Poly(N,N-bis(2-methoxyethyl)acrylamide), a thermoresponsive non-ionic polymer combining the amide and the ethyleneglycolether motifs

Poly(N,N-bis(2-methoxyethyl)acrylamide) (PbMOEAm) featuring two classical chemical motifs from non-ionic water-soluble polymers, namely, the amide and ethyleneglycolether moieties, was synthesized by reversible addition fragmentation transfer (RAFT) polymerization. This tertiary polyacrylamide is thermoresponsive exhibiting a lower critical solution temperature (LCST)–type phase transition. A series of homo- and block copolymers with varying molar masses but low dispersities and different end groups were prepared. Their thermoresponsive behavior in aqueous solution was analyzed via turbidimetry and dynamic light scattering (DLS). The cloud points (CP) increased with increasing molar masses, converging to 46 °C for 1 wt% solutions. This rise is attributed to the polymers’ hydrophobic end groups incorporated via the RAFT agents. When a surfactant-like strongly hydrophobic end group was attached using a functional RAFT agent, CP was lowered to 42 °C, i.e., closer to human body temperature. Also, the effect of added salts, in particular, the role of the Hofmeister series, on the phase transition of PbMOEAm was investigated, exemplified for the kosmotropic fluoride, intermediate chloride, and chaotropic thiocyanate anions. A pronounced shift of the cloud point of about 10 °C to lower or higher temperatures was observed for 0.2 M fluoride and thiocyanate, respectively. When PbMOEAm was attached to a long hydrophilic block of poly(N,N-dimethylacrylamide) (PDMAm), the cloud points of these block copolymers were strongly shifted towards higher temperatures. While no phase transition was observed for PDMAm-b-pbMOEAm with short thermoresponsive blocks, block copolymers with about equally sized PbMOEAm and PDMAm blocks underwent the coil-to-globule transition around 60 °C.


Introduction
Many non-ionic polymers in aqueous solution are thermoresponsive featuring a lower critical solution temperature (LCST), i.e., they are water-soluble or highly swollen below a characteristic transition temperature but are water-insoluble and collapsed above. Apart from the basic scientific interest in this behavior, its use for a plethora of possible "smart" applications has been discussed [1][2][3]. While many different polymer chemistries are known to exhibit LCST behavior in aqueous media [4,5], two major chemical motifs prevail. Water solubility is implemented either via amide moieties or via ethyleneglycol ether groups, as exemplified by the two arguably most studied thermoresponsive polymer systems, namely, poly(N-isopropyl acrylamide) (PNIPAm) [6] and polymers based on poly (ethyleneglycol) (PEG) [7,8]. The specific LCST is mainly determined by the polymer composition, i.e., in the case of homopolymers, by the chemical structure of the underlying monomer. Typically, small chemical changes of the monomer's molecular structure result in big changes of the LCST [4], whereat in particular for low-to-moderate molar masses, the precise value can be adjusted to a certain extent by incorporating functional end groups [9][10][11] or by the precise molar mass itself [4]. A more flexible control over the LCST value is achieved by using statistical copolymers. They can be either obtained by direct copolymerization of appropriate monomers in suitable amounts [12][13][14][15][16][17] or by partial chemical modification [18][19][20][21], and enable the fine-tuning of the LCST value. Yet, except for the rare case of ideal azeotropic copolymerizations (i.e., all copolymerization reactivity ratios are close to unity) [22][23][24][25][26][27], this gives rise to product mixtures that risk blurring the transition. In any case, the chemical complexity of such thermoresponsive copolymers is increased, which tends to render their chemical analysis as well as the interpretation of experimental findings complicated. This is particularly problematic when additional structural features are to be implemented into thermoresponsive polymers, such as blocky structures or complex functional moieties [28][29][30][31][32]. Therefore, there is a continuous quest for new monomers that yield thermoresponsive homopolymers.

