Article
Multiblock Polyurethanes Based on Biodegr- adable Amphiphilic Poly(ε-caprolactone)/ Poly(ethylene glycol) Segments as Candidates for Tissue Engineering Applications
Irene Bartolozzi, Stefania Cometa, Cesare Errico, Federica Chiellini, Emo Chiellini*
Laboratory of Bioactive Polymeric Materials for Biomedical and Environmental Applications (BIOlab) UdR-INSTM-Department of Chemistry and Industrial Chemistry, University of Pisa-Via Vecchia Livornese 1291, 56010, S. Piero a Grado (Pisa), Italy
* Corresponding author: emochie@dcci.unipi.it (Emo Chiellini) Tel.: 0039-050-2210301; Fax: 0039-050-2210332
Biodegradable amphiphilic multiblock poly(ether-ester-urethane)s were prepared by one-step bulk polycondensation of PEG and PCL macrodiols and HMDI with good yields and high molecular weights. The copolymers were characterized by 1H-NMR, FT-IR, SEC, TGA and DSC analysis. Different ratios of PEG/PCL, PEG macromonomer length and copolymer molecular weights allowed for tuning their hydrophilicity. Thanks to their tunable characteristics, the prepared multiblock copolymers can be exploited in the fabrication of biodegradable scaffolds for tissue engineering by means of the electrospinning technique.
Keywords: Polycondensation, Tissue engineering, Thermal properties, Block copolymers, Electrospinning.
Citation: Irene Bartolozzi et al, Multiblock Polyurethanes Based on Biodegradable Amphiphilic Poly(ε-caprolactone)/poly(ethylene glycol) Segments as Candidates for Tissue Engineering Applications, Nano Biomed. Eng. 2011, 3(2), 86-94.
DOI: 10.5101/nbe.v3i2.p86-94.
Biodegradable poly(ether-ester-urethane)s (PEEUs) have drawn attention in the biomedical field, where they have been used as bioabsorbable sutures [1, 2], drug delivery systems [3, 4], biodegradable vascular grafts [5] and, in general, in the fabrication of scaffolds for Tissue Engineering (TE) [6-8].In fact, suitable mechanical properties and bio- degradation rates of scaffolds for TE applications can be tuned by tailoring the chemical composition and the macromolecular architecture. In particular, the presence of hard and soft segments, their different ratios, as well as the polymer molecular weight, affect the final properties of PEEUs, making them suitable for various applications.Polyethylene glycol (PEG) and poly(ε-caprolactone) (PCL) are very extensively used soft segments for their well proofed biocompatibility, and they are combined in copolymers to afford useful features. PCL is extensively used as surgical material. Its hydro-biodegradation yields 6-hydroxyhexanoic acid, a natural occurring metabolite which ultimately can be metabolized to CO2 and water.It is a semicrystalline polymer with Tm around 60 °C and although hydro-biodegradable, its crystallinity and hydrophobicity result in long degradation times [9]. Low molecular weight PEG is a biocompatible hydrophilic and highly flexible polymer, not biodegradable but able to be eliminated from the body by the renal system (bioeliminable) [10]. It is often used in copolymers with PCL to increase the hydrophilicity and decrease the crystallinity of the polyester segment and thus to tune the mechanical properties and the biodegradation rates [11].PEEUs containing PEG and PCL have been prepared with different methods, in most cases by using a two step prepolymer technique. Chain extension of PCL- PEG-PCL triblock copolymers was carried out with different diisocyanates including, among the others, methylene-bis-(cyclohexyldiisocyanate) (MBCDI) [12] or hexamethylenediisocyanate (HMDI) [6, 13] to give alternating polyurethanes. Yeganeh et al. prepared elastomeric hydro-biodegradable PEG-PCL based polyurethanes for soft TE by chain extending epoxyterminated polyurethanes with a multistep synthesis [14]. As for the one-step synthesis, Lee et al. obtained random multiblock copolymers by one-pot condensation polymerization of PEG and PCL diols with HMDI [15].Polymeric materials based on PEEUs have often exhibited excellent elastomeric properties. These properties have been exploited to prepare nanofibrous three-dimensional scaffolds for vascular grafts applications, by an electrospinning process. This process provides complex architectures that have become extensively desired since they resemble that of the extracellular matrix (ECM) present in the living tissue.In this work, segmented PEEUs – coded as PEGCL copolymers – obtained by coupling PCL and PEG segments, have been prepared. In previous works, the hydrophilicity and the degradation rate, as well as the influence of the surface composition of these PCL/PEG- based materials on cell adhesion have been assessed [16, 17].Here we deepened the investigation on the synthesis and characterization of PEGCL copolymers, in view of their potential application as materials for TE. In particular, the synthesis of these random copolymers was optimised to afford a fast, reproducible, one-step and solvent-free method, and the structure-property relationships were also deeply investigated. Moreover, the attention was focused on the evaluation of the thermal properties of the proposed materials. The copolymers displayed phase segregation of the two components, in confirmation of our previous investigations [17]. Finally, a preliminary study on the suitability of these copolymers to be processed into nanofibers by electrospinning technology is reported.
