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Optical and Physical Properties of SiO2 Nanoparticles and Tetra Ortho Silicate Doped in Polyurethane Foams

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In this article optical and physical property of the composition of polyurethane open cell (PUOC) with two different concentrations of SiO2 nanoparticles (1 and 2wt. %) will be reported. Tetra ortho silicate (TEOS) as an organic agent with different
  [Malekfar ,  3(2): February, 201   http: // (C)  Inte IJESRT   INTERNATIONAL JOU Optical and Physical Pro R. M 1 Department of Physics, Tar In this article optical and phys different concentrations of SiO2 nano organic agent with different concen composition. Optical microscopy ima samples were measured. The cell size SiO2 was recognized as a best speci revealed that PUOC/1wt. % SiO2 and phase separation, DPS, and the hydr spectroscopy data. Two samples, PUO among the synthesized samples. By a increased. This is similar to the behavi the real density of samples were decre samples were calculated. By adding Si Keywords : polyurethane, SiO2, spectr Introduction Polyurethanes (PUs) are kind synthetic materials in industry that are coating, synthesizing and preparing l foams, thermoplastic elastomers and Nowadays, scientists are interested polyurethane with high performance some factors that affects the morpholo as the hard and soft sections of the P and weight of these two components construction of the chains of PU. organic polymers lack important pro stability at low temperatures and we strengths which has led in introdu materials doping for improving properties of organic matrixes. Orgcomposite hybrid materials have both organic polymers and inorganic mat flexibility, ductility, rigidity, high the etc… receiving these properties f inorganic and organic agents [4]. Silica NP is one of the po materials with high specific surface surface energy. It has been shown tha is useful for improving the characterist matrix especially in mechanical–theproperties [3]. In this research we ] I Imp  national Journal of Engineering Sciences & Research [842-846]   NAL OF ENGINEERING SCIENCES & R TECHNOLOGY erties of SiO2 Nanoparticles and Tetra O oped in Polyurethane Foams lekfar 1 , M. Nadafan and Z. Dehghani   iat Modares University, P. O. Box 14115–175, Teh  Abstract   ical property of the composition of polyurethane open c articles (1 and 2wt. %) will be reported. Tetra ortho si rations (0.05, 0.1, 0.15 and 0.2 Vol./Vol.) was ad   ging, watering uptake, FTIR and Raman spectroscopy f samples by adding SiO2 NPs and TEOS was decrease en for absorbing water. By focusing on the recorded PUOC/200 µ l TEOS have more covalent bonds than o gen bonding index, R, in samples were evaluated in  /1wt. % SiO2 and PUOC/800 µ l TEOS, have the highes ding SiO2 NPs and TEOS into PUOC, the apparent d or of real density in SiO2 NPs into PUOC but by addin sed. The total porosity, open porosity and closed porosi 2 NPs and TEOS into PUOC, the open porosity of samp scopy, porosity, density. s of attractive used widely in athers, fibers, so on [1–3]. in producing by changing gy of PU such U matrix, size and chemical Furthermore, erties such as ak mechanical ing inorganic the physical anic–inorganic advantages of rials such as rmal stability, rom both of ous inorganic area and high t silica doping ics of polymer rmal–chemical have tried to evaluate the presence of silica considering and focusing on it The most common silica organi of becoming easily purified an controllable rate of reaction, is T two sources of silica–SiO2 NP ortho silicate (TEOS) with open Furthermore the properties of usi as inorganic or organic source an investigated. Materials and Methods Silicon oxide nanopar type, Spherical particles, 15–20 purchased from US Research (Fig.1). Tetraethyl ortho silicate ( 99%) was used from Merck. diisocyanate (MDI, density=1. polyol (SROC: Semi Ri density=1.1g/cm3) was collected Co., Ltd., Tehran, Iran and deion as blowing agent. Preparation of PUOC/ SiO2 Two different weight p (1 and 2 wt. %) were dissolved i part solution individually. Dis SSN: 2277-9655 ct Factor: 1.852   Technology SEARCH rtho Silicate an, I.R. Iran ll (PUOC) with two licate (TEOS) as an ed to polyurethane of the synthesized . The PUOC/1wt. % aman spectra, it is hers. The degree of erms of their FTIR t R and DPS factors nsity of foams was TEOS into PUOC, y of the synthesized les was increased. in PU matrix with optical properties. precursor, for sake d having slow and EOS. We have used and tetra ethylene cell PUs structure. ng different sources new products were icles (99.5+%, S– m, amorphous) was Nanomaterials, Inc TEOS, C8H20O4Si, Diphenyl methane 3g/cm3), polyether id Open Cell, from Exxon Panah ized water was used ercent of SiO2 NPs nto open cell polyol olving carried out  [Malekfar ,  3(2): February, 2014] ISSN: 2277-9655 Impact Factor: 1.852   http: // (C)  International Journal of Engineering Sciences & Research Technology [842-846]   under vigorous electrical stirring for 20 seconds with 3000 rpm until a homogenous solution was achieved. After that MDI part was added to the solution by doing vortex at 2000rpm for 4–5 seconds. Then for a well prepared sample the cover of the container of PU/SiO2 was taken off. After 10–12 seconds reaction was ended by formation of foams in samples. The ratio of polyol:MDI was 1 (2ml):1(2ml). For the analysis purposes the samples were kept in the stream of the liquid nitrogen gas and then were cut in the slices with 1mm diameter. Figure 1. SEM   image of SiO2 nanoparticle prepared US Research Nanomaterials, Inc. Preparation of PUOC/TEOS Four different amounts of TEOS: 200, 400, 600 and 800 µ l were individually dissolved into 2ml of the open cell polyol. The procedure of preparing samples was the same as for PU/SiO2 samples, mentioned above, hence dissolving of TEOS into polyol part was easier than for SiO2 NPs. Results and Discussion Microscopic Evaluation In order to determine cell size of PU and observing its microstructure optical microscopy is used. For this aim, thin layers of PU nanocomposite and PU/TEOS with thicknesses of about 1mm were cut perpendicular to the rising direction of foam. The freeze–fractured surfaces of the samples were prepared at liquid nitrogen temperature and then examined. Different image of blank PU, PU containing nanocomposites of SiO2 or TEOS with different concentrations were collected. Fig. (2a) to (2e) show the transmitting optical microscopy images for PUOC including TEOS and SiO2 NPs. It can be seen in Fig. 2 that by increasing of SiO2 NPs in pure PUOC the cell sizes in the matrix have been changed, foams containing 1 and 2 wt. % SiO2 have lesser large cell sizes in comparison of their pure PUOC. However the cell networking looks to be destroyed in foams containing 2 wt. % SiO2.The PUOC structures have been changed by increasing of TEOS, figures show that the mean cell size of the foams decreases. By examining the micrographs it reveals that the mean cell sizes of all PUOC composites and PUOC nanocomposite samples can be classified in the following manner: Figure 2.  Microstructures of: (a) blank PUOC, (b) PUOC/1wt. % SiO2 (c) PUOC/2wt. % SiO2, (d) PUOC/200 µ l TEOS, (e) PUOC/400 µ l TEOS, (f) PUOC/600 µ l TEOS and (g) PUOC/800 µ l TEOS. The successive mean cell size of PUOC composite foams are: blank PUOC > PUOC/200 µ l TEOS > PUOC/400 µ l TEOS > PUOC/1wt% SiO2> PUOC/600 µ l TEOS > PUOC/2wt% SiO2> PUOC/800 µ l TEOS. FTIR Spectroscopy Analysis Fourier transform infra–red (FTIR) transmission spectra of the samples as powder–pressed KBr pellets was collected by using a Thermo Nicolet Nexus 670 FTIR spectrometer system with 4cm -1  resolution and in the wave number range from 4000 to 400cm -1  at room temperature.  