Open access

Electric Properties of Carboxymethyl Cellulose

Written By

Alexandar Metodiev Zhivkov

Published: August 28th, 2013

DOI: 10.5772/56935

From the Edited Volume


Edited by Theo van de Ven and Louis Godbout

Chapter metrics overview

4,721 Chapter Downloads

View Full Metrics

1. Introduction

The linear polymer carboxymethyl cellulose (CMC) as a polyelectrolyte is an object of consideration in this review. The emphasis is on the electric properties of CMC both as a free chain in solution and adsorbed on the solid surface. A special attention is paid to the mobility of counterions, electrostatically associated with the CMC polyelectrolyte chain.


2. Chemical structure

2.1. Molecular mass

Carboxymethyl cellulose [C6H7O(OH)3−x(OCH2COOH)x]n is a derivative of the regenerated cellulose [C6H10O5]n with hydroxy-acetic acid (hydroxy ethanoic acid) CH2(OH)COOH or sodium monochloroacetate ClCH2COONa. The CMC backbone consist of D-glucose residues linked by β-1,4-linkage. The molecular mass of one glucose unit in CMC chain is mCMC = 146.14 + 75.04 x, where x ≤ 3 is the degree of substitution (DS). As a rule CMC is produced as sodium salt [C6H7O(OH)3−x(OCH2COONa)x]n with DS = 0.4−1.2, then the molecular mass per unit is mNaCMC = 146.14 + 97.03 x ≈ 185−263 g/mol.

2.2. Structure of the chain backbone

As derivative of the cellulose (poly-β-D-glucose) [1,

2,3] CMC has inherited its main structural peculiarities: (a) rigidity of the glucose units (6-atoms rings in “armchair” conformation); (b) an almost fully extended conformation owing to impossibility for rotation round the C−O−C bonds between the glucose residues because of strong steric limitations (a consequence of the β-configuration at C-1 atom in 1,4-linkage); and (c) orientation of the bigger constituent groups (−OH, −CH2OH and −OCH2COOH) in the equatorial plane out of the saccharic ring. The cross-sectional dimension of the CMC chain is a sum of the diameter of the glucose ring (0.5 nm) and the size of the carboxymethyl group (0.4 nm, situated on the both side of the chain); the effective diameter of the chain is rather higher because the glucose residues are oriented not line in line but somewhat tilted along the backbone line [4]. The replacement of the H-atom of −OH-group with −CH2COO− causes a loss of the possibility of parallel association of CMC chains in sheet-like structures (a characteristic of the cellulose structure leading to supramolecular organization in microfibrils [5]) because of both steric hindrance and electrostatic repulsion but that does not exclude the possibility of intra- and intermolecular interaction by hydrogen bonds between the unsubstituted −OH groups.

In the literature the polymer unit of CMC chain is denoted as consisting of one or two glucose rings following the manner applying to the cellulose. The one unit way is chemically well-founded according the cellulose contents because all the glucose units are chemically identical (except those on the two ends of the chain). According to the conformation of the cellulose chain a more thought-out manner is the two glucose residues unit because this way allows distinguishing the cellulose (poly-β-D-glucose) and the amylose (poly-α-D-glucose), both linear chains of chemically identical glucose residues. The conformation of the polymer chains of these two polysaccharides differs drastically owing to the configuration at the anomeric C-1 atom: the β-1,4-linkage in the cellulose leads to inversed orientation of every second glucose ring according the previous one and to sterically conditioned full extended conformation because of impossible rotation round the C−O−C bonds between C-1 and C-4 atoms of the neighbour rings. In the case of the amylose the α-configuration at C-1 atom leads to uniform orientation of the glucose rings and to impossibility of extended conformation; due to the α-1,4-linkage amylose chain has a tendency to spiral conformation [5]. Since the linear charge density of the CMC chain is determined by the number of −COO− groups per glucose unit independently of its orientation, in this chapter the one glucose residue is accepted to denote the monomeric unit.

2.3. Distribution the carboxylic groups along the chain

The −CH2COOH group can be attached to every of the three hydroxyl groups of the cellulose monomer unit, so theoretically the degree of substitution (DS) can reach 3, but usually DS does not exceed 2. The distribution of −CH2COOH groups in the glucose unit and along the CMC chain is accepted to be random in the model [4] proposed to give the monomer composition of a sample with known DS. The model is based on the supposition that the substitute reaction occurs at random, i.e. each of the three −OH groups (at C-2, C-3 and C-6 position) of every monomer unit can be substituted in equal probability independently on the presence of another constituent in the same glucose unit. The experimental investigations [6,7,8] of the mole fraction of substituted monomers of CMC confirm the hypothesis for random distribution of the constituents. For example, at DS = 1.3 the mole fractions are about 0.2, 0.4, 0.3 and 0.1 for unsubstituted, mono-, di- and trisubstituted, respectively. On the base of these results it can be concluded that the −CH2COO− groups are also randomly distributed along the CMC chain and practically there are no regions containing more than one or two uncharged monomer units when DS is higher than 1−2. The absence of long uncharged segments allows accepting that the negative charges are almost evenly distributed along the CMC chain at high linear charge density (high DS and high degree of dissociation); that is important condition for applying the model of uniformly charged cylinder to CMC chain.

2.4. Contour length

The distance between two glucose units in CMC chain is 0.515 nm [4]. The contour length Lc (the length of the chain backbone if it is fully stretched but without deformation of the valence angles and bonds) is determined as a product of the number of monomers n and the length of one unit: Lc = 0.515 n (nm).

For example, at DS = 1.20 CMC chain with MNaCMC = 250 kDa (sodium salt) has 952 glucose residues and counter length Lc = 490 nm.


3. Electric properties of CMC in aqueous medium

In this section the characteristics of CMC as a free polyelectrolyte chain are overlooked, i.e. the chain has conformational freedom that does not or depends on the presence of other macromolecules, respectively in diluted solution or semi-concentrated ones. The chain is immersed in salt-free medium or in electrolyte with valency z. In the first case the counterions originate from the ionizable group of the chain: H+ or Na+ (in the case of CMC or its sodium salt NaCMC). A part of counterions can be electrostatically adsorbed losing their freedom; the rest are scattered by the thermal energy kT and are randomly distributed around the chain forming an ions cloud.

3.1. Dissociation of the carboxylic groups in CMC chain

3.1.1. Apparent dissociation constant

The effective dissociation constant Ka (respectively pKa = −logKa) of a weak polyelectrolyte depends on the neighbour electric charges in the chain and in the medium. The presence of other negative charges in the vicinity of a given COO− group leads to increasing of the electric field intensity and the local concentration of H3O+ ions. As a result the probability of protonation of the COO− group increases; respectively the equilibrium of the reaction COOH↔COO− +H+ is shifted to the non-dissociated form. That is why the dissociation capability of the ionizable groups in the polyelectrolyte chain can not be characterized by a constant like in the case of a simple (monomeric) acid (pKa = pH at α = 1/2). The apparent (effective) dissociation “constant” pKa = f(x,α,μ) of COOH groups in CMC chain is a function of the degree of substitution x, the degree of dissociation α (determined by pH of the medium), and the ionic strength μ; the first two factors determine the linear charge density of the chain.

3.1.2. Degree of dissociation

The degree of ionization (the fraction of the dissociated acid groups) α of a weak polyelectrolyte pKa depends on the apparent dissociation constant Ka(α) at given α and the H+ concentration:

log[α/(1α)] = pHpKa.E1

Ka can be represented as a sum of the intrinsic dissociation Ka0 and the electrostatic term ΔKa (owing to the influence of the neighbour electric charges):

pKa= pKa0+ΔpKa,E2

At equilibrium the shift ΔpKa is due to an alteration of the electrostatic free energy Gn of the polyacid at variation of n negatively charged groups [9]:

ΔpKa= (0.434/kT)(dGn/dn).E3

3.1.3. Experimental data

Potentiometric titration of CMC aqueous solutions shows that the degree of acid dissociation (ionization) α increases in the range of pH 2−6. The fact is determined by the moderate value of the dissociation constant Ka of the −COOH groups and allows defining CMC as a weak polyelectrolyte.

An addition of a low molecular salt to the CMC solution leads to increasing of the degree of dissociation α because of the screening of the electric field around the polyelectrolyte chain; the influence of the salt increases with α and the degree of substitution x, i.e. with the linear charge density. For CMC with DS x = 0.75 the degree of dissociation increases from α = 0.23 to 0.85 in the range pH 3.0 – 5.0 in 0.01 mol/L NaCl; at increasing of NaCl concentration up to 1 mol/L the dissociation increases from α = 0.43 to 0.98 in the same pH diapason [8]. The increasing of the ionic strength from 0.01 to 1 mol/L shifts pKa form 3.8 to 3.2; i.e. the dissociation at α = 0.5 is quadruplicately increased due to the electrostatic screening by Na+ ions.

3.1.4. Intrinsic dissociation constant

For aqueous solutions of CMC the experimental dependence of pKa on the degree of dissociation α is linear with a slope ΔpKa/Δα:

pKa= pKa0+ (ΔpKa/Δα)α.E4

That allows obtaining the intrinsic dissociation constant pKa0 by extrapolation to α = 0 on the plot pKa = f (α). Thus the extrapolated values are: pKa0 ≈ 3.3 in salt-free solution of CMC [10]; Ka0 ≈ 3.2 in NaCl solution with concentration 0.01, 0.05 and 0.1 mol/L; Ka0 ≈ 3.0 in 0.5 mol/L and Ka0 ≈ 2.95 in 1 mol/L NaCl [8].

