Plasticized Biodegradable Poly ( lactic acid ) Based Composites Containing Cellulose inMicro-and Nanosize

e aim of this work was to study the characteristics of thermal processed poly(lactic acid) composites. Poly(ethylene glycol) (PEG400), microcrystalline cellulose (MCC), and ultrasound-treated microcrystalline cellulose (USMCC) were used in 1, 3, and 5 weight percents to modify the attributes of PLA matrix. e composite �lms were produced by twin screw extrusion followed by �lm extrusion. e manufactured PLA-based �lms were characterized by tensile testing, differential scanning calorimetry (DSC), scanning electron microscopy (SEM), wide angle X-ray diffraction (WAXD), and degradation test.


Introduction
Poly(lactic acid) or PLA is a biobased thermoplastic polyester which can be produced from lactic acid derived from the fermentation of different naturally available polysaccharides.Furthermore, PLA is a biodegradable and compostable plastic with relative good properties compared to the other biodegradable, biobased plastics, thus PLA has got its potential in many applications such as in medical, drug delivery, and textile or packaging applications.However, PLA is too brittle for many applications, soens at relative low temperatures, and has weak water vapor and gas barrier properties compared to commercial polymers.To extend the application �eld the improvement of its properties (barrier, thermal, and mechanical) is required.
Many efforts have been taken to improve the week properties of PLA with different kind of materials including blending/compounding with other polymers, plasticizers, [1][2][3][4] reinforcing materials in micro-(e.g., natural �bers, particles) and nanosize (layered silicates, carbon nanotubes, nanoparticles, or nanocrystals) [5][6][7][8][9].One of the most promising material to improve the properties of the PLA can be the cellulose [10][11][12][13].Cellulose is the most abundant renewable, biodegradable polymer on the Earth, and its properties give a widespread industrial usage.Cellulose bears relatively reactive surface, thus it can be a good choice at producing PLA-based green composites/nanocomposites. Microcrystalline (MCC) and nanocrystalline cellulose can be both applied for improving the properties of PLA.Microcrystalline cellulose is commercially available cellulose nanocrystal, on the other hand it is not yet a commercially available product, but it can be achieved from MCC via acidic hydrolysis and/or ultrasonical (US), hydrodynamical cavitation treatment [14][15][16].It is necessary to mention that processing techniques have a remarkable impact on the adhesion properties of the resulting cellulose in composite/nanocomposite applications [17].Processability and properties of composites or nanocomposites are strongly affected by four main factors, which are characters of the components, composition, interfacial interactions, and structure [18].Using cellulose has got its limitations because cellulose or nanocellulose has a strong sensitivity to water and moisture, when it is dried it may form aggregates and display poor compatibility with the hydrophobic polymeric matrices.e polar surface of cellulose makes difficulties in uniform dispersion in apolar plastics.Although PLA is an apolar synthetic polymer it contains polar groups like C=O as well, which can help the interactions, for example the hydrogen bond formation between cellulose OH and PLA C=O groups [19].Interfacial interactions can be improved by different kind of physical (corona, plasma, laser, or  radiation) and chemical treatments [10].Compatibilizers such as alcene ketene dimmer, maleic-anhydride, phenyltrimethoxysilican, or poly(ethylene glycol) can provide stronger interactions as well.Poly(ethylene glycol) (PEG) can improve the interfacial interactions between PLA and cellulose, the C-O-C, and the O-H of the PEG can form H-bonding or dipolar interactions between matrix and reinforcing material [13].PEG can not only act as compatibilizer but as plasticizer as well thus reducing the brittleness of the PLA.In general, the lower the molecular weight the higher the plasticizing effect [2,20,21].PEGs with lower molecular weights have larger number of hydroxyl groups per mole compared to the PEGs with higher molecular weights.e -OH groups of the PEG chains are believed to develop hydrogen bonds between the polymer and the plasticizer replacing the polymer-polymer interactions [21], [22].Additionally to the higher plasticizing effect of low molecular weight poly(ethylene glycol), PEGs in liquid form can help the uniform dispersion of the cellulose preventing the cellulose feeding difficulties into the extruder during the melt compounding.
In this paper the effects of microcrystalline cellulose with and without ultrasound treatment and PEG 400 on the properties of the poly(lactic acid) produced by melt process were studied.