Synthesis of 4-(dodecylcarbamoyl)benzyl-3-(trimethylsilyl)propyl) carbonotrithioate (4dBtmsPTC, 4)
S-(4-(Trimethylsilyl)propyl) ethanethiol (8.22 g, 55.4 mol) and CS 2 (3.35 ml, 4.22 g, 55.4 mmol, 1.00 eq.) were dissolved in dry CH 2 Cl 2 (20 mL) and stirred at room temperature. Triethylamine (7.90 mL, 5.77 g, 57.1 mmol, 1.03 eq.) was added dropwise, while keeping the reaction at room temperature. The orange solution formed was stirred for 30 min. 4-Chloromethyl-N-dodecylbenzamide (17.79 g, 52.64 mmol, 0.95 eq.) was slowly added, and the reaction was stirred overnight. After dilution with more CH 2 Cl 2 (40 mL), the solution was washed with water (3 × 100 mL), the collected aqueous phases re-extracted with CH 2 Cl 2 (20 mL), and the combined organic phases finally washed with brine and dried over MgSO 4 . The organic solvent was removed under reduced pressure, and the raw product purified by two subsequent column chromatographies on silica gel using petrol ether:ethyl acetate (first with gradient: 10:1 (v/v) increasing to 10:4 (v/v); second with a fixed ratio of 20:1 (v/v)). Yield: 9.67 g, 18.4 mmol (39%), yellow wax In a typical procedure, monomer 1 (1.00 g, 5.34 mmol, 25 eq.) and CTA 3 (51.19 mg, 0.2112 mmol) were dissolved in benzene (2.00 mL) at ambient temperature. 2.57 mL of a stock solution of V-40 in benzene (2.00 mg mL −1 ) equivalent to 0.0212 mmol of initiator was added, and the homogenous reaction mixture were purged with N 2 for 45 min. The mixture was immersed into an oil bath preheated to 90°C and stirred. After 5 h, the polymerization was quenched by opening the flask to the air and cooling the mixture with an isopropanol/ dry ice bath. After warming to room temperature, 5 mL of THF were added, and the polymer was isolated by precipitation into diethylether. After drying in the vacuum oven (40°C, 1 mbar), the polymer was dissolved in water and lyophilized to obtain a viscous, yellowish mass. Yield: 0.82 g (78%) Various homopolymer samples were prepared by varying the relative amounts of monomer 1, CTA, and initiator V-40 (series P1), or by substituting CTA 3 by CTA 4 (series P1/ HE), while maintaining throughout a 10:1 M ratio of CTA:initiator. Homopolymerization of N,N-dimethylacrylamide (P2/HE) Monomer 2 (17.5 mL, 16.9 g, 0.170 mol, 202 eq.), CTA 4 (442.6 mg, 0.8415 mmol, 1 eq.), and V-40 (20.6 mg, 0.0843 mmol, 0.1 eq.) in benzene (76 mL) were purged with N 2 for 45 min. The mixture was placed into a preheated oil bath at 90°C and stirred for 3 h. Then, the polymerization was quenched by opening the flask to the air and rapid cooling. The polymer was isolated and purified by precipitating twice into diethylether. The collected polymer P2/HE was dried in the vacuum oven, dissolved in water, and lyophilized. Yield: 10.98 g (63%) hygroscopic yellow powder

Synthesis of block copolymers P2-1/HE
In a typical procedure, monomer 1 (1.02 g, 5.44 mmol, 100 eq.) and macroCTA P2/HE (0.87 g, 0.054 mmol) were dissolved in benzene (17.0 mL) at ambient temperature. 0.67 mL of a stock solution of V-40 in benzene (2 mg mL −1 ) equivalent to 0.0055 mmol were added. The solution was purged with N 2 for 45 min and placed into a preheated oil bath with a temperature of 90°C. After stirring for 3 h, the reaction was stopped by opening the flask to the air and cooling the flask with liquid nitrogen. The polymer P2-1b/HE was isolated and purified by twice repeated precipitations into diethylether. The polymer was dried in the vacuum oven, dissolved in water, and lyophilized. Yield: 1.34 g (71%), hygroscopic yellow powder

Methods and instrumentation
Elemental analysis was performed with a Vario ELIII microanalyzer (Elentar Analysensysteme, Hanau, Germany). Refractive indexes were determined with a NAR-3T refractometer (ATAGO CO., LTD., Tokyo, Japan) equipped with a DTM-3 thermostat. NMR spectra were recorded using a Bruker Avance 300 NMR spectrometer operating at 300 MHz for 1 H measurements and 75 MHz for 13 C measurements. Chemical shifts δ are given in ppm referring to the respective solvent peaks at δ ( 1 H) 7.26 ppm and δ ( 13 C) 77.16 ppm for CDCl 3 , and at δ (1H) 4.79 ppm for D 2 O. Fourier-transform infrared spectroscopy (FTIR) spectra were recorded using a Nicolet Avatar 370 FTIR spectrometer (Thermo Fisher Scientific) equipped with an ATR Smart Performer element and AMTIR crystal.
