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Light scattering by cooperative diffusion in semi-dilute polymer solutions
M. Adam, M. Delsanti, G. Jannink
To cite this version:
M. Adam, M. Delsanti, G. Jannink. Light scattering by cooperative diffusion in semi- dilute polymer solutions. Journal de Physique Lettres, Edp sciences, 1976, 37 (3), pp.53-56.
�10.1051/jphyslet:0197600370305300�. �jpa-00231234�
LIGHT SCATTERING BY COOPERATIVE DIFFUSION
IN SEMI-DILUTE POLYMER SOLUTIONS
M.
ADAM,
M. DELSANTI and G. JANNINK Service dePhysique
du Solide et de RésonanceMagnétique,
Centre d’Etudes Nucléaires de
Saclay,
BP n°
2,
91190Gif-sur-Yvette,
France(Re~u
le 5janvier
1976,accepte
le 9janvier 1976)
Résumé. - La diffusion Rayleigh de la lumière par des solutions semi-diluées de
polymères
met en évidence une diffusion coopérative qui croit avec la concentration.
Abstract. 2014 We report measurements of relaxation times of the autocorrelation function for the Rayleigh line of light scattered by semi-dilute
polymer
solutions.Classification
Physics Abstracts
7.146-7.221-7.610-5.660
Recent observations of
polymer
diffusive motionsby light scattering
have dealt with two extreme situations : the very dilute solution[1, 2],
in whichchains
perform,
asentities,
diffusivemotion,
and thenetwork
[3]
with fixeddensity
of cross links. Here the deformation of the structurespreads
out as adiffusive motion. From a
systematic study
of theeffect of average molecular
weight
M in betweencross
links,
a remarkableproperty
of this motion[3]
was established in swollen networks : the diffusion coefficient
Ds,
which is the ratio of elastic modulus to friction coefficient isinversely proportional
tothe power law of M as found in the diffusion coeffi- cient
Do
in very dilute solution. Thissuggests
that the relevantquantity
for the Mdependance
ofDs
is the average distance between cross links.
The semi dilute solution is an intermediate situation which has been considered
by
several authors[4, 5],
as networks with a finite lifetime. Viscoelastic pro-
perties [4, 6]
have beeninterpreted
in this way. Howe- ver, the situation was described aspurely random,
i.e. with total lossof hydrodynamic
as well as excludedvolume
effects,
so that the distance betweenneighbour
cross links would scale in a trivial manner with concentration. De Gennes
[7]
has shown on thecontrary
that this distance reflects basiclong
chainproperties
and that thedynamical
correlations in semi-dilute solutions are of fundamental interest.We shall try to
present
hisarguments
as follows :1)
There is a characteristicfrequency 7~,
abovewhich the solution can be considered as a network and below which it is seen as individual diffusive motions of the
chains ; TR depends
upon molecularweight
and concentration of thepolymers.
Therange of values taken
by TR
is well suited to an expe-riment on
light scattering by
diffusive network deformation.2)
As in thepermanent network,
the diffusion coefficient associated withdeformation, D~, depends
upon the average distance between
adjacent
crosslinks.
However,
thislength
does notdepend
upon molecularweight
of the chains. It isonly
a functionof concentration
where kB
is the Boltzman constant, T thetempera-
ture, ilo theviscosity
of the solventand ~
thedyna-
mical
screening length,
identical to the static charac- teristic correlationlength [8]
where v is the excluded volume exponent
(v = -1
inthree
dimensions)
and d the dimension of space.De Gennes
[7]
established this result as a consequence of two non trivial identifications :first,
the elasticmodulus of the network scales with concentration like the osmotic pressure ;
second,
thehydrodynamic screening length
scales like the excluded volumescreening [8] length ~ (eq. (2)).
Evidence for this
dynamical
correlation is deter- mined from the timedependence
of the observed autocorrelation function for theRayleigh
line in alight scattering experiment.
Theexperimental
setup is the same as described before in reference
[1].
Since the network deformation
corresponds
to awell defined range of
frequencies,
it isimportant
that the
experiment
be carried out in the proper momentum transfer k =(4 7c/~)
sin(0/2)
domain.Article published online by EDP Sciences and available at http://dx.doi.org/10.1051/jphyslet:0197600370305300
L-54 JOURNAL DE PHYSIQUE - LETTRES
Following
reference[7]
the smallest momentumkmin
is
directly
obtained formTR
which
gives
where
RF
is the coil radius ofgiration
at zero concen-tration ;
the concentration C*corresponds
to thesituation where the average distance between
neighbour
coils isequal
toRF,
i.e. the coilsbegin
to
overlap.
