3.2.1. Miscibility of PE-VOL/PD,L-LGA Blend
(A) Glass transition temperature
The heating DSC curves of neat PD,L-LGA, neat PE-VOL and those of their blends with different compositions are presented in
Figure 2. As shown in the curve profiles of the blends a confused transition zone is localized between 32 and 60 °C in which the
Tg values cannot be localized accurately because of the small difference existing between the
Tgs of the pure components PE-VOL(51 °C) and PD,L-LGA(36 °C) in which this gap does not exceed 15 °C. Consequently, the criterion which stipulates that the miscibility of a pair of polymers can proofed by the presence in the thermogram of the blend of an unique
Tg cannot be rigorously applied. The same thermograms also show an important depression in the melting temperature of PE-VOL incorporated in the blends with increasing PD,L-LGA content. This finding indicates that the crystalline yield of PE-VOL in the blend dramatically decreased.
Similar results were also observed by different authors using poly(butylene succinate-
co-butylene carbonate)/Poly(vinylphenol) blend [
47], poly(trimethylene terephthalate)/amorphous poly(ethylene terephthalate) blends [
48], and poly(vinylidene fluoride) (PVDF)/poly(methyl methacrylate) (PMMA) blends [
49]. This phenomenon may be thermodynamically traduced by the energy of the mixture accompanied by the exothermic interaction energy between the crystalline part of PE-
co-VAL and that of the amorphous part of PL-
co-GA.
(B) Melting temperature
The DSC thermograms of
Figure 2 also show the melting temperatures of the blends and these of their pure components and the data of the apparent melting temperatures and the heat of melting deducted are gathered in
Table 3. As can be seen from the thermal curves, of the blends only one endothermic peak was observed which is assigned to the apparent melting temperature of the PE-VOL semi-crystalline component. These thermal curves also reveals an important depression of the
Tm of this semi crystalline copolymer from 188 to 156 °C when is blended with PD,L-LGA.
The decrease of the melting temperature in a semi-crystalline polymer in a miscible blend is due to the thermodynamic interactions between its components. Indeed, the Flory–Huggins theory stipulates that a miscible blend containing a semi crystalline polymer is principally characterized by a depression in its melting temperature permitting the determination of interaction energy. In this same direction, the melting temperature of such polymer is principally affected by different thermodynamic parameters and also by its crystal thickness. In this same way, Hoffman–Weeks method permits the isolation of the morphology parameters from the undesired effects that act on the melting temperature of semi-crystalline polymer in its miscible blend using the equilibrium melting temperature,
, expressed by Equation (3) [
50]:
The isothermal crystallization process of pure semi-crystalline copolymer and in its blends were realized at different crystallization temperatures, and results obtained for the neat PE-VOL and the PE-VOL/PD,L-LGA containing equal ratio of each component are plotted in
Figure 3. Based on the variation of the apparent melting temperature
, Tm, versus the crystallization temperature,
Tc it was possible to deduct
relative to the pure PE-VOL and that in their blends as presented in
Figure 4 for the neat PE-VOL and PE-VOL/PD,L-LGA50 system with equal ratios of each component. Indeed, straight lines were obtained and
and
are deduced from the slope of the Hoffman–Weeks plot and the intercept of these curves with the straight
Tm =
Tc, respectively. It is important to note that the
value varied between zero and the unity. This parameter is used to estimate the stability of molten crystals. Indeed, when the
value is close to zero this indicates that the crystals is in its maximum stability and when this parameter is close to one this indicates that this crystals is in its instability state.
and
η values for pure PE-co-VAL and in the blends are listed in
Table 4.
As can be seen from these data, the equilibrium melting point of PE-VOL was found to be 184.9 °C, which agrees with that found in literature (187 °C) [
51] Concerning the PE- VOL/PD,L-LGA systems, the
of the PE-VOL phase decreased with PD,L-LGA content to reach a minimum of 166.8 °C when the polyester in the blend was 90 wt %. In other terms, the maximum extent of this melting temperature depression was 18.1 °C when the pure PE-VOL was converted to the PE-VOL/PD,L-LGA10 blend. In general, the
η values of PE-VOL in its blend, which varied from 0.12 to 0.34, are relatively small, revealing the stability of pure PE-VOL and PE-VOL in the blend. This parameter decreased slowly with increasing PD,L-LGA content to lose about two-thirds of the crystal stability of PE-VOL when 90 wt % of the polyester was incorporated. This suggests that the PE-VOL crystals become less and less stable, i.e., they have less thick lamellar thicknesses, when blended with PD,L-LGA. This fact is probably attributed to the morphological effect.
To rigorously confirm the miscibility of this pair of copolymers, noted by its appearance, it was necessary to use the Flory thermodynamic interaction parameter,
determined from the equation of Nishi and Wang, Equation (4) [
52], based on the Flory–Huggins theory.
where the subscripts 1 and 2 designate the amorphous PD,L-LGA copolymer and the semi crystalline PE-VOL copolymer, respectively.
is the volume fraction of polymer-1.
