Abstract
The changes in the crystalline structure and molecular mobility in the semi-crystalline vinylidene fluoride (VDF) and trifluoroethylene (TrFE) copolymer P(VDF75/TrFE25) caused by the ferroelectric→paraelectric phase transition were analyzed using variable temperature solid-state 19F magic angle spinning (MAS) and 1H→19F cross polarization/MAS nuclear magnetic resonance spectroscopy in the temperature range of 42–129 °C. The conformational exchange between trans and gauche at the VDF and VDF–TrFE head-to-head linkage gradually increases at temperatures above 77 °C, and the conformational exchange at the head-to-tail linkage has a key role in the ferroelectric→paraelectric phase transition. The anomalous decrease in the amorphous peak intensities and the presence of a T1ρF value similar to that of the crystalline domain at 122 °C indicate that cooperative motion occurs in both phases just above the transition temperature (Tc). The amorphous domain is assimilated by the crystalline domain upon lowering the temperature from 129 to 85 °C, which significantly increases the crystallinity to below Tc, as indicated by the shape of the spectra, and identical T1ρF and T1F values for the two domains at 85 °C.
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Introduction
Vinylidene fluoride (VDF)–trifluoroethylene (TrFE) copolymer (P(VDFx/TrFE1−x)), where x is the VDF molar fraction, is a typical ferroelectric polymer that shows a ferroelectric→paraelectric phase transition, which has garnered much interest in the effort to clarify its mechanism.1, 2 Two types of ferroelectric phases have been reported at room temperature, that is, the low-temperature (LT) and the cooled phase, depending on the VDF content and preparation conditions of the copolymer.2 In the LT phase, the CF2 dipoles are arranged in parallel because of the planar zigzag formed by the all-trans polymer chains, which is the same arrangement as the PVDF form I (β-form), whereas in the cooled phase, long trans segments are connected by irregular trans–gauche linkages along their chain axis to form a type of super lattice. However, the stable crystal structure in the high-temperature (paraelectric) phase is hexagonal and is composed of statistically mixed chains with TG+, TG–, T3G+ and T3G– conformations. These chains rotate about their axes via the one-dimensional diffusion of the conformational defects along the chain.
Several reports have shown that lamellar crystals grow in P(VDF/TrFE) films at VDF contents of x=0.60 to 0.82 when annealed at temperatures above the Curie point (Tc). In particular, annealing such polymers at elevated temperatures in the paraelectric phase increases the integrated X-ray diffraction intensities of the 110 and 200 reflections, which correspond to the all-trans chains, and sharpen the differential scanning calorimetry (DSC) endotherms observed at Tc.3, 4, 5, 6, 7 The efficient growth of lamellar crystals in the paraelectric phase has been explained using a sliding diffusion model for the polymer chains. For instance, a polyethylene lamellar crystal can thicken at higher pressures through the sliding diffusion of chains within the lamellae in the hexagonal phase. Thick lamellar crystals of polyethylene can only be grown in the hexagonal phase.8
In a previous article,9 we reported changes in the conformation and molecular mobility of single-crystalline (SC) films of P(VDF75/TrFE25),10 observed during the phase transition using solid-state 19F magic angle spinning (MAS) and 1H→19F cross polarization (CP)/MAS nuclear magnetic resonance (NMR) spectroscopy. On the basis of the shape of the spectra and the relaxation parameters of the observed crystalline signals in the 19F NMR spectra, it was determined that the conformation of the VDF–TrFE head-to-tail (H–T) linkage is unchanged up to 92 °C, whereas the VDF chain sequence and VDF–TrFE head-to-head (H–H) linkage undergo conformational exchange above 77 °C, the beginning temperature of the phase transition. This reveals that the VDF–TrFE H–T sequence is the most resistant component in polymer chains to the trans-gauche conformational exchange below the phase-transition temperature (Curie temperature, Tc). However, the broad signals attributable to the ferroelectric immobile phase disappeared at approximately the Tc, and all chain sequences that included TrFE units underwent significant conformational exchange. In addition, the T1ρF values for all the peaks decreased to a single value (ca. 20 ms) at 119 °C, which indicates a uniform, nematic liquid-crystal-like molecular motion accompanied by a full chain rotation occurred at this temperature. The significantly larger T1ρF values observed for peaks (ca. 20 ms) in the paraelectric phase (119 °C) than those in the amorphous domain (<4 ms) at ambient temperature supports the conclusion that the rotational motion of the polymer chains around their axis is restricted in the paraelectric phase. In this study, we focus on the changes to the molecular motion in the amorphous domain and on the fusion of the crystalline and amorphous domains accompanied by the ferroelectric→paraelectric phase transition in particular. Solid-state NMR enables us to selectively observe either the amorphous or crystalline domains by applying the appropriate pulse sequences.11, 12, 13 Using these techniques, we used variable temperature (VT) 19F MAS NMR measurements to analyze the heating and cooling processes for a semi-crystalline P(VDF75/TrFE25) system containing a significant amorphous domain.
