Polymers in disordered environments
A brief review of our recent studies aiming at a better understanding of the scaling behaviour of polymers in disordered environments is given. The main emphasis is on a simple generic model where the polymers are represented by (interacting) self-avoiding walks and the disordered environment by cri...
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irk-123456789-1527792019-06-13T01:25:18Z Polymers in disordered environments Blavatska, V. Fricke, N. Janke, W. A brief review of our recent studies aiming at a better understanding of the scaling behaviour of polymers in disordered environments is given. The main emphasis is on a simple generic model where the polymers are represented by (interacting) self-avoiding walks and the disordered environment by critical percolation clusters. The scaling behaviour of the number of conformations and their average spatial extent as a function of the number of monomers and the associated critical exponents γ and ν are examined with two complementary approaches: numerical chain-growth computer simulations using the PERM algorithm and complete enumerations of all possible polymer conformations employing a recently developed very efficient exact counting method. 2014 Article Polymers in disordered environments / V. Blavatska, N. Fricke, W. Janke // Condensed Matter Physics. — 2014. — Т. 17, № 3. — С. 33604:1-11 — Бібліогр.: 82 назв. — англ. 1607-324X DOI:10.5488/CMP.17.33604 PACS: 64.60.al, 07.05.Tp, 64.60.ah http://dspace.nbuv.gov.ua/handle/123456789/152779 en Condensed Matter Physics Інститут фізики конденсованих систем НАН України |
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A brief review of our recent studies aiming at a better understanding of the scaling behaviour of polymers in disordered environments is given. The main emphasis is on a simple generic model where the polymers are represented by (interacting) self-avoiding walks and the disordered environment by critical percolation clusters. The scaling behaviour of the number of conformations and their average spatial extent as a function of the number of monomers and the associated critical exponents γ and ν are examined with two complementary approaches: numerical chain-growth computer simulations using the PERM algorithm and complete enumerations of all possible polymer conformations employing a recently developed very efficient exact counting method. |
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Blavatska, V. Fricke, N. Janke, W. |
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Blavatska, V. Fricke, N. Janke, W. Polymers in disordered environments Condensed Matter Physics |
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Blavatska, V. Fricke, N. Janke, W. |
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Blavatska, V. |
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Polymers in disordered environments |
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Polymers in disordered environments |
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Polymers in disordered environments |
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Polymers in disordered environments |
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Polymers in disordered environments |
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polymers in disordered environments |
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Інститут фізики конденсованих систем НАН України |
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2014 |
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Polymers in disordered environments / V. Blavatska, N. Fricke, W. Janke // Condensed Matter Physics. — 2014. — Т. 17, № 3. — С. 33604:1-11 — Бібліогр.: 82 назв. — англ. |
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Condensed Matter Physics |
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AT blavatskav polymersindisorderedenvironments AT fricken polymersindisorderedenvironments AT jankew polymersindisorderedenvironments |
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2025-07-14T04:16:28Z |
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Condensed Matter Physics, 2014, Vol. 17, No 3, 33604: 1–11
DOI: 10.5488/CMP.17.33604
http://www.icmp.lviv.ua/journal
Polymers in disordered environments
V. Blavatska1, N. Fricke2, W. Janke2,3
1 Institute for Condensed Matter Physics of the National Academy of Sciences of Ukraine, 79011 Lviv, Ukraine
2 Institut für Theoretische Physik, Universität Leipzig, Postfach 100 920, 04009 Leipzig, Germany
3 Centre for Theoretical Sciences (NTZ), Universität Leipzig, Postfach 100 920, 04009 Leipzig, Germany
Received June 18, 2014, in final form July 15, 2014
A brief review of our recent studies aiming at a better understanding of the scaling behaviour of polymers in
disordered environments is given. The main emphasis is on a simple generic model where the polymers are
represented by (interacting) self-avoiding walks and the disordered environment by critical percolation clusters.
