# Development and Characterization of Photoinduced Acrylamide-Grafted Polylactide Films for Biomedical Applications

Authors: Mijanur Rahman; Paiboon Sreearunothai; Pakorn Opaprakasit
Journal: International Journal of Polymer Science
 (2017)

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## Abstract

Surface grafting of biodegradable/biocompatible polylactide (PLA) films by a UV-assisted reaction has been developed by employing a hydrophilic acrylamide (Am) monomer, an N,N′-methylenebisacrylamide (MBAm) cross-linker, and a camphorquinone (CQ)/N,N′-dimethylaminoethylmethacrylate (DMAEMA) photoinitiator/coinitiator system. The accomplishment of the process is confirmed by FTIR and XPS analyses. Physicochemical changes of the grafted PLA films are evaluated in terms of chemical structures, radiation-induced degradation followed by crystallization, morphology, thermal properties, and mechanical behavior. The results reveal that a low degree of PLA degradation through chain scission is observed in both blank and grafted PLA films. This generates more polar chain ends that can further induce crystallization. Results from contact angle measurements indicate that the grafted films have higher hydrophilicity and pH-responsive behavior. The incorporation of PAm on the film’s surface and the induced crystallization lead to improvements in certain aspects of mechanical properties of the films. The materials have high potential for use in biomedical and environmental applications, such as cell culture substrates or scaffolds or pH-sensitive absorbents.


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## Body

## 1. Introduction

Polylactide, PLA, is a versatile aliphatic thermoplastic polyester obtained from renewable sources [1]. The material is immensely attractive for industrial, packaging, agricultural, and biomedical applications, due to its outstanding properties, including biodegradability, biocompatibility, processability (techniques includes, extrusion, injection, blow molding, thermoforming, fiber spinning, or stretching), eco-friendliness (emit low carbon during its production), thermoplastic behavior (good shaping and molding capability), and comparable mechanical properties to petrochemical polymers (comparable to PET and better than PS) [1–4]. The material has been used in a wide range of applications, such as toxic metal adsorption, 3D printing, special coatings, dying, drug delivery system, cell attachment, and proliferation.Despite its advantages, some of its shortcomings, such as poor adhesive properties due to hydrophobic surface, lack of functionality, low surface energy, and lack of side-chain groups for further modifications, make its use inadequate towards some specific applications. Therefore, surface modifications of this polymeric material are needed, which can open the door for those applications by increasing its surface hydrophilicity and functionality.To improve surface adhesion properties of polymeric materials, irradiation and grafting techniques have been reported [5, 6], such as electrical discharge [7], ozonation and grafting [8], plasma treatments and surface grafting [9, 10], and also grafting through microwave [11] and UV irradiation [12]. These covalent grafting processes are very attractive as new desirable functional of different types can be introduced onto the polymer surfaces to change surface morphology, adhesiveness, and biocompatibility. For PLA, some research has been conducted on surface grafting with different materials [13, 14].Polyacrylamide (PAm) is a nontoxic, low cost polymer produced from the radical polymerization of its vinyl monomer. During the synthesis, N,N′-methylenebisacrylamide can be applied to partially cross-link the polymer chains. This polymer shows its strong hydrophilic nature, due to the presence of polar amide groups. The material has been commonly used as a flocculant in water treatment and as a supporting matrix for gel electrophoresis. Recently, its use for grafting modification of hydrophobic surfaces has been widely reported, such as polyacrylamide-g-agar [15], polyacrylamide-g-Nylon 6,6 [16], polyacrylamide-g-chitosan [17], and polyacrylamide-g-graphene [18].It is widely known that photografting of polymers through high-energy irradiation can create adverse effects on the bulk properties of the exposed substrates (e.g., gamma irradiation) [19] and in wet stage grafting (e.g., UV irradiation) [20, 21]. The most common effects are the induction of cross-linking and degradation processes. In the modification of PLA, photodegradation by chain scission was observed [19, 21]. To our knowledge, two studies investigated the grafting of PLA (particles and solution casting films) by acrylamide using benzophenone photoinitiator as a small part of respective full study [22, 23]. However, studies related to the quantitative analysis of the changes in bulk properties occurring during photografting of PLA (compression-molded films) are rare.The main purpose of this work is to develop poly(lactide-graft-acrylamide-co-N,N′-methylenebisacrylamide), P(LA-g-Am-co-MBAm) copolymer films that possess hydrophilic, reactive, and bioactive surfaces, by a UV-light assisted grafting reaction. PAm chains are grafted on and form a partial cross-linked structure by using cross-linker and coinitiator, along with photoinitiator, to speed up the reaction. The surface modification mechanisms and efficiency are characterized. Other physicochemical changes associated with the effect of UV irradiation, initiator, coinitiator, and solvent on the properties of the resulting PLA films are investigated. The materials have high potential for use in biomedical and environmental applications.


## 2. Materials and Methods

### 2.1. Materials

Commercial polylactide, PLA-4043D, was obtained from NatureWorks (USA). Acrylamide (Am) monomer and N,N′-methylenebisacrylamide (MBAm) cross-linker were supplied by Acros (USA). Camphorquinone (CQ) photoinitiator (Esstech, USA) and N,N′-dimethylaminoethylmethacrylate (DMAEMA) coinitiator (Fluka, USA) were used as received. Commercial grade methanol and ethanol solvents (Italmar, Thailand) and deionized water were used throughout the work. All chemicals were used without further purification.


