ARCHIEF
IN DILUTE SOLUTION
SUBJECTED TO A HYDRODYNAMIC. SHEAR FIELD
F.R. Cottrell, EW. Merrill, and K.A. Smith
Technica.l Report Prepared For
Office of Naval Research Contract Nonr 3963 (10)
Task NR 062-333 (1970)
This document. has been. approved for. public release and. sale; its distribution is unlimited.
Lab. v. Scheepsbo.uwkuncle
Technische Hogeschool
Deift
) DOCUMEHTATIE-d
eelc van de Onderafdeling d ouwkurn3eConformation of Polyisobutylene in Dilute
Solution Subjected to a Hydrodynaznic Shear Field*
F. II. COTTRELL, E. W. MERRILL, and K. A. SMITH, Department of Chemical EngineerIng, Massachusetts Institute of Technology, Cambridge,Massachusetts 02139
Synopsis
A new light-scattering experiment which allows a direct determination of the
con-formation of macromolecules deformed in flow is descnbed. Light-scattering
relation-ships based on the interference function are developed, and results of an experimental
study are detailed The deformed conformation of high molecular weight
polyiso-butylene was determined in a Couette-type shear field. Decalin was the solvent.
Vari-ables investigated were the shear rate (0 to 600 sec'), the polymer molecUlar weight
(1.0 X 10 to 1.6 X l0), and the polymer concentration (2.0 X lO' to 8.0 X l0
g/cc). Conformation variables determined were the orientation of the molecule in the shear field and its maximum and minimum extension ratios in the plane defined by the
direction of flow and the direction of the shear rate. The deformation of the molecule was found to be markedly discrepant when compared to the dynamic
macro-molecular models which assume complete coil flexibility, and more closely in agreement
with the recent theories of Cerf, developed for nonfree-draining coils which exhibit a
finite internal viscosity.
INTRODUCTION
The conformation of random coiling polymer molecules subjected to a hydrodynamic shear stress in dilute solution has been the subject of con-siderable interest for the past three decades. Several theoretical relation-ships exist in the literature'5 which account for the statistical shape of a series of macromolecular models in terms of the statistical distñbuti6n of distances separating the chain ends. Other relationships exist from models of the coil as an elastic sphere.6
Both categories qualitatively agree as to the nature of the coil
conforma-tion under flow condiconforma-tions. The originally spherical statistical shape of the random coil takes on an effipsoidal shape when subjected to a simple shear field. Deformation occurs in the plane defined by the flow and shear rate directions where motion of the segments can best be described as a tank tread rotation. Thai is, the time-averaged conformation of the macro-molecule rern.ins fixed while the segments rotate in an ellipsoidal path
This paper was presented in part at the International Symposium on Macromolecular Chemistry, Toronto, Canada, 1968.
416 corrilELL, MERRILL, AND SMITH
Fig. 1. Theoretical rnacromolecular statistical shape in a simple shear field. around the center of mass of the macromolecule. An illustrative example
of this behavior is shown in Figure 1.
Experimental evidence of the magnitude of the coil deformation has never been unequivocally determined. Birefringence measurements have allowed the determination of the orientation of the deformed coil but an absolute measure of the extent of coil deformation has, until now, been de-pendent upon theoretical estimates. Accordlingly, we have developed an experimental technique, based on the theories of light scattering, which allows the direct determination of the deformed macromolecular
conforma-tion under flow condiconforma-tions.
To further elucidate the nature of the deformed macronaolecular con-formation, the shear dependence of the intrinsic viscosity was also
deter-mined The results of these measurements will be published in another
paper.
LIGHT SCATTERING
It has been recognized for some time that light. scattering would allow a direct determination of the deformed conformation of the random coiling macromolecule in flow.
Relationships exist in the literature9 which
describe the theoretical interference of the light which would be scattered from macromolecules deformed according to the dumbbell model and theRouse model. It is also shown here that light-scattering experiments will
allow a direct determination of the flow deformed macromolecular
con-formation independent of any macromolecular model.
The parameter from which conformation information is determined is the inverse of the interference functiOn, P1, which can be written as:
= 1.0 + 167r2 sin2(O/2)p/X2 +
...
(1)where is the observation angle, A is the wavelength in the scattering me-dium, and p32 is the mean-squared radius of gyration of the intramolecular distances projected in the s direction. This direction is defined by a unit vector A along the direction of the incident beam and a unit vector B along the direction of observation such that:
The projected mean-squared radius of gyration, p2, is defined by the
rela-tionship:
-
1NN
2N282 (r11S)2 (3)
where N is the total number of segments in the polymer chain, S is the magnitude of the vector S, and r, is the position vector from segment i to segment j and the bar represents the time average. Random-coiling macromolecules in solutions at rest adhere to the relationship:
p02 = p02/3 (4)
where the subscript s refers to a projected gyration radius and zero refers
to the zero shear state.
