Resin and carbon foam production by cationic step-growth polymerization of organic carbonates†

Acid induced step-growth polymerizations of bis(p-methoxybenzyl) carbonate (pMBC), bis(m-methoxybenzyl) carbonate (mMBC) and difurfuryl carbonate (DFC) have been performed to produce resin-foams, because controlled release of carbon dioxide takes place during polymerization of those organic carbonates. The monomers are polymerized in bulk using p-toluene sulfonic acid (pTS) as a catalyst. The volume development of the foams is assisted by use of an appropriate surfactant and the crosslinking agent 1,3,5trioxane as co-components. A portion of carbon dioxide release is a function of the carbenium stability of the reactive intermediate derived from the monomer; DFC > pMBC ≫ mMBC. Resins derived from mMBC can be post-treated to release carbon dioxide after polymerization. The molecular structures of the resulting materials are investigated by solid state C-NMR spectroscopy and IR spectroscopy. Scanning electron microscopy was used to study foam morphology. The carbon dioxide release was monitored with TG-MS analysis. Finally, the polymer foams have been converted into carbon foams and investigated by means of mercury porosimetry.


Introduction
Polymer foams can be produced by physical, mechanical or chemical processing. 1 Physical processes are suitable for foaming of thermoplastic polymers as polystyrene and polyethylene due to addition of blowing agents (e.g.easily volatile hydrocarbons).Mechanical foaming processes are performed by blowing the polymer with compressed air or carbon dioxide (CO 2 ) gas.Polyurethane resins require chemical processes to develop gas (CO 2 ) during the reaction of components.Another approach is the use of templates by emulsion due to surfactants which stabilize nitrogen gas bubbles during UV-initiated polymerization of styrene. 2 Isocyanate derived fire prevention foams are used for isolation in electrical systems. 3,4However, the substitution of isocyanates is of importance because of their toxicity.In this work, an alternative route for foam production by chemical processing is presented.Shape persistent polymer foams consisting of anisolic resins 5,6 or polyfurfuryl alcohol 7 (PFA) have a high thermal stability.Therefore, they have been chosen as suitable materials for potential application in fire prevention. 8rbon dioxide release during formation of polyurethane foams is well established.Isocyanate groups react with traces of water and a decarboxylation reaction takes place starting from the carbamic acid intermediate (Scheme 1a). 9,10Organic carbonic acid derivatives are promising candidates for cationic polymerization because they can be synthesized from benzylic alcohols and phosgene or other carbonic acid derivatives.To achieve foam formation among carbon dioxide release, the carbonic acid ester must be constructed in such a way that Scheme 1 Comparison of (a) carbon dioxide release during reaction of isocyanate with water to (b) theoretically expected cationic step-growth polymerization of organic carbonates.† Electronic supplementary information (ESI) available.See DOI: 10.1039/ c6py01572g a Polymer Chemistry, Technische Universität Chemnitz, 09107 Chemnitz, Germany.E-mail: stefan.spange@chemie.tu-chemnitz.deboth, polymerization and carbon dioxide release, occur simultaneously.The idea for the structure of carbon dioxide-releasing monomers was inspired by the concept of twin polymerization of tetrafurfuryloxysilane (TFOS) 11,12 (Scheme 2a).Silicon as an element was substituted by carbon.However, the 4-fold substituted orthocarbonate of furfuryl alcohol is still not reported and our attempts to synthesize this compound are not of success.Thus, the organic carbonic acid ester difurfurylcarbonate (DFC) (Scheme 2b) and additionally para-and metamethoxybenzyl carbonates ( pMBC, mMBC) (Scheme 2c) are used for this work.
The organic carbonates are synthesized by the transesterification reaction of diethyl carbonate with the respective alcohol (Scheme 3).
