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Polímeros

versão impressa ISSN 0104-1428versão On-line ISSN 1678-5169

Polímeros vol.28 no.2 São Carlos abr./jun. 2018  Epub 21-Maio-2018

http://dx.doi.org/10.1590/0104-1428.12416 

Original Article

Effect of heat cycling on melting and crystallization of PHB/TiO2 compounds

Nichollas Guimarães Jaques1 

Ingridy Dayane dos Santos Silva1 

Manoel da Cruz Barbosa Neto1 

Andreas Ries2 

Eduardo Luis Canedo3 

Renate Maria Ramos Wellen1  * 

1 Departamento de Engenharia de Materiais, Universidade Federal da Paraíba – UFPB, João Pessoa, PB, Brazil

2 Departamento de Engenharia Elétrica, Universidade Federal da Paraíba – UFPB, João Pessoa, PB, Brazil

3 Departamento de Engenharia de Materiais, Universidade Federal de Campina Grande – UFCG, Campina Grande, PB, Brazil

Abstract

Compounds of poly(3-hydroxybutyrate) (PHB) and titanium dioxide (TiO2) with filler content between 1% and 10% were prepared in a laboratory internal mixer. The effect of heating and cooling rates on the crystallization and melting of PHB/TiO2 compounds was investigated by differential scanning calorimetry (DSC). Melt and cold crystallization rates rise with increasing cooling/heating rates. A higher cooling rate translates to a lower melt crystallization temperature, while a higher heating rate results in a higher cold crystallization temperature. TiO2 promotes melt crystallization of PHB, behaving as a nucleant agent. The total crystallinity developed after melt and cold crystallization decreases for low levels of TiO2, i.e. 2% per weight, and is almost independent of the heating/cooling rate. The melting temperatures and rates are minimally affected by both the heating rate and filler content. The results suggest that the desired PHB microstructure can be controlled by filler content and adjusted heating/cooling rate.

Keywords:  crystallization; DSC; melting; PHB; titanium dioxide

1. Introduction

Polymers are fundamental for most common materials of our modern society because they present several desired features like lightness, easy processability, softness and low cost. As polymers are easily suitable for multiple uses, companies have been using them increasingly in various areas, such as packaging, automotive, medical-hospital, construction, electro-electronics industries among many others. Nevertheless, the production of the most useful polymers is based on fossil fuels. Considered to be non-biodegradable, they need decades to degrade and are an important source of pollution; in particular situations ecological disasters are verifiable. Concerned with the ecological equilibrium in nature, the society has made a lot of efforts to preserve the environment and to improve it where possible.

Engaged with this issue, polymer researchers are seeking answers on how to decrease the use of petroleum based products, thus reducing pollution and toxic volatiles emission. The use of natural and biodegradable polymers appears as good option. Among these polymers, the polyhydroxyalkanoates (PHAs) seem to be a good choice. PHAs are linear aliphatic polyesters produced in nature by bacterial fermentation of sugar or lipids. They are used by the microorganisms to store carbon and energy. Many different monomers can be combined within this family to give materials with different properties. In the present work poly(3-hydroxybutyrate) (PHB) was selected for studying [1-6]. PHB possesses good oxygen permeability and ultra-violet resistance, it is nontoxic and has been used in the packing industry for years; it is biocompatible and hence suitable for medical applications; due to its good mechanical properties and fast biodegradation rates, it has been employed in restaurant disposables, i.e., cups and cutleries. Furthermore, a wide range of additives and polymers may be incorporated to PHB, producing blends and compounds, to improve its performance and to expand its possible applications[7-12].

Few articles are concerned with PHB crystallization and melting behaviour in the presence of fillers. For instance carbon black (CB) and babassu natural fibers induce PHB partial crystallization from the melt during cooling and partial cold crystallization on reheating[13-15]. The amount of polymer crystallization in each stage depends strongly on the cooling rate and the filler content, being the melting subtly affected by the fillers and experiment rates. In a recent study concerned with the influence of Zinc oxide (ZnO) on the PHB crystallization [16] it was found, that ZnO can neither be classified as a crystallization accelerator, nor as a crystallization inhibitor; the influence of zinc oxide on PHB crystallization is irregular and strongly dependent on its concentration, the melting of PHB/ZnO compounds was little modified by ZnO content and heating/cooling rates tested.

