Research Article | Open Access
Secondary Relaxation inside the Glass
The physical properties of the glass depend on the procedure used to produce the glass. In particular, if the glass is obtained through the variation of external thermodynamic parameters, the specific way in which the parameters are varied (thermodynamic history) has influence on the final properties. In this work, we studied the effect of thermodynamic history on secondary relaxation inside the glassy state on different molecular glass forming, namely, PPGE(poly[(phenyl glycidyl ether)-co-formaldehyde]), 1,18-bis (p methoxyphenyl) cyclohexane (BMPC), poly(propylene glycol)—(PPG400), phenolphthalein-dimethyl-ether(PDE), Poly(vinyl acetate) (PVAc), and poly(bisphenol A-co-epichlorohydrin) glycidyl end-capped (DGEBA). We found secondary relaxation change with thermodynamic history and depends on the value of the activation volume which activation entropy of secondary relaxation inside the glassy state. Also, we found most of the JG secondary relaxation change with thermodynamic history and most of the Non-JG secondary relaxation are not sensitive.
The state of the glass depends on the procedure used to produce the glass. In particular, if the glass is obtained through the variation of any external thermodynamic parameters, the specific way in which the parameter is varied (thermodynamic history) influences the molecular arrangement. For example, different combinations of pressure and temperature variations can be used, or only varying temperature, different cooling rates can be applied to the supercooled liquid. A further consequence is that thermodynamic properties such as enthalpy, volume, and so forth, also depend on the thermodynamic history. In addition, dynamic processes can change with the different molecular arrangement frozen in the glass. For example, they present different values of relaxation time and different intensity when the glass is prepared through different procedures. This phenomenon is well known for the structural relaxation measured just below the glass transition temperature, , after different cooling rates . The secondary relaxation was studied in several glassy systems, a study on GeO2 (HQGeO2) glass, that is, one of the strongest glass systems and showed that the quantitative relationship between activation energy of secondary relaxation () and agrees well with the empirical relation of the Johari-Goldstein relaxation, , also a study on the secondary () relaxation in La55Al25Ni20 metallic glasses showed a relation between activation energy of secondary relaxation glass transition temperature, .
As previously introduced, secondary relaxation processes are the only process active in the deep glassy state. For a long time, secondary processes were believed to reflect only simple and localized motion of the molecule, which should not be influenced by the molecular arrangement. Instead, it was recently evident that some secondary relaxation depend upon the thermodynamic history by which the glass is formed . Many experiments were performed testing the effect of different cooling rates on secondary processes, and usually a dependence on the relaxation strength and maximum frequency of the secondary process are observed both for intermolecular origin Johari-Goldstein (JG) and intramolecular secondary processes (non-JG relaxation), . Secondary relaxation originates from different types of motions: localized fluctuation of the whole molecules, or the rotational fluctuations of the side groups or parts of them. When motion depends on whole molecule it is designated as the Johari-Goldstein (JG) process. In another case, the investigation was performed at high-pressure, using different combinations of pressure and temperature variations. For example, a study about diisobutyl phthalate showed that the characteristic relaxation time changes when measured after different thermodynamic history. Dielectric loss curves of the secondary relaxation of diisobutyl phthalate are reported as measured for the same value of pressure and temperature, but after that, the glass was prepared through different thermodynamic paths. It is readily apparent that the various pathways yield very different frequencies for the maximum in the secondary relaxation process . In this study, we present experimental studies varying pressure and temperature of secondary processes in several glass formers. We present the study of the influence of thermodynamic history on the secondary process of different molecular glass formers, namely PPGE (poly[(phenyl glycidyl ether)-co-formaldehyde]), 1,18-bis (p methoxyphenyl) cyclohexane (BMPC), poly (propylene glycol)—(PPG400), phenolphthalein-dimethyl-ether (PDE), Poly(vinyl acetate) (PVAc), and Poly(Bisphenol A-co-epichlorohydrin) glycidyl end-capped (DGEBA). All of these systems present a complex relaxation scenario, with more than one secondary process. In this research, we focused on the slower secondary process of BMPC (non-JG relaxation), PDE (non-JG relaxation), DGEBA (JG relaxation) and PPGE (JG relaxation), the faster of PPG400 (non-JG relaxation) and the only one observed in and PVAc, whose microscopic origin is not clear. In such a way we have the possibility of studying the effect of thermodynamic history on secondary processes of JG type (PPGE, DGBEA), as well as of intramolecular origin (non-JG relaxation) (PDE, BMPC, PPG400).