Basically, there are two scenarios to consider.The carbonate monomer can polymerize under the release of carbon dioxide or the carbonate moiety remains intact after polymerization.As well, both scenarios can occur simultaneously.If the carbonate moiety remains after polymerization, it is assumed that the carbon dioxide release can be triggered on demand afterwards.Theoretically, it is expected that acid catalyzed poly-condensation of carbonates proceeds via carbenium intermediates (Scheme 1b).Thus, the formation of stabilized carbenium ions should favor carbon dioxide elimination during the polymerization process (Scheme 1b).The furan ring or the methoxy substituent at the para position of the phenyl ring is well suited to stabilize benzylic carbenium ions. 13,146][17] Therefore, it is expected that DFC and pMBC are suitable candidates as carbon dioxide sources for foam production at ambient temperature.The main objective of this study is to show the feasibility of this conception whether it is possible to deliver sufficient amount of carbon dioxide gas during resin fabrication.A crucial point is the fact that the alkylation reaction during polycondensation should also have an additional stabilizing effect on carbenium ion stability.An argument for this consideration is the significantly higher π-reactivity of the meta-substituted aromatics compared to that of the parasubstituted ones.Thus the order of π-reactivity of the monomers DFC > mMBC > pMBC does not follow the corresponding carbenium stability of the intermediate derived from the same monomer. 13,14heoretically, DFC and MBC, respectively, can produce per gram monomer 74 and 100 mL gaseous carbon dioxide if a complete conversion takes place.The objective of this study is the fabrication of foams containing anisolic 5,6 and polyfurfuryl alcohol resin by acid-catalyzed polymerization and to study some basic mechanistic aspects using model reactions in solution.
Solution 1 H-and 13 C-{ 1 H}-NMR experiments were performed on a Bruker DPX 250 NMR spectrometer.Deuterated chloroform (CDCl 3 ) was used as a solvent and an internal standard (δ H = 7.26 ppm; δ C = 77.16ppm).The solid state 13 C-{ 1 H}-CP-MAS-NMR measurements were performed at 9.4 T on a Bruker Digital Avance 400 spectrometer equipped with double-tuned probes capable of MAS (magic angle spinning).A 3.2 mm standard zirconium oxide rotor was used spinning at 15 kHz.Cross polarization with a contact time of 3 ms was used to enhance sensitivity.The recycle delay was 5 s.The external standard was tetrakis(trimethylsilyl)silane (δ H = 0.27 ppm; δ C = 3.55 ppm) and 1 H decoupling was performed with a TPPM pulse sequence.ATR-FTIR spectra were measured using a FTS 165 spectrometer (BioRad) and a Golden Gate single ATR accessory from LOT-Oriel GmbH.
Quantitative elemental analysis was carried out with a Vario El from the company Elementar Analysensysteme GmbH.
Differential scanning calorimetry (DSC) measurements were carried out in a 40 µL aluminium crucible with a DSC 1 from Mettler Toledo under a nitrogen atmosphere (50 mL min −1 ).The heating rate was 10 K min −1 .
Thermogravimetric (TG) analysis was performed with a thermogravimetric microbalance TG 209 F1 Iris® from NETZSCH.This device was coupled with a mass spectrometer (MS) MS 403C Aëolos®.The measurements were performed at a heating rate of 10 K min −1 under a helium atmosphere (50 mL min −1 ).
Size exclusion chromatography (SEC) measurements were performed with a PL-GPC 50 plus from Polymer Laboratories.An auto sampler PL-AS RT, a detector PC-RI and a column PLgel MIXED-D were used.The eluent was tetrahydrofuran (THF) at a flow rate of 1 mL min −1 at 40 °C.
Scanning electron microscopy (SEM) images were taken using a Nova NanoSEM 200 of FEI Company.The samples were sputtered with platinum before measurement.
The pores were studied at a low pressure with a Pascal 140 mercury porosimeter (Thermo Scientific).Afterwards, the pores were analysed at high pressure, utilising a Porosimeter 2000 (Fisons Instruments).
Synthetic procedures for pMBC, mMBC and DFC DFC 18,19 and pMBC 18 were prepared according to the literature, but the synthesis route was adapted for this work (Scheme 3).1][22] The reaction mixture was heated to 70 °C and ethanol was continuously removed by distillation in a vacuum.DFC is obtained as a slightly yellow liquid after distillation at 114 °C and 0.2 mbar.
In the case of pMBC and mMBC Cs 2 CO 3 was separated by washing with water.The organic products were extracted with ethyl acetate.All byproducts (methoxybenzyl alcohol and mono-substituted compound) were removed by distillation.The crude product remained in the residue.pMBC and mMBC were obtained after recrystallization with n-hexane as opaque solids with a melting point of 70 °C and 52 °C, respectively.

