FLEXIBLE OR SEMI-FLEXIBLE FOAM COMPRISING A POLYESTER POLYOL

Abstract

A flexible or semi-flexible foam, or a composition making it possible to obtain a flexible or semi-flexible foam, including a polyester polyol or a polymer comprising a polyester polyol. The polyester polyol is obtained by a first polycondensation (a) of an alcohol sugar Z in C3 to C8 and of two identical or different diacids Y and Y in C4 to C36 and a second polycondensation (b) of the product obtained in (a) with two identical or different diols X and X in C2 to C12.

Claims

1-14. (canceled)

15. A flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam comprising a polyester polyol or a polymer comprising a polyester polyol, said polyester polyol is obtained by a first polycondensation (a) of a C3 to C8 sugar alcohol Z and two identical or different C4 to C36 diacids Y and Y and a second polycondensation (b) of the product obtained in (a) with two identical or different C2 to C12 diols X and X.

16. A flexible or semi-flexible foam or a composition making it possible to obtain a flexible or semi-flexible foam comprising a polyester polyol or a polymer comprising a polyester polyol, said polyol polyester has the general formula Rx-Ry-ZRy-Rx wherein Z is a C3 to C8, preferably C4 to C7, typically C5-C6 sugar alcohol, Ry and Ry are diesters having formula OOCCn-COO with n between 2 and 34, preferably, between 3 and 22, typically between 4 and 10, Rx and Rx are identical or different C2 to C12, preferably C3 to C8, typically C4 monoalcohols.

17. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 15, wherein the sugar alcohol Z is chosen from glycerol, sorbitol, erythritol, xylitol, araditol, ribitol, dulcitol, mannitol and volemitol.

18. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 15, wherein the diacids Y and Y are independently chosen from butanedioic acid, pentanedioic acid, hexanedioic acid, heptanedioic acid, octanedioic acid, nonanedioic acid, decanedioic acid, undecanedioic acid, dodecanedioic acid, tridecanedioic acid, tetradecanedioic acid, pentadecanedioic acid, hexadecanedioic acid and mixtures thereof.

19. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 15, wherein the diols X and X are independently chosen from 1.2-ethanediol, 1.3-propanediol, 1.4-butanediol, 1.6-hexanediol, 1.8-octanediol, 1.10-decanediol, 1.12-dodecanediol and mixtures thereof.

20. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 15, further comprising at least one reaction catalyst, at least one swelling agent, a stabilizer, at least one polyisocyanate having a functionality at least equal to 2, optionally, at least one co-polyol.

21. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 15, further comprising at least one C2 to C8, preferably C3 to C7 co-polyol.

22. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 21, having a polyol polyester/co-polyol(s) ratio from 70/30 to 99/1, preferably, 75/25 to 95/5.

23. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 21, wherein the at least one co-polyol is chosen from ethylene glycol, glycerol, sorbitol, erythritol, xylitol, araditol, ribitol, dulcitol, mannitol and volemitol.

24. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 15, further comprising two co-polyols, typically in a ratio between 95/05 to 50/50, preferably 87/13 to 60/40.

25. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 15, further comprising two co-polyols chosen from glycerol and sorbitol, glycerol and erythritol, glycerol and xylitol, glycerol and araditol, glycerol and ribitol, glycerol and dulcitol, glycerol and mannitol or glycerol and volemitol.

26. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 15, comprising 50 to 130 parts of polyester polyol, 0 to 50 parts of at least one co-polyol, 100 to 500 parts of at least one polyisocyanate, 0.5 to 5 parts of at least one catalyst, 0 to 40 parts of at least one swelling agent 0 to 5 parts of a stabiliser and 0 to 20 parts of a flame retardant.

27. A panel or a block of flexible or semi-flexible foam comprising a flexible or semi-flexible foam according to claim 15, typically for thermal, sound or cryogenic insulation or for the filling of empty space or buoyancy assistance or for the damping of impacts and vibrations or for filtration.

28. A method for thermal, sound or cryogenic insulation, sealing or improving of the flotation, damping of impacts and vibrations or filtration through the deposition or the introduction of blocks or of panels comprising the flexible or semi-flexible foam according to claim 15 or by the spraying of the flexible or semi-flexible foam or of a composition making it possible to obtain the flexible or semi-flexible foam.

29. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 16, wherein the sugar alcohol Z is chosen from glycerol, sorbitol, erythritol, xylitol, araditol, ribitol, dulcitol, mannitol and volemitol.

30. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 16, further comprising at least one reaction catalyst, at least one swelling agent, a stabilizer, at least one polyisocyanate having a functionality at least equal to 2, optionally, at least one co-polyol.

31. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 16, further comprising at least one C2 to C8, preferably C3 to C7 co-polyol.

32. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 31, having a polyol polyester/co-polyol(s) ratio from 70/30 to 99/1, preferably, 75/25 to 95/5.

33. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 31, wherein the at least one co-polyol is chosen from ethylene glycol, glycerol, sorbitol, erythritol, xylitol, araditol, ribitol, dulcitol, mannitol and volemitol.

34. The flexible or semi-flexible foam or composition making it possible to obtain a flexible or semi-flexible foam according to claim 16, further comprising two co-polyols chosen from glycerol and sorbitol, glycerol and erythritol, glycerol and xylitol, glycerol and araditol, glycerol and ribitol, glycerol and dulcitol, glycerol and mannitol or glycerol and volemitol.

