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Deformation mechanism of nanoporous materials upon water freezing and meltingMaxim Erko, Dirk Wallacher, and Oskar Paris Citation: Applied Physics Letters 101, 181905 (2012); doi: 10.1063/1.4764536 View online: http://dx.doi.org/10.1063/1.4764536 View Table of Contents: http://scitation.aip.org/content/aip/journal/apl/101/18?ver=pdfcov Published by the AIP Publishing Articles you may be interested in Phase diagram of supercooled water confined to hydrophilic nanopores J. Chem. Phys. 137, 044509 (2012); 10.1063/1.4737907 Freezing of mixtures confined in silica nanopores: Experiment and molecular simulation J. Chem. Phys. 133, 084701 (2010); 10.1063/1.3464279 Capillarity-driven deformation of ordered nanoporous silica Appl. Phys. Lett. 95, 083121 (2009); 10.1063/1.3213564 Origin of the enthalpy features of water in 1.8 nm pores of MCM-41 and the large C p increase at 210 K J. Chem. Phys. 130, 124518 (2009); 10.1063/1.3103950 Dynamics of ultrathin metal films on amorphous substrates under fast thermal processing J. Appl. Phys. 102, 104308 (2007); 10.1063/1.2812560
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Deformation mechanism of nanoporous materials upon water freezingand melting
Maxim Erko,1,2 Dirk Wallacher,3 and Oskar Paris1,a)
1Institute of Physics, Montanuniversitaet Leoben, Franz-Josef-Strasse 18, 8700 Leoben, Austria2Department of Biomaterials, Max-Planck-Institute of Colloids and Interfaces, Research Campus Golm,14424 Potsdam, Germany3Helmholtz Zentrum Berlin f€ur Materialien und Energie, Hahn Meitner Platz 1, 14109 Berlin, Germany
(Received 7 September 2012; accepted 15 October 2012; published online 1 November 2012)
Temperature-induced non-monotonous reversible deformation of water-filled nanoporous silica
materials is investigated experimentally using in-situ small-angle x-ray scattering. The influence of
freezing and melting in the nanopores on this deformation is treated quantitatively by introducing a
simple model based on the Gibbs-Thomson equation and a generalized Laplace-pressure. The
physical origin of the melting/freezing induced pore lattice deformation is found to be exactly
the same as for capillary condensation/evaporation, namely the curved phase boundary due to the
preferred wetting of the pore walls by the liquid phase. As a practical implication, elastic properties
of the nanoporous framework can be determined from the temperature-deformation curves. VC 2012American Institute of Physics. [http://dx.doi.org/10.1063/1.4764536]
The phase behavior of fluids and condensed matter –
particularly that of water – in nanometer confinement is a
fascinating interdisciplinary topic, which attracts scientists
from fields as diverse as geology, biology, chemistry,
physics, and nanotechnology.1 The gas-liquid and the liquid-
solid transitions in nanopores are well known to be shifted
with respect to their bulk condensation pressure and their
bulk freezing temperature, respectively. The basic physics of
these phenomena is satisfactorily described by classical ther-
modynamics, i.e., by the Kelvin equation for capillary con-
densation and by the Gibbs-Thomson equation for the
melting point suppression.2 Much work has been devoted to
go beyond these simple pictures by sophisticated experi-
ments and by atomistic modeling and simulation attempts.3
However, still little recognized is the fact that the confining
porous framework is never infinitely stiff and will, therefore,
deform as a consequence of the interaction of the guest phase
with the solid pore walls. Sorption induced deformation of
porous solids is known already since many decades4,5 and
has recently attracted renewed interest, one goal being the
design of sensing and actuating materials.6 Experimentally,
such deformation has mainly been studied as a function of
gas pressure during adsorption and capillary condensation of
fluids in various nanoporous systems,7,8 and theoretical work
as well as simulations have been undertaken to describe the
observed non-monotonous deformation behavior with
pressure.9,10
Non-monotonous deformation of nanoporous materials
has also been observed for condensed matter transitions as a
function of temperature, i.e., as a consequence of freezing
and melting.11–14 It has been pointed out already by Everett12
and later on by Faivre et al.14 that the thermal expansion of
the bulk liquid and solid cannot explain the experimental
facts, as organic fluids with “normal” and water with
“anomalous” expansion showed a very similar deformation
behavior. As yet, in contrast to the well-established picture
for sorption strains due to the gas-liquid transition in nano-
pores, a coherent explanation for the pore wall deformation
due to a liquid-solid transition in confinement is still missing.