FTIR Spectroscopy of PUOC/SiO  2   The FTIR skeletal spectra in Fig. 3 of PUOC/SiO2 have some important features related to the presence of SiO2 NPs. The intensity of peaks at 635, 815, and 1103 cm -1  in Fig. 3 referred to Si–C [5], symmetric stretching/bending Si–O–Si bond [6,7] and asymmetric stretching Si–O–Si bond [7] which were increased by adding SiO2 NPs contents up to 2wt. %. These peaks had higher intensity in PUOC/2wt. %SiO2 in compared with PUOC/1wt. % SiO2 that it was concluded as the extra amount of SiO2 in PUOC/2wt. % SiO2 rather than PUOC/1wt. %SiO2. There are some peaks at 1460, 1540 and 3340 cm -1  assigned to the secondary reaction between isocyanate and urethane groups [8] of PUOC, N–H bending [9], and N–H bonds of urethane [10] in PUOC nanocomposite foams that the intensity of them decrease by adding SiO2 NPs up to 1wt. % and then increase up to 2wt. %. The number of cross linking sites in PUOC foam was increased by adding SiO2 NPs into polymer matrix. The fundamental factor for measuring physical properties of PUOC foam is phase separation. Xia and Song [11] can examine the degree of phase separation (DPS) by the Cooper method. There are two peaks at 1708 and 1718 cm -1  which are related to  [Malekfar ,  3(2): February, 2014] ISSN: 2277-9655 Impact Factor: 1.852   http: // (C)  International Journal of Engineering Sciences & Research Technology [842-846]   the bonded carbonyl and free carbonyl groups [2]. The hydrogen bonding index, R, is assigned to the ratio of absorption peak as bondedfree  RAA =  , where A bonded  is the absorbance peak intensity of 1708 cm-1 and A free  is the absorbance peak intensity of 1718 cm -1 . The hydrogen bonding index, R, and DPS increases up to 1wt. % SiO2 contents and begin to decrease up to 2wt. % SiO2 NPs. Figure 3. FTIR spectra of blank PUOC and PUOC/SiO2 nanocomposites. The R index and DPS factor were increased form blank PUOC nanocomposite foams to PUOC/1wt. % SiO2 nanocomposite and then decreased in PUOC/2wt. % SiO2 nanocomposite (Table 1). The data anticipate that silica NPs are probably dispersed in soft segments of PUOC/1wt. % SiO2 but by increasing the amount of SiO2 NPs, they prefer to disperse in hard segments.  FTIR Spectroscopy of PUOC/TEOS Fig. 4 has shown the detailed FTIR spectra of PUOC/TEOS composites. It is clear that all the spectra are similar but there are some differences among them. After adding TEOS to PUOC matrix some absorption peaks are created at 457, 1012, and 1080 cm -1  in all PUOC/TEOS composites. These peaks are related to Si–O–Si bond rocking vibration [12], Si–O–C bonding [5], and asymmetric Si–O–Si stretching mode [7]. In all of them the procedure is similar since by adding SiO2 NPs up to 600 µ l the intensity of these peaks decrease and then start to increase by adding up to 800 µ l to PUOC matrix. So the PUOC/600 µ lTEOS has less covalent bonding compared to others. There are two peaks at 1690 and 1718 cm -1  that are related to the bonded carbonyl and free carbonyl groups, respectively [2]. In this case, the hydrogen bonding index, R, and DPS decrease by adding TEOS contents up to 600 µ l and begin to increase up to 800 µ l TEOS into PUOC foams (Table 1). The results show that in low loading of TEOS in PUOC foams, the produced SiO2 by adding TEOS is set in hard segment. However, in high loading of TEOS it is set in soft segment. The intensity of peaks at 1460, 1535, and 3360 cm -1  are related to the secondary reaction between isocyanate and urethane groups [8], urethane N–H bending [9], and N–H bonds of urethane [10] in PUOC composite foams, respectively, which were decreased by adding TEOS contents up to 600 µ l and started to increase up to 800 µ l TEOS into polymer matrix. Figure 4. FTIR spectra of blank PUOC and PUOC/200 µ l, 400 µ l, 600 µ l, and 800 µ l TEOS. Raman Back-Scattering Analysis  Raman spectra of the samples were collected by using a Thermo Nicolet Almega dispersive micro-Raman spectrometer operating by a 532 nm laser line as the second harmonic of a Nd:YLF laser in a back-scattering configuration.  