Description

BRIEF DESCRIPTION OF THE FIGURES

Figures

[0088] FIG. 1: Foaming profile: evolution of the temperature (a), maximum height (b) and the foaming rate (c) with respect to the time of the foaming step

[0089] FIG. 2: a. FTIR spectra of formulated foams, b. FTIR spectra zoomed on the absorption zone of isocyanurates

[0090] FIG. 3: a. ATG curves of PU foams, under dry air, b. Derivative from ATG curves for PU foams, under dry air

[0091] FIG. 4: SEM image of PU foams in the transverse (T) and longitudinal (L) directions in the rising direction of the foam

[0092] FIG. 5: a) Module of conservation, modulus of loss and evolution of Tan of REF, and b) Evolution of Tan of REF and the bio-sourced foams

[0093] FIG. 6: Strain curves of REF and B100-2 bio-sourced foam, in a) longitudinal direction, b) transverse direction

[0094] FIG. 7: Deformation-stress curves of bio-sourced PU foams, in a) longitudinal direction, b) transverse direction

EXAMPLE

1. Material and Method

[0095] a. Reagents

[0096] Sorbitol was supplied by the company TEREOS (MERITOL, 98%, water content <0.5%, reducing sugar content <0.1%). 1,4-Butanediol (BDO, 99%) was obtained from SIGMA ALDRICH. Adipic acid (AA) (99%) was obtained from ACROS ORGANICS. Polyol polyether is an oxypropylated polyol of the company Huntsman (Daltolac R570), with an average functionality of 3.0 and an OH value of 570 mg KOH/g. The polyisocyanate is 4,4-methylenebis (diphenyl isocyanate) (MDI) polymer BORSODCHEM (ONGRONAT 2500). Two typical catalysts for the polyurethane foam were used: N, N-dimethylcyclohexylamine (DMCHA) and the 15% by weight solution of potassium 2-ethylhexanoate (KB) from MOMENTIVE and BORSODCHEM, respectively. The flame retardant is SHEKOY Tris (1-chloro-2-propyl) (TCPP) phosphate, the surfactant was polydimethylsiloxane (B84501) obtained from EVONIK and glycerol (gly) (99.5%) was obtained from FISHER SCIENTIFIC. INVENTEC isopentane was used as a physical swelling agent.

[0097] All of these chemicals were used as received without further purification.

[0098] b. Synthesis of a Polyester Polyol Based on Sorbitol (BASAB)

[0099] The sorbitol-based polyester polyol was synthesized by a two-step bulk polycondensation from sorbitol, 1,4-butanediol and adipic acid. One molar equivalent of sorbitol and two molar equivalents of adipic acid were charged into a 600 ml Parr thermoregulated reactor (Model No. 4568) equipped with a heating mantle, a mechanical stirrer with a U-shaped blade, a thermocouple, a Dean Stark having an output at the top of the capacitor to be able to link a vacuum pump and a low output to recover the condensate, an inlet and an outlet of inert gas. The medium was heated at 150 C. for three hours and then 2 molar equivalents of 1,4-butanediol relative to sorbitol were added. The reaction was continued for another six hours. Finally, the reactor was cooled to 60 C. and the residual acidity of the unreacted adipic acid was neutralized by the addition of an appropriate amount of K.sub.2CO.sub.3.

[0100] A viscous yellow polyol (BASAB) was recovered from the reactor and the general properties of BASAB are summarized in Table 1 and compared to the petrol-sourced polyether polyol. Further details concerning this synthesis are given in the patent application FR 16/01253.

TABLE-US-00001 TABLE 1 Reference and BASAB polyol Dynamic OH index - Acidity index - Median functionality Viscosity at titration (mg titration (mg Primary Secondary 25 C. (mPa .Math. s) KOH/g) KOH/g) hydroxyls hydroxyls petrol-sourced 670 570 Inferior to 5 3.0 (terminal) polyether polyol BASAB 24 300 200 382 9 3.4 0.8 2 4

[0101] c. Synthesis of PU Foams

[0102] PU foams were prepared with an isocyanate/hydroxyl (NCO/OH) molar ratio of 1.15. In order to determine the isocyanate content, all the reactive hydroxyl groups are taken into account, that is to say the polyols, the water and the possible solvents associated with the different catalysts. On the basis of the two-component foaming process, a premix containing polyol(s), catalysts, surfactant (polydimethylsiloxane, B84501), flame retardant (TCPP) and the swelling agent (s) is prepared. The swelling agents were chosen between isopentane (physical swelling agent) and water (chemical swelling agent). The total ratio of swelling agent remains constant in all formulations. In each preparation, the number of TCPP and surfactant parts is constant and equal to 10 parts for TCPP and 2.5 parts of surfactants. The total amount of polyol never exceeds 100 parts. When crude crystalline polyols such as sorbitol are used, they are first dissolved in water to break the crystallinity and increase their reactivity.

[0103] The mixture is stirred mechanically until a fine white emulsion is obtained with total incorporation of the swelling agent. The temperature of the mixture is controlled and adjusted to 20 C. The temperature of the polyisocyanate is also controlled and an adequate amount thereof is added rapidly to the emulsion. The whole reaction mixture is vigorously stirred for 5 s and then foamed freely in a 250 ml disposable beaker at room temperature (controlled at 20 C.) to monitor the kinetics of the foam or in the FOAMAT device. For further analysis, the foam samples were stored for three days at room temperature for complete maturation of the foam.

[0104] d. Characterization of the Foams Obtained

[0105] Thermogravimetric (TGA) analyzes were performed using a TA Hi-Res TGA Q5000 instrument in reconstituted air (flow rate 25 mL/min). 1-3 mg samples were heated from room temperature to 700 C. (10 C./min). The main characteristic degradation temperatures are those at most of the derivative of the weight loss curve (DTG) (Tdeg, max).

[0106] Infrared spectroscopy was performed with a NICOLET 380 Fourier transform infrared spectrometer used in reflection mode equipped with an ATR diamond module (ATR-FTIR). An atmospheric background was collected before the analysis of the sample (64 scans, 4.sup.1 cm resolution). All spectra were normalized to a stretch peak of the CH bond at 2950 cm.sup.1. Dynamic mechanical analysis (DMA) was performed on TRITEC 2000 (Triton) compressive devices. The samples were analyzed at a constant frequency of 1 Hz for a temperature range of 30 to 270 C. with a heating rate of 2 C./min and a constant static resistance of 0.5 N. Samples were 7.57.57.5 mm.sup.3.

