2.1. Effects of Compost Storage on Mass Change
At 30 °C, the relative masses of the samples of REF and V1 to V4 remained more or less unchanged within the range of the scatter of the mass determination after compost storage for 8 weeks.
Figure 2 indicates that the disintegration processes did not lead to mass decreases yet. The mass variations can be attributed to processes which occur within the initiation time, e.g., mass increase due to chemical reactions, humidity uptake, and remaining compost particles, or mass decrease due to releases of degradation reactions or loss of micro-plastic particles during cleaning.
At 60 °C, the relative masses remained unchanged only for 4 days.
Figure 2 shows that, for V1 and V2, a pronounced mass decrease was consequently observed. The REF exhibited a less pronounced mass decrease between day 5 and 6. The V3 showed a tendency of decreasing mass, whereas the V4 seemed to not be disintegrated, even after 7 days. This shows that the initiation times of disintegration are significantly affected by the chosen CECL and the induced chemical changes. Furthermore, significant disintegration was observed for the REF, V1, and V2 after 7 days at 60 °C. This supports the interpretation that the stains on the REF, V1, and V2 in
Figure 1 represented a beginning disintegration.
Because of the scatter of the mass measurements, the disintegration was confirmed only if the masses had decreased to less than 90% of the initial value. Thus, the time
t80% was the determined time at which the masses of the films reached 80% of their initial masses, as is shown in
Figure 2, and it represents the upper limit of the initiation time.
The data indicated that there was a mass increase at the beginning of the compost storage due to the initial disintegration processes. To estimate the mass scatter due to adsorbed and biodegradation-generated low molecular weight components, the initial masses of the DSC experiments were compared to the masses after the second heating runs. The mass losses were between 2 and 12%, which showed that there was a remarkable content of low molecular components in the films, as is shown in
Table 1.
After 8 weeks at 30 °C, the REF had lost 4% of its mass, and 7% of its mass after 7 days at 60 °C. The decrease in the V1 and V2 exceeded that of the REF, which showed that the biodegradation of the V1 and V2 was more pronounced. For the V3 and V4, the decreases were less than for the REF, which showed that cross-linking hindered biodegradation and decelerated disintegration. However, the decreases were still within the scatter of the relative masses during the initiation times. This is a further indication for a mass increase due to the uptake and generation of low molecular weight components during the initiation times of compost storage, in addition to the contributions of adherent compost particles.
For all compounds, the DSC traces of the first run differed significantly from the second run, as is shown in
Figure 3, and the enthalpies also differed between 20 and 170 °C. These differences can be attributed to the processing history (which was similar for all films) and the reached state of biodegradation. As polyamides are typically dried at 80 °C (a temperature which is also above the
Tg of PLA), the enthalpies between 70 and 90 °C were determined, as is shown in
Table 1. It can be seen that these enthalpies correlated qualitatively with the mass loss for the REF, V1, and V2 and that they were almost equal for the V3 and V4. Given that the content of CECLs was low, one can assume that the water contents of all films were identical. Thus, the differences in the mass losses in
Table 1 have to have been generated by volatile low molecular linked to the initial processes of biodegradation.
2.2. Effects of Compost Storage on Disintegration Kinetics
After compost storage at 60 °C, the films were further investigated with respect to their disintegration kinetics by determining the cross-sectional areas of holes to elucidate the kinetic parameters of initiation time
tinit and disintegration time
τdisint for the REF and for V1 to V4. The experimental data can satisfactorily be fitted by Equation (8) with a reasonable R
2, as are shown in
Figure 4 and
Table 2. In the model, a single dominating disintegration process was assumed using an approach that was used to describe the hydrolytic degradation of neat PLA, PLA modified with a carbodiimide, and PLA wood flour composites [
34,
35]. The smaller measured time dependent degrees of disintegration
xdisint of the REF, V1, and V2 when compared to the predicted values can be explained by the fact that the disintegration had already happened prior to the first visible holes.
