, the mass loss rate of MicroPCMs is higher than that of PPy/MicroPCMs. This indicates that PPy improves the thermal stability of the composites due to the higher thermal stability of the PPy itself, and the synergistic effect between the PPy and melamine resin.
3.3 Electrical conductivity of PPy/MicroPCMs
Effects of PPy contents in fabrication of PPy/MicroPCMs on conductivity are shown in Figure 7. The room conductivity of PPy/MicroPCMs is significantly affected by the contents or thickness of the shell layer. The conductivity of the composites increases from 0.1 S‧cm–1 to 0.33 S‧cm–1 as the PPy concentration increases from 3 to 10 wt%. In contrast, the electrical conductivity of PPy is 0.5 S‧cm–1. Obviously, the conductivity of these composites is lower than that of pure PPy, since the thickness of PPy on MicroPCMs is thinner.
Microencapsulated phase change materials were fabricated using n-octadecane as PCM, and melamine-formaldehyde as shell, via the in situ polymerization technique. The microcapsules were coated with polypyrrole to fabricate conductive microcapsules. The fabricated microcapsules have a homogeneous spherical profile and core/shell structure. The melting and freezing latent heats of the composites are 90.2 and 92.0 J/g, respectively, while the mass percentage of the n-octadecane in the composites is 49.7%. The thermal stability of heat-treated PPy/MicroPCMs was enhanced. The PPy/MicroPCMs exhibit a fairly high electrical conductivity of about 0.33 S‧cm–1 by adjusting the content of PPy. The electrical conductivity and phase change properties of PPy/MicroPCMs may be used in the field of camouflage technology and electronic cooling. The phase change material microcapsules can be used in the textile field to prepare fibers and fabrics with the functions of antistatic, heat storage and temperature regulation.
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About the article
Published Online: 2019-10-04
Citation Information: e-Polymers, Volume 19, Issue 1, Pages 519–526, ISSN (Online) 1618-7229, ISSN (Print) 2197-4586, DOI: https://doi.org/10.1515/epoly-2019-0055.
© 2019 Yun et al., published by De Gruyter. This work is licensed under the Creative Commons Attribution 4.0 Public License. BY 4.0