Raman Spectra of PUOC/SiO  2   The possible interaction between SiO2 NPs and PUOC foams was investigated by analyzing the recorded Raman spectra shown in Fig.5. In these composites by adding SiO2 NPs in PUOC matrix, the C–H wagging [13] bond was appeared in two composites at 870 cm -1  which they were not observed in pure PUOC. This peak was shifted to higher wave numbers by increasing the amount of SiO2 NPs in PUOC matrix. The Raman peak at 646 cm -1  is related to C–C–C bending [13] mode that is just in PUOC/1wt. % SiO2 with a weak intensity. Furthermore the Si–O–Si stretching vibration bond [12] is just existed in PUOC/1wt. % SiO2 at 1040 cm -1 . There is another Raman peak at 487 cm -1  that assigned to the rocking of Si–O–Si bond [14] and by increasing the amount of SiO2 NPs, this Raman peak is shifted to lower wave numbers. All samples have C–C stretching bond [13] at 1595 cm -1  but this bond at PUOC/2wt. % SiO2 has more intensity than pure  [Malekfar ,  3(2): February, 2014] ISSN: 2277-9655 Impact Factor: 1.852   http: // (C)  International Journal of Engineering Sciences & Research Technology [842-846]   PUOC and PUOC/1wt. % SiO2. The C–H bending and C–C stretching bonds [13] in all samples are at about 1500 cm -1 . As the intensity of this peak in PUOC/1wt. % SiO2 is higher than others, it reveals our expectation about the hardness of this composite. The interesting point is that by adding SiO2 in pure PUOC two more modes appear in them which are assigned to C–C bending and C–H bending at 1300cm -1 . These peaks start to shift toward lower wave numbers by adding SiO2 NPs up to 2wt. % in PUOC matrix. Figure 5. Raman spectra of blank PUOC, and PUOC/SiO2 nanocomposites.  Raman Spectra of PUOC/TEOS The detailed Raman spectra of PUOC/TEOS are shown in Fig. 6. The Raman peak at 626 cm -1  is related to existence of TEOS [12] which was observed in all PUOC/TEOS composites. This peak is shifted at 400 µ l TEOS with PUOC towards large wave numbers that it is related to the dispersion state of TEOS in the PUOC matrix. There is a Raman peak at 482 cm -1  that is assigned to rocking of Si–O–Si bond [14]. This peak is just in the 800 µ l and 600 µ l TEOS with PUOC samples, which existed for high concentrations of TEOS rather than in other synthesized composites. Furthermore this peak has shifted to higher wave numbers by increasing the amount of TEOS in PUOC matrix but the intensity of it started to decrease. There is a band which is presented in the 960–980 cm -1  region in all PUOC/TEOS composites and assigned to Si–O stretching vibrations of silanol (Si–OH) groups [14,15]. All peaks that are related to Si show the interaction between TEOS and PUOC that they lead to produce of SiO2 in PUOC matrix confirms our initial expectation. According to C–C stretching and C–H bending modes [13] at 1500 cm -1  among PUOC/TEOS composites it is seen that these peaks have higher intensity in 200 µ l TEOS in comparison with the related Raman spectrum of 800 µ l TEOS sample. These peaks are very weak in two other composites. The C–C–C bending mode [13] has appeared at 670 cm -1  in 200, 400 and 600 µ l TEOS with PUOC which was shifted to lower wave numbers by adding the amount of TEOS and it is reasonable to claim that the sample with 200 µ l TEOS has stronger bonds than the other composites. Figure 6. Raman spectra of blank PUOC, PUOC/200 µ l, 400 µ l, 600 µ l, and 800 µ l TEOS. Water Uptake In order to determine the water uptake and water absorption of the samples, all samples were cut to 10 mm *10 mm dimensions with 1mm thickness. The samples were dried in a vacuum oven for 24 hour and their dry weights were