Poly(vinyl alcohol): Physical Approaches to Designing Biomaterials for Biomedical Applications
Poly(vinyl alcohol) is a non-toxic, biosynthetic polymer and biocompatible polymer that has the ability to form hydrogels either via chemical or physical crosslinking. Whilst chemical crosslinking provides greater control on the properties of the resultant hydrogel, physically crosslinked hydrogels or blends with other biocompatible polymers are more suited for biomedical applications. In this paper we report a systematic study on the effect of varying concentrations of PVA, physical methods of crosslinking, and PVA-gelatin and PVA-PVP blends on the physical and mechanical properties of the hydrogels.
In the last few decades there has been a growing interest in biocompatible and biodegradable polymers that are being used to create scaffolds for tissue engineering. To design scaffolds for tissue engineering, the main requirements are high porosity, interconnected porous structure, large surface area, and a microenvironment that allows the cells to adhere, proliferate, differentiate, and retain its phenotype. It is well established that interconnected pores play an important role in cell engineering; however, with increasing porosity there is an inevitable loss in the mechanical properties. A large number of different polymers including hydrogels have been explored for different tissue engineering applications . Poly(vinyl alcohol) is a water soluble, nontoxic, biocompatible polymer that is able to exhibit hydrogen bonding by virtue of the hydroxyl groups present in the repeating units. PVA can form hydrogels either via chemical or physical crosslinking, which exhibit high water content. It can be chemically crosslinked with radiation or aldehydes to form hydrogels using chemicals such as glutaraldehyde, methanol, ethanol, propranolol, and acetone. However, many of these chemicals are not cytocompatible making it an unsuitable method despite being usually cheap and efficient [2–7]. Physical crosslinking methods such as air-drying and cryogelation by repeated freeze-thawing cycles of the aqueous polymer solutions are more biologically compatible but do not allow for the level of control available with other crosslinking methods . PVA three-dimensional networks are of considerable interest in biomaterial applications as the materials can be engineered to closely match human tissues. There has been a significant interest in the cryogenic gelation of PVA as a method of producing hydrogels for biomedical applications. Cryogenic gelation of PVA can lead to a porous structure and the ability for these polymers to absorb surrounding fluid, thus making them attractive candidates for tissue engineering. Furthermore, PVA blends of poly(vinyl pyrrolidone, PVP), gelatin, alginates, collagen and composites with calcium phosphates have been reported for potential use as scaffolds for bone tissue engineering. It is generally accepted that PVA chains can undergo crosslinking via a freeze-thaw process and the degree of crosslinking increases with the number of cycles, whilst the equilibrium water uptake can be altered either via physical crosslinking or by blending with other polymers.
Despite a large number of studies on PVA for biomedical applications, there is a lack of dedicated and systematic study of the properties of physically crosslinked PVA hydrogels. Our ultimate goal is to create composite scaffolds of PVA hydrogels that can in addition function as a carrier for growth factors and/or plasma rich platelets for bone growth. Thus in this study, we report the properties of PVA hydrogels crosslinked via facile physical crosslinking methods and PVA blends with gelatin and PVP, to further apply the optimum blends for future composite formulation.
2. Materials & Methods
Poly(vinyl alcohol) (PVA) granules (Merck, UK) of 145,000 mol·wt. and ≥98% hydrolysis, poly(vinyl pyrrolidone) (PVP) powder (Sigma-Aldrich, UK) and 40,000 mol·wt., Gelatin (FLUKA) were used in this study.
2.1. Preparation of PVA and PVP Solutions
PVA 10%, 20%, and 30% w/v solutions were prepared by dissolution of the appropriate amount of PVA granules in distilled water and mixed in a Duran bottle and magnetically stirred at 121°C until all the PVA granules dissolved to form a homogenous solution. Similarly, PVP (5% w/v) solution was produced by mixing appropriate amount of PVP powder and distilled water and magnetically stirred at room temperature.
2.2. PVA/Gelatin Blend Preparation
Blends were prepared by mixing the required amounts (Table 1) and placed in a hot water bath at 50°C and solution gently mixed. The blends were then physically cross-linked by 1 freeze thaw cycle, which consisted of first freezing the samples to −80°C for 1 hour in a freezer, then placing it in a (VirTis SP Scientific) freeze dryer at −59.4°C with vacuum set to 17 mT for 24 hours. After freeze drying the samples were thawed at room temperature for 12 hours.