It is interesting to compare the Ka0 of CMC with Ka of the acetic acid in diluted aqueous solution (when the electrostatic interactions between the next −COO− groups are negligible because of the big distance between acid molecules just in the opposite to the case of the polyelectrolyte chain). The thermodynamic acidity constant Ka of CH3COOH in aqueous medium is equal to 1.754 10−5 (calculated accounting the activity instead the concentration), thus pKa = 4.756 (the negative logarithm of Ka). So, the intrinsic dissociation constant Ka0 of the carboxylic groups of CMC (at pKa0 ≈ 3.0 in 0.5 mol/L NaCl) is about 60 times higher than Ka of the acetic acid −COOH group. This observation is opposite to the expectation (Ka0 = Ka at α→0 and Ka0 < Ka when α>0) if taking into account only the electrostatic interactions between the neighbour −COO− groups in the CMC chain. The difference in Ka0 and Ka can be explained with the different electronic structure of the two chemical substances. That suggest that the intrinsic dissociation constant of the three −COOH groups are different, especially of that directly attached to the glucose rings at C-2 and C-3 atoms and that at C-6 position.

3.1.5. Theoretical approach

The pH-induced shift of the apparent dissociation constant ΔKa determined by the change of the electrostatic free energy Gn of the polyion can be calculated by the work needed to display the elementary positive charge (proton) qe from the polyacid surface (where the electric potential is ψ0) to a infinite distance in the bulk (where ψ∞ = 0 by definition). Then (dGn/dn) in Eq. (3) effectively equals to qeψ0.

One of the models used for this calculations is the that of uniformly charged cylinder with radii a<b (2a is the mean diameter of the polyelectrolyte chain and 2(b−a) is the size of the adsorbed counterions). The ΔKa is proportional to the alteration of the electric potential owing to both the adsorbed (condensed) and diffuse counterions of all kinds (Na+ in the case of NaCMC), represented by the potentials ψ0 of the inner and ψ1 of the external cylinder. The potential ψ0 of the inner cylinder is determined by the degree of substitution x and the degree of dissociation α; the ψ1 potential can be calculated from the surface charge density of the inner cylinder and the capacity of a cylinder capacitor with radii b>a and interelectrode distance b−a. Then the shift ΔpKa can be represented as a sum of two terms determined by the charge density of the inner cylinder and the potential on the external one [11]:

ΔpKa= (0.217e2/πε0εrkT)ln(b/a)xα+ (0.434e/kT)ψ1,E5

where e is the elementary charge (proton); ε0εr is the absolute dielectric permittivity (electric constant ε0 and the relative dielectric permittivity εr); kT is the thermal energy at absolute temperature T (k is the Boltzmann constant).

In the case of NaCMC the Eq. (5) takes into account the two kinds of counterions: H+ ions determining the potential ψ0 of the inner cylinder and adsorbed Na+ cations determining ψ1 of the external one. By fitting the experimental data for the degree of dissociation α = f(pH) (obtained by titration of CMC solution with NaOH) with the parameters of the model of uniformly charged cylinder in Ref. [8] are found the intrinsic dissociation constant Ka0 = 3.2 (at 0.01−0.1 mol/L NaCl) and radius of the inner cylinder a ≈1 nm; the last quantity increases from a = 0.95 to 1.15 nm when the degree of substitution grows from x = 0.75 to 1.25. So, the calculated diameter 2a ≈ 2 nm is two times higher than that of the molecular cross-section of CMC chain if taken as a sum of the size the glucose ring (0.5 nm) and one attached COOH group (0.4 nm).

3.2. Linear charge density of CMC chain

The dissociation of carboxylic groups in aqueous medium determines the electric properties of CMC as polyelectrolyte. The number of COO− groups is determined by the degree of substitution (DS) and the degree of dissociation α. The linear charge density b−1 is equal to the ratio of ionized groups’ number to the contour length Lc. For example, CMC chain with DS = 1.20 and M = 250 kg/mol (sodium salt) has 952 residues, Lc = 490 nm and mean distance between two neighbour COO− groups b = 0.429 nm (b−1 = 2.33 charges/nm) at α = 1. For CMC with DS = 1.00 (b = 0.515 nm) the charge density is b−1 = 1.94 nm−1 at full dissociation or nearly one charge per nanometer at α = 1/2.

So defined charge density is determined by the chemical structure of CMC chain and could be designate as intrinsic linear charge density; it takes into account only chain’s own charges (COO− groups). The presence of adsorbed (condensed) counterions (Na+ in the case of sodium salt of CMC) decreases the effective charge density. The value of α obtained by potentiometric titration reflects all kinds of electrostatic interactions influencing on ΔKa including that of the condensed Na+ counterions and the alteration of H+ concentration in the vicinity of the polyelectrolyte chain. So, the using of experimental values of α gives the intrinsic linear charge density.

3.3. Counterions condensation on CMC chain

3.3.1. Condensation phenomenon and theoretical approaches

When a polyelectrolyte chain is immersed in aqueous solution of electrolyte the electrostatic field around the chain increases the local concentration of the diffuse counterions and decreases the one of the co-ions; the difference between the two concentrations is maximal at the chain surface and diminishes quasi-exponentially down to zero in the bulk. The distribution of the local concentration of the free ions is determined by the ratio between the electrostatic and the thermal energies. When this ratio increases above a critical value then part of counterions are electrostatically adsorbed on the chain forming temporary ion pairs with the electric charges of the polymer; the phenomenon is known as counterion condensation.

The distribution of the diffuse and condensed counterion considered as loosely and strongly associated with the polyion is a subject of several polyelectrolyte theories developed on the base of a few different models [12]; the most popular are: Katchalsky’s cylindrical cell model [13] and the Oosawa-Manning two state model [14]. In the both models the polyelectrolyte chain is considered as an infinite impenetrable cylinder on which surface the charges are smeared as a non-discrete quantity and uniformly distributed along the cylinder axis.

The main imperfections of the cylindrical models are: (1) the real polyelectrolyte chain can be assumed as strait only for a rigid fragment shorter than the persistent length lp and when the lp is much longer than the chain diameter (the semi-flexible chains like CMC have a form of curved rod when their contour length is commensurable with lp but the longer chains takes conformation of random coil); (2) the end-effects are neglected; that assumption is defensible only for enough long chains having big number of charges; (3) the charged groups are non-uniformly distributed along the chain backbone at incomplete degree of dissociation (α<1) and/or at irregular distribution of the dissociable groups as in the case of CMC (see paragraph 2.3); and (4) the chain’s charges can be considered as non-discrete quantity uniformly smeared on the cylinder only at a some distance from the surface (where the electric field is less inhomogeneous); at a shorter distance the charges should be considered as discrete and distributed according to the chain structure.

3.3.2. Cylinder cell model

In this model [15,16,17] a polyelectrolyte cylinder with radius a is localized in the center of an infinitely long cylinder cell with radius R; the distance (R−a) is divided into two zones. In the inner zone the centers of the adsorbed (condensed) counterions are uniformly distributed on a coaxial cylinder with radius b; the difference in radii (b−a) of the two cylinders is equal to the ion radius. The electric potential ψ0 (on the inner cylinder surface) is determined by the electric charges of the polyelectrolyte chain themselves. The potential in the inner zone (at distance b−a) follows lineally as in a homogeneous solid state body; that allows to consider the polyelectrolyte chain as a coaxial cylindrical condenser. The presence of two kinds of counterions with different radius and valence can be considered by introducing an additional cylinder in the inner zone [18,19]. The potential ψ1 of the cylinder with radius b is determined by the total chain’s charge including the adsorbed ions. In the external zone (R−b) the diffuse counterions are uniformly scattered according the balance between the electrostatic eψ1 and thermal energy kT; their size is assumed to be negligibly small (point charges). The potential in the external zone follows quasi-exponentially (in the case of symmetrical electrolyte in the medium) according the non-liner Poisson-Boltzmann equation in its cylinder form [20,21].

So, the cylinder cell model is a one-dimensional analog of the two-dimensional electric double layer (EDL) used in the colloid chemistry to describe the electric properties of a flat solid/liquid interface: the two inner cylinders are analogs of the solid surface and Stern layer (the EDL dense part). The difference is that at low potential (ψ1 < 25 mV in 1:1 electrolyte) ψ(x) follows exponentially with the distance x in the case on flat surface while in the case of cylinder the potential distribution ψ(x) is quasi-exponential. The main advantage of the cylindrical cell model is that it gives the radial counterions distribution around the polyelectrolyte chain; that is especially important in salt solutions. But its application is difficult because in the most cases it requires numerical solution of the non-liner Poisson-Boltzmann equation; the exact analytical solution is possible only for an infinite cylinder.

The application of the cylindrical cell model to NaCMC takes into account the two kinds of counterions (H+ and Na+) in their two states (adsorbed and diffuse): H+ ions determine the potentials of the inner (ψ0) cylinder and Na+ cations on the external (ψ1) one; and the both cations are in competition in the diffuse cloud determining the potential ψ(x) together with the OH− anions. The difference between the two counterions is principal at the surface: H+ are potential determining for COO− groups but Na+ are adsorbed (condensed); in the diffuse cloud this difference disappear: H3O+ and Na+ are in competition determined by their concentration in the bulk.