### 2.2. Preparation of PLA Films

PLA films were prepared by using a compression molding machine (Chareontut, Thailand). The PLA pellets were heated up to 190°C and pressed at 2100 PSI for 14 min, followed by air cooling to room temperature, to yield films with an average thickness of 0.22 mm. The films were then cut into pieces (5 × 8 cm2), termed as “neat” PLA film, and stored in a desiccator to avoid moisture absorption until further experiments.


### 2.3. Grafting Polymerization Procedure

A 10% (w/v) monomer solution was prepared by dissolving Am and MBAm at a weight ratio of 19 : 1 in methanol solvent. 0.1 g CQ and 0.1 mL DMAEMA (photoinitiator/coinitiator) were added at a ratio of (Am + MBAm) : CQ : DMAEMA = 100 : 1 : 1. It is noted that although DMAEMA can be used as a reactive monomer for forming of cross-link structures, the reagent was applied in a small amount in this study. Therefore, its possible cross-linking effect is negligible. The solution was sonicated for 1 min at room temperature. A blank solution was prepared by dissolving 0.1 g CQ and 0.1 mL DMAEMA in methanol. Photoactivation of PLA films was carried out by irradiating with UV-C (254 nm) using a UV lamp (ENF-260C/FE, Spectronics Corp., USA) for 20 min at room temperature. Essentially, neat PLA film was placed in a Petri dish and irradiated for 10 min. The film was turned over to equally irradiate the opposite side. The distance from the UV lamp to the film surface was fixed at 2.3 cm.To synthesize P(LA-g-Am-co-MBAm) grafted copolymer film, 20 mL of monomer solution was poured into a Petri dish containing UV-activated PLA film. The whole system was further irradiated for 20 min. The film was, then, washed with DI water and ethanol to remove residual monomer and ungrafted PAm chains. The films, passing through the photoinduced grafting polymerization, are defined as “grafted” PLA film. To perform “blank” experiments, 20 mL “blank” solution, consisting of only CQ and DMAEMA and methanol solvent, was poured into a Petri dish containing UV-activated PLA film, instead of monomer solution. The treated films are defined as “blank” PLA film. An overview of the synthesis process of the copolymer is shown in Figure1.Figure 1
Synthesis route of P(LA-g-Am-co-MBAm).


### 2.4. Characterizations

The average molecular weights and molecular weight distributions of the neat, blank, and grafted PLA films were determined by gel permeation chromatography (GPC), using a Waters 150-CV gel permeation chromatograph. Monodispersed polystyrene was employed as a standard, and THF was used as a solvent, with a flow rate of 1 mL/min. The success of the photoinitiated grafting was verified by Fourier Transform Infrared (FTIR) spectroscopy on a Thermo Scientific Nicolet iS5 FTIR spectrometer equipped with iD5 Attenuated Total Reflectance (ATR) accessory. All spectra were recorded in both transmission and ATR modes, with 64 scans at a 2 cm−1 resolution.X-Ray Photoelectron (XPS) spectroscopy was employed to characterize the chemical compositions of the surface. The measurements were performed on a PHI 5000 Versa Probe IIXPS system (ULVAC-PHI, Japan) with Al K radiation as the excitation source at the Synchrotron Light Research Institute (SLRI), Nakhon Ratchasima, Thailand. Contact angle measurements were performed to examine the degree of hydrophilicity of the film surfaces, through deionized water droplets at 3 pH values: 4, 7, and 10 by adapting the method of Stalder et al. [24]. The digital images of water droplets were processed with the ImageJ software, using the DropSnake plug‐in (Biomedical Imaging Group, EPFL). At least 10 replicates were measured for each film sample.X-ray diffraction spectroscopy (XRD) was conducted on the films for their crystalline content analysis. The measurements were conducted on a JEOL JDX-3530 diffractometer, using a monochromatic Cu Kα X-ray source at 40 kV and 30 mA. The samples were scanned from 2θ of 4–40°, with a 0.02 step size. Thermal behavior of the films was observed by Differential Scanning Calorimetry (DSC) on a DSC822e Mettler Toledo instrument. The samples were scanned with a double cycle from −20 to 170°C at a heating/cooling rate of 10°C/min, under N2 atmosphere.Cross-sectional topographies of the films were examined by Scanning Electron Microscopy (SEM) using a Hitachi SU8000 scanning microscope. The films were broken with the aid of liquid nitrogen. The samples were dried in a vacuum oven at 40°C overnight and sputter-coated with a 10 nm gold layer. Tensile properties of the film samples were examined using a universal tensile machine (Tinius Olsen: H5K-T UTM), according to ASTM D882-10, with a crosshead speed of 50 mm/min, using rectangle shaped specimens with 50 mm gauge length and 15 mm width. Prior to tensile testing, film specimens were conditioned in a vacuum oven at 25°C for 24 h. Data were taken from averaged values of at least 10 specimens for each sample.


## 2.1. Materials

Commercial polylactide, PLA-4043D, was obtained from NatureWorks (USA). Acrylamide (Am) monomer and N,N′-methylenebisacrylamide (MBAm) cross-linker were supplied by Acros (USA). Camphorquinone (CQ) photoinitiator (Esstech, USA) and N,N′-dimethylaminoethylmethacrylate (DMAEMA) coinitiator (Fluka, USA) were used as received. Commercial grade methanol and ethanol solvents (Italmar, Thailand) and deionized water were used throughout the work. All chemicals were used without further purification.


