construction of large-scale highly ordered macroporous monoliths of π-conjugated polymers
TRANSCRIPT
Communication
1940
Construction of Large-Scale Highly OrderedMacroporous Monoliths of p-ConjugatedPolymers
Zicheng Zuo, Yanbing Guo, Yuliang Li,* Jing Lv, Huibiao Liu,* Jialiang Xu,Yongjun Li
Large scale of well-ordered macroporous p-conjugated polymer monoliths have been success-fully prepared through a new approach using micrometer-sized naphthalene crystals astemplates. The macroporous monoliths of poly(p-phenylenevinylene) (PPV) and poly(p-phe-nyleneethynylene) (PPE) grew along the unidirectional freezing direction inside the templatenaphthalene crystals which lead to the formation ofcontrolling morphologies and homogeneousdiameters. The polymer monoliths show straightand lamella macroporous structures. The diametersof pores and the thickness of pore walls can becontrolled by tuning the freezing temperature.
Introduction
During the past decade, scientists have developed many
techniques for producing architectures of varied porous
materials due to their excellent properties on adsorbents,
separation materials, catalyst supports and hydrogen
storage.[1] Porous materials have been synthesized for
functionalmaterialswith controlled structures andproper-
ties and the porous structures with specific physical
properties was a key fundamental interest in porous
materials. Great efforts have been dedicated to the
preparations of 3D monolithic porous materials and 2D
porousmembranes.[2] However, the preparations of porous
materials are only limited on the inorganic compounds and
common polymers. Still, the design and fabrication of
Y. L. Li, Z. C. Zuo, H. B. Liu, Y. J. Li, Y. B. Guo, J. Lv, J. L. Xu,CAS Key Laboratory of Organic Solids, Beijing National Laboratoryfor Molecular Sciences (BNLMS), Institute of Chemistry, ChineseAcademy of Sciences, Beijing 100190, P. R. ChinaE-mail: [email protected]; [email protected]. C. Zuo, Y. B. Guo, J. Lv, J. L. XuGraduate University of Chinese Academy of Sciences, Beijing100080, P. R. China
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porous materials using functional polymers such as p-conjugatedpolymerswith controlled orderedporousarrays
are significant andongoinggreat challenges innanoscience
and nanotechnology. These functional conjugated porous
polymers provide compelling reasons for broad potential
applications as novel materials in organic electronics,
microfluidics, recognition and developing new applied
fields.[3,4] Recently, severalgroupshavedemonstratedsome
methods that are used to produce porousmaterials. Such as
themicroporousmonolithswere prepared by Sonogashira-
Hagihara coupling in the synthesis of polymers,[5] covalent
organic frameworks and the hyper-cross-linked poly-
mers;[6] emulsion templating methods are used widely to
produce well-defined porous polymers and inorganic
porous materials;[7] unconjugated polymer macroporous
monoliths were fabricated by using a metal–organic
coordination gel template[8] and the method of foaming.[9]
It is well known that p-conjugated polymers such as PPE,
PPV with many outstanding optical and electronic proper-
ties[10] and p-conjugated polymers can be easily
modified with various functional groups to construct
functional materials for applications in sensors,[11] organic
light-emitting diodes,[12] and field-effect transistors.[13]
However, the synthesis and properties of porous materials
DOI: 10.1002/marc.200900411
Construction of Large-Scale Highly Ordered Macroporous Monoliths . . .
based on functional p-conjugated polymers have not been
studied, and limited successes have been achieved in the
synthesis of non-conjugated porous polymers. One of the
most important items in preparing porous materials of p-conjugated polymers is in the development of the new
technique to overcome the small solubility originated from
the rigidmolecular structures of p-conjugated polymers.[14]
In this work, we propose a new concept of naphthalene
templating approach, which is a combination of naphtha-
lene crystals as templates and sublimation processes, to
preparewell-ordered porous PPV and PPEmonoliths. In this
approach, the naphthalene acts as a good solvent for
conjugated polymers when it is melted, and the naphtha-
lene crystals can act as ordered templates to synthesize
porous materials in unidirectional frozen. The unidirec-
tional frozen naphthalene can be easily removed by
sublimation at appropriate temperature, and the well-
ordered macroporous frameworks can be formed. The
preparation and the possible growth process of well-
orderedmacroporous structures based on the p-conjugatedpolymer PPV and PPE by the unidrectional freezingmethod
are shown in Scheme 1. In the preparation process, the
special solvent of naphthalene can be recycledmany times
without any pollution. This facile way is a low-cost and
environmentally friend method to prepare well-ordered p-conjugated polymer porous monoliths and it is also a well-
established method to tune synthesis of other organic and
inorganic porous materials.