Experimental
2.1.Materials and Methods.Poly(lactic acid) transparent, extrusion grade granulate was supplied from Shenzhen Bright China Industrial Co. with trade name Esun; microcrystalline cellulose was obtained from Sigma Aldrich in particle size <20 m.Poly(ethylene glycol) was received from Sigma Aldrich and used in liquid form with the average molecular weight of 400.
Since hydrolytic degradation of PLA can appear during the extrusion [23], PLA and MCC were properly dried (at 60 ∘ C for 4 day) prior to all the used processing technologies.e components (microcrystalline cellulose with and ( without ultrasound treatment at 1, 3, and 5 weight percent, poly(ethylene glycol) at 10 weight percent) were mixed in a COLLIN ZK25T four zoned compact laboratory twin screw corotating extruder with a screw speed of 50 rpm, and the temperature pro�le varied from 170 ∘ C at the feeding zone to 190 ∘ C at the die.e composite �lms (Table 1) were prepared on a twin screw extruder (LABTECH Scienti�c twin screw extruder with melt pump and LBRC-150 chill roll cast line) in the thickness of 90-110 microns.PEG400 which is a nontoxic, neutral, nonvolatile, nonirritating material was used as plasticizer, compatibilizer, and as dispersion helper as well.To indicate particle size reduction and to help the dispersion of the cellulose the MCC-PEG suspension was treated in an ultrasonic bath (with dual-frequency unittransducers frequencies of 25 and 75 kHz) for 40 min.To obtain nanosized cellulose chemicals were not used in order to keep the process "green".Control samples were prepared through the above-mentioned processes.were determined.All results presented are the average values of �ve measurements.e thermal properties were determined by differential scanning calorimetry (DSC) using Perkin Elmer DSC 7 calorimeter.Each sample was heated from ambient temperature to 200 ∘ C at a rate of 5 ∘ C/min under inert condition; curves obtained from second heating were analyzed.e degree of crystallinity was calculated from the following (1):

Characterizations
(5) (6) where Δ  and Δ cc are the enthalpy of fusion and crystallization at melting and crystallization temperature, respectively.Δ ∘  is the heat of fusion of a perfect orthorhombic PLA crystal with applying the value of 93.6 J/g.
In order to investigate the microstructure of the samples scanning electron microscopy (SEM) (Hitachi S-3400N) was used.e secondary electron images were taken of the fracture surfaces.e acceleration voltage was 20 kV, and the specimens were coated with gold to avoid charging.
Transmission electron microscopy (TEM) of the ultrathin PLA-based samples was carried out with Jeol JEM-2000EX transmission electron microscope.e acceleration voltage was 120 keV.
Wide-angle X-ray (WAXD) scattering measurements were carried out with a Philips PW1710 diffractometer.WAXD patterns were obtained at room temperature using nickel-�ltered Cu � radiation with generator tension of 50 kV, generator current of 40 mA, and a wavelength of 0.1544 nm, in range of 5-40 ∘ 2.
Degradation test was performed under industrial composting condition with temperature of 58 ∘ C and moisture content of 60 wt%.e test was performed for 45 days.