The times
t80% (to the mass decrease of 80%) exceeded the initiation times
tinit by three to four factors, as is shown in
Table 2. This shows that the initiation of disintegration depends on the considered property—mass loss or hole generation.
Obviously, some degree of disintegration has to happen prior to the appearance of the first holes. Thus, the determined initiation times tinit have to depend on the film thickness. If one assumes that the first appearance of holes depends linearly on the film thickness, the initiation time of V1 (30 µm instead of 25 µm) would be roughly 20% too long—leading to a corrected tinit ≈ 27 h. The V4 did not show any holes within 7 days, which indicated that the molecular structure generated by the CECL poly(4,4-dicyclohexylmethane carbodiimide) prevented significant disintegration.
The disintegration times τdisint show that the CECLs significantly affected the disintegration processes. The disintegration rates of the V1 and V2 exceeded that of the REF by 2.5 times and 4 times, respectively, whereas it was decreased to a factor 0.25 for the V3. Given that the V4 did not show any holes within 7 days, it was not evaluated.
2.3. Effects of Compost Storage on Mechanical Properties
The Young’s moduli in the extrusion direction (ED) were roughly double of those in transverse direction (TD), which reflected the film anisotropy due to processing. Compost storage of the REF and V1 to V4 for 8 weeks at 30 °C initially led to an increase in the Young’s moduli in the order of 20% before they were slowly decreased again, as is shown in
Figure 5. This increase can be explained by the annealing effects in the amorphous phases of PLA [
36] and by the post-crystallization of PBAT. The PLA in its disperse phase was protected by the PBAT matrix against any kind of degradation and disintegration at the beginning of the compost storage at 30 °C, and annealing could happen undisturbed. Jian et al. [
8] reported that PBAT starts to crystallize at 60 °C if heated for 10 °C/min during DSC. Therefore, a slow post-crystallization of amorphous PBAT can already be expected at 30 °C if humidity provides more mobility to the polymer chains. Both processes may increase stiffness. Interestingly, the maximum Young’s moduli were determined after 2 weeks in the ED, while 4 weeks were needed in the TD, which indicated that mechanical degradation happened differently in the ED and TD during initiation time. This can be understood by the fact that the films exhibit significantly different morphologies on their fracture surfaces in the ED and TD [
37]. Thus, during the initiation phase, one direction can be more affected by biodegradation processes than the other.
Compost storage for 8 weeks at 30 °C led to a continuous decrease in the tensile strengths of the REF, V1, and V2 in the order of 50 to 70% in the ED and TD. The V3 and V4 exhibited a plateau of tensile strength for 4 weeks in the ED before a decrease of 60 to 70% occurred. In the TD, the V3 exhibited a plateau of tensile strength for 4 weeks, and the V4 exhibited a plateau of tensile strength for 2 weeks.
The elongations at break exhibited a plateau for 2 weeks for the REF, V1, and V2 in the ED, with subsequent decreases of 35% (REF) and almost 100% (V1 and V2). For the V3, the plateau lasted 4 weeks, followed by a decrease of 20%, whereas no decrease was observed for the V4, even after 8 weeks. In the TD, the elongations at break of the REF and V2 exhibited a plateau for 2 weeks before they decreased, whereas the V1 showed a continuous decrease. Their elongations at break after 8 weeks dropped to 5 to 30% of the initial values. The V3 and V4 exhibited plateaus of elongations at break in the TD that lasted 4 weeks and 2 weeks, respectively, with subsequent decreases of 30 and 70%, respectively.
Compost storage at 60 °C, as is depicted in
Figure 6, had pronounced impact on the mechanical properties of the films. Annealing effects in the amorphous phase of the PLA did not continue to occur, as the PLA was now above the glass transition temperature. Therefore, no increases in Young’s moduli were further observed. After one week, it was hardly possible to perform tensile tests with films of the REF, V1, and V2, due to severe mechanical disintegration. In the ED and TD, the Young’s moduli of the REF remained on a plateau for the first 3 days. Then, they continuously decreased close to zero within a week. The Young’s moduli of the V1 and V2 continuously decreased after 7 days to 70% and 50%, respectively, in the ED and TD. For the V3, its Young’s moduli in the ED and TD remained on a plateau for 14 days before they decreased by at least 50%. The Young’s moduli of the V4 remained on a plateau for almost 28 days. Only the modulus in the ED was 15% lower after 28 days.