[0107] The quasi-static compression tests were carried out with an INSTRON dynamometer (E1000, USA), equipped with a load sensor of 1 KN, at room temperature and at a constant strain rate of 2.5 mm/min. The cubic samples used for the compression tests have dimensions of 25*25*25 mm.sup.3. Samples were tested in the longitudinal direction (corresponding to foam expansion during the process) and in the transverse direction. Young's modulus was defined as the slope of the stress-strain curves in the elastic region and the elasticity rate as the first maximum of the stress curve.

[0108] Thermal conductivity was measured from the heat flux. Typically, the device consists of a heating element with two thermocouples to obtain the temperature on the front and rear surfaces. The device is also equipped with two sensors dedicated to the measurement of heating time and cycle time. The heating and cycle times are used to correct the maximum conduction heat flux, which is necessary for the calculation of the thermal conductivity coefficient, by the Fourier law, used in steady-state thermal conduction. Plates of different materials with dimensions of 300*400*3 mm.sup.3 were used for the determination of the thermal conductivity coefficient.

[0109] The temperature of the foams, the heights and the rate of expansion, the density and the pressure of the foam were recorded using a FOAMAT FPM 150 (Messtechnik GmbH) equipped with cylindrical containers of 180 mm height and 150 mm diameter, an ultrasonic probe LR 2-40 PFT recording the height of the foam, a NiCr/Ni type K thermocouple and a FPM 150 pressure sensor. The data was recorded and analyzed with specific software.

[0110] The open cell count is determined using a Quantachrome Instruments Ultrapyc 1200e based on the technique of gas expansion (Boyle's Law). Cubic samples of foams (approximately 2.5 cm2.5 cm2.5 cm) are cut for a first measurement. Then, the cubic sample was cut into eight equivalent pieces and the measurement was repeated. This second measure makes it possible to correct the level of the closed cells from the damaged cells because of the cutting of the sample. Measurements were made according to EN ISO4590 and ASTM 6226.

[0111] Measurements of the apparent density of the foams were carried out according to the standard method EN 1602.

[0112] Foam cell morphology was observed on a HITACHI TM-1000 Field Emission Scanning Electron Microscope (SEM). The cube-shaped foam samples were cut with a microtome slide and analyzed in two characteristic orientations, longitudinal and transverse from the direction of the rise of the foam.

2. Results and Discussion

[0113] Five foams have been formulated, the detailed formulations are presented in Table 2. A petrol-sourced foam (hereinafter REF) is used as a reference. Formulations B85-2, B85-4, B100-2 and B100-4 are bio-sourced foams to be evaluated. The characteristics of the formulations as well as the kinetics of the foams obtained are presented in Table 2. The reference foam (REF) has the fastest kinetics with a cream time of 10 s, while all bio-sourced foams are up to 15 s. A 15 s cream time is an acceptable time for the formulation of such foams especially for foam panels continuously produced for the insulation of buildings.

TABLE-US-00002 TABLE 2 Formulation and Characteristics of PU Foams REF B85-2 B85-4 B100-2 B100-4 Formulation polyol Petrol- BASAB + BASAB + BASAB BASAB based gly + gly + sorbitol sorbitol Ratio de polyol 100 85 + 10 + 5 85 + 10 + 5 100 100 (parts) Physical 15.04 19.28 13.20 12.25 4.14 swelling agent (parts) Chemical 1.60 1.60 4.14 1.60 4.14 swelling agent (parts) Reference Cream (s) 10 27 16 15 22 times of String (s) 44 122 90 70 60 Tack-free (s) 66 300 210 115 110

[0114] The tack-free time is a surface indication of the formation of the PU network, but is not indicative of the end of the foaming process. According to this parameter, the polymerization stage of REF ends at the surface in 66 s, the other bio-sourced foams have times greater than 100 s. The tack-free time offset indicates a lower end-of-foaming reactivity. Thus, in the case of bio-sourced formulations, the entire polyurethane network is reached at longer times than for petrol-sourced foams. This can be particularly advantageous in the case of production of foam blocks by molding.

[0115] The measurements made by FOAMAT indicate that the reference foam REF reaches its highest expansion speed of 5 mm/s (FIG. 1, c) by 40 s, and by 70 s reaches its maximum height of 160 mm (FIG. 1, b). This expansion rate is a direct consequence of the exothermic polyaddition between the isocyanate and hydroxyl functions exhibiting a reaction enthalpy of 100.32 kJ/mol (M. lonescu, polyol chemistry and polyol technology, Rapra Technology, Shawbury, Shrewsbury, Shropshire, United Kingdom, 2005), the internal temperature of REF is stabilized only after 210 s at 170 C., indicating the complete polymerization time of the PU network. Foam B100-2 is the bio-sourced equivalent of REF and the FOAMAT measurement (FIG. 1) clearly indicates the effect of the polyol change from a petrol-sourced polyether to a bio-sourced polyester on the foaming temperature, the speed of expansion as well as the evolution of the foam height.

[0116] Thus, for the bio-sourced foam B100-2, the expansion rate is five times lower than that of REF. At the same time, the attained foam temperature during the foaming step for B100-2 is lower than for REF. The decrease in these two measures is indicative of a lower reactivity of the polyester (BASAB bio-sourced) compared with that of the polyether (petrol-sourced). This lower reactivity is explained by the lower accessibility of the secondary hydroxyl groups and the lower reactivity of the terminal hydroxyl groups of the bio-sourced polyester compared to the reference polyether.

[0117] The temperature curve B100-2 (FIG. 1, a) shows a delay of nearly 60 s compared to REF, corresponding to the time required for the system to reach the reaction temperature. This difference between B100-2 and REF is a direct consequence of the foaming speed. A similar profile is also observed on all the temperature curves of bio-sourced foams. This slower foaming rate does not represent a limit at the industrial level since it may vary depending on the catalyst used and may represent an advantage in molding processes to allow complete filling of the mold before polymerization of the foam.