Polymers were analyzed by size exclusion chromatography (SEC) in NMP + 0.1% LiBr with simultaneous UV and RI detection at room temperature (flow rate 0.5 mL min −1 ). The stationary phase used was a 300 × 8 mm 2 PSS GRAM linear M column (7 μm particle size). Samples were filtered through 0.45-μm filters and the injected volume was 100 μL.
Narrowly distributed polystyrene standards (PSS, Mainz, Germany) were used for calibration.
UV/Vis spectra were recorded on a PerkinElmer Lambda 25 UVVis Spectrometer, using quartz sample cells with 1 cm path length. Number average molar masses M n UV were calculated by end group analysis, using the extinction E at 309 nm of the π-π* transition of the trithiocarbonate chromophore in methanol. Values were calculated according to M n is the concentration of the polymer in solution, and d (cm) is the optical path length. The molar extinction coefficient ε of the trithiocarbonate chromophore was assumed to be 15,800 L mol −1 cm −1 at 309 nm in methanol, due to the structural similarity of the polymer bound trithiocarbonate end groups with the references 2-(((butylthio)carbonothioyl)thio) propanoic acid and N,N-dimethyl-2-(((butylth io)carbonothioyl)thio) propionamide [55].
Thermogravimetric analysis (TGA) was conducted under N 2 purged atmosphere using an apparatus SDTA851e (Mettler-Toledo, Giessen, Germany), in the temperature range from 25 to 900°C with a heating rate of 10 K min −1 . Differential scanning calorimetry (DSC) was performed with an apparatus DSC822e (Mettler-Toledo, Giessen, Germany), applying heating and cooling rates of 10 K min −1 for the first and second, and 30 K min −1 for the third and fourth heating and cooling cycles. Glass transition temperatures T g were taken from the second heating cycle that used a heating rate of 10 K min −1 via the midpoint method [56].
Dynamic light scattering (DLS) was carried out with a high-performance particle sizer (HPPS-5001, Malvern Instrument, Malvern, UK) using a He-Ne laser beam and a thermoelectric Peltier element to control the temperature of the sample cell. The backscattering mode was used at a scattering angle of Θ = 173°. Samples were prepared by dilution with Millipore water to the desired concentration, and measured in heating runs by raising the temperature in steps of 1°C equilibrating the sample for 120 s prior to each measurement. Temperature-dependent turbidimetry measurements were performed with a Cary 5000 (Varian) spectrometer with heating and cooling rates of 0.5 K min −1 . Temperatures are precise within 0.5 K.

Results and discussion
Monomer N,N-bis(2-methoxyethyl)acrylamide 1 was synthesized by the straightforward reaction of the amine with acryloylchloride, adapting previous procedures [33,47], and the so far scarce molecular analytical data available were completed. Figure 2 displays the 1 H and 13 C NMR spectra in CDCl 3 . The duplication of methylene signal characteristic for the 2-methyoxyethyl substituents on the amide nitrogen between 3.4 and 3.7 ppm is caused by the ambient temperature still relatively slow exchange (compared with the NMR frequency) between the trans-and cis-positions of the amide substituents, so that the respective signal groups do not completely coalesce.
Initially, monomer 1 was homopolymerized by radical polymerization employing the RAFT method to control molar masses and minimize the polymers' dispersities, Ð. For preparing a series of increasing molar masses of P1, the established RAFT agent S-benzyl-S′-propyl trithiocarbonate 3 was employed as CTA [52,53]. The polymerization recipes are compiled in Table 1, and the key characteristics of the obtained polymers in Table 2. The resulting general structure is displayed in Fig. 1, and a typical 1 H NMR spectrum in Fig. 2(c). In analogy to statistical copolymers of 2methoxyethylacrylate and N,N-dimethylacrylamide 2 [14], all polymers P1 were soluble in a large variety of solvents of strongly differing polarities, such as cold water, methanol, ethanol, trifluoroethanol, hexafluoroisopropanol, acetonitrile, N-methylpyrrolidone (NMP), dimethylsulfoxide (DMSO), ethyl acetate, acetone, α,α,α-trifluorotoluene, dioxane, tetrahydrofuran (THF), chloroform, dichloromethane, and benzene. Only diethylether and plain hydrocarbons such as pentane and hexane were found to be nonsolvents.