Vu and
ΔHu are the molar volume and the molar enthalpy of fusion of the repeating units, respectively.
R is the gas constant. χ
1,2 value is deducted from the slope of the linear curve of
Figure 5, indicating the variation of
versus the square of
and the data collected from the literature in which ΔH
uPE-VOL = 4.22 kJ mol
−1 [
53] and
VuPE-VOL = 37.80 cm
3 mol
−1 [
54]
VuPD,L-LGA = 88.06 cm
3mol
−1 calculated from the density of PD,L-LGA and the molar masses of lactide and glycolic acid co-monomer units. χ
1,2 and the interaction energy density between blend components, B, calculated from the
term of Nishi’s equation for this pair of polymers are −0.27 ± 0.02 and −11.67 ± 0.86, respectively. The negative sign of these values indicates miscibility in the amorphous part of the PE-VOL/PD,L-LGA system in all investigated compositions. These values are comparable to those created between the ester and hydroxyl groups in the polymer blends such as those investigated by Kuo et al. [
55] on the phenolic resin/poly(ε-caprolactone) system, which were
= −0.35 and B = −12.51. The interaction involved in the miscibility of this blend is principally caused by the hydrogen bonds developed between the carbonyl group of PD,L-LGA and the hydroxyl group of PE- VOL units.
3.2.3. Non Isothermal Crystallization Kinetics of PE-VOL and PE-VOL/PD,L-LGA Blend
The determination of the crystallinity degree,
, is obtained from the latent heat of the crystallization of crystalline polymer in the blend during the crystallization process. This parameter is expressed according to Equation (5) [
58]:
where
represents the apparent latent heat of crystallization of PE-VOL in the blend and
the extrapolation of the latent heat corresponding to the melting of PVA 100% crystalline. Note that the
taken from the literature has an average value of 157.8 J·g
−1 [
59]
φ is the mass fraction of the amorphous copolymer (PL-co-GA) incorporated in the blend. The values
for PE-VOL and PE-VOL/PD,L-LGA blend with different PE-VOH contents obtained from this equation are gathered in
Table 4.
Figure 7 shows the effect of the dispersion of PD,L-GLA in the blend on the non-isothermal crystallization kinetics of PE-VOL in the blend. As can be seen from these thermal curve profiles, the peak of the crystallization enthalpy is lower when the PD,L-LGA content in blend was 10 wt %. On the other hand, as in case of the neat PE-VOL, it was observed that, for all blend compositions, the
value of PE-VOL slowly shifted toward the lower temperatures as the cooling rate increased. This phenomenon was also revealed by different investigators [
60,
61,
62] and attributed this fact to a reduction of chain mobility and flexibility limiting the time of diffusion inside the crystalline lattice of the PE-VOL matrix. This fact leads to reduce the crystallization rate of the semi-crystalline copolymer in the blend. Indeed, when the blend samples are cooled down at relatively high cooling rates, the movement of PE-VOL chains do not seem to follow the cooling temperature regime imposed over time due to the influence of thermal hysteresis, which leads to a lower maximum crystallization temperature. When incorporated into the PE-VOL matrices, the macromolecular chains of PD,L-LGA act as an energy barrier preventing heat transfer to the PE-VOL chains. Therefore, at a high PD,L-LGA content in the blend, the crystallization process occurs at a relatively low temperature.
The degree of relative crystallinity,
, of PE-VOL in the blend versus temperature is given by Equation (6) [
63]:
where
and
T∞ are the beginning and finishing crystallization temperatures measured at the starting and finishing inflections of the crystallization peaks, respectively.
H is the heat of the crystallization process of neat PE-VOL or PE-VOL in the blend at temperature,
T.
can be determined after replacing integrations functions by the areas under the DSC crystallization peaks in the DSC thermograms from
T = to
T = T (
) and the area under the total crystallization peak (
), Equation (6) becomes:
The variation of the relative crystallization time,
is calculated from the temperature T at crystallization time
t and the cooling rate
β according Equation (8):
Typical plots of the variation of the relative crystallization degree of neat PE-VOL and PE- VOL in the blend as function of temperature,
, and time,
, are obtained during the non isothermal crystallization process and the curves of pure PE-VOL and PD,L-LGA/PE-VOL50 taken as examples are presented in
Figure 8A,B, respectively. Sigmoid pattern was obtained for each sample and the rate of the crystallization deducted from the slope is almost constant between 20% and 80% of the relative crystallinity and due to the spherulite impingement effect, these curve profiles tend to become flat beyond [
58].
