ph-switchable polymer nanostructures for controlled release
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Cite this: Polym. Chem., 2012, 3, 3007
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pH-switchable polymer nanostructures for controlled release†
Kay E. B. Doncom,a Claire F. Hansell,a Patrick Theatob and Rachel K. O’Reilly*a
Received 20th July 2012, Accepted 8th August 2012
DOI: 10.1039/c2py20545a
A diblock copolymer consisting of poly(methyl acrylate) (PMA) and poly(pentafluorophenyl acrylate)
(PPFPA) was synthesized by RAFT polymerization methods. The PPFPA block was then substituted
with N,N-diisopropylethylenediamine and the end group modified with one of two hydrophilic groups
to form pH-responsive copolymers. The self-assembly properties of these polymers were investigated
and shown by TEM and DLS to form micelles at acidic pH and vesicles at basic pH. The encapsulation
and controlled release of a hydrophilic dye molecule, Rhodamine B, was demonstrated using
fluorescence spectroscopy.
Introduction
The ability of amphiphilic block copolymers to self-assemble in
selective solvents, particularly water, has been of great interest to
scientists and has been widely studied in academia. These
amphiphiles self-assemble in order to minimize any unfavourable
interactions between the hydrophobic block and the aqueous
environment.1 Many morphologies are possible, from the
conventional spherical micelles,2 rods,3 cylindrical micelles4 and
vesicles,5–7 to the more exotic hamburger micelles8 and Janus
particle micelles.9,10 The structure of the particle formed is related
to the interfacial curvature favored by the amphiphile and the
effect this has on the packing of the polymer chains.1 This can be
predicted from a dimensionless factor known as the packing
parameter, p, which when simplified, is related to the amphiphilic
balance, or the ratio of hydrophobic to hydrophilic blocks, of the
block copolymer. For example, a micelle is formed when p# 1/3 ,
and vesicles are favoured when ½ # p # 1. Therefore changing
the length of the hydrophilic block will cause a change in the
packing parameter and in the morphology formed upon self-
assembly.
In recent years particular attention has been paid to stimuli
responsive polymers, which undergo a change in hydrophilicity
in response to external stimuli, such as light,11–14 temperature,15–23
pH,24–31 or a combination of stimuli.32–37 Copolymers made up of
one or more of these responsive blocks will undergo a phase
transition in response to a specific stimulus. This can result in a
morphology change such as from unimers to micelles,23,37–40
micelles to vesicles,1,15,16,41–43 or rod–coil transitions14,44 by
altering the amphiphilic balance of the copolymer and therefore
aUniversity of Warwick, Department of Chemistry, Gibbet Hill Road,Coventry, CV7 4AL, UK. E-mail: [email protected] for Technical and Macromolecular Chemistry, University ofHamburg, Bundesstrasse 45, D-20146, Hamburg, Germany
† Electronic supplementary information (ESI) available: Furthercharacterization of polymers and self-assembled structures. See DOI:10.1039/c2py20545a
This journal is ª The Royal Society of Chemistry 2012
its packing parameter. Within this area of research particular
interest has been paid to the potential ability of these responsive
amphiphilic polymers to encapsulate a small molecule and
release it in a controlled manner upon application of the specific
stimulus.28,29,45–47 This ability could have the potential to be used
in the medical or pharmaceutical industries, such as in targeted
drug delivery applications.
Controlled radical polymerization techniques such as Atom
Transfer Radical Polymerization (ATRP),48 Nitroxide Mediated
Polymerization (NMP)49 and Reversible Addition Fragmenta-
tion chain Transfer (RAFT) polymerization provide a facile
route to the synthesis of amphiphilic polymers as they allow the
formation of polymers with controlled architecture.50 Of these
techniques, RAFT provides an excellent route to the formation
of these ‘‘smart’’ polymers as it produces well-defined polymers,
with narrow polydispersities and predictable and controllable
molecular weight.51–53 RAFT also has a high tolerance for
functional groups within the growing polymer chain and retains
good control over end group fidelity, an important feature when
well-defined end groups are required. Functionality at the a end
of a polymer chain can be introduced pre-polymerization by
using a chain transfer agent containing the desired group. Post-
polymerization modification of the thiocarbonylthio group of
the chain transfer agent enables the introduction of a desired
functionality at the u chain end.54–59
Functionality within the polymer chain can be achieved by
directly polymerizing the desired monomer. However, for
monomers which may prove more difficult to directly polymerize
with good control an alternative route is through post poly-
merization functionalization of a scaffold polymer, for example
activated esters. Pentafluorophenyl acrylate is a good example of
an activated ester that can be polymerized by RAFT and has
been shown to be easily modified with both alcohols and
amines.60–66
Previous work within our group has shown that a diblock
copolymer consisting of a hydrophobic block, the temperature
responsive block PNIPAM and a charged hydrophilic RAFT
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end group can undergo a morphology transition from micelle to
vesicle in response to a change in temperature.15,16 This switching
behaviour was shown to be fully reversible and reproducible,
however, the time required for switching was slow. To improve
the utility of such morphology-switching materials we have
switched our focus to explore an alternative stimulus, namely
pH. Herein we report a new diblock copolymer containing a
hydrophobic block, a pH responsive block and a hydrophilic end
group. We investigate the self-assembly behaviour of this poly-
mer and show that it undergoes a morphology transition upon
decreasing the pH below the pKa of the responsive polymer. We
also show that the self-assembled structures are capable of
trapping a hydrophilic dye molecule and releasing it in a
controlled manner upon application of the stimulus.
