NMR relaxometry is one of the techniques that allow observing changes in the molecular mobility that come from materials’ morphology. T<sub>1</sub>H has been used to monitor food and polymer sciences. However, T
<sub>
2</sub
>H, although being a revealing as T
<sub>
1</sub
>H, is rarely used to analyze changes in thermoplastic systems it is more sensitive to the mobile region. High Impact Polystyrene nanomaterials were prepared through solution casting and were exposed for different times to UV light in the air. The samples, removed after each exposure interval, were characterized by T
<sub>
2</sub
>H, focusing on the changes in the relaxation data. The results for this parameter showed that the changes in the relaxation data come from the competition of chain scission and chain recombination processes, which occurs due to the UV light influence with increased time. The T
<sub>
2</sub
>H data indicated that the clay ratio can influence the chain degradation processes, acting to inhibit or accelerate the aging process [1] [2].
Degradation High Impact Polystyrene Nanocomposites Relaxometry Spin-Spin1. Introduction
Evaluation of the aging process of nanostructured materials by spectroscopic analysis is of great value to understand the chemical changes caused during aging, which influence the chemical and mechanical behavior of these materials [3] - [11] . Some studies of hybrid systems composed by polystyrene (PS) and montmorillonite have been carried out. In one of them, the authors prepared nanomaterials using PS/Cloisite15A by melt processing and monitored the chemical changes caused by exposure to ultraviolet (UV) light (λ > 300 nm) for up to 216 hours by FTIR spectroscopy. They concluded that the clay acts as a catalyst and promotes the degradation of this nanomaterial [12] .
Proton spin-spin relaxation time is not commonly used to probe changes in polymer systems, because in the solid-state the T2H is very short, and it makes hard to get much information with narrow variation between samples. Meantime, few studies have been published using these relaxation measurements to evaluate polymers, especially the degradation process of polymer nanocomposites. Therefore, we decided to measure this relaxation parameter to show how it can give good information about degradation changes.
The proton spin-spin relaxation time was measured to evaluate the changing in the intermolecular interactions and molecular mobility in the materials before and after being submitted to aging. This parameter is very useful to observe changes in the mobile phase, like in rubbers, which in this case can be directly related to the degradation process, whereas the scission of chains improves their molecular mobility and promotes a recombination processes. Both promote changes in the spin-spin relaxation time values. One of the pulse sequences that can be used to measure the spin-spin relaxation time is the Carr-Purcell-Mei- boom-Gill (CPMG) sequence, which allows measuring this parameter for different nuclei (here the hydrogen nucleus). The experiment used to measure of spin-spin relaxation time involves rotation of the proton magnetization from its stationary equilibrium state to a direction perpendicular or transverse to the external magnetic field B0, followed by return to equilibrium, during which the material undergoes two well-differentiated relaxation processes [13] [14] [15] [17] .
Spin-spin (T2H) relaxation time measurements are generally used to identify the heterogeneity of polymer materials containing domains with size of about ~25 to >50 nm, thus, providing information on domain size of polymer systems. This analysis can also permit the identification of the molecular motions, which modulate the intermolecular interactions resulting in changes of the proton relaxation times. In the solid state an increment in the spin-spin relaxation time means that the molecular mobility is reduced, as demonstrated in Figure 1 [11] [12] [13] . This feature makes this technique suitable to analyze the molecular dynamics of polymer systems, especially nanocomposites. An important advantage of relaxometry is that a nondestructive method which enables analyzing the sample in intact forms [17] [18] [19] [20] .
The main objective of this work was to evaluate the influence of clay addition on the degradation process of High Impact Polystyrene/organoclay systems, prepared by solution casting, submitted to aging, through the proton spin-spin relaxation time parameter. The High Impact Polystyrene is a polymer based in polystyrene (PS) with addiction of synthetic rubber, polybutadiene (PB) to improve the impact property and photodegraded process could be promoted a preferred oxidation of PB phase, reduction of molar mass, decrease in mechanical properties such as maximum elongation, tensile strength [22] .
Tendency of T<sub>1</sub>H and T<sub>2</sub>H values as a function of molecular size and increase viscosity (adapted from Reich, H. J, 2017) [<xref ref-type="bibr" rid="scirp.76421-ref21">21</xref>]
The proton spin-spin relaxation time was chosen because as far as we know it has not been used to evaluate nanomaterials, especially in studies around aging processing and thermoplastic polymers. There are several works related to elastomers that evaluate changes of these materials by spin-spin relaxation time, probably due to the sensibility and also because of the materials high molecular mobility [23] [24] .
