# Rheological Properties of Hydrophobically Associative Copolymers Prepared in a Mixed Micellar Method Based on Methacryloxyethyl-dimethyl Cetyl Ammonium Chloride as Surfmer

Authors: Rui Liu; WanFen Pu; Hu Jia; XiaoPei Shang; Yue Pan; ZhaoPeng Yan
Journal: International Journal of Polymer Science
 (2014)

---

## Abstract

A novel cationic surfmer, methacryloxyethyl-dimethyl cetyl ammonium chloride (DMDCC), is synthesized. The micellar properties, including critical micelle concentration and aggregation number, of DMDCC-SDS mixed micelle system are studied using conductivity measurement and a steady-state fluorescence technique. A series of water-soluble associative copolymers with acrylamide and DMDCC are prepared using the mixed micellar polymerization. Compared to conventional micellar polymerization, this new method could not only reasonably adjust the length of the hydrophobic microblock, that is,N
H, but also sharply reduce the amount of surfactant. Their rheological properties related to hydrophobic microblock and stickers are studied by the combination of steady flow and linear viscoelasticity experiments. The results indicate that both the hydrophobic content and, especially the length of the hydrophobic microblock are the dominating factors effecting the intermolecular hydrophobic association. The presence of salt influences the dynamics of copolymers, resulting in the variation of solution characters. Viscosity measurement indicates that mixed micelles between the copolymer chain and SDS molecules serving as junction bridges for transitional network remarkably enhance the viscosity. Moreover, the microscopic structures of copolymers at different experimental conditions are conducted by ESEM. This method gives us an insight into the preparation of hydrophobically associative water-soluble copolymers by cationic surfmer-anionic surfactant mixed micellar polymerization with good performance.


---

## Body

## 1. Introduction

The incorporation of a few hydrophobic units into a hydrophilic backbone results in hydrophobically associative water-soluble polymers. In aqueous solution, above a certain polymer concentration, the hydrophobic moieties associate and build a transitory three-dimensional cross-links, leading to unique rheological properties such as dramatic viscosity enhancement [1, 2], gelation [3], time-dependent effects [4], and marked elasticity [5, 6]. Such salient features result from the reversible association processes of the physical networks occurring under shear compared to that of polymers without associative groups. These polymers have triggered great attention in various applications, including petrochemicals, cosmetics, and pharmaceuticals [7–9].There have been substantial efforts with regard to the synthesis and properties of hydrophobically modified water-soluble polyacrylamides. Following Strauss et al. [10, 11] in the 1960s who developed the original hydrophobically modified water-soluble polymers called polysoaps by using n-dodecyl bromide and decyl vinyl ether as hydrophobic monomers, McCormick et al. [12], Morishima et al. [13], and Winnik et al. [14] launched an extensive research on such polymers from photophysical and rheological viewpoints. Notably, one of the most classical and well-studied methods to copolymerize acrylamide (AM) with a hydrophobic comonomer is a free radical micellar copolymerization technique [1]. However, the addition of well amount surfactant (above the critical micelle concentration, CMC) caused some negative influences, such as low-molecular weight caused by the chain transfer effects of surfactants [5], impurity within the surfactant, and the complicated treatment to remove the surfactants to obtain pure products [15]. An additional problem originates from the difficulty to prepare copolymers with both high associativity and good water compatibility because the microblocky hydrophobe of the copolymers is very limited to maintain solubility in water [16].To overcome these drawbacks, the conventional micellar copolymerization method is modified by using polymerizable surfactants, that is, surfmers, to substitute the traditional ones. Surfmers are a family of unique surfactants which not only have amphiphilic structures, that is, cationic or anionic long-chain alkyl structure, but also contain polymerizable vinyl double bonds [17–19]. Surfmer molecules form micelles at concentration above the CMC. Both micellar aggregation (N
agg) and CMC of such micellar systems could be mediated by adding either cosurfactants, such as electrolytes and medium chain-length alcohols, or surfactants [20–23]. Therefore, the hydrophobic microblock length, that is, N
H, of the copolymers chains was controlled. Mixing behavior of surfmer and cosurfactant has been widely investigated [24, 25]. On the other hand, due to an amazing interaction between the surfactants that are mixed, mixed micelles composed of binary surfactants have received increasing attention. Properties of binary mixed micelles upon hydrocarbon-hydrocarbon, hydrocarbon-fluorocarbon surfactants including nonionic-nonionic, anionic-nonionic, anionic-cationic, and zwitterionic-anionic mixtures were extensively investigated by advanced analytical techniques such as light scattering, small angle neutron scattering, and fluorescence probing measurement [26, 27]. Based on these experiments, a regular solution theory that accounts well for the characters of binary mixed micelles has been established in which the CMC values and N
agg values involved in different compositional mixtures depended on an interaction parameter (β) [22]. Apparently, the regular solution theory is also applied well in the surfactant-surfmer mixed micelle system. Chang and McCormick [28] firstly suggested that the microblock length of the cationic polymerizable surfactant dimethyl-dodecyl (2-acrylamidoethyl) ammonium bromide could be controlled by addition of cetyltrimethyl-ammonium bromide (CTAB) as a cationic cosurfactant. Direct experimental evidence of this behavior is reported by Zhang and Wu [23] from conductivity and fluorescence studies on the same mixed micelle system. Stähler et al. [29] found that cationic fluorocarbon-hydrocarbon surfmer pairs that bear the same hydrophobic compound may have the partial compatibility in single type of mixed micelles despite the repulsive headgroup interactions.It is thought that only the surfmer-surfactant mixed micellar system corresponds to the same charge, either positive or negative, the microblock of length could be adjusted. Can the cationic surfmer-anionic surfactant binary system share the same capacity in the preparation of hydrophobically associative polyacrylamide with good performance? This paper just addressed this issue. Firstly, a long-chain alkyl cationic surfmer of methacryloxy-ethyl-dimethyl cetyl ammonium chloride (DMDCC) was synthesized, and the properties of DMDCC-SDS (sodium dodecyl sulfate) mixed micelles are determined by conductivity measurement and a steady-state fluorescence technique. We discuss the synthesis and characterization of cationic associating copolymers prepared by DMDCC-SDS mixed micellar copolymerization with DMDCC as cationic hydrophobic comonomer. Particularly, we focus on the effect of the length and number of the hydrophobic microstructures on the rheological properties. In addition, we look at the effect of salt and surfactant on the apparent viscosity of copolymers.


## 2. Experimental Section

### 2.1. Materials

Acrylamide (Chengdu KeLong Chemical Reagent Co., Ltd.) was recrystallized twice from acetone and vacuum dried at room temperature prior to use. The azo-initiator V-50 (2,2′-azobis(2-amidinopropane)dihydrochloride) (UA, Alfa Aesar 99%) was used without further purification. N,N-Dimethyl-ethylamine methacrylate and cetyl chloride, purchased from Aldrich chemicals (purity, 99%), were used as received. Water was double deionized with a Millipore Milli-Q system. Other reagents were analytically pure and used as received.


### 2.2. Synthesis of Cationic Polymerizable Surfactant (DMDCC)

Scheme1 illustrates the synthesis of the cationic surfmer, methacryloxyethyl-dimethyl cetyl ammonium chloride (DMDCC). N,N-Dimethylethylamine methacrylate (28.2 g, 0.2 mol) was added into a 250 mL three-necked round-bottom flask and placed in an oil bath and agitated by a magnetic stirrer under a nitrogen atmosphere. Cetyl chloride (46.9 g, 0.180 mol) was subsequently added to the additional funnel. When the temperature increased to 85°C, cetyl chloride was added to the flask dropwise over a period of 6 h. After 42 h, the yellow viscous gel was obtained. The excess crude product was dissolved in a small amount of acetone at 45°C and cooled to −10°C and the yellow semisolid product was obtained. Further purification of the product was accomplished by recrystallization from a 1 : 1 (wt/wt) mixture of acetone and ether, yield of 61.8 g (85%).Scheme 1
Synthesis of the cationic surfmer (DMDCC).


### 2.3. Properties of DMDCC-SDS Binary Surfactant System

#### 2.3.1. CMC Values

CMC values of DMDCC and mixture of DMDCC-SDS were determined by conductivity on a digit conductivity meter. The conductivity,κ, of aqueous surfactant solutions was measured against the surfactant molar concentration at 50°C. The difference in the magnitude of the gradients above or below the inflection points in each sample results in a concomitant increase in the uncertainty of the CMC values. Thus, the CMC values of DMDCC and DMDCC-SDS were measured from the break points of the κ to c plots.


#### 2.3.2. Aggregation Number

Using pyrene as a probe, the aggregation numbers (N
agg) of DMDCC as well as mixture of DMDCC-SDS surfactants at different bulk mole fractions α
1 were determined by a steady-state fluorescence technique. Samples solutions with 0.1 mM of pyrene were prepared by adding a small amount of concentrated pyrene dissolved in acetone. All the samples were heated at 50°C for 12 h and then filtered with a 0.2 μm membrane filter before measurement. The quenching of pyrene monomer fluorescence, originating from excimer formation, was used to determine N
agg. Fluorescence decay data corresponded to the following equation:
(1)
ln
⁡
(
I
0
I
)
=
N
[
Q
]
(
C
t
-
CMC
)
,
where I
0 and I are the fluorescence intensities in the absence and presence of quencher of the pure/binary surfactant systems. [
Q
], C
t, and CMC are the quencher concentration, total surfactant concentration, and critical micelle concentration, respectively. The ln
⁡
(
I
0
/
I
) to [
Q
] at different compositions is pseudo-first-order. Therefore, values of Nagg were calculated from the slope of the pseudolinear fits. In each case the total surfactant concentration was constant.


### 2.4. Synthesis of the Copolymers

A 250 mL three-necked round-bottom flask is equipped with a mechanical stirrer, nitrogen inlet, and a thermometer. Acrylamide (AM) and methacryloxyethyl-dimethyl cetyl ammonium chloride (DMDCC) and sodium dodecyl sulfate (SDS) in the desired ratio are dissolved in 100 mL of deionized water and then placed in the flask. The total concentration of the monomers is kept constant at 1.0 M. The flask is purged with a small N2 stream for half an hour prior to being heated to 50°C. Polymerization is then initiated by addition of 0.35 mL of V-50 (1 wt% preferentially dissolved in the deionized water) via a pipette scaled to 1 mL under slow stirring. In this case, instead of potassim persulfate, v-50 was used as initiator to avoid the redox side reaction between mercaptan and persulfate. Polymerization is conducted continuously for 8 h at 50°C. The reaction mixture is diluted with five volumes of distilled water, and two volumes of acetone are then added with stirring to precipitate the polymers. The precipitated polymers are further washed twice with acetone and extracted with ethanol to remove all traces of water, surfactant, residual monomers, and initiator. The polymers are recovered by freeze-drying after vacuum-drying at 50°C for three days. For reference, PAM is prepared under identical experimental conditions and purification method mentioned above.


### 2.5. Characterization

#### 2.5.1. Spectroscopic Measurement

IR was carried out using Shimadzu-1800S spectrometer on KBr pellets in the range of 4000–400 cm−1. The peak intensities are characterized as follows: vs = very strong, s = strong, w = weak, ν corresponds to stretching elongation, and δ corresponds to bending elongation. 1H NMR spectra were measured with a Bruker AVanceII-400NMR spectrometer using D2O as a solvent at room temperature. Chemical shifts were determined by using TMS as an internal standard. The peaks multiplicities are characterized as follows: s = singlet, d = doublet, t = triplet, q = quartet, and m = multiplet.


#### 2.5.2. Molecular Weights

The intrinsic viscosities [η] of the polymers were determined by an automatic capillary viscometer (Ubbelohde type) in 0.1 M NaCl aqueous solution at room temperature. The molecular weight of each polymer sample was determined in water/methanol mixture (3/7 v
/
v) containing 0.1 M NaCl by classical light scattering using a multiangle spectrometer (AMTEC model MM1) at 633 nm. The refractive index increment (d
n
/
d
c) was measured at the same wavelength on a differential refractometer. The d
n
/
d
c value for PAM sample was equal to 0.16 mL g−1 [2].


#### 2.5.3. Rheological Measurements

Polymer solutions were prepared by dissolution of a known amount of the polymer powder in water and NaCl solution. The apparent viscosity of samples solution at low concentrations was determined by a Brookfield DV-III rheometer equipped with different sizes of spindles (different diameter depending on solution viscosity) at 25°C. Rheological experiments were carried out with a RS100 controlled-stress rheometer equipped with a cone plate geometry (angle 1°, diameter 35 mm). We measured flow curves by increasing the shear stress in regular steps and waiting at each step until equilibrium was attained. The shear rateγ
˙ ranged from 0.1–10 to 1000 s−1 according to the viscosity behavior of samples. To overcome the problem that a slight increase in stress caused a large jump in shear rate, we used controlled-rate mode of the rheometer which permits us to scan the whole shear rate range without large gaps. In all cases, we checked that the curves measured in controlled-stress and controlled-rate mode were well superposed. Dynamic measurements were conducted under strains and at frequencies of 0.01–100 Hz to lead to a linear response. All the experiments were conducted with a solvent trap to avoid any evaporation.


