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. 2024 Feb 29;57(5):2385–2393. doi: 10.1021/acs.macromol.3c02232

Unique Method for Facile Postsynthetic Modification of Nonisocyanate Polyurethanes

Sergei V Zubkevich 1, Maksim Makarov 1, Reiner Dieden 1, Laura Puchot 1, Vincent Berthé 1, Stephan Westermann 1, Alexander S Shaplov 1,*, Daniel F Schmidt 1,*
PMCID: PMC10938877  PMID: 38495389

Abstract

graphic file with name ma3c02232_0005.jpg

Nonisocyanate polyurethanes (NIPUs) are broadly investigated as a potential replacement for conventional polyurethanes (PUs) to eliminate the use of toxic isocyanates and reduce occupational hazards. One of the most popular approaches to NIPU synthesis is the polyaddition of cyclic bis(carbonate)s and diamines to form poly(hydroxyurethane)s (PHUs). However, such PHUs are highly hydrophilic due to the presence of two hydroxyl groups per repeat unit, and the resulting moisture absorption significantly degrades their thermomechanical performance and physical stability upon exposure to humidity, thus limiting their utility. Here, we introduce a simple and scalable approach for the modification of PHUs to increase hydrophobicity and adjust their properties. The proposed reaction between aldehydes and appropriately spaced hydroxyl groups in the polymer backbone resulted in high degrees of modification (up to 84%) and up to 3-fold reductions in water uptake at 85% RH. Furthermore, the use of aromatic aldehydes in particular enabled the retention of mechanical properties over a wide range of humidity levels, resulting in performance comparable to conventional PUs. Finally, we note that this approach is not limited to reducing moisture sensitivity alone and provides ample opportunities for imparting a broad range of novel properties to PHUs through an appropriate selection of functional aldehydes.

Introduction

Polyurethanes (PUs) are widely used and represent a versatile family of plastics, with an annual worldwide production of 24.7 million tons in 2021.1 The vast array of available precursors for these materials enables a broad range of applications, including foams, coatings, adhesives, automotive parts, medical devices, sporting goods, etc.2 The conventional synthetic pathway to linear PUs involves the reaction of diisocyanates with diols. However, isocyanates are toxic compounds that present respiratory and dermal hazards and can cause chronic illness or even death upon overexposure.3,4 As a result, extensive research in academia and industry has focused on alternative synthetic pathways for the preparation of PUs that avoid the use of hazardous isocyanates.5−10 These so-called nonisocyanate polyurethanes (NIPUs) are considered a “greener” alternative to PUs not only due to the less hazardous monomers in use but also thanks to the availability of biobased feedstocks for their synthesis.11−13

One of the most popular approaches for NIPU synthesis is the aminolysis of cyclic bis(carbonate)s (CCs) leading to the preparation of poly(hydroxyurethane)s (PHUs).14,15 This pathway is often preferred because it provides 100% atom economy and utilizes readily produced and minimally toxic CCs (Scheme 1A).

Scheme 1. (A) PHU1 Synthesis from Erythritol Dicarbonate (EDC) and 1,6-Hexamethylenediamine (HMDA); (B) Modification of PHU1 with Selected Aliphatic and Aromatic Aldehydes; (C) Synthesis of Conventional PU Control from 1,6-Hexamethylene Diisocyanate (HMDI) and 1,4-Butanediol (BDO).

Scheme 1

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However, there are several issues inherent to PHUs that remain unresolved and limit their potential application, most notably (a) low molecular weights due to slow polymerization kinetics, low reactivity of 5-membered CCs, and the occurrence of side reactions16,17 and (b) significant hydrophilicity9,18,19 due to the presence of numerous hydroxyl groups in the polymer backbone. The substantial moisture uptake of such PHUs generally results in the deterioration of their thermomechanical properties in humid environments or upon prolonged storage and can trigger hydrolytic depolymerization during processing.