Equation (1) treats the intramolecular interference of the scattered light according to the Debye method,'° which presupposes the existence of
opti-cally isotropic polymer segments which exhibit small excess polarizabilities
with respect to the solvent. Both presuppositions are generally justified in studies of macromolecular solutions at rest. However, under conditions of flow, slight modification to eq. (1) may be required in the case of large deformations and orientations of the random coils. Stevenson" and Rein-hold'2 have treated this problem theoretically using the macromolecular
dumbbell arid Rouse models, respectively. However, no attempt has been made in this study to account for depolarization effects since extremely
small macromolecular deformations were encountered
The properties of the interference function [eq. (1)] are such as to allow a direct determination of both the orientation of a deformed macromolecule
in a shear field as well as the magnitude of the deformation. In the present experiment, apparatus design dictated that the plane containing S [eq. (2)] coincide with the plane deflied by the shear rate and flow directions.
Thus, conformation information was determined only in this plane.
As an indicator of the orientation of the light-scattering coordinate system and the flow coordinate systems, a new angle f", is defined as the angle which the S direction makes with respect to the positive shear rate
direction. Because the square of the radius of gyration of the projected intramolecular distances is measured in light scattering, the sign of S is not important. Thus, ' is defined only in the half plane formed by the
shear rate axis in the positive direction of flow.
The orientation angle x can be directly determined through the use of the interference function. This angle is defined here as the angle between the positive shear rate direction and the major axis of the macromolecule (see Fig. 1). Study of eq. (1) shows that when S corresponds to the major
axis of the macromolecule (" = x),
takes on a maximum value and0_1 becomes a maximum. That is, when the major axis of the macro-molecule corresponds to the direction of 5, one experimentally observes maximum destructive interference or, in other words, a minimum of the scattered intensity for a given value of the observation angle The
con-1418 CorI'RELL, MERRILL, AND SMITH
verse is true for the superposition of S with the minor axis (f' = x ± 900) where p3' takes on a minimum va1ue Thus, experimental values of Pr1
taken as a function of fi' at constant observation angIe 0 and shear rate will allow a direct determination of the orientation angle of the deformed
macromolecule.
Once the orientation angle is determined, meaningful values of the pro-jected radii of gyration, (p32)
',
can be directly obtained through the use ofeq (1) In this experiment, values of Pr' are experimentally observed for given values of ' and and decreasing values of the observation angle 0. The use of these data and Equation (1) allows a direct -determination of
values ofPa2.
The projected radii of gyration are reported as a ratio to the values ex hibited by the zero shear state. An extension ratio, (1'), is defined as:
-[/2] 1/2
(5)where the subscript zero refers tO the zero shear state and the subscript s
refers to a projected radius of gyration
Because projections of the intramolecular dimension are measured in the plane containing s, only two extension ratios are independent. The
rela-tionship between the extension ratios is :8,13
(si/s)2a2 + (s2/s)2b2 (6)
where s, is the magnitude of the projection of s onto the major axis, s2
is the magnitude of the projection of s onto the minor axis, s is the
magni-tude of s, a is the major axis extension ratio defined as:
a =
= x)
(7)and b is the miuor.axis extension ratio defined as:
-b = (' = X + 90°)
- (8)MACROMOLECULAR CONFORMATION CRITERIA
Complete light-scattering conformation information would yisld values of
the orientation of the macromolecule in the shear field as well as projected gyration radii along the major (extended), minor (compressed), and per-pendicular directions of the deformed macromolecule Since the pro-jected root-mean-squared radius of gyration is related to the propro-jected root-mean-squared end-to-end distance along the same direction by a
constant factor, the extension, ratio may also be written as:
(9)
where is the mean-squared end-to-end distance of the flow deformed polymer coil along, the direction of x and tije subscript zerp refers to the zero shear state. - -Assigning the three orthogonal directions x, y, aid z to the major, minor, and perpendicular directions, respectively, a
r2 = x2 ± y2 + z2 =
2xo2 + y2Yo2 ± Ez2Zo2 (10) or, sinceby previousdefinition,= a, = = c, and = 1702 eq. (10) becomes:
= {(a2 + b2 + c2)/3} (11)
where the subscript zero refers to the undefOrmed end-to-end distance.
Assuming that the distribution of the projected end-to-end distances around the mean remains Gaussian in form along the three orthogonal directions x, y, and z; the joint probability function w(x,y,z) of finding the terminal bead at coordinates x to x + dx, y to y + dy, and z to z + dz
where the first segment is fixed at the origin can be written as:
w(x,y,z) = (3/22)½(1/abc)'2exp - (3/2) [x2/a2)
+ (y2/b2) + z2/c2)J} (12) Equation (12) dictates that the locus of points of equal probability of find-ing the terminal segment must satisfy the equation:
(x2/a2) + (y2/b2) ± z2/c2) = constant (13)
Thus, ivith the Gaussian assumption, the statistical shape of the deformed
macromolecule is that of an ellipsoid.
MATERIALS
The solvent decahydronaphthalene (Fischer Chemical Co., purified grade) was used throughout this study. Its selection was based on its refractive index which could be vaned by appropnate nuxing of its cis and trans isomers to match the refractive index of the glass shear cell used. Pertinent physical properties of the mixture at 25°C are: refractive index n0 = 1.476; viscosityo = 2.48cp.