2.3. Preparation of Hydrogel Films
PVA hydrogels were produced through physical crosslinking methods of air-drying only (AD), one cycle of freeze thawing (FT), and both air-drying followed freeze thawing (AD+FT). Air dried hydrogels were prepared by placing the PVA solutions in Petri dishes at room temperature and left to completely dry over a period of 7 days. Air-dried and freeze thawing specimens were allowed to dry partially and then subjected to the FT cycle as described. PVA : PVP gel blends (see Table 2) were first produced by freeze thawing to study the miscibility between the two polymers. Subsequently, 50 : 50 and 75 : 25 mix ratios were air-dried only to create hydrogels sheets for tensile testing.
2.4. Fourier Transform Infrared (FTIR)
Fourier transform infrared spectroscopy was carried out using a Perkin Elmer precisely spectrum FTIR spectrometer. FTIR spectra were obtained in the wavenumber range of 650–3500 cm−1 with 4 cm−1 resolution.
2.5. Equilibrium Water Uptake
The dried gels were cut in rectangular strips and weighed accurately prior to immersing them in distilled water at 37°C. After immersion the samples were periodically weighed by removing them and gently pressed between filter paper and the process was continued until there were no further gravimetric changes. The equilibrium water content (EWC) (%) was calculated using the following equation: wherein is hydrated weight when swollen and is the dry weight of hydrogel prior to swelling.
2.6. Tensile Testing
All hydrogel films were cut into standard dumbbell shapes and swollen to equilibrium state before testing. The tensile tests were carried out at rate of 5 mm/min using a Universal testing machine (Instron 5569A).
2.7. Differential Scanning Calorimetry (DSC)
A Perkin Elmer Jade series differential scanning calorimeter was used to determine the thermal properties and Perkin Elmer Jade series software to process raw data. 10–20 mg samples were carefully placed and sealed in aluminium pans (Perkin Elmer). The scans were carried out with reference pan calibrated using Indium49 under a Nitrogen7 atmosphere. Two cycles of heating and cooling were carried out, starting from −20°C to 200°C followed by a cooling cycle to 0°C at a rate of 10°C per minute. The temperature of the second heating cycle was raised to 280°C and the same cooling cycle followed. The glass transition temperature () and melting temperature () were calculated using the Pyris Jade DSC (Perkin Elmer) software.
3. Results and Discussion
3.1. Equilibrium Water Uptake
The dissolution of PVA is essential to form physical hydrogels. The dissolution of PVA in water is dependent on the molecular weight and the degree of hydrolysis of the polymer. It has been reported that high dissolution temperatures are required to dissolve PVA in water, especially if it has a high degree of hydrolysis [9, 10] due to the strong intra- and intermolecular hydrogen bonds. However, PVA with low degree of hydrolysis contains too many hydrophobic acetate groups, which renders the polymer too hydrophobic to dissolve in water. In this study we used a 98% hydrolysed PVA of molecular weight of 145,000 and conducted the dissolution in water at 121°C and mechanical agitation to yield clear polymer solutions with ease that did not require prolonged incubation in water. The EWC of the PVA hydrogels are shown in Table 3. Solutions of pure PVA at concentrations of 10%, 20%, and 30% by weight in water were subjected to three different treatments, namely, one cycle of freeze-thaw (1FT), air dried (AD), and air dried followed by one freeze thaw cycle (AD+1FT) to form hydrogels. The EWC showed that with increasing concentration of PVA there was a decrease, irrespective of the method used to form the hydrogels. The 20% and 30% PVA solutions were highly viscous, thus only 10% PVA solutions were used for preparation of the blends. The presence of PVP showed higher equilibrium water content than PVA. The PVA10 only control had the lowest EWC of 74% which increased to 83% and 85% in 75PVA : 25PVP and 50PVA : 50PVP showing that EWC increased by adding PVP. The higher EWC and less efficient cross-linking could be attributed to the presence of bulky side groups in PVP that could lead to an increase in the amorphous regions and less cross-linking in the hydrogel blends. Furthermore, the hydrophilic nature of PVP contributes to increasing the ingression of bulk water into the gel matrix and improving interactions with bound water thus leading to the higher EWC.