Experimental procedures
Samples and DSC measurements
P(VDF75/TrFE25), and an as-received commercial film (AR film) were supplied by Daikin Kogyo Co. Ltd (Osaka, Japan), dried in vacuo at 100 °C and used without further treatment.
DSC experiments were performed using a SEIKO SSS5000 DSC220 instrument (SEIKO, Tokyo, Japan) over the range from 30 to 140 °C at a heating/cooling rate of 5 °C min−1. The phase transition temperatures (Tc) of the AR film were determined to be 129 °C and 78 °C upon heating and cooling, respectively. The melting temperature (Tm) was determined as 150 °C by another DSC measurement at a heating rate of 10 °C min−1.
Nuclear magnetic resonance
Solid-state NMR experiments were conducted on a JEOL EX spectrometer (JEOL, Tokyo, Japan) operating at the resonance frequencies of 282.65 MHz for fluorine and 300.40 MHz for protons using a Chemagnetics APEX 19F/1H dual-tune probe (Fort Collins, CO, USA). Samples were spun at the magic angle at a rate of ωr=16 kHz. The fluorine and proton r.f. fields were adjusted to fulfill the Hartmann–Hahn sideband-matching condition, ω1H=ω1F–ωr=83 kHz. The temperature inside the rotor was calibrated using ethylene glycol absorbed onto tetrakis(trimethylsilyl)silane at the same spinning rate (16 kHz).14 The ambient probe temperature was estimated to be 68 °C at this spinning rate. The temperature was varied from 42 to 119 °C during the VT measurements. All NMR experiments were conducted under thermal equilibrium conditions at each temperature (signal acquisition began 15 min after setting the temperature). Fluorine chemical shifts are quoted relative to the signal for CFCl3 and were measured via replacement with a liquid sample of C6F6 (–163.6 p.p.m.) using an 83 kHz proton decoupling field to correct for the Bloch–Siegert effect.15 The samples were packed at the center of the rotor with 2.5-mm thickness along the axis to ensure the homogeneity of the r.f. fields and sample temperature. The number of acquisitions was 32 for all experiments, except the delayed CP experiments.
Figure 1 shows the NMR pulse sequences used in this study. The spin-lattice relaxation times in the rotating 19F (T1ρF) frame were measured via variable spin-lock time experiments. The relevant pulse sequence is depicted in Figure 1a. The spin-lock times (tSL) varied from 0.01 to 20 ms. The delayed CP sequence was used to selectively observe signals with long spin–spin relaxation times, T2, which generally corresponded to the mobile (amorphous) phase. The pulse sequence is shown in Figure 1b. The contact time (tCP) and delay time (τ) were set to 0.2 ms and 0.5 ms, respectively. The additional spin-lock period was used to measure the T1ρF of the mobile phase. However, the T1ρF measurement for the rigid (crystalline) phase was performed using a short CP followed by a spin-lock period, as shown in Figure 1c. This short contact time (tCP=0.1 ms) was used to eliminate the signals from the amorphous phase.