The polymer polyisobutylene (Enjay Chemical Co., L250 and L300) was fractionated by fractional precipitation from a dilute solution of ben-zene by addition of the nonsolvent acetone. Seven fractions were
col-lected from each master sample.
APPARATUS
Light-scattering measurements were taken of polymer solutions which were subjected to a Couette-type shear field in the annulus of a coaxial cylinder shear cell. Through the use of a constant speed motor with a suitable gear reduction unit, the inner cylinder could be rotated at a series of incremental rotational speeds (12, 30, 60, 120, 300, 600 rpm) while the outer cylinder was held stationary. The drive, mechanism of the inner cylinder was designed. after that used in the GDM viscometer.14 With this apparatus, eccentricities of revolution at the extreme rotor end were
1420 COTERELL, MERRILL, AND SMITH
Two sets of inner and outer cylinder pairs fabricated from Corning 7740 glass were used. The dimensions of the sets as well as the ratio of the shear rate to the rotational speed are given in Table I.
TABLE I
Shear Cell Dimensions
Heights of the cups and bobs were approximately 3.0 inches. b Calculated for the mean radial position of the annular area.
The use of the cell fabrication material, Corning 7740 glass, was dictated by refractive index considerations. By selection of the mixture of ci (n1 = 1.483) and trans (n = 1.470) decalin, which was usedas the solvent,
it was possible to match the refractive index of the glass parts (n = 1.474) Unfortunately, the 7740 glass is not of optical quality, and careful selection of the raw material is required to obtain acceptable parts. All glass
sur-faces of the shear cell were optically polished.
The fluid flow within the annular volume is subject to both vortex
generation and end effects. Flow visualization experiments with the use of aluminum flakes (Reynolds Metal Co., Paste No. 13) iii 1,1,2,2 tetrabrorno-ethane illustrated the absence of any appreciable flow-perturbing end effects prior to the onset of vortex flow, and theoretical calculations on the basis of the Taylor instability criteria'5 dictated the complete absence of vortex flow at rotational speeds below 300 rpm, while rotational speeds of 600 rpm were possible for polymer solutions exhibiting relative viscosities greater than 2.6.
The light-scattering apparatus used throUghout this experimentation was a modification of the Sofica light-scattering photometer (manufactured by Société Francaise d'Instruments de Contrôle et d'Analyse). Major modifications consisted of: (1) substitution of the shear cell in the place of the standard sample cell (accomplished by constructing the shear cell above the rotating bath plate) and (2) modification of the incident beam so that it could be shifted parallel to its ongmal propagation direction in the plane perpendicular to the axis of rotation of the shear cell Displacement of the incident beam to 0.43 in. of the centerline of the shear cell could be obtained. Reproducible adjustment of the incident beam to 0.004 in.
was possible. Incremental source apertures were also available to modify the dimensions of the incident beam. (3) There was modification of the secondary beam-defining optics so that it could be oriented to observe any predetermined pOint in the annular area of the shear cell. Incremental beam-defining apertures were also available for this apparatus. (4) An amplification system was introduced to allow accurate determinations of
Description Seti Set2
Outer cylinder ID, in. 0.997 1.030
Ijiner cylinder D, in. 0.892 0.912
VAT WALL (CONTAINING DECALIN) FIXED PRISM MOVEABLE PRISM WI N DOW ROTATABLE CYLINDER SCATTERED BEAM DEFINING OPTICS STATIONARY VOLUME CYLINDER ELEMENT LIGHT T RAP TOP VIEW
Fig. 2. Optical diagram of modified Sofica apparatus.
both the secondary intensity under zerO shear conditions and differential
intensity readings upon shearing the polymer solution.
An optical diagram of the modified Sofica instrument is shown in Figure
2. The experimental optical settings illustrated in Figure 2 are: the angle
defining the position of the incident beam, the angle 6 defining the position
of the secondary beam defining optics, and the observation angle 0. In terms of these settings, the angle I" dictating the mutual orientation of the light-scattering vector S and the direction of the positive shear rate for
clockwise rotation of the inner cylinder becomes:
and for counterclockwise rotation:
The incident and secondary beam defining apertures were selected so as to maintain the illuminated volume element within the annular area. Data taken in calibration experiments which registered the light scattered by the solvent ifiustrated that the presence of the rotating cup and sta-tionary outer cylinder in no way appreciably altered the secondary inten-sity scattered from the annular area over the range of experimental settings.
EXPERIMENTAL PROCEDURES AND RESULTS Polymer Characterization
Light-scattering data were observed by use of both blue (Xo = 4358 A) and green (X0 = 5461 A) incident light. Data were observed at incre-mental observational angles from 300 to 1500 and at concentrations
rang-1422 COTTIIELL, MERRILL, AND SMITH
TABLE II
Characterization Data Summary for Polyisobutylene in Decalih
For exampl& L300-F4 designates the fourth fraction taken in the fractionation of
the L-300 samp1e
ing from 1.5 .X 10i to 8.0 X 10
g/cc. Sample temperatures were maintained at 25.0 ± 0.1°C.The data were plotted according to the method of Zimm,'6 from which both the z-average radius of gyration,
and the weight-averge
üiolecular weight Jt?W were determined. High-angle light-scattering data were analyzed according to the method of Loucheux'7 which allowed determinations of both the number-average radius of gyration,(p2)1'1, and
the ratio of the weight-average to the number-average moleculai weight, Intrinsic viscosities were determined from first-Newtonian solution vis-cosities measured on the GDM14 viscometer. Sample concentrations
ranging from 1 5 X 10 to 8 0 X 10
g/cc were investigated at T =25.0 ± 0.05°C.