Based on experimental data from in-situ small-angle x-ray
scattering (SAXS) on water-filled cylindrical nanopores of
uniform diameter (MCM-41), this Letter provides a quantita-
tive explanation for this phenomenon. We highlight the strik-
ing similarity between the deformation as a consequence of
capillary condensation/evaporation and the melting/freezing
transition. In fact, we demonstrate that these two phenomena
rely on exactly the same physical mechanism, namely the
change of the curvature of a liquid meniscus in contact with
the gas phase or the solid phase, respectively.
The experimental details of in-situ SAXS measurements
at constant temperature or constant pore filling of ordered
nanoporous materials with cylindrical pores on a 2D hexago-
nal lattice were already reported elsewhere.7,10,15,16 MCM-
41 samples with different pore diameter ranging from 4.4 nm
down to 2.0 nm diameter were investigated in the tempera-
ture regime between 100 K and 280 K. The porous samples
were filled with water from the gas phase at 280 K to the
desired filling fraction within a volumetric adsorption sys-
tem. More experimental details are given in Ref. 16. The de-
formation of the porous systems was quantified by the shift
of the Bragg reflections originating from the pore lattice.
The pore lattice strain is ePL(T)¼ (q0 / q(T))� 1, where q0 is
the scattering vector length of the reference Bragg peak posi-
tion of the water filled sample at 280 K, and q(T) is the corre-
sponding peak position at temperature T. We note that by
this definition, the strain is arbitrarily set to zero at the begin-
ning of the first cooling cycle starting at 280 K.
Strain versus temperature curves for a full cooling and
heating cycle are exemplarily shown in Fig. 1 for a sample
with 4.4 nm pore diameter at a nominal water filling fraction
f¼ 0.99. In contrast to the empty (evacuated) sample also
shown in Fig. 1, the pore lattice deformation of the water-
filled sample is not monotonous with temperature within the
a)Author to whom corresponding should be addressed. Electronic mail:
0003-6951/2012/101(18)/181905/4/$30.00 VC 2012 American Institute of Physics101, 181905-1
APPLIED PHYSICS LETTERS 101, 181905 (2012)
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studied region. Four roughly linear regimes with different
magnitude and sign of the slope of the ePL(T) curve can be
identified (see inset in Fig. 1). Starting with the heating cycle
at low temperature, ePL increases with a slope about a factor
3 higher as compared to the empty sample (region I). This
increase, extending over more than 100 K, is continued by an
abrupt decrease of ePL within a narrow temperature interval
of less than 10 K (region II). It follows a linear increase
(region III) and a leveling off (region IV). Upon cooling, a
qualitatively similar behavior is found, but a broad hysteresis
is present in region I, and in region II-IV, the two curves are
also shifted with respect to the temperature axis. The strain
minima separating regions II and III upon cooling and heat-
ing correspond exactly to the freezing (Tf) and melting (Tm)
temperatures of water confined in the 4.4 nm pores, as deter-
mined independently by differential scanning calorimetry
(DSC)17 and Raman scattering.18
This general behavior is valid also for samples with
smaller pores (3.9 nm and 3.4 nm diameter). In particular, the
dip at the border between the regions II and III shifts system-
atically towards lower temperatures with decreasing pore size
and coincides perfectly with the corresponding water freezing
and melting temperatures in confinement.17,18 Thus, the sharp
step in region II clearly indicates freezing/melting of the con-
fined pore water. The shallow increase of ePL in region I can,
therefore, simply be attributed to the (normal) thermal expan-
sion of ice confined within the pores. Since the thermal expan-
sion coefficient of ice is much larger than the one of silica, the
larger slope for the water filled samples as compared to the
empty silica sample in region I is reasonable. However, a
quantitative treatment is difficult since it is known that about
two monolayers of non-freezable water cover the pore walls
even at very low temperatures. A dynamical transition of this
liquid-like layer around 180 K has been proposed recently,16,19
which may be connected to the hysteresis seen in region I. We
further note that the basic features sketched in the inset in Fig. 1
are recognized also for samples with pore sizes below 3 nm.