Due to the low molar mass of the sample P1b shown (Fig.  2(c)), characteristic signals of both end groups can be easily distinguished in the spectrum, namely, of the phenyl moiety originating from the R-group of CTA 3 at 7.1 to 7.3 ppm, and of the methyl moiety of the n-propyl residue originating from the Z-group at about 0.9 ppm. These signals enable the calculation of the number average molar mass M n using either of the two end groups (denoted M n NMR-R and M n NMR-Z ). However, the accuracy inevitably decreases rapidly with increasing molar masses. Additionally, the thiocarbonyl moiety of the Zgroup is a strong UV-chromophore with an absorbance maximum in the range of 305-310 nm and an extinction coefficient ε in the order of 10 4 L mol −1 cm −1 . This allows for a rather sensitive determination of the polymer's Z-group content even for high molar masses when the value of ε is known, and, thus, also to derive a number average molar mass value, denoted M n UV [55]. Moreover, assuming ideal conditions for the RAFT polymerization process, the theoretically expected number average molar mass M n theo can be calculated from the molar ratio of the monomer to the RAFT agent employed that is corrected by the monomer conversion. Furthermore, size exclusion chromatography (SEC) was used to analyze the molar mass distribution, and to calculate therefrom apparent number average molar masses M n app (calibrated to polystyrene) and the dispersities Ð. Altogether, the comparison of the various analytical molar mass data allows judging the controlled character of the polymerization, and, in particular, to estimate the degree of Z-group fidelity, i.e., the percentage of the polymer chains that bear an active end group. This is a crucial information for successful further chain extension as in the synthesis of block copolymers. Analyzing the data for P1a-P1f, we note in general relatively low dispersities Ð of 1.2-1.3, and good agreement of M n theo and M n NMR-R . This suggests that the RAFT polymerization of 1 is well controlled. We note that the M n app values derived from SEC systematically underestimate the molar masses of the P1 samples, i.e., the calibration using polystyrene standards is not optimal. Furthermore, we find that the M n NMR-Z and M n UV values agree reasonably well with the values of M n theo and M n NMR-R , indicating good preservation of the RAFT-active trithiocarbonate end group. Still, it appears that the M n NMR-Z and in particular the M n UV values tend to become higher than the M n NMR-R values with increasing molar masses, pointing to an increasing loss of active end groups. To a certain extent, such a loss is inevitable due to the inherent RAFT mechanism [57]. Moreover, the ether functions of 1 that are prone to radical side reactions via hydrogen abstraction might contribute to the loss. In any case, if molar masses up to 20,000 are aspired, the data demonstrate that RAFT polymerization of 1 proceeds smoothly. Even for higher molar masses, the extent of polymerization control is still reasonably good.
Additionally, we undertook preliminary experiments exploring the use of functionalized RAFT agent 4 for the polymerization of 1, in the perspective of synthesizing thermoresponsive polymeric surfactants. The mixed aliphatic-aromatic N-dodecylbenzamide moiety of the Rgroup of 4 will confer the needed segmental hydrophobic  character to polymers of structure P1/HE (see Fig. 1). Importantly, the use of CTA 4 albeit somewhat cumbersome to synthesize attaches the hydrophobic end groups by hydrolytically inert C-C bonds to such polymeric surfactants. This is an important advantage over most reported hydrophobized RAFT agents, where the hydrophobe is placed in the socalled Z-group that is inherently sensitive to hydrolysis [58][59][60][61][62][63][64]. Moreover, the particular choice of the various building blocks of CTA 4 was aimed at supporting polymer end group analysis by 1 H NMR, as they simplify the identification and quantification of both the R-and Z-groups attached to the polymers in the spectra [65][66][67]. For instance, the signals of the aryl protons in ortho position to the carboxyl moiety of the R-group appear close to 8 ppm, while the signal of the trimethylsilyl groups of the Z-group is positioned close to 0 ppm, i.e., in regions that are devoid of signals for most polymers and solvents used in NMR analysis. This allows not only the