Cong
Chang‡
,
Hua
Wei‡
,
Qian
Li
,
Bin
Yang
,
Ni
Chen
,
Jin-Ping
Zhou
,
Xian-Zheng
Zhang
* and
Ren-Xi
Zhuo
Key Laboratory of Biomedical Polymers of Ministry of Education & Department of Chemistry, Wuhan University, Wuhan, 430072, P. R. China. E-mail: xz-zhang@whu.edu.cn; Fax: +86-27-68754509; Tel: +86-27-68754509
First published on 12th January 2011
A core cross-linked (CCL) mixed micelle with dual responsive shells was constructed from two amphiphilic block copolymers poly(methyl methacrylate-co-3-(trimethoxysilyl)propyl methacrylate)-b- poly(N-isopropylacrylamide) (P(MMA-co-MPMA)-b-PNIPAAm) and P(MMA-co-MPMA)-b-poly(2-(diethylamino)ethyl methacrylate) (P(MMA-co-MPMA)-b-PDEA) via a two-step process: cooperative aggregation of the two block copolymers into core-shell mixed micelles in acidic aqueous solution at room temperature followed by cross-linking of the hydrophobic core via an acid-catalyzed sol–gel process. The reversibly structural transformation of the core-shell mixed micelles into core-shell-corona (CSC) mixed micelles took place when subjected to elevated temperature or pH value, that is, high temperature resulted in the fabrication of CSC mixed micelle with shrunk PNIPAAm chains as the inner shell and stretched PDEA chains as the outer corona, and alkaline pH led to the formation of CSC mixed micelle with collapsed PDEA chains as the inner shell and extended PNIPAAm chains as the outer corona. Due to the existence of thermo- and pH- dually responsive shells, the structurally stable CCL mixed micelle may find practical applications in biomedical fields such as drug delivery and intelligent release.
The atom transfer radical polymerization (ATRP) technique, as one of the most actively developing areas in polymer chemistry, allows the facile preparation of a broad range of polymers with well-controlled molecular weight and preselected composition, especially amphiphilic block copolymers with well-defined structure and functional groups, without the stringent requirement which is usually necessary for other types of living polymerization.19–22
On the basis of these concepts, herein we report the synthesis of two well-defined diblock copolymers: temperature-responsive poly(methyl methacrylate-co-3-(trimethoxysilyl) propylmethacrylate)-b-poly(N-isopropylacrylamide) (P(MMA-co-MPMA)-b-PNIPAAm) and pH-responsive P(MMA-co-MPMA)-b-poly(2-(diethylamino)ethyl methacrylate) (P(MMA-co-MPMA)-b-PDEA) with the same hydrophobic moiety of PMMA via successive ATRP, and further proposed a novel mixed micelle structure with dual responsive outer shells self-assembled from these two amphiphilic stimulus-responsive block copolymers. The resultant mixed micelle was composed of a hydrophobic PMMA core and combined temperature/pH dual responsive PNIPAAm/PDEA shells (Fig. 1).
Fig. 1 Schematic illustration of the CCL mixed micelle formation. Coaggregation of P(MMA-co-MPMA)-b-PNIPAAm and P(MMA-co-MPMA)-b-PDEA in aqueous solution followed by cross-linking of the micellar core. |
In addition, the structural stability and integrity of the supramolecular nanostructures is a crucial issue in the practical applications of current micelle formulation. In this work, MPMA bearing reactive trimethoxysilyl functions was introduced to the PMMA block as a comonomer to produce the core cross-linked (CCL) mixed micelle by using inorganic “silica-based” cross-linking strategy,23–25 which can fix the structure of the mixed micelle and permanently suppress the dissociation of non-cross-linked micelle into individual polymer chains under shear forces, dilution by gastric, blood or other body fluids and salinity fluctuations after administration.26–28
By increasing temperature or pH value, PNIPAAm and PDEA blocks were respectively rendered hydrophobic, therefore the resulting core-shell mixed micelle converted into core-shell-corona (CSC) mixed micelle with three-layered structure, namely, the shrunk PNIPAAm chains formed the inner shell and the stretched PDEA chains constructed the outer corona at elevated temperature, and the collapsed PDEA chains built the inner shell and the extended PNIPAAm chains constituted the outer corona at alkaline pH. This study, to our knowledge, is believed to present the first example of CCL mixed micelle with dual responsive shells.