[0118] An effect of the content of chemical swelling agent and in particular of water of the mixtures was also observed on the foaming parameters. Thus, the B100-4 foam was formulated with a higher water content than the B100-2 and REF mixtures. However, there is an improvement in the foaming parameters of B100-4 compared to B100-2 and REF. More particularly, B100-4 shows shorter string and tack-free times of 10 s and 5 s respectively compared to B100-2 (Table 2). Thus, the formulation B100-4 is advantageous in that it has foaming characteristics close to the petrol-sourced reference formulation (REF). Nevertheless, the formulation B100-2 remains of interest in that it allows a sufficiently long working time and suitable for production in molding for example of foam blocks.

[0119] The effect of water on foaming would be related to the high reactivity between isocyanate and water, namely a reactivity twice as high as that between isocyanate and alcohol. The exothermicity of the water-isocyanate reaction is clearly visible on the evolution of the temperature of the B100-4 foam from 30 to 140 C. at 47 s. Thus, there is an expansion rate for B100-4 which is respectively 1, 6 and 4 times greater than REF and B100-2, with an equivalent foam height.

[0120] In addition, if REF, B100-2 and B100-4 are compared, it is observed that the increase in the water content of the mixture compensates for the lower reactivity of BASAB and makes it possible to obtain a mixture having very good characteristics. temperature (FIG. 1a) expansion rate (FIG. 1c). Indeed, we observe that the expansion rate of B100-4 is 4 times higher than that of B100-2. B100-4 achieves a maximum expansion speed of 8 mm/s higher than that of REF which is 5.5 mm/s. In addition, the maximum temperature reached during the reaction increases by 20 C. between B100-2 and B100-4.

[0121] Consequently, compositions based on bio-sourced products having a good reactivity and therefore a foam kinetics completely comparable to that of petrol-based compositions in terms of temperature and rate of expansion can be obtained according to the invention.

[0122] In order to optimize the foaming kinetics, the impact of short, non-volatile and highly reactive polyols such as sorbitol and glycerol in the start of the foaming process has been studied (Table 2).

[0123] Compositions comprising only BASAB (B100-2 and B100-4) as a polyol or comprising a BASAB mixture, glycerol and sorbitol in a BASAB/glycerol/sorbitol ratio of 85/10/5 (B85-2 and B85-4) have been prepared.

[0124] The compositions B85-2 and B100-2 are distinguished from each other solely by the presence or absence of these small polyols. It is the same for the compositions B85-4 and B100-4. Thus, comparing the expansion rates of the B85-2 and B100-2 foams shown in FIG. 1 clearly shows the high reactivity of the BASAB-short diols mixture, compared to BASAB alone. Indeed, the expansion speed of the B100-2 foam never exceeds 2 mm/s, while that of B85-2 exceeds 3 mm/s. The effects of this high reactivity are also visible on the foaming temperature of B100-2, shown in FIG. 1a, which is 40 C. lower than that of B85-2. The resulting expansion of the foam is affected by the lowest temperature (FIG. 1b). The B85-2 foam height is twice as high as the B100-2 foam height, while they both have the same amount of swelling agents. Thus, with an identical amount of swelling agent, the BASAB glycerol and sorbitol mixture in a 85/10/5 BASAB/glycerol/sorbitol ratio shows a clear effect on the profile of the foaming kinetics of the formula and therefore on the height. as well as the final density of the foam.

[0125] It has been previously shown that for formulations containing BASAB, the increase in the water content of the mixture (B100-2 versus B100-4) offers a significant increase in the reactivity of the foam.

[0126] In the case of formulations containing the BASAB, glycerol and sorbitol mixture, the increase in the water content of the mixture (B85-2 versus B85-4) has no noticeable effect on the foaming kinetics. Indeed, the observed foam heights and temperatures are similar (FIGS. 2a and 2b).

[0127] If we compare this time the B85-4 and B100-4 formulations containing a high-water content and distinguished by the presence (B85-4) or not (B100-4) of short polyols, we observe a foaming profile faster for the formulation comprising BASAB alone. Indeed, the maximum foaming rate of the formula B100-4 is reached at a maximum value of 8 mm/s in 50 s, then decreases rapidly. While for formula B85-4, a maximum value of 3.5 mm/s in 100 s is observed. The main hypothesis explaining this phenomenon is the formation of channels inside the foam, obtained by deformation and coalescence of low mechanical resistance cells made of weakly crosslinked polymers. This phenomenon is promoted by the presence of short diols in the B85-4 formulation, which can act as a crosslinking agent. This hypothesis can be confirmed later with a study in SEM.

[0128] Compositions B85-2 and B85-4 both contain a BASAB mixture, glycerol and sorbitol, the B85-4 composition being distinguished by a high-water content. The resulting B85-2 and B85-4 foams reach a similar height with respect to the REF foam. Nevertheless, variations in expansion speed and temperature are observed.

[0129] Indeed, there is an increase in the temperature of the B85-2 foam after 60 s and a low foaming rate of 2 mm/s which is kept constant for 80 s. These variations can be attributed to the reaction of the short diols with the isocyanate functions carried by the polyisocyanates chosen for the formulation. When the temperature reaches 80 C., the BASAB polyol begins to react vigorously with free isocynate functions. There is then an increase in the foaming rate of B85-2 from 2 to 3 mm/s. A change in the slope is visible on the temperature curve shown in FIG. 1a. These evolutions are direct consequences of the increase in the exothermicity of the polymerization. Comparatively, in the B85-4 formulation comprising the BASAB glycerol and sorbitol mixture and a high-water content, the effect related to the high-water content masks that of the short polyols. Thus, during foaming, the temperature and the foaming speed increase drastically and the foam reaches a maximum height in 20 s (see FIGS. 1a, 1b and 1c) because of the highly exothermic reaction between the polyisocyanate and the water as previously explained.

[0130] As a result, the reactivity of the bio-sourced polyester polyol differs greatly depending on the foaming temperature and can be adapted using the combined or non-combined effects of swelling agent such as water and short diols such as glycerol and/or sorbitol.