The issue of slow polymerization kinetics can be partially solved by employing reactive extrusion (ReX) to the synthesis of PHUs.20 Compared to conventional batch melt polycondensation21 and solution polymerization,22 ReX is able to provide the following advantages:23 (1) it allows for high shear rates and excellent mixing of even very viscous media in the absence of any solvents as a function of the screw geometry; (2) it ensures the highest possible reaction rates by maximizing the concentrations of monomers and initiators/catalysts (if present); (3) it reduces the reaction times required to achieve high conversion during polycondensation; (4) it facilitates heat transfer, better maintaining the reaction temperature and reducing the rate of side reactions.

To address the hydrophilicity of PHUs, in this work, we suggest a novel24 postsynthetic modification approach inspired by the synthesis of poly(vinyl butyral)25 and involving the reaction of proximate pairs of hydroxyl groups in the PHU backbone with aldehydes to form cyclic acetals (Scheme 1B). Previously, several methods for consuming these hydroxyl groups during postsynthetic modification have been reported, including esterification with acetic anhydride,26,27 benzoyl chloride,27 or chloroacetyl chloride28 and silylation.27 However, the reagents used for such modifications were either corrosive or toxic, and no studies to determine the hydrophilicity of resulting polymers were conducted. In the approach suggested in this work, the only prerequisite for polymer modification is the presence and structural availability of two adjacent hydroxyl groups in the PHU chain. This can be achieved by using tailored bis(carbonate) monomers such as erythritol dicarbonate (EDC, Scheme S1 and Figures S1 and S2) or 4-vinylcyclohexene dicarbonate (4VCHDC, Scheme S2 and Figures S3–S8) in combination with the diamine(s) of choice, thus providing the requisite pairs of proximate hydroxyls, as shown in PHU1 (Schemes 1A and S3) and PHU2 (Scheme S4).

Results and Discussion

PHU Synthesis and Modification

First, we performed the optimization of PHU1 synthesis, previously reported by Mülhaupt et al.22 Optimization of the reactive extrusion conditions, including reaction time and temperature, nature and amount of hydrogen bond disrupting agent,16 etc., (see Section SVI) enabled the preparation of linear PHU1 with molecular weights as high as Mn(SEC) = 15 100 g mol–1 and Mw/Mn values in the range of 3.3–6.5. Based on a detailed analysis of all experiments in Table S1, it can be concluded that the optimal reaction conditions for the synthesis of PHU1 with the highest possible molecular weight and in the highest yield are as follows: 100 °C, 2.5 h, and the addition of 30 wt % of N-methyl-2-pyrrolidone (NMP) as a solubilizing and hydrogen bond disrupting agent (see Section SIII.1 and Figures S10–S14). The structure of PHU1 was confirmed by NMR following a method adapted from Cramail et al.29 According to NMR (Section SV.5), the ratio between first, second, and third repeat unit types (Scheme 2) was found to be equal to 34.0:58.5:7.5 mol %. This implies a total ratio of primary to secondary hydroxyl groups of (OH)I/(OH)II = 25:75. The presence of urea moieties20 was also detected as a concentration of approximately 1.5 mol %.

Scheme 2. Microstructure of PHU1 and Structures of Intramolecular Cyclic Acetals and Intermolecular Linear Acetals That May Form during the Modification of PHU1.

