Qian Xing*a,
Zefan Wangb,
Rongbo Lic,
Xia Dong*b and
Dujin Wangb
aSchool of Materials Science and Mechanical Engineering, Beijing Technology and Business University, Beijing 100048, PR China. E-mail: qxing@iccas.ac.cn; Tel: +86-10-68985337
bBeijing National Laboratory for Molecular Sciences, CAS Key Laboratory of Engineering Plastics, Institute of Chemistry, Chinese Academy of Sciences, Beijing 100190, PR China. E-mail: xiadong@iccas.ac.cn; Tel: +86-10-82618533
cPetrochina Petrochemical Research Institute, Beijing 102206, PR China
First published on 28th November 2016
Tetramethylenedicarboxylic di-(2-hydroxybenzohydrazide) (TMBH) has been proved to be an effective nucleating agent for poly (L-lactide) (PLLA). The correlation between the solubility of TMBH in a PLLA melt during the annealing treatment and its nucleating efficiency has been systematically investigated. The phase diagrams of the binary system consisting of PLLA and TMBH were constructed by differential scanning calorimetry and polarized optical microscopy. Depending on the annealing temperature (Tf) and TMBH concentration (CTMBH), TMBH may remain crystallites, or partially/completely dissolve into a PLLA melt, which greatly affected the crystallization kinetics and crystalline morphology of PLLA. When Tf was relatively lower and/or TMBH concentration was higher, TMBH crystallites remained solid in the PLLA melt after annealing treatment (e.g. Tf@180 °C and CTMBH@1 wt%), which could effectively enhance the crystallization rate and nucleation density of PLLA. The solubility of TMBH in the PLLA melt would be increased gradually with the increase of Tf and/or the decrease of CTMBH, e.g. TMBH would be partially dissolved into the PLLA melt for TMBH-1 at 200 °C. Furthermore, TMBH would be completely dissolved into the PLLA melt as Tf was raised to 230 °C with CTMBH ranging from 0.1 to 1 wt%. In this case, the soluble TMBH molecules would assemble into rod-like structures with lower specific area during the cooling process, which decreased the nucleating efficiency of TMBH and produced rod-like PLLA crystallites.
The crystallization rate of PLLA is so slow that it even remains amorphous after processing, resulting in a long processing cycle as well as poor heat resistance and dimensional stability. It has been proved that the addition of suitable nucleating agents has been one of the most effective manners to enhance the crystallization ability of PLLA. The generally adopted nucleating agents are inorganic fillers, such as talc, graphene oxide and carbon nanotubes; or macromolecular nucleators like poly(D-lactic acid) and polycaprolactone.9–18 On the other hand, some low molecular weight organic compounds, such as orotic acid, cyanuric acid and amides, have also been selected to nucleate the crystallization of PLLA.19–26 We have also investigated and conformed that the amide and hydrazide compound can efficiently improve the crystallization rate of PLLA.27,28 With respect to inorganic additives, these organic compounds are inclined to disperse more homogeneously in PLLA matrix, since they may show some solubility in PLLA melt. The solubility of the organic compounds during annealing treatment is primarily dependent on the final melting temperature and its concentration, and is critical to the following dispersion state and nucleating effect of the organic compounds during the cooling stage.24,29–33 It should be pointed out that as the temperature decreases some soluble organic compounds can crystallize and assemble into multiple superstructures with different nucleating efficiency. Varga et al. have found that the nucleating agent, N,N′-dicyclohexyl-2,6-naphthalenedicarboxamide (NJS), may partially or completely dissolve in iPP melt based on the final temperature of heating (Tf) and the initial concentration.32 These factors combining with the thermal conditions during cooling and crystallization could induce iPP to form different supermolecular structure such as needle, dendritic and microcrystalline structures as well as a spectacular “flower”-like agglomerate. Additionally, a dual nucleating effect can be observed which results from the partial α-nucleating ability of the lateral surface of NJS needle crystals. The previous researches mainly concentrated on the effect of the solubility of a nucleating agent on the crystallization behavior of iPP. Bai et al. selected TMC-328 (N,N′,N′′-tricyclohexyl-1,3,5-benzenetricarboxylamide) to tailor the crystallization rate and the crystalline superstructure of PLLA.24 They found that TMC-328 can be completely dissolved in PLLA melt at the annealing temperature 200 °C, and self-organize into fine fibrils prior to PLLA crystallization during the cooling process, resulting in the formation of three superstructures of PLLA crystals, including cone-like, shish-kebab like, and needle-like structure.