#### 2.5.4. Morphology

The microstructure of polymers in both aqueous and salt solutions was observed by environment scanning electron microscope (ESEM XL 30). The sample solutions were maintained at −3.5°C and the pressure was controlled below 5 Torr to keep samples solution state during the whole observation.


#### 2.5.5. Fluorescence

Fluorescence spectra were measured on a Lengguang 970CRT fluorescence spectrometer. All measurements were conducted at ambient temperature. The slit width of excitation and emission was kept at 5 nm during experiments. The excitation wavelength (λ) was set at 339 nm. The ration of the intensities of the third I
3 (385 nm) to first I
1 (375 nm) vibronic peak of fluorescence spectrum of pyrene probe was used as an estimate of micropolarity of pyrene microenvironment.


## 2.1. Materials

Acrylamide (Chengdu KeLong Chemical Reagent Co., Ltd.) was recrystallized twice from acetone and vacuum dried at room temperature prior to use. The azo-initiator V-50 (2,2′-azobis(2-amidinopropane)dihydrochloride) (UA, Alfa Aesar 99%) was used without further purification. N,N-Dimethyl-ethylamine methacrylate and cetyl chloride, purchased from Aldrich chemicals (purity, 99%), were used as received. Water was double deionized with a Millipore Milli-Q system. Other reagents were analytically pure and used as received.


## 2.2. Synthesis of Cationic Polymerizable Surfactant (DMDCC)

Scheme1 illustrates the synthesis of the cationic surfmer, methacryloxyethyl-dimethyl cetyl ammonium chloride (DMDCC). N,N-Dimethylethylamine methacrylate (28.2 g, 0.2 mol) was added into a 250 mL three-necked round-bottom flask and placed in an oil bath and agitated by a magnetic stirrer under a nitrogen atmosphere. Cetyl chloride (46.9 g, 0.180 mol) was subsequently added to the additional funnel. When the temperature increased to 85°C, cetyl chloride was added to the flask dropwise over a period of 6 h. After 42 h, the yellow viscous gel was obtained. The excess crude product was dissolved in a small amount of acetone at 45°C and cooled to −10°C and the yellow semisolid product was obtained. Further purification of the product was accomplished by recrystallization from a 1 : 1 (wt/wt) mixture of acetone and ether, yield of 61.8 g (85%).Scheme 1
Synthesis of the cationic surfmer (DMDCC).


## 2.3. Properties of DMDCC-SDS Binary Surfactant System

### 2.3.1. CMC Values

CMC values of DMDCC and mixture of DMDCC-SDS were determined by conductivity on a digit conductivity meter. The conductivity,κ, of aqueous surfactant solutions was measured against the surfactant molar concentration at 50°C. The difference in the magnitude of the gradients above or below the inflection points in each sample results in a concomitant increase in the uncertainty of the CMC values. Thus, the CMC values of DMDCC and DMDCC-SDS were measured from the break points of the κ to c plots.


### 2.3.2. Aggregation Number

Using pyrene as a probe, the aggregation numbers (N
agg) of DMDCC as well as mixture of DMDCC-SDS surfactants at different bulk mole fractions α
1 were determined by a steady-state fluorescence technique. Samples solutions with 0.1 mM of pyrene were prepared by adding a small amount of concentrated pyrene dissolved in acetone. All the samples were heated at 50°C for 12 h and then filtered with a 0.2 μm membrane filter before measurement. The quenching of pyrene monomer fluorescence, originating from excimer formation, was used to determine N
agg. Fluorescence decay data corresponded to the following equation:
(1)
ln
⁡
(
I
0
I
)
=
N
[
Q
]
(
C
t
-
CMC
)
,
where I
0 and I are the fluorescence intensities in the absence and presence of quencher of the pure/binary surfactant systems. [
Q
], C
t, and CMC are the quencher concentration, total surfactant concentration, and critical micelle concentration, respectively. The ln
⁡
(
I
0
/
I
) to [
Q
] at different compositions is pseudo-first-order. Therefore, values of Nagg were calculated from the slope of the pseudolinear fits. In each case the total surfactant concentration was constant.


## 2.3.1. CMC Values

CMC values of DMDCC and mixture of DMDCC-SDS were determined by conductivity on a digit conductivity meter. The conductivity,κ, of aqueous surfactant solutions was measured against the surfactant molar concentration at 50°C. The difference in the magnitude of the gradients above or below the inflection points in each sample results in a concomitant increase in the uncertainty of the CMC values. Thus, the CMC values of DMDCC and DMDCC-SDS were measured from the break points of the κ to c plots.


## 2.3.2. Aggregation Number

Using pyrene as a probe, the aggregation numbers (N
agg) of DMDCC as well as mixture of DMDCC-SDS surfactants at different bulk mole fractions α
1 were determined by a steady-state fluorescence technique. Samples solutions with 0.1 mM of pyrene were prepared by adding a small amount of concentrated pyrene dissolved in acetone. All the samples were heated at 50°C for 12 h and then filtered with a 0.2 μm membrane filter before measurement. The quenching of pyrene monomer fluorescence, originating from excimer formation, was used to determine N
agg. Fluorescence decay data corresponded to the following equation:
(1)
ln
⁡
(
I
0
I
)
=
N
[
Q
]
(
C
t
-
CMC
)
,
where I
0 and I are the fluorescence intensities in the absence and presence of quencher of the pure/binary surfactant systems. [
Q
], C
t, and CMC are the quencher concentration, total surfactant concentration, and critical micelle concentration, respectively. The ln
⁡
(
I
0
/
I
) to [
Q
] at different compositions is pseudo-first-order. Therefore, values of Nagg were calculated from the slope of the pseudolinear fits. In each case the total surfactant concentration was constant.


## 2.4. Synthesis of the Copolymers

A 250 mL three-necked round-bottom flask is equipped with a mechanical stirrer, nitrogen inlet, and a thermometer. Acrylamide (AM) and methacryloxyethyl-dimethyl cetyl ammonium chloride (DMDCC) and sodium dodecyl sulfate (SDS) in the desired ratio are dissolved in 100 mL of deionized water and then placed in the flask. The total concentration of the monomers is kept constant at 1.0 M. The flask is purged with a small N2 stream for half an hour prior to being heated to 50°C. Polymerization is then initiated by addition of 0.35 mL of V-50 (1 wt% preferentially dissolved in the deionized water) via a pipette scaled to 1 mL under slow stirring. In this case, instead of potassim persulfate, v-50 was used as initiator to avoid the redox side reaction between mercaptan and persulfate. Polymerization is conducted continuously for 8 h at 50°C. The reaction mixture is diluted with five volumes of distilled water, and two volumes of acetone are then added with stirring to precipitate the polymers. The precipitated polymers are further washed twice with acetone and extracted with ethanol to remove all traces of water, surfactant, residual monomers, and initiator. The polymers are recovered by freeze-drying after vacuum-drying at 50°C for three days. For reference, PAM is prepared under identical experimental conditions and purification method mentioned above.


## 2.5. Characterization

### 2.5.1. Spectroscopic Measurement

IR was carried out using Shimadzu-1800S spectrometer on KBr pellets in the range of 4000–400 cm−1. The peak intensities are characterized as follows: vs = very strong, s = strong, w = weak, ν corresponds to stretching elongation, and δ corresponds to bending elongation. 1H NMR spectra were measured with a Bruker AVanceII-400NMR spectrometer using D2O as a solvent at room temperature. Chemical shifts were determined by using TMS as an internal standard. The peaks multiplicities are characterized as follows: s = singlet, d = doublet, t = triplet, q = quartet, and m = multiplet.


### 2.5.2. Molecular Weights

The intrinsic viscosities [η] of the polymers were determined by an automatic capillary viscometer (Ubbelohde type) in 0.1 M NaCl aqueous solution at room temperature. The molecular weight of each polymer sample was determined in water/methanol mixture (3/7 v
/
v) containing 0.1 M NaCl by classical light scattering using a multiangle spectrometer (AMTEC model MM1) at 633 nm. The refractive index increment (d
n
/
d
c) was measured at the same wavelength on a differential refractometer. The d
n
/
d
c value for PAM sample was equal to 0.16 mL g−1 [2].


### 2.5.3. Rheological Measurements

Polymer solutions were prepared by dissolution of a known amount of the polymer powder in water and NaCl solution. The apparent viscosity of samples solution at low concentrations was determined by a Brookfield DV-III rheometer equipped with different sizes of spindles (different diameter depending on solution viscosity) at 25°C. Rheological experiments were carried out with a RS100 controlled-stress rheometer equipped with a cone plate geometry (angle 1°, diameter 35 mm). We measured flow curves by increasing the shear stress in regular steps and waiting at each step until equilibrium was attained. The shear rateγ
˙ ranged from 0.1–10 to 1000 s−1 according to the viscosity behavior of samples. To overcome the problem that a slight increase in stress caused a large jump in shear rate, we used controlled-rate mode of the rheometer which permits us to scan the whole shear rate range without large gaps. In all cases, we checked that the curves measured in controlled-stress and controlled-rate mode were well superposed. Dynamic measurements were conducted under strains and at frequencies of 0.01–100 Hz to lead to a linear response. All the experiments were conducted with a solvent trap to avoid any evaporation.


### 2.5.4. Morphology

The microstructure of polymers in both aqueous and salt solutions was observed by environment scanning electron microscope (ESEM XL 30). The sample solutions were maintained at −3.5°C and the pressure was controlled below 5 Torr to keep samples solution state during the whole observation.


### 2.5.5. Fluorescence

Fluorescence spectra were measured on a Lengguang 970CRT fluorescence spectrometer. All measurements were conducted at ambient temperature. The slit width of excitation and emission was kept at 5 nm during experiments. The excitation wavelength (λ) was set at 339 nm. The ration of the intensities of the third I
3 (385 nm) to first I
1 (375 nm) vibronic peak of fluorescence spectrum of pyrene probe was used as an estimate of micropolarity of pyrene microenvironment.


## 2.5.1. Spectroscopic Measurement

IR was carried out using Shimadzu-1800S spectrometer on KBr pellets in the range of 4000–400 cm−1. The peak intensities are characterized as follows: vs = very strong, s = strong, w = weak, ν corresponds to stretching elongation, and δ corresponds to bending elongation. 1H NMR spectra were measured with a Bruker AVanceII-400NMR spectrometer using D2O as a solvent at room temperature. Chemical shifts were determined by using TMS as an internal standard. The peaks multiplicities are characterized as follows: s = singlet, d = doublet, t = triplet, q = quartet, and m = multiplet.


## 2.5.2. Molecular Weights

The intrinsic viscosities [η] of the polymers were determined by an automatic capillary viscometer (Ubbelohde type) in 0.1 M NaCl aqueous solution at room temperature. The molecular weight of each polymer sample was determined in water/methanol mixture (3/7 v
/
v) containing 0.1 M NaCl by classical light scattering using a multiangle spectrometer (AMTEC model MM1) at 633 nm. The refractive index increment (d
n
/
d
c) was measured at the same wavelength on a differential refractometer. The d
n
/
d
c value for PAM sample was equal to 0.16 mL g−1 [2].


## 2.5.3. Rheological Measurements

Polymer solutions were prepared by dissolution of a known amount of the polymer powder in water and NaCl solution. The apparent viscosity of samples solution at low concentrations was determined by a Brookfield DV-III rheometer equipped with different sizes of spindles (different diameter depending on solution viscosity) at 25°C. Rheological experiments were carried out with a RS100 controlled-stress rheometer equipped with a cone plate geometry (angle 1°, diameter 35 mm). We measured flow curves by increasing the shear stress in regular steps and waiting at each step until equilibrium was attained. The shear rateγ
˙ ranged from 0.1–10 to 1000 s−1 according to the viscosity behavior of samples. To overcome the problem that a slight increase in stress caused a large jump in shear rate, we used controlled-rate mode of the rheometer which permits us to scan the whole shear rate range without large gaps. In all cases, we checked that the curves measured in controlled-stress and controlled-rate mode were well superposed. Dynamic measurements were conducted under strains and at frequencies of 0.01–100 Hz to lead to a linear response. All the experiments were conducted with a solvent trap to avoid any evaporation.


## 2.5.4. Morphology

The microstructure of polymers in both aqueous and salt solutions was observed by environment scanning electron microscope (ESEM XL 30). The sample solutions were maintained at −3.5°C and the pressure was controlled below 5 Torr to keep samples solution state during the whole observation.