Since for such small pores, no first order transition of water
in confinement takes place,16–18 and because the features are
strongly broadened with no clearly defined crossover
between the different regions, we do not include these data
in the subsequent analysis.
The pronounced contraction/expansion of the pore lattice
upon heating/cooling in region II obviously suggests assigning
this effect to the anomalous volume change between the liquid
and solid phases of the core water in the pores. However, sim-
ilar observations with the same sign of the deformation within
this region were reported from measurements with organic flu-
ids showing normal volume change upon freezing and melt-
ing.11,14 Moreover, after melting of the pore water, its volume
change with increasing temperature in region III should be
negative, and thus the progressively expansive deformation of
the pore lattice in this region is at least counterintuitive. Most
noteworthy, the strain curves within region III are all linear
with comparable slopes upon cooling and heating. This slope
decreases systematically with decreasing pore size. Before we
can introduce an explanation of the deformation behavior in
regions II and III, however we have first to answer a question
related to region IV.
The crossover from region III to IV upon heating coin-
cides exactly with the bulk water melting temperature of
273 K irrespective of the pore size, while this point is shifted
to lower temperatures (250–260 K) for the cooling cycle.
This indicates the freezing and melting of bulk ice at these
points upon cooling and heating, respectively, in the case of
freezing including a certain degree of supercooling. Since
the samples were filled from the gas phase to a nominal fill-
ing fraction of f¼ 0.99, there should, however, be no excess
water available outside the pores allowing bulk ice forma-
tion. Nevertheless, since the pores are open, they can take up
water molecules from the gas phase in the surrounding con-
tainer upon cooling. Moreover, since the water in the pores
expands below 277 K with decreasing temperature, this leads
also to an increase of the pore filling fraction. A rough esti-
mate together with the uncertainty related to the determina-
tion of the nominal filling fraction shows that condensation
of water outside the pores at the surface of the micrometer
sized MCM-41 powder grains is possible. In order to check
this experimentally, additional measurements with different
nominal pore filling fractions were performed for one of the
samples. Fig. 2 shows the strain curves obtained for the heat-
ing cycle at nominally f¼ 0.1 and f¼ 0.6 (partially filled),
f¼ 0.99 (filled), and f> 1 (overfilled). The filled and the
overfilled samples show almost perfect agreement in the
regions II–IV. Only in region I, the slope is different, which
may be related to the additional external constraint that in
the overfilled sample the whole grain is fully embedded into
bulk ice at low T. For a filling fraction of f¼ 0.6, there is no
more kink at 273 K, indicating that there is no more bulk ice
present, as expected. At this partially filled state, the meso-
pores are contracted already at high temperatures due to the
presence of concave liquid-vapor menisci.7 The slope of the
straight line in region III is similar to that of the empty
sample, the deviation being tentatively attributed to a
temperature-induced change of the interfacial energy
FIG. 1. Pore lattice strain versus temperature for the sample with 4.4 nm
pore diameter. The black circles are from the empty sample (filling fraction
f¼ 0). The blue (triangles down) and red (triangles up) curves stem from the
water filled sample (f¼ 0.99) for the cooling and heating cycles, respec-
tively. Freezing (Tf) and melting (Tm) temperatures of the confined pore
water are indicated, and the vertical dashed line is at 273 K. The inset
sketches the four temperature regions I–IV.
181905-2 Erko, Wallacher, and Paris Appl. Phys. Lett. 101, 181905 (2012)
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between the pore liquid and the surrounding vapor phase. This
deviation vanishes for filling fractions as low as f¼ 0.1 where
only a water film covers the pore walls.17 Here, the strain
curves show a roughly linear increase of the strain with tem-
perature for the whole region, the slope matching the one of
the empty sample. A deeper analysis on how temperature
affects the deformation behavior of partly filled samples goes,
however, beyond the scope of this Letter. The following dis-
cussion, therefore, focuses solely on water-filled nanopores in
contact with a bulk ice phase outside the pores.