Results and discussion
Selective observation of the amorphous and crystalline domains
Figure 2a (top) shows the direct polarization (DP) 19F MAS NMR spectra (tSL=0 ms) with broadband 1H decoupling for an AR film at 42 °C. The high-frequency (from –88 to –130 p.p.m.) and low-frequency (from –195 to –210 p.p.m.) signals correspond to the 19F nuclei in the CF2 and CHF groups of the P(VDF75/TrFE25), respectively. This spectrum is significantly different from that of the crystal-like (SC) film,9 which has broad components that are predominant in both the high- and low-frequency regions. On the basis of the 19F solution spectra reported by Mabboux and Greason,16 the three peaks at –88.4 (peak 1am, CF2–CH2–CF2–CH2–CF2), –102.2 (peak 3am, CF2–CH2–CF2–CHF–CF2) and –109.2 p.p.m. (peak 4am, CF2–CH2–CF2–CF2–CH2) were assigned to the CF2 groups in the VDF region. The subscript ‘am’ for the peak numbers indicates a signal from the amorphous region. Peak 5am at –119.5 p.p.m. (CF2–CHF–CF2–CHF–CF2) and peak 6am at –127.0 p.p.m. (CH2–CF2–CF2–CHF–CH2) were assigned to the CF2 adjacent to a CHF. Peak 7am at –195.8 p.p.m. was assigned to the –CF2–CH2–CF2–CH2–(CHF–CF2)–CF2–CH2–CF2–CH2– sequences, where the VDF and TrFE units are linked H–H. The other marked CHF peak, observed at –203.7 p.p.m. (peak 8am), was assigned to the –CF2–CH2–CF2–CH2–(CF2–CHF)–CF2–CH2–CF2–CH2– sequences, where VDF and TrFE units are linked H–T. Figure 2a (bottom) shows the crystalline selective spectrum obtained using the spin-lock pulse sequence (tSL=20 ms, Figure 1a). Peaks 2LT and 8LT were assigned to the VDF chain sequence and the H–T linkage in the all-trans crystalline domain, respectively.9 The subscript ‘LT’ for the peak numbers indicates signals from the LT phase in the crystalline domain. The effective suppression of the sharp amorphous signals indicates that the molecular mobility of the amorphous domain is significantly different from that of the crystalline domain. This situation is similar to the PVDF homopolymer.12 In addition, the amorphous selective spectra obtained using the delayed CP pulse sequence, both with and without spin-locking (tSL=0 and 5 ms), are shown in Figure 2b. The intensities of the broad crystalline signals in Figure 2a (top; i.e., 2LT and 8LT) were significantly reduced in Figure 2b. The 19F magnetization decay for peaks 1am, 7am and 8am observed by delayed CP followed by variable 19F spin-lock experiments are shown in Figure 3. The T1ρF values obtained by fitting the decays using either a single- or double-exponential function were incorporated into the figure. As peak 1am overlapped the remnant of the crystalline signals, two relaxing components were observed with the longer component containing the spin diffusion from the crystalline to the amorphous domains. As shown in Figure 2b, peak 1am almost entirely disappeared after spin-locking for 5 ms, whereas the two CHF resonances (peak 7am and 8am) were still observed. This was expected based on the longer T1ρF components of the latter signals (4.7 and 5.0 ms) relative to the former signal (2.0 ms). These results suggest that the molecular mobility was larger at the VDF sequence near the spin-lock frequency (100 kHz) than the CHF units. Furukawa et al.17 reported that the frequency dependence of the relative permittivity (real part, ɛ′, and imaginary part, ɛ″) for P(VDF65/TrFE35) showed a wide distribution during heating from 103 to 108 Hz with a maximum of approximately 106 Hz at 40 °C. Ishii et al.18, 19, 20 examined the temperature dependence of the line width, second moment and T1H of P(VDF-TrFE) at VDF contents from 52 to 72% using wide-line proton NMR, and they found a T1H relaxation process at approximately 30 to 80 °C, which would likely be caused by the motion of the chain backbone in the partially crystalline region. They also suggested that the molecular mobility of the VDF component was different from that of the TrFE component, which may undergo a 180° flip-flop motion. As describe below, peak 7 exhibited a shorter T1F component than peak 1, which was presumably caused by the rapid motion of the TrFE units. Although it is not easy to infer the dynamics of the local TrFE unit from these 19F NMR measurements, the short relaxation of T1F may correspond to this flip-flop motion.
The decays of the 19F magnetization for the 2LT and 8LT peaks measured using a short CP followed by a variable spin-lock time experiment at 42 °C are also shown in Figure 3. A short contact time (0.1 ms) was used to reduce the influence of the amorphous domain on the decay of the crystalline signals. However, two T1ρF components were observed for both peaks (2LT and 8LT), and the shorter components were attributable to the amorphous resonances caused by spectral overlap, that is, to spectral spin diffusion. The T1ρF values for the crystalline domain were approximately 10 times larger than those of the amorphous domain as shown by the DP spectrum using a long spin lock (Figure 2a (bottom)). We discuss the temperature dependence of the T1ρF values in both the amorphous and crystalline domains in the following sections to clarify the changes to the molecular mobility within each domain.