Scheme 1 Synthesis of P(MMA-co-MPMA)-b-PNIPAAm and P(MMA-co-MPMA)-b-PDEA diblock copolymers. |
1H NMR was employed to characterize the structure of the prepared block copolymers. Fig. 2(A) showed the 1H NMR spectrum of P(MMA-co-MPMA) in CDCl3. The molar ratio of MMA and MPMA units in the P(MMA-co-MPMA) block was determined to be 57:1 based on the integral ratio of resonance signals at 3.6 ppm (a) and 3.5 ppm (b), characteristic peaks of MMA (-OCH3) and MPMA (-(OCH3)3) units, respectively. In comparison to Fig. 2(A), we found that the characteristic peaks of PNIPAAm (5.9–7.0 ppm (c, -NH-), 4.0 ppm (d, -CH(CH3)2), 1.0 ppm (e, -CH(CH3)2)) and PDEA (4.0 ppm (f, -OCH2-), 2.7 ppm (g, -OCH2CH2-), 2.5 ppm (h, -N(CH2CH3)2), 1.1 ppm (i, -N(CH2CH3)2)) blocks also appeared in the 1H NMR spectra of the purified P(MMA-co-MPMA)-b-PNIPAAm (Fig. 2(B)) and P(MMA-co-MPMA)-b-PDEA (Fig. 2(C)), confirming the successful synthesis of the block copolymers. However, the invisible resonance signals of MPMA unit were probably due to its rather low content in the block copolymer.
Fig. 2 1H NMR spectra of (A) P(MMA285-co-MPMA5), (B) P(MMA285-co-MPMA5)-b-PNIPAAm351 and (C) P(MMA285-co- MPMA5)-b-PDEA290 in CDCl3. (The blue star in (A) is ascribed to the residual DMF.) |
SEC-MALLS were further utilized to determine the molecular weights of the as-prepared copolymers. It can be found from Table 1 that Mn of P(MMA-co-MPMA)-b-PNIPAAm (67,100 Da) and P(MMA-co-MPMA)-b-PDEA (80,700 Da) were both larger than that of P(MMA-co-MPMA) (27,090 Da). MMA, MPMA and DEA exhibited similar activity in the polymerization because they were all methacrylate monomers, as a result, the molecular weight distribution (Mw/Mn) of P(MMA-co-MPMA)-b-PDEA block copolymer was bigger than its precursor of P(MMA-co-MPMA) as expected. However, NIPAAm, as an acrylamide, possessed different polymerizable property, which possibly accounted for the decreased Mw/Mn value after its polymerization. In addition, the variation of Mw/Mn value after the second-step ATRP was also confirmed by the SEC traces presented in Fig. S1.† In comparison to the SEC trace obtained for the P(MMA-co-MPMA) random copolymer precursor, there were clear shifts to the higher molecular weights for the P(MMA-co-MPMA)-b-PNIPAAm and P(MMA-co-MPMA)-b-PDEA diblock copolymers (Fig. S1†), indicating a high initiating efficiency of the P(MMA-co-MPMA)-Br macroinitiator for the polymerization of NIPAM or DEA, and a successful preparation of the target diblock copolymers by consecutive ATRP. The appearance of a small peak at elution time 24 min in the SEC trace of P(MMA-co-MPMA) was feasibly attributed to the existence of oligo(methyl methacrylate) (OMMA). Although the product P(MMA-co-MPMA) has been purified by repeated precipitation, it remained difficult to get rid of OMMA completely possibly due to their similar properties. However, this small peak was also observed in the SEC traces of both block copolymers, indicating that OMMA exhibited no initiating ability for the further polymerization, therefore the effect of such impurity on the properties of the final diblock copolymers was negligible. The degrees of polymerization (DP) of the MMA and MPMA units were calculated to be 285 and 5 according to the molar ratio of these two units (57:1) and the molecular weight of P(MMA-co-MPMA) block (27,090 Da). Then the DP of PNIPAAm and PDEA blocks were estimated to be 351 and 290 from the corresponding molecular weight (67,100 Da and 80,700 Da) of the two diblock copolymers, respectively. The diblock copolymers were thus denoted P(MMA285-co-MPMA5)-b-PNIPAAm351 and P(MMA285-co-MPMA5)-b-PDEA290. It should be pointed out that the actual composition of the copolymer can be calculated based on either the integrity ratio in the NMR spectra or the absolute molecular weight determined by SEC-MALLS. Both methods were used in our experiment, however, the results obtained from molecular weight were closer to the molar feed ratio of the copolymer, therefore we, herein, only report the calculation of the real composition using the data from molecular weight.