The scaling behaviour of the number of conformations and their average spatial extent as a function of the
number of monomers and the associated critical exponents γ and ν are examined with two complementary ap-
proaches: numerical chain-growth computer simulations using the PERM algorithm and complete enumerations
of all possible polymer conformations employing a recently developed very efficient exact counting method.
Key words: self-avoiding walks, percolation clusters, PERM chain-growth computer simulations, exact
enumerations
PACS: 64.60.al, 07.05.Tp, 64.60.ah
1. Introduction
Polymers in chemical and biological physics are often characterized by a linear chemical architecture
and behave as (semi-)flexible chains. Typical examples of flexible polymers are synthetic polymers with
a carbon backbone, such as polyethylene, where the carbon bonds along the backbone can easily rotate
against each other [1–3]. Recently, much interest has been paid to semiflexible polymers, mostly because
important biopolymers such as DNA, actin filaments in eukaryotic cells and some other proteins belong
to this class [4, 5]. Typically, such biopolymers are supramolecular assemblies with a relatively large
monomer diameter representing many atoms. Some synthetic polymers also exhibit bending stiffness
over short distances along the chain. The competition between thermal energy and the bending energy
of the polymer sets a characteristic length scale, the persistence length lp, describing the crossover be-
tween two main regimes: for chain lengths much larger than lp, any polymer behaves as a flexible chain,
whereas for chain lengths much smaller than the persistence length, the polymer attains the limit of a
rigid rod.
The conformational properties, that is size and shape of polymer coils, play an important role in
models explaining the viscous flow and other hydrodynamic properties of polymer fluids. It is well estab-
lished [1–3] that under good solvent conditions the conformation of a flexible chain can be characterized
by a number of universal properties. This enables one to classify a broad variety of polymers, indepen-
dently of their precise chemical structure, into a single universality class in space dimension d . Physically
relevant cases are both polymers in three spatial “bulk” dimensions, d = 3, and polymers which are com-
pletely adsorbed onto a planar substrate and hence confined to two dimensions. A simple example is the
averaged radius of gyration RG, which defines the effective size of a typical N -monomer chain and obeys
the scaling law
〈R2
G〉 ∼ N 2ν
, (1.1)
where the universal exponent ν takes on the value ν = 3/4 in d = 2 dimensions [6] and ν = 0.587597±
0.000007 in d = 3 dimensions [7] for different flexible polymers in a good solvent. Another impor-
© V. Blavatska, N. Fricke, W. Janke, 2014 33604-1
http://dx.doi.org/10.5488/CMP.17.33604
http://www.icmp.lviv.ua/journal
V. Blavatska, N. Fricke, W. Janke
tant conformational characteristic is the universal averaged asphericity A [8], distinguishing completely
stretched, rod-like conformations (A = 1) from spherical ones (A = 0). For flexible polymers in good sol-
vents, independent of their chemical structure, A = 0.431± 0.002 in d = 3 [9], indicating a significant
anisotropy of polymer coil conformations. Due to universality, the conformational properties of flexible
macromolecules mentioned above are perfectly captured within the lattice model of self-avoiding walks
(SAWs) [10].
In general, the overall size and shape of a complex polymer macromolecule are controlled by the
monomer-monomer interactions, usually including van der Waals attraction and, if the constituents are
charged, also long-range Coulomb interaction. In continuum models, the hard-core repulsion and van
der Waals attraction can be modelled by Lennard-Jones potentials. Employing a lattice discretization
of space, one considers the so-called interacting self-avoiding walks (ISAWs) (sometimes also denoted
as “self-attracting self-avoiding walks (SASAWs)”), where apart from the self-avoidance constraint, rep-
resenting the hard-core potential, the van der Waals contribution is modelled by a nearest-neighbour
interaction,
H =−ǫNi . (1.2)
Here the parameter ǫ sets the energy scale and Ni counts the number of contacts of the polymer with
itself. This may be depicted as a step-like potential which qualitatively corresponds to a Lennard-Jones
interaction with large-distance cutoff. Such polymer models have been applied to a large variety of prob-
lems including protein folding (where ǫ depends on the type of interacting residues) and surface adsorp-
tion [11–19]. They provide a coarse-grained approximation to flexible Θ-polymers and are a suitable and
very efficient way for studying generic properties of the collapse and freezing transitions for relatively
long polymer chains.