3.3.3. Bjerrum length

The dependence of electrostatic energy on the distance between two ions (a negative and positive) leads to condition for equality of the electrostatic and thermal energies; the critical distance is called Bjerrum length:

lB = e2/4πε0εkTE6

where e is the elementary charge (electron); ε0ε is dielectric permittivity of the medium (the relative permittivity ε and electric constant ε0 in SI); kT is the thermal energy (the Boltzmann constant k and the absolute temperature T). In aqueous medium: lB = 0.712 nm at 20ºC (ε= 80.08) and lB = 0.700 nm at 25ºC (ε= 78.25). The Bjerrum length is about 3.8 times higher than the crystal radius of Na atom and commensurable with the diameter of hydrated Na+ ion (the counterion in salt-free solution of NaCMC).

Although Bjerrum had formulated the length lB as a criterion for ion pair formation in a concentrated electrolyte solution, Eq. 6 is used in the Oosawa-Manning two-state polyelectrolyte theory for estimation of the electrostatic interactions between the polymer charges and small counterions.

3.3.4. Two-state model

In this model the counterions (electrostatically associated to the polyelectrolyte chain) are separated into two categories according their physical state: condensed (strongly bound and located inside a narrow potential valley along the polymer backbone) and free counterions (loosely bound and freely moving in the volume surrounding the chain). On the base of this model Manning has developed a simple theory for counterion condensation on isolated infinitively long cylinder immersed in a liquid medium with a vanishingly low ion concentration [22]. Such conditions appear in aqueous solutions of rigid or semi-flexible chains as DNA and CMC at low polymer concentration in salt free solution (counterions originate from the polymer sample: Na+ in the case of NaCMC).

The Manning’s model consider the polyelectrolyte chain as a liner polyion with average distance b0 between its charges surrounded by a cylinder with radius a. The main parameter is the dimensionless charge parameter ξ determined by the linear charge density b0−1 and the Bjerrum length lB ≈ 0.7 nm (at room temperature):

ξlB / b0=e2/4πε0εkTb0.E7

A counterions condensation appears when ξ>1, i.e. when the mean distance between the two neighbour charges of the polyelectrolyte chain is smaller than 0.7 nm. When the degree of dissociation α increases until ξ<1, the linear charge density b−1 = N/Lc (determined by the total number N of unit charges per unit contour length Lc) increases linearly up to a limit where b0 = lB; in this region b = b0. At the point ξ = 1, the liner dependence b−1 = f (α) is broken and goes as a plateau at ξ>1, then N = const. I.e. at ξ>1 the effective charge density b−1 has its maximal value for a given linear polyelectrolyte and does not increase more although the chain’s own charges b0 continue to increase with α; this constancy of the total charge N is due to counterion condensation [23].

The fraction φ of the chain’s charges neutralized by the condensed counterions with valency z is equal to:

φ= 11/zξ= 1b0/zlB.E8

This equation allows determining the quantity of the condensed counterions when the quantity of the chain’s own charges (per unit contour length) is known. Like so the condensed ions fraction is determined by the distance between the ionizable groups along the chain and the degree of dissociation α.

By that way the Manning’s theory connect the counterions condensation with the chemical structure of the polyelectrolyte chain (the length of the polymer units and the nature of the ionizable groups) and the conditions of the medium (pH and temperature) together determining the quantity of chain’s own charges (equal to the total counterions quantity). The theory allows defining two fractions of counterions having different mobile capability: the condensed ions are immobile (during the existence of the Bjerrum pairs) while the ‘free’ ones are mobile undergoing impacts with the solvent molecules.

The Manning’s theory does not give exact value of the condensed ions fraction even when its two limits of validity (an infinitely long cylinder and vanishingly small concentration of small ions) are satisfied because Eq.(8) is derived on the base of analytical solution of the cylindrical Poisson-Boltzmann equation in its linearized form (assuming sinh ψ ≈ ψ) [24]. The numerical calculation of the non-linear cylindrical Poisson-Boltzmann equation shows that at small ξ (up to ξ ≈ 1/2) the liner dependence b−1 ≡ N/Lc = f (α) coincides with the Manning’s line but it is not broken at ξ = 1 and does not go on a plateau after this point. At ξ>1 the curve continue to increase although its slope decreases with ξ; this discrepancy increases with the ionic strength [8]. That means that the condensed ions fraction is smaller than the predicted by the Manning’s theory. Nevertheless its experimental verification has shown an excellent agreement between the theoretical and experimental values in the case of double stranded DNA: at predicted φ = 0.76 the obtained by NMR condensed counterions fraction is 0.75 [25].

3.3.5. Application of Manning’s theory to CMC

The distance between two glucose units in CMC chain (0.515 nm) and the degree of dissociation α determine the liner charge density b0−1. For CMC with degree of substitution DS = 1.00 the limit (ξ = 1) for the ions condensation appears at α = 0.72 according to Manning’s theory. At full dissociation (α = 1) the charge density is b0−1 = 1.94 nm−1 and the dimensionless parameter is ξ = 1.38 (at 20ºC), so condensation of Na+ counterions on COO− groups appears even in salt-free solution of NaCMC; the fraction of the condensed counterions is φ = 1−1/ξ = 0.28.

For CMC with DS = 1.20 the mean distance between two COOH groups is equal to 0.43 nm, so the charge density parameter is ξ = 1.66 at α = 1. At pH 6.0 the degree of dissociation is α ≈ 0.95 [8], ξ = 1.58 and the condensed counterions fraction is equal to φ = 0.37. So, the CMC chain remains negatively charged when it is immersed in salt-free aqueous medium at pH 6.0; about 63% of the dissociated groups are compensated by the diffuse counterions in the ionic atmosphere.

3.3.6. Relation between condensation and dissociation

The apparent dissociation constant pKa of the acid groups is shifted with ΔpKa relatively to its intrinsic value pKa0 due to the increased local concentration of H3O+ ions because of the strong electric field around the polyelectrolyte chain; the value of ΔpKa is proportional to the charge density b0−1(α) determined by the degree of dissociation α (Eq.3). It is reasonable to suppose that ΔpKa depends on counterions condensation both indirectly (by the effective value of b−1) and directly (forming ions pair [COO−Na+] instead COOH and influencing on the polarization of O−H electron-pair link in COOH groups). This means that the dependence of ΔpKa on α should have different course at ξ<1 and at ξ>1. This hypotheses can be experimentally tested by determining α = f(pH) and pKa = f(α) by potentiometric titration of aqueous solution of CMC.

For CMC with DS = 0.80 and 0.90 the charge parameter ξ is equal to 1 at α = 0.90 and 0.80; so, at these values of α the dependence pKa(α) should change its slope. This effect must be stronger at high ionic strength where the counterion condensation increases. Although in the last case the Manning’s theory is inapplicable, the limiting value ξ=1 also can be used as the dependence b−1(α) begins to deflect from line in the region of ξ≈1 as the numerical solution of the non-linear Poisson-Boltzmann equation shows [8].

The potentiometric titration α = f(pH) [8] shows that in salt-free solution the dependence pKa = f(α) is almost linear in the range α = 0.1−0.9 for CMC with DS = 0.81. The addition of NaCl up to 1 mol/L decreases the slope of the dependences pKa (α) but they are absolutely liner in the studded interval α = 0.25−0.97 for CMC with DS = 0.91.

The absence of a curvature of the experimental dependence pKa(α) at ξ≈1 shows out that counterions condensation does not influence the degree of dissociation (in the frame of the experimental accuracy). This result can be explained with the different nature of H+ and Na+ binding to COO− groups: the proton is involved in covalent linkage (coupled electron pair between H and O atoms) while the sodium ion is electrostatically bound. The different energy of these two kinds of banding leads to longer life of the COO−H links in comparison to the COO−Na+ bonds and respectively to much higher affinity of COO− groups to H+ than to Na+ ion.

Nevertheless, the presence of Na+ ions in the medium influences the COOH ↔ COO−+ H+ equilibrium by the local concentration of H+ in the diffuse cloud where H3O+ and Na+ ions are in competition being electrostatically equivalent; the evidence for that is the decreasing slope of the dependence pKa(α) at increasing concentration of NaCl [8]. This fact together with the absence of visible influence of Na+ condensation on α shows out that the physical state of the counterions (immobile or free moving) is not as important as its concentration in the vicinity of the polyelectrolyte chain. This conclusion demonstrates the advantages of the cylindrical cell model (distinguishing the counterions by their distance from the surface and considering their local concentration) in comparison with the two-state model (separating the counterions into two categories according their motility and disregarding the ‘free’ counterions distribution).


4. Conformation of free CMC chain in aqueous medium

As a polyelectrolyte the conformation of CMC chain is determined by its chemical structure and electric properties determining the chain rigidity and linear charge density; the both quantities also depend on the medium parameters (pH, ionic strength and temperature). The electrostatic interactions could be neglected at low pH and/or high salt concentration; then the chain could be considered as a non-charged.

The main structural peculiarity of the cellulose and its derivatives are the rigidity of the glucose rings and the impossibility of rotation around the C−O−C bonds between the neighbour rings because of β-1,4-linkage; the both factors determine the rigidity of the chain backbone. Although very restricted oscillations round the C−O−C bonds occur and that decrease orientational correlation of the monomer units (regarding the line defined by the first init). That means that the orientation of every glucose unit strongly dependents on the orientation of significant number its neighbours but the orientational correlation decreases slowly along the chain. So, the CMC chain can be defined as a semi-flexible; that allows applying the model of worm-like chain.