It has been extensively confirmed that the physical/mechanical properties and end-use performance of semi-crystalline polymer are strongly dependent on its crystallization behavior.33–36 Therefore, the realization of effective control on the crystallization rate and crystal structure of semi-crystalline polymer seems very important. Recently, the low molecular weight hydrazide compound tetramethylenedicarboxylic disalicyloylhydrazide (TMBH) has been proved to be a very promising nucleating agent for PLLA.27,37 However, no attention has been paid to the dissolution state of TMBH in PLLA melt and its effect on the subsequent crystallization behavior of PLLA though it is very important for the macroscopic performance. In present study, a series of PLLA/TMBH composites were prepared through melt blending and the phase diagram of these binary systems was constituted. Both the final annealing temperature and the TMBH concentration were adjusted to mediate the dissolution state of TMBH. The subject of this paper is to perform a more detailed study on how the solubility of TMBH in PLLA melt affects the crystallization rate and crystal structure of PLLA, which may provide theoretical guidance for the selection of processing temperature of PLLA/TMBH composites to obtain high performance biodegradable materials.
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Fig. 1 DSC curves of neat PLLA and its TMBH composites: (a) cooling curves at 5 °C min−1, (b) heating curves at 10 °C min−1. |
POM images for the crystalline structure evolution of PLLA during the non-isothermal crystallization are shown in Fig. 2 and 3. It can be seen from Fig. 2 that TMBH crystallites have dissolved into PLLA melt completely after heating to 200 °C for 5 min when TMBH content was less than 1 wt%. In contrast, for TMBH-1, the loading of TMBH was so high that the particles only partially dissolved into PLLA melt with the existence of some TMBH crystallites. Consequently, the crystalline structure of PLLA varied with the solubility of TMBH in different PLLA/TMBH composites. There were not any PLLA crystals detected in neat PLLA and TMBH-0.1 during the cooling process, indicating the poor nucleation ability of neat PLLA and low content of TMBH. As the TMBH content increased to 0.3 wt%, TMBH crystallized from the melt and formed small crystallites prior to PLLA, which enhanced the nucleation density and crystallization rate of PLLA effectively. When TMBH content reached 0.5 wt%, TMBH could self-assemble to rod-like structure and then induce the epitaxial crystallization of PLLA. Additionally, for TMBH-1, the preexisting TMBH crystallites in PLLA melt can serve as heterogeneous nucleating sites for PLLA, resulting in the formation of a variety of small PLLA crystals.
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Fig. 2 POM images for the crystalline structure variation of neat PLLA and its TMBH composites during the cooling scan from 200 to 60 °C at 5 °C min−1. |
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Fig. 3 POM images for the crystalline structure variation of neat PLLA and its TMBH composites during the heating scan from 60 to 200 °C at 10 °C min−1. |
The crystalline structure development of neat PLLA and its TMBH composites in the following heating process is shown in Fig. 3. The visual field of neat PLLA still remained dark at 120 °C, whereas some tiny crystallites have been formed at 140 °C. For TMBH-0.1, it is obvious that tiny PLLA crystals have emerged at 120 °C and filled the whole visual field at 140 °C. On the other hand, the existing PLLA crystals in TMBH-0.3, TMBH-0.5 and TMBH-1 coarsened gradually with the increase of temperature from 60 to 140 °C and consequently the visual field became much brighter. This indicates that TMBH can also accelerate the occurrence of cold crystallization of PLLA. Based on the above results, it can be concluded that the nucleation density and crystalline structure of PLLA crystals are directly related to the dissolution and dispersion state of TMBH in PLLA matrix.