VT measurements
Heating process. Figure 4 shows the VT DP 19F MAS NMR spectra of an AR film upon heating. The heights of peaks 1am, 7am and 8am increase continuously over the temperatures from 42 to 114 °C, whereas their half-widths decrease, which confirms the molecular motion in the amorphous domain gradually becomes more vigorous. At 100 °C, a new peak, 7HT, appeared at a higher frequency, separated from peak 7am. This peak was assigned to the H–H linkage in the paraelectric crystalline domain, because its chemical shift agreed well with that observed for the paraelectric phase in the P(VDF75/TrFE25) SC film from our previous study.9 However, peak 8HT, assignable to the H–T linkage, appeared at –201.8 p.p.m. and 114 °C. These phenomena are explicable by the initiation of the trans-gauche conformational exchange in the crystalline domain, as previously observed for the SC film.9 The conformational changes to the VDF chain sequence in the crystalline domain can be recognized in the CP/MAS spectra. Figure 5 shows the VT 1H→19F CP/MAS NMR spectra with a short contact time (0.1 ms) with the AR film upon heating. It should be noted that the small, sharp signals for the amorphous domain (peaks 1am, 7am and 8am) were also observed at the same peak positions in the DP spectrum at 42 °C. Above 77 °C, peak 1am increased in intensity and gradually shifted to higher frequency. Judging by the above findings, the exchange motion in the crystalline domain occurs above 77 °C at the VDF sequence and the H–H linkage, whereas the conformation of the H–T linkage remains stable below 107 °C. The conformational exchange behavior in the crystalline domain of the AR film agrees with that previously observed for the SC film.9
Figures 4 and 5 show the signal intensities of peaks 1HT and 8HT increased rapidly between 114 and 129 °C, whereas the intensity of peak 2LT decreased. These results indicate the ferroelectric→paraelectric phase transition occurred in this temperature range, which agrees with the sharp endotherm in the DSC experiments (129 °C, chart not shown). An anomaly in the shape of the spectra was observed at 122 °C in Figure 4. The intensity of peak 1am abruptly decreased, whereas that of peak 1HT increased complimentarily (see the magnified spectra in Figure 4). An increase in peak 1HT was also observed in the short CP spectrum (Figure 5), which suggests that the molecular motion in the crystalline domain slowed abruptly at this temperature. At this point, the intensities of peaks 7am and 8am also decreased in the DP spectrum, whereas those of peaks 7HT and 8HT increased. These phenomena clearly indicate a cooperative motion occurred in both the amorphous and crystalline domains during the phase transition, which slowed and fused the molecular motion in both domains. This anomalous increase in the dielectric constant and slowing of the dielectric relaxation spectra have also been observed for P(VDF/TrFE) at approximately the Tc,17, 21, 22 which was explained as a large corrective polarization fluctuation perpendicular to the chain axis. Ohigashi et al.23 reported that the diffuse scattering profile for the hexagonal (002) diffraction of the TG and TG′ units agreed well with the calculated curve assuming rotation in the TGTG′ sequence. In addition, a larger dielectric relaxation strength was observed for ɛ// than ɛ⊥ (electric field is parallel and perpendicular to the chain axis, respectively), which was attributed to the flip-flop motion of the TGTG′ sequence. Moreover, Tanaka et al.24 reported that annealing at just below Tc induced a large growth in the crystalline length along the c axis. The slow down and fusion in both the crystalline and amorphous domains observed in this study could have been caused by the propagation of conformational exchanges beyond the interface between the crystalline and amorphous domains, with incorporating conformational kinks into the amorphous domain.
Figure 6 illustrates the changes in the molecular conformation and the motion in both the crystalline and amorphous domains caused by the heat-induced phase transition based on the changes in the VT spectra (Figures 4 and 5). The phase transition was induced as follows. First, the fraction of the conformational exchange increased at the VDF and H–H linkage at 77 °C. Then, the conformational exchange at the H–T linkage became vigorous at over 107 °C. Hence, the H–T linkage had a key role in the phase transition. The cooperative motion occurred in both the amorphous and crystalline domains at the phase-transition temperature of 122 °C. After the completion of the phase transition at 129 °C, peak 1am reappeared with a narrow linewidth (see the magnified spectra). These results indicate that the cooperative motion occurring in both the crystalline and amorphous domains collapsed in the paraelectric phase, and the molecular motion in the amorphous domain became independent from the crystalline domain. 19F relaxation time analyses justify these phenomena as described below.