Experimental Part
Preparation of Porous Polymeric Monoliths
The p-conjugated polymers PPE and PPV are synthesized according
to the reports.[15] The chemical structures of the polymers are
Scheme 1. Chemical structures of PPV and PPE (A) and the illus-trations of as-prepared well-ordered polymeric macroporousmonoliths by naphthalene templating. (B) The preparation ofthe structures by unidirectional freezing of naphthalene solutionof conjugated polymers. The temperature of the cold bath istunable. (C) The proposed growth process of well-ordered porousmonoliths. The straight naphthalene crystals with lamella struc-ture are formed.
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illustrated in Scheme 1A. To produce well-ordered polymer porous
monoliths, as-synthesizedPPE (100mg)andPPV(100mg)werewell
mixed with naphthalene powders (1 g) respectively. The polymer
concentrations were fixed at Cf¼9.1%. The mixtures were poured
into a test tubewith 10mmindiameter and 50mmin length. Then
the mixtures were stirred and heated to 110 8C in the oil bath. The
elevated temperature helps PPE or PPV to dissolve into themelting
naphthalenewhich is a good solvent for polymers. To preparewell-
ordered structures, the naphthalene solution containing polymer
PPE and PPV were transferred into the attemperator respectively,
which ensures that the temperature can be kept stable. Then the
PPV and PPE naphthalene solutions were lowered vertically into a
water bath of 10 8C at the rate (Vf) of 1 cm �min�1. After the tube
was entirely submerged into the water bath, it was kept in the
water for further 30min. The polymer solutions were frozen into
solid state and the main frameworks were formed. To prepare the
well-ordered porous structures with smaller wall thickness,
the freezing temperature (Tf) was declined and the solutions were
unidirectional frozen in a cold bath of �78 8C. Then the prepared
monoliths were transferred into the oil bath maintained at 45 8Cand aged in it for 6 h in order to further strengthen the main
frameworks. Finally, thenaphthalene in the sampleswas sublimed
completely at 40 8C for 5h by a vacuum condition (20 Pa). The
process for thepreparationofwell-orderedmacroporousmonoliths
is illustrated in Scheme 1B, and the possible formation process is
shown in Scheme 1C.
Characterization of Porous Polymeric Monoliths
Themorphologies of the prepared porous polymermonolithswere
examined by the field-emission scanning electronmicroscopy (FE-
SEM) Hitachi S-4300 at an acceleration voltage of 10KV and an
electrical currentof8mA.Before theSEMexaminations,all samples
were sputter coated approximately 5nm of gold. To further
investigate the well-ordered scaffolds and the optical properties,
the monoliths were carefully scraped into thin slices with a small
blade and theas-prepared sliceswere transferred onaglassplate to
performthe confocal laser scanningmicroscopy (CLSMthe FV1000-
IX81). The pore diameter distributions of the as-prepared porous
monolithswerecalculatedbymercury intrusionporosimetryusing
an instrument of PoreMaster GT 60. Themonolithswere subjected
to a pressure cycle starting from approximately 0.8 psi to 2300psi
in predefined steps to give pore diameter and pore volume
information.
Results and Discussion
The prepared porous polymer monoliths were character-
ized by scanning electron microscopy. Figure 1a is the
photograph of the large scale well-ordered PPV macropor-
ous monoliths prepared at Tf¼�78 8C by the naphthalene
templating method. SEM image of the vertical section of
PPVmonoliths (Figure 1b) showed that it was well-ordered
macroporous structures. As shown in Figure 1b, the porous
channels were almost parallel to each other along the
freezing direction and the length of the well-ordered
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Z. C. Zuo et al.
Figure 1. The well-ordered macroporous polymeric monoliths prepared at Tf¼�78 8C.(a) the photograph of large scale PPV. SEM images: (b) the vertical section of PPV, (c) thecross section of PPV. (d) The photograph of large scale PPE. SEM images: (e) the verticalsection of PPE, (f) the cross section of PPE. The arrow represents the growth direction.The insets were the magnified images of well-ordered pore walls corresponding to theircross sections.