In the ED and TD, the tensile strengths of the REF, V1, and V2 decreased continuously to approximately 20% of their initial values after 7 days. For the V3, its Young’s moduli in the ED decreased continuously to less than 20% after 28 days, whereas in the TD, they decreased to 30% during the first 2 days and remained on that plateau for 2 weeks before they further decreased to less than 20%. For the V4, the tensile strength in the ED decreased continuously to approximately 40% after 28 days, whereas in the TD, it remained on a plateau for 3 days before it decreased to 30%.
The elongations at break in the ED and TD of the REF remained on a plateau for 1 day and then decreased to approximately 10% of their initial values after 3 days. For the V1, a plateau was observed in the ED for 1 day with a subsequent decrease that was almost close to zero after 7 days. In the TD, the decrease close to zero was already reached after 3 days. The V2 exhibited a continuous decrease and reached elongations at break of a few percentage points after 7 days in the ED and after 3 days in the TD. The V3 exhibited a plateau for 1 day and a slow decrease to a few percentage points after 14 days in both the ED and TD. For the V4, a plateau was observed for 3 days, followed by a decrease to 50% in the ED and 10% in the TD.
Tensile strengths and elongations at break indicate a high sensitivity with respect to structural changes of the films, and they showed that the films of the REF and V1 to V4 had also been mechanically degraded during compost storage at 30 °C. Obviously, these processes were still in the state of initiation with negligible effects on film masses. At 60 °C, the degradation processes were significantly accelerated, as the REF, V1, and V2 were severely disintegrated after 7 days (see
Figure 1), and both their tensile strengths and elongations at break dropped to low values.
2.4. Effects of Compost Storage on Thermal Properties
The biodegradation caused by compost storage affected the thermal properties in a significant manner, as the DSC curves of the first heating run after 8 weeks at 30 °C differed significantly from those after 7 days at 60 °C (see
Figure 7), which also occurred for the corresponding transition temperatures and heats of fusions, as is shown in
Table 3.
After compost storage for 8 weeks at 30 °C, the glass temperatures of the PLA hard segments
Tg,hs were increased by 4 °C (REF, V1, and V2), 2 °C (V3) and 3 °C (V4), as can be seen in
Table 3. This shows that annealing and physical aging of the amorphous PLA phase took place during compost storage. Furthermore, an endothermal peak at 65 °C appeared for all compounds, as is shown in
Figure 7a. Given that it did not appear after compost storage at 60 °C (see
Figure 7b), it was probably the result of a relaxation peak of the amorphous PLA caused by long storage times below the PLA glass temperature. Given that it was more pronounced for the REF, V1, and V2, one can conclude that the biodegradation had proceeded more significantly.
After compost storage for 7 days at 60 °C (see
Table 3), only the V1 and V2 exhibited an increase in the
Tg,hs of 2 °C, whereas it was decreased by 2 °C (REF), 5 °C (V3), and 3 °C (V4). Due to the pronounced state of disintegration, it is unclear if the increase in the
Tg,hs of the V1 and V2 was linked to the PLA or to the PLA being chemically modified by biodegradation. The decreases in the
Tg,hs of the REF, V3, and V4 can be interpreted through the softening of amorphous PLA due to the absorption of water or other low molecular components. In addition, the DSC traces of the REF and V1 to V4 exhibited a second step-like transition at 75 °C (see
Figure 7b), whose appearance cannot be explained yet.