Polymerization of pMBC, mMBC and DFC
The polymerization of carbonates in solution was monitored with 1 H-NMR spectroscopy.Therefore, in an argon atmosphere 1 g carbonate and 0.1 g naphthalene as standards were dissolved in 1 mL CDCl 3 .The acid (tenth mol regarding the monomer) was mixed with 1 mL CDCl 3 and added to the carbonate solution at room temperature.At different time intervals a NMR sample was taken from the reaction mixture.
The polymerization in melt was performed in a Teflon vessel.2.0 g (0.007 mol) of the monomer pMBC or mMBC was melted while heating until 70 °C and 100 °C, respectively.Afterwards, the vessel was removed from the heating bath.After five minutes 0.13 g (0.0007 mol) p-toluene sulfonic acid monohydrate ( pTS) was added to the monomer melt under vigorous stirring.The Teflon vessel was removed from the heating bath after a homogenization time of two minutes.
In the case of pMBC a strong gas development at 70 °C takes place.The polymerization of pMBC was annealed at 70 °C and 150 °C each for 2 hours.For mMBC an annealing temperature of 100 °C and 150 °C was chosen each for 2 hours.
DFC is liquid at room temperature (RT).Thus, pTS can be added to the monomer at RT.For polymerization, 2.0 g (0.009 mol) DFC and 0.17 g (0.0009 mol) pTS were mixed under vigorous stirring.An immediate discoloration of slightly yellow to dark brown takes place.After two minutes, the Teflon vessel was moved to a 60 °C hot heating bath and annealed for four hours.The polymerization starts after two minutes as indicated by a strong gas evolution.
For polymerization with 1,3,5-trioxane (TO) as a crosslinking agent and/or a surfactant (S), 0.20 g (0.002 mol) TO and/or 0.02 g (1 wt%) S were mixed with the monomer.The polymerizations were also investigated at lower temperatures of 100 °C and 90 °C.
Post-condensation was performed by heating the sample up to 250 °C at a heating rate of 2 K min −1 under an argon atmosphere.The end temperature was maintained for two hours.For conversion of the polymer into a carbon material the sample was heated at 4.3 K min −1 to 800 °C and treated for 3 h at this temperature under an argon atmosphere.
The endorsements A and P of the labels indicate the performed annealing and pyrolysis process.