4.1. Theoretical definitions

The conformation of an individual polymer chain is described by its end-to-end distance h (the distance between the first and the last polymer units) or by radius of gyration Rg (averaged mean-square distance between the units and the center of mass); these quantities are averaged in time for one chain or for an ensemble of chains at a given moment: h and Rg. The CMC chain with contour length Lc has n = Lc/l units with length l = 0.515 nm. The value of l is taken equal to the size of the glucose residue (instead the length of C−C bound as in the case of flexible polymers) because of the rigidity of the glucose rings.

4.1.1. Unperturbed random coil

In the model of free-articulated chain (Kuhn’s model) the real chain is replaced by a hypothetical chain with length Lc = AKNK consisting NK>1 segments with length AK = sl (every segment has s monomeric units with length l); the rotation between the neighbour segments is completely free. For an unperturbed random coil the Kuhn’s theory gives for the mean-square end-to-end distance h2:


and for the statistical segment length:

NK=Lc2 / h20.E10

This equation allows determining AK and NK from the experimentally measured molecular mass M ~ Lc and h20 or the mean-square radius of gyration Rg2. For an unperturbed random coil at NK>>1:

Rg20=h20/= (AK/6)Lc.E11

The distribution of the segments of an unperturbed random coil is Gaussian at (a) Lc/AK > 10 and (b) when the polymer is immersed in “ideal solvent” (θ-solution or θ-temperature when the interactions polymer-polymer, polymer-solvent and solvent-solvent are compensated); for such coil h20 and Rg20 are proportional to the couture length Lc according the Eqs. (9) and (11) [26].

4.1.2. Expanded random coil

Out of the θ-conditions the proportionality between h2, Rg2 and Lc is infringed but the chain can be return to conformation of unperturbed random coil changing the thermodynamic properties of the solvent by the temperature and addition of salts; an indication for θ-point is an absence of dependence of h2 or Rg2 on the polymer concentration.

The linear expansion factor αe is determined by the ratio between the random coil size (averaged end-to-end distance h21/2 or radius of gyration Rg21/2) and its unperturbed value:

αe=h21/2 / h201/2=Rg21/2 / Rg201/2.E12

In “good solvent” (αe > 1) or “bad solvent” (αe < 1) the chain has more expended or compact conformation, respectively. The dependence of αe on the medium conditions is explained by the term “excluded volume” (equal to zero in “ideal solvent”) which includes the physical volume of the chain and the difference of repulsion and attraction forces between polymer segments when distant chain units encounter owing their thermal motion; the probability of such collisions increases with the chain length and decreases with the rigidity of the chain: αe ~ Lc/AK. The excluded volume additionally increases in the case of polyelectrolytes (at low polymer concentration) because of the electrostatic repulsion between the distant intermolecular chain units.

4.1.3. Persistent length

At Lc/AK < 10 the proportionality between h2, Rg2 and Lc is infringed (the segment distribution is non-Gaussian even in θ-solvent), so the Eqs. 9-12 are inapplicable. To describe the conformation of such short and rigid chains the worm-like chain model is introduced; its peculiarity is the continuously changing chain curvature.

The averaged angle φL between the tangents to two points at distance L1 along a worm-like chain is given by the expression:

cos φL= exp (L1/lp)E13

where the persistent length lp describes the e fold decreasing of the orientational correlation. In such way lp is a measure for the rigidity (local stiffness) of the worm-like chain; at Lc ≤ lp the chain can be described as a more or less curved rod. Comparison with the Kuhn model (at NK>1) gives the ratio: lp = (1/2) AK.

The unperturbed radius of gyration Rg201/2 can be expressed by the ratio between the persistent and contour lengths y = lp/Lc:

Rg20=Lc2{(1/3)y y2+ 2y3 2y4 [1  exp(1/y)]}.E14

This equation allows describing the size of chins of all length and rigidity including the both limits: rigid rod (very shot and rigid chains, then Rg20 = (1/12) Lc2) and Gaussian coil (long and flexible chains at Lc/lp >20 in θ-solvent).

The random coil expansion in good solvent leads to increase of the effective persistent length lp = lp0 + lpe, where the two terms represent the intrinsic persistent length and the electrostatic component, respectively. The electrostatic term decreases with the ionic strength of the medium; that manifest itself as decreasing of the random coil size (h21/2 or Rg21/2) when the salt concentration of the polymer solution increases.

4.2. Experimental methods

The classical techniques for experimental investigation of the polymer chain conformation in liquid medium are those of the viscometry and the static light scattering.

4.2.1. Viscometry

The viscometry is the technique most frequently employed in physical chemistry of polymer solutions. The method is based on the measure of the dynamic viscosity of the solvent η0 and of polymer solution η with concentration c and extrapolation of the relative viscosity η/η0 to c = 0. The characteristic viscosity (the limiting viscosity number) defined as:

[η] = limc0[(η/η01) / c]E15

is connected with the molecular mass M and the end-to-end size h201/2 of the macromolecules:

[η] =KMa,   and       [η] =Φh23/2/ME16

where K and a are constants specific for a given polymer/solvent solution; Φ ≈ 2.1 1023 (when the dimensions of [η] and h201/2 are cm3/g and cm, respectively) is a unspecific constant for linear chains with conformation of random coil in good solvent.

The constant a gives information about the form of the macromolecules: a = 1.8 for rigid thin rod with axes ratio ≥100; for unperturbed random coil a = 0.5 and increases up to 0.8 for an expanded coil. The method is widely used due to its experimental simplicity but it is not absolute requiring calibration with monodisperse fractions with independently determined molecular mass M. Once the constant K and a are known the equations (16) allows determining the mass and size of the random coil by measuring [η].

4.2.2. Small angle static light scattering

The second widely used method for determination of the polymer chain mass and conformation is the static light scattering [27]. Its main advantage is that it is absolute: for determination of the squared radius of gyration Rg2 and molecular mass M a calibration with polymer fractions is not required. Because the relative size (Rg21/2/λ is small relatively to the wavelength λ (in the medium), the small angle approximation (equation of Guinier) is applicable for the light scattering of polymer solutions with weight concentration c:

cH/Rθ= 1/M+ (16π2/3) (n0/λ0)2 Rg2ñ sin2(θ/2),E17

where H ~ [(n02/λ04)(dn/dc)2] is an optical constant (specific for a given pair polymer/solvent but not depending on c in diluted solution) determined by the refractive indexes of the polymer solution n and the medium n0 at wavelength λ0 (in vacuum); the increment of the refractive index (dn/dc) = (n−n0)/c (at c→0) is measured by refractometry. The scattering coefficient (Rayleigh ratio) Rθ = I/I0 is determined by the quantities measured in the experiment: intensities of the incident light I0 and the scattered I at angle θ. For determination of Rg2 it is not required to know the absolute values of c and H: it is enough to measure the dependence 1/Iθ ~ sin2(θ/2) at a few c and extrapolate 1/Iθ to c = 0. The extrapolated to θ = 0 concentration dependence c/R0º ~ A2c (not considered in Eq. 17) gives the second virial coefficient A2 which allows determination of the random coil expansion factor αe [28].

4.3. Factors determining CMC chain conformation

4.3.1. Rigidity and molecular mass

The impossibility of rotation between the neighbour glucose units reflects in high persistent length lp = 5−20 nm of the cellulose and its derivatives [29]; this value is one-two orders higher than for polymers with flexible chains (lp = 0.2 nm for poly(ethylene glycol) [26]). The relatively high value of the lp allows to define CMC chain as worm-like and suggest that (depending on the contour length Lc) its conformation is rod-like at Lc<lp or random coil at Lc>lp. As a rule CMC samples have enough high M and than Lc >> lp; that predicts random coil conformation. This expectation is conformed experimentally by viscometry and light scattering.

The viscometry measurements of aqueous solutions of cellulose and its derivatives showed out that the factor a in Eq. (16) lies near to a ≈ 0.8 [29]; this value is characteristic for expanded random coil. The light dependence on the presence of charged or non-charged lateral groups conform the supposition that the CMC rigidity is determined mainly by the β-1,4-linkage in the chain backbone; for comparison: a ≈ 0.5 (defined for non-expanded random coil) for amylose acetate due to α-1,4-linkage [26]).

CMC conformation is studied by small angle static light scattering (at eleven fixed angles θ = 44º−151º) in combination with size exclusion (gel permutation) chromatography and refractive index detector [8]. That technique allows continuous measuring of Rθ and c while the given fraction is eluted and on-line determining of Rg2 and M from the initial slope of cRθ−1 = f [M−1, sin2(θ/2)] according to Eq. (17). The measurements of CMC samples with degree of substitution DS = 0.75−1.25 have given Rg21/2 = 30−140 nm and mean-weight mass Mw = 120−1100 kg/mol (these masses correspond to contour length Lc ≈ 260−2800 nm). On Fig. 1 is shown the experimental dependence of Rg on mean-weight Mw or mean-number Mn molecular mass; the difference between Mw and Mn is due to the polydispersity of the polymer samples (the polydispersity index is Mw/Mn ≈ 1.6−2.7).

Figure 1.

Dependence of the radius of gyration Rg on the mean-weight molecular mass Mw (the bottom abscissa), or mean-number molecular mass Mn (the top abscissa) of CMC with DS = 0.75 (), 0.91 () 0.99 () and 1.25 (). The values of Rg are measured by static light scattering; the data are taken from Ref. [8].