## 2.5.5. Fluorescence

Fluorescence spectra were measured on a Lengguang 970CRT fluorescence spectrometer. All measurements were conducted at ambient temperature. The slit width of excitation and emission was kept at 5 nm during experiments. The excitation wavelength (λ) was set at 339 nm. The ration of the intensities of the third I
3 (385 nm) to first I
1 (375 nm) vibronic peak of fluorescence spectrum of pyrene probe was used as an estimate of micropolarity of pyrene microenvironment.


## 3. Result and Discussion

### 3.1. Characterization of DMDCC-SDS Mixed Micelles

SDS was chosen to study the micellar behavior of DMDCC-SDS binary mixed system, because it bears the same hydrophobic long chain as DMDCC and the most common surfactant used in radical micellar copolymerization, and, most importantly, mixture of cationic (DMDCC) and anionic (SDS) surfactants has a net interaction (β
<
0). In the case of binary mixed micelles composed of cationic-anionic pairs, the CMC of the surfactant mixture can be calculated as follows:
(2)
1
CMC
m
=
α
1
f
1
m
CM
C
1
+
α
2
f
2
m
CM
C
2
,
where CMC
m is the critical micelle concentration of binary mixed surfactants, the subscripts 1, 2 represent DMDCC and SDS, respectively. CM
C
1, CM
C
2 are the critical micelle concentration of single surfactant species, α
1 and α
2 are the bulk mole fractions of the respective surfactants in the system, and f
1
m, f
2
m are the activity coefficients that can be found by using the regular solution theory,
(3)
ln
⁡
f
1
m
=
(
α
2
m
)
2
β
,
ln
⁡
f
2
m
=
(
α
1
m
)
2
β
,
where β is an interaction parameter, quantifying the net interaction between the surfactant species in the mixed micelle. α
1
m and α
2
m are the mole fractions of the single surfactant in mixed system which are written as follows:
(4)
α
1
m
=
α
1
f
2
m
CM
C
2
α
1
f
2
m
CM
C
2
+
α
2
f
1
m
CM
C
1
,
α
2
m
=
1
-
α
1
m
.Figure1 shows the CM
C
m of DMDCC-SDS binary mixed system as a function of DMDCC mole fraction in solution. We can see that the CMC values of single SDS and DMDCC in aqueous solution are 8 mM, 0.82 mM, respectively. For the DMDCC-SDS mixed system, the CMC values of anionic surfactant SDS significantly decrease by adding a small amount of DMDCC without causing any precipitation. Interestingly, the CMC values of the binary surfactant remain almost constant with the increase in DMDCC molar fraction in aqueous solution.Figure 1
Variation of critical micelle concentration of DMDCC-SDS binary mixture system as a function of DMDCC mole fraction (T
=
50°C).The CMC of mixed surfactants strongly depends on parameter valuesβ. Positive β values imply a net repulsive force between the surfactant components, whereas negative β values imply a net attractive force. The more negative β values are, the stronger the net interaction between the surfactants in the mixed system will become; thus the CMC of mixed surfactants is much lower. For reference, the CMC of DTAB-SDS mixed system as the function of CTAB mole fraction is depicted in Figure 2. The strong synergetic effect (β
=
-
13.2) indicated that there was a large net attraction between the surfactants.Figure 2
Variation of critical micelle concentration of DTAB-SDS binary mixture system as a function of DTAB mole fraction [22], reproduced from [22], with permission from John Wiley & Sons.The much lower CMC values of SDS are obtained by adding cationic surfactant DTAB. We note that DMDCC bears almost the same structure as DTAB. Therefore, we can draw a conclusion that the CMC behavior of DMDCC-SDS mixed system, as shown in Figure3, has the same dynamic character as that of DTAB-SDS. However, the aggregation morphology of DMDCC-SDS mixed system as the mole fraction of DMDCC has unique dynamic character, which is shown in Figure 1. The N
agg value of anionic surfactant SDS significantly increases by adding a small amount of DMDCC and then remains almost constant with the increase in DMDCC molar fraction in aqueous solution, which could be written as follows:
(5)
N
agg
m
=
α
1
m
N
agg
1
+
α
2
m
N
agg
2
,
where N
agg
1 and N
agg
2 are the respective aggregation number values of DMDCC and SDS in aqueous solution. The length of hydrophobic microblock in hydrophobically modified polyacrylamide prepared by conventional radical micelle copolymerization is determined by
(6)
N
H
=
[
H
]
N
agg
[
S
]
-
CMC
,
where [H], [S], and CMC are the mole concentration of the hydrophobic monomer, the mole concentration of surfactant, and critical concentration of surfactant, whereas the length of hydrophobic microblock from mixed micelle copolymerization should be rewritten as
(7)
N
H
=
(
[
H
]
-
CM
C
H
)
N
agg
m
[
H
+
S
]
-
CM
C
(
H
+
S
)
.Figure 3
Schematic representation of the mixed DMDCC-SDS micelles compared to pure DMDCC micelles and pure SDS micelles.In the DMDCC/SDS mixed system,CM
C
H is the CMC of surfmer and CM
C
H
+
S is the critical micelle concentration of DMDCC-SDS binary mixed micelles and N
agg
m which is determined by steady-state fluorescence quenching technique. Therefore, the length of microblock could be tuned reasonably by the mixed micelle technique.


### 3.2. Synthesis and Characterization

The copolymers poly(AM/DMDCC) with low amounts of cationic hydrophobe were obtained in water using a DMDCC-SDS binary mixed micellar polymerization (Scheme2). The characteristic of the copolymer is depicted in Table 1. For DMDCC, IR (KBr, ν/cm−1): 3432 (s, ν(C=O)), 2919 (vs, ν
as(C–H)), 2844 (s, ν
s(C–H)), 1633 (w, ν(C=C)), 1299 (s, ν(C–N)), 1167 (vs, ν(C–C)) 1028 (w, ν(C–O)). For copolymer 0.75DM12.8, IR (KBr, ν/cm−1): 3450 (vs, ν
s(NH2), ν(C=O)), 2925 (w, ν(C–H)), 1025 (w, ν(C–O)), 628 (s, δ(C–H)). 1H NMR (400 MHz, D2O, δ/ppm): 1.11 (q, 2Hg; CH2), 1.58 (d, 2Ha; CH2), 2.16 (d, 1Hb, CH), 2.36 (t, 3Hc, CH3), 2.48 (s, 3Hf, CH3), 3.59 (m, 2He, CH2), 3.72 (q, 2Hd, CH2) (Figures 4 and 5).Table 1
Structural parameters of the copolymers.
Samplea
Polymer composition mol %
N
H
b
Polymer characterization
AM
DMDCC
SDS
S
c
10
-
6
×
M
w g mol−1
[η]mL g−1
[
η
]
calc
d mL g−1
Solubility in watere
PAM
100
0
0
0
0
3.50
610
755
+
+
0.5DM4.5
99.5
0.5
1.75
4.5
25
3.15
586
697
+
+
0.5DM9.3
0.8
9.3
12.4
3.29
540
720
+
0.5DM12.7
0.5
12.7
9
3.25
520
714
+
0.5DM92
0
92
0.6
1.64
299
428
±
0.75DM4.6
99.25
0.75
5.5
4.6
25
2.22
335
536
+
+
0.75DM9.3
2.1
9.3
17
3.06
470
683
+
0.75DM12.8
1.35
12.8
13
3.35
418
730
+
0.75DM92
0
92
0
/
/
/
−
aThe first number indicated the mole frication of hydrophobic monomer, and the final number indicated the rounded value of N
H (e.g., 0.5DM5 stands for a polymer that contains 0.5 mol % of DMDCC with N
H
≈
4.5). bNumber of hydrophobes per micelle ≈ hydrophobic block length. cNumber of hydrophobic blocks per chain (i.e., stickers)30 calculated using the relationship S
=
(
M
W
/
2
m
)
[
H
]
/
N
H, where m is the molecular weight of the monomer unit (acrylamide, m = 71) and M
W
/
2
m corresponds to the number average degree of polymerization,
N. dIntrinsic viscosity calculated using relationship [
η
]
=
9.33
×
1
0
-
3
M
W
0.75 established for PAM31. e++, easily soluble; +, soluble; ±, cloudy solution; −, difficult to dissolve.Scheme 2
Copolymerization of AM and DMDCC.Figure 4
IR spectra of the DMDCC and copolymer 0.75DM12.8.Figure 5
1HNMR spectra of copolymer 0.75DM12.8.


### 3.3. Rheological Behavior

#### 3.3.1. Viscometric Behavior in Dilute Solution

The effect of the hydrophobic microblock length, that is,N
H value, and the concentration of hydrophobic monomer on intra- and intermolecular interaction is depicted in Figure 6. Apparent viscosity is plotted as a function of polymer concentration for three copolymers (0.5DM4.5, 0.5DM9.3, and 0.75DM9.3) and for the corresponding polyacrylamide.Figure 6
Apparent viscosity as a function of polymer concentration for copolymers 0.75DM12.8, 0.5DM12.7, and 0.5DM9.3 samples and for a PAM sample (T
=
25°C, the inlet of apparent viscosity is partially enlarged for purpose of smart understanding).All the samples are well measured at a constant shear rate of 7.34 s−1. In extremely dilute solution regime (c
P < 0.05 g dL−1), the apparent viscosity of copolymers is lower than that of PAM due to intramolecular association which leads to the coil of chain. This effect is enhanced by increasing either the N
H or the hydrophobe concentration. And it is well explained that the [
η
] of all the poly(AM/DMDCC) is reduced compared to that of PAM and inverse to the N
H value. Because the [
η
] of the polymer was determined by automatic capillary viscometer at low polymer concentration, intermolecular interaction was gradually enhanced with the increase in polymer concentration. Above a critical concentration, that is, CAC, an upward curvature in the apparent viscosity can be observed. The apparent viscosity increases more markedly and shows up at lower concentration with increasing the hydrophobic length at the same hydrophobe concentration. The CAC of 0.5DM4.5 and 0.5DM9.3 is 0.15 g dL−1 and 0.13 g dL−1, respectively. On the other hand, 0.75DM9.3 and 0.5DM9.3 have the same hydrophobic microblock length; the increase in hydrophobe also enhances thickening efficiency. This behavior can be explained by the increase in sticker reported in Table 1, which makes the intermolecular interactions much stronger, and the CAC of 0.75DM9.3 is 0.11 g dL−1. The upturn of apparent viscosity in case of the PAM is due to the onset of chain overlap, that is, c
*, and related to the chain size. The viscosity upturn observed for poly(AM/DMDCC) cannot be attributed to a chain overlap since poly(AM/DMDCC) had the similar range of molecular weight. Moreover the chain overlap behavior was long-term effect which occurred at high polymer concentration. Therefore, the remarkable viscosity onset is a result of the formation of hydrophobic microdomain caused by hydrophobic intermolecular interaction. The hydrophobic microblock length directly influences the thickening efficiency. However, when the N
H goes beyond a certain value, negative impact, such as low rate polymer conversion and the poor solubility, would occur, which accorded with the general law of the water-soluble associating polymer prepared by conventional radical micelle copolymerization [4, 16, 30].