Results and discussion
The carbonates pMBC, mMBC and DFC were synthesized by the transesterification reaction of diethyl carbonate with the respective alcohol (Scheme 3) to avoid the use of toxic carbonyl dichloride.All organic carbonates were characterized with appropriate spectroscopic methods (see the Experimental part).DSC measurements of the carbonates with p-toluenesulfonic acid monohydrate (pTS) as an acid catalyst in a nitrogen atmosphere were performed to study the reaction behavior during polymerization (Fig. 2).DSC investigations show an exothermic peak for pMBC and mMBC at 66 °C and 89 °C, respectively indicating a higher reactivity for pMBC.DFC already reacts with pTS at 30 °C.The results were confirmed by TG-MS measurements (thermogravimetric analysis coupled with mass spectrometry) while adding pTS in a helium (He) atmosphere (Fig. 3).The TG curve of pMBC shows an onset temperature of 64 °C for polymerization and of 92 °C for mMBC.MS detects the ion current of the mass to charge ratio (m/z) of 44 and 18 which can be attributed to CO 2 and water.DFC releases the carbon dioxide during polymerization over a broad temperature range (40-150 °C).A slow mass loss occurs above this temperature interval.In contrast to DFC, pMBC shows a fast CO 2 displacement associated with a rapid mass loss in TG analysis.mMBC shows a slowly increasing ion current of CO 2 beginning at 86 °C that reaches its maximum at 140 °C.
Thus, the results of DSC measurements are in accordance with the theoretically suggested stability of the carbenium intermediates.The more stable the carbenium intermediate, (DFC > pMBC ≫ mMBC), the lower the necessary trigger temperature for the polymerization and associated carbon dioxide release.
To study some basic aspects of the reaction mechanism, which was theoretically postulated in Scheme 1b, liquid .9ppm can be detected too.mMBC and pMBC conversion can be monitored using trifluoromethanesulfonic acid (TFMSA) as a catalyst (a tenth mol regarding to the amount of carbonate).DFC is too reactive to monitor polymerization induced with TFMSA by 1 H-NMR spectroscopy.By dropping the acid dissolved in CDCl 3 to the carbonate solution, an immediate precipitation of polyfurfurylalcohol resin takes place.Even after several days the mMBC conversion is incomplete whereas 60% of pMBC was converted after one minute.In this initial time mMBC behaves unreacted.
Water and carbon dioxide releases as by-products during the polymerization of carbonates have been evidenced (Fig. S1 †).The water formed seems to have no effect on the course of the reaction, because of the good stability of these carbonates against water.Thus, p-toluenesulfonic acid monohydrate ( pTS) can be promptly used as an acid catalyst.
The experimental conditions for the synthesis of the target resin materials are adjusted according to the results of DSC and TG-MS measurements.The three carbonates are polymerized in melt.Different additives such as surfactants and crosslinking agents were used to optimize the experimental para-  meters to achieve good quality of the foam.Experimental parameters are summarized in Table 1.
The obtained anisolic resins pMBC_150 (Table 1, Fig. 7a) and mMBC_150 (Table 1, Fig. 7d) are meltable when synthesized without the use of an additional crosslinking agent.The melting process can be seen in an endothermic peak in DSC curves in Fig. 8. Furthermore, they are soluble in polar solvents (CH 2 Cl 2 , CHCl 3 , tetrahydrofuran, acetone) which allows analysis by means of liquid 1 H-and 13 C-NMR spectroscopy and size exclusion chromatography (SEC).The results (Table 2, Fig. 4) show oligomers with a broad molecular weight distribution.The solubility can be explained by the fact that only one methylene-bridge per aromatic unit is present in the monomer.Therefore, only oligomers are formed (Table 2, Fig. 4).For this reason, 1,3,5-trioxane (TO) was added as a crosslinking agent to produce shape persistent foams.TO serves as an additional Friedel-Crafts reagent because it delivers -CH 2 -bridges which connect the oligomeric anisolic resin chains.
Molecular structure formations during the crosslinking of pMBC and mMBC with TO are shown in Scheme 4. pMBC prefers the formation of carbenium ions during cationic catalysis due to the good stabilization effect of the methoxy group at the para-position.The p-methoxybenzyl carbenium ion can react in electrophilic substitution with an aromatic compound to form an anisolic resin under complete release of CO 2 (Scheme 4a).In contrast, the m-methoxybenzyl carbenium ion shows low carbenium stability because the cation cannot readily be stabilized by a methoxy group at the meta-position.Thus, the formation of a carbenium ion intermediate from the carbonate moiety is inhibited in the first stage of cationic polymerization.In contrast to this fact, the mMBC shows a high reactivity for Friedel-Crafts alkylation.Thus, polymerizations of combination of mMBC with 1,3,5-trioxane yield crosslinked carbonate structures where the carbonate unit remains intact.Further annealing or acid treatment leads to the release Table 1 Performed experiments with the molar ratios of the monomer (n M ) compared to the acid catalyst (n pTS ) and the curing agent (n TO ) as well as used mass ratios of the surfactant (m S ).Furthermore, the endorsement of the label indicates the final polymerization temperature