## 2.2. Preparation of PLA Films

PLA films were prepared by using a compression molding machine (Chareontut, Thailand). The PLA pellets were heated up to 190°C and pressed at 2100 PSI for 14 min, followed by air cooling to room temperature, to yield films with an average thickness of 0.22 mm. The films were then cut into pieces (5 × 8 cm2), termed as “neat” PLA film, and stored in a desiccator to avoid moisture absorption until further experiments.


## 2.3. Grafting Polymerization Procedure

A 10% (w/v) monomer solution was prepared by dissolving Am and MBAm at a weight ratio of 19 : 1 in methanol solvent. 0.1 g CQ and 0.1 mL DMAEMA (photoinitiator/coinitiator) were added at a ratio of (Am + MBAm) : CQ : DMAEMA = 100 : 1 : 1. It is noted that although DMAEMA can be used as a reactive monomer for forming of cross-link structures, the reagent was applied in a small amount in this study. Therefore, its possible cross-linking effect is negligible. The solution was sonicated for 1 min at room temperature. A blank solution was prepared by dissolving 0.1 g CQ and 0.1 mL DMAEMA in methanol. Photoactivation of PLA films was carried out by irradiating with UV-C (254 nm) using a UV lamp (ENF-260C/FE, Spectronics Corp., USA) for 20 min at room temperature. Essentially, neat PLA film was placed in a Petri dish and irradiated for 10 min. The film was turned over to equally irradiate the opposite side. The distance from the UV lamp to the film surface was fixed at 2.3 cm.To synthesize P(LA-g-Am-co-MBAm) grafted copolymer film, 20 mL of monomer solution was poured into a Petri dish containing UV-activated PLA film. The whole system was further irradiated for 20 min. The film was, then, washed with DI water and ethanol to remove residual monomer and ungrafted PAm chains. The films, passing through the photoinduced grafting polymerization, are defined as “grafted” PLA film. To perform “blank” experiments, 20 mL “blank” solution, consisting of only CQ and DMAEMA and methanol solvent, was poured into a Petri dish containing UV-activated PLA film, instead of monomer solution. The treated films are defined as “blank” PLA film. An overview of the synthesis process of the copolymer is shown in Figure1.Figure 1
Synthesis route of P(LA-g-Am-co-MBAm).


## 2.4. Characterizations

The average molecular weights and molecular weight distributions of the neat, blank, and grafted PLA films were determined by gel permeation chromatography (GPC), using a Waters 150-CV gel permeation chromatograph. Monodispersed polystyrene was employed as a standard, and THF was used as a solvent, with a flow rate of 1 mL/min. The success of the photoinitiated grafting was verified by Fourier Transform Infrared (FTIR) spectroscopy on a Thermo Scientific Nicolet iS5 FTIR spectrometer equipped with iD5 Attenuated Total Reflectance (ATR) accessory. All spectra were recorded in both transmission and ATR modes, with 64 scans at a 2 cm−1 resolution.X-Ray Photoelectron (XPS) spectroscopy was employed to characterize the chemical compositions of the surface. The measurements were performed on a PHI 5000 Versa Probe IIXPS system (ULVAC-PHI, Japan) with Al K radiation as the excitation source at the Synchrotron Light Research Institute (SLRI), Nakhon Ratchasima, Thailand. Contact angle measurements were performed to examine the degree of hydrophilicity of the film surfaces, through deionized water droplets at 3 pH values: 4, 7, and 10 by adapting the method of Stalder et al. [24]. The digital images of water droplets were processed with the ImageJ software, using the DropSnake plug‐in (Biomedical Imaging Group, EPFL). At least 10 replicates were measured for each film sample.X-ray diffraction spectroscopy (XRD) was conducted on the films for their crystalline content analysis. The measurements were conducted on a JEOL JDX-3530 diffractometer, using a monochromatic Cu Kα X-ray source at 40 kV and 30 mA. The samples were scanned from 2θ of 4–40°, with a 0.02 step size. Thermal behavior of the films was observed by Differential Scanning Calorimetry (DSC) on a DSC822e Mettler Toledo instrument. The samples were scanned with a double cycle from −20 to 170°C at a heating/cooling rate of 10°C/min, under N2 atmosphere.Cross-sectional topographies of the films were examined by Scanning Electron Microscopy (SEM) using a Hitachi SU8000 scanning microscope. The films were broken with the aid of liquid nitrogen. The samples were dried in a vacuum oven at 40°C overnight and sputter-coated with a 10 nm gold layer. Tensile properties of the film samples were examined using a universal tensile machine (Tinius Olsen: H5K-T UTM), according to ASTM D882-10, with a crosshead speed of 50 mm/min, using rectangle shaped specimens with 50 mm gauge length and 15 mm width. Prior to tensile testing, film specimens were conditioned in a vacuum oven at 25°C for 24 h. Data were taken from averaged values of at least 10 specimens for each sample.