3.2. FTIR Spectroscopy
A comparison of the FTIR spectra of the three air-dried hydrogels prepared from different concentrations of PVA is shown in Figure 1. All showed characteristic absorption bands of PVA which can be assigned to the vibrations arising due to C=O, C–H, C–OH, C–O bonds. A strong characteristic feature of PVA is the O–H stretching band indicating the presence of both the strong hydrogen bonding internally to OH or terminal vinyl OH groups and broad peaks centred at 3265, 3285, and 3269 cm−1  which were observed for the three hydrogels. Hydroxyl groups from residual water also contribute to the peak intensity . Two strong peaks arising from the C–H stretching of the alkyl groups at 2916 cm−1 to 2969 cm−1 are characteristic of the C–H symmetric () and CH2 asymmetric () stretching vibration, with their position suggesting that the hydrocarbon chains of the polymer take a transzigzag conformation. The weak peak at 1595 cm−1–1636 cm−1 can be assigned to the C=O group from the residual acetate in PVA that results from manufacturing and handling of PVA from hydrolysis of polyvinyl acetate. The peaks arising at 1416 cm−1–1424 cm−1 can be assigned to the –CH2 bending with deformation bands of C–CH3 appearing at 1377 cm−1. The peaks at 1263 cm−1 and 1326 cm−1 are associated with CH2 wagging and the C–C, C–O–C stretching vibrations, respectively. The sharp absorption bands indicate that the film formed by this process resulted in a semicrystalline PVA. The peaks at 1038–1088 cm−1 are attributed to –C–O–H bending and C–O stretching vibration coupled with O–H bending vibration. The atactic form of PVA is also shown by the peaks at 915 cm−1 (CH2 rocking) and at 836 cm−1–845 cm−1 (C–C stretching) [12–14]. No major distinct differences were observed in the spectra; however, in general, broad, high intensity peaks in PVA 30 were noted as possibly arising due to the higher concentration of the polymer.
The FTIR spectra of the PVA-AD, PVA-FT, and PVA-AD+FT are shown in Figure 2, which indicates that there is a higher degree of crosslinking in the FT and AD+FT groups as the peaks associated with –OH are sharp with lower intensity in comparison to just air dried PVA gel. The stretching of CH2 groups are observed through peaks at 2920 cm−1 (symmetric), 2850 cm−1, 1420–1492 cm−1 (bending/scissoring), 1280–1315 cm−1 (wagging), and 1167–1229 cm−1 (twisting) . Stretching of the C–O bonds from primary alcohol groups in PVA can be observed through the peaks at 1050–1095 cm−1 in crosslinked PVA, and this peak is associated more with the aliphatic ethers present in crosslinked polymers.
The FTIR spectra of PVA blends with gelatin and PVP are shown in Figure 3. As expected, there are differences between the spectra of PVA-gelatin, PVP, and PVA. The hydroxyl peaks are also present in the PVP control but it is a broader and much shallower peak centred at 3412 cm−1. This peak could possibly be attributed to hydroxyl groups from the water bound to the PVP polymer chains, and alkyl vibrations are similarly shown by the broad peak centred at 2818 and 1427 cm−1. Most notably the peak at 1651 cm−1 is prominent in the PVP control. This is commonly associated with the carbonyl groups but in the case of PVP it is more likely due to the presence of C–N stretching in PVP . The increase of PVP content in the blend shows a shift in the hydroxyl peak to higher frequencies and a broadening and shallowing of the peak possibly due to the reduction in hydroxyl groups. The narrowing and increasing intensity of the C–N peak at 1651 cm−1 is to be expected with the increase in PVP content. The distortions in the peaks at the region around 3290 and 1650 cm−1 are thought to show the strong interaction between the hydroxyl groups of PVA and the carbonyl groups of PVP.
Characteristic bands of gelatin, NH stretching, amide I, CO, and CN stretching as well as amide II and amide III can be observed in Figure 3. Amide A with an absorption wavelength of 3296 cm−1 tends to merge with a CH2 stretch peak when carboxylic acid groups exist in intermolecular associations. Amide I bands at 1632 cm−1 have been attributed to intermolecular associations with imide residues. The CH2 bending and wagging vibrations raise two bands at amide II 1535 cm−1 and amide III 1334 cm−1 with final skeletal stretching at both 1080 cm−1 and 638 cm−1 [16–18]. The blends showed characteristic peaks of the components PVA and gelatin and the intensity of the characteristic peak varied with concentration of the components.