The above cited experimental results allow describing the conformation of CMC chains with lp ≈ 15−17 nm at different molecular mass M. At Lc ≤ lp the CMC chain has a conformation of bend rod which curvature changes in time due to the thermal motion; the chain with Lc ≈ 15 − 17 nm has 29−33 glucose units and M = 3648−4134 g/mol (in the case of NaCMC with DS = 1.0). At Lc > 10AK the CMC chain has a conformation of random coil; a chain 10 times longer than the Kuhn segment (AK = 2lp ≈ 30−34 nm) has 582−660 glucose units and M = 142−160 kg/mol. So, NaCMC with M higher than 150 kg/mol has a conformation of some expanded random coil.

4.3.2. Linear charge density and ionic strength

The viscometry data [29] for high molecular CMC show out that the expansion factor αe in aqueous medium (good solvent for CMC, αe>1) is additionally increased due to the electrostatic repulsion between COO− groups; the effect increases in the range pH 2−6 (α ≈ 1 at pH 7) due to the liner charge density b−1(α) increasing with the degree of dissociation α. The expansion of the random coil reflects in increased value of the effective persistent length lp = lp0 + lpe and its electrostatic component lpe; the effect is influenced by the ionic strength of the medium. The value of the intrinsic (structural) component lp0 of the persistent length is estimated to be 5.0 nm in high salt concentration (where the electrostatic interactions are negligible) [30]. In water/cadoxen (Cd2+-ethylendiamine complex) mixtures lp0 = 8.5 nm was obtained [31].

Static light scattering [8] also show out that the random coil size of CMC depends on the ionic strength; the effect is proportional to the number of Kuhn segments NK = Lc2 / 6Rg20 for chain with contour length Lc. At NK = 100 the radius of gyration decreases from Rg21/2 ≈ 190 nm (in 0.02 mol/L NaNO3) to 140 nm (in 0.1 mol/L). That indicates for diminishing of αe and lpe with the ionic strength owing to decrease of the electrostatic component of the excluded volume (the origin for the random coil expansion).

It seems that the decreasing of Rg21/2 with salt concentration is caused not entirely by the electrostatic shielding of COO− groups; an additional factor is the structural rigidity (lp0) diminished with dehydration of CMC chain. This effect is probably one of the reasons for high difference (reaching 3 times) of the values of lp0 obtained at low and high ionic strength; another reason is the imperfections of the theories employing to estimate lp0 from data obtained by hydrodynamical (viscometry, dynamic light scattering) and statical (static light scattering, potentiometric titration) methods.

At pH 7.0 (α≈1) the light scattering data show out a linear dependence of Rg21/2 on M in the range Mw = 120−1100 kg/mol (Fig. 1); linear is also the dependence of Rg21/2 on the number of statistical segments NK [8]. The both dependences do not depend measurably on the degree of substitution DS = 0.75−1.25 (in this range the charge parameter ξ increases from 1.04 to 1.73). This independence on DS could be considered as evidence for counterion condensation; i.e. the effective linear charge density b−1 does not increase (at ξ>1) with chain’s charges (the number of COO− groups per unit length of CMC backbone) due to adsorption of Na+ ions. This conclusion is done in Ref. [8] but it is not enough reliable because Rg21/2 of CMC chain is determined mainly by its structural parameters (lp0 and Lc) but lightly depends on its electric properties (b−1) because lp0 >> lpe.

4.4. CMC according to the wormlike chain models

For CMC the salt concentration needed to reach the state of unperturbed random coil (θ-solvent) has been estimated to be about 5 mol/L NaCl [32]. Because this concentration is practically unreachable, the CMC random coil is always expanded. That is why an electrostatic worm-chain theory is needed to evaluate the unperturbed random coil parameters, in particular to distinguish the structural and electrostatic components of the excluded volume and the persistent length.

In Ref. [8] the experimental data (obtained by static light scattering) have been used to calculate the CMC molecular parameters according to the models of Odijk [33] and Davis [32]; the last is better validated. The Davis’ model gives the following parameters (for CMC with DS = 1.25 in 0.02 mol/L NaNO3): (a) expansion factor increasing with M in the range αe ≈ 1.16−1.40 at Mw = 120−1100 kg/mol (Lc = 254−2330 nm); (b) electrostatic component of the persistent length lpe = 2.9 nm; and (c) intrinsic persistent length (estimated as a fitting parameter) lp0 = 17 nm. In 0.10 mol/L NaNO3 these quantities are: αe ≈ 1.07−1.14; lpe = 0.8 nm; and lp0 = 15 nm [8].

In the same work lp0 ≈ 6 nm (for CMC with DS = 0.9 in salt-free and in 0.01 mol/L NaCl) and lp0 ≈ 3.5 nm (in 0.1 mol/L NaCl) was estimated from dependence pKa (α) (obtained from titration curves α(pH)); the values of lp0 are calculated using the theory of Katchalsky and Lifson [34]. This values are 3−4 fold decreased according to the obtained by Davis’s theory (from scattering data for Rg(M)); the discrepancy reflects rather the imperfections of the theoretical models for wormlike chain than the inaccuracy of the employed experimental methods. It seems that the Davis model gives more realistic values because the Katchalsky-Lifson model overestimates the electrostatic energy [8].

4.5. Peculiarity of CMC chain

The comparison between the intrinsic lp0 ≈ 15−17 nm and electrostatic lpe ≈ 1−3 nm components of the persistent length (both obtained by Davis model) shows that the high rigidity of CMC chain is predominantly due to its chemical structure but the electrostatic repulsion plays a minor role although the linear charged density is high at neutral pH (about 2 charges per nm); that leads to relatively low expansion factor (αe ≈ 1.2−1.4) even for very long chains (Lc = 0.3−2,3 μm) at low ionic strength.

For comparison: the uncharged chain of poly(ethylene glycol) (PEG) with contour length Lc= 26 nm has NK = 35 statistical segments with length AK = 0.73 nm, unperturbed radius of gyration Rg201/2 ≈ 1.8 nm and expansion factor αe = 1.31 [35]. I.e. due to the flexibility of the PEG chain its Kuhn segment is about 40 times shorter than that of CMC.


5. Electric polarizability of CMC

5.1. Counterions polarizability of free CMC chains

5.1.1. Electric polarizability of polyelectrolytes in solution

When an external electric field with strength E is applied to polyelectrolyte solution an electric polarization γE appears (the coefficient γ is named polarizability) [36]. The polarization of polyelectrolytes in aqueous medium is determined mainly by migration of counterions along the chain; this assertion follows from the strong dependence of γ on the counterions quantity (determined by the linear charge density b−1 and pH-dependent by the degree of dissociation α). The contribution of other kinds of polarization (electronic, atomic and orientation of polar groups) is negligible in fields with moderate strength; a measurable orientation of short rigid chains as DNA fragments is possible only in high voltage electric field [37].

In sinusoidal electric field the frequency ν determines the time for which the counterions move in one direction and results in the γ magnitude when the half-period is not enough long to reach equilibrium allocation; the critical frequency ν1/2 is defined as ν where γ decreases twofold. The value of ν1/2 = 1/2πτi is determined by the relaxation time τi of the polarization which depends on the distance of migration and the diffusion coefficient of the counterions. So, the polarizability dispersion (the frequency dependence γ = f(ν)) gives information for the counterions mobility.

The theories describing the polyelectrolyte polarization (the magnitude of γ and its frequency behaviour γ(ν)) are based on different physical models considering migration of counterions with diffusion coefficient Di on distance L along a linear polyion. Schwarz’s equation [38,39] give ν1/2 = 4Di/πL2 for strongly elongated particles with length L. According Mandel the polarization γi and the relaxation time τi of one-dimensional lattice with length L in the case of one type of counterions with valency z, mobility u and total number N are [40]:

γi = (z2e2/12kT) NL2   and     τi = (1/12ukT) L2E18

where e, k and T are the elementary charge, Boltzmann constant and the absolute temperature.

According Oosawa fluctuation theory the counterions polarization appear in both presence and absence of external electric field; in the last case a spontaneous dipole moments appears due to fluctuation of counterions concentration along the polyelectrolyte chain [41,42]. In the case of N number monovalent counterions the main component of the polarizability is:

γi = (e2/2πkT) NL2     and     τi = (1/4π2ukT) L2E19

The most of the theories consider polyelectrolyte polarization as displacement of one-state counterions or does not distinguish the contribution of the diffuse and condensed counterions. One of the exclusion is Minakata’s stochastic theory [43] considering an infinite linear chain of discrete charges which counterions have different transitional mobility depending on the distance from the polyion. The theory shows that the counterions contribution depends on the potential barrier which they have to overcome jumping from one lattice site to the next, so the loosely bound (diffuse) counterions give the main electric polarization at higher frequency; the contribution of strongly bound (condensed) counterions should appear at lower ν. Thus, the two kinds of counterions are distinguished by their increment to the magnitude of γ and by the relaxation frequency ν1/2.

5.1.2. Polarizability of CMC at random coil conformation

The counterions polarizability is usually studied by the dielectric permittivity [44] or conductivity [45,46] of polyelectrolyte solutions; the first method is well working in salt-free solution and the second – in small-ions electrolyte. The measuring signal is electrical: the capacitance or active current between two electrodes. At these techniques the applied field does not influence the conformation of the polyelectrolyte chain because the field strength is very low and the polarization is due to counterions replacement only. An imperfection of the both methods is that they require high polymer volume fraction because the both polyelectrolyte and the bulk contribute to the measured signal (dielectric or conductivity current); that complicates the interpretation because of the intermolecular interactions at increased polymer concentration. Another problem is the electrode polarization; that limits the ion strength at permittivity measuring.