To the best of our knowledge, there is not any study in the literature dealing with the melting as well as with the crystallization of PHB/TiO2. From the literature is known that TiO2 could greatly improve the total solar reflectance, thus an appropriate content of TiO2 filler counteracts the thermal and photodegradation of plastics exposed to the sun. Antibacterial activity of TiO2 has been presented in the literature; the packing, textile and health-care industries have successfully used TiO2 in their products with the objective to reduce the risk of microorganism transmission. Adding to the biodegradable nature of PHB this research is dealing with a very promising compound [17-26]. The non-isothermal melt and cold crystallization, and melting processes of PHB/TiO2 nanocompounds were investigated by differential scanning calorimetry (DSC) applying heating/cooling/reheating cycles (six different heating/cooling rates); thermal parameters related to these processes are presented with the main objective to provide a reference of crystallization and melting parameters for these compounds.

2. Materials and Methods

2.1 Materials

Poly(3-hydroxybutyrate) (PHB), a random copolymer with approximately 4% of 3-hydroxyvalerate units, was supplied by PHB Industrial SA (Brazil). Its characteristic thermal transition temperatures are presented in Table 1 . Melt crystallization (Tmc), cold crystallization (Tcc) and melting peak (Tmp) temperatures were obtained during cooling and reheating, according to ASTM D-3418 standard, applying a cooling/heating rate of 10°C/min.

Table 1 Thermal transition temperatures (°C) of PHB obtained by the authors.  

Tg Tmc Tcc Tmp
2 71.9 54.3 172.6

Titanium dioxide (TiO2), was purchased from Evonik Degussa Co. (manufacturer’s specification P25), with a surface area of 50 m2/g and a 75:25 anatase:rutile ratio. According to the manufacturer, the mean crystal sizes of the anatase and rutile phases are approximately 25 and 94 nm, respectively.

2.2 Methods

PHB and TiO2 were used as received. The components were mixed for 10 minutes using a Haake Rheomix 600 laboratory internal mixer fitted with high intensity (roller type) rotors with the chamber wall kept at 190˚C and a nominal rotor speed of 60 rpm. The TiO 2 content ranged from 1% to 10% by weight.

Scanning electron microscopy images were acquired with a LEO 1430 unit, from Zeiss. The polymer samples were fractured in liquid nitrogen to avoid plastic deformation and coated with a carbon layer in order to avoid the accumulation of charges.

Thermal analysis was performed in a TA Instruments DSC Q20 V24.9 differential scanning calorimeter, under a nitrogen flow of 50 mL/min to minimize oxidative degradation, to which the PHB is susceptible [27-29]. Samples of approximately 5 mg were tested in aluminiun pans. A new specimen was used for each run. A blank curve was obtained for each heating/cooling/reheating stage to ensure that no contamination of the instrument had taken place. A thermal cycle of four stages was used: (1) heating from 25˚C to 190˚C (first heating stage); (2) isothermal stage: the samples were held at 190°C for 3 min to eliminate any residual crystallinity and erase the previous thermal history; (3) the melt was cooled to 20˚C (cooling stage) and then (4) reheated to 190˚C (second heating or reheating stage). Tests were conducted at constant heating and cooling rates of 5, 7.5, 10, 15, 20 and 30°C/min.

Figure 1 shows a typical DSC output with the indicated cycles. Four thermal events were identified in most DSC tests. They were denominated as follows: F1: melting during the first heating stage; C1: melt crystallization during cooling; C2: cold crystallization during reheating, and finally F2: a second melting event.

Figure 1 Typical DSC output for PHB/1%TiO2 heating/cooling/reheating at 10°C/min (exothermic peaks up), showing the phase change events: first melting (F1 ), melt crystallization (C1), cold crystallization (C2), and second melting (F2).  