Scheme 2

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As the next step, PHU1 was used as the parent polymer for the creation of a series of modified linear PHUs bearing aliphatic or aromatic substituents (Scheme 1B and Table 1). The formation of cyclic acetals was achieved through the reaction between the corresponding aldehyde and pairs of adjacent hydroxyl groups in the PHU1 main chain, catalyzed by p-toluenesulfonic acid (pTSA). Optimization of the reaction conditions was carried out using the modification of PHU1 with butyraldehyde as representative of the overall approach (see Section SVII, Table S2, and Figures S44 and S45). Varying the excess of aldehyde, the amount of pTSA, the temperature, and the duration of the reaction, it was possible to achieve as high degree of modification as 84% (Table 1, PHU1-Bu). The optimal conditions were determined to be as follows: NMP as a reaction solvent, [PHU1] ≈ 10 wt %, 5.63 mol. equiv of aldehyde, 0.38 mol. equiv of pTSA, 70 °C, 72 h. The structure of the resultant PHU1-Bu was fully confirmed by NMR analysis (Section SV.1 and Figures S17–S22). Due to the complexity of the NMR spectrum, it was not possible to unambiguously attribute the signals relative to 5-, 6-, or 7-membered cyclic acetals. By taking into account the ratio between repeat unit types (58.5:34.0:7.5 mol %) determined for PHU1 (Scheme 2 and Section SV.5), it is expected that a similar ratio holds for 5-, 6-, and 7-membered cyclic acetals as well. However, since the reaction conversion is not quantitative and varies depending on the chosen aldehyde, the precise ratio between cyclic acetals remains somewhat uncertain. Moreover, by analogy with bulk acetalization of poly(vinyl alcohol), one can propose the formation of intermolecular acetals leading to branched structures or even cross-linked polymers (Scheme 2). It has been previously reported that such unwanted reactions can be effectively suppressed by performing the modification reaction in dilute solution rather than in bulk25 and through the use of reaction media and temperatures capable of suppressing hydrogen bonding30 – all of which applies to the current work, modification reactions having been carried out in the NMP solution at 70 °C. While the presence of intermolecular acetals cannot be proven or refuted by NMR due to the complex nature of the resultant spectra and the overlapping of the signals of interest, two observations are worth noting. First, in addition to a significant increase in solubility following modification in comparison to the parent PHU1 (Section SV.3 and Table S2), the lack of a gel fraction in the modified PHUs rules out significant cross-linking.25 The decrease in the breadth of the molecular weight distribution (Mw/Mn = 8.05 (PHU1), 6.77 (PHU1-Hept), 5.58 (PHU1-ArCN)) following modification (Figure S81) rules out significant branching.30 Taken together, these observations are consistent with intramolecular cyclic acetal formation as the predominant modification reaction.

Table 1. Properties of Modified PHUs vs Controls PHU1 and PU.

  precipitated powders
 melt processed bars
 films
  water uptake (wt %)g G′ (MPa)h
sample mod. (%)a Tg (Tm) (°C)b Tg (Tm) (°C)c Xc (%)d Tonset (°C)e Tα (°C)f E′ (MPa)f Xc (%)d 45% RH 65% RH 85% RH 45% RH 65% RH 85% RH water contact angle (deg)i
PHU1   50 (97, 130) 58 (104, 134) 14.8 185 81 1690 10.3 2.0 3.7 7.5 1600 360 54 91.7 ± 0.8
PHU1-Bu 84 41 44 (108) 0.3 185 56 1660 0 1.1 2.1 3.6 210 53 2.7 106.7 ± 1.1
PHU1-Hept 84 33 36 (111) 0.7 215 45 1270 0.2 1.1 1.9 3.0 89 24 2.5 109.3 ± 0.4
PHU1-FHept 35j 34 42 (111) 3.6 155 k k k k k k k k k 110.0 ± 0.3
PHU1-Ph 43 43 (94) 50 (100) 5.6 205 86 1530 1.9 0.7 1.7 3.7 600 210 140 96.4 ± 0.6
PHU1-ArCN 51 52 (115) 55 (119) 6.3 175 88 2360 3.4 1.0 1.9 4.7 770 450 56 95.6 ± 0.6
PHU1-ArCF3 61 57 59 0 195 71 1610 0 0.8 1.5 3.2 530 330 200 97.3 ± 0.4
PHU1-PrPh 80 42 46 0 225 51 1310 0 0.2 1.1 2.4 420 330 74 89.8 ± 0.7
PUl   (187) 45 (188) 56.0 200 42 2200 35.2 0.4 0.4 1.1 460 400 300 95.1 ± 3.0
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a

By 1H NMR (see Supporting Information).

b

By DSC in N2 at a heating rate of 5 °C/min; Tm was taken as peak maximum.

c

By DSC in N2 at a heating rate of 10 °C/min; Tm was taken as peak maximum.

d

Degree of crystallinity determined by DSC in N2 at a heating rate of 10 °C/min (see Supporting Information).

e

By TGA in air at a heating rate of 5 °C/min.

f

Storage modulus (E′) and Tα (taken as peak maximum from the loss modulus (E″) curve) measured by DMTA at a heating rate of 5 °C/min.

g

Determined after 11 days of conditioning at selected humidity levels and 22 °C.

h

Storage modulus (G′) at 0.1 Hz measured via torsional rheometry at 25 °C and indicated humidity level after conditioning at selected humidity levels and 22 °C for 3 days.

i

Water contact angle measured on films at 22 °C.

j

By 19F NMR with external standard (C6F6).

k

Not determined due to low extent of modification.

l

For comparison.