In real physical processes, this ideal picture is further complicated by the fact that structural obstacles
(impurities) in the environment may alter the behaviour of the system. The density fluctuations of obsta-
cles may lead to a large spatial inhomogeneity and create pore spaces, which are frequently of fractal
structure [20]. The understanding of the behaviour of macromolecules in porous environments, that is
in the presence of structural disorder, e.g., in colloidal solutions or microporous membranes [21], is of
great importance in polymer physics. In particular, a related problem is relevant when studying the pro-
tein folding dynamics in a cellular environment. Biological cells can be described as a highly disordered
(“crowded”) environment due to the presence of a large amount of soluble and insoluble biochemical
species, which can be estimated to occupy up to 40% of the total aquabased volume [22, 23]. It is known
that structural obstacles strongly affect protein folding and aggregation [24]. Here, we will model the dis-
ordered environment generically by forcing the SAWs to only walk on the sites of percolation clusters at
the threshold value [25, 26] where they exhibit a self-similar, fractal structure [27].
As established by de Gennes [2], the scaling properties of infinitely long flexible polymers can be
evaluated by analyzing the critical behaviour of the n-component vector spin model in the formal n → 0
limit (so-called polymer limit). In particular, the polymer size exponent ν as defined in the scaling law
(1.1) is related by universality to the correlation length critical index of the n = 0-component model,
whereas the universal shape parameters of polymer chains can be computed by field theoretic methods
in terms of the critical amplitude ratios of this model [8]. Correspondingly, the problem of polymers in
disordered environments can be mapped to analyses of the critical behaviour of the randomly diluted
n-vector model in the polymer limit [28, 29].
Another class of problems concerns the behaviour of polymers in the presence of a planar substrate,
which can be either energetically neutral (presenting a purely geometrical constraint), or attractive for
the polymer [15–17, 30–36]. In the latter case, the polymer will be adsorbed to the surface at low tem-
peratures and desorbed at high temperatures. The adsorption of polymers on surfaces is a long-standing
problem which plays an important role in a number of technological applications (lubricants, stabiliza-
tion of colloids) and biology (adsorption of biopolymers onto membranes) [37]. For example, much in-
terest has been paid recently to experimental studies of the adsorption of peptides onto semiconductor
substrates [38, 39], being of particular importance for future sensory devices and pattern recognition at
the nanometer scale.
A subject of particular interest is the adsorption of polymers onto disordered (fractal) surfaces, since
naturally occurring substrates are usually rough and energetically (or structurally) inhomogeneous [40,
33604-2
Polymers in disordered environments
41], and the fractal surface geometry is known to have a crucial effect on adsorption phenomena [42,
43]. Already simple physical arguments suggest that by increasing the surface irregularity, the number
of polymer-surface contacts is strongly altered relative to the idealized planar surface without being
balanced by a loss in configurational entropy. This is a consequence of changes in the probability of
polymer-surface contacts with increasing roughness. A fractal surface is in general characterized by its
fractal dimension ds (ds = 2 corresponds to a flat surface). In particular, it was shown that adsorption is
enhanced (diminished), when the fractal dimension of the surface is larger (smaller) than 2 [44].
The rest of this mini-review is organized as follows. In the next section, the employed methods, PERM
chain-growth computer simulations and exact enumerations, are described and their merits and draw-
backs compared. Section 3 contains an overview of our results for the scaling behaviour of SAWs on
“bulk” percolation clusters and a shorter paragraph on the adsorption properties to a fractal surface. Fi-
nally, in section 4 we finish with some concluding remarks and give an outlook to ongoing and future
work.