For each thermal event, the starting and end points of departure from the underlying baseline were visually established in a plot of energy flow (J) versus time ( t). The fractional crystallization (or melting) x for the event was computed as a function of time by integration[30]:

x(t)=1E0t1t|J(t)J0(t)|dt (1)

Where: J0 is the virtual baseline during the event (a straight line in the present case), and E0 is the total latent heat of the phase change:

E0=t1t2|J(t)J0(t)|dt (2)

and t1 and t2 are the initial and final times. The rate of the phase change (crystallization or melting) c is:

c(t)=dxdt=|J(t)J0(t)|E0 (3)

from which the peak (maximum) and average crystallization rates may be computed. The fractional crystallization/melting x and the rate of crystallization/fusion c may be expressed as functions of temperature (T) by knowing the linear relationship between time and temperature during the event:

T=T1+ϕ(tt1) (4)

Where: T1 is the sample temperature at the starting point t1, and ϕ is the (constant) rate of heating or cooling during the event. The specific latent heat of crystallization or melting (or enthalpy, because the phase change occurs at constant pressure) is computed from E 0, the polymer fraction wP and the sample mass mS:

ΔH=E0wPmS (5)

The mass crystallinity change ∆Xc during the event is estimated, taking into account the heat of fusion of PHB 100% crystalline:

ΔXc=ΔHΔHm0 (6)

A value of ∆H0m =146 J/g at the equilibrium melting temperature T0 m = 185°C was previously reported in the literature[31].

3. Results and Discussions

Figure 2 presents a SEM image of PHB/10%TiO2; despite the fact that TiO2 nanoparticles were not treated with a surface modifier, SEM image confirms their homogeneous distribution in the PHB matrix.

Figure 2 Scanning electron micrograph of PHB/10%TiO2, as obtained after mixing.  

Figure 3 displays the DSC scans for neat PHB and all PHB-TiO2 compounds for a fixed heating/cooling rate (10°C/min). Four events are recognized: the first melting (A), melt crystallization (B), cold crystallization (C) and the second melting (D).

Figure 3 DSC scans of neat PHB and PHB-TiO2 compounds obtained during the first heating (A), melt crystallization (B), cold crystallization (C) and second melting stages (D) (constant 10°C/min scanning rate).  

As can be seen from Figure 3 , the TiO2 filler has no significant influence on the first melting event (A). Melt crystallization and cold crystallization are the most affected events by the filler.

As TiO2 promotes melt crystallization in a similar way as a nucleant agent, the cold crystallization events vanish, as the crystallization process has been more completed during the melt crystallization event. The higher the filler content, the smaller is the observed cold crystallization peak.

Results gathered from previous works performed with neat PHB, PHB/Babassu, PHB/Carbon black and PHB/ZnO compounds about the influence of heating and cooling rates on PHB phase transition are very similar to these presented in this paper, in general, it is observed that PHB partially crystallizes from the melt during the cooling and partially cold crystallizes on reheating, and that the relative amount of polymer crystallizing in each stage strongly depends on the cooling rate and filler content. Regarding the influence of the fillers, addition of babassu filler in higher concentrations (10 to 50 wt%) increased the crystallization peak temperature and crystallization rate; carbon black acted as a nucleating agent during PHB crystallization. The effect of ZnO on the PHB crystallization is unclear and strongly dependent on its concentration, behaving as an accelerator or an inhibitor upon changing of filler content[13-16].

The second melting events (D) are different from the first melting events (A), a fact that can be seen from the shape of the peaks. Note that the first heating refers to the melting of PHB as obtained some time after processing (fully crystalline phase, no cold crystallization could be observed prior to first melting), whereas the second heating refers to the melting of PHB obtained during the more controlled cooling stage of the experiment. In this stage, the samples had undergone melt crystallization, followed by cold crystallization. During reheating stage, i.e., for the second fusion event (D) all samples showed complex (double) endothermic peaks upon addition of several filler contents: a first small melting peak followed by a larger peak at a higher temperature; this first small peak can also manifest as a shoulder of the larger peak. This behavior is more pronounced when the TiO2 content is high, and the heating rate is lowest (results not shown).