Results and Discussions
Stress-strain curves of the neat and the modi�ed samples in machine and in cross directions are shown in Figures 1 and  2. According to the results neat PLA showed no necking; it had broken with very little elongation, and it exhibited no or little plastic deformations.On the other hand most of the modi�ed samples containing PEG400 and cellulose showed plastic deformation with yielding.e maximal improvement at machine direction in strain at peak (Figure 4) was 106% (strain was 4.2%) in case of PLA containing 1 wt% USMCC with PEG; at cross section sample with the same composition showed the highest improvement (113%), where the strain was 4.178%.More remarkable improvement was observed in case of strain at break (Figure 5), where samples with UStreated MCC showed signi�cant enhancement at machine and cross directions as one can see in Figures 1 and 2. e strains at break in the machine direction are 303.5, 236.0%, and 183.4% in case of using 1, 3, and 5 wt% of USMCC with 10 wt% of PEG, respectively.e neck which was formed during strain soening extended along these samples, and large amount of cold drawing occurred with little strain hardening.e high srain-to-failure and the high thoroughness were mainly due to void formation which was indicated by stress whitening [24,25] (Figure 6).e microvoids release the plastic constraint in the matrix, triggering large-scale plastic deformations [25].e incorporated particles cavitate in the matrix that adsorbs higher energies (Cotterell [26]) which resulted in improvement of tensile energy absorption (Figure 5).e tensile energy absorption was enhanced almost in every case (excluded samples containing 1 and 5 wt% MCC and PEG400 without ultrasound treatment).e explanation of the higher strain and energy absorption of the samples modi�ed with ultrasound-treated cellulose lies on the fact that the treatment resulted in �ne particles formation.e smaller cellulose particles have got higher surface area which provides the possibility of better adhesion in the interface.Although strain at break was improved, stress at peak (Figure 3), ultimate strength (Figure 4) and Young-modulus (Figure 5) were reduced as expected.
Scanning electron microscopic (SEM) images (Figure 7) were taken of the facture surfaces aer the tensile tests.As the images demonstrate the neat PLA shows rigid broken surface; no plastic regions can be observed.In contrast sample containing PEG 400 shows plastic deformations as well as the other modi�ed samples.MCC particles can be clearly seen in the fracture surfaces, but the dispersion and the distribution are optimal.Although samples with US treatment contain microsized particles, which involves that the size reduction was not complete, other results indicate that the samples contain smaller particles as well.
Aer cutting ultrathin �lms of the composites transmission electron microscopy (TEM) was carried out.In Figure 8 cellulose particles can be seen in the poly(lactic acid) matrix, the less the concentration of the MCC-PEG suspension was the more effective the US treatment became.ere are small particles under 100 nm in the composites containing USMCC.Because of the sensitivity of the PLA to the relative high-acceleration voltage closer images could not be taken.
DSC measurement (Figure 9 and Table 2) was used to characterize the thermal properties of neat PLA, and PLAbased composites.Glass transition temperatures ( g ) of the modi�ed materials were decreased or cannot be observed due to the plasticizer which provided more �exibility to the polymer chains.In the DSC heating scans all PLA and PLA-based samples showed exothermic peak which attributed to the cold crystallization ( cc ).e amorphous part of the modi�ed poly(lactic acid) samples started to form organized structure at lower temperatures ( cc ).Due to the presence of PEG enhanced chain mobility occurred in the amorphous phase, and PLA crystallizes with more ease at lower temperatures.e exothermal cold crystallization peaks are smaller and thinner compared to the neat PLA, but as one can see in some cases the melting peaks are wider indicating higher crystallinity.e melting temperatures did not show notable difference except the difference of the two melting peaks.�hile the neat PLA bears two well-de�ned individual peaks, the �rst melting peaks of the composites are not so strong, and they shied to lower temperatures.e two melting peaks of neat PLA can be due to the coexistence of two kind of crystalline structure or because of the melting behavior with melt recrystallization model [27,28] or due to the dual lamellae population [28].e smaller peaks can indicate that the plasticizer and the additives changed the crystal structure of the PLA (in case of (7) no other peak can be observed).According to the enthalpies and the calculated crystallinity the cellulose may act as nucleating agent especially when untrasonical treatment was used.Pei et al. [29] reported that the nucleating effect is enhanced if homogenous cellulose dispersion in poly(lactic acid) matrix is achieved.is indicates that more homogenous structure was obtained with US treatment which modi�ed the cellulose characteristics as well and probably caused signi�cant size reduction.
e WAXD diffractograms are shown on Figure 10.On Figure 10(a) the WAXD pattern of the neat PLA and MCC, and on Figure 10(b) the WAXD pattern of the composite materials comparing to the neat PLA are presented.e neat PLA shows four main peaks which can be corresponded to the different crystal structures.e peak at 2   ∘ (5.304 Ǻ ) is the peak of homocrystal form, while the other peaks (2   ∘ , 16.7 ∘ , 19.5 ∘ , 24.9 ∘ -9.230 ∘ , 4.564 ∘ , and 3.521 Ǻ , resp.) can be attributed to the stereocomplex crystal form [30,31]. e broad hump shows amorphous nature.In case of MCC the peaks that occurred at 2   ∘ , 22.4 ∘ , 35.00 ∘ (5.676 ∘ , 3.961 ∘ , 2.598 Ǻ ) are corresponding to the cellulose I polymorph structure [11]; a board peak appeared as well at 2   ∘ .e composites (letters mean the same as in the Table 1) show no peaks but broad hump with shoulder (except in case of PLA containing 3 wt% MCC and 10 wt% of PEG where a little peak can be observed at 2   ∘ ).Mathew et al. [11] explains that this phenomenon occurs due to the fast cooling rates during extrusion which indicate low crystallinity.e diffractograms show regular trend in the intensity of the shoulder (later board peak); the higher the MCC content the higher the peak formed around at 2  22 ∘ ; moreover, higher intensity appeared when ultrasound treatment was used, probably due to the higher crystallinity of cellulose caused by the treatment, which degraded some of the amorphous regions in the MCC [15].e intensity of the peak (which can be originated mainly from the PLA crystallinity but from the MCC as well) around 2   ∘ on the other hand does not show any regular trends in intensity change.e degradation rates of modi�ed samples were slightly faster than the rate of neat PLA.For the day 45 all the samples fragmented and became invisible to the naked eyes.During the degradation test scanning electron microscopic images were done.In Figure 11 degradation process can be seen.Aer 14 days white dots appeared on the sample surfaces, which were contributed to the activity of the microorganisms.e SEM images proved that the degradation of PLA was truly biodegradation; the tiny bacteria can be clearly seen in the images.e small dots became small holes as time went by; the holes together formed bigger holes, and �nally the samples fragmented into small, invisible pieces or they totally biodegraded.