[0131] Water is a chemical swelling agent and is the simplest way to increase the rate of expansion, but it also results in an increase in the urea bond content in the final foam. As these bonds induce a stiffness of the segments, the increase in their presence should affect the mechanical properties of the foam.

[0132] In view of the above results, it has been shown that the water content of the composition and thus the production of urea bonds can be limited by combining BASAB with short polyols such as glycerol and sorbitol. Indeed, they act as a reaction inducer and facilitate the physical expansion of the foam limiting the formation of urea.

[0133] The analysis of the chemical composition of the PU foams was carried out by infrared spectroscopy (FT-IR). Functional groups linked to PUs and polyisocyanurates (PIRs) were targeted (FIG. 2a). This analysis makes it possible to obtain a spectrum (FIG. 2a) presenting different peaks. The large peak at 3300 cm.sup.1 corresponds to the stretching of the NH groups. The peak at 2270 cm.sup.1 corresponds to the residual free NCO. The presence and value of these peaks are consistent with the NCO/OH molar ratio of the formulation of 1.15. The hydroxyl groups are visible by the deflection of the baseline up to 3600 cm.sup.1. These groups are certainly secondary non-reactive hydroxyl groups of BASAB. The NH groups also show a torsion signal at 1510 cm.sup.1. The broad peak at 2950 cm.sup.1 corresponds to the stretching of the CH bond present in the PU backbone and the signal at 1595 cm.sup.1 corresponds to at the ArH stretch of the phenyl groups of the polyisocyanate (M. Rogulska, AJ Therm. Anal. calorimeter. 114 (2013) 903-916). Several peaks were attributed to the urethane function, including CO stretch with hydrogen bonds at 1709 cm.sup.1, CO stretch at 1220 cm.sup.1 and then the two peaks merged at 1062 cm.sup.1 and 1017 cm.sup.1 associated with symmetric stretching of NCOO bonds and stretching of CO bonds (B R Barrioni, Mater. Sci. Eng. C. 52 (2015) 22-30).

[0134] The urea functions have already been described (A.M.B.M. MUSTAFE, FTIR studies on 2K polyurethane paint, 2005) as found in the form of a broad peak at 1647 cm.sup.1. It has been assumed that their low urethane content induces a weaker signal at the origin of the offset from the baseline of the spectrum signal in the 1700-1600 cm.sup.1 region. Then, the last important peak appearing on all the spectra at 1412 cm.sup.1 is attributed to the isocyanurate absorption band. He indicates that even in the PU formulation with small isocyanate function excess, a small amount of isocyanurate is formed. The amount of isocyanurate bound to peak intensity (FIG. 2b) shows a good correlation with the previously recorded foam temperature. This is consistent with the high temperature required to obtain the PIR material (Hofmann-1870-Berichte_der_deutschen_chemischen_Gesellschaft.pdf, (n.d.)). The triisocyanuric rings thus introduced into the foam increase the degree of crosslinking of the foams concerned. In conclusion, foams obtained from bio-sourced products (BASAB alone or in admixture with glycerol and sorbitol) are in the same way as the petrosourced foams (REF) polyurethane-isocyanurate (PUIR) foams.

[0135] In order to determine the temperature resistance of the foams, a thermogravimetric analysis (TGA) was performed on each of the foams and made it possible to obtain ATG and DTG thermograms (see FIG. 3a). Weight loss following two-stage thermal degradation is observed for the reference composition. The first weight loss corresponds to the decomposition of the polyether urethanes and polyol, with a maximum of the DTG curve at 250 C. The second weight loss is attributed to cleavage of the carbon-carbon bond with a maximum on the DTG curve at 560 C. These results are in agreement with previous work reported in the literature (H. Ulrich, Recent Advances in Isocyanurate Technology, J. Cell. Plast. 17 (1981) 31-34; A. Arbenz, et al., J. Polym. About. (2017); A. Celzard, Polym. Degrad. Stab. 96 (2011) 477-482). The thermal stability of the foams is influenced by several parameters depending on the raw material initially used for the formulation.

[0136] For example, the decomposition temperature of the urethane group is influenced by its surroundings. It has been reported that the urethane function surrounded by two alkyls has an initial decomposition at 250 C., while surrounded by two aryl groups, it would start at 120 C. (J. Simon, Chromatographia. 25 (1988) 99-106). This decomposition is mainly induced by the thermal reversibility of the urethane function, according to the main decomposition pathways, which are the reverse reaction, the dissociation, the formation of amines and the transcarbamoylation.

[0137] All bio-sourced foams have a lower thermal stability than the reference, with weight loss starting at 170 C. It should be noted that except in the case where a fire performance is required, the conditions of installation and use of the foams generally take place at temperatures well below 170 C. Therefore, the bio-sourced foams obtained represent an alternative of interest for many applications. The degradation of the foams as observed is complex because of the addition of the different chemical groups derived from the polyester polyol. In fact, the polyesters are subjected to two main impairments, which are the and hydrogen splits (H. Abe, Macromol. Biosci. 6 (2006) 469-486), resulting in competitive degradation with degradation of the urethane function. During this analysis, no particular effect related to the addition of the short polyols in the formulation was detected, since the DTG thermograms are similar for most bio-sourced foams.

[0138] Only the B85-4 sample with a BASAB, glycerol and sorbitol mixture and a high-water content shows different ATG and DTG thermograms. Its weight loss is slower than other bio-sourced foams. This is consistent with its formulation because its high-water content induces the formation of urea which is more thermally stable than the urethane function (D. K Chattopadhyay, J. Polym. Sci. Part B Polym. Phys. 44 (2006) 102-118). The latter foam therefore has better thermal stability than other bio-sourced foams and thus potentially has a better resistance to fire and high temperatures.