determination of the true number average molar masses M n but enables also the first-hand estimation of the RAFT-active end group fidelity by comparing the integrated signals specific to the R-and Z-groups. Both informations are generally difficult to obtain, especially in the case of amphiphilic polymers which, e.g., often tend to interact either with SEC column material, and/or to associate in the eluent. In a second stage, we explored the use of monomer 1 for constructing thermoresponsive block copolymers. For this purpose, we first polymerized monomer 2, N,Ndimethylacrylamide (DMAm), to produce a polymer that is water-soluble over the full temperature range between 0 and 100°C [23,68], using the RAFT agent 4. Subsequently, we employed this homopolymer P2/HE as macroCTA for the chain extension with monomer 1. This yields block copolymers with a permanently hydrophobic end group at one terminus of the polymer chain (due to the use of CTA 4), and a hydrophilic-to-hydrophobic reversibly "switchable" end block made of the polymer of 1 on the opposite terminus (see Fig. 1). This design results in a polymer surfactant architecture which can be thermally switched between the structure of classical polymeric surfactants with one hydrophobic end group (similar to fatty alcohol ethoxylates) and the one of associative telechelics that dispose of two, here nonsymmetrical, hydrophobic end groups [69]. Key molecular data of the various polymers prepared with CTA 4 are listed in Table 2. For homopolymers P1/HE and P2/HE, we note good agreement not only between the M n theo and M n NMR-R values, but also with the respective values M n NMR-Z . This finding, together with the low dispersities Ð of 1.2 for P2/HE, suggests that the RAFT polymerization using CTA 4 is also well controlled. Still, notwithstanding the good agreement of the values for M n theo , M n NMR-R and M n NMR-Z , sample P1/HE presents a relatively high dispersity of 1.4-1.5 in the SEC analysis. Also, the M n app value even more underestimates the true molar mass of P1/HE than we noted for the series of samples P1a-P1f prepared using CTA 3. These apparently inconsistent findings might be due to some weak interaction of the end-functionalized polymer P1/HE with the column material, thus provoking a tailing of the elugram towards longer elution times, which consequently reduces M n app but increases Ð. In any case, the analytical data show that the trithiocarbonate group is largely preserved, and sample P2/HE represented a good macroCTA for the chain extension with monomer 1. The data in Tables 1 and 2 also demonstrate the successful chain extension up to high conversions to produce the block copolymers P2-1a/HE and P2-1b/HE. Still, the analytical data indicate that the RAFT-active trithiocarbonate group was largely lost at the end of the chain extension step, despite the low values of about 1.2 for Ð.
Thermal analysis showed that the polymers were thermally stable up to at least 200°C according to thermogravimetric analysis TGA (Fig. 3(a)), when presumably the decomposition of the trithiocarbonate end groups sets in [70,71]. Notable mass loss took only place at temperatures beyond 300°C. Differential scanning calorimetry showed (compared with most reported polyacrylamides) a rather low glass transition for polymers P1 (Fig. 3(b)), which approaches about 10°C for high molar masses (Fig. 4), indicating an intramolecular plasticizer effect of the methoxyethyl groups. This value compares surprisingly well with the reported glass transition of about 5°C for the 1:2 statistical copolymer of dimethylacrylamide 2 and 2-methoxyethylacrylate [14]. In contrast, sample P2/HE displayed a glass transition at about 115-120°C, in agreement with the literature on P2 [14,72,73]. Polymers P1/HE and P2/HE showed an additional small transition at about 40°C, which is attributed to the alkyl chain terminus (Fig. 3(c)). Noteworthy, the block copolymers P2-1a/HE (T g = 80°C) and P2-1b/HE (T g = 58°C) (Fig. 3(d)) did only show one glass transition, which is located between those of the respective homopolymers and decreases with an increasing share of P1 in the block copolymers. This suggests that the two different polyacrylamide blocks are compatible in the bulk phase.

Behavior in aqueous solution
The thermoresponsive behavior of the polymers P1 in aqueous solution was investigated by temperature-dependent turbidimetry (see Fig. 5).