Building on this work, various aldehydes (both aliphatic and aromatic) were used to modify the parent compound PHU1 (Scheme 1B and Section SV.2). The degree of modification was found to be dependent on the nature of the aldehyde and was determined using NMR (1H or 19F; Section SV.3). The utilization of compounds containing nonaromatic aldehyde groups (Table 1, PHU1-Bu, PHU1-Hept, and PHU1-PrPh) resulted in high degrees of modification ranging from 80 to 84%. Fluorinated 3,3,4,4,5,5,6,6,7,7,7-undecafluoroheptanal (F-heptaldehyde), in contrast, gave only 35% modification (Table 1, PHU1-FHept) probably due to unwanted oligomerization of the F-heptaldehyde. Compounds containing aromatic aldehyde groups demonstrated a lower reactivity in comparison to that of their aliphatic counterparts (Table 1, PHU1-Ph). While this can be explained by a combination of steric and electronic effects, the latter seems to predominate, as deduced from the comparison between PHU1-Ph (43% degree of modification) and PHU1-PrPh (80% degree of modification). In aromatic aldehydes, the lone pair of electrons on the carbonyl oxygen can be delocalized by the benzene ring through resonance, thus making the electron density on the oxygen less available for nucleophilic attack and decreasing the success of modification as in the case of PHU1-Ph. The introduction of the aliphatic bridge between the aldehyde function and the benzene ring as in 3-phenylpropionaldehyde suppresses this resonance and increases the degree of modification. However, the aromatic aldehydes can be activated through the introduction of electron-withdrawing substituents in the para position of the benzene ring, thus yielding increases in the extent of modification from 43 to 51 and 61% for PHU1-Ph, PHU1-ArCF3, and PHU1-ArCN, respectively (Table 1).

To further confirm these trends, another parent PHU (PHU2) having two adjacent hydroxyl groups was modified with 3-phenylpropionaldehyde (Scheme S13 and Section SV.1.8) under optimal reaction conditions, yielding an extent of modification as high as 50%. This lower value was anticipated due to the larger spacing between the hydroxyl functions (Scheme S13), given that the formation of cyclic acetals with more than 7 carbon atoms is believed to be less favorable. The large distances present between the hydroxyl groups in some structural isomers make it impossible to form cyclic acetals and lead to further decreases in the extent of modification. Nevertheless, this example one more time demonstrates the applicability of the method given the existence of appropriate structures in the parent PHU. Finally, for comparison purposes, a conventional polyurethane PU with a structure analogous to that of PHU1 was prepared via the reaction of 1,6-hexamethylene diisocyanate and 1,4-butanediol (Scheme 1C).

PHU Properties in a Dry State

Following their preparation, the thermal and mechanical properties of the modified PHUs were assessed using DSC (Figures S46–S65), DMTA (Figure S67), and TGA methods. Modification with compounds containing aliphatic aldehyde groups led to small decreases in the glass transition temperature (Table 1, PHU1-Bu, PHU1-Hept, and PHU1-PrPh), with the magnitude of the decrease observed to be proportional to the length of the side chain (Table 1, PHU1-Bu and PHU1-Hept) at a comparable degree of modification. In contrast, the use of compounds containing aromatic aldehyde groups resulted in similar (PHU1-Ph, PHU1-ArCN) or higher Tg values (in the case of PHU1-ArCF3) vs the parent PHU1.