Table II summarizes the characterization data observed for these
samples.
The Mark-Houwink relationship determined for the system is:
[] = 2.2 X i0-4MO.70 (16)
which agrees well with the relationship reported by Ram.'8
The number-average root-mean-squared radius of gyration is related to the numbet-verage molecular weight by the relationship:
(,,2)h/S = 0.24M°
(17) where the radius of gyration is expressed ii Angstroms. This relationship [eq. (17)] agrees well with the Fox-Flóry treatment of the intrinsic
vis-cosity and the empirical eq. (16).
Values of the universal viscosity constant, ci,, were alculated from the relationship:
{i
]j/()h/2(6)/!
(18)The mean value of the data exhibited by the fractionated samples with the standard deviation is;
ci, = (1.46 ± 0.16) x 10" Sample no. Fractions .&3,, X 10 ['plo dug (p2)/2 A (i,,h/i, A
Ji/M,.
LS-1 L-250 5.9 11.3 2000 860 3.2 LS-2 L-300 11.8 20.0 2600 1300 3.1 LS-3 L-300-F3 16.8 25.0 3000 200 1.1 LS-4 L-300-F5 10.5 18.9 2500 2200 1.3 LS-6 L-250.F4 5.3 10.2 1850 1200 L7 LS-9 L-300-F4 15. 23.9 2800 2800 1.1Light-scattering interference function data which were observed for any one sample for both incident beam wavelengths were found to superimpose to a single curve when plotted versus the parameter [sin2(O/2) J/X2 This
normalization technique agrees with the 1)ebye treatment'° of the
inter-ference function.
The differential refractive index required in light-scattering 'calculations was measured in the Rayleigh Laboratory interferometer manufactured by the Carl Zeiss Company. A value of cm/dc = 0.0374 cc/g was obtained for the incident beam wavelength of Xo = 5461 A at25°C. A value of dn/dc
= 0.043 ± 0.004 cc/g was back-calculated from light-scattering data for
the wavelengthX0 = 4358 A.
Orientation Angie Determination
Values of the light scattered by the polymer solution under zero shear conditions; In,,, as well as the change of the light scattered upon shearing LI were taken as data for incremental values of the angle (see Fig. 2).
The observation angle was arbitrarily fixed to either 0 = 90° or0 = 60°.
Values of ' were calculated from eqs. (14) and (15). Values of the ratio of the excess light scattered under shear conditions .to that scattered from
the zero shear state were calculated from the relationship:
-
+
(19)-
JO-
JO)/J,jwhere the subscript zero refers to the zero shear state, p to the polymer
solution, and the superscript zero refers to the solvent. The value of (J2,/I,) of eq. (19) was determined from shear cell measurements while
the value of [(4,, - I0)/4,,] was determined from the zero shear
char-1.2 1.1 1.0 0 0 0.9 0.8' 0.7 I I
-
CONSTANTS USED IN SAMPLE LS -3\ PETERLIN EQUATION a rl.245
- \
b0.96 \ \ ci.o \-\
(25'734o .i-
SOLUTION TO '.. PETERLIN EQUATION S 9 = gO' C 3.6 x1Og/cc 290 sec g 15.5 0 0 20 40 60 80 100 120 140 160 180Fig. 3. Ratio of excess light scattered from sheared to zero shear states vs. orientation
of S with respect to shear field, 0'; (--), solution of Peterlin7 equatiOn with
1424 COrFRELL, MERRILL, kND SMITH 0 0 1_i to 0.9 0.8
.
-I I SAMPLE LS-9-2 0.0688 9/31 -0 90' 3 14.2 120 140 160 180 20 40 60 41Fig. 4. Example of orientation angle determination.
acterization data. Figure 3 illustrates the results of some preliminary
data which were observed over the entire range ofvalues of c1'.
Generally, the data of the type illustrated by Figure 3 were observed to exhibit a maximum and a minimum separated in values of
' by 9O.
The data appear symmetrical around the maximum and minimum and the extreme positions of the curve were unaltered by the selection of the
ob-servation angle.
The orientation angle was determined from the value of 1' at which the value of [(I,, - 10)/(I,,. - 10)] was observed to become a maximum. Data for any one determination were observed at a constant observation angle, 9, shear rate, , and polymer concentration.
In that this value of cf"
('max) is indicative of the orientation of the minor axis of the macromole-cule with respect to the positive shear rate, the orientation angle is cal-culated from the relationship:
-X max
Figure 4 illustrates typical data from which an orientation angle
deter-mination was made.
Data were observed for three fractionated molecular weight samples (10 < il?,, < 1.7 X 10) at a series of concentrations (3 X 10 g/cc < c < .9 X 10 g/cc) under shear rates to approximately 600 sec'. Figure 5 illustrates the summation of these data with the estimated limit of error of each determination.