Conclusions
During this research MCC, ultrasound-treated MCC, and PEG 400 were used to modify the properties of the PLA.According to the results small amount (1 wt%) of US-treated cellulose in PEG 400 was enough to reduce remarkably the brittleness of the PLA and to create a though material.Slighter improvement occurred when PEG400 or MCC with PEG400 was only used.e thermal properties of the foils did not change signi�cantly except the cold crystallization temperature which shied to lower values attributed to chain mobilizing effect of the plasticizer.e presence of PEG400 and MCC and especially the US-treated MCC indicated higher crystallinity.Although amorphous characteristic was stronger probably due to the fast cooling rates during the �lm extrusion process, XRD results showed enhancement in the crystallinity of cellulose which was attributed to the ultrasound treatment.While SEM images showed that microsized cellulose particles still remained (despite the US treatment) TEM images proved that the size of the particles was reduced remarkably too.Possibly a hybrid of microand nanocomposite was formed.Although further research is needed to improve the compatibility between cellulose and PLA, materials in micro-and nanosize derived from cellulose could play a large role in the improvement of PLA.

F 1 :
Stress-strain curves in machine direction.

F 3 :F 4 :
Stress at peak and strain at peak in machine and in cross directions.Stress at break and strain at break in machine and in cross directions.

F 5 :F 6 :
Young modulus and tensile energy absorption in machine and in cross directions.Optical microscopic images of the stress whitening (a) comparison of nonstressed and stressed regions, (b) closer view of the microvoid formation.T 2: ermal properties measured by DSC.

F 7 :F 8 :
SEM micrographs of the tensile fractured surfaces.�EM images of the modi�ed samples.

F 9 :
DSC curves of neat PLA and PLA-based samples.

F 10 :
Diffraction patterns of MCC, neat PLA, and PLA-based composites.

F 11 :
SEM and photo images of degradation mechanism of PLA �lms under composting condition.