Copolymer | M n (Da) | M w/Mn |
---|---|---|
P(MMA-co-MPMA) | 27,090 | 1.61 |
P(MMA-co-MPMA)-b-PNIPAAm | 67,100 | 1.37 |
P(MMA-co-MPMA)-b-PDEA | 80,700 | 1.85 |
Fig. 3 (A) TEM images and (B) size distributions of CCL mixed micelles: (A1, B1) at pH 5, 20 °C; (A2, B2) in DMF; (A3, B3) at pH 5, 45 °C; (A4, B4) at pH 9, 20 °C. Scale bars indicate 700 nm. |
After cross-linking, the lyophilized CCL mixed micelles were dissolved in an organic solvent to prove sufficient cross-linking and further explore their shape persistence against alteration of solvents. Fig. 3(A2) displayed the TEM image obtained for the CCL mixed micelles in DMF, which convincingly showed that the cross-linked structure of the mixed micelle was still after transfer into the organic medium, in which the assembly would be destroyed. After switching the solvent from water to DMF, the CCL mixed micelles maintained their integrity and still exhibited well-defined spherical shapes with diameters ranging from 130 to 390 nm. The structure coincided with the morphology observed in the aqueous phase (Fig. 3(A1)). It turned out that cross-linking resulting from the hydrolysis and condensation of trimethoxysilyl functions was effective and the mixed micellar structure was locked by cross-linking of the hydrophobic core. Similar results were reported in our previous studies23,24 as well.
As shown in Fig. 3(B2), the average size of the CCL mixed micelles was around 301 nm, which agreed roughly with the value observed by TEM. In addition, upon comparison of part B2 and B1 in Fig. 3, we found that the size of the CCL mixed micelle (301 nm) recorded in DMF was larger than that measured in water (210 nm). The reason was probably that DMF was capable of dissolving P(MMA-co-MPMA), PNIPAAm and PDEA blocks; hence, both the core and shell of the CCL mixed micelles were fully solvated and swelled in DMF. However, the use of water as the solvent resulted in insufficient mobility and contraction of PMMA block, leading to a smaller size.
From the optical absorbance of the micelle aqueous solution as a function of temperature (Fig. 4), we found that the P(MMA-co-MPMA)-b-PNIPAAm micelle (Fig. 4(A)) underwent a change in its structure at the temperature corresponding to the LCST of PNIPAAm homopolymer, ca. 33 °C. The results confirmed that the completely phase-separated core-shell micellar structure led to the unaltered LCST behavior of the shell-forming block. However, the absorbance of P(MMA-co-MPMA)-b-PDEA micelle kept constant with increasing temperature (Fig. 4(C)), indicating that the P(MMA-co-MPMA)-b-PDEA micelle was stable against temperature and exhibited no thermo-sensitivity. Most importantly, the CCL mixed micelle (Fig. 4(B)) constructed from the coaggregation of the two block copolymers exhibited almost the same LCST behaviors (LCST value and response rate) as the P(MMA-co-MPMA)-b-PNIPAAm micelle, suggesting that the PDEA chains had little effect on the thermo-responsiveness of the PNIPAAm chains in the dual responsive shells of the mixed micelle, therefore we concluded that the desired CCL mixed micelle with unaltered thermo-sensitivity was developed.
Fig. 4 Thermo-sensitive behaviors of micelle solution at pH 5: (A) P(MMA285-co-MPMA5)-b-PNIPAAm351 micelles, (B) CCL mixed micelles, and (C) P(MMA285-co-MPMA5)-b-PDEA290 micelles. |
The lyophilized CCL mixed micelles were re-dissolved in different aqueous media for morphology observation to further confirm their dual sensitivity. TEM images of the CCL mixed micelles revealed the presence of well-dispersed spherical micelles of around 100–240 and 110–310 nm in diameter at pH 5, 45 °C (Fig. 3(A3)) and pH 9, 20 °C (Fig. 3(A4)), respectively. It was worth pointing out that for the individual P(MMA-co-MPMA)-b-PNIPAAm or P(MMA-co-MPMA)-b-PDEA micelles, large aggregates were believed to precipitate from the micelle solution when the temperature increased above the LCST of PNIPAAm or pH rose above the pKa of PDEA due to the insolubility of PMMA, PNIPAAm (at temperature higher than its LCST) and PDEA (at alkaline pH) chains. However, stable mixed micelles with regularly shape were observed irrespective of increased temperature (Fig. 3(A3)) or pH value (Fig. 3(A4)) under TEM visualization, which was attributed to the presence of PNIPAAm/PDEA dual shells in the structure of the mixed micelles, that is, the hydrophilic PDEA or PNIPAAm chains can still stabilize the micelles and prevent the formation of aggregates at pH 5 or 20 °C respectively. The results further confirmed the formation of mixed micelles at the molecular level from the mixture of P(MMA-co-MPMA)-b-PNIPAAm and P(MMA-co-MPMA)-b-PDEA. The particle sizes estimated from TEM were systematically smaller than those measured by DLS, which were ∼564 and 578 nm in diameter for the CCL mixed micelles at pH 5, 45 °C (Fig. 3(B3)) and pH 9, 20 °C (Fig. 3(B4)), respectively. In comparison to the data at pH 5, 20 °C (Fig. 3(A1), we found that the mixed micelles became larger when subjected to high temperature (45 °C, Fig. 3(A3)) or alkaline pH (pH 9, Fig. 3(A4)). The reason was probably that the structural transformation of PNIPAAm or PDEA chains from the stretching state as the hydrophilic shells to the contracting status as the hydrophobic inner shells increased the hydrophobic domain in the micellar structure,35,36 since the hydrophobic region was emphasized after negative staining in TEM specimen,37 the mixed micelles with enlarged size were visualized consequently.