Sample Molar ratios [mol%]
Mass   of CO 2 and the formation of methylene bridges (Scheme 4b).The subsequent release of carbon dioxide from the crosslinked mMBC resin samples is explainable by the fact that the introduced para-or ortho-alkyl substituents (Fig. 4b) improves carbenium ion stability compared to the only m-methoxy substituent previously present.This result is a strong support for the suggested mechanism and agrees with the results of the model reactions of the pure monomers when treated with an acid in solution.

Molecular structure investigations of the resins
Phenol formaldehyde resins ( phenolic resins) have been well studied and established polymers for more than one century. 23,24Anisol derivatives can be likewise polymerized by a polycondensation reaction with formaldehyde or derivatives. 5,6Extensive investigations on molecular structure formation have not been reported in the literature, yet.
The investigations of the anisolic resin molecular structures arising from cationic polymerization of pMBC and mMBC and combinations of these monomers with TO confirm the suggested reactions as postulated in Scheme 4. The molecular structures were proven by means of solid state 13 C-NMR (Fig. 5c) and ATR-FTIR spectroscopy (Fig. S2, ESI †).mMBC has three positions for electrophilic substitution, two at the orthoand an additional one at the para-position with regards to the methoxy group.The methylene group at the meta-position is predetermined from the monomer structure (Fig. 5b).Therefore, polymers from mMBC show more signals in the solid-state 13 C-{ 1 H}-CP-MAS spectra (Fig. 5c) in contrast to the spectra of pMBC polymers.Thus, two additional signals are observed.The signal C-7 (136-147 ppm) indicates a substituted aryl carbon atom at the meta-position.Signal C-6 (117-124 ppm) suggests an unsubstituted aryl carbon atom at the para-position to the methoxy group.In the case of polymers obtained from pMBC only one substitution pattern is possible (Fig. 5a), because one methylene group situated at the para-position to the methoxy group in the monomer is present.
The cationic polymerizations were performed at 90 °C with trioxane (1TOone additional methylene bridge per monomer) too.The obtained anisolic resins of mMBC and pMBC are meltable and soluble in polar organic solvents (CH 2 Cl 2 , CHCl 3 , tetrahydrofuran, acetone).The SEC profiles (Fig. 4) show a twice-as-high number average molecular mass (M n = 2790 g mol −1 ) for mMBC/1TO_90 compared to pMBC/ 1TO_90 (M n = 1147 g mol −1 ).The weight average molar mass (M W ) of mMBC/1TO_90 exhibits a 6-fold higher value compared to pMBC/1TO_90.This resulted in a high polydispersity index (PDI) of 7.6 (Fig. 4) for mMBC/1TO_90 which shows that very different chain lengths with irregular molecular weights exist.
This result is consistent with the high possibility of mMBC to undergo cross-linking reactions due to the mesomeric structures.Furthermore, a strong carbonyl vibrational band in the ATR-FTIR spectrum (Fig. S3, ESI †) is found.In contrast, in pMBC/1TO_90 the carbonyl band (Fig. S3, ESI †) disappears completely.The liquid 13 C-{ 1 H}-NMR spectra (Fig. S6, ESI †) of the pre-polymerized organic carbonates mMBC and pMBC with TO at 90 °C exhibit the reaction behaviour more clearly.pMBC reacts completely during the formation of methylene bridges and release of CO 2 .The defined signals for the -CH 2carbon atoms of o,p′-, p,p′-and o,o′-linkage between aromatic units at 35.1, 40.2 and 30.2 ppm are found in the liquid 13 C-{ 1 H}-NMR spectrum (Fig. S6, ESI †), respectively.Furthermore, the signals for the -CH 2carbon atoms (93.6 ppm) of unreacted TO are found.The intact carbonyl carbon atom (C) in the 13 C-{ 1 H}-NMR spectra of mMBC/1TO_90 is overlaid with the signal of the C-2 carbon atom of the anisolic resin.DFC shows an outstanding behavior, because it consists of reactive furfuryl moieties which additionally can undergo crosslinking at the methylene bridge (C-5-position) during polymerization in acidic media. 29This reaction is due to the fact that the furan ring stabilizes furfurylium ions in a significant manner.Thus, the carbenium ions derived from DFC prefer to abstract hydride ions from CH 2 -bridged furan ring chains.This is added to the -CH 2 cation to form methyl-end groups.As a consequence of this behavior, conjugated polyfurfuryl alcohol structures are built.As well, the furan ring can be opened during cationic polymerization resulted in the formation of levulinic acid derivatives (Fig. S13a, ESI †). 7However, many other side reactions can occur by acid catalyzed furfuryl alcohol polymerization. 