Figure 2. SEM images of the cross sections of well-ordered PPV(a, b) and PPE (c, d) monoliths with different wall thickness. Themonoliths were prepared under the same immersion rates(Vf¼ 1cm �min�1), same polymer concentrations (Cf¼9.1%),different freezing temperatures (Tf). (a, c) Tf¼ 10 8C;(b, d) Tf¼�78 8C.
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macropores exceeded 500mm. The cross sections of
Figure 1c showed that vertical to the freezing direction,
the pore structures were also parallel to one another. The
inset magnified SEM image showed that the diameter of
well-orderedporeswasabout10mm.Figure1dshowed that
large scale well-ordered monoliths of PPE were also
produced by the naphthalene templating method.
Figure 1e and 1f also demonstrate that uniform parallel
channels were built and the porous channels were almost
paralleled to each other along the freezingdirection and the
vertical direction, respectively. The well-ordered channels
were as long as 400mm. The inset magnified SEM image
showed that the diameter of well-ordered channels of PPE
was about 10mm.
The well-ordered macroporous structures had the nacre-
likearchitecturesofsomenaturematerials, suchasshellfish
nacrewhichhadhighperformance.[16,17] Ournewnaphtha-
lene-based method provides an optional process for the
preparation of these high performance macroporous
materials. The new naphthalene-based process can be
comparedwith aqueous directional freezing process for the
production of aligned silica fibers,[18] zirconia fibers,[19]
porous alumina fibers[20] and microhoneycombs,[21] and
the CO2-based methods for the preparation of well-aligned
‘‘fish bone’’ porous materials,[22] where the porous struc-
tures are directed by the advancing of ice crystals and CO2
crystals. In the naphthalene-based method, the polymers
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were dissolved in the melting naphtha-
lene. The polymer solution was frozen
into the solid state with the decreasing
of temperatures. On the process of
solidification, the degressive tempera-
ture causes the phase separation in
the naphthalene solution, and the
long, straight naphthalene crystals
with lamella shape are generated inside
the system. Then the lamella naphtha-
lene crystals act as templates to induce
the solidification of conjugatedpolymers
along the freezing direction. Under 40 8C,the naphthalene crystals were subli-
mated in vacuum and the well-ordered
macroporous polymer architectures
were achieved. The macropores that are
templated from the spaces occupied by
thenaphthalenecrystals areproducedby
the following removal of naphthalene
crystals.
The wall thickness of the well-ordered
macroporous scaffolds and the width of
the pore diameter are extremely impor-
tant factors inbuilding catalyst supports,
photonic and electronic materials. It can
greatly affect the mass transfer ability
and the pressure drop in usages. The freezing temperatures
have great influence in tuning the wall thickness of the
orderedmacroporous structures. Figure2aand2c showthat
DOI: 10.1002/marc.200900411
Construction of Large-Scale Highly Ordered Macroporous Monoliths . . .
the wall thicknesses of PPV and PPE macroporous scaffolds
produced at 10 8C were both about 2mm. When the Tf was
decreased to �78 8C, the wall thickness rapidly reduced to
about 600nm and 500nm for PPV and PPE monoliths,
respectively (Figure2band2d). FromtheSEMimages, itwas
observed that the pore diameters were also affected by the
freezing temperatures. For the macroporous monoliths of
PPV, the pore diameters at 10 8C were about 8mm
(Figure 2a), and the pore diameters were decreased to
about 4mmat�78 8C (Figure 2b). At the same time, the pore
diameters had a rapid decrease from 8mm (10 8C) to 4mm
(�78 8C) in the PPEmacroporous scaffold (Figure 2c and 2d).
In this system, the pore diameters among paralleled walls
were thought to be influenced by the temperature gradient
in the liquid-solid interface and the solidification velocity,
which are important functions on the process of unidirec-
tional frozen formelt alloy.[23]When the polymer solutions
solidified at�78 8C, the temperature gradient in the liquid-
solid interfacewas greater than that of at 10 8C. The greatergradient caused the fast solidification of naphthalene, and
then thegrowth timeofnaphthalene crystals vertical to the
solidification direction was shortened. It was concluded
that wider pore diameters among walls can be produced
under higher freezing temperatures.[24] Therefore, the size
of pores can be tuned by controlling the solidification
temperatures.
Thewell-orderedmacroporous structures of PPV and PPE
were also confirmed by fluorescence images (Figure 3).