measured as Wd. The wet weight of soaking samples (Wt) was examined in deionised water at room temperature at different immersion times up to 96 hours. Water absorption of the samples was calculated by using the following relation [16]: (%)100(1) td d  WW W W  −= ×  The mean value of three different readings was taken. Fig. 7 shows the water absorption of PUOC /TEOS and SiO2 NPs. The most water uptaking of PUOC samples is related to the samples with 1 wt. % SiO2 NPs into polymer matrix. Water uptake of the samples with SiO2 NPs is higher than pure samples; this is reasonable for the inherent hydrophilic of SiO2 NPs. The best amount of TEOS for absorbing water in PU is 200 µ l TEOS even though 600 µ l TEOS in PUOC is the nearest absorbing water to 200 µ l TEOS. As was seen the best component of PUOC in terms of absorbing water is PUOC/200 µ l TEOS, but the best nanocomposite component in PUOC has lesser concentration of SiO2 NPs in PUOC matrix. Apparent Density And Real Density  [Malekfar ,  3(2): February, 2014] ISSN: 2277-9655 Impact Factor: 1.852   http: // (C)  International Journal of Engineering Sciences & Research Technology [842-846]   For obtaining apparent and real density, three various specimens were cut from different regions of the prepared foams and the average values of the densities were measured. The apparent density (bulk density) is calculated by dividing of the masses by the related volumes which have the dimension of kg/m 3  or gr/cm 3 . A common way to measure the bulk density of a porous material is based on Archimedes’ principle, by hydrostatic balance and immersing of samples in the water. Figure 7. Water absorption of PUOC/SiO2 NP– TEOS. Fig. 8 shows the apparent density of PUOC foams versus the SiO2 NP and TEOS loading segments. In this image with the addition of filler, the apparent density increases at higher loading segments. By increasing sample’s apparent density, the mean cell sizes were reduced. Figure 8. Apparent density of blank PUOC, PUOC/TEOS and PUOC/SiO2 NPs. This can also be understood from the optical microscopy images. However, the apparent density was increased much more, in compared to PUOC sample, by adding SiO2 NPs with 2wt. % concentration. The real density of the samples were measured by immersing them and recording the water displacement (pycnometry) as it introduced the ratio of its mass to the volume enclosed by an envelope of water surrounding the foam [17]. The real density of PUOC foams versus the SiO2 NPs and TEOS loading fractions is seen in Fig. 9. When the mean cell size of the foams increased, the real density of them decreased. It is probably related to the higher mass in the same volume. This result was the same for TEOS added to PUOC foam. Furthermore by adding SiO2 NPs into PUOC foams, the behaviors of the real densities are bit different to each other. In PUOC, by adding SiO2 NPs the real density was decreased (Table 1). One reason would be due to the creation of interconnectivity between cells of PUOC foams. As it can be seen, the real density of PUOC is higher than the apparent density of them. It can be understood that the amount of NPs is an important factor in water absorption and determining of density in the samples. Figure 9. Real density of blank PUOC, PUOC/TEOS and PUOC/ SiO2 NPs. Porosity As it was mentioned during chemical reaction of producing foams, the blowing agent causes the micro vides in the cell strut which plays a major role in determination and construction of porosity. The fraction of the total volume that is not occupied is porosity [18]. Fig. 10 shows the total porosity, open porosity and closed porosity of the PUOC samples versus the TEOS and SiO2 NPs loading fractions. By using the following equation [19], the percentage of the total porosity of the prepared samples was measured.
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