2. Methods
Whereas for continuum polymer models Markov chain Monte Carlo (MC) and Molecular Dynamics
(MD) simulations are the methods of choice [45–47], for lattice polymer models alternative numerical
techniques may be employed that are better tailored to the problem at hand. The methods in a first class,
chain-growth algorithms, are based on stochastic sampling, similarly to standard MCmethods. In certain
situations, some variants are also suitable for continuum studies [48–50]. The second type, complete or
exact enumerations, on the other hand, explicitly exploit that the configuration space of lattice polymers
is discrete. Complete enumerations yield exact averages of the polymer statistics for a given lattice struc-
ture. The numerical complexity of the method, however, grows in general exponentially with the number
of monomers so that only relatively short chains (with of the order of 30÷50 monomers) can be inves-
tigated by this means. In the next two subsections, first the specific chain-growth algorithm “PERM” will
be briefly explained. Subsequently, for the special case of critical percolation clusters at the percolation
threshold as depicted in figure 1, it is shown how the exponential complexity of complete enumerations
can be reduced to a polynomial one when their self-similar fractal structure is exploited in a suitable way.
2.1. PERM chain-growth algorithm
The algorithm underlying the pruned-enriched Rosenbluth method (PERM) [51] is based on ideas
from the very first days of Monte Carlo simulations, the Rosenbluth-Rosenbluth (RR) method [52] com-
bined with enrichment strategies [53]. To grow a polymer chain, one places the nth monomer at a ran-
domly chosen nearest-neighbour site of the last placed (n−1)th monomer and continue iteratively until
the total length of the chain n = N is reached.
In order to obtain correct statistics, any attempt to place a new monomer at an already occupied
site results in discarding the entire chain. This leads to the problem of an exponential “attrition”, which
means that the number of discarded chains grows exponentially with the chain length N . Clearly, this
renders the method useless for long chains. In the RR method, occupied neighbours are avoided without
discarding the chain. This would introduce a bias in the proper statistics which, however, can be cor-
rected by giving a weight Wn ∼
∏n
l=2
ml to each sample conformation in the nth step, where ml is the
number of free lattice sites to place the l th monomer. When an ensemble of chains of total length N is
constructed, any new chain has to start from the same starting point, until the desired number of chain
conformations is obtained. The configurational averaging for, e.g., the end-to-end distance r ≡
√
R2(N )
is then given by
〈r 〉=
∑
confW conf
N
r conf
∑
confW conf
N
=
∑
r
r P (r, N ) , (2.1)
where W conf
N
is the Rosenbluth weight of an N -monomer chain in a given conformation and P (r, N ) is the
distribution function for the end-to-end distance.
33604-3
V. Blavatska, N. Fricke, W. Janke
Figure 1. (Color online) Example of a critical percolation cluster in two dimensions. Colors show the
chemical distance to the origin, which is in the red center. Sites more than 300 steps away are not shown.
While the chain grows by adding monomers, its Rosenbluth weight will fluctuate. PERM suppresses
these fluctuations by a population control, namely by “pruning” conformations with too small weights
and by “enriching” the sample with copies of high-weight conformations [51]. These copies are made
while the chain is growing and continue to grow independently of each other. Pruning and enrichment
are performed by choosing thresholds W <
n and W >
n depending on the estimate of the partition sum
Zn =
∑
confW conf
n of the n-monomer chain. These thresholds are continuously updated as the simulation
progresses. The zeroth iteration is a pure chain-growth algorithm without reweighting. After the first
chain of full length has been obtained, we switch to W <
n , W >
n . If the current weight Wn of an n-monomer
chain is less than W <
n , a random number r=0,1 is chosen; if r=0, the chain is discarded, otherwise it is
kept and its weight is doubled. Thus, low-weight chains are pruned with probability 1/2. If Wn exceeds
W >
n , the conformation is doubled and the weight of each copy is taken as half the original weight. To up-
date the threshold values, one may apply similar empirical rules as in [12, 13, 54]: W >
n =C (Zn/Z1)(cn/c1)2
and W <
n =0.2W >
n , where cn denotes the number of the created chains having length n, and the parameter
C É 1 controls the pruning-enrichment statistics. After a certain number of chains of total length N is
produced, the iteration is finished and a new so-called tour starts.