Experimental
Materials
N,N-dimethylformamide (DMF 99.9%), 1,4-dioxane, N,N-diiso-
propylethylenediamine and all other chemicals were used as
received from Aldrich and Tokyo Chemical Industry unless
otherwise stated. AIBN [2,20-azobis(2-methylpropionitrile)] was
recrystallized twice frommethanol and stored in the dark at 4 �C.Methyl acrylate (MA) was passed over a short column of alumina
immediately prior to use in order to remove the inhibitor. Pen-
tafluorophenyl acrylate (PFPA) was synthesized according to
literature procedures.60 Triethylene glycol methyl ether acrylate
was synthesized according to literature procedures.67
Characterization
Nuclear magnetic resonance (1H and 13C NMR) experiments
were recorded at 400 or 500 MHz in CDCl3 or MeOD on a
Bruker DPX-400 or Bruker AM500 spectrometer. 19F NMR
spectra were recorded at 300 MHz in CDCl3 or MeOD on a
Bruker Avance 300 spectrometer. Chemical shifts are reported in
parts per million relative to CHCl3 (7.26 ppm for 1H and 77.0
ppm for 13C) or MeOD (4.84 ppm for 1H and 49.0 ppm for 13C).
Size exclusion chromatography (SEC) measurements were
obtained in either HPLC grade CHCl3 or DMF containing 0. 1
MNH4BF4 with a flow rate of 1 mL min�1, on a set of two PLgel
5 mm Mixed D columns plus a guard column. Cirrus SEC soft-
ware was used to analyze the data using poly(methyl methacry-
late) (PMMA) standards. Hydrodynamic diameters (Dh) and size
distributions of the self-assembled structures in aqueous solu-
tions were determined by dynamic light scattering (DLS). The
DLS instrumentation consisted of a Malvern Zetasizer NanoS
instrument operating at 25 �C with a 4 mW He–Ne 633 nm laser
module. Measurements were made at a detection angle of 173�
(back scattering) and Malvern DTS software was utilized to
analyze the data. All measurements were run at least three times
with a minimum of 10 runs per measurement. TEM measure-
ments were made by drop deposition of 4 mL solution onto an
oxygen plasma treated carbon-coated copper grid. Analysis was
performed on a JEOL TEM 2011 operating at 200 keV. Number
average particle diameters (Dav) were generated from the analysis
of a minimum of 50 particles from at least three different
micrographs. Fluorescence measurements were recorded on a
Perkin Elmer LS 55 spectrometer. Infrared spectrometry was
3008 | Polym. Chem., 2012, 3, 3007–3015
recorded on a Perkin Elmer Spectrum 100 FT-IR ATR unit.
Mass spectra were recorded on a Bruker Esquire 2000 ESI
spectrometer. Dialysis tubing was bought from Spectrum labs
with a molecular weight cut off 3.5 kDa.
Formation of the diblock copolymer
MA (4.00 g, 0.93 mmol, 50 equiv.) CTA 1 (ref. 68) (0.36 g, 46.5
mmol) and AIBN (15.3 mg, 0.09 mmol, 0.10 equiv.) were dis-
solved in 1,4-dioxane (2 : 1 volume compared to monomer) and
placed in an oven-dried ampoule under the flow of nitrogen with
a stirrer bar. The ampoule was degassed by at least three freeze–
pump–thaw cycles and released to and sealed under nitrogen.
The polymerization mixture was then heated at 65 �C for 2 hours
20 minutes to afford 2, conversion ¼ 73% (see Scheme 1). The
polymer was purified by precipitation into a stirred solution of
cold MeOH : H2O (10 : 1) three times, followed by dissolution in
THF, drying over anhydrous MgSO4, removal of the THF and
drying in vacuo to yield a yellow oily polymer. Mn (1H NMR) ¼
3.8 kDa, Mn (CHCl3 SEC) ¼ 2.6 kDa, Mw/Mn ¼ 1.07. 1H NMR
(400 MHz, CDCl3): d 0.88 (t, 3H, J ¼ 6.9 Hz, CH2CH3 of CTA
end group), 1.20–1.38 (br m, 20H, (CH2)10CH3 of CTA end
group), 1.40–2.10 (br m, 80H, CHCH2 of polymer backbone),
2.24–2.40 (br s, 40H, CHCH2 of polymer backbone), 3.34 (t, 2H,
J¼ 7.2 Hz, SCSSCH2 of CTA end group), 3.60–3.70 (br s, 120H,
OCH3 of PMA side chain), 4.88 (q, 1H, J¼ 7.6 Hz, CH3CHPh of
CTA end group), 7.12–7.28 (m, 5H, ArH in CTA end group). 13C
NMR (125 MHz, CDCl3): d 221.4, 175.8–175.6, 174.8–174.2,
170.4, 146.2, 146.2, 128.4, 126.9, 126.2, 52.9, 51.7, 50.5, 50.4,
50.0, 41.3–41.1, 37.5, 36.0–34.1, 31.9, 29.6, 29.5, 29.4, 29.3, 29.0,
28.9, 27.8, 23.0, 22.6, 22.5, 22.4, 22.2, 21.8, 14.1. FTIR nmax/cm�1
2953 and 2854 (alkane C–H stretch), 1729 (C]O ester stretch),
1435 and 1378 (C]C aromatic stretch).