These materials were additionally observed to be semicrystalline as well (Table 1), with PHU1-FHept (Figure S57), PHU1-Ph (Figure S59), and PHU1-ArCN (Figure S61) displaying DSC endotherms at ∼100 °C attributed to the melting of the crystalline phase.31 The highest degree of crystallinity (∼56%) was observed in the control PU (Figure S51), in full agreement with published data.31,32 A modest degree of crystallinity (∼15%) was observed in parent PHU1 (Figure S48), while PHUs modified with compounds containing aromatic aldehyde groups showed even lower levels of crystallinity (∼6%). Finally, PHUs modified with compounds bearing aliphatic aldehyde groups displayed the lowest levels of crystallinity (∼0.5%). While all attempts to crystallize these materials in subsequent DSC cycles failed, dissolution of the amorphous (melted) PHU in THF and repeated precipitation in Et2O resulted in the regeneration of semicrystalline material. The cooling of the modified PHUs in the compression mold under vacuum induced crystallinity as well, albeit to a lesser extent than in the case of solvent-precipitated material (Table 1). The observed crystallinity was further confirmed (qualitatively) by WAXD analysis (Figures S67–S70).

DMTA analyses were performed on polymer bars in tension mode (Figures 1A,B and S66). The observed Tg (Tα more exactly) values for PHU1 and all modified PHUs were slightly higher than those determined by DSC with the same heating rate (Table 1). Nevertheless, the tendency in PHUs Tg was found to be in good agreement with DSC. The storage modulus (E’) of the modified PHUs is presented in Figure 1A and Table 1. The glassy plateau of the majority of the modified PHUs is higher than that of the parent PHU1 but generally lower than that of the conventional PU. Only the PHU modified with 4-formylbenzonitrile displayed a glassy plateau comparable to that of PU (Table 1, PHU1-ArCN). Nevertheless, these results confirm that the modification method presented here can provide similar or greater levels of thermomechanical performance vs the parent PHU1.

Figure 1.

Figure 1

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Temperature dependence of storage (E′) (A) and loss moduli (E″) (B) for modified PHUs, PHU1, and PU samples measured by DMTA; room temperature water uptake of modified PHUs, PHU1, and PU at 45, 65, and 85% RH (C).

The tensile properties of selected PHUs were studied as well (Section SXIV, Table S6, and Figure S82). While the tensile strength decreased from 20.7 ± 1.1 MPa for parent PHU1 to 10.2 ± 1.8 for PHU1-Bu and 6.7 ± 0.7 for PHU1-ArCF3, the elongation at break was found to be less dependent on the PHU structure (Figure S82), with similar results for PHU1 (1.77 ± 0.26%) and PHU1-Bu (1.79 ± 0.19%) and slightly lower values for PHU1-ArCF3 (0.80 ± 0.09%). Such shifts in properties are most readily explained by a reduction in the level of intermolecular hydrogen bonding since the majority of pendant hydroxyl groups are involved in the formation of cyclic acetal groups, and are entirely consistent with early reports of decreases in tensile strength with increasing degree of acetalization in poly(vinyl alcohol) as well.33

PHU Properties at Different Humidities

The next step in this work consisted of the investigation of the PHU properties as a function of the relative humidity (RH). First, the room temperature water uptake of modified PHUs was studied at three humidity levels (45, 65, and 85% RH) and compared to that of parent PHU1 and conventional PU (Table 1 and Figures 1C and S71 and S72). The consumption of the free hydroxyl groups in the modified PHUs resulted in significant reductions in hydrophilicity by a factor of 2–3 times as compared to neat PHU1. The most pronounced effect was observed for PHU1-PrPh, which displayed only 2.4% of water uptake after 11 days of conditioning at 85% RH vs 7.5% for the parent PHU1. The smallest improvement was observed in the case of PHU1-ArCN, probably due to the presence of polar CN groups. To ensure that the sorption of water does not lead to hydrolysis of the modified PHUs, a comparative study of dry samples and those conditioned for 4 weeks at 85% RH was performed via GPC and NMR (Section SXIII and Figures S76–S79). Figure S80 undoubtedly demonstrates that there is no change in Mw as a consequence of exposure to moisture. Consistent with this observation, NMR spectra (Figures S76–S78) show that the degree of modification remains unchanged after prolonged conditioning as well.