According to the literature[32-42], such double peaks appearing in the fusion region may originate from (1) melting, recrystallization and re-melting during heating, (2) the presence of more than one crystal modification (polymorphism), (3) different morphologies (lamellar thickness, distribution, perfection or stability), (4) physical aging or/and relaxation of the rigid amorphous fraction, or (5) different molecular weight species. Although PHB degradation has been reported in some papers, for instance, PHB/Bentonite Organoclay compounds[43], in this work the degradation of PHB, as investigated by thermogravimetry (TG) (results not shown), was verified occurring at temperatures higher than 270oC, that is, well above the melting range observed in Figure 3 .

Figure 4 presents the development of the relative crystallinity as function of temperature for neat PHB and PHB-TiO2 compounds; the data were obtained from DSC thermal scans. All plots have the sigmoidal shape characteristic of phase transformation in polymers.

Figure 4 Relative crystallinity versus temperature for neat PHB and PHB-TiO2 compounds considering melt crystallization at cooling rate 10°C/min.  

One may observe the displacement of the sigmoid plots in Figure 4 to higher temperatures with increasing TiO2 concentration.

For a given cooling/heating rate and TiO2 content, the melt crystallization peak temperature is higher than the cold crystallization peak temperature, as shown in Figures 5 and 6 . Numerical values are given in Table 2 .

Figure 5 Crystallization peak temperature for melt crystallization of neat PHB and PHB-TiO 2 compounds as a function of filler content and cooling rate.  

Figure 6 Crystallization peak temperature for cold crystallization of neat PHB and PHB-TiO 2 compounds as a function of filler content and heating rate.  

Table 2 Melt and cold crystallization parameters of compounds - Neat PHB. 

Neat PHB
Melt Crystallization Cold Crystallization
ϕ Tmp cmax ΔHm ΔXc Tmp cmax ΔHm ΔXc
(°C/min) (°C) (min−1) (J/g) (%) (°C) (min−1) (J/g) (%)
5 77.2 0.26 44.01 30.1 -- -- -- --
7.5 69.6 0.25 27.81 19.1 50.8 1.06 11.45 7.8
10 71.9 0.31 17.74 12.2 54.3 1.28 21.61 14.8
15 64.0 0.54 5.21 3.6 64.0 1.52 38.66 26.5
20 -- -- -- -- 71.8 1.68 53.56 36.7
30 -- -- -- -- 81.2 1.98 28.20 19.3
PHB + 1%TiO2
Melt Crystallization Cold Crystallization
ϕ Tmp cmax ΔHm ΔXc Tmp cmax ΔHm ΔXc
(°C/min) (°C) (min−1) (J/g) (%) (°C) (min−1) (J/g) (%)
5 84.3 0.27 31.30 21.4 -- -- -- --
7.5 68.8 0.30 26.78 18.3 46.9 1.13 4.21 2.9
10 65.6 0.42 18.81 12.9 49.1 1.49 9.17 6.3
15 63.1 0.57 7.72 5.3 56.3 1.82 34.0 23.3
20 -- -- -- -- 56.3 1.94 31.04 21.3
30 -- -- -- -- 78.0 2.12 51.95 35.6
PHB + 2%TiO2
Melt Crystallization Cold Crystallization
ϕ Tmp cmax ΔHm ΔXc Tmp cmax ΔHm ΔXc
(°C/min) (°C) (min−1) (J/g) (%) (°C) (min−1) (J/g) (%)
5 79.2 0.36 35.99 24.7 -- -- -- --
7.5 76.9 0.43 30.54 20.9 -- -- -- --
10 70.3 0.47 28.49 19.5 -- -- -- --
15 65.3 0.56 20.15 13.8 53.5 1.86 11.90 8.15
20 -- -- -- -- 59.6 2.24 27.08 18.5
30 -- -- -- -- 78.2 1.82 36.92 25.3
PHB + 4%TiO2
Melt Crystallization Cold Crystallization
ϕ Tmp cmax ΔHm ΔXc Tmp cmax ΔHm ΔXc
(°C/min) (°C) (min−1) (J/g) (%) (°C) (min−1) (J/g) (%)
5 86.3 0.43 29.69 20.3 -- -- -- --
7.5 83.2 0.56 31.12 21.3 -- -- -- --
10 77.8 0.68 28.61 19.6 -- -- -- --
15 69.7 0.71 24.12 16.5 52.9 2.69 0.67 0.5
20 66.4 0.86 26.42 18.1 55.0 2.52 6.24 4.3
30 -- -- -- -- 72.5 1.95 15.16 10.4
PHB + 10%TiO2
Melt Crystallization Cold Crystallization
ϕ Tmp cmax ΔHm ΔXc Tmp cmax ΔHm ΔXc
(°C/min) (°C) (min−1) (J/g) (%) (°C) (min−1) (J/g) (%)
5 91.2 0.58 36.52 25.0 -- -- -- --
7.5 87.9 0.78 37.75 25.9 -- -- -- --
10 83.7 0.92 35.56 24.4 -- -- -- --
15 78.3 1.05 30.82 21.1 -- -- -- --
20 72.9 1.21 31.54 21.6 -- -- -- --
30 -- -- -- -- -- -- -- --