7,26,29,30The possible structures of polyfurfuryl alcohol are illustrated in Fig. 6.The polymer obtained by cationic polymerization of DFC shows the molecular structures of polyfurfuryl alcohol.Furthermore, a downfield 13 C-NMR signal at 204 ppm relating to a carbonyl group and a carbonyl vibration in the ATR-FTIR spectrum (Fig. S2, ESI †) was found due to the formation of levulinic acid. 7am formation studies DFC has been found to be the best carbonate monomer to achieve foams by the chemical foaming process S7, ESI †).However, the foam collapses rapidly when DFC or the other organic carbonates are polymerized without any agent to stabilize the micro gas seeds when polymerization starts within the monomer melt.In order to achieve a high volume enlargement, the displaced carbon dioxide must be trapped as small bubbles in the reaction media.For this purpose a polydimethylsiloxane-based surfactant with methoxy-terminated ethylenoxide side chains (Fig. 1) was used as a dispersing agent while the polymerization mixture was vigorously stirred.Attempts to use other dispersing agents such as aerosil® (Ox50, 300) or polydimethyl siloxane (PDMS) give no satisfactory results (Fig. S8, ESI †).Nevertheless, the anisolic resins produced by this procedure show no high volume enlargement.Only mMBC/1TO/S_150 (Fig. 7f ) has extended to 5-fold the volume of the monomer melt.A reason for this fact could be the increasing viscosity due to higher possibility for crosslinking in mMBC.Due to its reactivity and formation of side reactions, DFC shows the best results in foam formation (DFC/ S_60 Fig. 7h) even without using a crosslinking additive.A volume enlargement to 10-fold regarding the monomer volume can be observed.The SEM image of DFC/S_60 (Fig. 7h) shows a mixture of open-and closed-cell microstructure. 1 The problem during cationic polymerization of mMBC and pMBC seems to be the low viscosity of the mixture during polymerization and CO 2 elimination.Therefore, the gas does escape while the polymers are not yet sufficiently solidified.
The thermal properties of the anisolic and polyfurfuryl alcohol resins were studied by DSC measurements (Fig. 8).It is conspicuous that the polymer mMBC/TO_100, which was synthesized at only 100 °C, exhibits a strong exothermic peak in DSC measurement (Fig. 8).A subsequent heating does release the chemical bonded CO 2 which was proved with TG-MS measurement (Fig. S9, ESI †).
The TO quantity was varied in the ratios 1, 2, 4 and 6 regarding the methylene bridges per monomer unit (Table S2, Fig. S10, ESI †) in order to increase the viscosity of the mixture during the pre-polymerization of mMBC.However, a higher volume expansion cannot be achieved when a higher content of the crosslinking agent is used.In the ATR-FTIR spectra,  increased carbonyl vibration bands from the 1 to 4 TO ratio occurred and a decrease in the extractable content with dichloromethane (DCM) (Table S2, ESI †) was observed.After extraction of soluble fractions, the carbonate structure remains in the crosslinked polymer.The extractable content and the thermal stability also show the good cross-linking ability of mMBC.During extraction with DCM the anisolic resin pMBC/ 4TO/S_100 loses 89.2 wt% of its mass, whereas mMBC/4TO/ S_100 has a mass loss of only 12.9 wt% (Table S2, ESI †).
Additionally, the pyrolysis of pMBC/4TO/S_100 and mMBC/ 4TO/S_100 shows a mass loss of 37.3 wt% and 50.0 wt% (Table S2, ESI †), respectively.Moreover, a higher content of TO increases the thermal stability of mMBC polymers during pyrolysis.As well, it is found that the more intensive the carbonate vibration band (Fig. S11b †) the more carbonate structures are present in the polymer.This leads to a higher mass loss (Table S2, ESI †) during the annealing process at 250 °C (Ar) and TG analysis (Fig. S9, ESI †) at 300 °C (He).However, no additional volume enlargement was observed after annealing.In SEM images all samples show closed and open isolated spherical bubbles on the surface. 1 For samples with 2 and 4 TO, areas with fine-porous structures (SEM Fig. S15, ESI †) are found.By addition of TO, the polymerization of pMBC at 100 °C (Table S2 †) leads to a dense monolith (Fig. S10, ESI †) without any volume expansion and no carbonate vibration band in ATR-FTIR spectra (Fig. S11b, ESI †).
The polymerization of mMBC with 1 TO at 90 °C results in an increasing viscosity which inhibits the fast escape of the blowing gas in a thermal pre-annealing process at 250 °C.The obtained foam mMBC/1TO/S_90-A is shown in Fig. 9d.The SEM image of mMBC/1TO/S_90 (Fig. 9c) shows a flat structure.pMBC/1TO/S_90 (Fig. 9a) exhibits roundly shaped cavities in the SEM images due to CO 2 elimination.After annealing of pMBC/1TO/S_90, flat structures were found, whereas mMBC/ 1TO/S_90-A (Fig. 9d) is foamed under formation of open-and closed-cell microstructures. 1 The TG-MS measurements (Fig. 10) show for mMBC/1TO/S_90 a higher mass loss of 16.7 wt% in contrast to 9.9 wt% for pMBC/1TO/S_90.During these mass losses only mMBC/1TO/S_90 releases carbon dioxide which was monitored by MS measurement (Fig. 10, m/z = 44).The mass loss of pMBC/1TO/S_90 is due to the release of carbon monoxide and water regarding the thermal degradation of the polymer. 316][37] Thus, the polymer foams were converted into carbon foams by pyrolysis at 800 °C in an Ar atmosphere.
In order to determine the porosity and pore volume of the material, two selected carbon foams were investigated by means   of mercury porosimetry (Table 3, Fig. S16, ESI †). 38,39DFC/S_60-P has a high porosity of 87% and high pore volume, whereas mMBC/1TO/S_90A_P has only a porosity of 21% (Table 3).Both carbon foams have irregular pore sizes (Fig. S11, ESI †), but DFC/S_60-P shows smaller average pore diameters of 77 μm (Table 3).With nitrogen sorption measurements only very low specific surface areas could be measured. 40Thus, no micro-and meso-pores are present in the carbon foams.