Polymer 6 was synthesized in a similar manner, [CTA] : [M] ¼1 : 40, time ¼ 1 hour 35 minutes, conversion ¼ 50%. Mn (1H
NMR) ¼ 2.1 kDa, Mn (DMF SEC) ¼ 2.6 kDa, Mw/Mn ¼ 1.11.1H NMR (400 MHz, CDCl3): d 0.88 (t, 3H, J ¼ 6.7 Hz, CH2CH3
of CTA end group), 1.18–1.34 (br m, 20H, (CH2)10CH3 of CTA
end group), 1.40–2.10 (br m, 40H, CHCH2 of polymer back-
bone), 2.24–2.40 (br s, 20H, CHCH2 of polymer backbone), 3.34
(t, 2H, J¼ 7.4 Hz, SCSSCH2 of CTA end group), 3.60–3.70 (br s,
60H, OCH3 of PMA side chain), 4.88 (q, 1H, J ¼ 7.5 Hz,
CH3CHPh of CTA end group), 7.12–7.28 (m, 5H, ArH in CTA
end group). 13C NMR (125 MHz, CDCl3): d 221.4, 175.8, 175.6,
174.8, 174.3, 174.2, 170.4, 146.2, 128.4, 126.9, 126.2, 52.9, 51.7,
50.5, 50.4, 49.9, 41.3–41.1, 37.5, 36.0–34.0, 31.9, 29.6, 29.49, 29.4,
29.3, 29.0, 28.8, 27.7, 23.0, 22.6, 22.6, 22.4, 22.2, 21.7, 14.1. FTIR
nmax/cm�1 2953 and 2854 (alkane C–H stretch), 1729 (C]O ester
stretch), 1435 and 1378 (C]C aromatic stretch).
PFPA (9.21 g, 38.7 mmol, 120 equiv.), homopolymer 2 (1.23 g,
3.2 mmol) and AIBN (10.5 mg, 0.66 mmol, 0.2 equiv.) were
dissolved in 1,4-dioxane (1 : 1 volume compared to monomer)
and placed in an oven-dried ampoule under the flow of nitrogen
with a stirrer bar. The ampoule was degassed at least three times
and released to and sealed under nitrogen. The polymerization
mixture was then heated at 65 �C for 1 hour 45 minutes to afford
diblock copolymer 3, conversion ¼ 76%. The polymer was
purified by precipitation into cold hexanes three times and dried
in vacuo to yield a yellow powder.Mn (1HNMR)¼ 27.5 kDa,Mn
This journal is ª The Royal Society of Chemistry 2012
Scheme 1 Synthetic route for polymers 2–9.
‡ Although not ideal due to the potential for transamidation,N,N-dimethylformamide was utilized as the solvent due to the limitedsolubility of the charged tertiary amine acrylate in other organic solvents.
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(CHCl3 SEC) ¼ 7.7 kDa, Mw/Mn ¼ 1.29. 1H NMR (400 MHz,
CDCl3): d 0.88 (t, 3H, J ¼ 6.8 Hz, CH2CH3 of CTA end group),
1.20–1.34 (br m, 20H, (CH2)10CH3 of CTA end group), 1.40–2.40
(br m, 280H, CHCH2 of polymer backbone), 2.40–2.58 (br s,
40H, CHCH2 of polymer backbone), 3.0–3.15 (br s, 100H,
CHCH2 of polymer backbone), 3.34 (m, 2H, SCSSCH2 of CTA
end group), 3.60–3.70 (br s, 120H, OCH3 of PMA side chain),
7.12–7.28 (m, 5H, ArH in CTA end group). 13C NMR (125MHz,
CDCl3): d 174.9, 170.1, 170.0, 169.8, 169.7, 142.0, 141.9, 140.8,
140.0, 139.9, 138.9, 138.8, 136.7, 128.4, 127.0, 126.9, 126.2, 124.4,
51.7, 41.3, 41.1–39.9, 36.2–33.0, 32.9, 32.8, 30.3, 29.6, 29.5, 29.4,
29.3, 29.0, 28.9, 25.6, 22.7, 14.0. 19F NMR (400 MHz, CDCl3):
d �162.8 (br s, 2F, ArF in polymer side chain), �157.3 (br s, 1F,
ArF in polymer side chain),�153.8 (br s, 2F, ArF in polymer side
chain). FTIR nmax/cm�1 2956 (alkane C–H stretch), 1783 and
1737 (C]O ester stretch), 1517 and 1471 (C–F stretch), 1453
(C]C aromatic stretch).