#### 3.3.2. Steady Flow Experiments

Apparent viscosity as a function of shear rate is conducted for three copolymers modified by 0.5 mol% DMDCC and for PAM. The viscosity/shear rate curves of the copolymers and PAM at concentration of 1.0 g dL−1 and 2.0 g dL−1 are shown in Figures 7 and 8. It is interesting to figure out that the rheological properties of the copolymers are strongly dependent on N
H and polymer concentration.Figure 7
Variation of apparent viscosity as a function of shear rate for PAM, 0.5DM12.7, and 0.5DM4.5 (c
p
=
1.0 g dL−1, T
=
25°C).Figure 8
Variation of apparent viscosity as a function of shear rate for PAM, 0.5DM12.7, and 0.5DM4.5 (c
p
=
2.0 g dL−1, T
=
25°C).PAM exhibits the classic rheological behavior, that is, a slight shear thinning effect after Newtonian plateau. All the copolymers present the same type of behavior. For poly(AM/DMDCC), at 1.0 g dL−1 concentration, a shear thickening domain reaches first followed by shear thinning. The shear thickening is interpreted in terms of the balance between intra- and intermolecular associations. At a certain shear rate, the shear forces are strong enough to extend the polymer coils and disrupt the intramolecular hydrophobic interactions. The intramolecular hydrophobic microdomain is released and favors forming intermolecular hydrophobic interactions, resulting in an increase in viscosity. Further increasing shear rate, these interactions are gradually broken and shear thinning behavior is observed. This behavior was general agreement with the nonionic hydrophobically modified polyacrylamides [31].To determine the role of theN
H in the apparent viscosity, for all polymers, the values of viscosity (η
0) which corresponded to the shear rate (γ
˙
*) and shear stress (σ
*) on the onset of Newtonian plateau were reported in Table 2. Apparent viscosity increases with the increasing of shear rate; at such shear rate (γ
˙
*), this plateau is attainable as shown in Figures 7 and 8, and beyond which the fluid presents a shear thinning behavior; the values of the stress threshold σ
*
=
γ
˙
*
η
0.Table 2
Rheological values ofσ
*, γ
˙
*, and η
0 for poly(AM/DMDCC) and PAM at concentration of 1.0 g dL−1 and 2.0 g dL−1.
Polymer
c
p = 1.0 g dL−1
c
p = 2.0 g dL−1
σ
* (Pa)
γ
˙
* (s−1)
η
0 (mPa·s)
σ
* (Pa)
γ
˙
* (s−1)
η
0 (mPa·s)
PAM
0.93
10.3
90
3.6
10
357
0.5DM4.5
1.09
1.66
658
8.2
0.56
14650
0.5DM9.3
1.55
1.23
1264
9.78
0.36
27160
0.5DM12.7
2.07
0.76
2723
13.15
0.25
62600In case of PAM, a higherγ
˙
* is presented compared to that of copolymers. With the increase in shear rate, shear force is strong enough to disrupt the gauss coils structured by the macromolecular chains overlap and entanglement, and the original chain orientation is released to form orderly orientation, resulting in a decrease in viscosity. As for copolymers, the length of hydrophobic microblock 4.5 (0.5DM4.5) is enough to induce an increase in the solution viscosity. Lengthening of hydrophobic microblock enhanced the degree of association facilitating shear thickening behavior. At a certain shear rate, the shear forces are strong enough to extend the copolymer coils and disrupt the intramolecular hydrophobic interactions, resulting in the decrease of viscosity.The stress threshold valuesσ
*show that the longer the N
H, the higher the σ
*. This indicates that more stress force is required to disrupt the molecular interactions with increase in the length of hydrophobic microblock, which results in a stronger transitory three-dimensional network. At the identical polymer concentration, the increase in N
H is accompanied by a decrease of γ
˙
*, shortening the Newtonian zone. The solution became more sensitive to shear rate. For example, at a concentration of 1.0 g dL−1, the shear rate γ
˙
* of copolymers 0.5DM12.7 and 0.5DM9.3 is 0.76 s−1 and 1.23 s−1, respectively, compared to 1.66 s−1 of copolymer 0.5DM4.5. Higher viscosity at low shear rate indicates a more pronounced shear thickening domain and a longer shear thinning plateau. At higher shear rate, the copolymer viscosity trends towards that of PAM, but even at 1000 s−1, the value is mainly greater indicating that intermolecular interaction also existed.We should figure out that even at a higher concentration (2.0 g dL−1), shear thickening domain is also observed, and both copolymers show classical shear thickening subsequent shear thinning behavior within the range of shear rate. This owning to the fact that beside molecular weight and polymer concentration the nature of hydrophobic monomer also influences shear thickening efficiency. The apparent viscosity/shear rate curves at the characteristic values at the Newtonian plateau are also given in Table 2. We also observe that increasing the concentration shortens the shear thickening plateau, while the magnitude of the η
0 increases with increasing polymer concentration. The values reported in Table 2 confirmed that, for cationic hydrophobic associative polyacrylamides, concentration, especially, N
H, had great effects on steady flow rheological properties.


#### 3.3.3. Linear Viscoelasticity

Figures9 and 10 present illustration of the oscillatory response for poly(AM/DMDCC) and PAM at 1.0 g dL−1 in aqueous solution. The variations of the storage (G
′) and loss (G
′′) modulus are curved versus frequency (f). The slopes of G
′ and G
′′ in the terminal zone for polyacrylamide are 2.2 and 0.98. Note that the slopes of G
′ and G
′′ will not keep constant, which are dependent on the PAM concentration [4].Figure 9
Storage (G
′) and loss (G
′′) modulus as a function of frequency for copolymers 0.5DM12.7, 0.5DM9.3, and 0.5DM4.5 and for PAM (c
p
=
1.0 g dL−1, T
=
25°C).Figure 10
Storage (G
′) and loss (G
′′) modulus as a function of frequency for copolymers 0.75DM12.8, 0.75DM9.3, and 0.75DM4.6 and for PAM (c
p
=
2.0 g dL−1, T
=
25°C).However, for copolymers modified by hydrophobic groups, at low frequencies, the behavior of the shear modulus is Maxwellian, indicating the variations ofG
′(f) and G
′′(f) that scaled as f
2 and f, respectively. The curves obtained for the different series of copolymers have a profile similar to that for solutions whose viscoelastic properties are governed by chain entanglements. These solutions are characterized at low frequency by a slope of G
′ and G
′′, where the values of G
′ were below that of G
′′. Above the frequency at which curves G
′(f) and G
′′(f) cross each other (G
c), the shape of these curves deviates from Maxwellian behavior, indicating the presence of faster relaxation processes, which superimpose each other on the main slow relaxation process. This behavior can be interpreted in terms of the copolymers polydispersity and imperfections in the macromolecular microstructure, which should inevitably broaden the relaxation spectra. The dynamics of the system are scaled by the slope of G
′ and G
′′ in the terminal zone, G
c, and characteristic time t
c (1
/
f) at a frequency corresponding to the crossing point G
c. According to the sticky reputation theory of Leibler et al. [32], the value of t
c indicated the disentanglement time of polymer chain limited outside the tube. The values obtained are reported in Table 3.Table 3
Values of the slopes of the storage modulusG
′ and the loss modulus G
′
′ in the terminal zone and values of the crossing time t
c for the polymers.
Polymer
Slope
G
c (Pa)
t
c (s)
G
′ (Pa)
G
′
′ (Pa)
PAM
2.2
0.98
/
<0.01
0.5DM4.5
1.6
1.17
1.51
0.32
0.5DM9.3
1.35
1.05
2.27
0.86
0.5DM12.7
1.27
0.86
2.45
2.85
0.75DM4.6
1.46
1.15
1.79
0.82
0.75DM9.3
1.25
0.93
2.78
1.92
0.75DM12.8
1.32
0.96
3.56
6.25The presence of the hydrophobic group into macromolecular chain increased both moduli and the terminal zone is shifted toward low frequencies due to the transitional network junctions by hydrophobic associations. 0.5 DM4.5 exhibits a slight increase in the modulus at Hz compared to that of PAM, while copolymer 0.5 DM9.3 shows a more marked enhancement withG
c
=
2.27 Pa at 1.17 Hz. Increasing the microblock length of the hydrophobe or its hydrophobic molar proportion in the polymer is accompanied by the increase in the modulus and the slower relaxation time. Both the storage (G
′) and loss (G
′′) modulus reflected the strength of the intermolecular interactions. At the identical hydrophobic proportion, G
c (G
′
=
G
′′) of 0.75DM9.3 is 2.78 Pa compared to 1.79 Pa of 0.75DM4.6. Also, in consideration of the similar N
H
, the value of G
c was, respectively, 2.45 Pa and 3.56 Pa for 0.5DM12.7 and 0.75DM12.8. Note that the storage (G
′) and loss (G
′′) modulus exhibit uncoordinated variation over the frequency considered. G
′ becomes larger than G
′′ after the cross-point, indicating the domination of elastic part.On the other hand, timet
c also increased significantly with the strength of the intermolecular associations, that is, with the lifetime of the hydrophobic groups in interaction form. For copolymers 0.5DM4.5 and 0.75DM4.6, the relaxation time is, respectively, 32 and 82 times the values for PAM. We also find the longer N
H with less hydrophobic proportion had the equivalent t
c to that shorter N
H with more hydrophobic proportion. The relaxation time is 0.82 s for 0.75DM4.6 to 0.85 s for 0.5DM9.3. Moreover, at the same hydrophobic proportion, the increase in t
c was even more pronounced when N
H increases. The second relaxation time is not observed and it will probably be located at higher frequencies which is experimentally inaccessible since the response is no longer linear.


### 3.4. Additives Influence

#### 3.4.1. Influence of Salt

The apparent viscosity as a function of NaCl concentration for 0.75DM12.8 and PAM at polymer concentration of 0.15 g dL−1 and 0.75 g dL−1 was represented in Figure 11. The values of the curves are expressed in terms of a relative viscosity, that is, the ratio of the viscosity in the presence of salt to the viscosity in salt-free solution.Figure 11
Relative variation of the viscosity with NaCl concentration for copolymer 0.75DM12.8 and PAM at two different concentrations (shear rate 7.34 s−1, T
=
25°C).The behavior of PAM exhibits almost the same trend at two different concentrations in the whole salt concentration range. At low salt concentration, the viscosity decreases smoothly upon the increase in salt content, and above the certain salt concentration, relative constant apparent viscosity is exhibited. For PAM, increasing the concentration slightly shifts the constant apparent viscosity towards the lower salt concentration. At the highest salt level, the viscosity of PAM at 0.75 g dL−1 is about 85% of its initial value in pure water. This can be explained that the polarity of solvent is changed in the presence of salt, resulting in the oppression of macromolecular chain accompanied by slight decrease of the apparent viscosity. However, for copolymer 0.75DM12.8 in salt solution, the variation of the viscosity depends significantly on the polymer concentration. For copolymer 0.75DM12.8 dilute solution (0.15 g dL−1), slightly higher than critical concentration (0.11 g dL−1), apparent viscosity increases with increasing of NaCl concentration. At NaCl concentration of 0.80 g dL−1, apparent viscosity reaches the maximum value (3 times that value in salt free solution), subsequently decreases steeply, and it finally becomes close to that of PAM. Solution polarity induced by the presence of NaCl enhances intermolecular interaction between hydrophobic groups of the chains and the good salt-thickening behavior is observed. On the other hand, with further increasing the salt concentration, the hydrophobic microstructures turn compact and isolated macromolecules resulting in the disappearance of intermolecular interaction and the decrease of the apparent viscosity. This behavior supports the conclusion that, below the chain overlap regime, the thickening efficiency arises from the intermolecular interaction between the hydrophobic segments of the chains. Once the transient network is disrupted into small clusters, the viscosity is significantly lowered. Conversely, over the chain overlap regime (0.75 g dL−1), apparent viscosity of copolymer 0.75DM12.7 almost keeps constant after attaining the maximum value (3.5 times that value in salt-free solution). This can be ascribed to the high degree of chain overlap and even entanglement at this concentration prevents the network from disruption. For copolymer 0.75DM12.7, when the salt concentration is above 10 g dL−1, either clouding or separation is observed.


#### 3.4.2. Influence of Surfactant

Figure12 depicts the dependence of the variation viscosity for copolymers 0.75DM12.7 and 0.75DM9.3 on the SDS concentration. SDS and hydrophobic monomer DMDCC bear the opposite charges; thus, interaction between copolymer chain and SDS occurs. Surfactant molecules first absorb at the hydrophobic units at low surfactant concentrations to form hydrophobic clusters. With continuously increasing concentration of SDS, the microdomain is reinforced by mixed micelles formed by hydrophobic groups and surfactant expanding the clusters size, resulting in the increase in viscosity. Near the CMC of SDS, significantly cooperative interaction between the copolymer chain and surfactant molecule is constructed due to mixed micelles serving as junction points for transitional network. And the maximum value of viscosity for copolymer 0.75DM12.8 is observed (2 times that of value in SDS-free solution). Beyond the CMC of SDS, hydrophobic segments of copolymer chains are dissolved into micelles formed by much numbers of surfactant molecules, disrupting junction points, resulting in the decrease of viscosity.Figure 12
Variation of apparent viscosity of as a function of SDS concentration for copolymers 0.75DM12.8 and 0.75DM9.3 at 0.5 g dL−1 (shear rate 7.34 s−1, T
=
25°C).It is noteworthy that the increasing ofN
H shifts the maximum viscosity toward the higher SDS concentration and more remarkable viscosity is observed. For copolymer 0.75DM12.8 the maximum viscosity, 1750 mPa·s, is exhibited at the SDS concentration of 8.5 mM compared to 1530 mPa·s for 0.75DM9.3 at the SDS concentration of 6.7 mM. Cooperatively, as the SDS concentration is raised above CMC, a large viscosity for 0.75DM12.8 is still observed. Two points can be used to interpret that the viscosity for 0.75DM12.8 in the presence of surfactant is much higher than that of value for 0.75DM9.3, that is, hydrophobic association and ionic attraction. Hydrophobic associations reduce the contacts of the hydrophobic segments of polymer chain with water leading to lowering the free energy of the system [3]. It is discussed above that the longer the hydrophobic microblock, the stronger the intermolecular association, and thus, less free energy of the system. Ionic attraction between SDS molecules and copolymer chains is obviously enhanced with prolonging the length of cationic hydrophobic groups per chain. In the case of cationic, nonionic, and zwitterionic surfactants, whether the length of hydrophobic microblock plays a role in the rheological behavior should be further studied.


