Influence of Rigid Segment Type on Copoly(ether-ester) Properties

The growing ecological awareness of society created the tendency to replace petrochemically based materials with alternative energy carriers and renewable raw materials. One of the most requested groups of polymer materials with significant technological importance is thermoplastic elastomers (TPE). They combine the properties of elastomers such as flexibility with the typical properties of thermoplastics, like easy processing. Herein, one compares the influence of rigid segments on the properties of copoly(ester-ether). Thermoplastic polyesters based on bio-1,6-hexanediol and terephthalic (T), furanic (F), and napthalate (N) diesters, i.e., PHT, PHF, and PHN, were obtained employing melt polycondensation. Additionally, to grant elastic properties of polyesters, systems containing 50 wt.% of bio-based polyTHF®1000 (pTHF) with a molecular mass of 1000 g/mol, have been prepared. The composition and chemical structure have been determined by 1H nuclear magnetic resonance (NMR) and Fourier transformed infrared spectroscopy (FTIR) analyses. The temperatures corresponding to phase transition changes were characterized by differential scanning calorimetry (DSC) and dynamic mechanical thermal analysis (DMTA) analyses. The crystalline structure was examined by X-ray diffraction (XRD) analysis. Additionally, the influence of pTHF–rich segment on the tensile properties, water absorption, as well as thermal and thermo-oxidative stability, has been analyzed. It was found that incorporation of soft phase allows creation of thermoplastic elastomers with tensile characteristics comparable to the commercially available ones, by means of elongation at break higher than 500%, low values of tensile modulus, without exhibiting yield point.


Introduction
The increasing awareness in the field of ecology within our society has led to the necessity of creating demand for replacing chemical products made from petroleum with renewable raw materials. Therefore, there is a growing interest in materials like poly(tetrahydrofuran) (polyTHF). PolyTHF is a bio-based derivative from 1,4-butanediol [1]. This material possesses characteristic high chain flexibility, and because of that it has a low melting point between −15 • C to 30 • C, which depends on its molecular weight. The bio-based PolyTHF ® 1000 produced by BASF has identical properties to a petrochemicalbased product [1]. PolyTHF can be used in the production of spandex fibers or artificial leather [2]. Furthermore, it can be used for the synthesis of thermoplastic polyurethane [1,2]. Another material worthy of notice is 1,6-hexanediol (1,6-HDO) produced by Rennovia Inc. Bio-based 1,6-HDO is synthesized from glucose. 1,6-HDO finds applications in the production of coatings, adhesives, and elastomers [3]. been analyzed, to evaluate the utilitarian properties of the synthesized polyesters and copoly(ether-esters).

Synthesis of PHF, PHT, PHN, and Copoly(ether-ester)s Based on Them
Synthesized polyesters and PEE were obtained from dimethyl terephthalate (DMT, Sigma-Aldrich, Germany), dimethyl naphthalene (DMN, Sigma-Aldrich, Germany), dimethyl 2,5-furanodicarboxylate (DMFDC, 99%, Henan Coreychem Co., Ltd., Zhengzhou, China), 1,6-hexylene glycol (HDO, Rennovia Inc., Santa Clara, CA, USA), and poly(tetrahydrofuran) (pTHF, BASF, Ludwigshafen, Germany) with a molecular mass of 1000 g/mol. Materials were synthesized in two steps (Figure 1). In the first step, transesterification of diester (DMFDC/DMT/DMN) by HDO with the presence of the first portion of catalyst (tetrabuthyl orthotitanate, Ti(OBu) 4 , (Fluka)) was carried out. Secondly, the polycondensation stage was performed in the presence of the second portion of catalyst (also Ti(Obu) 4 ) along with the thermal stabilizer, Irganox 1010 (Ciba-Geigy, Basel, Switzerland). Additionally, during polycondensation of copoly(ether-ester)s pTHF was added. The synthesis was performed in a 1 dm 3 high-pressure reactor (Autoclave Engineers, Erie, PA, USA). The reactor is equipped with a condenser, cold trap for collecting the by-product, and vacuum pump. During the transesterification, the reactor was loaded with DMFDC/DMT/DMN, HDO, and catalyst. The molar ratio of the diester (DMFDC/DMT/DMN) and glycol (HDO) was 1:1.5. The first step of reaction was performed in the presence of a constant flow of nitrogen at the temperature and time that can be found in Table 1. During the transesterification, methanol was distilled and collected as the first by-product. The end of the first step was signalized by the amount of effluent by-product. When 90% of the stoichiometric amount of methanol was ceased, the process was completed. Subsequently, one increased the temperature up to 210 • C and added a catalyst and thermal stabilizer to the reactor. Additionally, if it was the synthesis of copoly(ether-ester)s, pTHF was added to the reactor. The reaction temperature was increased to a value of the end temperature of the polycondensation (Table 1). A vacuum was applied to remove HDO excess and lower the final pressure to 25 Pa. The progress of polycondensation was monitored by observation of stirring torque change, which was used to evaluate the melt viscosity of the product. The end of the polycondensation process was signalized by the proper value of melt viscosity of the reaction mixture that was adequate to the value of melt viscosity of a high molecular mass of the polymer material. After the polycondensation process, the material was extruded from the reactor into the water bath with the use of compressed nitrogen. All synthesized copoly(ether-ester)s were named as follows: rigid segment-b-diester unit-flexible segment, since for the flexible segment one diester unit (F/T/N) is included with pTHF sequence, e.g., PHF-b-F-pTHF. In the same manner, all of the other copoly(ether-esters) based on diester of terephthalate (T) and naphthalene (N) acids were designated.   Subsequently, the extruded materials were pelletized on the laboratory mill. Then materials were injection molded using Boy 15 (Dr Boy GmbH&Co., Neutstadt, Germany) for a dumbbell shape sample, type A3, that was being used for DMTA, water absorption, and tensile measurements. Before injection molding, pellets were dried for 24 h under a vacuum at the temperature of 55 °C. The parameters of injection can be found in Table 2.  /50  30  170  8  45  7  25  PHT  30  190  30  70  5  20  PHT-b-T-pTHF 50/50  30  150  12  50  6  6  PHN  30  230  25  50  5  10  PHN-b-N-pTHF 50/50  30  210  25  50  5  5 Tf-temperature of form; Ti-temperature of injection; Pd-holding down pressure; Pi-injection pressure; ti-time of injection; tc-time of cooling.