The abscissa scales of Figure 5, labeled $' and $c0r, are defined by the relationships:
= (21)
and
$cor = $'(,,/c)/(,9/c)o
(22)where is the solvent viscosity (o = 2.48 ep), (,/c) is the viscosity
num-ber at ',
/ç)o is the first-Newtonian value, and the other symbls take on their normal meanings. As illustrated by Figure 5, these parameterso 5 100 I I lollI 2 90 80 70 60 50 40 30 pI 4.' -0 10 10 15 20 -/-20 Cor 30 40 50 25 60 Fig. 5. Oñentation angle with limit of error versus
normalize both the concentration and molecular weight dependence of the orientatiOn angle to a single curve. This type of normalization procedure was first applied to extinction angle data observed in birefringence
experi-ments.'9 Its use is derived from the normalization parameter j3, dictated
by the Rouse and dumbbell macromolecular models. This quantity $ is related to the parameters used here by the relationship:
$ = lim $' = [}0M0/RT
(23)C
The lines drawn on Figure 5 represent the best fit of the data to the theoretical equation:
x = (w/4) + [tan'(8/m)J/2
(24)where m is an adjustable constant.
Extension Ratio Determinations
The extension ratio was determined from the square root of the ratio of the limiting slopes (c = constant, sin2O/ + 0) of the inverse of the inter-ference function (data plotted according to the Zimm16 method) of the sheared to zero shear state. Data for these determinations were observed at constant values ofcJ'
For a fixed macromolecular sample, concentration, and shear rate, the data acquisition procedure fOr determining a major axis extension ratio is
as follows. The value of 4)' by the definition of the experiment, is set to x. Apparatus geometry settings are calculated from eqs. (14) and (15) for values of 0 of 900, 750, 600, and 450 Using these instrument settings,
52 TONI 8cor/2.5)
SYMBOL SAMPLE CONC (flic),
9l0l 02 91/9 0 LS -3 3.60 33.3 0 LS -3 7.20 41.5 V LS-3 667 46.5 o LS-3 5.90 35.7 LS-4 6.50 27.3 LS -4 5.20 21.0 £ LS-4 8.70 31.0 Q LS-9 6.88 360
1426 COTTRELL, MERRILL, AND SMITH 1.5 10 SAMPLE LS-9 l,=4360A 285 SEC
ER0 SHEAR DATA
£SHEAR DATA=-.
10 2.0 3.0
Sin2 I2 KC , K
5 xl0cc/g
Fig. 6. Zimm plot for shear data corresponding to '1" = x
values of the light scattered by the polymer solution, 1,,,, and the change of the scattered intensity upon shearing, Al,, are recorded as data for each observation angle. The ratio (I, - 1°)/(I,,, - 10) is calculated from eq. (19) and applied as a corrective ratio to the zero shear state characterization data. That is, the Zimm plot can be corrected by the relationship
Kc/R9 = Kc/R9,, ('i':
I i)
(25)where K is the optical constant, c the polymer concentration and R9 is the modified Rayleigh ratio, where the subscript zero refers to the zero shear state. Illustrative data of the correction are shown in Figure 6.
As illustrated in Figure 6 and as generally observed in this study, the extrapolation to zero angle on the Zimm plot appears, withm experimental error, to be independent of the shear rate. This fact ifiustrates the
negli-gible dependence of the second virial coefficient on the shear rate. Figure 6 can then be used in the determination of the extension ratio. NOte that the angular slope of the Zimm plot may be evaluated as:
16,r22
f
14.0
and that an equivalent slope, T0' my be determined from the zero shear data. By definition of the extension ratio then:
= (27)
-
.T - hmj2
* oro(Kc/R0n
- (26)1.3 1.2 1.1 1.0 0.9 £ -V ASSUMED M0800ISPERSED 'BCOA2IOP 09
-a :1.0. 0.013 8 SYMBOL SAMPLE LOJC2 9181.10 (h1:0M1 153 6.88 ]73 AV 15.9 4.58 32 6 o L5-3 540 37.8 S LS 4 650 27.] 0 LU-I 5.20 26.0 0 10 20 30 a
Fig. 7. Major and minor axis extension ratios vs.
$'. ()
theoretical results ofpolydispersity analysis.
In this experimentation, the major axis extension ratio a was determined by the method described above. The minor axis extension ratio b was cilculated from data observed at values of 4' = x ± 450, the major axis
extension ratios, and the use of eq. (6).
Three fractionated molecular weight samples were investigated, ranging from 4 X 10-a g/cc to 7 X 10
g/cc and shear rates to 600 sec. The
summation of these data is plotted in Figure 7 versus the parameter i3'.Also shown on Figure 7 are the results of a polydispersity analysis in which the monodisperse behavior was assumed; a Schultz-Zimm distribu-tion of molecular weights was assumed; and the Z-average extension ratio calculated for a corresponding weight-average value of 3. The averaging technique was dictated by the physics governing the interference function and the experimental values of fi which were used. An outline of this
cal-culation may be found in Appendix A.