2.2. Exact enumeration
The straightforward exact enumeration method for SAWs is to use brute force and generate all pos-
sible conformations; see [55–57]. However, the computational work load becomes rapidly prohibitively
high since the number of walks Z increases exponentially with the number of steps N ,
Z ≃µN Nγ−1
= Nγ−1
e
N lnµ
. (2.2)
Here, γ is another universal exponent depending only on the dimension and µ is the non-universal so-
called connectivity constant which besides the dimension does also depend on the details of the consid-
ered lattice.
Fortunately though, we recently discovered that the fractal structure of percolation clusters offers a
way to circumvent this problem [58, 59]. The actual implementation of our method is rather complicated
and will not be explained here in detail, but the basic ideas are fairly simple. The key lies in the obser-
vation that the critical clusters are very weakly connected, so that they could be divided by cutting only
a small number of bonds. Thanks to the self-similarity, this applies on all length scales. We can, there-
fore, partition the cluster into a hierarchy of nested “blobs” with very few interconnections in order to
factorize the enumeration (see figure 2). This factorization property is the main clue of the method.
33604-4
Polymers in disordered environments
Figure 2. (Color online) Decomposition of a critical percolation cluster into nested blobs and the corre-
sponding tree hierarchy. The starting position of the SAW is marked black (in blob A).
We start by enumerating all SAW segments of any length through the smallest blobs and divide them
into different classes, depending on how they connect the different entries to the blob. For instance, if a
blob has two connections (a and b) to its parent in the hierarchy, we distinguish between the following
classes: segments starting at a and terminating within the blob, segments starting at b and terminating
within the blob, and segments connecting a and b. For the terminating segment classes, we also mea-
sure the mean distance of the chain end to the origin. We then “renormalize” the smallest blobs, treating
them essentially as point-like, while we repeat the procedure for the next larger blobs that contain them.
The new segments should then be matched with the right segment classes from before to determine their
multiplicity and average end-point distances. This scheme is applied repeatedly going to ever larger blobs
and ultimately the whole percolation cluster. Correctly implemented, this method achieves polynomial
(rather that exponential) increase of computation time with the number of steps, thus allowing for walks
of several thousand steps. In fact, we can exactly enumerate as many as 101000 chain conformations —
which with standard techniques would take very long indeed (well, with current computers much longer
than the estimated age of our Universe . . . ). Our recursive algorithm can be used in any dimension as
is illustrated in figure 3 for the three-dimensional case, but we have only recently generalized our com-
puter implementation to more than two dimensions [60, 61], so that results for physical quantities on
percolation clusters in three or more dimensions are still somewhat premature.
The efficiency of our recursive enumeration method depends on the self-similar, fractal blob-like
structure of the critical percolation clusters, allowing a factorization of the counting problem. Away from
the percolation threshold, its performance deteriorates and PERM chain-growth simulations may be supe-
rior. Also, for measuring more detailed shape characteristics, such as the full gyration tensor and related
universal shape invariants [62, 63] as well as for a generalization to Θ-polymers [63, 64], PERM is more
flexible. So in this sense the two methods are complementary to each other.
3. Results
Let us start with our results for the scaling properties of SAWs on d -dimensional critical percolation
clusters [65–69]. To be precise, in the PERM simulations we rather considered the (geometric) backbone
of the cluster which is the subset of the cluster consisting of all bonds (or sites) through which a “current”
can flow, i.e., it is the structure left when all “dangling ends” are eliminated from the cluster. The usual
argument is that SAWs can be trapped in such “dangling ends”, so that infinitely long chains can only
exist on the backbone of the cluster.