All reagents were purchased from Sigma Aldrich unless otherwise noted. Toluene (J.T. Baker) was re fl uxe d ove r sodi um a nd di st i l l e d be fore use . 1,6-Hexamethylendiisocyanate (HMDI) was distilled at reduced pressure (65 °C/0.2 mbar). PEG-diol (MW 2000 or 3400) and PCL-diol (MW 2000) were dried by azeotropic distillation with toluene and further dried under vacuum. Tin(2-ethyl-hexanoate) (SnOct2) was used as received.
PEG- and PCL-diols in different ratios were thoroughfully dried by azeotropic distillation with toluene and then under vacuum. A stoichiometric amount of 1,6-hexamethylenediisocyanate was added to the melted mixture together with a few drops of SnOct2. The solution was stirred at 70 °C. The copolymers were recovered after double precipitation in methanol and petroleum ether and dried until constant weight (yields 85-95%).1H-NMR (CDCl3, 200 MHz) δ: 1.3-1.4 (2 H, CH2-CH2-CH2), 1.6-1.7 (6 H, CH2-CH2-NH, CH2-CH2-O-C=O, CH2-CH2-C=O-O), 2.3 (2 H, CH2-C=O-O, PCL), 3.1 (4 H, CH2-CH2-NHC=O, HMDI), 3.6 (4 H, CH2-CH2-O, PEG), 4.1(2 H, CH2-CH2-O-C=O, PCL), 4.2 (2 H, O-CH2-CH2-O-C=O-NH, PEG) ppm.FT-IR (cast film): 3445-3370 (NH), 2950 and 2865(νCH2 aliphatic), 1725 (ν C=O ester), 1660 (C=O amide I),1540 (C=O amide II), 1243 (νCOO ester), 1110 (νC-O-C,ether) cm-1.
FT-IR spectra were acquired on a Perkin-Elmer 1600 x FTIR spectrometer on polymer cast films. 1H-NMR spectra were acquired on a Varian Gemini 200 spectrometer in CDCl3.Size exclusion chromatography (SEC) analyses were performed at a flow rate of 1.0 ml min-1 by using a Jasco PU-1580 HPLC liquid chromatograph connected to Jasco 830-RI and Perkin-Elmer LC-75 spectrophotometric (λ = 260 nm) detector, and equipped with two Mixed-D PLgel columns (300x7.5 mm). Chloroform was used as the eluent and the calibration curve was prepared by using mono-dispersed polystyrene standards.Differential scanning calorimetry (DSC) measurements were performed by using a Mettler TA 4000 instrument on samples of 10-15 mg, under nitrogen atmosphere, at a heating and a cooling rate of 10 °C min-1.Thermogravimetric analysis (TGA) measurements were carried out with a TAQ 500 MFC system equipped with thermogravimetric analyzer software in the temperature range from 30 to 600 °C at 10 °C min-1 heating rate under nitrogen.Wide Angle X-ray Diffraction (WAXD) patterns were acquired by using nickel-filtered Cu-Kα radiation (Rigaku Denki Model RAD-C diffractometer). The X-ray diffractometer operated at 40 kV and 180 mA in the 2θ scanning mode between 5 and 35 degrees.