The PBAT melting temperature Tm1 of the REF was increased from 113 °C to 117 °C after compost storage for 8 weeks at 30 °C. This shows that post-crystallization processes led to a growth of lamellae thickness. The Tm1 values of the V1 to V4 initially ranged between 105 and 109 °C, but were significantly increased during compost storage: They increased by 16 °C (V1), 11 °C (V2), 9 °C (V3), and 12 °C (V4). The initial mean lamellae thicknesses of the crystalline PBAT of the V1 to V4 were smaller than those of the REF due to the crystallization-disturbing effects of the CECLs. This initial situation allowed for post-crystallization that led to a significant growth of mean lamellae thicknesses that were similar for the REF, V3, and V4 and higher mean growth for the V1 and V2. During compost storage for 8 weeks at 30 °C, the heats of fusion ΔHm1 increased significantly. For the REF, V1, and V2, they increased by a factor of two. For the V3 they increased by a factor of 1.5, and for the V4, they increased by a factor of 4, which indicated post-crystallization.
The PLA melting temperature Tm2 of the REF increased by 8 °C after compost storage for 8 weeks at 30 °C. This showed that post-crystallization had taken place, as well as a growth of lamellae thickness. For the V1 to V4, the Tm2 decreased between 0 °C and 3 °C, which indicated that the structural changes caused by the CECLs limited the growth of the lamellae thickness. The heats of fusion ΔHm2 were increased by a factor of 2.5 for the REF, V1, and V3, which indicated post-crystallization in their PLA phases. The ΔHm2 remained constant for the V2, whereas it decreased by a factor of 0.4 for the V4. When considering the changes in the ΔHm2, one has to keep in mind that the melting peaks of the PLA overlap partly with those of the PBAT. Thus, the precise determination of the ΔHm2 requires peak deconvolution, which may lead to smaller differences between the REF and V1 to V4.
After compost storage for 8 weeks at 30 °C, all compounds had higher
Tm1, increased
ΔHm1, and partly increased
ΔHm2. This explains the increasingly brittle behavior of the films, the initial increases in Young’s moduli, and their “constancy” during compost storage, in spite of the first biodegradation, as is shown in
Figure 5.
After compost storage for 7 days at 60 °C all compounds exhibited higher melting temperatures of the PBAT
Tm1—5 °C (REF), 20 °C (V1), 13 °C (V2), 7 °C (V3), and 10 °C (V4)—and increased heats of fusion
ΔHm1—by a factor of three (REF, V1 and V2), factor of two (V3), and factor of four (V4). This indicated pronounced post-crystallization and growth of the lamellae thickness, which can be partly attributed to the biodegradation of the amorphous PBAT [
38].
The PLA melting temperature Tm2 of the REF increased by 7 °C after 7 days at 60 °C, which indicated post-crystallization with the formation of thicker lamellae. For the V1 to V4, the Tm2 decreased by 5 °C (V1), 10 °C (V2), 1 °C (V3), and 4 °C (V4). This shows that the CECLs hindered the formation of thick lamellae. The heats of fusion ΔHm2 increased by a factor of 3 (REF), a factor of 2 (V1), a factor of 1.2 (V2) and a factor of 2.5 (V3), which indicated post-crystallization of the PLA. For the V4, the ΔHm2 could be considered as unchanged.
The crystallization temperatures Tcr of the REF, V1, and V2 increased by more than 10 °C for both composting conditions. For the V3 and V4, the Tcr decreased by 15 °C and 4 °C, respectively, thus indicating structural changes of the polymer chains that hindered crystallization.
Interestingly, the REF, V1, and V2 exhibited enthalpy minima at 90 to 95 °C after compost storage at 30 °C. Therefore, overall enthalpies were determined for the temperature range of 20 to 170 °C, as well as for three temperature ranges, in order to address the disintegration processes of the amorphous PBAT (20 to 95 °C), the crystalline PBAT (95 to 142 °C) and the crystalline PLA (142 to 170 °C).
Table 4 reveals that the biodegradation reached different stages in the corresponding temperature ranges. The V3 and V4 were hardly disintegrated according to visual inspection (see
Figure 1), and for both storage conditions had a total enthalpy of 22 J/g. Therefore, this value was taken as a reference value for the following considerations. This can also be justified as the overall enthalpies of the REF and V1 to V4, and the initial states were (21 ± 2) J/g in the first run and (17 ±1) J/g in the second run.