Polymer 7 was synthesized in a similar manner, [CTA] : [M] ¼1 : 40, time ¼ 1 hour 50 minutes, conversion ¼ 87%. Mn (1H
NMR) ¼ 11.8 kDa, Mn (DMF SEC) ¼ 8.7 kDa, Mw/Mn ¼ 1.13.1H NMR (400 MHz, CDCl3): d 0.88 (t, 3H, J¼ 6.9 Hz, CH2CH3
of CTA end group), 1.20–1.38 (br m, 20H, (CH2)10CH3 of CTA
end group), 1.40–2.40 (br m, 140H, CHCH2 of polymer back-
bone), 2.40–2.50 (br s, 20H, CHCH2 of polymer backbone), 3.0–
3.15 (br s, 50H, CHCH2 of polymer backbone), 3.34 (m, 2H,
SCSSCH2 of CTA end group), 3.60–3.70 (br s, 60H, OCH3 of
PMA side chain), 7.12–7.28 (m, 5H, ArH in CTA end group). 19F
NMR (400 MHz, CDCl3): d �162.8 (br s, 2F, ArF in polymer
side chain), �157.3 (br s, 1F, ArF in polymer side chain), �153.8
(br s, 2F, ArF in polymer side chain). 13C NMR (125 MHz,
CDCl3): d 174.9, 170.1, 169.8, 169.7, 169.5, 169.4, 142.0, 141.9,
140.8, 139.99, 139.9, 138.9, 136.9, 128.5, 127.0, 126.3, 124.4, 51.7,
This journal is ª The Royal Society of Chemistry 2012
41.3–40.0, 36.1–34.7, 31.9, 29.6, 29.6, 29.4, 29.4, 29.1, 28.9, 22.7,
14.1. FTIR nmax/cm�1 2955 (alkane C–H stretch), 1783 and 1737
(C]O ester stretch), 1516 and 1471 (C–F stretch), 1450 (C]C
aromatic stretch).
Synthesis of the charged tertiary amine acrylate
Dimethylaminoethyl acrylate (DMAEA) (5.00 mL, 0.03 mol, 1
equiv.) was dissolved in petroleum ether (100 mL). Methyl
iodide (20.5 mL, 0.33 mol, 10 equiv.) was added and left to stir
for 1 hour. The solution was then filtered and the solid dried to
give a white solid (8.50 g, 91%). 1H NMR (400 MHz, D2O): d
3.11 (s, 9H, N+(CH3)3), 3.67 (m, 2H,CH2CH2N), 4.53 (m, 2H,
COOCH2), 5.92 (dd, 1H,2J ¼ 1.2 Hz, 3J ¼ 14.0 Hz, CHH]
CH), 6.11 (m, 1H, CHH]CH), 6.35 (dd, 1H,2J ¼ 1.2 Hz, 3J ¼23.2 Hz, CHH]CH). 13C NMR (125 MHz, D2O): d 54.6, 59.1,
66.1, 128.8, 132.9. FTIR nmax/cm�1 3020 (alkene C–H stretch),
3002 and 2949 (alkane C–H stretch), 1731 (C]O acrylate
stretch), 1621 (C]C alkene stretch), 1267 and 1278 (C–O
stretch), 1061 (C–N stretch). ESI MS: expected 158.12, found
158.12.
Substitution of the PFPA and end group modification
The substitution of the PPFPA scaffold and subsequent end
group modification proceeds via a one-pot, two step method, the
general procedure for which is as follows.
The diblock copolymer was dissolved in DMF‡ at a concen-
tration of 150 mg mL�1 and placed in an oven-dried ampoule.
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The ampoule was degassed at least three times and released to
and sealed under nitrogen. In a separate oven-dried ampoule
N,N-diisopropylethylenediamine (1.5 equiv. per PFPA) was
dissolved in DMF and the ampoule was degassed by three
freeze–pump–thaw cycles and released to and sealed under
nitrogen. The amine solution was transferred to the polymer
solution using air sensitive techniques. The solution was stirred
at room temperature overnight. 19F NMR was used to confirm
the full modification of pentafluorophenyl groups. In order to
modify the end group of the polymer, the desired end group
acrylate (100 equiv.), PBu3 (20 equiv.) and hexylamine (20 equiv.)
were separately dissolved in DMF and placed into individual
oven-dried ampoules. These three ampoules were then degassed
and released to and sealed under nitrogen. Air sensitive tech-
niques were used to transfer, firstly, the acrylate solution into the
polymer solution, followed by the PBu3 solution. After stirring
for 10 minutes, air sensitive techniques were used to transfer the
hexylamine solution into the polymer solution. The polymer
solution was then stirred overnight. The polymer was purified by
exhaustive dialysis against water, incorporating both acidic and
basic water changes. The polymer was recovered by lyophiliza-
tion to yield diblock copolymer 4, 5, 8 or 9. Full side chain
conversion was observed and end group modification was
calculated to be 100% by 1H NMR spectroscopy in both cases.
Polymer 4.Mn (1HNMR)¼ 23.9 kDa,Mn (DMF SEC)¼ 23.1
kDa, Mw/Mn ¼ 1.19. 1H NMR (400 MHz, MeOD): d 1.11–2.50
(br m, 420H, CHCH2 of polymer backbone), 1.35–1.50 (br s,
1200H, N(CH(CH3)2)2 of DIPEA side chain), 2.65 (t, 2H, J¼ 7.2
Hz, SCH2CH2COO of end group), 2.90 (br m, 2H,
SCH2CH2COO of end group), 3.16–3.42 (br s, 200H,
NHCH2CH2N of DIPEA side chain), 3.40–3.90 (br m, 520H,
NHCH2CH2N and N(CH(CH3)2)2 of DIPEA side chain and
OCH3 of PMA side chain), 4.55 (br, 2H, COOCH2CH2N of end
group), 7.10–7.30 (m, 5H, ArH of end group). 13C NMR (125
MHz, MeOD): d 176.9, 176.7, 176.6, 129.6, 128.2, 128.2, 68.9,
52.4, 50.8, 46.0, 43.7, 42.7, 42.1, 35.9, 21.2. FTIR nmax/cm�1:
3303 (N–H amide stretch), 2964 (alkane C–H stretch), 1737 (C]
O ester stretch), 1646 (C]O amide stretch), 1536 (N–H amide
bend), 1361 and 1185 (C–N stretch).