We now return to the deformation behavior in regions II
and III. There is a remarkable similarity between the strain
as a function of temperature in water filled samples shown in
Figs. 1 and 2, and the “strain-isotherms” obtained during
adsorption and condensation of fluids as a function of the
reduced vapor pressure p/p0 at constant temperature T (see,
e.g., Fig. 1 in Ref. 7 or Fig. 6 in Ref. 10). In Ref. 7, the situa-
tion was interpreted within a classical thermodynamic pic-
ture with the experimentally observed pore lattice strain ePL
assumed to be proportional to the Laplace pressure P due to
a hemispherical liquid-vapor interface in the cylindrical
pores.
P ¼ 2ccoshR¼ MPL ePL; (1)
c¼ cLV is the liquid-vapor specific interfacial energy (surface
tension) and h is the wetting angle of the liquid phase. The
proportionality constant was denoted “pore load modulus”
MPL, which takes into account the peculiar loading situation
of the porous framework by a negative pressure within each
single pore, as well as the fact that the Laplace pressure
might not directly correspond to the bulk stress within the
pore walls. Combining Eq. (1) with the Kelvin equation
lnðp=p0Þ ¼ P Vm=ðRGTÞ, a direct proportionality between
ePL and ln(p/p0) results
ePL ¼1
MPL
RGT
Vmlnðp=p0Þ; (2)
Vm is the molar volume of the liquid phase and RG and T the
gas constant and temperature, respectively. Equation (2)
allows determining MPL from experimental data without
detailed knowledge of the surface tension cLV, the wetting
angle h, or the meniscus curvature radius R. It is even not
necessary to assume any details of the liquid-vapor interface.
A pictorial explanation of the strain isotherm for a fluid fully
wetting the pore walls is sketched in Fig. 3. Region I is
explained by the so called “Bangham effect,”4 i.e., the
adsorption of a wetting fluid at the pore walls lowers the
interfacial energy and leads to an expansive deformation of
the porous material. Region II is characterized by the sponta-
neous filling of cylindrical pores with radius R, with the neg-
ative Laplace pressure inducing a contractive deformation of
the pore lattice. In region III, finally, the liquid-vapor inter-
face is pinned at the pore ends, where the change of the cur-
vature according to the Kevin equation leads to an expansion
of the pore lattice with pressure until p¼ p0. The finite width
of region II is due to a (though small) pore size distribution
of the used MCM-41 materials. It has been shown by Schoen
et al.10 that the functional analysis of such data is even not
restricted to the presence of a curved liquid-vapor interface,
as an expression equivalent to Eq. (2) can be derived from a
thermodynamic analysis without taking any interfacial ge-
ometry into account. Nonetheless, we further stick to the
very useful concept of the curved interface to ease the fol-
lowing discussion for liquid-solid interfaces.
A liquid that wets the pore wall material in equilibrium
with its solid phase will be thermodynamically favored in
confinement. This is the simple physical reason for the melt-
ing point suppression of liquids in confinement. Formally,
the concept of the Laplace pressure from Eq. (1) is equally
applicable to a hemispherical liquid-solid interface within a
cylindrical pore, with c¼ cLS being now the liquid-solid spe-
cific interfacial energy.2 Within classical nucleation theory,
this quantity is formally furthermore connected to the Gibbs-
Thomson equation DT ¼ T0 � T ¼ 2cLSVmT0=ðR HmÞ, T0
being the bulk melting temperature and T the melting
FIG. 2. Lattice strain versus temperature for the sample with 3.9 nm pore
diameter during heating for four different nominal pore filling fractions.
f¼ 0.1 (black/circle), f¼ 0.6 (green/ diamond), f¼ 0.99 (red/triangle up),
and f> 1 (magenta/ squares). The melting temperature of water within the
pores (233 K)17,18 and the bulk melting temperature of water (273 K) are
indicated by vertical lines.
FIG. 3. Schematic view of the analogy between the vapor-liquid (upper
part) and the solid-liquid (lower part) phase transition mechanism in cylin-
drical nanopores, leading to the observed deformation behavior of the pore
lattice in regions II and III (middle part). The silica walls (dark grey) are in
contact with the (wetting) liquid water phase (blue/light grey) and with the
water vapor (upper part) or the solid ice phase (lower part) in white.