Preliminary experiments of electrospinning were performed on the PEGCL-I-25_2 copolymer. The electrospinning apparatus consisted of a 10 ml syringe equipped with a 21-gauge blunt needle, a syringe pump (BSP- 99 M, Braintree Scientific Inc., Braintree, MA) and two high voltage power supplies of opposite polarity (Spellman High Voltage, UK). To obtain focused fiber collections, a screen-to screen electrode configuration was employed, composed of two parallel metallic screens at different electrical potentials, one functioning as a fiber collector and the other one as an auxiliary electrode. The fluid was fed at a given flow rate to the metallic needle jutting out of a hole in the middle of one plate and the fibers were collected onto the other plate.A solution of PEGCL-I-25_2 in chloroform (10 % w/v) was electrospun at 2mL hour-1 flow rate with spinning voltage at 30 and 46 KVolt and 30 cm distance needle to collector.Morphological analysisThe top surface of polymeric nanofibrous samples was investigated by means of scanning electron microscopy (SEM; Jeol LSM 5600LV, Japan).
The biodegradable segmented PEEUs were synthesised by one-step random condensation polymerization, as shown in Scheme 1.PEG macrodiols with molecular weight 2000 or 3400 and PCL macrodiols with molecular weight 2000 were used in different ratios (Table 1).PEG- and PCL-diol oligomers were reacted in bulk together with stoichiometric amounts of HMDI as chain extender. The reaction was speeded up by adding SnOct2 as catalyst and stopped when viscosity was too high to allow the stirring of the mixture. To remove the catalyst, the copolymer was recovered by double precipitation in methanol and petroleum ether with yields ranging between 85-95%.FT-IR spectra exhibited the most significant peaks of the two components, qualitatively confirming the co- presence of PEG and PCL. Fig. 1 shows the overlaid FT- IR spectra of PCL-HMDI and PEGCL-I-25_1.The absorption bands at 1110 and 1243 cm-1 (a and b) are attributed to the characteristic C-O-C stretching vibration of the repeated O-CH2-CH2- units of PEG backbone and –C(=O)O– stretching vibrations of PCL repeated units, respectively. The absorption band at 1540 cm-1 (c) (N-H bending vibrations) confirms the formation of a urethane group in the copolymers. The strong C=O stretching band at 1725 cm-1 (d) is attributed to -C(=O)O-CH2- ester bonds typical of PCL moieties. No absorption is observed in the range of 2270-2285 cm-1 range, thus confirming that the NCO groups of HMDI have reacted completely. 1H-NMR spectra exhibited all the relevant peaks of the two components. The ratio of the PEG and PCL blocks was calculated from the relative intensities of the peak at 3.6 ppm for the (CH CH O) of PEG and from the peak at 4.1 ppm for the (CH2-OC=O) of PCL and is in agreement with the ratio of the feed mixture.SEC analysis did not show any low molecular weight peaks attributable to the starting macromonomers. However, as expected in a polycondensation process, fairly broad molecular weight distributions were observed, suggesting that low molecular weight components might still be present after the purification. It should be highlighted that the calibration curve with polystyrene does not allows for determining the real MW value, being the hydrodynamic volume of PS fairly different from that of the PCL/PEG polymers and therefore a different standard or a different technique should be employed. Nevertheless, this method is useful for a comparative evaluation among the set of the prepared polymers.
Scheme 1 Synthesis of PEEUs.
Fig. 1 FT-IR spectrum of PEGCL-I-25 and PCL-HMDI.
Table 1. Characterization of the PEGCL copolymers.
a) PCL MW = 2000; b) Evaluated by SEC.