## 3. Results and Discussion

### 3.1. GPC Measurements

GPC results reveal a significant effect of UV irradiation on PLA films in the presence of “blank” and monomer solutions. Table1 summarizes the results of molecular weights (MW) of films after the treatment for 40 min. A decrease in MW from a neat PLA film to blank PLA film (around 10%) and to grafted PLA film (roughly 16%) is observed. This is attributed to an increase in the content of low MW fragments, as a result from chain scissions during the treatment.Table 1
GPC results of neat, blank, and grafted PLA films.
Sample
Average molecular weights
M
-
n
M
-
w
PDI
Neat PLA
9.6 × 104
2.0 × 105
2.1
Blank PLA
8.6 × 104
1.7 × 105
2.0
Grafted PLA
8.1 × 104
1.7 × 105
2.1However, no secondary peaks can be observed in GPC chromatograms, as shown in Figure2, and the polydispersity index (PDI) value remains relatively stable, between 2.0 and 2.1. This strongly suggests that chain scissions occur randomly along the chains and confirms that degradation occurs homogeneously through the film thickness.Figure 2
GPC chromatograms of neat (i), blank (ii), and grafted PLA (iii) films.


### 3.2. FTIR Spectroscopy

Chemical structures and chain conformations are characterized by ATR-FTIR spectroscopy. Figure3(a) shows spectra in the characteristic region of O-H and N-H stretching and C=O overtone modes. Sharp bands, located at 3700–3450 cm−1, are associated with overtone combination modes. Difference spectra are also shown to provide clearer spectral changes. A new positive difference band, appearing after the blank and grafting treatments at 3294 cm−1, is due to O-H stretching mode of newly generated -OH and -COOH end groups as a result from partial degradation by UV irradiation. A band at 3383 cm−1, observed only after the grafting treatment, is associated with the N-H asymmetric stretching mode of PAm, which can be used for quantitative measurement of the grafting content. The N-H symmetric stretching mode is overlapped with the stretching band of free O-H groups at around 3213 cm−1. On the difference spectra, N-H symmetric stretching band is located at 3198 cm−1.Figure 3
FTIR (transmission) spectra of neat (i), blank (ii) and grafted PLA (iii) films. Subtracted (difference) FTIR spectra of the corresponding samples are shown on the upper part.
(a)
(b)There is also a positive difference band at 1692 cm−1 (amide I), as shown in Figure 3(b), confirming the presence of the grafted acrylamide chains. An amide II mode is observed as a weak broad band at around 1599 cm−1, while a C-N stretching mode (amide III) appears at 1417 cm−1 in the subtracted spectra of the grafted sample.FTIR spectra recorded in ATR mode in the C-H stretching region are shown in Figure4(a). Neat PLA shows bands at 2995 and 2945 cm−1 of the asymmetric and symmetric stretching of -CH3 groups and at 2880 cm−1 of the stretching mode of -CH groups, whose relative intensities slightly decrease in the blank and grafted samples. After treatments, 2 new bands are developed at 2917 and 2850 cm−1, indicating the presence of new C-H vibrations of LA end groups [25]. This is likely a result from partial degradation and structural changes of PLA chains.Figure 4
FTIR spectra of neat (i), blank (ii), and grafted PLA (iii) films in the C-H stretching vibrational region (a), the C=O stretching vibration region (b), and the skeletal vibration region (c), indicating changes in conformations and crystalline characteristics of the film samples.
(a)
ATR
(b)
ATR
(c)
TransmissionIt is well known that the C=O stretching mode of PLA is sensitive to its structure and chain conformation [26, 27]. The samples subjected to blank and grafting experiments show splitting C=O bands at 1756 and 1746 cm−1, as shown in Figure 4(b), corresponding to a gauche-trans (gt) crystalline conformation and an amorphous structure, respectively [28]. In contrast, a broader single amorphous band is observed in the neat sample. This confirms the formation of crystalline domains after the treatments.In addition, bands at 988 and 809 cm−1 (the out-of-plane bending of N-H), as depicted in Figure 4(c), can also be used to quantitatively confirm the presence of PAm and its content. An amorphous characteristic band at 956 cm−1 shows a decrease in intensity in the blank and grafted films, compared to neat PLA. Simultaneously, a sharp PLA α-crystal’s band appears at 921 cm−1 in the 2 treated films [29, 30]. The results firmly ensure that there is a significant transformation of amorphous phase to crystalline domains, due to conformational changes induced by newly formed -OH and -COOH terminals, as observed in GPC results.


### 3.3. XPS Analysis

XPS spectra of neat PLA and PAm-grafted PLA surfaces are compared. Figures5(a) and 5(b) show 2 strong signals of C1s and O1s for the surfaces of both samples, while a distinct N1s signal of PAm is only observed in the grafted sample [31, 32]. The presence of this signal ultimately indicates the success of the photografting reaction. Figure 5(c) shows 3 bands associated with C-C/C-H, C-O, and O-C=O components, in the C1s region [10]. The relative intensity of the C-C/C-H component increases as a result from the grafting reaction, while those of the other 2 bands of C-O, O-C=O components decrease. This is because the incorporation of PAm on the PLA surface leads to a decrease in relative contents of ester C-O and O-C=O, but an increase in the C-C/C-H composition [33, 34]. The corresponding O1s signals, as shown in Figure 5(d), reflect the surface contents of O-C=O and C-O groups [35]. Both signals show a decrease in intensities from neat PLA to the grafted film, because of a dilution effect from the presence of PAm. The existence of amide oxygen, N-C=O, is visible as a weak shoulder, located at the lower energy region of the O-C=O band of the grafted film. This is also confirmed by an appearance of the distinct signal of N1s, as shown in Figure 5(e).Figure 5
XPS spectra of neat (a) and grafted PLA (b) films (full spectra) and expanded scaled spectra in the C1s (c), O1s (d), and N1s (e) regions of neat and grafted PLA films.
(a)
(b)
(c)
(d)
(e)