Figure 3 presents the fluorescence images of well-ordered
macroporous structures of PPV and PPE excited with
wavelength of 559nm. According to the fluorescent
properties of the polymers, PPV displayed red fluorescence
Figure 3. The fluorescence images of the well-ordered polymermonoliths. (a) PPV, Tf¼ 10 8C; (b) PPV, Tf¼�78 8C; (c) PPE,Tf¼ 10 8C; (d) PPE, Tf¼�78 8C. Vf¼ 1 cm �min�1, Cf¼9.1%. Bothof the samples were excited at 559nm.
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and PPE displayed yellow fluorescence when they were
excited with wavelength of 559nm. Figure 3a shows that
the PPV monoliths (Tf¼ 10 8C) were composed of well-
ordered pore structures. Figure 3b indicated that therewere
uniform well-ordered macroporous channels in PPV
monoliths (Tf¼�78 8C) and the channels are parallel to
one another.With decrease of the freezing temperature, the
wall thickness of PPV pores had a dramatically decrease
(Figure 3a and3b). Figure 3c and 3d also display that both of
PPE monoliths were composed of well-ordered uniform
pores and the wall thickness had an obvious decline by the
decrease of Tf. The average pore diameters of scaffolds PPV
andPPEpreparedat 10 8Cwere obviouslywider than that of
PPV and PPE produced at�78 8C. The pore diameters in the
fluorescence images were according to that in SEM images
(Figure2). Thepurefluorescence imagesofbothPPVandPPE
indicate that the naphthalene was completely removed
from the porous framework and the well-ordered macro-
porous monoliths could be prepared by the new naphtha-
lene-templating method.
The dependence of Tf and the pore size distribution have
been studied by the instrument of mercury intrusion
porosimetry. The curves in Figure 4 show that the pore
diameters of PPV and PPEmonoliths prepared at 10 8Cwere
larger than those prepared at�78 8C. Figure 4a showed that
the curve of well-ordered PPV scaffolds prepared at 10 8Chad a broad peak centered at 35mm, and Figure 4b showed
that the curve of well-ordered PPE scaffolds prepared at
10 8Chad a similar broad peak centered at 40mm.When the
freezing temperature declined to �78 8C, the curve of PPV
monoliths gave a broad peak centered at 7mm, and the
curve of PPE monoliths gave a similar broad peak centered
at about 6mm. The small peaks at about 3mm in Figure 4a
and 4bmight be caused by the damages of themacoporous
structures by the intrusion of mercury. It was shown that
similar pore diameter distributions of PPV and PPE
monoliths were produced at the same freezing tempera-
tures. Although the polymers concentration were kept
stable, the dramatic decrease in the average pore diameter
was observed when the Tf declined from 10 8C to �78 8C(PPV: from 6.07mm to 3.88mm; PPE: from 9.05mm to
2.62mm). The median pore diameters of PPV obtained at
10 8C are about 25.01mmand the pore diameters of PPE are
about 28.73mm. When the Tf rapidly decreased to �78 8C,the median pore diameters of PPV and PPE also rapidly
decreased to8.77mmand5.97mm, respectively. The specific
surface area of macroporous of PPV and PPE produced at
10 8C was about 4.68m2 � g�1 and 2.88m2 � g�1, and it
increased to 9.80m2 � g�1 and 8.65m2 � g�1, respectively.
Conclusion
We demonstrated a novel naphthalene-templating tech-
nique for controlled preparation of well-ordered porous
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Z. C. Zuo et al.
Figure 4. The curves of pore diameter distributions of PPV and PPE with well-orderedmacroporous structures (a) PPV, Tf¼ 10 8C, (b) PPE, Tf¼ 10 8C, (c) PPV, Tf¼�78 8C, (d) PPE,Tf¼�78 8C.
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monoliths of p-conjugated polymers. Our results show that
the pores can be formed in macroporous polymers by
the unidirectional freezing inside the template naphtha-
lene crystals. The wall thickness and macroporosity of the
polymermonoliths canbe tunedby controlling the freezing
temperature and rate. The approach may potentially be
extendable to the productions of well-ordered porous
functional materials for application in catalyst supports,
electronic materials, batteries materials and organic solar
cells.
Acknowledgements: This work was supported by the NationalNature Science Foundation of China (20831160507, 20873155 and20721061) and the National Basic Research 973 Program of China.
Received: June 11, 2009; Revised: July 10, 2009; Published online;August 27, 2009; DOI: 10.1002/marc.200900411
Keywords: p-conjugated polymer monoliths; naphthalene-tem-plating; unidirectional freezing; well-ordered macroporous
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