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Fig. 4 Temperature/composition diagrams of PLLA/TMBH binary systems: (a) crystallization temperature, (b) melting temperature. The denotation L refers to liquid, S to solid, T to TMBH, and P to PLLA. |
Thereby, TMBH crystallites form certain structures in the polymer-rich liquid, which could serve as effective nucleating sites for the subsequent crystallization of PLLA. Under the same annealing temperatures, the dissolution degree of TMBH varies with the changes of TMBH concentration in different PLLA/TMBH composites (Fig. 4b). It's notable that both the crystallization temperature and melting temperature of TMBH increase gradually with the increase of TMBH loadings. That is to say that the easier TMBH dissolves into PLLA melt, the lower its content is. It's expected that the dissolution state of TMBH would affect its assembled structure and nucleating effect on PLLA.
DSC curves of PLLA/TMBH composites after annealing at different temperatures are shown in Fig. 5. The characteristic crystallization and melting parameters are summarized in Table 1. It's known from Fig. 4b that the complete dissolution temperature of TMBH in TMBH-0.3 is around 180 °C. Therefore, TMBH crystallites could completely dissolve into PLLA melt under the tested annealing temperatures. The soluble TMBH molecules would crystallize around 139 °C forming tiny crystallites during the cooling process, and thus behave as heterogeneous nucleating agent accelerating the crystallization of PLLA effectively. The crystallization parameters of PLLA, including crystallization temperature (Tc), crystallization enthalpy (ΔHc), cold crystallization temperature (Tcc), cold crystallization enthalpy (ΔHcc) and relative crystallinity (Xc, Xcc), vary very little for TMBH-0.3 after annealing at different temperatures. This is mainly ascribed to the complete dissolution and homogeneous dispersion of TMBH in PLLA melt, which produces the equivalent influence on its nucleating effect.
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Fig. 5 DSC curves of PLLA/TMBH composites after annealing treatment at different temperatures: (a1, b1, c1) cooling curves at 5 °C min−1, (a2, b2, c2) heating curves at 10 °C min−1. |
Samples | Tf (°C) | Melt crystallization | Cold crystallization | ||||
---|---|---|---|---|---|---|---|
Tc (°C) | ΔHc (J g−1) | Xc (%) | Tcc (°C) | ΔHcc (J g−1) | Xcc (%) | ||
Neat PLLA | 180 | — | — | — | 130.2 | 3.3 | 3.5 |
200 | — | — | — | 130.1 | 3.0 | 3.2 | |
230 | — | — | — | 130.4 | 3.4 | 3.7 | |
TMBH-0.3 | 180 | 99.5 | 12.5 | 13.4 | 109.3 | 12.7 | 13.6 |
200 | 99.7 | 15.7 | 16.9 | 107.8 | 13.3 | 14.3 | |
230 | 100.4 | 13.0 | 14.0 | 111.0 | 12.6 | 13.5 | |
TMBH-0.5 | 180 | 103.2 | 22.2 | 23.8 | 111.0 | 5.8 | 6.2 |
200 | 98.6 | 10.2 | 11.0 | 110.3 | 14.4 | 15.5 | |
230 | 98.6 | 9.7 | 10.4 | 110.7 | 14.6 | 15.7 | |
TMBH-1 | 180 | 107.8 | 24.1 | 25.9 | — | — | — |
200 | 99.4 | 14.0 | 15.0 | 111.0 | 12.5 | 13.4 | |
230 | 97.7 | 7.9 | 8.5 | 111.8 | 15.8 | 17.0 |
In the case of TMBH-0.5, the dissolution temperature of TMBH in PLLA melt is around 195 °C (Fig. 4b). Therefore, TMBH crystallites could not dissolve in PLLA melt and still remain solid state if Tf is selected at 180 °C. These preexisting TMBH particles could act as efficient nucleating sites induce the crystallization of PLLA at 103.2 °C with the crystallization enthalpy of 22.2 J g−1. The solubility of TMBH would increase gradually with the annealing temperature and finally the TMBH crystallites would completely dissolve in PLLA melt as the value of Tf raised to 