2. Experiment and Materials
Poly[(phenyl glycidyl ether)-co-formaldehyde] (PPGE) with average molecular weight, g/mol, K, was purchased from Aldrich. Glassy PPGE shows two secondary processes, the slower being of JG type and the faster probably related to local motion of the epoxy subunits, [6–12]. Phenolphthalein-dimethylether (PDE), with g/mol, was synthesised in the laboratory of professor H. Sillescu and obtained from Professor M. Paluch. The glass transition temperature of PDE at atmospheric pressure is about 298 K, and was observed to vary nearly linearly with pressure with a coefficient of about 0.26 K/MPa (up to 200 MPa) PDE sample. Glassy PDE presents three different relaxation processes: so-called excess wing, and two secondary relaxation processes. The excess wing reflects the JG relaxation, whereas both the secondary processes reflect local motions of parts of the molecule [13–18]. 1,18-bis (pmethoxyphenyl) cyclohexane (BMPC) with average molecular weight, gr/mol, and at ambient pressure around K, was synthesised in the laboratory of professor H. Sillescu and obtained from Professor M. Paluch. Glassy BMPC showed two secondary relaxations whose molecular origin is not clear at all, [17, 18]. Poly(propylene glycol)-(PPG400) with average molecular weight g/mol, was purchased from Fluka. In glassy PPG400, we observe two secondary relaxations, the slower was identified as the true Johari-Goldstein relaxation , whereas the faster is supposed to originate from intramolecular motions. Poly(Bisphenol A-co-epichlorohydrin), glycidyl end-capped (DGEBA) with average molecular weight ~380 g/mol and glass transition temperature K, was purchased from Shell Co. under the trade name of Epon 828. In the glassy state, two secondary processes are present, and the slower one was identified as the JG process [20–22]. Poly(vinyl acetate) (PVAc) with Kg/mol, and K, is purchased from Aldrich. PVAc has interesting structural variations and can be obtained in the atactic, and thus amorphous form, which is crucial for investigations of the glass transition. PVAc has been often chosen to test the current aspects of various theories related with glass transition phenomena. An ample dipole moment makes PVAc a good candidate of dielectric spectroscopy . Dielectric measurements were carried out by a dielectric spectrometer (α-Novocontrol) in the frequency interval 10−2–107 Hz. For measurements at ambient pressure, the sample was placed in a parallel plate cell (diameter 30 mm, gap 0.1 mm) and the temperature control was performed with a precision better than 0.1 K by using a dry nitrogen stream-based system. For measurements at high-pressure, the sample was placed in a parallel plate cell (diameter 20 mm, gap 0.05 mm) that, properly insulated from the external environment, was located inside a pressure chamber. Pressure variations (0.1–600 MPa) were generated by a manual pump and transmitted to the sample through silicon oil. A liquid circulator connected to a jacket, wrapped around the pressure room, allowed the control of temperature (353–233 K) within 0.1 K.