The half time,
t1/2, of the crystallization process was deducted from the curves of
Figure 8B at 50% of the relative crystallization of pure PE-VOL and PD,L-LGA/PE-VOL systems and the data obtained are plotted in
Figure 9. For the pure PE-VOL, in general these curve profiles reveal an increase in the
t1/2 with increasing the cooling rate. On the other hand, when the PD,L-LGA was incorporated in the PE-VOL matrix the
t1/2 passed by a minimum at 30 wt % of this amorphous copolymer in the blend. Indeed, the crystallization process of PE-VOL in the blend was dramatically decelerated when the PD,L-LGA content was 30%, in which the t
1/2 loses 45% – 83% of its value depending on the cooling rate. This observation can be explained by the fact that at a relatively low PD,L-LGA content, the macromolecular chains of this last copolymer cluster cannot restrict the motion of the PE-VOL macromolecular chains but act as heterogeneous nucleating agents during the non-isothermal crystallization process and therefore accelerate the crystallization. At a higher PD,L-LGA content, the macromolecular chains of PD,L-LGA clusters act as a barrier that restricts the thermal motion of PE-VOL macromolecular chains and therefore retards the formation of crystals. As a result, the addition of a large amount of PD,L-LGA can delay the overall crystallization process.
Among many models that have been developed to investigate the non-isothermal ctystallization kinetics [
64,
65,
66,
67] the Ozawa Equation (9) extended from that given by Avrami Equation (10) [
68] is adopted in this work to study the non-isothermal crystallization kinetics of the PE-VOL/PD,L-LGA blend and its pure semi-crystalline component.
The Avrami equation originally applied for isothermal crystallization is also applied for non-isothermal crystallization by assuming that the specimen is cooled at a constant cooling rate. Note that
Xt and
XT represent the relative degrees of crystallinity at time (
t) and temperature (
T), respectively,
k and
kT are the crystallization kinetics rate constant and the cooling function of non-isothermal crystallization at temperature
(T), respectively,
β is the cooling rate, and
n and
m are the isothermal Avrami and the Ozawa exponents depending on the dimension of crystal growth and nucleation mechanism, respectively. Equation (10) can be linearized as follows:
As can be seen from the plots of
ln[−ln(1 − Xt)] versus
ln(β) for PE-VOL and PE-VOL/PD,L-LGA systems in
Figure 10, all specimens containing different PD,L-LGA contents showed straight lines indicating that the Ozawa equation Equation (8) described the primary process of non-isothermal crystallization of pure PE-VOL and its blends perfectly. The values of
kT and
m deduced from the intercept and slope of these curves, respectively, are gathered in
Table 6. As can be seen from these data, the value of
m for pure PE-VOL increased from 1.24 to 1.55 with the crystallization temperature, which agrees with the results of the literature [
69]; however, the values of
m for the blends, in general, are opposite that of pure PE-VOL and randomly fluctuated between 1.55 and 3.60 depending on the temperature and PE-VOL/PD,L-LGA composition, suggesting that the introduction of PD,L-LGA content in the PE-VOL matrix does not significantly influence the growth of crystals. In certain cases of PE- VOL/PD,L-LGA systems, the small increase of
m observed when the temperature increased reveals a small change in the crystallization mechanism, probably due to the decrease in the viscosity of blend caused by a rupture of the strong interactions between hydroxyl groups of PE-VOL chains for the profit of the weak interactions between hydroxyl of PE-VOL and carbonyl of PD,L-LGA. The increasing
m values are usually attributed to the change from instantaneous to sporadic nucleation [
70] According to typical polymer crystallization reports, an
m value of 2 indicates that the crystal growth is sporadic and spherical and occurs from nuclei. Heterogeneous nucleation has been suggested for fractional
m values in polymer crystallization [
71] The
kT value related to the all over crystallization rate decreased when the temperature decreased, except in the blend with 25% of PD,L-LGA content in which this parameter increased. This means for PE-VOL and PE- VOL/PD,L-LGA blends with PD,L-LGA content inferior to 25 wt%, the crystallization rate increased when the temperature decreased, especially in the case of pure PE-VOL, in which this parameter dramatically decreased. In addition,
kT values depend on the PE-VOL/PD,L-LGA composition.
The crystallization activation energy (
) associated with the overall crystallization process is evaluated from the rates of crystallization using the Kissinger Equation (12) [
72]:
where
R and
are the gas constant and the peak crystallization temperature, respectively.
is obtained from the slope of the plots
Rln(
β/Tc2) versus
1/T of
Figure 11. The curve (on the top) indicating the variation of the crystallization activation energy versus the PE-VOL content showed that the
passed by a maximum at 337 ± 12 Kj when the PE-VOL content in the blend was 75 wt %. The increase in
can be explained by the increase in the miscibility of PE-VOL/PD,L-LGA system because increasing the PD,L-LGA in the blend results in dilution of PE-VOL chains at the crystal growth front and contributes to the reduction of mobility of PD,L-LGA chains due to the higher
Tg of the blend than that of pure PE-VOL, thus a higher value for PE-VOL crystallization occurs in the blends.