Figure 7a shows the temperature dependence of the T1ρF values for peaks 1am, 7am and 8am obtained via direct spin-lock experiments (Figure. 1a) upon heating. The values of the shorter T1ρF components for each peak did not change significantly between 56 and 107 °C, despite the tendency of the T1ρF for peak 1am to increase with the temperature. Considering the Tg of this copolymer is less than 0 °C,21 this phenomenon suggests that the motion at frequencies much higher than 100 kHz become dominant in the amorphous VDF chain sequences at elevated temperatures. As shown in Figure. 7b, the ratio of the shorter T1ρF components began decreasing at 85 °C, whereas the ratio of the longer T1ρF components increased complimentarily, which means that rapid molecular motions, such as the conformational exchange between trans and gauche conformers in the amorphous domain, were significantly stimulated, and thus the T1ρF values for the shorter relaxation components began increasing above 85 °C. Therefore, the longer components consisted of not only the crystalline domain but also a certain portion of the amorphous domain at temperatures over 85 °C. The temperature dependence of the T1ρF values for the crystalline domain is shown in Figure 7c. These values ranged from 20 to 90 ms between 42 and 107 °C. Although these T1ρF values may have relatively large errors, they indicate an absence of molecular motion at approximately 100 kHz. Note that the T1ρF values decreased from 25 to 30 ms, to 15 ms, and became identical for all peaks between 114 and 122 °C. As reported in our previous paper,9 the T1ρF of the crystalline domain of the SC film abruptly collapsed to a unique value at 119 °C, which indicated a uniform molecular motion involving all of the chain sequences rotating around their chain axis was induced.2, 25, 26 The same change in molecular motion occurred in the crystalline domain of the AR film during the phase transition.
Figures 8a and b show the decay of the 19F magnetization in the variable spin-lock experiments at 122 and 129 °C, respectively. All of these decays can be fitted using single-exponential functions. At 122 °C, the crystalline (1HT, 7HT, 8HT) and amorphous (7am, 8am) signals exhibit similar T1ρF values; however, the T1ρF of peak 1am is slightly smaller. This finding supports the existence of cooperative motion in both the amorphous and crystalline domains as indicated by the spectral shapes (Figure 4). Similar T1ρF values (ca. 20 ms) were obtained for peaks 7HT and 8HT at 129 °C as shown in Figure 8b; however, the T1ρF of peak 1HT was significantly shorter (12 ms) than the others, which indicates the amorphous domain moves more rapidly than the crystalline domain in the paraelectric phase. In addition, the T1ρF of peak 1am was significantly shorter than those of peaks 7am and 8am, but close to that of peak 1HT, which indicates the molecular mobility of the VDF chain sequence in the amorphous domain is less than that of the TrFE units, and cooperative motion occurs between the crystalline and amorphous domains in the VDF chain sequence.
The temperature dependence of the spin–lattice relaxation times, T1F, upon heating is summarized in Table 1. The integrated signal intensity was used for peak 1, which includes both 1am and 1HT. Two decay components were observed for each peak in the temperature range from 42 to 119 °C. Because these T1F values were obtained via a DP inversion-recovery pulse sequence, the longer components include contributions from the crystalline domains. The shorter T1F components indicate that 20 to 30% of the amorphous phase experienced vigorous motion at several hundreds of MHz at 42 °C. This fast motion presumably corresponds to the conformational exchange between trans and gauche conformers and the flip-flop of the TrFE units.18, 19, 20 The shorter components of T1F gradually increased upon heating from 42 to 100 °C, whereas the longer components decreased. Simultaneously, the ratios of the shorter components increased by up to 40–50% at 100 °C. These facts indicate that the conformational exchange was gradually activated at elevated temperatures. The proportion of the short components in peaks 7am and 8am increased rapidly above 77 °C. In addition, an anomalous increase in T1F was observed in the long components of peaks 7 and 8 at 114 °C, and jumped to 0.5 s at 119 °C (only one relaxing component was observed for each peak at this temperature). These facts suggest the rapidly moving TrFE units slowed down at just below the Tc, whereas no significant change occurred in the VDF sequences, which agrees well with the T1ρF behaviors mentioned above. It should be noted that the anomalous behavior observed for peaks 7 and 8 corroborates the role of the TrFE units as an anchor that prevents full chain rotation just below the Tc upon heating.