### 3.4. Surface Properties

Contact angle measurements are used to characterize surface wettability and pH-responsive behavior of the samples. The contact angle (CA) values were measured at 25°C by using water droplets at pH of 4, 7, and 10. The results, as summarized in Figure6, show that neat PLA film has a CA value of 68°, reflecting its slightly hydrophilic nature compared to other polyolefin. Upon treating with “blank” or monomer solutions, the resulting films exhibit lower CA values, indicating higher degree of hydrophilicity. The results confirm that treating PLA films with blank solutions under UV irradiation leads to slight chain scissions and formation of newly generated polar -OH and -COOH end groups and hence an increase in the surface hydrophilicity. Further decrease in the CA value is observed in grafted PLA film, as a result from the presence of both grafted PAm chains and the newly generated PLA polar end groups.Figure 6
Contact angle (CA) values of neat, blank, and grafted PLA films, measured by using water droplets at various pH values.Interestingly, pH-dependent behavior is observed in “blank” and grafted PLA films, whereas the CA values measured at different pH for neat film remain significantly unchanged. The lowest CA values of the 2 treated samples are observed at pH 4, which slightly increase when a neutral solution is employed. However, a sharp increase in the value is obtained when the pH of the water droplet is increased to 10. The results confirm that both treated films have negative polarity surfaces, due to the presence of grafted functional groups and newly generated end groups, as already described. At acidic and neutral pH, interaction between the positively charged species in the water droplet and the negative polarity surface leads to higher wettability. In contrast, at high pH values, the presence of OH− results in strong repulsion of the water droplet and the film surface, reflecting by a higher CA value or lower wettability. In addition, the degree of pH-dependent property also increases from blank to grafted films, due to an increase in the content of surface negative functionalities.


### 3.5. XRD Spectroscopy

Crystalline characteristics of films before and after treatments are examined. It is clearly observed that after blank and grafting processes, the films became opaque (almost completely white), whereas neat PLA film is transparent. This is due to formation of crystalline domains in the films. To verify this and calculate the crystalline contents of the samples, XRD is employed and the diffractograms are shown in Figure7. Neat PLA has almost completely amorphous structure, as a very weak diffraction peak at 2θ = 16.8° is observed. In contrast, 4 characteristic sharp peaks appear in the blank and grafted films at 2θ = 14.9°, 16.7°, 19.1°, and 22.4°, corresponding to (010), (110/200), (203), and (205) planes, reflecting their semicrystalline nature [36, 37]. Results on crystallinity (%) show that the neat sample has only 2% crystalline content, whereas a considerable increase in the values to 35% and 29% is observed in the blank and grafted counterparts. The value for the blank sample is slightly higher than the grafted films, indicating that the grafting of PAm on the film surface may interrupt PLA’s chain arrangement and, hence, lower its degree of crystallinity.Figure 7
XRD diffractograms of neat (i), blank (ii), and grafted PLA (iii) films.


### 3.6. Thermal Properties

Effects of grafting polymerization on thermal properties of the films are investigated by DSC, as presented in Figure8. The glass transition temperature (Tg) and melting temperatures (Tm) of the samples are identified. Double melting endothermic peaks are clearly witnessed in the grafted PLA film (142.7 and 152.7°C), whereas, in the neat (138.7°C) and blank (146.7°C) samples, a single Tm is observed. These split endotherms are associated with two distinct crystalline structures of PLA: disordered imperfect α′ crystalline and ordered perfect α crystalline forms. The lower endotherm Tm(I) is related to the α′ form which is generated under restricted conditions. This form almost simultaneously recrystallizes into α form when the restricted conditions are released. The higher TmII corresponds to the perfect crystals from reorganization and the primary α form. The two processes, the melting of the α′ form and the recrystallization into α form, can be considered as the α′-α phase transition. This phase transition was hindered in the grafted sample, however, due to chain entanglements by PAm on the PLA surface. Subsequently, thickening of the imperfect α′ crystal form occurs.Figure 8
DSC thermograms (1st heating curve) of neat, blank, and grafted PLA films.The degree of crystallinity (Xc) was also calculated from the enthalpy of melting of 1st heating thermograms by comparing with semicrystalline PLA measured at the equilibrium point (93.0 J/g) [38]. The results, as summarized in Table 2, show an increase in the crystalline contents from 2% for neat PLA to 26% for blank and 23% for grafted films. This agrees with those observed in XRD experiments, reflecting a transformation of amorphous PLA structures to crystalline domains during the blank and grafting treatments. The blank and grafted films exhibit slightly higher (64.4°C) and lower (59.0°C) Tg, compared to the intermediate value of neat PLA (62.3°C). Generally,Tg value increases with an increase in crystallinity and decreases with the introduction of plasticizers to the polymer matrix. Although crystalline domains are developed in both the blank and grafted films, the grafted film shows lowerTg. This is likely because the medium-sized grafted PAm chains, which contain a high content of chain ends, can act as a plasticizer for the PLA matrix.Table 2
Thermal properties derived from DSC (1st heating) experiments of neat, blank, and grafted PLA films.
Sample
T
g (°C)
T
m
(
I
) (°C)
T
m
(
I
I
) (°C)
Δ
H
m (J/g)
X
c (%)
Neat PLA
62.3
138.7
153.7
1.36
2
Blank PLA
64.4
146.7
152.7
24.20
26
Grafted PLA
59.0
142.7
152.7
20.98
23