200 or 230 °C. As a consequence, the rearrangement and reassemble of the soluble TMBH molecules would occur before nucleating the crystallization of PLLA during the cooling process. This may result in the formation of PLLA crystals with certain superstructure and decrease the crystallinity and crystallization temperature of PLLA. Otherwise, in the subsequent heating scan, the phenomenon of cold crystallization begins at lower temperatures if annealed at 200 or 230 °C, while releases much higher cold crystallization enthalpy. As the content of TMBH achieves 1 wt%, it becomes more difficult for TMBH to dissolve in PLLA melt. PLLA crystallites can only partially dissolve in PLLA matrix even annealing at 200 °C. In the cooling process after annealing at 180 °C, TMBH particles in TMBH-1 could provide more active nucleating surfaces for PLLA than TMBH-0.5, and thus PLLA crystallizes at a higher temperature with higher crystallization enthalpy. Otherwise, the values of Tc and Xc decrease obviously after annealing at 200 and 230 °C, indicating the decrease of nucleating efficiency of TMBH. It can be seen that for both TMBH-0.5 and TMBH-1 the nucleating effect of TMBH decreases gradually with the increase of its solubility and annealing temperatures. However, the cold crystallization behavior in the following heating process shows an opposite tendency. That is to say that the insoluble TMBH particles during the annealing treatment exhibit better nucleating effect in the cooling stage, whereas the soluble TMBH particles show better nucleating ability on cold crystallization in the heating stage. The solubility of TMBH in PLLA melt and its nucleating efficiency show great dependence on both the annealing temperature and the concentration of TMBH. The dissolution extent of TMBH increases with the annealing temperature and decreases with the increase of TMBH content.
For TMBH-0.3, the nucleating ability of TMBH is similar to each other after annealing at 180, 200 or 230 °C, since TMBH can completely dissolve in PLLA melt at these temperatures. The crystalline structure evolution of PLLA during the non-isothermal crystallization is equivalent to that annealed at 200 °C (Fig. 2 and 3). Therefore, the following section mainly focuses on crystalline evolution of TMBH-0.5 and TMBH-1.
The influence of annealing temperature on the crystalline structure evolution of TMBH-0.5 during the non-isothermal crystallization is shown in Fig. 6. Some bright particles can be observed in POM images during the annealing at 180 °C, indicating the existence of TMBH crystallites. These tiny crystallites can enhance the crystallization rate and nucleating density of PLLA as effective heterogeneous nucleating sites, and large amounts of PLLA crystallites have formed until the temperature decreases to 110 °C. As Tf increased to 200 or 230 °C, the visual fields still remain dark after the annealing treatment, indicating that TMBH crystallites have dissolved into PLLA melt completely. The soluble TMBH molecules would self-assemble into rod-like crystals with the gradual decrease of temperature, which then induce the epitaxial crystallization of PLLA. The PLLA crystals replicate the rod-like structure of TMBH with length of tens of microns. It's notable that the nucleating efficiency of soluble TMBH is lower than the insoluble TMBH because of the self-assembly and the decrease of specific area of TMBH. As the temperature decreased to 60 °C, the brightness of the visual fields and the crystal density decrease obviously with the increase of annealing temperature from 180 to 230 °C.