The spin-spin relaxation time is more sensitive to changes than T1H, and during the aging process the molecular dynamic of chains changes. These changes can be detected by the changes in values relaxation time and also in the domain curve distribution.
2. Materials and Methods2.1. Materials
ViscogelS7, modified with DMBHTA, was acquired from Bentec-Laviosa S.A., and was used as received. High-impact polystyrene in pellet form was received from Innova S.A. It contains 5% polybutadiene by weight and has glass transition temperature of 98˚C. The solvents chloroform and toluene were obtained from TediaBrazil and their quality degree was P.A.
2.2. Nanocomposite Preparation
Polymer solubilization was carried out in a 250-mL Erlenmeyer flask with 50 mL of chloroform and 100 mL of toluene by mechanical stirring for 24 h. The desired amount (1, 2 or 3 wt%) of ViscogelS7 was weighed and dispersed in 50 mL of chloroform by mechanical stirring for 24 h. After obtaining a homogeneous mixture, the clay dispersion was poured into the polymer solution and the obtained dispersion was stirred for a further 24 h. Afterward, the resulting mixture was placed in Petri dishes (150 mm diameter), which were then placed in an oven for 24 h at ~40˚C to remove the solvents and to generate the films. High Impact Polystyrene films were also obtained as described above without adding the ViscogelS7 in order to compare the obtained materials. The samples were named considering the polymer and pair of solvents used (HTC), and the proportion of organoclay used varied from 0 to 3 wt% (HTC0, HTC1, HTC2 and HTC3) [25] .
2.3. Aging Test
The films obtained were cut with length of 1.5 cm, height of 6 cm and variable widths of approximately 0.33 cm. All the films were measured in three points by micrometer tool and the samples were subjected to ultraviolet radiation with wavelength of 340 nm emitted by a xenon lamp in a chamber with air circulation (Q-SUN Xenin Test Chamber), at times from zero to 400 hours, with intervals of 100 hours between each withdrawal, following the procedure described in ASTM G155 (1999).
2.4. NMR Relaxation Measurements
The 1HNMR spin-spin relaxation measurements were performed in a Maran Ultra 23 low-field NMR spectrometer, operating at 23.4 MHz (for protons) and equipped with an 18-mm variable temperature probe, operating at 300 K. Proton spin-spin relaxation time (T2H) was measured by Carr-Purcell-Meiboom-Gill (CPMG) pulse sequence and the values of this parameter were determined [10] . The CPMG was carried out using 100 ms of τ, with 4096 scans and 5 s as recycle delay. The obtained data were processed using the Winfit program and the WinDXP software, both of which come with the equipment.
3. Results and Discussion
The spin-spin relaxation time is a parameter that is sensitive to fast movements, as is spin-lattice relaxation time, but T2H is much shorter than T1H in solids. Generally speaking, a uniform relaxation value means that the sample is homogeneous, while variable values of this parameter are produced by heterogeneous structures.
The spin-spin relaxation data were analyzed focusing on two situations: one related to the increase of clay proportion while maintaining aging time constant (Table 1) and the second one keeping a fixed clay proportion while varying the aging time (Table 2). To analyze the effect of the last parameter, the tendency of spin-spin values was also plotted, as shown in Figure 2 and Figure 3.
Table 1 presents the values of proton spin-spin relaxation time for HTC samples before and after being submitted to the aging process, while Figure 2 shows the tendency of each process.
Before submitting the samples to aging, the spin-spin relaxation time for the hydrogen nucleus did not change, indicating that the samples’ molecular behavior did not change with the clay proportion, as seen in Graphic 1.
Effect of clay ratio on proton spin-spin relaxation time as a function of aging time
SAMPLES
T2H (ms) (±2%)
0h
100h
200h
300h
400h
HTC00
16
55
78
80
81
HTC01
12
28
61
92
80
HTC02
15
56
80
84
80
HTC03
13
93
82
77
94
Effect of aging time on T<sub>2</sub>H of each clay rati
T2H (ms) (±2%)
Aging Time (h)
HTC00
HTC01
HTC02
HTC03
0
16
12
15
13
100
55
28
56
93
200
78
61
80
82
300
80
92
84
77
400
81
80
80
94
Tendency of T<sub>2</sub>H values as a function clay ratio (<xref ref-type="table" rid="table1">Table 1</xref>)
After aging for 100 hours, the pure polymer and sample HTC02 presented the same average T2H value, indicating this clay proportion generated morphology in the polymer matrix that is not affected by aging action in relation to the molecular mobility behavior. However, samples HTC01 and HTC03 presented distinct behaviors, due to the difference in morphology and clay distribution in the matrix, in comparison with HTC02. Sample HTC01less degraded, demonstrating possible protection of the clay from UV radiation, characteristic of exfoliated morphology, while in HTC03 the action of the UV radiation was stronger, causing greater degradation, characteristic of intercalated morphology. That behavior can possibly be explained by refraction of the UV rays by the clay layers, causing them to spread within the matrix, similar to what happens with visible light, causing loss of transparency in systems containing nanoclay.