### 3.7. Morphology

The cross-sectional areas of all films are analyzed by SEM to observe morphological changes before and after blank and grafting experiments. SEM micrographs at different magnifications of the blank and grafted films show profound morphological changes, that is, transition from complete amorphous to semicrystalline structures, as observed as white crystalline domains dispersed over the whole cross-sectional area, as shown in Figure9. It is, therefore, concluded that the crystallization mechanisms involve nucleation steps from the initiator, coinitiator, and methanol solvent molecules, which penetrate into the film matrix, and also local induced crystallization by -OH and -COOH chain ends, generated from a low degree of chain scissions.Figure 9
Cross-sectional SEM micrographs of neat, blank, and grafted PLA films at different magnifications.


### 3.8. Mechanical Properties

Mechanical properties of all films are examined by tensile experiments. The properties typically correlate with chemical structures, molecular weights, and crystallinity of polymers. All PLA films exhibit the stress-strain behavior of normal plastic materials, in which yielding is observed before breaking, as shown in Figure10. The tensile strength of the samples shows a slight drop, whereas stress at break exhibits a moderate rise from neat to blank and grafted films. The drops in tensile strength and Young’s modulus are directly related to the partial chain scissions of PLA, which have taken place in both blank and grafted films. Although enhancement of crystallinity in those 2 films is observed, the effect of molecular weights reduction overwhelmed the crystalline effect in this case.Figure 10
Stress-strain curves (a) and Young’s modulus and elongation at break values (b) of neat, blank, and grafted PLA films.
(a)
(b)In contrast, the elongation at break of the 2 treated samples increases sharply, compared to neat film. This can be explained in terms of a toughening effect from the presence of crystalline domains, which act as physical cross-links holding the chains before rapture. Moreover, the grafted PLA film exhibits a higher elongation at break value than the blank film. This is likely because of the presence of slightly cross-linked P(Am-co-MBAm) grafted chains on the film surface.


## 3.1. GPC Measurements

GPC results reveal a significant effect of UV irradiation on PLA films in the presence of “blank” and monomer solutions. Table1 summarizes the results of molecular weights (MW) of films after the treatment for 40 min. A decrease in MW from a neat PLA film to blank PLA film (around 10%) and to grafted PLA film (roughly 16%) is observed. This is attributed to an increase in the content of low MW fragments, as a result from chain scissions during the treatment.Table 1
GPC results of neat, blank, and grafted PLA films.
Sample
Average molecular weights
M
-
n
M
-
w
PDI
Neat PLA
9.6 × 104
2.0 × 105
2.1
Blank PLA
8.6 × 104
1.7 × 105
2.0
Grafted PLA
8.1 × 104
1.7 × 105
2.1However, no secondary peaks can be observed in GPC chromatograms, as shown in Figure2, and the polydispersity index (PDI) value remains relatively stable, between 2.0 and 2.1. This strongly suggests that chain scissions occur randomly along the chains and confirms that degradation occurs homogeneously through the film thickness.Figure 2
GPC chromatograms of neat (i), blank (ii), and grafted PLA (iii) films.


## 3.2. FTIR Spectroscopy

Chemical structures and chain conformations are characterized by ATR-FTIR spectroscopy. Figure3(a) shows spectra in the characteristic region of O-H and N-H stretching and C=O overtone modes. Sharp bands, located at 3700–3450 cm−1, are associated with overtone combination modes. Difference spectra are also shown to provide clearer spectral changes. A new positive difference band, appearing after the blank and grafting treatments at 3294 cm−1, is due to O-H stretching mode of newly generated -OH and -COOH end groups as a result from partial degradation by UV irradiation. A band at 3383 cm−1, observed only after the grafting treatment, is associated with the N-H asymmetric stretching mode of PAm, which can be used for quantitative measurement of the grafting content. The N-H symmetric stretching mode is overlapped with the stretching band of free O-H groups at around 3213 cm−1. On the difference spectra, N-H symmetric stretching band is located at 3198 cm−1.Figure 3
FTIR (transmission) spectra of neat (i), blank (ii) and grafted PLA (iii) films. Subtracted (difference) FTIR spectra of the corresponding samples are shown on the upper part.
(a)
(b)There is also a positive difference band at 1692 cm−1 (amide I), as shown in Figure 3(b), confirming the presence of the grafted acrylamide chains. An amide II mode is observed as a weak broad band at around 1599 cm−1, while a C-N stretching mode (amide III) appears at 1417 cm−1 in the subtracted spectra of the grafted sample.FTIR spectra recorded in ATR mode in the C-H stretching region are shown in Figure4(a). Neat PLA shows bands at 2995 and 2945 cm−1 of the asymmetric and symmetric stretching of -CH3 groups and at 2880 cm−1 of the stretching mode of -CH groups, whose relative intensities slightly decrease in the blank and grafted samples. After treatments, 2 new bands are developed at 2917 and 2850 cm−1, indicating the presence of new C-H vibrations of LA end groups [25]. This is likely a result from partial degradation and structural changes of PLA chains.Figure 4
FTIR spectra of neat (i), blank (ii), and grafted PLA (iii) films in the C-H stretching vibrational region (a), the C=O stretching vibration region (b), and the skeletal vibration region (c), indicating changes in conformations and crystalline characteristics of the film samples.
(a)
ATR
(b)
ATR
(c)
TransmissionIt is well known that the C=O stretching mode of PLA is sensitive to its structure and chain conformation [26, 27]. The samples subjected to blank and grafting experiments show splitting C=O bands at 1756 and 1746 cm−1, as shown in Figure 4(b), corresponding to a gauche-trans (gt) crystalline conformation and an amorphous structure, respectively [28]. In contrast, a broader single amorphous band is observed in the neat sample. This confirms the formation of crystalline domains after the treatments.In addition, bands at 988 and 809 cm−1 (the out-of-plane bending of N-H), as depicted in Figure 4(c), can also be used to quantitatively confirm the presence of PAm and its content. An amorphous characteristic band at 956 cm−1 shows a decrease in intensity in the blank and grafted films, compared to neat PLA. Simultaneously, a sharp PLA α-crystal’s band appears at 921 cm−1 in the 2 treated films [29, 30]. The results firmly ensure that there is a significant transformation of amorphous phase to crystalline domains, due to conformational changes induced by newly formed -OH and -COOH terminals, as observed in GPC results.