Conclusions
The cationic step-growth polymerization of organic carbonates derived from furfuryl alcohol and methoxy-substituted benzyl alcohols has been presented as a suitable method to produce foamy resins by chemical processing.The gaseous carbon dioxide release in melt is the tool to obtain foams directly during polymerization.para-Toluenesulfonic acid is a suitable catalyst when dissolved in the monomer melt at a temperature which is lower as needed for the polymerization process.Both, polymerization and foam formation take place simultaneously by appropriate heating.Importantly, the use of an appropriate surfactant is essential to reproducibly produce foams of high volume expansion.
It is striking that the process of carbon dioxide release is a function of the carbenium ion stability of the reactive monomer fragment.The better the carbenium ion is stabilized by the aryl substituent, the more efficient is the carbon dioxide release directly during the polymerization.Thus, the associated foam formation enhances in the order of mMBC < pMBC < DFC.DFC is found to be the best monomer for this purpose.The m-methoxy substituent is less suitable to stabilize a carbenium ion, but it improves the reactivity of the aromatic ring.mMBC readily undergoes Friedel-Crafts polymerization with 1,3,5-trioxane under maintenance of the carbonate moiety.This type of resin is suitable as a polymeric precursor to trigger foam formation by a post-thermal treatment.Future work is suggested to use these carbonate monomers in simultaneous polymerization with twin monomers to fabricate inorganic-organic hybrid foams which can be converted into micro-and meso-porous carbon foams.