Similar trends were observed in an investigation of water contact angles (Table 1 and Figure 2). The modification of PHU1 resulted in a decrease in the wettability of the polymer surface and an increase in contact angles from 91.7° to as high as 109.3°. The most pronounced improvement was observed for PHUs modified with aldehydes containing (fluorinated) linear hydrocarbon segments (Table 1, PHU1-Bu, PHU1-Hept, and PHU1-FHept), where an increase in the length of the alkyl tail resulted in an increase in CA (Table 1, PHU1-Bu and PHU1-Hept).

Figure 2.

Figure 2

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Frequency dependence of storage moduli (G′) for modified PHUs, PHU1, and PU controls, measured after conditioning at different humidity levels and wettability (water contact angles, CAs) of respective polymer films.

Such modifications resulted in reduced wettability not only in comparison to the parent hydrophilic PHU1 but also vs conventional PU. The modification of PHU1 with compounds containing aromatic substituents also increased the measured water contact angles but to a lesser extent (Table 1, PHU1-Ph, PHU1-ArCF3, and PHU1-ArCN), with the most pronounced effect for the aromatic substituent containing a CF3 group. An exception was observed for PHU1-PrPh, which, despite a high extent of modification, gave a CA quite similar to that of the parent PHU1 and below that of both PHU1-Bu and PHU1-Ph. As this result would not be expected based on structural arguments alone, one possible explanation is that this material experiences strong local interactions with liquid water, enabling reorganization of the polymer surface (during the formation of the film) to display only the most polar functional groups. This is consistent with the much larger drop in G′ observed in this system vs PHU1-Ph as RH is increased and may be further aided by the limited ability of the propylphenyl substituents to self-associate and pack space efficiently in contrast to linear alkyl substituents like those present in PHU1-Bu for instance. While the in-depth studies necessary to fully understand this phenomenon are beyond the scope of the current report, it is nevertheless noteworthy that water-induced surface reorganization has long been reported in the literature for some of the conventional polyurethanes.34−37

The mechanical properties vs humidity for modified PHUs were studied via torsional rheometry on polymer bars (Figures 2 and S73–S75). The samples were conditioned for 3 days at the selected humidity level and were then characterized in torsion mode at room temperature while maintaining the same humidity levels inside the rheometer chamber. The storage modulus (G′) values were found to display only modest decreases with increasing humidity for conventional PU. In contrast, much larger decreases were observed in the case of PHU1 (Figure 2), with G′ reduced by nearly 2 orders of magnitude when moving from 45 to 85% RH. Data taken after 14 days of conditioning were similar (Figure S76), implying that 3 days was sufficient to realize equilibrium moisture uptake in these specimens. This large difference in the moisture sensitivity of the elastic response is explained by the presence of large concentrations of hydrophilic OH groups in PHU1 leading to significant water uptake (Figure 1C) and subsequent plasticization of the polymer by the absorbed water. The rheometer data for the modified PHUs (Figure 2) showed opposing trends as a function of the aldehyde type. While the use of aliphatic aldehydes resulted in even larger decreases in G′ with increasing humidity as compared with the parent PHU1 (Figure 2, PHU1-Bu), the use of aldehydes containing aromatic rings led to substantial reductions in the sensitivity of the modulus to humidity (Figure 2, PHU1-Ph, PHU1-ArCF3, and PHU1-PrPh).