Thermal properties
The thermal behaviour of the PEGCL copolymers was investigated by differential scanning calorimetry (DSC) and the relevant data are reported in Tables 2 and 3.In Fig. 2, the DSC traces relevant to the second heating cycle applied to the PEGCL copolymers were shown.Samples were first heated to 150 °C to erase the thermal history, then cooled to -100 °C and heated again to 120°C. The scans were run at 10 °C min-1 and glass transitions and melting events were evaluated in the second heating scans. Both PEG and PCL are semicrystalline polymers and therefore a similar behaviour is expected from their copolymers. The glass transition temperature (Tg) was not detected for PEG2000 and PEG3400 oligomers. A large melting peak at 55.4 °C and a very small one at 39.0 °C were observed for PEG2000; in the case of PEG3400, two adjacent melting peaks, falling at 55 and 57 °C, were detected. The two peaks present in the endotherm in the second heating curve correspond to the melting of PEG lamellae with different fold numbers [18]. PCL2000 exhibited a Tg at –66.9 °C and two melting peaks at 45.2°C and 50.4 °C. For all the copolymers, a single glass transition was observed, which was attributed to the PCL component. Compared to the pristine PCL2000, the Tg values were shifted of 10-12 °C to higher temperature, namely around-55 - -57 °C, thus suggesting a stiffening of the structure due to the increase in molecular weight and to the strong interchain interactions established through H-bonds between urethane groups and carbonyl or ether oxygen atoms. In addition, the presence of crystalline domains, which form physical crosslinking, might contribute to this stiffening.In the first cooling scan, the PEG2000, PEG3400 and PCL2000 oligomers exhibit a single crystallization peak at 30.7, 34.4 and 26.7 °C, respectively. The examined copolymers exhibit two crystallization peaks: the first one around 8-15 °C is attributed to the PCL component, since also PCL-HMDI exhibits a single crystallization peak at13.6 °C. The second peak appears at lower temperature and is attributed to the PEG component, whose crystallization is strongly affected by the PCL content. In fact, PEGCL-I-50 exhibits a peak around 0-3 °C and with a crystallization enthalpy comparable to the first peak, while PEGCL-I-25_1 exhibits a peak around – 31°C, with a very small enthalpy. PEGCL-II-25, having PEG3400, exhibits a peak around – 8 °C, with a higher enthalpy value than that detected for PEGCL-I-25_1. Finally, PEGCL-I-25_2, having higher MW, exhibits a single exothermic peak at 1.6 °C, indicating a strong hindrance to the crystallization process (Table 2). During the second heating scan, PEGCL-I-50 exhibits two fairly sharp melting peaks, the first at 35-36 °C and the second at 47-48 °C. PEGCL-I-25_1 exhibits a small exothermal peak at about –35 °C after the Tg, attributed to the cold crystallization of PEG segments that achieve more freedom after the glass transition and are capable to arrange in a small crystalline domain [19, 20].PEGCL-I-25_1 also exhibits a small melting peak at 18-22 °C and a second one at 45-47 °C. The first peak is broader and was attributed to the PEG component, which is in lower amount and whose crystallization is strongly hampered by the PCL segments, while the second peak with sharper shape was attributed to the melting of PCL crystalline domains. This is confirmed by the fact that the single melting peak of PCL-HMDI appears at 46.4°C. Also PEGCL-II-25 exhibits two melting points, the first one broad, at about 40 °C, and the second one sharp, at about 46 °C. PEGCL-I-25_2, having a very high molecular weight, exhibits a single melting peak around 42 °C (Table 3).Few conclusions can be drawn, which are further confirmed by WAXD measurements. In particular, WAXD has been used to qualitatively evaluate crystallinity of the copolymers, since the crystalline structure of PEG and PCL domains exhibit characteristic diffraction patterns. In Fig. 3, PCL-HMDI, PEGCL-I-50, PEGCL-I-25_1 and _2 WAXD diffraction spectra are reported, in comparison with PCL2000 and PEG2000 macrodiols used for their synthesis.In particular, WAXD patterns of PCL macrodiol show an intense peak at 2θ= 21.7° and a smaller one at 23.8°, whereas PEG macrodiol shows two almost equally intense peaks at 2θ= 19.4° and 23.7°. Therefore we used peaks at 21.7° and 19.4° for PCL and PEG crystals identification, respectively.The crystalline structure of PCL-HMDI almost corresponds to that of PCL macrodiol. In PEGCL-I-50 WAXD patterns, both PCL and PEG diffraction peaks are detected. In PEGCL-I-25_1, an obviously intense PCL crystal diffraction peak and a quite weak one for PEG crystal are observed, while no diffraction peaks typical of crystalline PEG appear in the spectrum of PEGCL-I-25_2, showing that PEG blocks resulted enable to crystallize. This finding, in good agreement with DSC results, can be assigned to the high