### 3.5. Fluorescence Investigation

The intensity ratioI
3
/
I
1 of the third (385 nm) to the first (375 nm) vibronic peak in the fluorescence emission spectrum of pyrene is sensitive to the polarity of the local microenvironment of the pyrene probe [12, 14]. This ratio is directly proportional to polarity. Thus, the values of I
3
/
I
1 provide significant evidence for the formation of hydrophobic microdomains at salt concentrations and the development of bridge points or mixed micelles when surfactant is added. Figure 13 depicts the fluorescence spectra of 0.2 g dL−1 0.75DM12.8 for pyrene at different conditions. The I
3
/
I
1 value is 0.706 in aqueous solution, which increases to 0.835 in 8 mM SDS solution where the pyrene probe is located in the mixed micelles constructed by surfactant molecules and hydrophobic segments of 0.75DM12.8. Additionally, the I
3
/
I
1 value in 5.85 g dL−1 solution is 0.883 higher than that in aqueous solution, indicating that the hydrophobic microdomains became more compact in the high salt concentration. These results agree favorably with that obtained from viscosity.Figure 13
Fluorescence spectra of pyrene in 0.25 g dL−1 0.75DM12.8 solutions at different conditions.


### 3.6. Morphology of Networks

The microscopic structures of poly(AM/DMDCC) at different experimental conditions are observed through ESEM at room temperature and the morphological images are shown in Figure14. In extremely dilute solution of copolymer 0.5DM12.7, intramolecular associations of hydrophobic segments compact polymers chains and an irregular microstructure is observed, which, of course, lowers viscosity. At the critical association concentration shown in Figure 14(b), three-dimensional network formed by intermolecular association results in a regular morphology and dramatically enhances solution viscosity. These three-dimensional networks are disrupted in the presence of higher concentration salt and broke into small clusters. As shown in Figure 14(c), for copolymer 0.75DM12.8, morphology of salt aggregation is observed due to high concentration of salt. At higher polymer concentration, as exhibited in Figure 14(d), high degree of chain entanglement protects three-dimensional networks from disruption and keeps viscosity relatively stable. Adding SDS, a significantly cooperative interaction between the copolymer chain and surfactant leads to more regular microstructures than these of copolymer solution. Moreover, for copolymer 0.75DM12.8 with the longest N
H, at the CMC of SDS, both intermolecular hydrophobic interactions and ionic attractions are cooperative to promote the aggregation behavior of copolymer; thus, the most regular microstructures are observed.ESEM images of poly(AM/DMDCC) at different experimental conditions; (a) 0.5DM12.7 with 0.075 g dL−1; (b) 0.5DM12.7 with 0.15 g dL−1; (c) 0.75DM12.8 with 0.15 g dL−1 in 2 g dL−1 salt solution; (d) 0.75DM12.8 with 0.75 g dL−1 in 2 g dL−1 salt solution; (e) 0.5DM12.7 with 0.5 g dL−1 in 8 mM SDS solution; (f) 0.75DM12.8 with 0.5 g dL−1 in 8 mM SDS solution.
(a)
(b)
(c)
(d)
(e)
(f)


## 3.1. Characterization of DMDCC-SDS Mixed Micelles

SDS was chosen to study the micellar behavior of DMDCC-SDS binary mixed system, because it bears the same hydrophobic long chain as DMDCC and the most common surfactant used in radical micellar copolymerization, and, most importantly, mixture of cationic (DMDCC) and anionic (SDS) surfactants has a net interaction (β
<
0). In the case of binary mixed micelles composed of cationic-anionic pairs, the CMC of the surfactant mixture can be calculated as follows:
(2)
1
CMC
m
=
α
1
f
1
m
CM
C
1
+
α
2
f
2
m
CM
C
2
,
where CMC
m is the critical micelle concentration of binary mixed surfactants, the subscripts 1, 2 represent DMDCC and SDS, respectively. CM
C
1, CM
C
2 are the critical micelle concentration of single surfactant species, α
1 and α
2 are the bulk mole fractions of the respective surfactants in the system, and f
1
m, f
2
m are the activity coefficients that can be found by using the regular solution theory,
(3)
ln
⁡
f
1
m
=
(
α
2
m
)
2
β
,
ln
⁡
f
2
m
=
(
α
1
m
)
2
β
,
where β is an interaction parameter, quantifying the net interaction between the surfactant species in the mixed micelle. α
1
m and α
2
m are the mole fractions of the single surfactant in mixed system which are written as follows:
(4)
α
1
m
=
α
1
f
2
m
CM
C
2
α
1
f
2
m
CM
C
2
+
α
2
f
1
m
CM
C
1
,
α
2
m
=
1
-
α
1
m
.Figure1 shows the CM
C
m of DMDCC-SDS binary mixed system as a function of DMDCC mole fraction in solution. We can see that the CMC values of single SDS and DMDCC in aqueous solution are 8 mM, 0.82 mM, respectively. For the DMDCC-SDS mixed system, the CMC values of anionic surfactant SDS significantly decrease by adding a small amount of DMDCC without causing any precipitation. Interestingly, the CMC values of the binary surfactant remain almost constant with the increase in DMDCC molar fraction in aqueous solution.Figure 1
Variation of critical micelle concentration of DMDCC-SDS binary mixture system as a function of DMDCC mole fraction (T
=
50°C).The CMC of mixed surfactants strongly depends on parameter valuesβ. Positive β values imply a net repulsive force between the surfactant components, whereas negative β values imply a net attractive force. The more negative β values are, the stronger the net interaction between the surfactants in the mixed system will become; thus the CMC of mixed surfactants is much lower. For reference, the CMC of DTAB-SDS mixed system as the function of CTAB mole fraction is depicted in Figure 2. The strong synergetic effect (β
=
-
13.2) indicated that there was a large net attraction between the surfactants.Figure 2
Variation of critical micelle concentration of DTAB-SDS binary mixture system as a function of DTAB mole fraction [22], reproduced from [22], with permission from John Wiley & Sons.The much lower CMC values of SDS are obtained by adding cationic surfactant DTAB. We note that DMDCC bears almost the same structure as DTAB. Therefore, we can draw a conclusion that the CMC behavior of DMDCC-SDS mixed system, as shown in Figure3, has the same dynamic character as that of DTAB-SDS. However, the aggregation morphology of DMDCC-SDS mixed system as the mole fraction of DMDCC has unique dynamic character, which is shown in Figure 1. The N
agg value of anionic surfactant SDS significantly increases by adding a small amount of DMDCC and then remains almost constant with the increase in DMDCC molar fraction in aqueous solution, which could be written as follows:
(5)
N
agg
m
=
α
1
m
N
agg
1
+
α
2
m
N
agg
2
,
where N
agg
1 and N
agg
2 are the respective aggregation number values of DMDCC and SDS in aqueous solution. The length of hydrophobic microblock in hydrophobically modified polyacrylamide prepared by conventional radical micelle copolymerization is determined by
(6)
N
H
=
[
H
]
N
agg
[
S
]
-
CMC
,
where [H], [S], and CMC are the mole concentration of the hydrophobic monomer, the mole concentration of surfactant, and critical concentration of surfactant, whereas the length of hydrophobic microblock from mixed micelle copolymerization should be rewritten as
(7)
N
H
=
(
[
H
]
-
CM
C
H
)
N
agg
m
[
H
+
S
]
-
CM
C
(
H
+
S
)
.Figure 3
Schematic representation of the mixed DMDCC-SDS micelles compared to pure DMDCC micelles and pure SDS micelles.In the DMDCC/SDS mixed system,CM
C
H is the CMC of surfmer and CM
C
H
+
S is the critical micelle concentration of DMDCC-SDS binary mixed micelles and N
agg
m which is determined by steady-state fluorescence quenching technique. Therefore, the length of microblock could be tuned reasonably by the mixed micelle technique.


## 3.2. Synthesis and Characterization

The copolymers poly(AM/DMDCC) with low amounts of cationic hydrophobe were obtained in water using a DMDCC-SDS binary mixed micellar polymerization (Scheme2). The characteristic of the copolymer is depicted in Table 1. For DMDCC, IR (KBr, ν/cm−1): 3432 (s, ν(C=O)), 2919 (vs, ν
as(C–H)), 2844 (s, ν
s(C–H)), 1633 (w, ν(C=C)), 1299 (s, ν(C–N)), 1167 (vs, ν(C–C)) 1028 (w, ν(C–O)). For copolymer 0.75DM12.8, IR (KBr, ν/cm−1): 3450 (vs, ν
s(NH2), ν(C=O)), 2925 (w, ν(C–H)), 1025 (w, ν(C–O)), 628 (s, δ(C–H)). 1H NMR (400 MHz, D2O, δ/ppm): 1.11 (q, 2Hg; CH2), 1.58 (d, 2Ha; CH2), 2.16 (d, 1Hb, CH), 2.36 (t, 3Hc, CH3), 2.48 (s, 3Hf, CH3), 3.59 (m, 2He, CH2), 3.72 (q, 2Hd, CH2) (Figures 4 and 5).Table 1
Structural parameters of the copolymers.
Samplea
Polymer composition mol %
N
H
b
Polymer characterization
AM
DMDCC
SDS
S
c
10
-
6
×
M
w g mol−1
[η]mL g−1
[
η
]
calc
d mL g−1
Solubility in watere
PAM
100
0
0
0
0
3.50
610
755
+
+
0.5DM4.5
99.5
0.5
1.75
4.5
25
3.15
586
697
+
+
0.5DM9.3
0.8
9.3
12.4
3.29
540
720
+
0.5DM12.7
0.5
12.7
9
3.25
520
714
+
0.5DM92
0
92
0.6
1.64
299
428
±
0.75DM4.6
99.25
0.75
5.5
4.6
25
2.22
335
536
+
+
0.75DM9.3
2.1
9.3
17
3.06
470
683
+
0.75DM12.8
1.35
12.8
13
3.35
418
730
+
0.75DM92
0
92
0
/
/
/
−
aThe first number indicated the mole frication of hydrophobic monomer, and the final number indicated the rounded value of N
H (e.g., 0.5DM5 stands for a polymer that contains 0.5 mol % of DMDCC with N
H
≈
4.5). bNumber of hydrophobes per micelle ≈ hydrophobic block length. cNumber of hydrophobic blocks per chain (i.e., stickers)30 calculated using the relationship S
=
(
M
W
/
2
m
)
[
H
]
/
N
H, where m is the molecular weight of the monomer unit (acrylamide, m = 71) and M
W
/
2
m corresponds to the number average degree of polymerization,
N. dIntrinsic viscosity calculated using relationship [
η
]
=
9.33
×
1
0
-
3
M
W
0.75 established for PAM31. e++, easily soluble; +, soluble; ±, cloudy solution; −, difficult to dissolve.Scheme 2
Copolymerization of AM and DMDCC.Figure 4
IR spectra of the DMDCC and copolymer 0.75DM12.8.Figure 5
1HNMR spectra of copolymer 0.75DM12.8.


## 3.3. Rheological Behavior

### 3.3.1. Viscometric Behavior in Dilute Solution

The effect of the hydrophobic microblock length, that is,N
H value, and the concentration of hydrophobic monomer on intra- and intermolecular interaction is depicted in Figure 6. Apparent viscosity is plotted as a function of polymer concentration for three copolymers (0.5DM4.5, 0.5DM9.3, and 0.75DM9.3) and for the corresponding polyacrylamide.Figure 6
Apparent viscosity as a function of polymer concentration for copolymers 0.75DM12.8, 0.5DM12.7, and 0.5DM9.3 samples and for a PAM sample (T
=
25°C, the inlet of apparent viscosity is partially enlarged for purpose of smart understanding).All the samples are well measured at a constant shear rate of 7.34 s−1. In extremely dilute solution regime (c
P < 0.05 g dL−1), the apparent viscosity of copolymers is lower than that of PAM due to intramolecular association which leads to the coil of chain. This effect is enhanced by increasing either the N
H or the hydrophobe concentration. And it is well explained that the [
η
] of all the poly(AM/DMDCC) is reduced compared to that of PAM and inverse to the N
H value. Because the [
η
] of the polymer was determined by automatic capillary viscometer at low polymer concentration, intermolecular interaction was gradually enhanced with the increase in polymer concentration. Above a critical concentration, that is, CAC, an upward curvature in the apparent viscosity can be observed. The apparent viscosity increases more markedly and shows up at lower concentration with increasing the hydrophobic length at the same hydrophobe concentration. The CAC of 0.5DM4.5 and 0.5DM9.3 is 0.15 g dL−1 and 0.13 g dL−1, respectively. On the other hand, 0.75DM9.3 and 0.5DM9.3 have the same hydrophobic microblock length; the increase in hydrophobe also enhances thickening efficiency. This behavior can be explained by the increase in sticker reported in Table 1, which makes the intermolecular interactions much stronger, and the CAC of 0.75DM9.3 is 0.11 g dL−1. The upturn of apparent viscosity in case of the PAM is due to the onset of chain overlap, that is, c
*, and related to the chain size. The viscosity upturn observed for poly(AM/DMDCC) cannot be attributed to a chain overlap since poly(AM/DMDCC) had the similar range of molecular weight. Moreover the chain overlap behavior was long-term effect which occurred at high polymer concentration. Therefore, the remarkable viscosity onset is a result of the formation of hydrophobic microdomain caused by hydrophobic intermolecular interaction. The hydrophobic microblock length directly influences the thickening efficiency. However, when the N
H goes beyond a certain value, negative impact, such as low rate polymer conversion and the poor solubility, would occur, which accorded with the general law of the water-soluble associating polymer prepared by conventional radical micelle copolymerization [4, 16, 30].