TABLE-US-00003 TABLE 3 Morphology of PU Foams REF B85-2 B85-4 B 100-2 B 100-4 Longitudinal Feret max, 376 91 432 157 443 146 362 134 408 122 direction D.sub.F.sup.max (m) Feret min, 194 39 227 69 174 47 173 58 110 25 D.sub.F.sup.min (m) D.sub.F.sup.max/D.sub.F.sup.min 1.96 0.35 1.92 0.47 2.60 0.8 2.17 0.76 3.78 0.93 Traversal Feret max, 217 33 350 114 232 66 277 100 380 88 direction D.sub.F.sup.max (m) Feret min, 182 33 245 77 170 47 171 52 104 28 D.sub.F.sup.min (m) D.sub.F.sup.max/D.sub.F.sup.min 1.21 0.15 1.46 0.36 1.38 0.25 1.65 0.42 3.79 0.97

[0139] The analysis of the morphology of the foams was carried out by a SEM analysis and coupled to an evaluation of the anisotropic ratio (R) of the cells of the foam. The SEM images presented in FIG. 4 show microstructures of foam samples in the longitudinal direction (L) and in the transverse direction (T) at the rise of the foam. Different and non-homogeneous structures with open-cell PU foams are obtained except with the reference, which has a homogeneous foam of closed cells.

[0140] In the longitudinal direction, all cells have a polyhedral form with clear anisotropy (R) (Table 3) and ellipsoid forms (R=1.9 to 3.8). This phenomenon is increased by the partially free foaming process used with foam growth in the longitudinal direction. In contrast, cells are more spherical in the transverse direction (1.21R1.65) with the exception of B100-4 (BASAB and high water content) where the cells are ellipsoidal in both directions.

[0141] In addition to the shape of the cells, the SEM images provide the overall structure of the foams. When comparing foams obtained from a formulation comprising BASAB and a high-water content, B100-4 exhibits extensively elongated cells at the origin of small pipes in the material. While B100-2 corresponding to the formulation with BASAB and a lower water content, is closer to a conventional open cell structure. This difference can be easily explained by the high content of chemical swelling agent (water) in B100-4.

[0142] Water is very reactive, it induces a rapid release of carbon dioxide creating pipes oriented inside the foam and breaking the honeycomb structure. A physical swelling agent has a softer expansion control by evaporation in the air microbubbles incorporated during mechanical stirring of the polyol premix (N. S. Ramesh, et al., Polym. Eng. Sci. 34 (1994) 1685-1697), which gives a more spongy structure.

[0143] The foam samples from a formulation with a mixture of polyols (B85-2 and B85-4) show a cellular structure with an inferion coefficient R compared to B100-2 and B100-4. Their cellular structure is related to a higher crosslinking density during the formation of the PU network in the foaming process. The higher crosslinking density is induced by the addition of polyfunctional glycerol and sorbitol which limit gas expansion and increase the rigidity of the material.

[0144] Consequently, the variable reactivity of BASAB as a function of the content of expansion agent or of small polyols (C2 to C6) during the foaming process makes it possible to adapt the cellular structure of the foams obtained. The structure of the foam having an impact on its mechanical properties, the BASAB therefore allows the following formulation to obtain foams of various mechanical qualities.

[0145] BASAB also makes it possible to obtain foams having different structural characteristics from foams comprising products that are petroleum-based in alveolar form.

[0146] However, it is close to structures of other petrochemical foams not presented in this study. It will be noted that this difference in morphology gives these bio-sourced foams properties of semi-flexible structures with a formulation similar to that of the petrol-sourced reference presented.

[0147] A tomographic analysis was performed (not shown) and confirms the observations to the SEM. Indeed, the tomographic images show a very complex structure, with a non-homogeneous shape and size of the cells in agreement with the SEM images.

[0148] In order to better characterize mechanically and thermally the foams obtained, the thermal conductivity coefficients and the apparent density of all the foams studied (Table 4). The apparent densities of all foams are between 23 and 41 kg/m and the apparent density of the reference foam is measured at 30.7 kg/m.sup.3. Of the bio-sourced foams, B85-2 foam has an apparent density greater than 2 kg/m.sup.3 compared to B85-4 foam samples and the B100-2 density is 16 kg/m.sup.3 greater than density B100-4. This means that foams with a higher water content are more expanded, which is in good correlation with the previous observation.

[0149] Thus, all bio-sourced foams with a higher water content exhibit a higher rate of expansion and a higher temperature inducing an increase in gas expansion in these foams compared to the REF or their counterparts containing less water. water (B 100-2 VS B100-4 and B85-2 VS B 85-4). This phenomenon is particularly marked for samples B100-2 and B100-4 where the increase in the quantity of water causes a decrease of nearly 40% of the apparent density.

TABLE-US-00004 TABLE 4 Characteristics of the foams Foam Chemical Apparent Longitudinal Percentage Thermal sample swelling density size of the of closed conductivity name agent (parts) (kg/m.sup.3) cells(m) cells (%) (mW/m K) REF 1.6 30.7 0.8 194 39 93 25 0.0013 B85-2 1.6 25.4 1.6 227 69 2 51 0.0042 B85-4 4.14 23.1 0.3 174 47 2 51 0.0021 B 100-2 1.6 41.2 3.5 173 58 10 40 0.0035 B 100-4 4.14 25.3 1.8 110 25 9 35 0.0015

[0150] Furthermore, it is found that the REF foam shows the lowest thermal conductivity value of 25 mW/m. K because of its high content of closed cells. In fact, the level of closed cells is responsible for 60 to 65% of the thermal properties of low density foams (H. Fleurent, J. Cell. Plast. 31 (1995) 580-599). Surprisingly, even if bio-sourced PU foams have a thermal conductivity of between 35 and 51 mW/mK, they have a majority of open cells. Indeed, these values of thermal conductivity are equivalent to those observed for the air (40 mW/(m.Math.K)) or glass wool (30 to 40 mW/(m.Math.K)) which are very good thermal insulators.