3. Results and Discussion
Representative isothermal dielectric loss spectra of the investigated glass formers in the glassy state are presented in Figure 1. We acquired dielectric spectra by varying pressure from 0.1 MPa up to the maximum value of 600 MPa. For all the systems, we can observe a peak corresponding to the secondary relaxation: in the following this relaxation will be named as β-relaxation with the exception for PPG400 that, in agreement with the literature, will be called γ-relaxation. In the case, of PPGE, DGEBA, and PDE we observe at high frequencies a rise in the signal partly due to the presence of a faster relaxation, which however is never completely visible with our apparatus for high-pressure measurements. In the case of BMPC and PPG400 at low frequencies, the tail of the structural peak is still present in some spectra. The β-relaxation in PPGE, DGEBA, PDE, and PVAc moves to lower frequencies faster than the secondary relaxation in BMPC and PPG400, Figure 1. It is reported that the β-secondary process of PPGE and DGEBA is of the JG type [24, 25], whereas the β-process of PDE and BMPC and the γ-process of PPG400 are non-JG [26, 27]. We analyzed spectra in terms of a Havriliak and Negami (HN) function for the structural process, (1), and a Cole-Cole equation ( at (1)) for the secondary relaxation In the cases of PPGE, PDE, and DGBEA, we added an HN equation for fitting the faster secondary relaxation (γ-relaxation). The shape parameters used in the HN equation for the γ-relaxation in these three systems were obtained from fitting of spectra at very low temperature and ambient pressure where the γ-relaxation can be clearly observed. Moreover, a similar procedure was used for fitting the tail of the structural peak when present in the spectra.
The pressure dependence of secondary relaxation for different materials with different origins is represented in Figure 2. The maximum frequency was calculated by, , where is the parameter from fit with C.C. function.
The logarithm of the frequency of maximum decreases linearly with increasing pressure for all the systems. This dependence can be described by the pressure counterpart of the temperature Arrhenius law, equation (2), [28–30] By the analysis of the pressure dependence of the relaxation frequency, we obtained the values of activation volume , Table 1.
The effect of temperature on secondary relaxation is presented in Figure 3. The analysis of dielectric spectra below was performed using the same procedure as described in the previous paragraph.
The maximum frequency of secondary peak is reported in Figure 4, as a function of temperature for the different systems. We reproduced such behaviour with equations, namely, (3) where is the temperature dependence of the relaxation time, and , and represent, activation enthalpy and entropy of secondary relaxation, the Boltzmann constant, and the Plank constant. We found the activation entropy, , and activation enthalpy, , from Eyring equation (3). The obtained parameters are reported in Table 2.
Usually, both activation energy and enthalpy barriers increase with pressure, whereas activation entropy is almost insensitive or even sometimes decreases. In the case of PDE, activation energy decreases with the increase of pressure that is not clear but it may depend on the thermodynamic history used to prepare the glassy PDE. The behaviour of these parameter evidences the expected trend that the increase of density and the reduction of free volume hinder the motions related to the secondary relaxation, even when this is of intramolecular origin.
For studying the effect of thermodynamic history on secondary relaxations, we investigated glasses produced at the same values of external thermodynamic parameters but obtained through different thermodynamic paths. For each material, we started the experiment from a thermodynamic point (, ), with changing the pressure and temperature along two different paths we got final points (, ), Figure 5. In the first path A, we pressurized the liquid isothermally to the final pressure (at a temperature above at ambient pressure), and then we cooled it down to at constant pressure. In the second path B, we isobarically cooled the system from to , and then we increased pressure isothermally to . Each material with the exception of PPG400 was vitrified by compression along the path A and by cooling along the path B. The estimated values of temperature and pressure at which materials were vitrified, together with the parameters characterizing the different paths for each material are reported in Table 3. The cooling rates at ambient and higher pressures were 0.95 K/min, and the rate of increasing pressure was 10 MPa/min.
Dielectric loss peaks after two different paths are reported for the secondary processes of the six systems in Figure 6. The spectra are vertically shifted to have the same value of permittivity at the maximum. The frequency of maximum of the β-peak of PPGE shows a big change after two different thermodynamic histories as well as that of PDE, PVAc, and DGBEA. Instead, the maximum frequencies of β-relaxation of BMPC and of γ-relaxation of PPG400 are not affected by the preparation of the glass. In all systems where the secondary relaxation is affected by the thermodynamic history, the maximum frequency in glasses prepared along path A is lower than in glasses prepared along path B.
Density variations can affect the secondary relaxation time. This is the case in our systems, since we observed that the relaxation frequency decreases on increasing pressure at fixed temperature, Figure 2. In fact, isothermal compression of a system corresponds to variations of density but not of thermal energy. The extent of the density effect on the secondary dynamics depends on the investigated system. For example, secondary relaxation in PDE and PPGE is more sensitive to pressure (larger values for activation volume) than that in BMPC and PPG400, Table 1. Glasses present different values of thermodynamic parameters, as density and expansivity, depending on their thermodynamic history. Since it is believed that such parameters affect the secondary relaxation dynamics, it is reasonable that also different relaxation frequencies can be observed for the secondary process.