Fig. 1
Fig. 1 Molecular structure of the silicone polyether surfactant.
1 H-NMR studies of the monomers by acid treatment in solution (CDCl 3 ) were performed (Fig. S1, ESI †).The 1 H-NMR spectra show a decrease of the carbonate concentration as a function of the reaction time while methylol signals (-CH 2 OH) between 4.4 and 4.7 ppm and the signals of methylene-bridges (-CH 2 -) (3.3 and 4.0 ppm) appear.NMR-spectra series are shown in Fig. S1, ESI.† Traces of methylether bridges (-CH 2 OCH 2 -) in the region of 4.4 and 4

Fig. 3
Fig. 3 TG-MS curves of the carbonates pMBC, mMBC and DFC while adding pTS.The emission of CO 2 (m/z = 44) and water (m/z = 18) was monitored with mass spectrometry.

Scheme 4
Scheme 4 Acid induced step growth polymerization of (a) pMBC and (b) mMBC with addition of 1,3,5-trioxane as a curing agent.pMBC directly forms an anisolic resin network under the release of carbon dioxide, whereas mMBC is crosslinked while a portion of the carbonate units remains intact.Possible positions for electrophilic substitution are marked.Fig.4SEC profiles of the soluble anisolic resins.

Fig. 5
Fig.5 (a, b) Possible molecular structures and (c) solid-state13 C-{ 1 H}-CP-MAS spectra of the anisolic resin obtained from pMBC (dashed lines) and mMBC (full lines) compared with the polymers crosslinked by TO.

Fig. 6
Fig.6Solid-state13 C-{ 1 H}-CP-MAS spectrum of the polyfurfuryl alcohol obtained from DFC and the assignment of the different carbon atoms to molecular structures moieties.

Fig. 7
Fig. 7 SEM images of the polymerization products of (a) pMBC_150, (b) mMBC_150 and (c) DFC_60 in comparison to the polymers where 1,3,5trioxane (TO) and/or a surfactant (S) was used.The inset shows the macroscopic image of the foams.The label of the picture indicates the used additive and reaction temperature.

Fig. 9
Fig. 9 Pictures and SEM images of the anisolic resins (a) mMBC/ 1TO_90 and (c) pMBC/1TO_90 produced at 90 °C with 1,3,5-trioxane.The polymers were annealed (A) at 250 °C in a second step.(d) mMBC/ 1TO_90-A shows a volume enlargement and a change of its morphology from a flat surface to open-and closed-cell microstructures.

Fig. 10
Fig. 10 TG-MS measurements of anisolic resins obtained by cationic polymerization of pMBC and mMBC at 90 °C.The emission of CO 2 (m/z = 44) was monitored with mass spectrometry (MS).

Table 2
Corresponding results of the SEC profiles of soluble anisolic resins referenced to the polystyrene standardSampleM n [g mol−1] M w [g mol−1] PDI