molecular weight of PEGCL-I-25_2. In general, it seems that the two components of the multiblock copolymers have the ability to segregate in domains and crystallize separately, but when the molecular weight is very high as for PEGCL-I-25_2, this process is somehow hampered, as confirmed by the previously reported surface investigation of these copolymer films [17] and a single large melting peak is observed.The presence of the two components mutually affects the crystallization and melting temperatures. In particular, PCL domains crystallize first and interfere with PEG crystallization, whose exothermal peak is shifted to lower temperature and has a broader shape. Also all the melting peaks are shifted to lower temperatures than the pristine oligomers. This behaviour has been previously reported for PEG/PCL copolymers [21].The large undercooling, calculated as ∆T = Tm-Tc, which was observed for most of the melting/crystallization transitions, confirms the mutual interference in the crystallization process, which requires lower temperatures to be accomplished. For the examined copolymers, ∆T values are in the range of 35-52 °C for the transition of PEG domain and 30-40 °C for that of PCL domain.Previous studies on the thermal behaviour of PEG- PCL block copolymers agree that if PCL segment is long enough, its crystallization occurs first during the cooling from the melt, fixing the whole structure of the spherulites and leading to a significant undercooling and imperfect crystallization of the PEG block [22].When PCL segments are shorter, there is a significant mutual influence of the two components, which leads to imperfect spherulites morphology [23]. The interaction of the two components also affects the crystallinity of the two domains, which can be calculated from the fusion enthalpy of the relevant melting peak, normalized to its actual content, supposing that there is no contribution from the other component. For instance, to calculate the percentage of crystallinity of the PCL domain, the ∆Hm of the relevant peak is normalized to the weight content ofPCL in the copolymer and rationed to the ∆Hm of a 100%
Table 2. DSC first cooling scan of the PEGCL copolymers and their macromonome
Table 3. DSC second heating scan of PEGCL copolymers and their macromonomers.
Fig. 2 DSC second heating scans of PEGCL copolymers and their precursors.
Fig. 3 WAXD patterns of PCL and PEG macrodiols, PCL-HMDI and PEGCL copolymers. The star and the solid dot indicate the diffraction peaks used for PCL and PEG crystal identification, respectively.
Fig. 4 TGA thermograms of PEGCL copolymers and their precursors (Heating rate: 10 °C/min to 600 °C under N2).
Table 4. TGA results of PEGCL copolymers and their acromonomers.
a: T onset was calculated at weight loss % = 2%;
b: Residue was calculated at 580°C.
Thermal stability of the copolymers was evaluated by thermal gravimetric analysis at 10 °C min-1 heating rate under non-oxidative conditions (Fig. 4 and Table 4).The Tonset of the degradation was defined as the temperature at which 2% of weight loss was measured and crystalline PCL (∆Hm = 139.5 J g-1) [24]. Crystalline the decomposition temperature (Td) as the temperature at which the maximum decomposition rate was measured percentage for PCL-HMDI and for PEGCL-I-25_1, PEGCL-I-25_2 and PEGCL-II-25 copolymers ranges between 43 and 47%, while for PEGCL-I-50 is between 30-35%. during a degradation step. The pristine PEG2000 exhibits a Tonset at 301.8 °C and a single decomposition step at 405.4 °C, while PEG3400 a Tonset at 327.2 °C and a single decomposition step at 397.9 °C. PCL2000 exhibits a Tonset at 244.2 °C and two decomposition steps at 333.1°C and 406.9 °C, respectively, which give some credit for a thermal degradation involving two consecutive mechanisms [25]. For all the investigated oligomers the residue at 580 °C was below 1%.The homopolymer PCL-HMDI showed only one decomposition step. This is partly due to the higher molecular weight of the copolymers and partly due to the absence of low molecular weight oligomer/polymer chains present in the PCL-HMDI homopolymer sample. It should be noted that the GPC analysis of the copolymers gave a broader molecular weight distribution with high polydispersity indexes, while PCL-HMDI had narrower PDI = 1.7 (see Table 1). All the copolymers containing PEG2000 exhibit a similar Tonset around 280 °C, an intermediate value between those of the two components, and two decomposition steps, as depicted in Table 4.The first one at 300-320 °C with a weight loss (∆w1) is approximately in agreement with the PCL content and the second one around 396 °C is relevant to the PEG component as confirmed also by the weight loss (∆w2). For all the investigated copolymers the residue at 580°C was below 3%. The copolymer containing PEG3400 exhibits a Tonset around 267 °C and complete degradation occurs at about 378 °C, a value lower than its precursors.