### 3.3.2. Steady Flow Experiments

Apparent viscosity as a function of shear rate is conducted for three copolymers modified by 0.5 mol% DMDCC and for PAM. The viscosity/shear rate curves of the copolymers and PAM at concentration of 1.0 g dL−1 and 2.0 g dL−1 are shown in Figures 7 and 8. It is interesting to figure out that the rheological properties of the copolymers are strongly dependent on N
H and polymer concentration.Figure 7
Variation of apparent viscosity as a function of shear rate for PAM, 0.5DM12.7, and 0.5DM4.5 (c
p
=
1.0 g dL−1, T
=
25°C).Figure 8
Variation of apparent viscosity as a function of shear rate for PAM, 0.5DM12.7, and 0.5DM4.5 (c
p
=
2.0 g dL−1, T
=
25°C).PAM exhibits the classic rheological behavior, that is, a slight shear thinning effect after Newtonian plateau. All the copolymers present the same type of behavior. For poly(AM/DMDCC), at 1.0 g dL−1 concentration, a shear thickening domain reaches first followed by shear thinning. The shear thickening is interpreted in terms of the balance between intra- and intermolecular associations. At a certain shear rate, the shear forces are strong enough to extend the polymer coils and disrupt the intramolecular hydrophobic interactions. The intramolecular hydrophobic microdomain is released and favors forming intermolecular hydrophobic interactions, resulting in an increase in viscosity. Further increasing shear rate, these interactions are gradually broken and shear thinning behavior is observed. This behavior was general agreement with the nonionic hydrophobically modified polyacrylamides [31].To determine the role of theN
H in the apparent viscosity, for all polymers, the values of viscosity (η
0) which corresponded to the shear rate (γ
˙
*) and shear stress (σ
*) on the onset of Newtonian plateau were reported in Table 2. Apparent viscosity increases with the increasing of shear rate; at such shear rate (γ
˙
*), this plateau is attainable as shown in Figures 7 and 8, and beyond which the fluid presents a shear thinning behavior; the values of the stress threshold σ
*
=
γ
˙
*
η
0.Table 2
Rheological values ofσ
*, γ
˙
*, and η
0 for poly(AM/DMDCC) and PAM at concentration of 1.0 g dL−1 and 2.0 g dL−1.
Polymer
c
p = 1.0 g dL−1
c
p = 2.0 g dL−1
σ
* (Pa)
γ
˙
* (s−1)
η
0 (mPa·s)
σ
* (Pa)
γ
˙
* (s−1)
η
0 (mPa·s)
PAM
0.93
10.3
90
3.6
10
357
0.5DM4.5
1.09
1.66
658
8.2
0.56
14650
0.5DM9.3
1.55
1.23
1264
9.78
0.36
27160
0.5DM12.7
2.07
0.76
2723
13.15
0.25
62600In case of PAM, a higherγ
˙
* is presented compared to that of copolymers. With the increase in shear rate, shear force is strong enough to disrupt the gauss coils structured by the macromolecular chains overlap and entanglement, and the original chain orientation is released to form orderly orientation, resulting in a decrease in viscosity. As for copolymers, the length of hydrophobic microblock 4.5 (0.5DM4.5) is enough to induce an increase in the solution viscosity. Lengthening of hydrophobic microblock enhanced the degree of association facilitating shear thickening behavior. At a certain shear rate, the shear forces are strong enough to extend the copolymer coils and disrupt the intramolecular hydrophobic interactions, resulting in the decrease of viscosity.The stress threshold valuesσ
*show that the longer the N
H, the higher the σ
*. This indicates that more stress force is required to disrupt the molecular interactions with increase in the length of hydrophobic microblock, which results in a stronger transitory three-dimensional network. At the identical polymer concentration, the increase in N
H is accompanied by a decrease of γ
˙
*, shortening the Newtonian zone. The solution became more sensitive to shear rate. For example, at a concentration of 1.0 g dL−1, the shear rate γ
˙
* of copolymers 0.5DM12.7 and 0.5DM9.3 is 0.76 s−1 and 1.23 s−1, respectively, compared to 1.66 s−1 of copolymer 0.5DM4.5. Higher viscosity at low shear rate indicates a more pronounced shear thickening domain and a longer shear thinning plateau. At higher shear rate, the copolymer viscosity trends towards that of PAM, but even at 1000 s−1, the value is mainly greater indicating that intermolecular interaction also existed.We should figure out that even at a higher concentration (2.0 g dL−1), shear thickening domain is also observed, and both copolymers show classical shear thickening subsequent shear thinning behavior within the range of shear rate. This owning to the fact that beside molecular weight and polymer concentration the nature of hydrophobic monomer also influences shear thickening efficiency. The apparent viscosity/shear rate curves at the characteristic values at the Newtonian plateau are also given in Table 2. We also observe that increasing the concentration shortens the shear thickening plateau, while the magnitude of the η
0 increases with increasing polymer concentration. The values reported in Table 2 confirmed that, for cationic hydrophobic associative polyacrylamides, concentration, especially, N
H, had great effects on steady flow rheological properties.


### 3.3.3. Linear Viscoelasticity

Figures9 and 10 present illustration of the oscillatory response for poly(AM/DMDCC) and PAM at 1.0 g dL−1 in aqueous solution. The variations of the storage (G
′) and loss (G
′′) modulus are curved versus frequency (f). The slopes of G
′ and G
′′ in the terminal zone for polyacrylamide are 2.2 and 0.98. Note that the slopes of G
′ and G
′′ will not keep constant, which are dependent on the PAM concentration [4].Figure 9
Storage (G
′) and loss (G
′′) modulus as a function of frequency for copolymers 0.5DM12.7, 0.5DM9.3, and 0.5DM4.5 and for PAM (c
p
=
1.0 g dL−1, T
=
25°C).Figure 10
Storage (G
′) and loss (G
′′) modulus as a function of frequency for copolymers 0.75DM12.8, 0.75DM9.3, and 0.75DM4.6 and for PAM (c
p
=
2.0 g dL−1, T
=
25°C).However, for copolymers modified by hydrophobic groups, at low frequencies, the behavior of the shear modulus is Maxwellian, indicating the variations ofG
′(f) and G
′′(f) that scaled as f
2 and f, respectively. The curves obtained for the different series of copolymers have a profile similar to that for solutions whose viscoelastic properties are governed by chain entanglements. These solutions are characterized at low frequency by a slope of G
′ and G
′′, where the values of G
′ were below that of G
′′. Above the frequency at which curves G
′(f) and G
′′(f) cross each other (G
c), the shape of these curves deviates from Maxwellian behavior, indicating the presence of faster relaxation processes, which superimpose each other on the main slow relaxation process. This behavior can be interpreted in terms of the copolymers polydispersity and imperfections in the macromolecular microstructure, which should inevitably broaden the relaxation spectra. The dynamics of the system are scaled by the slope of G
′ and G
′′ in the terminal zone, G
c, and characteristic time t
c (1
/
f) at a frequency corresponding to the crossing point G
c. According to the sticky reputation theory of Leibler et al. [32], the value of t
c indicated the disentanglement time of polymer chain limited outside the tube. The values obtained are reported in Table 3.Table 3
Values of the slopes of the storage modulusG
′ and the loss modulus G
′
′ in the terminal zone and values of the crossing time t
c for the polymers.
Polymer
Slope
G
c (Pa)
t
c (s)
G
′ (Pa)
G
′
′ (Pa)
PAM
2.2
0.98
/
<0.01
0.5DM4.5
1.6
1.17
1.51
0.32
0.5DM9.3
1.35
1.05
2.27
0.86
0.5DM12.7
1.27
0.86
2.45
2.85
0.75DM4.6
1.46
1.15
1.79
0.82
0.75DM9.3
1.25
0.93
2.78
1.92
0.75DM12.8
1.32
0.96
3.56
6.25The presence of the hydrophobic group into macromolecular chain increased both moduli and the terminal zone is shifted toward low frequencies due to the transitional network junctions by hydrophobic associations. 0.5 DM4.5 exhibits a slight increase in the modulus at Hz compared to that of PAM, while copolymer 0.5 DM9.3 shows a more marked enhancement withG
c
=
2.27 Pa at 1.17 Hz. Increasing the microblock length of the hydrophobe or its hydrophobic molar proportion in the polymer is accompanied by the increase in the modulus and the slower relaxation time. Both the storage (G
′) and loss (G
′′) modulus reflected the strength of the intermolecular interactions. At the identical hydrophobic proportion, G
c (G
′
=
G
′′) of 0.75DM9.3 is 2.78 Pa compared to 1.79 Pa of 0.75DM4.6. Also, in consideration of the similar N
H
, the value of G
c was, respectively, 2.45 Pa and 3.56 Pa for 0.5DM12.7 and 0.75DM12.8. Note that the storage (G
′) and loss (G
′′) modulus exhibit uncoordinated variation over the frequency considered. G
′ becomes larger than G
′′ after the cross-point, indicating the domination of elastic part.On the other hand, timet
c also increased significantly with the strength of the intermolecular associations, that is, with the lifetime of the hydrophobic groups in interaction form. For copolymers 0.5DM4.5 and 0.75DM4.6, the relaxation time is, respectively, 32 and 82 times the values for PAM. We also find the longer N
H with less hydrophobic proportion had the equivalent t
c to that shorter N
H with more hydrophobic proportion. The relaxation time is 0.82 s for 0.75DM4.6 to 0.85 s for 0.5DM9.3. Moreover, at the same hydrophobic proportion, the increase in t
c was even more pronounced when N
H increases. The second relaxation time is not observed and it will probably be located at higher frequencies which is experimentally inaccessible since the response is no longer linear.


## 3.3.1. Viscometric Behavior in Dilute Solution

The effect of the hydrophobic microblock length, that is,N
H value, and the concentration of hydrophobic monomer on intra- and intermolecular interaction is depicted in Figure 6. Apparent viscosity is plotted as a function of polymer concentration for three copolymers (0.5DM4.5, 0.5DM9.3, and 0.75DM9.3) and for the corresponding polyacrylamide.Figure 6
Apparent viscosity as a function of polymer concentration for copolymers 0.75DM12.8, 0.5DM12.7, and 0.5DM9.3 samples and for a PAM sample (T
=
25°C, the inlet of apparent viscosity is partially enlarged for purpose of smart understanding).All the samples are well measured at a constant shear rate of 7.34 s−1. In extremely dilute solution regime (c
P < 0.05 g dL−1), the apparent viscosity of copolymers is lower than that of PAM due to intramolecular association which leads to the coil of chain. This effect is enhanced by increasing either the N
H or the hydrophobe concentration. And it is well explained that the [
η
] of all the poly(AM/DMDCC) is reduced compared to that of PAM and inverse to the N
H value. Because the [
η
] of the polymer was determined by automatic capillary viscometer at low polymer concentration, intermolecular interaction was gradually enhanced with the increase in polymer concentration. Above a critical concentration, that is, CAC, an upward curvature in the apparent viscosity can be observed. The apparent viscosity increases more markedly and shows up at lower concentration with increasing the hydrophobic length at the same hydrophobe concentration. The CAC of 0.5DM4.5 and 0.5DM9.3 is 0.15 g dL−1 and 0.13 g dL−1, respectively. On the other hand, 0.75DM9.3 and 0.5DM9.3 have the same hydrophobic microblock length; the increase in hydrophobe also enhances thickening efficiency. This behavior can be explained by the increase in sticker reported in Table 1, which makes the intermolecular interactions much stronger, and the CAC of 0.75DM9.3 is 0.11 g dL−1. The upturn of apparent viscosity in case of the PAM is due to the onset of chain overlap, that is, c
*, and related to the chain size. The viscosity upturn observed for poly(AM/DMDCC) cannot be attributed to a chain overlap since poly(AM/DMDCC) had the similar range of molecular weight. Moreover the chain overlap behavior was long-term effect which occurred at high polymer concentration. Therefore, the remarkable viscosity onset is a result of the formation of hydrophobic microdomain caused by hydrophobic intermolecular interaction. The hydrophobic microblock length directly influences the thickening efficiency. However, when the N
H goes beyond a certain value, negative impact, such as low rate polymer conversion and the poor solubility, would occur, which accorded with the general law of the water-soluble associating polymer prepared by conventional radical micelle copolymerization [4, 16, 30].