After compost storage for 7 days at 60 °C, the total enthalpies of the REF, V1, and V2 were around 33 J/g, whereas they remained around 22 J/g for the V3 and V4, which were identical to the total enthalpies of the REF, V1, V3, and V4 after compost storage for 8 weeks at 30 °C (with the V2 being the only compound with the highest disintegration rate at a total exhibited enthalpy of 26 J/g). In the second heating runs, similar DSC traces with similar mean total enthalpies of (16.2 ± 0.4) J/g for compost storage after 8 weeks at 30 °C and (16.4 ± 1.1) J/g for compost storage of 7 days at 60 °C were measured for the REF and V1 to V4. This means that the difference between the first heating runs could mainly be attributed to processes of biodegradation.
Obviously, the V3 and V4 disintegrated the least and had identical total enthalpies. However, the enthalpies were differently distributed between the temperature ranges for the two conditions of compost storage: between 20 and 95 °C, they were 7 J/g (8 weeks at 30 °C) versus 12 J/g (7 days at 60 °C), and between 95 and 142 °C, they were 12.5 J/g (8 weeks at 30 °C) versus 10 J/g (7 days at 60 °C).
The enthalpies with respect to the temperature ranges indicated that different biodegradation processes occurred at 30 °C and 60 °C. The total enthalpies after compost storage for 7 days at 60 °C of the REF, V1, and V2 were between 31 and 33 J/g. The enthalpies between 20 and 95 °C, as well as between 95 and 142 °C, increased by 60 to 70% with respect to the REF at 30 °C. This shows that new stages of biodegradation were reached in both temperature ranges. The enthalpies between 142 and 170 °C showed that the crystalline PLA seemed to not be subjected to the severe biodegradation at that point.
2.5. Effects of Compost Storage on Mean Molecular Masses
Gel permeation chromatography (GPC) was used to check if molecular degradation has occurred during compost storage, as is shown in
Table 5. The results confirm the earlier findings of MFR measurements [
33] that the CECLs caused cross-linking in the V3 and V4, as their molecular masses (Mn ≈ 75,000 g/mol) are roughly doubled compared to the REF. The REF, V1, and V2 with molecular masses around 44,000 g/mol showed that the CECLs did not significantly change the molecular masses and, as a consequence, the macromolecular structure. Thus, the CECL molecules have to be either grafted to a polymer chain if there are chemical reactions or remain as low molecular components in the polymer matrix. The significantly higher MFR values of the V1 and V2 when compared to the REF in [
33] were explained by chain scission. However, according to the GPC results, as are shown in
Table 5, this cannot be the reason for the higher melt flow rate (MFR) values. This means that the unreacted CECLs in the V1 and V2 have to act as flow agents. The GPC curves of the REF and V1 to V4 showed a single peak, as is shown in
Figure 8, in contrast to double peak chromatograms observed by Fu et al. [
39], which were independent of the PBAT–PLA ratio. The single peak chromatograms can be explained by fact that the height of the pure PBAT peak exceeded by five to six times that of the pure PLA regarding what corresponded to the PBAT–PLA ratio. Thus, the PLA peak remained small and overlaid by the PBAT peak.
Compost storage at 30 °C did not change the molecular mass of the REF, V1, V3, and V4 with respect to the accuracy of the measurement. Only the V2 exhibited further cross-linking with increased molecular masses in the order of 10%. Compost storage at 60 °C led to molecular degradation of the REF and V1 after 7 days, and also to further cross-linking of the V2 in the order of 10%. For the V3 and V4, molecular degradation was neither detected at 30 °C nor at 60 °C.
The GPC results clearly show that, under the given composting conditions, molecular degradation started only after 3 days at 60 °C for the REF and V1. This means that the determined mass losses shown in
Figure 2 and the growth of the hole area have to have been caused by mechanical disintegration towards micro-plasticization.