Polymer 5. Mn (1HNMR)¼ 23.9 kDa,Mn (DMF SEC)¼ 23.1
kDa,Mw/Mn¼ 1.19. 1HNMR (400MHz,CDCl3): d 0.90–1.11 (br
s, 1200H, N(CH(CH3)2)2 of DIPEA side chain) 1.20–2.40 (br m,
420H, CHCH2 of polymer backbone), 2.40–2.50 (br s, 200H,
NHCH2CH2NofDIPEAside chain), 2.75 (m,4H,SCH2CH2COO
of end group), 2.90–3.30 (br m, 300H, NHCH2CH2N and
N(CH(CH3)2)2 of DIPEA side chain), 3.39 (br s, 3H, OCH3 of end
group), 3.47–3.56 (m, 8H, (OCH2CH2O)2 of end group), 3.60–3.69
(br s, 120H, OCH3 of PMA side chain), 3.69–3.72 (m, 2H,
COOCH2CH2O of end group), 4.20–4.27 (m, 2H, COOCH2CH2O
of end group), 6.30–7.00 (br s, 100H, CHNHC of DIPEA side
chain), 7.10–7.30 (m,5H,ArHof endgroup). 13CNMR(125MHz,
CDCl3): d 174.9, 128.4, 127.0, 126.9, 126.2, 71.9, 70.6, 69.1, 69.0,
63.8, 59.0, 51.7, 48.7, 48.7, 45.3, 44.3, 42.7, 42.7, 41.3, 40.0, 35.1,
35.0, 34.9, 32.1, 31.9, 29.6, 29.3, 23.1, 21.3, 20.8, 14.1. FTIR nmax/
cm�1: 3294 (N–H amide stretch), 2964 (alkane C–H stretch), 1737
(C]Oester stretch), 1648 (C]Oamide stretch), 1536 (N–Hamide
bend), 1361 and 1185 (C–N stretch).
3010 | Polym. Chem., 2012, 3, 3007–3015
Polymer 8.Mn (1HNMR)¼ 10.4 kDa,Mn (DMF SEC)¼ 14.2
kDa, Mw/Mn ¼ 1.14. 1H NMR (400 MHz, MeOD): d 0.90–1.10
(br s, 500H, N(CH(CH3)2)2 of DIPEA side chain) 1.20–2.40 (br
m, 210H, CHCH2 of polymer backbone), 2.40–2.52 (br s, 100H,
NHCH2CH2N of DIPEA side chain), 2.68 (m, 2H,
SCH2CH2COO of end group), 2.78 (br m, 2H, SCH2CH2COO of
end group), 2.90–3.20 (br m, 200H, NHCH2CH2N and
N(CH(CH3)2)2 of DIPEA side chain), 3.50–3.62 (br s, 63H,
OCH3 of PMA side chain), 4.55 (br, 2H, COOCH2CH2N of end
group), 7.10–7.30 (m, 5H, ArH of end group). 13C NMR (125
MHz, MeOD): d 176.9, 176.6, 129.6, 128.2, 127.4, 52.5, 50.8,
46.0, 43.7, 42.8, 42.2, 35.9, 21.2. FTIR nmax/cm�1: 3304 (N–H
amide stretch), 2966 (alkane C–H stretch), 1737 C]O (ester
stretch), 1646 (C]O amide stretch), 1533 (N–H amide bend),
1383 and 1185 (C–N stretch).
Polymer 9.Mn (1HNMR)¼ 10.4 kDa,Mn (DMF SEC)¼ 14.9
kDa, Mw/Mn ¼ 1.11. 1H NMR (400 MHz, CDCl3): d 0.90–1.10
(br s, 500H, N(CH(CH3)2)2 of DIPEA side chain) 1.20–2.40 (br
m, 210H, CHCH2 of polymer backbone), 2.40–2.50 (br s, 100H,
NHCH2CH2N of DIPEA side chain), 2.75 (m, 4H,
SCH2CH2COO of end group), 2.90–3.20 (br m, 200H,
NHCH2CH2N and N(CH(CH3)2)2 of DIPEA side chain), 3.39
(br s, 3H, OCH3 of end group), 3.47–3.56 (m, 8H, (OCH2CH2O)2of end group), 3.60–3.69 (br s, 63H, OCH3 of PMA side chain),
3.69–3.72 (m, 2H, COOCH2CH2O of end group), 4.20–4.27 (m,
2H, COOCH2CH2O of end group), 7.10–7.30 (m, 5H, ArH of
end group). 13C NMR (125 MHz, CDCl3): d 174.9, 128.4, 127.0,
126.9, 126.2, 71.9, 70.6, 69.1, 69.0, 63.8, 59.0, 51.7, 48.7, 48.7,
45.3, 44.3, 42.7, 42.7, 41.3, 40.0, 35.1, 34.9, 32.1, 31.9, 29.6, 29.3,
23.1, 21.3, 20.8, 14.1. FTIR nmax/cm�1: 3295 (N–H amide
stretch), 2965 (alkane C–H stretch), 1737 (C]O ester stretch),
1647 (C]O amide stretch), 1535 (N–H amide bend), 1361 and
1185 (C–N stretch).