181905-3 Erko, Wallacher, and Paris Appl. Phys. Lett. 101, 181905 (2012)
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temperature of a (hemi-) spherical solid particle with radius
R, and Hm is the molar melting enthalpy. Assuming again
that the deformation of the pore lattice upon melting is pro-
portional to the generalized Laplace pressure given in Eq.
(1) with c¼ cLS, we obtain
ePL ¼1
MPL
Hm
VmT0
DT: (3)
This equation is very similar in its structure to Eq. (2) and
predicts a linear increase of the pore lattice strain with tem-
perature as experimentally observed in region III of our data
(see Figs. 1 and 2). The geometric situation is again sketched
in Fig. 3, with the solid-liquid transition in confinement
being fully analogous to the vapor-liquid transition in
regions II and III. Upon melting, in region II, a liquid bridge
forms at Tm out of the solid phase and grows parallel to the
pore axis until it reaches the pore end. Here, the liquid is
now in contact with bulk ice outside the pore via a hemi-
spherical meniscus creating a Laplace pressure, which leads
to the abrupt pore lattice contraction. In region III, the curva-
ture of this meniscus increases with temperature according to
the Gibbs Thomson equation, leading to a linear increase of
the strain with temperature until T reaches T0¼ 273 K. But
obviously, the analogy sketched in Fig. 3 does not extend to
region I, which is described by the Bangham effect for
adsorption and by thermal expansion of pore ice for heating
(see discussion above). It does also not apply to region IV,
where the detailed behavior will be strongly dependent on
the outer shape of the pore mouths and the grains and the
amount of water outside the pores. We stress once more that
the picture sketched in Fig. 3 for the liquid-solid transition
breaks down for partially filled pores since then, the pore liq-
uid will not anymore be in equilibrium with the bulk solid
phase outside the pores.
Equation (3) allows deducing the pore load modulus
from the slope of the strain-temperature curve in region III
(see Fig. 1), again without any detailed knowledge of the
geometric and energetic properties of the interface between
the two phases being required. Table I lists the values of MPL
obtained from the average of the cooling and heating cycles.
We note that there is no systematic difference of MPL
between heating and cooling, suggesting the concept to be
valid for both, the melting and the freezing transition. We
conjecture that the details of the hysteresis and the differen-
ces in region II may be rationalized by a more rigorous ther-
modynamic treatment,20 which is out of the scope of this
Letter. Table I also lists the MPL values obtained for the
liquid-vapor transition of pentane in the same samples using
Eq. (2).7 There is a systematic difference, with the values
obtained in this work being about 15% larger. This differ-
ence is not completely understood, since the determination
of MPL with Eqs. (2) and (3) does not require the knowledge
of any specific interfacial energy of the involved phases, but
only well-known fluid quantities. It is interesting to note that
for capillary evaporation, the pore load modulus for the ma-
terial with 3.9 nm pores was also larger for water (14.7 GPa)
as compared to pentane (13.9 GPa). Therefore, we attribute
this difference to the more complex interaction of water with
the pore walls, as chemical interactions would make the
application of the Kelvin- and the Gibbs-Thomson equations
more questionable.
We are grateful to G. H. Findenegg for discussions and
providing the samples; to A. Hoell, S. Haas, and D. Tatchev
for help with the experiments at the SAXS beamline of the
BESSY II storage ring at HZB Berlin; and to the European
LIght Sources Activity (ELISA) for financial support.
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TABLE I. Pore load modulus obtained from the freezing/melting of con-
fined water. The influence of the empty sample was corrected, and the values
used to calculate MPL with Eq. (3) were Hm¼ 6.01 kJ/mol, Vm¼ 1.8 10�5
m3/mol, and T0¼ 273 K.17 The modulus values are compared with those
obtained from the evaporation of n-pentane (C5H12) using Eq. (2) within the
same samples.7
1 Pore diameter nm MPL (this work) GPa MPLa GPa
2 3.4 18.9 6 1.2 15.8
3 3.9 16.5 6 0.3 13.9
4 4.4 12.8 6 1.5 11.2
aReference 7.
181905-4 Erko, Wallacher, and Paris Appl. Phys. Lett. 101, 181905 (2012)
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