[0151] The polyurethanes and the polyurethane-urea have a heat capacity (Cp) within a range of 0.422 to 0.665 cal. g.sup.1.Math. C..sup.1 and 0.389 to 0.513 J.Math.g.sup.1.Math.K, respectively (J. E. Mark, ed., Polymer data handbook, 2nd ed., Oxford University Press, Oxford, New York, 2009). In general, the low Cp values of the polymers constituting the foams are an explanation for the low thermal conductivity of the material compared with non-polymeric materials such as metal foams. The B85-4 and B85-2 or B100-4 and B100-2 foams show close thermal conductivity to each oter, probably because of their equivalent closed cell rate and similar cell sizes.

[0152] In this case, relative density does not seem to play a major role. However, the thermal conductivity of the B100-4 and B100-2 foam systems is lower than B85-4 and B85-2. Bio-sourced foams are generally open systems, so the main difference between B100-4 and B100-2 is their bulk density. The thermal conductivity coefficient of the B100-4 foam is lower due to its low bulk density compared to B100-2. B85-4 and B85-2 have the same bulk density and similar closed cell levels, roughly the same cell sizes; it therefore seems normal that the two foam systems have the same coefficient of thermal conductivity.

[0153] The prepared bio-sourced foams have characteristics of interest in terms of thermal conductivity and therefore insulating properties comparable to that of petrol-based foams. The best results are obtained for bio-sourced foams with a formulation with high water content and in the absence of co-polyol.

[0154] Surprisingly, the bio-sourced foams have a small percentage of closed cells, especially compared to the petrol-sourced foam used as a reference for the base of the formulations. Nevertheless, a large number of open-cell petrol-based foams are available on the market and do not necessarily have as good thermal conductivity as BASAB-based bio-sourced foams.

[0155] A Dynamic Mechanical Analysis (DMA) was performed to characterize the viscoelastic properties of the foams as a function of temperature, in particular to define the typical relaxation temperatures of the polyurethane network constituting the foam. The evolution of the conservation module, the loss module and the loss factor (Tan ) as a function of the temperature for the reference (REF) is presented in FIG. 5-a). As commonly observed, the conversion module remains higher in the glassy region, before a sudden drop in the glass transition region. The Tan spectrum shows only a peak, which gives a relaxation temperature that can be associated with the glass transition temperature (Tg) of the soft segments of the foams. This temperature is about 200 C. for the PU foam samples. The dynamic mechanical analysis (DMA) tests performed on bio-sourced PU foams, show as expected a decrease in viscoelastic properties and Tg (FIG. 5-b and Table 5).

[0156] This confirms that in bio-sourced PU foams the mobility of the polymer chains is increased. This increase is mainly due to the presence of the residual OH groups, previously observed by FTIR in bio-sourced foams. The lowering of the relaxation temperatures and viscoelastic properties of bio-sourced foams makes it possible to deduce a decrease in their friability compared to the very rigid REF foam.

[0157] Thus, it is clear from the results reported in Table 5 that the conservation modules are similar for bio-sourced foams B100-2 and B10-4. On the other hand, the conservation module of the B85-4 bio-sourced foam is 1.65 times greater than the B85-2 foam conservation module. The slight increase in modulus of preservation and Tg for B85-4 foam compared to B85-2 foam is probably due to the presence of chemical swelling agent. As previously explained, this high level of chemical swelling agent leads to the formation of hard segments (due to the formation of urea linkages) in the material. All these variations in thermal and viscoelastic properties will be well explained in the section of mechanical properties.

[0158] The mechanical properties were evaluated by a 50% compression analysis of the foam samples. The various foams were analyzed on a plate compression bench in order to highlight the difference in compressive strength and resilience of the foams as a function of the orientation of the stress. These properties are evaluated by the measurement of the Young's moduli and conservation of different foam.

[0159] FIG. 6 compares the mechanical properties in compression of the reference and the bio-sourced foam B100-2, at ambient temperature in the longitudinal and transverse directions. In the case of a stress exerted in the longitudinal direction, it is observed that the stress increases linearly with the deformation (due to the elastic behavior of the two foams), before reaching the plastic yield point (FIG. 6a). After the plastic yield point, the stress remains almost constant due to the densification of the foam. In the case of a stress exerted in the transverse direction, the behavior of the foam is different (FIG. 6b). Indeed, after an elastic region to the point of plastic flow, the stress continues to increase, which corresponds to the densification of the foam. It has also been noted that the residual deformation after unloading is less than that in the longitudinal direction. This is a consequence of the structure of the cells oriented according to the rising direction of the foam (J. D'Souza, et al., J. Appl. Polym. Sci. 131 (2014)). This alignment leads to the development of anisotropic behavior which contributes to increasing the mechanical properties in the longitudinal direction relative to the transverse direction. The SEM observations and the Feret diameter results confirm the orientation of the cells. Furthermore, open cell porous structures of bio-sourced foams allow better air recirculation within the materials. Participating in reducing the residual deformation after unloading the compression stress. This is particularly marked for formulations B85-2 and B85-4 whose residual deformation is less than 10%.

[0160] The difference observed between the mechanical properties of the foams depending on whether the stress exerted is longitudinal or transverse could be explained in the following manner After the elastic region, observed for all the foams, the structure of the cells oriented in the longitudinal direction breaks under the loading at the origin of the observed residual deformation. While in the transverse direction, the shape of the elongate cell is more likely to undergo greater deformation before breaking. These hypotheses are supported by the work of J. Anderson et al (J. Andersons, et al., Mater. Of. 92 (2016) 836-845), whose work has focused on the stiffness and strength of closed-cell polyisocyanurate foams and the anisotropy of foam stiffness between the longitudinal and transverse directions.

[0161] Compared to the reference, the B100-2 bio-sourced foam has different mechanical properties, with a Young's modulus and a lower plastic pour point shown in Table 5. In fact, the Young modulus and the plastic yield point in the longitudinal direction are respectively 8.5 and 0.31 MPa for the reference and 3 and 0.08 MPa for B100-2 (see Table 5). The same trends are measured in the cross direction for the B100-2 foam compared to the reference (Table 5). These drastic variations in properties come mainly from the morphology of the foams. In addition, the closed cell content of these foams decreased from 90 to 10% between the reference and B100-2, respectively (Table 4). Thus, under compression, the compression of the gas contained in the closed cells of the reference contributes to increasing its mechanical properties with respect to the B100-2 foam (J. D'Souza, et al J. Appl. Polym. Sci. 131 (2014)).