As illustrated by this plot, the parameter ' does appear to normalize the concentration ependence of the extension ratios. However, a discrep-ancy does exist in comparing the data illustrated bysamples LS-9 and LS-3
with LS-4. Comparison with the results of the polydispersity analysis shows that this discrepancy can easily be explained in terms of varying
degrees of polydispersity which exists between the samples.
Figure 8 graphically represents the statistical shape of the deformed iiacromolecular coils in that it represents a solution to eq. (13) by use of
experimental values of the extension ratios and orientation angles.
Alternative Method of Data Analysis
Peterlin79has developed theoretical relationships determining the inter-ference function for the deformed dumbbell and Rouse macromolecular models. Peterlin's solution to the dumbbell model can be generalized to
Ri, :133
M/
:2
1.4
1428 COTTRELL, MERRILL, AND SMITH Q (Flow Direction)
Fig. 8.. Statistical shape of deformed macromolecular coil..
account for the light scattered by a macromolecule exhibiting extension ratios a, b, and c as well as an orientation angle x. The relationships written in terms of the present. nomenclature and experimental geometry are:
P0 =
2f
(1 - u) exp X'(u + Lu2)ldu
(28)where
= xa'
X = 16,r2 sin2 (O/2)/X2
L=(a2+b2+c2-3)/3
8' =
[a2 ç2 (ëf'- x) +
l$2 Sjfl2(4" - x)]/(L + 1)
The limiting form of eq. (28) as applied to the zero shear state (a b =
c = 1) yields the familiar Debye expression or:
P0, = 2/X2[e_X - (1 + X)j
(29)The absolute values of the interference function calculated from these
equations are inaccurate as is expected of a somewhat polydispersed polymer
in a good solvent. However, the ratio of values, P6/P0,,, when calculated with the extension ratios and orientation angles observed here may be used
to calculate values of (I, JO)/ JO)which agree closely with
experi-méntà1 data. Figure 3 illustrates this comparison; an outline of the
cal-culation is given in Appendix B.
.1=30 '(-85' -125 b=0.94 5=20 Z82 =1.29 b=095 =115, b0.9B = 10,
The values of the minimum and maximum exhibited by the solution to the Peterlin equation on Figure 3 are primarily determined by the major and minor axis extension ratios respectively while their positions are deteriniiied by the oiiciitation angle. The significance of the agreement illustrated by Figure 3 is that conformation extension ratios and orientation angles may be obtained by curve fitting the Peterlin equation to the actual data. This procedure would eliminate the need of acquiring data at incre-mental decreasing observation angles in the extension ratio determinations
and thus greatly simplifying the experimental procedures.
The actual solutions to eq. (28) were carried out by a numerical integra-tion technique on a computer. Experimental variables were used in eqs. (28) and (29) with the exception of the extension ratio c (perpendicular to
the flow and shear rate directions) which was assumed to be unity.
DISCUSSION
The values of the orientation angle reported here agree well with the values observed for the same polymer solvent system by birefringence measurements and with predicted theoretical values.
Table III lists a series of theoretical and experimental values of m of eq.
TABLE III
Theoretical and Experimental Values of m from Equation (24) Experimental system/model
Dumbbell model
Rouse model: free-draining Rouse model: nonfree-draining PIB-gasoJine
PIB-decalin
PIB-decalin (based on
PIB-decalin (based on j5'cor)
m 1.0 2.5 4.88 0.78 1.89 3.6 ± 0.9 2.5 E0.5
Data extrapolated to zero concentratiàn by Peterlin.3
(24) obtained from the macromolecular models, birefringence data, and the results of this study. Comparison of the experimental data is difficult because of the existence of varying degrees of polydispersity of the inves-tigated material. Polydispersity has the effect of lowering the experi-mental values of m. On allowing for this factor, agreement with the
ex-perimental results from birefringence is considered good.
The values of the. extension ratios reported here are markedly different from those predicted by the macromolecular models which assume freely flexible polymer molecules (no internal viscosity). In making this
com-parison, it is most convenient to report values of the mean coil expansion given by eq.. (11). Figure 9 illustrates the comparison of data reported
here to predictions of the dumbbell and Rouse macromolecular models.
Reference Peterlin7 Zimm'° Zirnm2° Tsvetkov andFrisman22 Brodnyam et al.21 This study This study
1430 COTTRELL, MERRILL, AND SMITH
D U NA B B E LL
MODEL
RESULTS OF THIS STUDY
Fig. 9. Comparison of models of freely flexible macromolecules to experimental results.
ROUSE MODEL(3) FREE-DRAINING ROUSE MOOEL(3) NON-FREE- DRAINING 11.0 z 9.0 z 8.0 4 w 7.0 -J G.0
0
Li z 5.0 4 w 4.0 3.0 L 2.0 1.0 0.1 1.0 10 100Fig. 10. Comparison of the experimental mean coil extension with the theoretical result of Cerf5 far nondraining coils with finite internal viscosities.
Figure 10 illustrates the results of the recent calculations of Cerf5 for non-free-drarnmg coils with finite internal viscosities The parameter sho n on
this figure is the thmensionless effective ngidity factor, n, defined by the relationship:
n = (30) where Na is Avogadro's number, and '1' is the intrinsic rigidity factor of the polymer chain representative of steric hindrance to free rotation. Also
shown in Figure 10 are the results of this study ca1cuited from eq. (11)
with experimental values of a and assuming values of b = C = 1.0.