Self assembly techniques
Solvent switch. A general procedure for solvent switch is given.
The polymer was dissolved in DMF to a concentration double of
that required and stirred overnight. 18.2 MU cm�1 water was
added at 0.6 mL min�1, after which the opaque solution was
dialyzed against 18.2 MU cm�1 water, incorporating at least 6
water changes. The final concentration of the self-assembled
solution was calculated by measuring the final volume.
Direct dissolution. The polymer was dissolved in acidic water
(below pH 2.5) and was stirred overnight.
Size-switching studies. The polymer was dissolved at a
concentration of 0.25 mg mL�1 in acidic water (<pH 2.5). To
achieve the transition from micelle to vesicle, the pH was slowly
increased until a slight blue tint was seen and then stirred to allow
the particles to stabilize. The pH of the solution was dropped in
order to achieve the morphology change from vesicle to micelle.
The reversibility of the response was tested by repeating the pH
switch cycle.
Release studies. The polymer was dissolved in DMF at 2 mg
mL�1 after which Rhodamine B was added to a concentration of
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0.2 mg mL�1 and the solution was stirred overnight. 18.2 MU
cm�1 water was added at a speed of 0.6 mLmin�1. After addition
the solution was dialyzed against 200 mL of 18.2 MU cm�1
water. After leaving for at least 6 hours to allow the system to
equilibrate, the dialyzate was tested for fluorescence at an exci-
tation wavelength of 540 nm and the emission at 575 nm recor-
ded. After two water changes, where the system showed no
fluorescence, the solution was removed from the dialysis bag, the
pH reduced to approximately 2.5 and then dialyzed against
acidic water. Again, the system was left to reach equilibrium each
time the water was changed and the fluorescence recorded.
Fig. 1 SEC traces showing the chain extension of 2 with PFPA to form
block copolymer, 3.
Results and discussions
Block copolymer synthesis
Our goal was to create a diblock copolymer consisting of a
hydrophobic block, a responsive block which would change its
hydrophilicity in response to a change in pH, and a hydrophilic
head group that would direct self-assembly. There are many
other pH-responsive polymers that have been widely investigated
within the literature, mainly based on 2-(diethylamino)ethyl
methacrylate69–71 and 2-(dimethylamino)ethyl methacrylate,71
and the self-assembly and responsive behaviour of polymers of
these monomers have been studied. The polymer, poly(2-(N,N-
diisopropylamino) ethyl acrylate), investigated within this report
was chosen since it has been largely unexplored within the liter-
ature and it has been reported to be more stable than the ethyl-
and methylamine versions.72 Another reason this particular
monomer was chosen is due to a reportedly lower pKa for the
methacrylate version than that for the ethylamine or methyl-
amine equivalent.71 The higher pKas of the methyl- and
ethylamine equivalents render them hydrophilic at neutral pH,
whereas 2-(N,N-diisopropylamino)ethyl methacrylate
homopolymer was found to have a lower pKa, (ca. 6.0) meaning
it is hydrophobic at neutral pH and for our self-assembly
objectives this is desirable. To the best of our knowledge there are
no accounts of the desired monomer, 2-(N,N-diisopropylamino)
ethyl acrylate, being polymerized in the literature. The methac-
rylate version, 2-(N,N-diisopropylamino)ethyl methacrylate, has
been polymerized by ATRP72–74 and RAFT previously, although
in the case of RAFT polymerization the formation of diblock
copolymers led to a loss of control, shown by broad poly-
dispersities (Mw/Mn > 1.4).75–77 These polymers have potential in
drug delivery due to their pH responsivity.74 Attempts within our
group to directly polymerize 2-(N,N-diisopropylamino)ethyl
acrylate have been unsuccessful (see ESI Tables S1 and S2†).
Therefore in order to obtain a diblock copolymer containing this
functionality, a different route was followed. A scaffold polymer
comprising of poly(methyl acrylate) and poly(pentafluorophenyl
acrylate) was instead synthesized. The activated ester penta-
fluorophenyl acrylate was chosen as the resulting polymer could
then be easily substituted with amines61,62 such as N,N-diiso-
propylethylene diamine, resulting in the desired polymer
functionality.
The chain transfer agent (CTA) employed has been reported
previously.68 CTA 1 (see Scheme 1) was used to polymerize
methyl acrylate to form a block, 2,Mn (1H NMR)¼ 3.8 kDa,Mn
(CHCl3 SEC)¼ 2.5 kDa andMw/Mn¼ 1.06. This was then chain
This journal is ª The Royal Society of Chemistry 2012
extended with pentafluorophenyl acrylate to form the diblock
copolymer, 3, as a yellow solid, with an activated ester block
length of 100, Mn (1H NMR) ¼ 27.5 kDa, Mn (CHCl3 SEC) ¼7.7 kDa and Mw/Mn ¼ 1.29. The disparity between the Mn
calculated from NMR and the Mn given by SEC is due to the
solvophobicity of the polymer causing interactions with the SEC
column and the structural difference between the PMMA stan-
dards and the diblock 3. The efficient chain extension can be seen
by SEC analysis as shown in Fig. 1. A small amount of tailing is
observed for the reactive diblock copolymers. However, once the
PFPA block has been substituted, the polydispersity decreases
and tailing is not as pronounced (see ESI Fig. S4 and S7†).