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Fig. 6 POM images for the crystalline structure variation of TMBH-0.5 during the cooling scan from different annealing temperatures to 60 °C at 5 °C min−1. |
The crystalline structure variation of TMBH-0.5 in the following heating process is shown in Fig. 7. It can be seen that the existing PLLA crystals become much brighter with the increase of the temperature from 90 to 140 °C. Especially, the coarsening of the rod-like structure of PLLA crystals seems more significant for samples annealed at 200 or 230 °C. This reveals that the cold crystallization of PLLA has been promoted by the addition of TMBH, and the crystalline structure is greatly dependent on the solubility of TMBH under different annealing temperatures.
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Fig. 7 POM images for the crystalline structure variation of TMBH-0.5 during the heating scan from 90 to 140 °C at 10 °C min−1. |
POM images for the crystalline structure evolution of TMBH-1 under the same thermal treatment are shown in Fig. 8 and 9. For TMBH-1, it has been proved that TMBH crystallites cannot dissolve in PLLA melt completely until annealed at 210 °C. Therefore, large amounts of TMBH crystallites can be distinguished during the in situ observation at 180 °C and they provide large numbers of nucleating sites for PLLA. This effectively promotes the crystallization rate and nucleating density of PLLA with the formation of very tiny crystallites. As the annealing temperature increased to 200 °C, TMBH begins to partially dissolve into PLLA and only the insoluble TMBH particles can be observed in the POM image. In this case, the crystallization rate and nucleation density of PLLA are lower than that annealed at 180 °C when cooled to the same temperature (e.g. 110 °C). In contrast, TMBH can totally dissolve into PLLA melt during the annealing at 230 °C, and then self-assemble to rod-like crystalline structure during the cooling stage. Herein, the size of rod-like TMBH crystals seems larger than that of TMBH-0.5 when cooled to 110 °C, which decreases the nucleating density of PLLA crystals. It is evident that the nucleating efficiency of TMBH is in inverse proportion to its solubility due to the time-consumed self-assemble process and the smaller specific area at higher annealing temperature.
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Fig. 8 POM images for the crystalline structure variation of TMBH-1 during the cooling scan from different annealing temperatures to 60 °C at 5 °C min−1. |
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Fig. 9 POM images for the crystalline structure variation of TMBH-1 during the heating scan from 90 to 140 °C at 10 °C min−1. |
The crystalline structure development of TMBH-1 in the heating process is shown in Fig. 9. The nucleating effect of TMBH on the crystallization of PLLA is efficient in the cooling stage after annealing at 180 °C and the cold crystallization of PLLA almost cannot be detected with the increase of temperature. Correspondingly, the crystalline structure varies very little. When Tf increased to 200 and 230 °C, the birefringence phenomenon of PLLA crystals becomes stronger gradually and the visual fields become brighter, indicating the occurrence of cold crystallization. Especially, for sample annealed at 230 °C, the pre-forming rod-like structure of PLLA crystals would continue to grow and coarsen as the temperature increased to 120 °C, while some tiny crystals are also nucleated and formed. Finally, in the visual field at 140 °C, there are mainly two kinds of PLLA crystals, i.e. rod-like structure and tiny crystallites. It can be noted that the crystallization of PLLA after annealed at 200 or 230 °C cannot be completed during the cooling process and the molecular chains arrange regularly into the crystal unit cell in the following heating process.