As already pointed out by Cerf,5 direct comparison of the results and theory is not currently possible due to the lack of intrinsic rigidity factor 'I' characteristic of the PIB macromolecule. However, as an order of mag-nitude estimate, a value of n = 45 can be calculated assuming a value of 'I' = 1.6 X 1Q g/sec as has been determined for the polystyrene rnol-cule.23'24 Reference to Figure 10 illustrates that the theoretial.and experi-mental mean coil expansions, compared in this manner, to be of the same
order of magnitude but of divergent forms. CONCLUSIONS
Light-scattering measurements of macromolecular solutions under flow
will allow a direct determination of the flow determined conformation of the macromolecule Complete light-scattering information will yield three
independent extension ratios of the coil and its onentation m the shear
field.
Experimental data reported here for the polyisobutylenedecahn system indicates the deformation of the macromolecules in a simple shear field to be severely limited.. The major axis extension ratio a can be given by the. relationship:
a= 1.0 + 0.013I3°
0 30 (31)while the orientation angle follows the relationship:
x (7r/4)
+ [tan(fi/3.6)]/2
(32) T he form of orientation angle relationship is in agreement with thepre-dictions of the macro inoleculaf tnodels which assume freely flexible
macro-molecules, while the extension ratios are markedly discrepant with the pre-dictions of these models and more in agreement. with the Cerf model5
which assumes a finite coil internal viscosity.
APPENDIX A
The mean-square radius of gyration obtained from light scattering is a
z-average value defined by the relationship:
= (A-i)
where W is the weight fraction of material having a molecular weight of
M to M + dM and
is the mean-square radius of gyration of thismolecular weight species. This same type of relationship can be written for the projected gyration radii.
1432 COTTRELL, MERRILL, AND SMITH
The extension ratio measured in this experimentation is:
tel")
[/(i)]'/2
(A-2)whereas the monodispefsed extension ratio may be given by the relation-ship:
= f($)
(A-3) Equations (4), (16), and (18) may be combined to yield the relationship:= FM'3
(A-4)where F is a constant.
Equations (A-1)--(A-4) may be combined to descnbe the polydispersed
extension ratio as:
[(')
]2' (A-5)The value of , which is experimentally measured, contains the product of the intrinsic viscosity and the weight-average molecular weight. The ihtiinsic viscosity is dependent upon a viscosity-average molecular weight which is assumed to be essentially equal to the weight-average value be-cause of the high value of the exponent in the Mark-Houwink equation and the relatively low degree of polydispersity in the samples. The experi-mental Value of used to characterize the sample is described by the relationship:
= (K0"?/RT)M'.7 (A-6)
where the equivalent relationship for the monodispersed species would be written as:
= (K'qo'/RT)Mj'7 (A-7)
To describe the polydispersity of the polymer sample, a Schultz-Zimm
distribution was used. This function can be written as: W = (yZ+l/z!)MZeYMi
y = (z + 1)/Mu
(A-8)(z + 1)/z =
where W represents the weight fraction of material of molecular weight of
MtoM + dM.
The monodispersed behavior remains to he described. From Figure 7,
the most motiodisperse samples appeared lo yield a In:LJUr axis dependence
on $ of the form
a2 = 1 + i3°-° = fC8)
0(\-9)
Equations (A-6)-(A-9) may then be substituted into eq. (A.5) to yield an expression for the extension ratio for the polydispersed state, a. The
independent variables of this calculation are
and M/A?.
The actual calculation of values of a were carried out by a numerical integration technique on a computer. The results of this calculation are
shown in Figure 7.
APPENIMX B
At finite concentration and observation angle,
Kc/R0 = (P0-'/J(?) + 2A2c + ...
(B-i)For simplification the following quantities are defined:
lim (Kc/R0) D (B-2)
c.O
o tLIId lim (Kc/Re) = E (B-3) o 0 such thatE - D = 2A2c
(B-4)Equations (B-1)-(B-4) may be combined to give:
P0' = [(Kc/R0) - (E - D) ]/D
(B-5)and from the equivalent relationship for the zero shear state:
P
(Kc/R0,) - (E - D)
(B-6)
Po,0
[(I,,, - I0)/(I - I) ](Kc/R9,0) - (E - D)
or
1 10
I p -
(B7)- 10
[(P00/P0) ] [(Kc/Ro,j] - (E - D) + (E - D)
In that values of Kc/R9,0, E, and D are directly determinable from the Zimm plot of zero shear rate data, eq. (B-7) relates the interference function
ratio to the experimental ratio of the excess scattered light.
This work was supported by the Office of Naval Research under Contract Norir 3963(10) and done in part at the Computation Center at the Massachusetts Institute of
Technology, Cambridge, Massachusetts.