3.3. Differential Scanning Calorimetry
The observed glass transition temperature () and melting temperatures () of the prepared hydrogels are shown in Table 4. The first heating cycle of 1FT PVA displayed two endothermic peaks that can be attributed to the loss of moisture or melting of crystallites due to the strong hydrogen bonding between PVA-water and PVA chains themselves . Melting temperatures () for all the PVA gels stayed comparable and ranged between 220.6 and 227°C, and the literature value for PVA is reported to be 230°C which is slightly higher than the observed values . The of PVA gels prepared by air drying (AD) (58.0–74.25°C) was lower with values than those of AD+1FT and 1FT (61.1−75.2°C, 69.4–73.4°C), respectively, indicating higher crosslinking occurred with AD+1FT and 1FT cycle than with just AD. Literature values for of PVA have been reported to be around 80°C  but other studies report a range between 59°C and 74°C . Thermal analysis of PVA : PVP blends showed ranging from 210.5 (25% PVA) to 229°C (75% PVA). As expected, no peak was observed in the PVP control as the melting point of PVP is beyond the range of the DSC cycle used. It can also be observed that of PVA/PVP blends decreased with increasing concentration of PVA; this could be due to the fact that PVA has a lower than that of PVP and hence decreases values of the blends as concentration of PVA is increased. temperatures of PVA : PVP blends were comparable to those reported by Cauich-Rodriguez et al. .
From the thermal analysis of PVA : gelatin blends, the measurements of indicate an increase in comparison to PVA 10% (w/v) thus indicating that materials have undergone some crosslinking. temperatures of gelatin have been reported to be around the range of 180°C–210°C and represent the blocks of imino acids such as proline and hydroxyproline and amino acids such as glycine . The blends showed peaks attributable to PVA ranging from 218 (20PVA1FT) to 226°C (80PVA1FT).
3.4. Tensile Strength of the Hydrogels
The tensile properties of the differently crosslinked gels were characterised by the ultimate tensile strength (UTS) and the Young’s modulus of the hydrated gels. Figure 4 shows the effect of the different treatments to enable physical crosslinking in the PVA gels. The figure clearly indicates that the UTS increases with increasing concentration of PVA as expected with no significant difference between the 1FT and the cumulative AD and FT films; however, air drying on its own yielded the weakest gels. The wet tensile properties observed in this study were much higher than the values reported in a study dedicated to creating PVA hydrogels using a photo-crosslinking approach . The tensile modulus is shown in Figure 5 with a clear indication that the cumulative air-drying and 1FT lead to higher modulus for the 10%, 20%, and 30% PVA hydrogels. The tensile strength and Young’s modulus of the hydrated PVA-PVP and PVA-gelatin blends prepared by the AD+1FT method are shown in Figures 6 and 7, respectively, which show that higher PVA content yielded superior tensile strength. At this stage only the AD+1FT method was used to prepare the films as they clearly yielded the stronger gels. The result of the tensile testing showed that the higher EWC of the blend films was detrimental to the tensile properties of PVA when freeze thawed but when air-dried it increased the stiffness of PVA significantly. The lower mechanical properties under wet conditions could be attributed to the increase in amorphous regions due to PVP’s bulky side groups or the dilution of PVA or a combination of both factors. The tensile properties of the PVA blends with both PVP and gelatin indicate that they are sufficiently strong enough to be used for tissue engineering applications such as skin.
The study showed that the concentration of PVA clearly had an effect on the degree of crosslinking with air drying in conjunction with freeze-thawing yielding superior gels. The blends with gelatin or PVP increased the EWC of the hydrogels, however, which also had a detrimental effect on the mechanical properties. It was clear that hydrogels with better mechanical properties were obtained by using the combination of air-drying and freeze-thawing for creating blends, and thus this process will be used in our future work.
Conflict of Interests
The authors declare that there is no conflict of interests regarding the publication of this paper.
The authors would like to thank the University of Botswana School of Medicine for funding Shathani Nkhwa and King’s College London Medical School studentship for funding Kristo Fernando Lauriaga.
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