Dielectric spectroscopy of aqueous solutions of NaCMC shows two dispersions: high-frequency [47] and low-frequency [48]; the presence of two dispersions is typical for polyelectrolytes. The high-frequency dispersion is independent on the contour length but the low-frequency is strongly dependent on it; on this base the two frequency regions are attributed to counterions moving along chain’s parts or along the hole polyelectrolyte chain, respectively [49,50].

5.1.3. Polarizability of CMC at orientation in electric field

At high field strength the counterions polarization is accompanied with orientation of the polyelectrolyte chain backbone; as a result optical anisotropy of the solution appears. Electro-optical methods are based on registration of the anisotropy of the refractive index Δn (birefringence) or the absorption coefficient (dichroism) [51]. A principal advantage of these techniques is that the bulk does not contribute to the measuring signal; that allows multiplying the sensitivity be increasing the optical path and work at lower polymer concentrations. Another important advantage is the possibility to obtain information for both electrical and hydrodynamical properties of the polyelectrolyte chain by measuring the steady-state Δns and transient Δnt anisotropy. These properties can be separately studded by the measuring Δns ~ γE2 and Δnt ~ Δnsexp(−t/τ0) with time t after switching off the electric field (τ0 is the relaxation time determined by the coefficient of friction of macromolecules with given size and form).

The capabilities of the electric birefringence to study aqueous solution of NaCMC are demonstrated in Ref. [52]. In this work the orientation of CMC with M = 30−250 kg/mol is done by applying of a single high voltage rectangular impulse; the field strength reaches E ≈ 2 MV/m. The results show that the polarizability increases with M but the slope of γ = f(Lc) decreases in the range M ≈ 5−100 kg/mol and reaches plateau at M ≈ 250 kg/mol. The found dependence of γ on Lc is different from predicted by Eqs. (17,18) (γ ~ L2); the reason for that is revealed comparing the measured disorientation time τ0 with calculated ones for rigid rod, bending rod and worm-like chain. The comparison show out that the experimental values of τ0 corresponds to the rigid rod model (τ0 ~ L3) only for very short chains with mass less than M ≈ 5 kg/mol; this M corresponds to 20 glucose residues and Lc ≈ 10 nm. This value of Lc coincides with the persistent length lp = 5−15 nm obtained by viscometry and static light scattering (see section 4.3).

From the result in Ref. [52] it follows that the counterions are moving along the CMC chain on a distance commensurable with lp. At higher distance the counterions displacement is limited by the local curvature of the chain backbone (which determine the field component along the chain); when the curvature is higher than right angle the counterions are moving in opposite directions along two neighbour chain segments. That means that lp instead Lc should be used when estimating γ and τi. So, concerning counterions polarizability the long CMC chain can be presented as a consequence of rods likewise the free-articulated chain in the Kuhn model. That allows explaining the experimental fact that γ(Lc) is almost constant at M ≈ 250 kg/mol [52]; at these M the NaCMC chain with DS = 1 has Lc ≈ 530 nm and about 16 statistical segments with length AK = 2lp ≈ 34 nm.

Hydrodynamic behaviour of CMC in electric field suggests that in the case of long chain the orientation of its segments is accompanied by deformation of the random coil; the degree of deformation is determined by both polarizability and rigidity of the chain. The contribution of both electrical and mechanical properties complicates the interpretation of the experimental results about the polarizability of chains with Lc > lp.

Demonstration of that are dependences Δns(ν) of CMC with 230, 1100 and 2000 glucose units (Lc ≈ 120, 570 and 1030 nm) described in Ref. [53]. In this work the sinusoidal field with low strength in combination with very sensitive detection (based on an amplitude modulation of the birefringence signal) is used. The results show out that the dispersion curves Δns(ν) are quite different at frequencies under and up a few kilohertz. In the hertz diapason Δns has negative values indicating predominant orientation across the electric field; the absolute value │−Δns│decreases with diminishing of the degree of dissociation α and with increasing of M, CCMC and CNaCl (concentrations of CMC and the added NaCl, respectively); Δns becomes positive (orientation along the field) at high values of M, CCMC and CNaCl even at α = 1. The dependence on α, M, CCMC and CNaCl in kilohertz diapason is analogical although there Δns is positive in all conditions. The dependence of Δns(ν) on α and CNaCl in both low and high frequency diapasons confirms that the orientation-deformation of CMC chain is due to counterion polarization. In the same time the dependency of Δns(ν) on M and CCMC suggest a complicated relation between of the electrically induced conformation of CMC chain and its electrical (γ) and mechanical (lp) properties; an manifestation of that is the unexpected negative value of Δns. This complexity does not allow application of the theories developed for counterions polarizability γ(L) of straight rigid polyions and do very difficult the interpretation of the experimental dependence Δns(ν) in order obtaining information about γ(Lc) at Lc >> lp.

5.2. Polarizability of CMC adsorbed on colloid particles

5.2.1. Electrophoretic mobility of CMC-alumina particles

A polyelectrolyte adsorption on solid/liquid interface allows overcoming the difficulties connected with the electrically induced conformation of long CMC chains. In this case the parts of the adsorbed chain are immobilized on the hard surface and that hinders chain deformation. An additional advantage has the adsorption on colloid particles with submicron size; then an electric field with moderate strength is enough to orientate the particles due to the their big size (in comparison with the polymer random coil). Then the electro-optical method employed allows registering reliably the orientational degree averaged over the particles ensemble; due to high sensitivity of this technique it is possible to work at low particle concentration.

The adsorption of polyelectrolytes alters the electric and hydrodynamic properties of the solid/liquid interface; an indication for that is the change of the electrophoretic mobility uel of the particles. On Fig. 2 is shown the dependence of uel on the concentration CCMC of NaCMC at adsorption on alumina (γ-Al2O3) particles [54]; uel = v/E is measured by the technique of micro-electrophoresis (microscopic measuring of the velocity v in electric field with strength E). The dependence uel(CCMC) is studded at pH 6 where the alumina surface is positive (the isoelectric point is at pH 8.5) and the COO− groups of CMC are almost fully dissociated; the opposite charge sign is a precondition for electrostatic adsorption. The change of uel sign from positive to negative indicates over-equivalent adsorption of CMC and predominant exposition of the polyelectrolyte charges. The steep slope of the curve before the isoelectric point reflects the well known fact that all added polyelectrolyte is adsorbed on the surface at low polymer concentration; that is a characteristic of polyelectrolyte adsorption on an oppositely charged surface [55,56]. The plateau at high CCMC reflects the saturated adsorption because electrostatic repulsion of already recharged surface and the CMC macromolecules.

Figure 2.

Dependence of electrophoretic mobility uel [10−8 (m/s)/(V/m)] of γ-Al2O3 particles on the concentration CCMC [g/L] of NaCMC in water-polymer suspension.

The concentration dependence uel(CCMC) shows out that the surface electric properties of the CMC covered alumina particles are determined predominantly by the charge of the adsorbed layer; the particle surface charge does not manifest itself apparently because of electrostatic and hydrodynamic shielding by the polyelectrolyte layer. This gives opportunity to study electro-optically the electric polarizability of CMC being adsorbed on the colloid particles; in the case the hard core of coated particles determines their optical properties but the orientation depends on the counterions polarization in the polyelectrolyte layer.

5.2.2. Electric light scattering in suspension

The theory of this method [57] is developed in the Rayleigh-Debye-Gans approximation [58] which restricts: (a) the relative refractive index n = n1/n0 (n1 and n0 are the refractive indexes of the particles and the medium, respectively); and (b) the relative size L/λ (where L is the particle length and λ is the wavelength in the medium; λ = λ0/n0 when λ0 is the wavelength in the vacuum). The light scattering intensity I0 at random orientation of the particles is determined by the function of internal interference P(θ) (form-factor) at scattering angle θ [27]:


where: k – the apparatus constant determined by the scattering volume and the solid angle of the photoreceiver; c – the particle weight concentration; H – the optical constant defined by λ0, n0 and n1; M – the particle mass.

When an electric field is applied to the suspension, the light scattering intensity IE is changed due to particles orientation [59]. The absolute electro-optical effect (EOE) ΔI = IE − I0 can be determined by the functions of internal interference at certain degree of orientation P(θ, E) and at random orientation P(θ) [60]:

ΔI=kcHM[P(θ,E) P(θ)],E21

At an orientation degree Φ (varying from 0 at random orientation to 1 at full orientation):

P(θ,E) =P(θ)+A(KL)×Φ(γ,E,T),E22

where: KL = 2π(L/λ)sin(θ/2). The optical function A(KL) is determined by the form and relative size L/λ of the particles; the expressions for A(KL) are different at low and high degree of orientation. The value of Φ at steady-state EOE is a function of the electric polarizability γ, the electric field strength E and the temperature T.