When a system is vitrified along path A, it is first compressed in the liquid state and then in the glassy state, whereas along the path B the system is compressed only in the glassy state, Figure 5. It is known that the compressibility of the liquid is larger than that of the glass. Moreover, compressing is usually more effective than cooling in increasing the density. According to these general considerations, one can expect that glasses prepared along path A are denser than those prepared along path B. Moreover, it is expected that denser systems present slower secondary relaxation, Figure 2. This idea is consistent with the observed results, Figure 6. In fact, in glassy PPGE, DGEBA, PVAc, and PDE prepared along path A, the secondary relaxation is slower than in glasses prepared along path B, and from the pressure dependence of the relaxation frequency, we know that this result can be related to a greater density of the latter sample. The question now is to understand if the density variation is the main factor determining the dependence of the secondary dynamics on thermodynamic history of the glass. Of course, for studying this issue density measurements are necessary, in connection to the dynamic ones. However, a rough estimation can be performed basing only on dynamics. In fact, the pressure dependence of secondary dynamics is determined in relation to its density dependence. If we assume that the expansivity of the four investigated systems is similar, then the different pressure dependences reflect different density dependences. In other words, with this approximation, we can use the value of activation volume as a rough estimation of the density dependence of the secondary relaxation. In Figure 7, we plot the relative variation of the frequency of the maximum loss peak, as calculated after the two paths. We observe that this quantity correlates with the activation volume in our systems: the bigger is the activation volume, the bigger is the effect of thermodynamic history on secondary relaxation. In other words, the larger is the pressure dependence of secondary relaxation frequency, the larger is the effect of thermodynamic history on it.
Figure 8 shows normalized difference between frequencies of maximum of secondary relaxation as a function of activation entropy, , as it was estimated by (3) . PPGE has big value of activation entropy, ( J/mol), and the value of activation entropy for BMPC is small ( J/mol). Activation entropy values for PDE, DGBEA, and PVAc also intermediate between them. In Figure 8, it is observed that the normalized difference between frequencies of maximum of secondary relaxation increases with activation entropy, with the only exception of PPG400, as expected from the general idea that secondary relaxations with a more complex nature behave more similarly to the structural process. The case of PPG400 can be explained by considering the microscopic nature of its faster secondary process (that here considered). It is suggested that its microscopic origin is related to the motion of the hydroxyl end groups, which can interact with each other through the formation of hydrogen bonds [32, 33]. Due to this interaction, the hydroxyl group cannot move independently and for this reason the relaxation appears to be quite complex (high value of ). However, the hydroxyl group is very small and its motion is local not depending on the density of the material (weak pressure dependence). Our results showed that a greater sensitivity to the thermodynamic history is expected for secondary processes of intermolecular origin (JG) (e.g., PPGE and DGBEA) and less sensitivity is founded for non-JG relaxation (for example BMPC and PPG400). But also we can find some non-JG relaxation that they are senstive to the thermodynamic history (similar to the PDE and PVAc).
In this work, we performed several experiments with the aim of characterizing the dependence of the secondary relaxations on the thermodynamic history used to produce the glass. We investigated the effect that the thermodynamic path (pressure and temperature variations) followed in the vitrification procedure has on the characteristic frequency of the secondary relaxation (both for JG and non-JG relaxations), when measured in the glassy state at the same conditions of temperature and pressure. Secondary processes with larger activation volume and activation entropy are more dependent on the thermodynamic history. This result suggests that secondary relaxations reflecting complex motion are more sensitive to the preparation of the glass. The greater sensitivity could be related to variations of the local density of the environment where the process occurs: in fact, the dependence is more evident in those materials where the secondary process has more pressure, that is, density, and sensitivity.
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Copyright © 2011 Soheil Sharifi and Jahanbakhsh Mashaiekhy Asl. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.