The melt crystallization peak temperature ( Figure 5 ) decreases with an increase in the cooling rate and increases with an increase in the filler content.

The melt crystallization peak rates ( Figure 7 ) are proportional to the cooling rate and strongly dependent on the TiO2 content. The cold crystallization temperature ( Figure 6 ) and peak rate ( Figure 8 ) increase with an increase in the heating rate when TiO2 filler concentration is low (up to 1%); their full dependence on filler content is unclear, but in general, the temperature decreases with an increase in the TiO2 content.

Figure 7 Crystallization maximum rate for melt crystallization of neat PHB and PHB/TiO2 compounds as a function of the filler content.  

Figure 8 Crystallization maximum rate for cold crystallization of neat PHB and PHB/TiO2 compounds as a function of the filler content.  

Figure 7 and 8 show the melt and cold crystallization peak rates which increase significantly with increasing filler concentration. This allows to classify titanium dioxide as a crystallization accelerator.

Figure 9 presents the results for the degree of crystallinity, which was computed using Equation 6 . Initially, there is a decrease in the crystallinity for PHB compounds with TiO2 content up to 2%. For higher filler concentrations no trend is observable; results are independent of the heating/cooling rate as well as of the filler content, even considering the high uncertainty of DSC estimates of crystallinity[44]. The observed drop in crystallinity for the highest heating/cooling rate might be explained with a suppressed crystallization under the effect of fast cooling and heating process.

Figure 9 Total crystallinity developed during melt and cold crystallization as function of filler content for several cooling/heating rates.  

4. Conclusions

The cooling and heating rates have a strong influence on the melt and cold crystallization of PHB and its compounds with titanium dioxide. Increasing the cooling rate results in lower melt crystallization temperatures and promotes higher crystallization rates. Both, cold crystallization rates and cold crystallization peak temperatures increase with the heating rate. The addition of titanium dioxide accelerated the melt crystallization, suggesting TiO2 as a nucleant agent for PHB. The total crystallinity as obtained after melt and successive cold crystallization, decreases for low levels of TiO2, i.e., less than 2% per weight, and it is quite independent of the heating/cooling rate after that. The melting temperatures and rates are minimally affected by both the heating rate and filler content. Summing up, controlling the cooling and heating rates as well as adding TiO2 makes PHB crystallization changeable, and consequently its processing parameters, thus a cost-effective processing may be tailored.

5. Acknowledgements

Authors would like to thank PHB Industrial SA (Brazil) for kindly supplying PHB resin. NGJ, IDSS and MCBN thank CNPq for their scholarships.

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Recebido: 10 de Outubro de 2016; Revisado: 20 de Julho de 2017; Aceito: 27 de Julho de 2017

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