After exposure for 200 hours in the aging chamber, samples HTC00, HTC02 and HTC03 showed the same average T2H value, indicating that with the addition of the respective clay proportions, the morphology and distribution obtained is not affected by action of UV radiation on the matrix. However, a protective effect characteristic of exfoliated morphology was noted in sample HTC01 for aging time up to 200 h.
After aging for 300 hours, no significant alterations were noted in the molecular mobility of samples HTC00, HTC02 and HTC03. However, the molecular mobility increased in sample HTC01 as indicated by higher T2H value, suggesting that at this proportion the prolonged action of the nanoparticle contributed to break the polymeric chains.
Finally, after accelerated aging for 400 hours, the T2H values of samples HTC00, HTC01 and HTC02 were the same. This behavior demonstrates that with these percentages, the aging effect was more pronounced than the morphology formed by the addition of clay. For sample HTC03, the molecular mobility increased in relation to the other samples.
Table 2 exhibits the effect of the clay ratio in relation to the aging time and Figure 3 shows the tendency of aging time on T2H behavior.
The relaxation time T2H of sample HTC00 increased progressively with aging time. This increase can be explained by the increased molecular mobility of the chains and indicates a probable scission of the chain by the action of the UV light, allowing more freedom for movement of smaller chains.
Sample HTC01 presented different behavior due to the presence of the clay, which protected the polymer matrix from the action of UV light up to 200 hours. After exposure for 300 hours, the system reached maximum molecular mobility, possibly due to changes in the clay distribution, generated by scission
Tendency of spin-spin relaxation time as a function of aging time on T<sub>2</sub>H, as reported in <xref ref-type="table" rid="table2">Table 2</xref>
of the chains of the polymer matrix, which altered the orientation of the clay layers in the matrix. After 400 hours, the molecular mobility decreased due to new interactions between the components of the nanocomposites or recombination of chains.
Sample HTC02 initially presented a progressive increase in molecular mobility, reaching a plateau between 200 and 400 hours, during which the clay did not have a significant influence.
In sample HTC03, an abrupt increase in molecular mobility was observed, demonstrating the photo-degenerative character of the system containing 3% clay in function of its distribution in the matrix. We also observed a random molecular dynamics behavior with increased exposure time, suggesting that the processes of scission and recombination of chains occurred in parallel.
4. Conclusions
The T2H relaxation time measurements provided important information, such as the effect of aging time and clay proportion, to the degradation process of nanostructured materials prepared with High Impact Polystyrene and organoclay through solution casting.
In the nanostructured materials, the results indicated that the clay can act to inhibit or promote the action of the aging process according to the clay concentration and the structure formed with the nanoparticles and polymer matrix. Addition of 1% of clay acted to protect the High Impact Polystyrene system up to 200 hours of aging, after which it acted as a catalyst. The samples containing 2% clay showed the same behavior as the matrix, with slight effect of aging time. Clay at the concentration of 3% acted as a catalyst and revealed the existence of two competitive mechanisms: scission and recombination, from materials exposed from 100 and 400 hours to UV.
Regarding to UV exposure, the T2H values increased with increasing aging time, indicating that the scission process occurs over time. The maximum scission occurred with 300 hours of aging, proved by the changes in the molecular domain.
Finally, the measurement of spin-spin relaxation proved to be an effective way to show the changes in the molecular dynamics also in thermoplastic nano- materials during the aging process.
Acknowledgements
We thank CNPq, CAPES, FAPERJ and PETROBRAS for the financial support of this work.
Cite this paper
Silva, P.S.R.C., Iulianelli, G.C.V. and Tavares, M.I.B. (2017) Spin-Spin Relaxation Time to Evaluate Degradation of HIPS/Organoclaynano Composites by Aging. Materials Sciences and Applications, 8, 342-350. https://doi.org/10.4236/msa.2017.85023
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