## 3.3. XPS Analysis

XPS spectra of neat PLA and PAm-grafted PLA surfaces are compared. Figures5(a) and 5(b) show 2 strong signals of C1s and O1s for the surfaces of both samples, while a distinct N1s signal of PAm is only observed in the grafted sample [31, 32]. The presence of this signal ultimately indicates the success of the photografting reaction. Figure 5(c) shows 3 bands associated with C-C/C-H, C-O, and O-C=O components, in the C1s region [10]. The relative intensity of the C-C/C-H component increases as a result from the grafting reaction, while those of the other 2 bands of C-O, O-C=O components decrease. This is because the incorporation of PAm on the PLA surface leads to a decrease in relative contents of ester C-O and O-C=O, but an increase in the C-C/C-H composition [33, 34]. The corresponding O1s signals, as shown in Figure 5(d), reflect the surface contents of O-C=O and C-O groups [35]. Both signals show a decrease in intensities from neat PLA to the grafted film, because of a dilution effect from the presence of PAm. The existence of amide oxygen, N-C=O, is visible as a weak shoulder, located at the lower energy region of the O-C=O band of the grafted film. This is also confirmed by an appearance of the distinct signal of N1s, as shown in Figure 5(e).Figure 5
XPS spectra of neat (a) and grafted PLA (b) films (full spectra) and expanded scaled spectra in the C1s (c), O1s (d), and N1s (e) regions of neat and grafted PLA films.
(a)
(b)
(c)
(d)
(e)


## 3.4. Surface Properties

Contact angle measurements are used to characterize surface wettability and pH-responsive behavior of the samples. The contact angle (CA) values were measured at 25°C by using water droplets at pH of 4, 7, and 10. The results, as summarized in Figure6, show that neat PLA film has a CA value of 68°, reflecting its slightly hydrophilic nature compared to other polyolefin. Upon treating with “blank” or monomer solutions, the resulting films exhibit lower CA values, indicating higher degree of hydrophilicity. The results confirm that treating PLA films with blank solutions under UV irradiation leads to slight chain scissions and formation of newly generated polar -OH and -COOH end groups and hence an increase in the surface hydrophilicity. Further decrease in the CA value is observed in grafted PLA film, as a result from the presence of both grafted PAm chains and the newly generated PLA polar end groups.Figure 6
Contact angle (CA) values of neat, blank, and grafted PLA films, measured by using water droplets at various pH values.Interestingly, pH-dependent behavior is observed in “blank” and grafted PLA films, whereas the CA values measured at different pH for neat film remain significantly unchanged. The lowest CA values of the 2 treated samples are observed at pH 4, which slightly increase when a neutral solution is employed. However, a sharp increase in the value is obtained when the pH of the water droplet is increased to 10. The results confirm that both treated films have negative polarity surfaces, due to the presence of grafted functional groups and newly generated end groups, as already described. At acidic and neutral pH, interaction between the positively charged species in the water droplet and the negative polarity surface leads to higher wettability. In contrast, at high pH values, the presence of OH− results in strong repulsion of the water droplet and the film surface, reflecting by a higher CA value or lower wettability. In addition, the degree of pH-dependent property also increases from blank to grafted films, due to an increase in the content of surface negative functionalities.


## 3.5. XRD Spectroscopy

Crystalline characteristics of films before and after treatments are examined. It is clearly observed that after blank and grafting processes, the films became opaque (almost completely white), whereas neat PLA film is transparent. This is due to formation of crystalline domains in the films. To verify this and calculate the crystalline contents of the samples, XRD is employed and the diffractograms are shown in Figure7. Neat PLA has almost completely amorphous structure, as a very weak diffraction peak at 2θ = 16.8° is observed. In contrast, 4 characteristic sharp peaks appear in the blank and grafted films at 2θ = 14.9°, 16.7°, 19.1°, and 22.4°, corresponding to (010), (110/200), (203), and (205) planes, reflecting their semicrystalline nature [36, 37]. Results on crystallinity (%) show that the neat sample has only 2% crystalline content, whereas a considerable increase in the values to 35% and 29% is observed in the blank and grafted counterparts. The value for the blank sample is slightly higher than the grafted films, indicating that the grafting of PAm on the film surface may interrupt PLA’s chain arrangement and, hence, lower its degree of crystallinity.Figure 7
XRD diffractograms of neat (i), blank (ii), and grafted PLA (iii) films.