## 3.3.2. Steady Flow Experiments

Apparent viscosity as a function of shear rate is conducted for three copolymers modified by 0.5 mol% DMDCC and for PAM. The viscosity/shear rate curves of the copolymers and PAM at concentration of 1.0 g dL−1 and 2.0 g dL−1 are shown in Figures 7 and 8. It is interesting to figure out that the rheological properties of the copolymers are strongly dependent on N
H and polymer concentration.Figure 7
Variation of apparent viscosity as a function of shear rate for PAM, 0.5DM12.7, and 0.5DM4.5 (c
p
=
1.0 g dL−1, T
=
25°C).Figure 8
Variation of apparent viscosity as a function of shear rate for PAM, 0.5DM12.7, and 0.5DM4.5 (c
p
=
2.0 g dL−1, T
=
25°C).PAM exhibits the classic rheological behavior, that is, a slight shear thinning effect after Newtonian plateau. All the copolymers present the same type of behavior. For poly(AM/DMDCC), at 1.0 g dL−1 concentration, a shear thickening domain reaches first followed by shear thinning. The shear thickening is interpreted in terms of the balance between intra- and intermolecular associations. At a certain shear rate, the shear forces are strong enough to extend the polymer coils and disrupt the intramolecular hydrophobic interactions. The intramolecular hydrophobic microdomain is released and favors forming intermolecular hydrophobic interactions, resulting in an increase in viscosity. Further increasing shear rate, these interactions are gradually broken and shear thinning behavior is observed. This behavior was general agreement with the nonionic hydrophobically modified polyacrylamides [31].To determine the role of theN
H in the apparent viscosity, for all polymers, the values of viscosity (η
0) which corresponded to the shear rate (γ
˙
*) and shear stress (σ
*) on the onset of Newtonian plateau were reported in Table 2. Apparent viscosity increases with the increasing of shear rate; at such shear rate (γ
˙
*), this plateau is attainable as shown in Figures 7 and 8, and beyond which the fluid presents a shear thinning behavior; the values of the stress threshold σ
*
=
γ
˙
*
η
0.Table 2
Rheological values ofσ
*, γ
˙
*, and η
0 for poly(AM/DMDCC) and PAM at concentration of 1.0 g dL−1 and 2.0 g dL−1.
Polymer
c
p = 1.0 g dL−1
c
p = 2.0 g dL−1
σ
* (Pa)
γ
˙
* (s−1)
η
0 (mPa·s)
σ
* (Pa)
γ
˙
* (s−1)
η
0 (mPa·s)
PAM
0.93
10.3
90
3.6
10
357
0.5DM4.5
1.09
1.66
658
8.2
0.56
14650
0.5DM9.3
1.55
1.23
1264
9.78
0.36
27160
0.5DM12.7
2.07
0.76
2723
13.15
0.25
62600In case of PAM, a higherγ
˙
* is presented compared to that of copolymers. With the increase in shear rate, shear force is strong enough to disrupt the gauss coils structured by the macromolecular chains overlap and entanglement, and the original chain orientation is released to form orderly orientation, resulting in a decrease in viscosity. As for copolymers, the length of hydrophobic microblock 4.5 (0.5DM4.5) is enough to induce an increase in the solution viscosity. Lengthening of hydrophobic microblock enhanced the degree of association facilitating shear thickening behavior. At a certain shear rate, the shear forces are strong enough to extend the copolymer coils and disrupt the intramolecular hydrophobic interactions, resulting in the decrease of viscosity.The stress threshold valuesσ
*show that the longer the N
H, the higher the σ
*. This indicates that more stress force is required to disrupt the molecular interactions with increase in the length of hydrophobic microblock, which results in a stronger transitory three-dimensional network. At the identical polymer concentration, the increase in N
H is accompanied by a decrease of γ
˙
*, shortening the Newtonian zone. The solution became more sensitive to shear rate. For example, at a concentration of 1.0 g dL−1, the shear rate γ
˙
* of copolymers 0.5DM12.7 and 0.5DM9.3 is 0.76 s−1 and 1.23 s−1, respectively, compared to 1.66 s−1 of copolymer 0.5DM4.5. Higher viscosity at low shear rate indicates a more pronounced shear thickening domain and a longer shear thinning plateau. At higher shear rate, the copolymer viscosity trends towards that of PAM, but even at 1000 s−1, the value is mainly greater indicating that intermolecular interaction also existed.We should figure out that even at a higher concentration (2.0 g dL−1), shear thickening domain is also observed, and both copolymers show classical shear thickening subsequent shear thinning behavior within the range of shear rate. This owning to the fact that beside molecular weight and polymer concentration the nature of hydrophobic monomer also influences shear thickening efficiency. The apparent viscosity/shear rate curves at the characteristic values at the Newtonian plateau are also given in Table 2. We also observe that increasing the concentration shortens the shear thickening plateau, while the magnitude of the η
0 increases with increasing polymer concentration. The values reported in Table 2 confirmed that, for cationic hydrophobic associative polyacrylamides, concentration, especially, N
H, had great effects on steady flow rheological properties.


## 3.3.3. Linear Viscoelasticity

Figures9 and 10 present illustration of the oscillatory response for poly(AM/DMDCC) and PAM at 1.0 g dL−1 in aqueous solution. The variations of the storage (G
′) and loss (G
′′) modulus are curved versus frequency (f). The slopes of G
′ and G
′′ in the terminal zone for polyacrylamide are 2.2 and 0.98. Note that the slopes of G
′ and G
′′ will not keep constant, which are dependent on the PAM concentration [4].Figure 9
Storage (G
′) and loss (G
′′) modulus as a function of frequency for copolymers 0.5DM12.7, 0.5DM9.3, and 0.5DM4.5 and for PAM (c
p
=
1.0 g dL−1, T
=
25°C).Figure 10
Storage (G
′) and loss (G
′′) modulus as a function of frequency for copolymers 0.75DM12.8, 0.75DM9.3, and 0.75DM4.6 and for PAM (c
p
=
2.0 g dL−1, T
=
25°C).However, for copolymers modified by hydrophobic groups, at low frequencies, the behavior of the shear modulus is Maxwellian, indicating the variations ofG
′(f) and G
′′(f) that scaled as f
2 and f, respectively. The curves obtained for the different series of copolymers have a profile similar to that for solutions whose viscoelastic properties are governed by chain entanglements. These solutions are characterized at low frequency by a slope of G
′ and G
′′, where the values of G
′ were below that of G
′′. Above the frequency at which curves G
′(f) and G
′′(f) cross each other (G
c), the shape of these curves deviates from Maxwellian behavior, indicating the presence of faster relaxation processes, which superimpose each other on the main slow relaxation process. This behavior can be interpreted in terms of the copolymers polydispersity and imperfections in the macromolecular microstructure, which should inevitably broaden the relaxation spectra. The dynamics of the system are scaled by the slope of G
′ and G
′′ in the terminal zone, G
c, and characteristic time t
c (1
/
f) at a frequency corresponding to the crossing point G
c. According to the sticky reputation theory of Leibler et al. [32], the value of t
c indicated the disentanglement time of polymer chain limited outside the tube. The values obtained are reported in Table 3.Table 3
Values of the slopes of the storage modulusG
′ and the loss modulus G
′
′ in the terminal zone and values of the crossing time t
c for the polymers.
Polymer
Slope
G
c (Pa)
t
c (s)
G
′ (Pa)
G
′
′ (Pa)
PAM
2.2
0.98
/
<0.01
0.5DM4.5
1.6
1.17
1.51
0.32
0.5DM9.3
1.35
1.05
2.27
0.86
0.5DM12.7
1.27
0.86
2.45
2.85
0.75DM4.6
1.46
1.15
1.79
0.82
0.75DM9.3
1.25
0.93
2.78
1.92
0.75DM12.8
1.32
0.96
3.56
6.25The presence of the hydrophobic group into macromolecular chain increased both moduli and the terminal zone is shifted toward low frequencies due to the transitional network junctions by hydrophobic associations. 0.5 DM4.5 exhibits a slight increase in the modulus at Hz compared to that of PAM, while copolymer 0.5 DM9.3 shows a more marked enhancement withG
c
=
2.27 Pa at 1.17 Hz. Increasing the microblock length of the hydrophobe or its hydrophobic molar proportion in the polymer is accompanied by the increase in the modulus and the slower relaxation time. Both the storage (G
′) and loss (G
′′) modulus reflected the strength of the intermolecular interactions. At the identical hydrophobic proportion, G
c (G
′
=
G
′′) of 0.75DM9.3 is 2.78 Pa compared to 1.79 Pa of 0.75DM4.6. Also, in consideration of the similar N
H
, the value of G
c was, respectively, 2.45 Pa and 3.56 Pa for 0.5DM12.7 and 0.75DM12.8. Note that the storage (G
′) and loss (G
′′) modulus exhibit uncoordinated variation over the frequency considered. G
′ becomes larger than G
′′ after the cross-point, indicating the domination of elastic part.On the other hand, timet
c also increased significantly with the strength of the intermolecular associations, that is, with the lifetime of the hydrophobic groups in interaction form. For copolymers 0.5DM4.5 and 0.75DM4.6, the relaxation time is, respectively, 32 and 82 times the values for PAM. We also find the longer N
H with less hydrophobic proportion had the equivalent t
c to that shorter N
H with more hydrophobic proportion. The relaxation time is 0.82 s for 0.75DM4.6 to 0.85 s for 0.5DM9.3. Moreover, at the same hydrophobic proportion, the increase in t
c was even more pronounced when N
H increases. The second relaxation time is not observed and it will probably be located at higher frequencies which is experimentally inaccessible since the response is no longer linear.


## 3.4. Additives Influence

### 3.4.1. Influence of Salt

The apparent viscosity as a function of NaCl concentration for 0.75DM12.8 and PAM at polymer concentration of 0.15 g dL−1 and 0.75 g dL−1 was represented in Figure 11. The values of the curves are expressed in terms of a relative viscosity, that is, the ratio of the viscosity in the presence of salt to the viscosity in salt-free solution.Figure 11
Relative variation of the viscosity with NaCl concentration for copolymer 0.75DM12.8 and PAM at two different concentrations (shear rate 7.34 s−1, T
=
25°C).The behavior of PAM exhibits almost the same trend at two different concentrations in the whole salt concentration range. At low salt concentration, the viscosity decreases smoothly upon the increase in salt content, and above the certain salt concentration, relative constant apparent viscosity is exhibited. For PAM, increasing the concentration slightly shifts the constant apparent viscosity towards the lower salt concentration. At the highest salt level, the viscosity of PAM at 0.75 g dL−1 is about 85% of its initial value in pure water. This can be explained that the polarity of solvent is changed in the presence of salt, resulting in the oppression of macromolecular chain accompanied by slight decrease of the apparent viscosity. However, for copolymer 0.75DM12.8 in salt solution, the variation of the viscosity depends significantly on the polymer concentration. For copolymer 0.75DM12.8 dilute solution (0.15 g dL−1), slightly higher than critical concentration (0.11 g dL−1), apparent viscosity increases with increasing of NaCl concentration. At NaCl concentration of 0.80 g dL−1, apparent viscosity reaches the maximum value (3 times that value in salt free solution), subsequently decreases steeply, and it finally becomes close to that of PAM. Solution polarity induced by the presence of NaCl enhances intermolecular interaction between hydrophobic groups of the chains and the good salt-thickening behavior is observed. On the other hand, with further increasing the salt concentration, the hydrophobic microstructures turn compact and isolated macromolecules resulting in the disappearance of intermolecular interaction and the decrease of the apparent viscosity. This behavior supports the conclusion that, below the chain overlap regime, the thickening efficiency arises from the intermolecular interaction between the hydrophobic segments of the chains. Once the transient network is disrupted into small clusters, the viscosity is significantly lowered. Conversely, over the chain overlap regime (0.75 g dL−1), apparent viscosity of copolymer 0.75DM12.7 almost keeps constant after attaining the maximum value (3.5 times that value in salt-free solution). This can be ascribed to the high degree of chain overlap and even entanglement at this concentration prevents the network from disruption. For copolymer 0.75DM12.7, when the salt concentration is above 10 g dL−1, either clouding or separation is observed.