The
upperlimit
of the momentum range isgiven by
Beyond kmax
the deformation modes are nolonger cooperative; they
propagatealong
each individualchain,
without any contribution to the network.Such modes have been observed
[2]
in very dilutesolutions,
for which however there are no collective deformations.The
appropriate k
range is shown infigure 1,
in betweenkmax
andkmin,
as a function ofC/C*.
ThekRF
versusC/C* plane
is further divided into 4regions : below kmin
andkRF
= 1(respectively
IIand
IF), corresponding
to diffusion of the center of mass ; abovekmax
andkRF
= 1(respectively
IIIand
III’),
in which the deformation of the individual chainsbegin
to contribute to thedecay
of the auto-correlation function.
Theory [7]
thuspredicts
that inregion I, figure
1 :a)
the autocorrelation function is asingle
expo- nential function oftime ;
b)
the inverse relaxation time’t" -1
isproportional to k2
c)
the diffusion coefficient isindependant
of mole-cular
weight
and varies with concentration asgiven by (1), (2),
i.e. asC3/4.
In
region II, propositions a)
andb)
are known toFIG. 1. - Representation of the range of concentration and momentum transfer for the predicted existence of cooperative
diffusive modes (I). The other regions correspond to diffusive
motion of the coil center of mass (II and II’), and to a superpo- sition of center of mass motion and coil deformation (III and III’).
The horizontal lines indicate the k values of the experiment
+ sample 1 ; ~ sample 2.
hold true ; but the diffusion coefficient is
essentially independent
of concentration and decreases with molecularweight. By
contrast, inregion III, theory
and
experiment
have shown[2]
that the autocorre-lation function must be fitted with at least two expo- nential functions.
The autocorrelation function was measured :
1)
at constantkRF,
for different values ofC/C*
(horizontal
lines infigure 1) ;
2)
at constantC/C*,
for different values ofkRF (vertical
line infigure 1).
The
polymer
used in thisexperiment
ispolystyrene
and the solvent is benzene. Characteristics of the
system
aregiven
in table I.TABLE I
Description of the polystyrene sample
in benzene solutionIn this concentration range of interest
(C > C*)
the solution contains many dust
particles trapped by
the
network,
whose effect can be seen on thelight
beam
through
thesample.
Thesignal
of thelight scattering experiment
isinterpreted
asheterodyne,
the local oscillator
being
thelight
scatteredelastically by
these dustparticles.
In the range CC*,
thelow
viscosity
of the solution allows the dustparticles
to fall to the bottom of the
cell,
so thesignal
is inter-preted
ashomodyne.
In order to match the observedvalues,
the relaxation times obtained in the dilute range aremultiplied by
a factor two.In all cases, the autocorrelation function was
fitted with a
single exponential.
Thequality
of thefit in
region
I is about the same as inregion
II. Wehave not tried to
improve
the fit inregion III,
since this is not theprimary
purpose of theexperiment.
A
typical
result is shown infigure 2,
where the inverse relaxation times aregiven
as a function of C.The value of
’t" - 1,
measured at different k values arenormalized to the same nominal k value
(kN)
accor-ding
to the rulewhere
iexp
is the value measured at k and whereCurve 1 in
figure
2corresponds
to the lower valuesof kRF (see
TableII).
BelowC *,
the inverse relaxation time’t" -1
isessentially
constant : it is identified asthe diffusion coefficient of the individual coils.
Beyond C*,
the valuesof r-’
are seen to increase : the diffusion iscooperative.
Thus aspredicted by
FIG. 2. - Normalized inverse relaxation times as a function of concentration : ’r -1 =
T-’ kNI k2
where 1:exp’ k2 are measured values and kN = 3.86 x 105 cm-1, + sample 1, . sample 2.Curve 1 : measured at kRF N 1. Curve 2 : measured at kRF > 1 ;
+ + + + + normalized inverse relaxation time exptrapolated
at C = 0, sample 1. MM normalized inverse relaxation time
extrapolated at C = 0, sample 2.