Substitution of the PFPA groups and end group modification
In order to easily form two polymers (4 and 5) which bear the
same polymer backbone but different end groups, previously
established chemistries were used to substitute the penta-
fluorophenyl acrylate block61 and modify the end group54 at the
same time in a one-pot, two step method. Firstly, the PFPA
block was substituted with N,N-diisopropylethylenediamine and
the conversion of all the ester groups was confirmed by 19F NMR
spectroscopy. The disappearance of the broad polymer signals
at �153.8, �157.3 and �162.8 ppm and appearance of sharp
pentafluorophenol signals at �162.9 and �165.7 ppm was
observed, indicating the complete conversion of the activated
ester groups (see ESI Fig. S2†). The complete conversion was
also confirmed by analysis of the FT-IR spectra of the polymers.
The PFPA C]O ester stretch at 1783 cm�1 disappeared and was
replaced by a C]O stretch at 1646 cm�1, relating to the amide
group formed, with the MA ester stretch at 1737 cm�1 remaining
unchanged (see ESI Fig. S3†).
Subsequent addition of PBu3, hexylamine and the charged
acrylate monomer afforded the end group modification of the
polymer via thiol–ene chemistries. The trithiocarbonate group of
the RAFT end group was observed to have been removed by the
absence of a UV signal in the SEC analysis. The polymers were
purified by dialysis first against acidic then basic water and after
lyophilization the now white polymers 4 and 5were collected and
the full substitution of the PFPA block with the amine was again
confirmed by the appearance of new signals at 3.20, 3.60 and 3.80
ppm in the NMR relating to the NHCH2CH2 and the
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NHCH2CH2 and NCH(CH3)2 respectively. These peaks inte-
grate as expected when set against known signals, such as the
methyl acrylate side chain signals, which would not have been
affected by the substitution or end group modification processes.
The incorporation of the end group was observed by 1H NMR
spectroscopy. In the case of polymer 4, which bears the charged
tertiary amine end group, the appearance of new signals at 4.50
and 2.80 ppm for the CH2 next to the sulfur and the CH2 next to
the charged tertiary amine confirmed the successful end group
modification. In the case of polymer 5, which bears a triethylene
glycol end group, the CH3 signal of the TEGA end group is
clearly observable at 3.7 ppm as is the signal at 4.50 ppm which
relates to the CH2 next to the carbonyl group. The dispersity of
both the polymers were not negatively affected by the substitu-
tion as confirmed by SEC, 4: Mn (DMF SEC) ¼ 23.1 kDa and
Mw/Mn ¼ 1.19; 5: Mn (DMF SEC) ¼ 21.5 kDa and Mw/Mn ¼1.21).
Self-assembly properties
To investigate the self-assembly properties of these diblock
copolymers a solvent switch strategy was employed.78,79 The
polymers were dissolved in DMF at a concentration double to
that desired and then water was added slowly to achieve the
desired concentration, followed by exhaustive dialysis against
18.2 MU cm�1 water. For the charged polymer 4, a slightly
turbid solution with a pH of 7.4 and concentration of 0.16 mg
mL�1 was obtained after exhaustive dialysis. DLS measurements
showed the presence of large structures, Dh (by number) ¼ 340
nm with a dispersity, Ð, of 0.204. TEM analysis by drop depo-
sition onto a formvar grid, followed by staining with uranyl
acetate confirmed the presence of these large structures with an
average size of 353 nm (determined by counting at least 50
particles, see Fig. 2). No shrinkage of the particles relative to
Fig. 2 (Top) Schematic of morphology change of 4 with pH. (Bottom left)
uranyl acetate; (middle) DLS plot showing change in size with change in pH;
with uranyl acetate. Scale bars ¼ 200 nm.
3012 | Polym. Chem., 2012, 3, 3007–3015
their hydrodynamic diameters was observed in this case. This
perhaps is a coincidence or could be a result of the charged end
groups repelling each other, suggesting that the structure simply
collapses as it dries on the TEM substrate. We propose that these
nanostructures are vesicular in nature given the size of these
particles and also the predicted packing parameter based on the
amphiphile structure. To investigate the pH responsivity of
polymer 4 a small amount of the solution was taken and the pH
adjusted to 1.75 with dilute HCl, ca. 0.2 mL. Immediately the
turbidity disappeared and after stirring overnight smaller parti-
cles were observed by DLS analysis. These particles had a size (by
number) of 35.9 nm and a rather high Ð of 0.414. This large
dispersity is due to the presence of a larger population in the
intensity data, likely to be caused by the aggregation of the
micelles. This solution was further analyzed by TEMwith uranyl
acetate staining and spherical micelles with an average size of
31 nm were observed. These micelles seemed to be aggregated in
parts on the TEM grid, which supports our observation of
aggregation in the DLS results, see Fig. 2.
Polymer 5 was also self-assembled in a similar manner to
polymer 4 to give a slightly turbid solution at a concentration of
0.12 mg mL�1 at a pH of 7.8. Analysis by DLS showed large
structures with a size (by number) of 191 nm and a Ð of 0.074.