## 3.6. Thermal Properties

Effects of grafting polymerization on thermal properties of the films are investigated by DSC, as presented in Figure8. The glass transition temperature (Tg) and melting temperatures (Tm) of the samples are identified. Double melting endothermic peaks are clearly witnessed in the grafted PLA film (142.7 and 152.7°C), whereas, in the neat (138.7°C) and blank (146.7°C) samples, a single Tm is observed. These split endotherms are associated with two distinct crystalline structures of PLA: disordered imperfect α′ crystalline and ordered perfect α crystalline forms. The lower endotherm Tm(I) is related to the α′ form which is generated under restricted conditions. This form almost simultaneously recrystallizes into α form when the restricted conditions are released. The higher TmII corresponds to the perfect crystals from reorganization and the primary α form. The two processes, the melting of the α′ form and the recrystallization into α form, can be considered as the α′-α phase transition. This phase transition was hindered in the grafted sample, however, due to chain entanglements by PAm on the PLA surface. Subsequently, thickening of the imperfect α′ crystal form occurs.Figure 8
DSC thermograms (1st heating curve) of neat, blank, and grafted PLA films.The degree of crystallinity (Xc) was also calculated from the enthalpy of melting of 1st heating thermograms by comparing with semicrystalline PLA measured at the equilibrium point (93.0 J/g) [38]. The results, as summarized in Table 2, show an increase in the crystalline contents from 2% for neat PLA to 26% for blank and 23% for grafted films. This agrees with those observed in XRD experiments, reflecting a transformation of amorphous PLA structures to crystalline domains during the blank and grafting treatments. The blank and grafted films exhibit slightly higher (64.4°C) and lower (59.0°C) Tg, compared to the intermediate value of neat PLA (62.3°C). Generally,Tg value increases with an increase in crystallinity and decreases with the introduction of plasticizers to the polymer matrix. Although crystalline domains are developed in both the blank and grafted films, the grafted film shows lowerTg. This is likely because the medium-sized grafted PAm chains, which contain a high content of chain ends, can act as a plasticizer for the PLA matrix.Table 2
Thermal properties derived from DSC (1st heating) experiments of neat, blank, and grafted PLA films.
Sample
T
g (°C)
T
m
(
I
) (°C)
T
m
(
I
I
) (°C)
Δ
H
m (J/g)
X
c (%)
Neat PLA
62.3
138.7
153.7
1.36
2
Blank PLA
64.4
146.7
152.7
24.20
26
Grafted PLA
59.0
142.7
152.7
20.98
23


## 3.7. Morphology

The cross-sectional areas of all films are analyzed by SEM to observe morphological changes before and after blank and grafting experiments. SEM micrographs at different magnifications of the blank and grafted films show profound morphological changes, that is, transition from complete amorphous to semicrystalline structures, as observed as white crystalline domains dispersed over the whole cross-sectional area, as shown in Figure9. It is, therefore, concluded that the crystallization mechanisms involve nucleation steps from the initiator, coinitiator, and methanol solvent molecules, which penetrate into the film matrix, and also local induced crystallization by -OH and -COOH chain ends, generated from a low degree of chain scissions.Figure 9
Cross-sectional SEM micrographs of neat, blank, and grafted PLA films at different magnifications.


## 3.8. Mechanical Properties

Mechanical properties of all films are examined by tensile experiments. The properties typically correlate with chemical structures, molecular weights, and crystallinity of polymers. All PLA films exhibit the stress-strain behavior of normal plastic materials, in which yielding is observed before breaking, as shown in Figure10. The tensile strength of the samples shows a slight drop, whereas stress at break exhibits a moderate rise from neat to blank and grafted films. The drops in tensile strength and Young’s modulus are directly related to the partial chain scissions of PLA, which have taken place in both blank and grafted films. Although enhancement of crystallinity in those 2 films is observed, the effect of molecular weights reduction overwhelmed the crystalline effect in this case.Figure 10
Stress-strain curves (a) and Young’s modulus and elongation at break values (b) of neat, blank, and grafted PLA films.
(a)
(b)In contrast, the elongation at break of the 2 treated samples increases sharply, compared to neat film. This can be explained in terms of a toughening effect from the presence of crystalline domains, which act as physical cross-links holding the chains before rapture. Moreover, the grafted PLA film exhibits a higher elongation at break value than the blank film. This is likely because of the presence of slightly cross-linked P(Am-co-MBAm) grafted chains on the film surface.


## 4. Conclusions

P(LA-g-Am-co-MBAm) films were successfully prepared by UV-assisted graft polymerization. The grafted PLA surface becomes more hydrophilic, compared to its blank and neat PLA film counterparts. The surface also exhibits pH-dependent properties, due to the presence of the grafted PAm chains. The treatments of both blank and Am monomer solutions under UV irradiation trigger slight photodegradation and subsequent induced crystallization of the blank and grafted films, which have significant effects on the molecular structure, morphological, thermal, mechanical properties, and crystallinity of the films. The materials have high potential for use in biomedical applications, such as cell culture substrates or scaffolds which are responsive to pH changes, or in environmental applications as absorbents for various contaminant species.



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*Source: 5651398-2017-12-12.xml*