The relative EOE ΔI/I0 does not depend on k, c, H, M and it is defined at a moment t only by P(θ,E) and P(θ), which are functions of the particles’ form, size and optical anisotropy:

ΔIt /I0= [P(θ,E) /P(θ)]  1 = [A(KL) /P(θ)]×Φ(γ,E,T,t).E23

In the steady-state Φ (γ, E, T) depends only on the ratio between the orientation energy γЕ2 and the energy of random motion kT. Then EOE at low degrees of orientation (γE2<< kT) is:

ΔIs/I0= [A(KL) /P(θ)]×(γE2/15kT).E24

The electro-optical results described below are obtained at θ = 90º by cell with platinum electrodes at interelectrode distance of 2.6 mm. The light scattering intensities I0 (in absence of electric field) and ΔIs (in sinusoidal field with strength E ≤ 54 kV/m) were measured after reaching steady-state polymer adsorption.

5.2.3. Kilohertz polarizability of CMC-alumina particles

Figures 3 and 4 represent the field dependence ΔΙ /Ι0 = f(E2) at several CMC concentrations. The linearity of the graphics means that the degree of orientation is low, i.e. γЕ2<<kT. Therefore γ is proportional to the slope of the lines [(ΔΙ /Ι0) /E2] according to eq. (23).

Figure 3.

Dependence of steady-state EOE (ΔIs /I0)×100 in water-polymer suspension of γ-Al2O3 particles on the squared field strength E2 [108 V2m−2] at 1 kHz and NaCMC concentrations CCMC = (4 − 6) ×10−4 g/L NaCMC (under the recharging point).

Figure 4.

Field strength dependence (the same as in Fig. 3) at CCMC = (5 − 50) ×10−3 g/L NaCMC (above the recharging point).

Fig. 3 shows out that the polarizability decreases with CMC concentration but Fig. 4 demonstrates just the opposite: γ increases with CCMC. The both trends correlate with the concentration dependence of the electrophoretic mobility uel(CCMC) (Fig. 2) which reflects the alteration in the total surface charge of the particles with adsorbed CMC. That means that the magnitude of γ depends mainly on the total charge of the diffuse counterions (which decreases before the recharging point and increases after it). So, the kilohertz polarizability is due predominatingly to the diffuse counterion but that does not exclude participation of condensed ions.

5.2.4. High frequency dispersion of CMC-alumina polarization

The change of the half-period 1/2ν of the applied sinusoidal electric field allows altering the ions migration distance and by that the contribution to γ of the counterions being in two physical states: adsorbed and diffuse. According the theory (see paragraph 5.1.1) the condensed cations have diminished mobility along the CMC chain due to the strong electrostatic interaction with the charged COO− groups. The critical frequency ν1/2 ~ Di/L2 depends on the polyion length L and the diffusion coefficient Di of the counterions electrically associated to the polyelectrolyte chain (Eqs. 17, 18); so, at constant L (absence of particles aggregation, see Ref. [54]) the value of ν1/2 gives information about the counterions mobility. The dispersion dependence γ(ν) shows the magnitude and ν1/2 of the polarizability components with different Di/L; that allow distinguishing the contribution of the condensed and diffuse counterions.

Figure 5.

Normalized high frequency dependence of EOE (ΔI/I0) of alumina particles in water (curve 1) and in aqueous solution NaCMC (Mw = 250 kg/mol) at concentrations: 4∙10−4 g/L (curve 2), 6∙10−4 g/L (curve 3) and 1∙10−2 g/L (curve 4). The EOE ΔIs/I0 at 1 kHz is taken to be one for all curves.

The frequency dependences of EOE of alumina particles with size 0.3 μm in CMC solution is shown in Fig. 5. The total particle charge is positive for curves 1−3 and negative for curve 4 (recharged surface). The critical frequency decreases with the adsorbed CMC amount: ν1/2 ≈ 550 kHz (curve 2), ν1/2 ≈ 220 kHz (curve 3) and ν1/2 ≈ 80 kHz (curve 4).

The form of the dispersion curves γ(ν) indicates that the polarization is due to one kind of counterions; in the case of different Di/L the curves should have a shoulder with fixed ν1/2 but increasing increment while the CMC adsorbed amount grows. The value of ν1/2 at saturated adsorption (curve 4) is not very different from that at small CMC surface concentration (curves 3 and 2) and bare particle (curve 1) determined by the diffuse counterions polarization; this fact together with the absence of noticeable shoulder allows concluding that the polarizability of the CMC covered surface (curve 4) is due to the diffuse counterions around the particles. The displacement of the ν1/2 to lower frequencies could be explained with their decreased mobility because of the presence of polymer layer, i.e. the effective diffusion coefficient Di is smaller than that of free ions in solution.

Nevertheless, the results in Fig. 5 do not exclude unambiguously the condensed counterions participation in the polarization. The absence of the increasing shoulder at CMC adsorption could be owing to equal ratio Di/L for the condensed and diffuse counterions. In this case DNa of the condensed Na+ ions should be 400 times less than that of the diffuse ones assuming L = lp = 15 nm for bound counterions and L = 0.3 μm (the particle size) for the free ones.

To exclude the possibility that the values of ν1/2 ~ Di/L2 of the diffuse and condensed counterions polarization coincide due to unique combination of L and Di we have studied the concentration dependence γ(CCMC) which reflects the magnitude of γ as function of the quantity of both kinds of counterions [54]. The measurements are performed at ν = 1 kHz where the half-period 1/2ν is long enough to reach the equilibrium distribution of counterions in any moment t in a field with instantaneous strength Et = E0sin(2πνt); indication for that is the plateau at all CCMC (Fig. 5).

5.2.5. Concentration dependence of CMC-alumina polarizability

The contribution of the diffuse and condensed counterions can be estimated by comparing the concentration dependences of the polarizability γ(CCMC) and mobility uel(CCMC). This approach is based on the fact that the condensed counterions move together with the polyelectrolyte chain in a permanent electric field, that is why they are not seen in methods based on the translational motion in a d.c. electric field [61]. I.e. the uel gives information about the quantity of the diffuse counterions only while the polarizability in a sinusoidal field reflects participation of the all movable counterions.

When the amount of adsorbed CMC increases with CCMC then the ratio condensed/diffuse counterions alters but in a different way before and after the isoelectric point. The quantity of condensed ions increases for all CCMC concentrations where adsorption appears but the quantity of the diffuse counterions decreases before the recharging point and increases after it. The comparison between γ(CCMC) and uel(CCMC) at lower CCMC concentrations can give unambiguous information about the relative contribution of the diffuse and condensed counterions due to the opposite change of their quantity. In this concentration range the slope of the dependence γ(CCMC) should be negative but smaller than that of uel(CCMC) taking into account that the adsorbed CMC introduces approximately one condensed and two diffuse Na+ counterions on every three COO− groups (see paragraph 3.3.5).

Fig. 6 refutes this expectation: both the curves have the same slope before the isoelectric point; this disproves the hypothesis that the condensed ions participate in the polarization. The difference at the higher CMC concentrations can be explained by the different influence of the polymer layer on the behaviour of the counterions in direct and sinusoidal electric field and by the way the figure is constructed: the two quantities are equated (γ = uel) at CCMC = 0.

Figure 6.

Fig. 6. Dependences of the absolute value │uel│ of the electrophoretic mobility (curve 1, left ordinate) and the electric polarizability γ (curve 2, right ordinate) of γ-Al2O3 particles on the concentration CCMC of NaCMC. The uel and γ are given in relative units assumed to be equal in the absence of CMC. The sign of uel is positive at CCMC under 3 mg/L (the red part of the curve) and negative above this concentration (the blue part).

So, the correlation between the concentration dependences γ(CCMC) and uel(CCMC) indicates that the kilohertz polarizability of the alumina particles with adsorbed CMC is determined by the diffuse counterions.

5.2.6. Comparing with the literature

A low frequency shift of the polarizability with ν1/2 ≈ 3 kHz is found at saturated CMC adsorption on ferrioxide particles [62]. That value of ν1/2 is 25 times lower than ours (curve 4 on Fig. 5) although in both experiments the same CMC specimen (Mw = 250 kg/mol, DS = 1.2) is studied. The difference in ν1/2 could be related to the different particles employed; this suggests that the value of ν1/2 is determined by L rather than by Di. An additional argument is that the ν1/2 ≈ 80 kHz of CMC coated alumina particles lies in the frequency region specific for the diffuse counterions polarizability of elongated ellipsoids with L ≈ 0.3 μm (taking into account that ν1/2 ~ 1/L2) [63]. That means that the interfacial polarization of CMC coated particles is determined by the diffuse counterions displacement around the whole particle but not along the CMC chains. If the bound counterions are the origin of the electric polarization then a shoulder on the dispersion curve should appear and its increment must be proportional to the surface CMC amount.

In Ref. [62] a principally different conclusion is drawn: the electric polarizability of CMC coated particles is due to the condensed counterions. The interpretation is based on the low-frequency shift of the dispersion curves employing the Schwarz’s equation ν1/2 = 4Di/πL2 and using the literature value Di = 6 10−11 m2/s [64] for bound Na+ in a CMC solution; the CMC chain is assumed to be a straight polyion with length L = 505 nm (equal to the contour length Lc of CMC with M = 250 kg/mol). Then, accepting that the estimated ν1/2 = 300 Hz is close to the experimentally obtained ν1/2 ≈ 3 kHz, the authors conclude that the orientation of CMC coated particles in the electric field is due to condensed counterions polarization along the adsorbed polyelectrolyte chains.