The presence of large structures was confirmed by TEM analysis,
with an average particle size of 126 nm. This is smaller than seen
in the DLS and we attribute this to either a staining artefact or
the drying and collapse of the vesicle on the TEM support. Once
again we propose that these nanostructures are vesicular in
nature. The pH of this solution was reduced to 3.7 with dilute
HCl (ca. 0.2 mL), which resulted in smaller structures with a Dh
by number of 45 nm observed in the DLS and analysis by TEM
confirming the presence of micelles with an average size of 34 nm,
see Fig. 3. The solutions had to be left stirring at least overnight
in order for the smaller structures to equilibrate. If left for less
Representative TEM image of 4 self-assembled at pH 1.75, stained with
(right) representative TEM image of 4 self-assembled at pH 7.4, stained
This journal is ª The Royal Society of Chemistry 2012
Fig. 3 (Left) Representative TEM of 5 self-assembled at acidic pH, stained with phosphotungstic acid; (middle) DLS graph showing the change in size
of 5 with pH; (right) representative TEM of 5 self-assembled at basic pH, stained with uranyl acetate. Scale bars ¼ 200 nm.
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time then multiple sizes were seen during DLS analysis. Since
such a small volume of acid was added to lower the pH and
induce the morphology change, no significant change in polymer
concentration occurred.
Since these self-assembled structures were observed to require
relatively long times to stabilize after a morphology transition
had occurred, we hypothesized that a smaller block length may
afford a faster morphology transition. Therefore a new PPFPA–
PMA scaffold, 7, was constructed. This new scaffold was
substituted with N,N-diisopropylethylenediamine and the end
groupmodified in the same manner as before, to form polymers 8
(Mn (DMF SEC) ¼ 14.2 kDa, and Mw/Mn ¼ 1.14) and 9 (Mn
(DMF SEC) ¼ 14.9 kDa and Mw/Mn ¼ 1.12). The successful
incorporation of the different end groups into the polymers 8 and
9 was once again confirmed by 1H NMR spectroscopy. The self-
assembly of these new polymers was investigated. Due to the
shorter hydrophobic block lengths in polymers 8 and 9, direct
dissolution was utilized rather than solvent switch. Polymer 8
was dissolved in acidic water at a pH of 2.25. After stirring, the
solution was analyzed by DLS and the presence of small struc-
tures with a Dh of 37 nm, Ð ¼ 0.39 was observed. Then dilute
NaOH was used to carefully raise the pH of the solution to 8.5,
above the pKa of the polymer, resulting in a turbid solution that
showed large structures in the DLS, with a Dh ¼ 97 nm and
Ð ¼ 0.101. This pH switching cycle was repeated three times,
Fig. 4 Graph showing the increase and decrease in size with change in
pH. The size change is repeatable and reversible.
This journal is ª The Royal Society of Chemistry 2012
with fully reversible and reproducible results, see Fig. 4. The
transition in both directions took only a short amount of time to
stabilize, typically 10 to 15 minutes, showing that the smaller
block lengths allow the morphology transition to happen more
quickly. Similar results were seen for polymer 9, see ESI
Fig. S13.†
Encapsulation and release of hydrophilic dye
Since the polymers form vesicles in neutral or basic environ-
ments, encapsulation of a hydrophilic species and release upon
acidifying the solution should be possible. In order to clearly see
any release, a hydrophilic fluorescent dye, Rhodamine B, was
chosen to be encapsulated in the polymer nanostructures. Poly-
mer 8 was self-assembled using solvent switch methods at a
concentration of 1.0 mg mL�1 in the presence of the Rhodamine
B at a concentration of 0.2 mg mL�1. The solution was then
dialyzed against a known volume of water and following equil-
ibration the water was changed and a sample taken for fluores-
cence analysis. This was repeated until no more Rhodamine B
was detected in the surrounding dialysis water. At this point the
pH of the solution inside the dialysis bag was measured as 7.5
and had a significant fluorescence response, showing that there
was Rhodamine B present, trapped within the interior water pool
of the vesicles. The pH of the polymer solution was then dropped
to pH 2.5 and stirred overnight, at which point the solution was
dialyzed against acidic water. Again the water was changed after
equilibration time and the dialyzate tested. There was a response
in the dialysis water immediately after the pH change, showing
that Rhodamine was released upon morphology change. This
demonstrated that the vesicles were able to encapsulate the
hydrophilic dye and release it in response to pH, see Fig. 5.
Conclusions
Polymer scaffolds bearing activated ester pentafluorophenyl
acrylate (PFPA) groups were successfully synthesized by RAFT
methods. The PFPA groups were easily substituted with N,N-
diisopropylethylene diamine and the RAFT end group modified
with either a charged tertiary amine acrylate or triethylene glycol
methyl ether acrylate, to give pH-responsive block copolymers
with the same backbone but different end groups. These poly-
mers were all found to self-assemble in aqueous solution at basic
Polym. Chem., 2012, 3, 3007–3015 | 3013
Fig. 5 Fluorescence graph of the dialyzate showing the release of
Rhodamine B upon lowering of pH. Solid line ¼ pH 7.5, dashed line ¼pH 2.5.
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pH to form vesicles and all exhibited a morphology transition to
a micelle upon lowering the pH. The larger block copolymers
took longer to stabilize after a morphology switch than the
smaller block copolymers. In addition the encapsulation and
controlled release of a hydrophilic dye, Rhodamine B, was
demonstrated.
Acknowledgements
The authors wish to thank the University of Warwick and
EPSRC for funding. The SEC equipment used in this research
was obtained through Birmingham Science City: Innovative
Uses for Advanced Materials in the Modern World with support
from Advantage West Midlands (AWM) and part funded by the
European Regional Development Fund (ERDF). Also thanks to
Mr Ian Portman-Hands (University of Warwick) for help with
TEM characterization.
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