In the PERM simulations, we adjusted the pruning-enrichment control parameter such that on aver-
age 10 chains of total length N (= 90,80,70 in d = 2,3,4) are generated per iteration [12, 13], and per-
33604-5
V. Blavatska, N. Fricke, W. Janke
Figure 3. (Color online) Computation time (in seconds on a typical 3 GHz PC) needed for the complete
enumeration of all conformations of an N -step self-avoiding walk on a critical percolation cluster in
three dimensions using our recently developed recursive exact enumeration algorithm. The straight lines
in the log-log plot clearly indicate a power-law dependence on N instead of the exponential increase for
standard enumeration techniques.
formed 106 iterations. Also, what is even more important for efficiency, we made sure that in almost
all iterations at least one such a chain was created. By comparison with our exact enumeration results
for randomly selected clusters, we have recently checked [70] that once PERM has managed to squeeze
the chains through the bottlenecks of the percolation cluster, the convergence to the exact result is very
fast. Initially, however, PERM needs a sufficient period of time to explore the landscape and to adjust the
thresholds of the population control.
In the given problem we have to perform two types of averaging: The first average is performed
over all SAW conformations created with PERM on a single backbone according to (2.1), and the second
average is carried out over different realizations of disorder,
〈r 〉=
1
Nc
Nc
∑
i=1
〈r 〉i , (3.1)
where Nc is the number of different clusters. In our PERM simulations we took Nc = 1000.
In this way we arrived at the data for the end-to-end distance shown in figure 4 [65]. To estimate the
critical exponent νpc , we employed in a log-log representation linear least-square fits with varying lower
cutoff for the number of steps Nmin. The χ2 value (sum of squares of normalized deviation from the
regression line) serves as a test of the goodness of fit and thus determines fit ranges where the leading
scaling ansatz (1.1) is acceptable. The resulting estimates of the exponent νpc [65] are compiled in the
second last line of table 1, where previously obtained results [71–76] are listed also for comparison.
With our new exact enumeration scheme, we have so far only analyzed the two-dimensional case
[58, 59]. Our result for νpc in the last line of table 1 is based on walks with up to N = 1000 steps averaged
over 200000 percolation clusters at pc (working here with the full cluster, not the backbone). In the least-
square fit to the scaling law (1.1), the first 500 steps were excluded to reduce finite-size effects. In the
meantime we have extended our exact enumeration program to up to seven dimensions, and by several
technical refinements of the actual computer implementation we can now handle walks with over 10000
steps exactly. The data analysis, however, is still in progress and will be reported elsewhere [60, 61].
Estimates of the exponent γ in (2.2) are much more difficult to obtain since γ appears in the sublead-
ing term, which in the present context is a severe problem because Z exhibits strong fluctuations from
cluster to cluster. In fact, the distribution of Z has log-normal character due to the fact that Z is effectively
a product of random variables. Still, performing least-square fits to
ln Z
N
=
ln A
N
+ lnµ+ (γ−1)
ln N
N
, (3.2)
33604-6
Polymers in disordered environments
Figure 4. Disorder averaged end-to-end distance vs the number of steps obtained in PERM chain-growth
simulations in double logarithmic scale for SAWs on the backbone of percolation clusters in d=2 (pluses),
d=3 (stars), d=4 (open squares). Lines represent linear fitting, statistical error bars are of the size of
symbols.
we obtain for instance in two dimensions from PERM simulations [68] the estimates µ = 1.566±0.005,
γ = 1.350±0.008 and from the exact enumerations [58] (in the interval N = 10−50) µ = 1.567±0.003,
γ= 1.35±0.03, which are in surprisingly close agreement. Note that µ is basically given by the product of
the connectivity constant for the regular square lattice and the percolation threshold (2.6385×0.592746 =
1.5639) and that γ is hardly distinguishable from its value for the regular two-dimensional lattice (γ =
43/32 = 1.3437. . . ). With PERM we have estimated µ, γ also in three and four dimensions [68], whereas
the exact enumeration data still have to be analyzed [60, 61].