The interpretation in Ref. [62] is wrong because the CMC chain with a contour length Lc = 0.5 μm cannot be considered as rod-like neither free in the solution nor adsorbed on the particle surface. It is well known that parts of adsorbed chain take a quasi-planar (two-dimensional) conformation and the rest of the chain retains a three-dimensional conformation [65], so the form of adsorbed CMC is predetermined by its conformation in solution. A free CMC chain with M = 250 kg/mol has the conformation of a random coil with NK ≈15 statistical segments (see section 4.3) and a radius of gyration Rg = 44 nm (Fig. 1). So, for a CMC chain with Lc = 0.5 μm the magnitude of γ and the critical frequency ν1/2 cannot be estimated using the contour length Lc in the equations derived for the polarizability of straight polyions. This conclusion is confirmed by results for CMC in aqueous solution: the experimental dependence γ(Lc) does not correspond to γ ~ Lc2 predicted by Eq. (17, 18) but has a plateau at M ≥ 200 kg/mol [52]; so, the dependence ν1/2 ~ L−2 (according Schwarz’s equation) is also not applicable for long CMC chains.

My opinion is that the polarizability of the polymer covered particles is due to the diffuse counterions but their mobility is decreased because of the presence of the polymer layer, i.e. the effective diffusion coefficient Di is smaller than that of the free ions in solution. The reason for such interpretation is the fact that the dispersion curve displacement (towards lower ν1/2) increases with the CMC amount on the particle surface.


  1. 1. D. A.ReesAdv. Carbohydr. Chem. Biochem. 2419691969267332
  2. 2. V. S. R.RaoN.YathindraP. R.SundararajanBiopolymers 819691969325333
  3. 3. B. K.SathyanarayanaV. S. R.RaoBiopolymers 111972197213791394
  4. 4. E.OttH. M.SpurlinM. W.GrafflinCellulose and Cellulose Derivatives,part II, High Polymers, vol. V, Interscience publishers, New York, 1954
  5. 5. D. E.MetzlerBiochemistry, Academic press, New York, 1977
  6. 6. J.ReubenH. T.ConnorCarbohydr. Res. 11519831983113
  7. 7. Z.MaZ.WiebangZ.LiChineseJ.Polym. Sci. 7 (1989
  8. 8. C. W.HoogendamA.De KeizerM. A.CohenStuartB. H.BijsterboschJ. A. M.SmitJ. A. P. P.Van DijkP. M.van der Horst, J.G. Batellaan, Macromolecules 311998199862976309
  9. 9. A.KatchalskyN.ShavitH.EisenbergJ.PolymSci. 13195419546984
  10. 10. F. H.CrowdhuryS. M.NealeJ.PolymSci. 1 (1963
  11. 11. L.ZhangT.TakematsuT.NorisuyeMacromolecules 20 (1987
  12. 12. A. V.DobryninM.RubinstainProg. Polym. Sci. 302005200510491118
  13. 13. A.KatchalskyZ.AlexandrowiczInB. E.ConwayR. G.Baradas (Eds.), Chemical physics of ionic solutions, London, Wiley, 1966295346
  14. 14. F.OosawaPolyelectrolytes, New York, Marcel Dekker, 1971
  15. 15. R. M.FuossA.KatchalskyS.LifsonProc. Natl. Acad. Sci. USA 3719511951579586
  16. 16. Z.AlexandrowiczA.KatchalskyJ.PolymSci. Part A 11963196332313260
  17. 17. A.KatchalskyPure Appl. Chem. 2619711971327374
  18. 18. T.NishioA.MinakataJ.ChemPhys. 113200020001078410792
  19. 19. T.NishioA.MinakataJ.PhysChemB.1072003200381408145
  20. 20. H.OhshimaK.Furusawaeds.), Electrical Phenomena at Interfaces: Fundamentals, Measurements and Applications, 2ed edition, Dekker, New York, 1998
  21. 21. H.OhshimaTheory of Colloid and Interfacial Electric PhenomenaElsevier/Academic Press, Amsterdam, 2006
  22. 22. G. S.ManningJ.ChemPhys. 5119691969924933
  23. 23. G. S.ManningPolyelectrolyte binding, 1219791979443449
  24. 24. H.OhshimaBiophysical Chemistry of BiointerfacesWiley, 2010
  25. 25. C. R.CantorP. R.SchimmelBiophysical Chemistry, W.H. Freeman and Company, San Francisco, 1980
  26. 26. S. R.RafikovV. P.BudtovY. B.MonakovIntroduction in physico-chemistry of polymer solutions, Nauka, Moscow, 1978
  27. 27. B. E.EskinLight Scattering by Polymer Solutions and Macromolecule Properties, Nauka, Leningrad, 1986
  28. 28. B. E.EskinScattering of Light by Polymer Solutions, Nauka, Moscow, 1973
  29. 29. M.YalpaniPolysaccharides, Elsevier, New York, 1988
  30. 30. M.RinaudoInJ. F.KennedyG. O.PhillipsP. O.WilliamsL.Piculell (eds), Cellulose and cellulose derivates: physicochemical aspects and industrial applications, Woodhead Publishing Limited, Cambrige, U.K., 1995
  31. 31. P. N.LavrenkoO. V.OkatovaV. N.TsvetkovH.DautzenbergB.PhilippPolymer 3119901990348352
  32. 32. R. M.DavisMacromolecules 241991199111491155
  33. 33. T.OdijkBiopolymers 181979197931113113
  34. 34. A.KatchalskyS.LifsonJ.PolymSci. 13195419544355
  35. 35. A. M.ZhivkovJ. Colloid Interface Sci. 11320072007122127
  36. 36. S. S.DukhinV.N. Shilov Dielectric Phenomena and Double Layer in Disperse Systems and Polyelectrolytes, Wiley, New York, 1974
  37. 37. D.PorschkeM.AntosiewiczInS. P.Stoylovand M. V.Stoimenova (eds.), Molecular and Colloid Electro-optics, Taylor & Francis, New York, 2007
  38. 38. G.SchwarzJ.PhysChem. 661962196226362641
  39. 39. M.MandelA.JenardTransactions Faraday Soc. 591963196321583169
  40. 40. M.MandelMol. Phys. 419611961489496
  41. 41. F.OosawaBiopolymers 919701970677688
  42. 42. A.MinakataN.ImaiF.OosawaBiopolymers 1119721972347354
  43. 43. A.WarashinaA.MinakataJ.ChemPhys. 581973197347434749
  44. 44. M.MandelInS.Krause (Ed.) Molecular Electro-Optics, Plenum Press, New York, 1981
  45. 45. A.MinakataH.TakahashiT.NishioJ.NagayaA.TaniokaColloids & Surfaces A:20920022002213218
  46. 46. A.MinakataT.NishioM.KimuraS. -I.YanoY.TanakaT.ShimizuColloids & Surfaces B: Biointerfaces 5620072007277280
  47. 47. L. -G.AllgenS.RoswallJ.PolymerSci. 1219541954229236
  48. 48. A.OgaA.TakimotoR.HayakawaY.WadaRept. Progr. Polymer Phys. Japan, 24 (1981
  49. 49. M.MandelAnn. New York Acad. Sci. 303197719777487
  50. 50. ThVreugdenhil, F. van der Touw, M. Mandel, Biophys. Chem. 10197919796780
  51. 51. FredericqE.HoussierC.Electric Dichroism and Electric Birefringence, Clarendon press, Oxford, 1973
  52. 52. A. R.FowerakerB. R.JenningsPolymer 1619751975720724
  53. 53. T.YamamotoY.MoriN.OokuboR.HayakawaY.WadaColloid & Polymer Sci. 260198219822026
  54. 54. A. M.ZhivkovR. P.HristovJ.PhysicsCondensed Matter 22 (2010pp).
  55. 55. J.GregoryS.BaranyAdvances Colloid. Interface Sci., 16920112011112
  56. 56. F.BordiS.SennatoD.TruzzolilloJ.PhysCondens. Matter 21 (2009pp.).
  57. 57. S. P.StoylovColloid Electro-optics- Theory, Techniques and Applications, Acad. Press, London, 1991
  58. 58. H.C. van de Hulst, Light Scattering by Small Particles, John Wiley, New York, 1957.
  59. 59. A. A.SpartakovA. A.TrusovA. V.VoitylovV. V.VojtylovInS. P.Stoylovand M. V.Stoimenova (eds.), Molecular and Colloid Electro-optics, Taylor & Francis, New York, 2007
  60. 60. A. M.ZhivkovInS. P.Stoylovand M. V.Stoimenova (eds.), Molecular and Colloid Electro-optics, Taylor & Francis, New York, 2007
  61. 61. M. C.StuartR.De VriesH.LyklemaPolyelectrolytes, in: Lyclema H. (Ed.), Fundamentals of interface and colloid science, vol. V, Elsevier, London, 2005
  62. 62. TsRadeva, K. Kamburova, J. Colloid Interface Sci. 29320062006290295
  63. 63. V. N.ShilovYuB.BorkovskajaS. N.Budankova, in: S.P. Stoylov, M. Stoimenova (eds.), Molecular and Colloid Electro-optics, Taylor & Francis, New York, 2007
  64. 64. N.OocuboY.HiraiK.ItoR.HayakawaMacromolecules 221989198913591366
  65. 65. G. J.FleerM. A.Cohen-stuartJ. M. H. M.ScheutjensT.CosgoveB.VincentPolymers at interfaces, London, Chapman & Hall, 1993

Written By

Alexandar Metodiev Zhivkov

Published: August 28th, 2013