Fig. 5 SEM micrographs of electrospun PEGCL-I-25_2 (d = 30 cm, V=30 KVolt) with 100 μm (a) and 50μm (b) scalebar
Fig. 6 SEM micrographs of electrospun PEGCL-I-25_2 (d = 30 cm, V=46 KVolt) with 100 μm (a) and 50 μm (b) scalebar.
For tissue engineering applications, a polymeric material needs to be easily processed into a highly porous scaffold with a high surface area to volume ratio andan interconnected pore network [26]. PCL/PEG-based copolymers or blends are usually electrospinned by melt- electrospinning [27, 28].In this work, the copolymer PEGCL-I-25_ 2 copolymer was processed by using a standard solution electrospinning technique and was preferred among the other copolymers in virtue of its higher molecular weight. High molecular weight polymers enable a better entanglement of the macromolecular chains in solution during electrospinning which is necessary for fibers formation [29].A solution of PEGCL-I-25_2 in chloroform (10% w/v) was electrospun at a spinning voltage at 30 KVolt and 30 cm distance needle to collector. In the electrospinning process, polymeric jets undergo an electrostatic instability deriving from mutual repulsion of charges that leads to the rapid rotation of the polymeric jet in the whipping process, with the formation of an untidy conical fibrous mesh [30].The electrospinning process of the prepared PEGCL-I-25_2 solution did not exhibit the previously mentioned phenomena and resulted in the deposition on the collector of a single fibre which followed a random pattern (Fig. 5).This phenomenon is quite common in the electrostatic drawing of non-conductive fluids [31]. What is used in these cases is a mixture of solvents (e.g. chloroform/ DMF) one having a higher dielectric constant to increase the solution conductivity. This has already been proved to be a good expedient to improve morphology and diameters of fibers during electrospinning of low conductivity polymer solutions [32].However, in our case it was sufficient to vary the applied potential to obtain a jet with a significant stronger whipping motion that resulted in entangled fibers with reduced diameters. When the potential was increased from 30 to 46 KVolt (while keeping the distance 30 cm) homogenous electrospun fibers mats were obtained. Fibers appeared curly and flexible, with diameters in the range 1-3 μm and only very few sub-micron fibers were present (Fig. 6).This preliminary results show than these polyurethanes could be of particular interest for TE applications due to their ability to be processed by electrospinning technology. Work is in progress in order to evaluate the processability by electrospinning of the other copolymers reported in Table 1, i.e. having lower molecular weight, different PCL/PEG ratio or different PEG segment’s length and finally to evaluate the influence of these characteristics on their biological response.
Random multiblock amphiphilic PEEUs containing PEG and PCL segments were prepared by an optimised one-step and solvent-free synthetic route with high yields. The prepared copolymers displayed phase segregation of the two components, which mutually affect the thermal properties of the material.
The work was performed within the framework of FIRB–2005 – prot. RBIN043BCP, PRIN–2006– prot. 2006038548 projects and within the general scope NoE Expertissues CT –2004 –500328. The authors wish to thank Mr. Narducci for the SEM images.
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Copyright:(c) 2011 Irene Bartolozzi, et al. This is an open-access article distributed under the terms of the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original author and source are credited.
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