The transmission of the solutions showed a sharp transition from clear to opaque for the heating, and vice versa for the cooling runs (Fig. 5(a)). These transitions were fully reversible. The hysteresis between cooling and heating runs was very small indicating a relatively quick rehydration and resolubilization of the collapsed polymer coils. This behavior is similar to the one of PDEAm [74][75][76], but contrasts with the one of PNIPAm [74,76,77]. The different transition behaviors were attributed to the N-H group of the secondary amide moiety specific for PNIPAm, which is assumed to enable interchain hydrogen bonds that act as "cross-linking points" inside the swollen polymer chain and delay the diffusion of water into the dense aggregates [74][75][76][77], but other kinetic effects seem also responsible [78][79][80]. Furthermore, the two methoxyethyl groups attached to the amide moiety of P1 might facilitate the diffusion of water because they provide additional hydrophilicity in analogy to poly((meth)acrylate)s that bear oligo (ethylene oxide) side chains [24,46]. Up to 10 g L −1 , the cloud points shift towards lower temperatures with increasing concentration. Except for the oligomeric sample of P1a with a molar mass of 1.9 kg mol −1 , the phase transitions of all samples slowly approached a temperature minimum with increasing concentration (Fig. 5(b)). To investigate the influence of the molar mass, homopolymers P1a-f were synthesized with molar masses varying from about 2 to 100 kg mol −1 using CTA 3. This CTA was chosen to introduce only rather small propyl and benzyl end groups into the polymers, in order to minimize end group effects on the LCST. Figure 5 (b) illustrates that with increasing molar mass, the cloud points are initially increasing. Only when the molar mass becomes sufficiently high at around 10 kg mol −1 (P1c), the cloud point at 10 g L −1 seems to approach a maximum temperature, reaching a plateau value of around 46°C. This trend does not follow the classical Flory-Huggins theory, according to which polymers become less soluble with growing molar mass as the combinatorial entropy term of mixing becomes less favorable [81,82]. We explain this behavior by the sensitivity of the coil-to-globule transition of P1 to the presence of even small hydrophobic end groups, as known for other thermoresponsive polyacrylamides as, e.g., PNIPAm [9,82] or poly(N-acryloyl pyrrolidine) PNAP [83]. With increasing length of the polymer chain, the polymer's inherent hydrophilicity can increasingly outweigh the hydrophobic contribution of the end groups, so that the cloud point approaches an upper limiting value.
To gain a better understanding of how hydrophobic end groups influence the phase behavior of P1, we studied also the homopolymer P1/HE bearing a marked hydrophobic end group incorporating the hydrophobic dodecyl chain. Having a molar mass of around 30 kg mol −1 , P1/HE is well comparable to P1d, their main difference being the hydrophobicity of the end groups. For P1/HE, the cloud points are notably lowered to the temperature of about 42°C compared with the cloud point of P1d of around 46°C. This indicates a higher solubility for the polymer with the less hydrophobic end groups. This marked influence of the hydrophobic end group is in We note that the limiting cloud point values of our samples approached the range between 42 and 46°C with increasing molar masses, which is above the originally reported value of 41.5°C by Ito [33], but lower than the values of 49.5°C reported by Yamazaki et al. [47] and of 58.4°C reported by Hidaka et al. [36]. These differences might be due to differing molar masses, dispersities, and/or end groups of these samples, which were synthesized by classical free radical polymerization. Also, different tacticities might be responsible taking the reports for other polyacrylamides including PDEAm into account [42,[84][85][86]. However, the scarce analytical data reported preclude from a more thorough discussion.
In most cases, thermoresponsive polymers are not employed in pure water, but their applications include solution additives such as salts. In addition to the effect of ionic strength, ion specific effects on the LCST have been reported, which follow the so-called Hofmeister series [87]. This series empirically describes the ability of salts to precipitate proteins from aqueous solution. This phenomenon is more pronounced for anions than for cations following the typical order: The anions on the left side of the series are referred to as kosmotropes, originally supposed to "structure" bulk water, while those on the right side are called chaotropes originally supposed to "break" bulk water structure. Several ionic properties such as size, polarizability, hydration energetics, and the partition coefficient influence their precipitation. The presence of such anions can also influence the phase transition behavior of thermoresponsive polymers such as PNIPAm [42,[88][89][90][91] or PDEAm [42,92]. Consequently, we explored the effect of representative sodium salts on the cloud point of P1 using sample P1f via DLS, employing the fluoride F − that is regarded to be highly kosmotropic, the thiocyanate SCN − that is regarded to be highly chaotropic, and the chloride Cl − designating the dividing line between those two types (Fig. 6).