As an interesting side result, we obtained with PERM also numerical estimates for the averaged as-
phericity, prolateness, and size ratio of the chains in two and three dimensions [62]. All these shape
characteristics can be expressed in terms of combinations of the components of the gyration tensor. They
increase gradually with increasing polymer chain length— the fractal structure of the percolation cluster
drives the longer polymer chain conformations to become more and more prolate. Our results quantita-
Table 1. Estimates of the exponent νpc for SAWs on critical percolation clusters. EE: exact enumerations,
RG: field-theoretic renormalization group, MC: Monte Carlo simulations. For SAWs on the regular lattice
one has: νSAW(d=2)=3/4 [6], νSAW(d=3)=0.587597±0.000007 [7], νSAW(d Ê 4)=1/2.
νpc \ d 2 3 4
EE [71] 0.770±0.005 0.660±0.005
[56] 0.778±0.015 0.66±0.01
[56] 0.787±0.010 0.662±0.006
RG [72] 0.785 0.678 0.595
[73] 0.796 0.669 0.587
MC [74] 0.77±0.01
[75] 0.783±0.003
[76] 0.62–0.63 0.56–0.57
PERM [65] 0.782±0.003 0.667±0.003 0.586±0.003
EE [58] 0.7754±0.0015
33604-7
V. Blavatska, N. Fricke, W. Janke
Figure 5. (Color online) Sketch of a polymer chain grafted with one end to a randomly selected site of
an attractive two-dimensional percolation cluster modelling a fractal surface with fractal dimension
d
pc
s = 91/48 ≈ 1.896 < 2.
tively indicate that the shape parameters of typical polymer conformations change significantly relative
to the obstacle-free case. For example, we obtained for the (universal) asphericity of SAWs in three di-
mensions 〈A3〉 = 0.435±0.002 on a regular lattice in good agreement with [9] and 〈A
pc
3
〉 = 0.743±0.005
on critical percolation clusters: The shape tends to be more anisotropic and elongated due to the fractal
structure of the disordered environment.
Let us finally briefly comment on the conformational statistics of polymers interacting with disor-
dered substrates. Particularly interesting is the case of an attractive substrate, where below a critical
temperature TA , a second-order phase transition into an adsorbed state takes place. As order param-
eter, one considers the fraction Ns/N , where Ns is the average number of monomers adsorbed to the
surface and N is the length of the polymer chain. In the limit of long chains, it obeys the scaling law
〈Ns〉/N ∼ Nφs−1, where φs is the so-called surface crossover exponent [30]. In the language of lattice
models, disordered surfaces can be modelled as a two-dimensional regular lattice with different types of
randomly distributed defects as sketched in figure 5. Fractal properties emerge at the (two-dimensional)
percolation threshold where a spanning percolation cluster of attractive sites with fractal dimension1
d
pc
s = 91/48 ≈ 1.896 < 2 appears [77].
In reference [78] we have studied this problemwith the help of PERM. We examined the behaviour of
the components of the radius of gyration 〈R2
g||
〉, 〈R2
g⊥
〉 in directions parallel and perpendicular to the
surface and found that the critical exponent governing the scaling of the size of the polymer chain
adsorbed on the fractal substrate is larger than that for a homogeneously attractive surface. A value
ν
pc
2
= 0.772± 0.006 is obtained [78, 79], to be compared with the compatible result ν
pc
2
= 0.782± 0.003
for the average size of a polymer strictly confined onto a two-dimensional percolating cluster [65, 68] and
ν2 = 0.742±0.006 ≈ 3/4 for a plain surface. Examining the peak structure of the heat capacity, we obtained
an estimate for the surface crossover exponent of φ
pc
s = 0.425±0.009, compared to φs = 0.509±0.009 for
the plain surface [78, 79]. As expected [44], the adsorption is diminished when the fractal dimension of
the surface is smaller than that of the plain Euclidean surface due to the smaller number of contacts of
monomers with attractive sites.