[0162] An analysis of the response to the deformation stresses of the foams was carried out on the bio-sourced foams in order to point out the variations of the mechanical properties among the bio-sourced foams. The stress-strain curves of all bio-sourced foams in the longitudinal direction are shown in FIG. 7a. In general, it is noted that the Young's modulus and the plastic yield point of the B100-2 foam are higher than those of the B85-4, B85-2 and B100-4 foams, respectively (FIG. 7a). In addition, the B100-4 foam has the lowest Young's modulus and plastic yield point. More generally it is found that the foams B85-4, B85-2, B100-4 have weaker mechanical properties than B100-2. The improved mechanical properties of B100-2 can be explained by its higher density compared to other foams.

[0163] The B100-2 foam has a majority of open cells, small cells and a higher bulk density than other bio-sourced foams. In compression, the rapid densification and the good distribution of the load lead to improve the mechanical properties and more particularly the conservation modulus, Young's modulus and the plastic yield point.

[0164] Formulation B100-4 has water and isopentane as swelling agent. After the foaming process, the high open cell content and the lower density explain the weaker compression properties of the resulting B100-4 foam.

[0165] The slight improvement in the mechanical properties measured by the conservation modulus or the modulus in the transverse direction (Table 5) of B85-4 compared to the B85-2 sample is also due to the chemical structure of the two materials. Indeed, the B85-4 bio-sourced foam is produced with a higher water content than the B85-2 foam. In addition, it is also important to note that the presence of glycerol and sorbitol in the B85-4 and B85-2 formulations increases the crosslinking density. A similar phenomenon is observed if we compare the mechanical properties of B85-4 and B100-4 foams. Indeed, the B85-4 foam has better mechanical properties than the B100-4 foam. This confirms that the effect of water on polymerization is more moderate between B85-4 and B85-2 foams compared to B100-4 and B100-2 foams. As a result, the stress-strain curves of the B85-4 and B85-2 formulations are between those of the B100-4 and B100-2 formulations. These observations thus demonstrate the great influence of the swelling agent or crosslinking agent on the mechanical properties of the PU foam.

TABLE-US-00005 TABLE 5 Comparison of Mechanical Properties of the different foams REF B85-2 B85-4 B100-2 B100-4 Bulk density 30.7 0.8 25.4 1.6 23.1 0.3 41.2 3.5 25.3 1.8 (Kg/m.sup.3) Conservation 13.08 1.95 3.23 2.35 2.30 modulus (MPa) Glass transition 194.0 189.8 184.2 192.0 185.3 temperature ( C.) Longitudinal 8.5 0.8 5.8 0.3 5.2 0.7 3.0 0.3 2.1 0.5 direction modulus (MPa) Traverse 1.8 0.12 0.43 0.08 0.52 0.03 0.5 0.02 0.21 0.06 direction modulus (MPa) Plastic yield 0.320 0.030 0.063 0.003 0.069 0.003 0.084 0.005 0.052 0.002 point in longitudinal direction (MPa) Plastic yield 0.130 0.004 0.016 0.002 0.020 0.003 0.023 0.007 00.004 0.0006 point in traverse direction (MPa)

[0166] The transverse compression-stress curves of B85-4, B100-4, B85-2 and B100-2 are shown in FIG. 7, b. Obviously, the difference in the mechanical properties observed between the different bio-sourced foams follows the same trend as those observed in the longitudinal direction. However, FIG. 7, b, shows that the stress-strain behavior is very different from that of the longitudinal direction, which shows a clear anisotropic mechanical behavior of bio-sourced foams. A careful examination of the slopes of stress-strain curves in the elastic region indicates that the Young's modulus measured in the transverse direction is 10 times lower than that in the longitudinal direction for B85-4 and B100-4. This ratio is about 14 and 6 for B85-2 and B100-2, respectively. This decrease is less pronounced for elastic stress. For the B100-2 foam, for example, the yield stress in the transverse direction is only 3 times lower than that determined in the longitudinal direction.

[0167] In conclusion, open cell PU foams have been successfully developed from sorbitol-based polyester polyol and have been studied. The swelling agent, polyol or mixture of polyols and co-polyol have been shown to be key parameters for the modulation of kinetics, foaming profile and properties of bio-sourced foams through the range of reactivity offered by BASAB. The use of water as a chemical swelling agent in the formulation of foams has effectively improved the characteristic times (kinetics), the expansion rate and the foaming temperature. It also significantly reduces the foam density from 41 to 25 kg/m.sup.3 with respect to the same foams inflated with a physical expansion agent (isopentane) when only the bio-sourced polyol is used. A range of PU foams with different mechanical properties was then obtained. The mechanical compression tests show that the mechanical properties are very different in the longitudinal and transverse direction.

[0168] Thus, the prepared foams exhibit a significant anisotropy of their mechanical properties. In addition, all of the foams exhibit significant changes in Young's modulus, plastic yield point, and stress at the beginning of the densification region. These results are fully consistent with the viscoelastic properties measured by DMA. The glass transition decreases when the bio-sourced polyol is used for the formulation, compared to the petro-sourced reference. In addition, for bio-sourced foams the use of chemical and physical swelling agents allows variations in bulk density, closed cell count and foam microstructure.

[0169] Bio-sourced PUR foams meet the requirements of a wide range of applications from furniture to acoustic and thermal insulation of buildings, as they have a low coefficient of thermal conductivity and a high rate of open cells. PU bio-sourced foams seem particularly suited to the new demand for thermal and acoustic insulation due to their high open cell content and their elastic behavior. The anisotropy of the mechanical properties of such foams can also be used for filling applications of all kinds in the building in particular. Indeed, foams also having a low thermal conductivity can be deformed in the longitudinal direction at the rise of the foam and then return to their original size to fill spaces present in a defective part of the initial insulation of a building.