Cooling process. Figures 9 and 10 show the DP 19F MAS and 1H→19F CP/MAS NMR spectra, respectively, of the AR film upon cooling. The intensity of the sharp amorphous signal of the VDF chain sequence (peak 1am) decreased between 129 (Figure 5) and 122 °C, and was assimilated into peak 1HT, which decreased in intensity and experienced a low-frequency shift once the temperature was lowered to 85 °C. Simultaneously, the intensity of peak 1HT increased in the short CP spectra, which contrasts the DP spectra and indicates the molecular motion of the VDF chain sequence slowed markedly as the temperature was lowered. The low-frequency shift in peak 1HT corresponded to a decrease in the gauche conformer of the VDF chain sequence. Similar spectral changes were observed for the spectral region of CHF fluorines. The sharp amorphous resonances for peaks 7am and 8am weakened in the DP spectra, and significant increases were observed in the crystalline peaks 7HT and 8HT from 122 to 85 °C. These observations demonstrate that the cooperative molecular motion was initiated and spread over the paraelectric crystalline and amorphous domains in this temperature range. In addition, the amorphous domain was gradually assimilated into the crystalline domain where the molecular motion slowed and the number of gauche conformers in the VDF sequence and H–H linkage decreased with decreasing temperatures.
The sudden appearance of broad crystalline signals throughout the spectrum at 77 °C in Figure 9 indicates that the transition from the paraelectric to the ferroelectric phases occurred between 85 and 77 °C. This temperature range also matched the transition temperature measured by DSC. Lowering the temperature further promptly decreased the intensities of the sharp signals, and the crystalline signals increased complementarily. The spectral shape measured at 42 °C in the DP spectrum was quite different from the one measured before heating (Figure 4), and the sharp, amorphous resonances were only weakly observed after heating. These findings supports the suggestion that molecular chains containing considerable amounts of the gauche conformer in the amorphous domain were gradually incorporated into the crystalline domain, which consisted entirely of the trans conformer, by annealing. As the molecular chains underwent vigorous rotational and sliding motions along the chain axis in the hexagonal phase, the annealing procedure significantly improved their arrangement and removed conformational defects via this sliding motion. The spectral changes and T1ρF measurements (described below) upon cooling suggest the sliding motion was extensively diffused within the amorphous domain in the hexagonal phase.
The changes in the T1F values upon cooling are summarized in Table 2. A single relaxation component was observed for each peak, and the T1F values were identical for all of the peaks between 122 and 85 °C. These values tended to decrease from 0.60 s at 122 °C to 0.44 s at 85 °C, which implies uniform molecular motion occurred at approximately several MHz in the paraelectric phase and slowed gradually with decreasing temperature. Two relaxation components were observed below the phase-transition temperature (77–85 °C for cooling) for each peak: the longer T1F components attributable to the crystalline domain were over 2 s, and the shorter ones attributable to the amorphous domain continually decreased throughout the phase transition. The proportion of the shorter components promptly decreased to 20–25% at 42 °C after the phase transition, which indicates the conformational exchange motion was frozen, and the polymer chains were in all-trans conformation in the ferroelectric phase. The longer T1F components at 77 °C are above 3 s, which was significantly longer than those below 70 °C. Although a full understanding of the long T1F components was not achieved, they may be related to the changes in the motional mode caused by the termination of the chain rotation. The longer components gradually increased from 77 to 43 °C, which indicated the molecular chains in the crystalline domain stabilized at lower temperatures.
The temperature dependence of T1ρF upon cooling is summarized in Table 3. These values for peaks 7am and 8am promptly decrease upon cooling from 129 to 114 °C similarly to those for peaks 7HT and 8HT (Figure 11 and Table 3). In addition, the T1ρF value of peak 1am approached those of peaks 7HT and 8HT between 122 and 107 °C. As mentioned above, a decrease in the signal intensities of the amorphous peaks and the increase in those of the crystalline peaks was observed in the DP and short CP spectra, respectively, across the same temperature range. These facts also support that the molecular motion in the amorphous domain slowed and began cooperating with that of the crystalline domain in the paraelectric phase (H–T phase). Upon lowering the temperature to 85 °C, the T1ρF values became identical for all peaks (ca. 10 ms), which indicates there was no difference in the molecular mobility at approximately 100 kHz between the amorphous and H–T crystalline phases.