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Fig. 11 POM images of PLLA isothermally crystallized at 125 °C for 90 min quenched from different annealing temperatures. |
DSC traces of PLLA/TMBH composites isothermally crystallized at 125 °C are compared in Fig. 12. The well-known Avrami equation was employed to analyze the isothermal crystallization kinetics (eqn (1) and (2)):39,40
1 − Xt = exp(−Ktn) | (1) |
ln[−ln(1 − Xt)] = ln![]() ![]() ![]() | (2) |
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Fig. 12 DSC curves (a1, b1, c1) and the corresponding Avrami plots (a2, b2, c2) for PLLA/TMBH composites isothermally crystallized at 125 °C after annealing at different temperatures. |
Samples | Tf (°C) | n | ln![]() |
t1/2 (min) |
---|---|---|---|---|
TMBH-0.3 | 180 | 3.8 | −8.4 | 7.9 |
200 | 3.5 | −7.7 | 8.0 | |
230 | 3.5 | −7.8 | 8.2 | |
TMBH-0.5 | 180 | 3.5 | −8.2 | 9.4 |
200 | 3.9 | −9.3 | 10.1 | |
230 | 3.9 | −9.2 | 10.0 | |
TMBH-1 | 180 | 3.0 | −5.8 | 6.3 |
200 | 3.6 | −8.7 | 10.0 | |
230 | 3.8 | −9.6 | 11.4 |
It has been known that for TMBH-0.3, TMBH can dissolve into PLLA melt completely under all the investigated temperatures. As a result, the pre-forming TMBH crystallites during the cooling process show the similar nucleating ability on the isothermal crystallization of PLLA at 125 °C. The value of t1/2 is around 8 min for all the TMBH-0.3 samples even though they were annealed at different temperatures. For TMBH-0.5, the crystallization half-time is relatively shorter for that annealed at 180 °C, since the nucleating efficiency of TMBH decreases due to the formation of rod-like structure after annealing at 200 or 230 °C. In the case of TMBH-1, the insoluble TMBH crystallites during the annealing at 180 °C exhibit the best nucleating effect on the isothermal crystallization of PLLA. Additionally, the solubility of TMBH increases gradually with the annealing temperature, which decreases the nucleating efficiency of TMBH and prolongs the overall crystallization time of PLLA. Obviously, the nucleating efficiency of TMBH on the isothermal crystallization of PLLA is also closely related to its dissolution state during the annealing treatment. It can be seen that the crystallization rate of PLLA increases with TMBH content if TMBH remains insoluble in PLLA melt, whereas decreases with TMBH content if TMBH totally dissolved into PLLA melt.
For TMBH-1, the state of TMBH in PLLA melt changes from solid to partial and total dissolution with the increase of annealing temperature from 180 to 230 °C. The crystalline structure evolution of TMBH-1 was selected to illustrate the influence of the solubility of TMBH on its nucleating effect during the isothermal crystallization, as shown in Fig. 13. The birefringence phenomenon of TMBH could be clearly observed at 180 or 200 °C, since TMBH crystallites cannot dissolve completely in PLLA melt. Upon cooled to 125 °C, the pre-existing TMBH particles induce PLLA to crystallize quickly and large amounts of tiny PLLA crystallites have emerged after 5 min. It can be noted that PLLA crystallites seems little larger in sample annealed at 200 °C than that at 180 °C. This may be attributed to the self-assemble of the partially dissolved TMBH molecules at 200 °C, which leads to the formation of TMBH crystallites and PLLA crystals with larger size. After annealing at 230 °C, soluble TMBH molecules first self-assemble into rod-like crystallites during cooling to 125 °C and then induce the epitaxial crystallization of PLLA. Comparatively, the crystallization rate and nucleation density of PLLA are much less than that annealed at 180 or 200 °C.
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Fig. 13 POM images of TMBH-1 isothermally crystallized at 125 °C quenched from different annealing temperatures. |
WAXD patterns of PLLA and its TMBH composites fully isothermally crystallized at 125 °C are shown in Fig. 14. The characteristic diffraction peaks of the α form of PLLA crystals locate at 16.7° and 19.1°, corresponding to the crystal plane of (110)/(200) and (203),41,42 respectively. It can be seen that both neat PLLA and its TMBH composites exhibit α form after annealing at 200 °C, while for TMBH-1 PLLA crystals also possess α form under the annealing temperatures. These WAXD patterns reveal that the addition of TMBH and the variation of annealing temperature don't change the conventional form of PLLA crystals.
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