1Please note that in references [65, 66, 68, 78, 79] inadvertently a wrong value of 91/49 has been quoted. In table 2 of refer-
ence [68], this led to an incorrect value of 7/9 (≈ 0.7777.. . ) for a Flory-type approximation, which properly should read 144/187
(≈ 0.7700.. . ).
33604-8
Polymers in disordered environments
4. Concluding remarks and outlook
The scaling behaviour of polymers in disordered environments is a longstanding problem that has
been investigated inmany publications over the last 25 years. At a closer look, however, there still remain
many open questions and controversial issues. In most numerical studies so far, for technical reasons the
length N of the polymer chains has been quite short, so that it is not guaranteed at all that the true
asymptotic behaviour has been observed. This issue is for instance important when discussing whether
SAWs on the backbone of a critical percolation cluster exhibit the same critical exponents as on the full
cluster. Our recently further improved exact enumeration scheme [60] allows us now for the first time
to study the chains in up to d = 7 dimensions with over 10000 monomers exactly and hence offers a
completely new perspective. Our preliminary data analysis indeed suggests that new insights into an old
problemmay be expected in the near future.
It is also possible to generalize our enumeration method to Θ-polymers in disordered environments
which enables us to study with unprecedented accuracy the collapse and freezing transitions of IASWs
on critical percolation clusters. A stretching force [26, 57, 63, 64, 80, 81] can also be taken into account.
Finally, a careful comparison with related random walk types, e.g., kinetic growth walks [82], may shed
new light on the rather involved statistical properties of polymers in disordered environments.
Acknowledgements
This work has been supported by an Institute Partnership Grant “Leipzig–Lviv” of the Alexander von
Humboldt Foundation. Financial support by the Sächsische DFG Forschergruppe FOR877 under Grant
No. JA 483/29-1 and the DFG Sonderforschungsbereich SFB/TRR 102 (project B04) is gratefully acknowl-
edged.
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Полiмери у невпорядкованих середовищах
В. Блавацька1 , Н. Фрiке2, В. Янке2,3
1 Iнститут фiзики конденсованих систем Нацiональної академiї наук України, 79011 Львiв, Україна
2 Iнститут теоретичної фiзики, Унiверситет Лейпцига, 04009 Лейпциг, Нiмеччина
3 Центр теоретичних дослiджень (NTZ), Унiверситет Лейпцига, 04009 Лейпциг, Нiмеччина
Подаємо короткий огляд наших недавнiх дослiджень, метою яких є краще розумiння скейлiнгової по-
ведiнки полiмерiв у невпорядкованих середовищах. Основна увага придiляється простiй узагальненiй
моделi, в рамках якої полiмери представляються як (самовзаємодiючi) випадковi блукання iз самопере-
тинами, а невпорядковане середовище — як критичний перколяцiйний кластер. Проаналiзовано скей-
лiнгову поведiнку кiлькостi можливих конформацiй та усередненого просторового видовження полiмера
як функцiї кiлькостi мономерiв, а також отримано значення вiдповiдних критичних показникiв γ та ν,
застосовуючи два взаємодоповнюючi пiдходи: чисельнi симуляцiї в рамках алгоритму зростаючого лан-
цюжка (PERM) та точний перерахунок всiх можливих конформацiй iз використанням недавно розвиненої
дуже ефективної методики.
Ключовi слова: випадковi блукання, перколяцiйний кластер, комп’ютернi симуляцiї зростаючого
ланцюжка (PERM), методи точного перерахунку
33604-11
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http://dx.doi.org/10.1103/PhysRevLett.98.048101
http://dx.doi.org/10.1103/PhysRevLett.98.128101
Introduction
Methods
PERM chain-growth algorithm
Exact enumeration
Results
Concluding remarks and outlook
|