Two T1ρF components were observed below the phase transition for all of the peaks. The longer and shorter components correspond to the ferroelectric crystalline and amorphic domains, respectively. The T1ρF values of the longer components promptly increased from 77 to 63 °C, which indicates the rotational motion in the paraelectric phase suddenly ended, and the polymer chains all reverted to the trans conformer in both the VDF chain sequence and the TrFE units. These conformational changes were also clearly observed in the short contact CP spectra.
Conclusions
The changes in the molecular conformation, phase structure and molecular mobility of semi-crystalline P(VDF75/TrFE25) films containing significant amorphous domains, which were caused by the ferroelectric to paraelectric phase transition, were analyzed using solid-state 19F MAS and 1H→19F CP/MAS NMR. A delayed CP pulse sequence was used to selectively observe signals from the amorphous domain, whereas short CP experiments were used to eliminate the signals from the amorphous domain. The T1ρF values of the amorphous signals were estimated to be 2.0 ms for the VDF chain sequence and 4.7–5.0 ms for TrFE units at 42 °C, which suggests a higher molecular mobility occurs for the former in the amorphous domain at approximately 100 kHz.
The VT experiments indicated that the molecular motion in the amorphous domain was closely related to that of the crystalline domain near the phase-transition temperature upon both heating and cooling. The anomalous decrease in the signal intensity of peak 1am and its T1ρF value being similar to the crystalline domain at 122 °C indicate a cooperative motion occurred in both phases at the phase-transition temperature. Changes in the conformation and molecular mobility of the crystalline domain in the AR film were practically identical to those in the SC film: the conformational exchange between trans and gauche gradually increased in VDF and at the VDF–TrFE H–H linkage with elevating temperatures, and the conformational exchange motion at the H–T linkage induced the phase transition. The amorphous domain was assimilated into the crystalline domain upon lowering the temperature from 129 to 85 °C as shown by the spectral shapes, and identical T1ρF and T1F values for the two domains at 85 °C, which significantly increased the crystallinity below the Tc.
References
Furukawa, T. Ferroelectric properties of vinylidene fluoride copolymers. Phase Transitions 18, 143–211 (1989).
Tashiro, K. in Ferroelectric Polymers (ed. Nalwa H. S.) Ch. 2, 63–181 (Marcel Dekker, New York, 1995).
Ohigashi, H. & Koga, K. Ferroelectric copolymers of vinylidenefluoride and trifluoroethylene with a large electromechanical coupling factor. Jpn J. Appl. Phys. 21, L455–L457 (1982).
Koga, K. & Ohigashi, H. Piezoelectricity and related properties of vinylidene fluoride and trifluoroethylene copolymers. J. Appl. Phys. 59, 2142–2150 (1986).
Koga, K., Nakano, N., Hattori, T. & Ohigashi, H. Crystallization, field-induced phase transformation, thermally induced phase transition, and piezoelectric activity in P(vinylidene fluoride-TrFE) copolymers with high molar content of vinylidene fluoride. J. Appl. Phys. 67, 965–974 (1990).
Tanaka, R., Tashiro, K. & Kobayashi, M. Annealing effect on the ferroelectric phase transition behavior and domain structure of vinylidene fluoride (VDF)-trifluoroethylene copolymers: a comparison between uniaxially oriented VDF 73 and 65% copolymers. Polymer 40, 3855–3865 (1999).
Barique, M. A. & Ohigashi, H. Annealing effects on the Curie transition temperature and melting temperature of poly(vinylidene fluoride/trifluoroethylene) single crystalline films. Polymer 42, 4981–4987 (2001).
Hikosaka, M. Unified theory of nucleation of folded-chain crystals (FCCs) and extended-chain crystals (ECCs) of linear-chain polymers: 2. Origin of FCC and ECC. Polymer 31, 458–468 (1990).
Aimi, K., Ando, S., Avalle, P. & Harris, R. K. Solid-state 19F MAS and 1H→19F CP/MAS NMR study of the phase transition behavior of vinylidene fluoride-trifluoroethylene copolymers: 1. Uniaxially drawn films of VDF 75% copolymer. Polymer 45, 2281–2290 (2004).
Ohigashi, H., Omote, K. & Gomyo, T. Formation of ‘‘single crystalline films’’ of ferroelectric copolymers of vinylidene fluoride and trifluoroethylene. Appl. Phys. Lett. 66, 3281–3283 (1995).