At temperatures well below the phase transition, P1f has a hydrodynamic diameter of~25 nm which is comparable with the values reported for single PDEAM chains of similar molar mass [93]. Within the precision of the measurement, the hydrodynamic diameter seems to be unchanged upon the addition of the salts. In pure water, the cloud point of P1f is 45°C. When NaCl is added, the cloud point shifts slightly towards lower temperatures. The observed rather weak salting-out effect of Cl − was similar not only to other polyacrylamides such as PNIPAm [88,94], PDEAm [42,92], or PNAP [83] but also  to polymethacrylates bearing oligo (ethyleneglycolether) side chains [83]. The ability to lower the phase transition temperature becomes more pronounced when NaF is added. The strongly hydrated F − induces a marked salting-out effect, decreasing the cloud point of P1f to 34°C. Contrariwise, the addition of NaSCN raises the cloud point to 52°C, clearly showing the salting-in effect of the weakly hydrated and highly polarizable SCN − anion. The kosmotropic and chaotropic nature of F − and SCN − , respectively, with the corresponding salting-out and salting-in effects was also demonstrated on low dispersity PNIPAm of similar [94] and other molar masses [88,95]. However, the influence on the phase transition temperature of PNIPAm was less pronounced than for P1f revealing the higher ion specific response of polymers of bMOEAm 1 to such salts.
It is interesting to note that P1f produced rather long-lived colloidal aggregates in pure aqueous solution above the cloud point. Such aggregates are often referred to as mesoglobules, the precise reasons for their formation still being under discussion [4,6,96]. Such a behavior seems typical for PNIPAm in dilute aqueous solution, for which it has been intensely studied, but has been also described occasionally for other non-ionic thermoresponsive polymers [4,6]. Mesoglobules were reported to be destabilized when inorganic salts, typically chlorides, were added, resulting in macroscopic phase separation [6]. Figure 6 shows that this was also the case for P1f in the presence of NaCl or NaF, but not when adding NaSCN. On the basis of our limited experiments, it could only be speculated whether and how the sensitivity of mesoglobules to electrolytes is correlated to the kosmotropic and chaotropic nature of their anions, but this may be a point worth to be addressed in future studies for refining the understanding of the mesoglobule phenomenon.
In addition to the homopolymers, we explored the thermoresponsive behavior of the block copolymers P2-1a/ HE and P2-1b/HE as potentially "smart" surfactants by DLS and turbidimetry (Fig. 7).
Both block copolymers have a hydrodynamic diameter of 10 nm at temperatures well below the phase transition. This is similar to homopolymer samples P1c-d with comparable chain lengths as the thermoresponsive block of the copolymers has, but lower than the hydrodynamic diameter observed for the high molar mass polymers P1e-f. This points to a marked influence of the thermoresponsive block on the coil size in water ( Fig. 7(b)), possibly due to the compatibility of the P1 and P2 blocks as indicated in the DSC thermograms.
Noteworthy, for P2-1a/HE bearing a short P1 block with around 40 repeating units of bMOEAm, no phase transition occurred up to a concentration of 5 g L −1 . In contrast, when a longer thermoresponsive block of around 100 repeat units was incorporated as in P2-1b/HE, we observed a fully reversible phase transition with a very small hysteresis analogously to the behavior of the homopolymers. Still, the phase transition temperature increased markedly compared with the homopolymers. As demonstrated, the water solubility of polymers P1 is strongly affected by hydrophobic end groups. Obviously, this is also the case for hydrophilic groups attached to P1, such as the P2 block (PDMAm). The enhanced solubility in water increases the cloud point and shifts the phase transition to around 60°C, which is almost 15°C higher than for the P1 homopolymers. Most likely, enhanced solubility accounts also for the lacking phase transition of P2-1a/HE in the studied temperature range, as the thermoresponsive P1 block is apparently too short to counterbalance the effect of the strongly hydrophilic P2 block attached. We note that structurally similar block copolymers of P2 and PDEAm (PDMAm-b-PDEAm) showed only slightly higher phase transition temperatures compared with PDEAm homopolymers [97]. This is also the case for block copolymers of P2 and PNIPAm [98,99]. Accordingly, the additional ethyleneglycolether motifs in the analogous tertiary polyacrylamide P1, PbMOEAm, render the phase transition considerably more sensitive to attached hydrophilic blocks.