References
J. J. Herm:uis, Physiea, 10, 777 (1943).
W. Kuhn arid II. Kuhn, Hclv. C/urn. Ada, 26, 1394 (1943). A. Peterlin, J. Chem. Phys., 39,224 (1963).
Chr. Reinhold and A. Peterlin, J. C/rem. Phys., 44,4333 (1966). R. Cerf, C.R. Acad. Sci. (Paris), C267, 1112 (1968).
1434 COTTR.ELL, MERRILL, AND SMITH
R. Cerf, J. Chim.Phys., 48,59 (1951).
A. Petèrlin, W. Heller, and M. Nakagaki, J. C/tern. Phys., 28,470 (1958). A. Peterlin, J. Polym.&i., 23, 189 (1957).
A. Peterlin and Chr. Reinhold, J. Chem. Ph ye., 40, 1029 (1964).
10 P Debye, Technical Report CR 637, pnvate communication to Reconstruction
Finance Corporation, Office of Rubber Reserve (1945), in Light Scattering from Dilute Polymer Solution.s, D. McIntyre and F. Gornick, Eds., Gordon and Breach, New York,
1964.
A. F. Stevenson and H. L. Bhatragar, J. Chern. Phys., 29, 1336 (1958). Chr. Reinhold and A. Peterlin, Physica, 31,522 (1965).
F. R. Cottrell, Sc.D. Thesis, Massachusetts Institute of Technology, Cambridge,
Massachusetts, 1968.
P. J. Gilinson, C. R. Douwalter, and E. W Merrill, Trans. Soc. Rheol., 7, 319
(1963).
S. Chandrasekhar, Hydrodynarnic and Hydromagnetic Stability, Clarendon Press, Oxford, England, 1961, Chap. VII.
B. H. Zimm, J.. Chem. Phys., 16, 1093 (1948).
C. Loucheux, G. Weill, and H. Benoit, J. C/tim. Phys., 55, 540 (1958).
A Ram, Sc.D. Thesis, Massachusetts Institute of Technology, Cambridge, Mas-sachusetts, 1961.
A. Peterlin, in Rheology Theory and Applications, Vol. I, F. R. Eirich, Ed., Aca-demic Press, New York, 1956.
B. H. Ziinm, J. Chem. Phys., 24,269 (1956).
J. G. Brodnyam, F. H. Gaskins, and W. Philipoff, Trans. Soc. Rheol., 1, 109
(1957).
V. N. Tsvetkov andE. Fristnan, Acta Physicochim. U. R. S. 5., 20, 61(1945). A. Peterlin, J. Polym. Sci. A-., 5, 179 (1967).
R. Cerl, J. Phys. Radium, 19, 122 (1958).
Received March 10, 1969
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(SecurIty classification of title, body of abstract and indexing annotation must be entered when the overall report is classified,) I. ORIGINATING ACTIVITY (Corporate author)
Massachusetts Institute. of. Technology
20. REPORT SECURITY CLASSIFICATION
UNCLASSIFIED
2b. GROUP
3. REPORT TITLE
Conformation of Poiyisobuty.lene. in Dilute Solution. Subjected to a Hydrodynamic Shear Field
4. PESCRIPTIVE NOTES (Type of report and.lnclusjve dates)
Technical Report
5. AUTHOR(S) (First name, middle initial, last name)
F.R.. Cottrell, EW..Merrii.1,.and K..A. Smith
6. REPORT DATE
May, 1970
70. TOTAL NO. OF PAGES
. 20
7b. NO. OF REFS
24
80. CONTRACT OR GRANT NO.
Nonr 3963 (10)
b. PROJECT NO.
Task NR 062-333
C.
d.
9a. ORIGINATORS REPORT NUMBER(S)
9b. OTHER REPORT NO(S) (Any other numbers that may be a8slgnedthis report)
10. DISTRIBUTION STATEMENT
ii. SUPPLEMENTARY NOTES 12. SPONSORING MILITARY ACTIVITY
Office. of. Naval Research
13. ABSTRACT
A new. lightP.scattering. experiment.which. allows a. direct determination of the conformation, of. macromolecules, deformed in flow. is. described. Light-scattering relationships. based. on. the. .interference function. are developed, and results of
an. experimental, study. are...detai lecL . The. deformed. conformation of high molecular
weight. po.lyisobuty.lenewas. determined in a Couette-type. shear fIeld.
Deca.lin was the. solvent. Variables: investigated were .the..shear rate. (C. to 600 sec'.1), the polymer molecuiar.we.ight (1.0 X 1O to 1.6 X l07),.and.the.polymer concentration
(2.0x 10' to 8.0X .io: g/cc). Conformation..varjab.les determined were the
orientation, of. thea mo.lecule.,in. the. shear field. and .it.s maximum and minimum
extension ratios. in.the. plane. defined .by. the.direction. of flow and the. direction of. the shear rate ..The. deformation of the macromo.lecule.
was found to be. markedly discrepant when. compared..to the..dynamic macromo.lecular models which assume
complete coil fiexi.bil.ity,..and more closely in.agreement w.ith the recent.. theories of Cerf., deeloped...for.nonfree1..drajnjng coils. which. exhibit a finite, internal v.iscosity. ADM .1 ._....,_ -. I NOV 65 S/N 0101-807-6811 Security ClassificaUon A- 31408
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