TABLE II
Description of
theexperiments
(*) The values of ~-1 normalized in the limit C -+ 0 are obtained
- from the diffusion coefficients reported in reference [1].
de
Gennes,
in semi-dilutesolutions,
the observed diffusion coefficient increases with concentration.We also notice that two different molecular
weights yield
the samet - 1
values inregion
I. This is to becompared
to the molecularweight dependence
inregion
II(Fig. 2,
curve1~).
Theslope
of curve 1 inregion
I is 0.7 ±0.05,
to becompared
to the theore- ticalvalue,
0.75.Curve 2
corresponds
to values ofkRF
far aboveunity.
This a border line case, sinceonly
a fewpoints
of this curve
belong
toregion
I. The effect of coil deformation modes at low concentration isclearly
seen in
region
III : the’t"-1
values have increased.The exact
contribution
of center of mass diffusion and individual coil deformation cannot be deter- mined from thesedata,
since we haveinterpreted
the autocorrelation function with a
single exponential (for kRF greater
thanunity,
thisprocedure
ismeanningful only
insideregion I).
As in case ofcurve
1, ’t"-1
increases with Cbeyond
C*. Theslope
is however much smaller
(0.42).
This fact may be attributed to the contribution of the individual coil deformationmodes,
as ifthey
coexisted with thecooperative
modes. There would be astrong
crossover effect in
reciprocal
space. Thispoint
is illustratedby figure 3,
where data at constantC/C*
areplotted
as a function of k. One would
expect z-1/k2
to beindependent
of k inregion
I. In fact this ratio increasesslightly
as k increases. Thedifficulty
ininterpreting
the data accross I and III’ is great, since the auto- correlation functions have very different
analytical
behaviours in I and III’
respectively (ref. [7]).
FIG. 3. - Inverse relaxation times divided by k2, for different
k values, at C/C * = 5.6.
Starting
from theboundary C/C *
=1,
we have tested the networkproperties
of the semi-dilutepoly-
mer solutions
by light scattering experiments.
The
cooperative
diffusion coefficient which isdirectly
obtained from thedecay
of the autocorre-lation increases with concentration.
This coefficient is
identically
the same for twomolecular
weights
of the coils.The situation is very different from the dilute-
solution,
for which the observed diffusion coefficientcleary
decreases with molecularweight
of the coil and for which there is nostriking
concentrationdependence.
There is a
difficulty
incomparing experimental
results and theoretical
predictions, arising
from thefact that the coil network is associated with a narrow
L-56 JOURNAL DE PHYSIQUE - LETTRES
range of
frequencies
in thevicinity
of C*. Howeverthe
qualitative
features observedclearly
indicate that the coils form a network as soon asthey overlap.
Note added in
proof.
- Dr. S. Candau has drawnour attention to the work of
Rehage, G., Ernst,
0.and
Fuhrmann, J.,
discuss.Faraday
Soc. 49(1970)
208 in which the
polymer
concentration diffusionis
reported
athigh
concentrations and which indi- cates a behaviour related to the resultspointed
in thisletter.
Acknowledgments.
- We wish to thank Pr. P.G. de Gennes for
suggesting
thisexperiment
andDr. S. Candau for
helpfull
criticism of themanuscript.
References
[1] ADAM, M., DELSANTI, M., to be submitted to J. Physique.
[2] KING, T. A., KNOX, A., MCADAM, J. D. G., Chem. Phys. Lett.
19 (1973) 351.
[3] MUNCH, J. P., CANDAU, S., DUPLESSIX, R., PICOT, C., BENOIT, H.,
J. Physique Lett. 35 (1974) 239.
See also DUPPLESSIX, R., Thesis. Strasbourg (1975).
[4] FERRY, J. D., Viscoelastic properties of polymers, New York, London (J. Wiley) 1961.
[5] JANESCHITZ-KRIEGEL, H., Adv. Polymer Sci. 6 (1969) 170.
[6] PETERLIN, A., Pure Appl. Chem. 12 (1966) 563.
[7] DE GENNES, P. G., to be submitted to Macromolecules.
[8] DAOUD, M., COTTON, J. P., FARNOUX, B., JANNINK, G., SAR-
MA, G., BENOIT, H., DUPLESSIX, C., PICOT, C. et DE GENNES,
P. G., Macromolecules 8 (1975) 804.