Holstein, P., Harris, R. K. & Say, B. J. Solid-state 19F NMR investigation of poly(vinylidene fluoride) with high-power proton decoupling. Solid State Nucl. Magn. Reson. 8, 201–206 (1997).
Wormald, P., Apperley, D. C., Beaume, F. & Harris, R. K. Fluorine-19 solid-state NMR investigation of regiodefective semicrystalline α-poly(vinylidenefluoride). Polymer 44, 643–651 (2003).
Hazendonk, P., Harris, R. K., Ando, S. & Avalle, P. The DIVAM sequence: selective excitation of signals from both rigid and mobile domains in a fluoropolymer. J. Magn. Reson. 162, 206–216 (2003).
Aliev, A. E. & Harris, K. D. M. Simple technique for temperature calibration of a MAS probe for solid-state NMR spectroscopy. Magn. Reson. Chem. 32, 366–369 (1994).
Bloch, F. & Siegert, A. Magnetic resonance for nonrotating fields. Phys. Rev. 57, 522–527 (1940).
Mabboux, P. Y. & Gleason, K. K. 19F NMR characterization of electron beam irradiated vinylidene fluoride-trifluoroethylene copolymers. J. Fluorine Chem. 113, 27–35 (2002).
Furukawa, T., Ohuchi, M., Chiba, A. & Date, M. Dielectric relaxations and molecular motions in homopolymers and copolymers of vinylidene fluoride and trifluoroethylene. Macromolecules 17, 1384–1390 (1984).
Ishii, F., Odajima, A. & Ohigashi, H. Ferroelectric transition in vinylidene-trifluoroethylene copolymer studied by nuclear magnetic resonance method. Polym. J. 15, 875–882 (1983).
Ishii, F. & Odajima, A. Proton spin lattice relaxation in vinylidene fluoride/trifluoroethylene copolymer I. vinylidene fluoride. Polym. J. 18, 539–546 (1986).
Ishii, F. & Odajima, A. Proton spin lattice relaxation in vinylidene fluoride/trifluoroethylene copolymers II. effects of vinylidene fluoride content upon spin relaxation processes. Polym. J. 18, 547–555 (1986).
Koizumi, N., Haikawa, N. & Habuka, H. Dielectric behavior and ferroelectric transition of copolymers of vinylidene fluoride and trifluoroethylene. Ferroelectrics 57, 99–119 (1984).
Omote, K., Ohigashi, H. & Koga, K. Temperature dependence of elastic, dielectric, and piezoelectric properties of ‘single crystalline’’ films of vinylidene fluoride trifluoroethylene copolymer. J. Appl. Phys. 81, 2760–2769 (1997).
Ohigashi, H., Omote, K., Abe, H. & Koga, K. Chain motions in the paraelectric phase in single crystalline films of vinylidene fluoride and trifluoroethylene copolymer P(VDF/TrFE). J. Phys. Soc. Jpn. 68, 1824–1827 (1999).
Tanaka, R., Tashiro, K. & Kobayashi, M. Annealing effect on the ferroelectric phase transition behavior and domain structure of vinylidene fluoride (VDF)–trifluoroethylene copolymers: a comparison between uniaxially oriented VDF 73 and 65% copolymers. Polymer 40, 3855–3865 (1999).
Tashiro, K., Takano, K., Kobayashi, M., Chatani, Y. & Tadokoro, H. Structure and ferroelectric phase transition of vinylidene fluoride-trifluoroethylene copolymers: 2. VDF 55% copolymer. Polymer 25, 195–208 (1984).
Tashiro, K., Takano, K., Kobayashi, M., Chatani, Y. & Tadokoro, H. Structural study on ferroelectric phase transition of vinylidene fluoride-trifluoroethylene copolymers (III) dependence of transitional behavior on VDF molar content. Ferroelectrics 57, 297–326 (1984).
Acknowledgements
We thank T Kodani at Daikin Kogyo Co., Ltd. for providing the P(VDF75/TrFE25) copolymer. We also thank RK Harris, P Avalle, DC Apperley and P Wormald for their help with the measurements and for their discussion.
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Aimi, K., Ando, S. Solid-state 19F MAS and 1H→19F CP/MAS NMR study of the phase-transition behavior of vinylidene fluoride–trifluoroethylene copolymers: 2. semi-crystalline films of VDF 75% copolymer. Polym J 44, 786–794 (2012). https://doi.org/10.1038/pj.2012.114
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DOI: https://doi.org/10.1038/pj.2012.114