### 3.4.2. Influence of Surfactant

Figure12 depicts the dependence of the variation viscosity for copolymers 0.75DM12.7 and 0.75DM9.3 on the SDS concentration. SDS and hydrophobic monomer DMDCC bear the opposite charges; thus, interaction between copolymer chain and SDS occurs. Surfactant molecules first absorb at the hydrophobic units at low surfactant concentrations to form hydrophobic clusters. With continuously increasing concentration of SDS, the microdomain is reinforced by mixed micelles formed by hydrophobic groups and surfactant expanding the clusters size, resulting in the increase in viscosity. Near the CMC of SDS, significantly cooperative interaction between the copolymer chain and surfactant molecule is constructed due to mixed micelles serving as junction points for transitional network. And the maximum value of viscosity for copolymer 0.75DM12.8 is observed (2 times that of value in SDS-free solution). Beyond the CMC of SDS, hydrophobic segments of copolymer chains are dissolved into micelles formed by much numbers of surfactant molecules, disrupting junction points, resulting in the decrease of viscosity.Figure 12
Variation of apparent viscosity of as a function of SDS concentration for copolymers 0.75DM12.8 and 0.75DM9.3 at 0.5 g dL−1 (shear rate 7.34 s−1, T
=
25°C).It is noteworthy that the increasing ofN
H shifts the maximum viscosity toward the higher SDS concentration and more remarkable viscosity is observed. For copolymer 0.75DM12.8 the maximum viscosity, 1750 mPa·s, is exhibited at the SDS concentration of 8.5 mM compared to 1530 mPa·s for 0.75DM9.3 at the SDS concentration of 6.7 mM. Cooperatively, as the SDS concentration is raised above CMC, a large viscosity for 0.75DM12.8 is still observed. Two points can be used to interpret that the viscosity for 0.75DM12.8 in the presence of surfactant is much higher than that of value for 0.75DM9.3, that is, hydrophobic association and ionic attraction. Hydrophobic associations reduce the contacts of the hydrophobic segments of polymer chain with water leading to lowering the free energy of the system [3]. It is discussed above that the longer the hydrophobic microblock, the stronger the intermolecular association, and thus, less free energy of the system. Ionic attraction between SDS molecules and copolymer chains is obviously enhanced with prolonging the length of cationic hydrophobic groups per chain. In the case of cationic, nonionic, and zwitterionic surfactants, whether the length of hydrophobic microblock plays a role in the rheological behavior should be further studied.


## 3.4.1. Influence of Salt

The apparent viscosity as a function of NaCl concentration for 0.75DM12.8 and PAM at polymer concentration of 0.15 g dL−1 and 0.75 g dL−1 was represented in Figure 11. The values of the curves are expressed in terms of a relative viscosity, that is, the ratio of the viscosity in the presence of salt to the viscosity in salt-free solution.Figure 11
Relative variation of the viscosity with NaCl concentration for copolymer 0.75DM12.8 and PAM at two different concentrations (shear rate 7.34 s−1, T
=
25°C).The behavior of PAM exhibits almost the same trend at two different concentrations in the whole salt concentration range. At low salt concentration, the viscosity decreases smoothly upon the increase in salt content, and above the certain salt concentration, relative constant apparent viscosity is exhibited. For PAM, increasing the concentration slightly shifts the constant apparent viscosity towards the lower salt concentration. At the highest salt level, the viscosity of PAM at 0.75 g dL−1 is about 85% of its initial value in pure water. This can be explained that the polarity of solvent is changed in the presence of salt, resulting in the oppression of macromolecular chain accompanied by slight decrease of the apparent viscosity. However, for copolymer 0.75DM12.8 in salt solution, the variation of the viscosity depends significantly on the polymer concentration. For copolymer 0.75DM12.8 dilute solution (0.15 g dL−1), slightly higher than critical concentration (0.11 g dL−1), apparent viscosity increases with increasing of NaCl concentration. At NaCl concentration of 0.80 g dL−1, apparent viscosity reaches the maximum value (3 times that value in salt free solution), subsequently decreases steeply, and it finally becomes close to that of PAM. Solution polarity induced by the presence of NaCl enhances intermolecular interaction between hydrophobic groups of the chains and the good salt-thickening behavior is observed. On the other hand, with further increasing the salt concentration, the hydrophobic microstructures turn compact and isolated macromolecules resulting in the disappearance of intermolecular interaction and the decrease of the apparent viscosity. This behavior supports the conclusion that, below the chain overlap regime, the thickening efficiency arises from the intermolecular interaction between the hydrophobic segments of the chains. Once the transient network is disrupted into small clusters, the viscosity is significantly lowered. Conversely, over the chain overlap regime (0.75 g dL−1), apparent viscosity of copolymer 0.75DM12.7 almost keeps constant after attaining the maximum value (3.5 times that value in salt-free solution). This can be ascribed to the high degree of chain overlap and even entanglement at this concentration prevents the network from disruption. For copolymer 0.75DM12.7, when the salt concentration is above 10 g dL−1, either clouding or separation is observed.


## 3.4.2. Influence of Surfactant

Figure12 depicts the dependence of the variation viscosity for copolymers 0.75DM12.7 and 0.75DM9.3 on the SDS concentration. SDS and hydrophobic monomer DMDCC bear the opposite charges; thus, interaction between copolymer chain and SDS occurs. Surfactant molecules first absorb at the hydrophobic units at low surfactant concentrations to form hydrophobic clusters. With continuously increasing concentration of SDS, the microdomain is reinforced by mixed micelles formed by hydrophobic groups and surfactant expanding the clusters size, resulting in the increase in viscosity. Near the CMC of SDS, significantly cooperative interaction between the copolymer chain and surfactant molecule is constructed due to mixed micelles serving as junction points for transitional network. And the maximum value of viscosity for copolymer 0.75DM12.8 is observed (2 times that of value in SDS-free solution). Beyond the CMC of SDS, hydrophobic segments of copolymer chains are dissolved into micelles formed by much numbers of surfactant molecules, disrupting junction points, resulting in the decrease of viscosity.Figure 12
Variation of apparent viscosity of as a function of SDS concentration for copolymers 0.75DM12.8 and 0.75DM9.3 at 0.5 g dL−1 (shear rate 7.34 s−1, T
=
25°C).It is noteworthy that the increasing ofN
H shifts the maximum viscosity toward the higher SDS concentration and more remarkable viscosity is observed. For copolymer 0.75DM12.8 the maximum viscosity, 1750 mPa·s, is exhibited at the SDS concentration of 8.5 mM compared to 1530 mPa·s for 0.75DM9.3 at the SDS concentration of 6.7 mM. Cooperatively, as the SDS concentration is raised above CMC, a large viscosity for 0.75DM12.8 is still observed. Two points can be used to interpret that the viscosity for 0.75DM12.8 in the presence of surfactant is much higher than that of value for 0.75DM9.3, that is, hydrophobic association and ionic attraction. Hydrophobic associations reduce the contacts of the hydrophobic segments of polymer chain with water leading to lowering the free energy of the system [3]. It is discussed above that the longer the hydrophobic microblock, the stronger the intermolecular association, and thus, less free energy of the system. Ionic attraction between SDS molecules and copolymer chains is obviously enhanced with prolonging the length of cationic hydrophobic groups per chain. In the case of cationic, nonionic, and zwitterionic surfactants, whether the length of hydrophobic microblock plays a role in the rheological behavior should be further studied.


## 3.5. Fluorescence Investigation

The intensity ratioI
3
/
I
1 of the third (385 nm) to the first (375 nm) vibronic peak in the fluorescence emission spectrum of pyrene is sensitive to the polarity of the local microenvironment of the pyrene probe [12, 14]. This ratio is directly proportional to polarity. Thus, the values of I
3
/
I
1 provide significant evidence for the formation of hydrophobic microdomains at salt concentrations and the development of bridge points or mixed micelles when surfactant is added. Figure 13 depicts the fluorescence spectra of 0.2 g dL−1 0.75DM12.8 for pyrene at different conditions. The I
3
/
I
1 value is 0.706 in aqueous solution, which increases to 0.835 in 8 mM SDS solution where the pyrene probe is located in the mixed micelles constructed by surfactant molecules and hydrophobic segments of 0.75DM12.8. Additionally, the I
3
/
I
1 value in 5.85 g dL−1 solution is 0.883 higher than that in aqueous solution, indicating that the hydrophobic microdomains became more compact in the high salt concentration. These results agree favorably with that obtained from viscosity.Figure 13
Fluorescence spectra of pyrene in 0.25 g dL−1 0.75DM12.8 solutions at different conditions.


## 3.6. Morphology of Networks

The microscopic structures of poly(AM/DMDCC) at different experimental conditions are observed through ESEM at room temperature and the morphological images are shown in Figure14. In extremely dilute solution of copolymer 0.5DM12.7, intramolecular associations of hydrophobic segments compact polymers chains and an irregular microstructure is observed, which, of course, lowers viscosity. At the critical association concentration shown in Figure 14(b), three-dimensional network formed by intermolecular association results in a regular morphology and dramatically enhances solution viscosity. These three-dimensional networks are disrupted in the presence of higher concentration salt and broke into small clusters. As shown in Figure 14(c), for copolymer 0.75DM12.8, morphology of salt aggregation is observed due to high concentration of salt. At higher polymer concentration, as exhibited in Figure 14(d), high degree of chain entanglement protects three-dimensional networks from disruption and keeps viscosity relatively stable. Adding SDS, a significantly cooperative interaction between the copolymer chain and surfactant leads to more regular microstructures than these of copolymer solution. Moreover, for copolymer 0.75DM12.8 with the longest N
H, at the CMC of SDS, both intermolecular hydrophobic interactions and ionic attractions are cooperative to promote the aggregation behavior of copolymer; thus, the most regular microstructures are observed.ESEM images of poly(AM/DMDCC) at different experimental conditions; (a) 0.5DM12.7 with 0.075 g dL−1; (b) 0.5DM12.7 with 0.15 g dL−1; (c) 0.75DM12.8 with 0.15 g dL−1 in 2 g dL−1 salt solution; (d) 0.75DM12.8 with 0.75 g dL−1 in 2 g dL−1 salt solution; (e) 0.5DM12.7 with 0.5 g dL−1 in 8 mM SDS solution; (f) 0.75DM12.8 with 0.5 g dL−1 in 8 mM SDS solution.
(a)
(b)
(c)
(d)
(e)
(f)


## 4. Conclusion

A novel cationic surfmer, methacryloxyethyl-dimethyl cetyl ammonium chloride (DMDCC), was synthesized in the experiment. For DMDCC-SDS binary mixed surfactants system, conductivity measurement and a steady-state fluorescence technique indicated that synergetic mixed micelles were obtained due to strong net attraction between cationic (DMDCC) and anionic (SDS) surfactants, which dramatically reduce the CMC and keep the Nagg almost stable. Therefore, this new method could not only reasonably adjust the length of the hydrophobic microblock (N
H) but also sharply reduce the amount of SDS. Utilizing a DMDCC-SDS mixed micellar copolymerization method, a series of water-soluble associative copolymers with acrylamide (AM) and DMDCC are synthesized.The incorporation of hydrophobic segments into polymer chains induces a strong enhancement of apparent viscosity. Rheological measurements including steady flow and linear viscoelasticity experiments are used to study the association process in the semidilute regime of copolymers. In the whole shear rate range of steady flow experiments, a shear thickening behavior of copolymers is exhibited and followed by shear thinning. Increasing hydrophobic microblock enhances the degree of association and results in shear thickening behavior towards lower share rate. The presence of the hydrophobic group into macromolecular chain increased both storage (G
′) and loss (G
′) modulus. At low frequencies, solution behaves as a Newtonian liquid and, at high frequencies, originating from strong intermolecular association, solution exhibits as an elastic solid with storage modulus higher than loss modulus. Relaxation time (t
c) is also calculated to interpret the degree of intermolecular association formed by hydrophobic segments. And the results indicate that both the hydrophobe content and especially the length of the hydrophobic microblock are found to be the two main factors inducing an increase in the final relaxation time.In the vicinity of the critical associative concentration, the presence of salt influences the dynamics transformation between intramolecular and intermolecular junctions resulting in changing the solution viscosity. However, at higher copolymer concentration, governed by chains entanglement and intermolecular associations, viscosity enhancement is observed in the whole salt concentration range. Apparent viscosity measurement performed on the copolymer indicates that both ionic attraction and intermolecular interactions play a great role. At the CMC of SDS, the formation of mixed micelles between the copolymer chain and surfactant which serve as junction bridges for transitional network remarkably enhances the viscosity. What is more, the microscopic structures for copolymers at different experimental conditions conducted by ESEM confirm the results discussed above.



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*Source: 875637-2014-05-15.xml*