〈Rg〉 and 〈Rh〉 of the CCL mixed micelle under different conditions were further determined by LLS analyses. It can be seen from Table 2 that the 〈Rg〉 and 〈Rh〉 recorded at high temperature (45 °C, pH 5) or alkaline pH (25 °C, pH 9) were both larger as compared with the data measured at room temperature and acidic pH (25 °C, pH 5). The increase of micelle dimension observed in LLS study agreed well with the results of TEM and size distribution measurements, also confirming the occurrence of structural transformation in the mixed shells of micelle at elevated temperature or pH value. In addition, the 〈Rg〉/〈Rh〉 value of the mixed micelles was determined to be around 0.7 under different conditions, close to the theoretical calculated value for a uniform sphere (∼0.8),24,38 indicating a spherical shape as well as ill-uniform core-shell structure for the CCL mixed micelle.
Fig. 5 shows the temperature- and pH-dependent 1H NMR spectra for the CCL mixed micelles recorded in D2O. Note that the proton signals from PMMA chains were invisible because they formed the immobile and non-solvated micellar core in D2O. At pH 5 and 20 °C (Fig. 5(A)), all the characteristic signals of PNIPAAm (d and e) and PDEA (f, g, h and i) blocks were readily visible, indicating that both blocks were hydrophilic and molecularly solvated. Increasing the temperature to 45 °C at pH 5 (Fig. 5(B)) led to the hydrophobic collapse of the stretched PNIPAAm chain from an extended-coil conformation to a shrunken-globule conformation, as evidenced by the significant attenuation of peaks d and e associated with PNIPAAm block, however, the characteristic resonances of the PDEA block were clearly evident, which was reasonable as this block was soluble at pH 5 due to the protonation of tertiary amine residues. Based on our assumption, CSC mixed micelles consisting of a cross-linked PMMA core, PNIPAAm inner shell, and protonated PDEA outer corona formed at pH 5 and 45 °C (Fig. 6).
Fig. 5 1H NMR spectra of CCL mixed micelles in D2O: (A) pH 5, 20 °C; (B) pH 5, 45 °C; (C) pH 9, 20 °C; (D) pH 9, 45 °C. |
Fig. 6 Schematic illustration of temperature and pH double responsive structural changes for CCL mixed micelle. |
Conversely, upon adjusting to pH 9 and 20 °C (Fig. 5(C)), the stretched PDEA chains collapsed due to their deprotonation, leading to the complete disappearance of characteristic peaks of PDEA chains, while the signals of PNIPAAm chains were still clearly visible because of their hydrophilicity at temperatures below the LCST. The results indicated the formation of three-layer micelle structure with cross-linked PMMA core, hydrophobic PDEA inner shell, and hydrophilic PNIPAAm outer corona at pH 9 and 20 °C (Fig. 6).
In addition, starting from the state at pH 5 and 20 °C, all the characteristic peaks of PNIPAAm and PDEA blocks were hardly detected at pH 9 and 45 °C, further confirming the occurrence of transformation from the hydrophilic to hydrophobic state for both blocks at high temperature and pH value (Fig. 6).
From the above discussion, we concluded that the CCL core-shell mixed micelles self-assembled from the mixtures of P(MMA285-co-MPMA5)-b-PNIPAAm351 and P(MMA285-co-MPMA5)-b-PDEA290 converted into CSC mixed micelles at elevated temperature or pH value. The resultant CSC mixed micelle possessed a three-layered structure with the hydrophobic PMMA block as the compacted core surrounded by the collapsed PNIPAAm blocks as the inner shell and soluble PDEA chains as the outer corona at high temperature, or shrunk PDEA blocks as the inner shell and stretched PNIPAAm chains as the outer corona at alkaline pH. In addition, it is worth pointing out that the transformation of both shell-forming blocks was reversible as demonstrated by the transition from a turbid solution to a transparent solution when the aqueous temperature was decreased from above (45 °C) to below (20 °C) the LCST or the aqueous pH shifted from alkaline (pH 9) to acidic (pH 5) value.
Footnotes |
† Electronic supplementary information (ESI) available: SEC traces of P(MMA285-co-MPMA5), P(MMA285-co-MPMA5)-b-PNIPAAm351, and P(MMA285-co- MPMA5)-b-PDEA290. See DOI: 10.1039/c0py00373e |
‡ Both authors contributed equally to this paper. |
This journal is © The Royal Society of Chemistry 2011 |