For example, the storage moduli of PHU1-PrPh at 45 and 65% RH show only modest differences, with a large decrease not observed until 85% RH. The behavior of PHU1-Bu and PHU1-Hept is most obviously explained by the low Tg (41 and 33 °C, respectively) and lack of crystallinity apparently induced by modification with compounds containing aromatic aldehydes. In such materials, the absorption of even small amounts of water will plasticize the entire mass of the polymer, reducing the Tg to values below RT and leading to much more significant softening than in the case of materials with either higher initial Tg values or some level of crystallinity (Table 1, PHU1-Ph, PHU1-ArCN, and PHU1-ArCF3). In contrast, the use of aromatic aldehydes provides modified PHUs with the most consistent behavior vs humidity (Figure 2, PHU1-Ph, PHU1-ArCN, and PHU1-ArCF3). The decrease in the storage modulus for PHU1-ArCF3 was found to be only 2.5-fold between 45 and 85% RH and is comparable to the 1.5-fold decrease for conventional PU. Surprisingly, PHU1-Ph, which has only 43% of modification, was also able to retain its mechanical properties after exposure to 85% RH, displaying a 4-fold decrease in storage modulus (slightly less than that for PHU1-PrPh). This could be explained by the presence of crystallinity in PHU1-Ph compared to the fully amorphous nature of PHU1-PrPh and by the relative lack of mobility of the phenyl substituents in the former case as compared to the propylphenyl substituents in the latter case.

Finally, it was observed that the storage moduli (G′) of PHU1 and to a lesser extent PHU1-Bu and PHU1-PrPh show a greater frequency dependence at elevated RH levels as compared to the other materials studied (Figure 2). This behavior would seem to be best explained by a change in Tα due to plasticization with absorbed water, as has been estimated using the Fox equation38 (Section SXII and Table S5). These calculations reveal that at the highest RH level (85%) three of the five PHUs studied (PHU1, PHU1-Bu, and PHU1-PrPh) are expected to give α transition temperatures of ∼40 °C vs ∼55 °C for PHU1-ArCF3 and ∼65 °C for PHU1-Ph. While such results are necessarily approximate, they indicate that the hydration of PHU1, PHU1-Bu, and PHU1-PrPh results in a decrease in the main relaxation temperature to the point where it is close enough to the measurement temperature that the modulus begins to exhibit a significant frequency dependence (as expected near the main relaxation). In contrast, the PU control does not exhibit such behavior in spite of its similarly low Tα of ∼40 °C due to its much higher crystalline fraction (∼35%). Here, the high-stiffness crystalline fraction dominates the mechanical response of the PU and provides a higher, less frequency-dependent modulus vs PHUs with the same main relaxation temperature but much lower levels of crystallinity (∼0–10%).

Conclusions

In this work, we have shown that specifically tailored PHUs with proximate hydroxyl groups in the backbone can be readily modified by a simple reaction with aldehydes. The suggested approach allows for PHU modification that significantly improves hydrophobicity and reduces the impact of humidity on the mechanical response. Moreover, keeping in mind the ready availability of a broad range of available functional aldehydes, this method provides an easy means of imparting novel/application-specific properties to PHUs, greatly increasing their potential utility.

Acknowledgments

This work was supported by the EU Commission’s Marie Curie IIF grant “SPRUT” (No. 101066839) under the HORIZON-TMA-MSCA-PF-EF action and in part by Luxembourg National Research Fund (FNR) through project SAFFIA (Agreement Number INTER/MERA20/15020254). M.M. is grateful to the Luxembourg Institute of Science and Technology (LIST) for the sponsorship of his internship and work in the Materials and Research Technology Department (MRT). Dr. Andrey A. Tyutyunov (A. N. Nesmeyanov Institute of Organoelement Compounds Russian Academy of Sciences (INEOS RAS)) is gratefully acknowledged for supplying 3,3,4,4,5,5,6,6,7,7,7-undecafluoroheptanal free of charge.

Supporting Information Available

The Supporting Information is available free of charge at https://pubs.acs.org/doi/10.1021/acs.macromol.3c02232.

  • Additional experimental details including materials and methods; synthesis of cyclic carbonate monomers; PHU1 and PHU2 synthesis and modification; PU synthesis; determination of extent of PHU modification using NMR; determination of crystallinity degree in polymers; discussion and analysis including optimization of PHU synthesis and modification; DSC plots; DMTA plots; representative WAXD plots; water absorption plots; storage moduli (G′) plots at different humidity levels; GPC plots and tensile plots (DOCX)

The authors declare no competing financial interest.

Supplementary Material

ma3c02232_si_001.docx (111.1MB, docx)

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