Characterization Methods
The chemical structure and composition of the synthesized materials were investigated by 1 H NMR spectroscopy. Before the experiment, samples were subjected to esterification. 1 H NMR spectroscopy was carried out on Bruker spectrometer operating at a fre-  Subsequently, the extruded materials were pelletized on the laboratory mill. Then materials were injection molded using Boy 15 (Dr Boy GmbH&Co., Neutstadt, Germany) for a dumbbell shape sample, type A3, that was being used for DMTA, water absorption, and tensile measurements. Before injection molding, pellets were dried for 24 h under a vacuum at the temperature of 55 • C. The parameters of injection can be found in Table 2.

Characterization Methods
The chemical structure and composition of the synthesized materials were investigated by 1 H NMR spectroscopy. Before the experiment, samples were subjected to esterification. 1 H NMR spectroscopy was carried out on Bruker spectrometer operating at a frequency of 400 MHz (Bruker, Karlsruhe, Germany). The chloroform-d CDCl3 at a concentration of 10 mg/mL was used to dissolve samples. For internal chemical shift reference, tetramethylsilane (TMS) was used.
The polyesters and copoly(ether-ester)s were characterized using an FTIR spectrophotometer Nicolet iS 5 FTIR Spectrometer (Thermo Fisher Scientific Inc., Waltham, MA, USA). Samples were tested with the attenuated total reflectance (ATR) technique. Each sample was scanned 17 times over the frequency range of 4000-400 cm −1 .
Density was studied by hydrostatic weighing method with the use of AGN200C (Axis LLC, Gdańsk, Poland).
Additionally, water absorption tests were performed in cold and boiling water. The measurement was carried out according to the procedures recommended in ASTM D570. Firstly, the dumbbell shape samples were dried at 55 • C for 24 h. Subsequently, samples were cooled to room temperature and weighted. The measurement of water absorption in boiling water was carried out for 30 min, after that samples were cooled in distilled water for 15 min. The water absorption in cold water was investigated by immersing samples in distilled water at 23 • C for 24 h. The water on the surface of the samples was removed with filled paper. After that, samples were weighted. Each reported value is an average of 3 test specimens.
Differential Scanning Calorimetry (DSC) measurement was performed using F1 Phoenix (Netzsch, Selb, Germany). The measurements were carried out over a temperature range of −50 • C to 300 • C and again cooled to −50 • C with a speed of 10 • C/min for polyesters. Copoly(ether-ester)s were investigated in the temperature range of −90 • C to 300 • C and again cooled to −90 • C with the same speed as polyesters. Additionally, only PHT and PHT-b-T-pTHF were heated to 250 • C. First heating was used only for deleting the thermal memory of the samples. In addition, in order to compare the DSC results with dynamic mechanical thermal analysis (DMTA) results, by means of phase transition temperatures, the DSC measurement was also carried out with the heating/cooling rates of 3 • C/min in the temperature ranges adequate for polyesters and copoly(ether-esters), as above. The melting and crystallization temperatures (T m , T c ) were measured at the maximum of endo-and exothermic peaks, respectively. The glass transition temperature (T g ) was taken as the midpoint of the change of the heat capacity (∆C p ).
The X-ray diffraction (XRD) patterns of the catalysts were recorded with Empyrean (Malvern Panalytical, Malvern, UK) using CuK (λ = 0.154 nm) as the radiation source. The samples were scanned in a 2θ angle range of 10-35 • (with a step size of 0.05).
The dynamic mechanical thermal analysis (DMTA) was obtained using a DMA Q800 (TA Instruments, New Castle, DE, USA) working in a temperature range from −100 • C to the polymer melt temperature, at a frequency of 1 Hz and a heating rate of 3 • C/min. The properties were determined based on modulus changes and the ability of attenuation as a function of temperature and frequency of load changes.
The thermal and thermo-oxidative stability of materials were characterized using TGA92-16.18 (Setaram, Caluire-et-Cuire, France). The thermal stability was investigated in the atmosphere of argon when thermo-oxidative in the atmosphere of dry, synthetic air (N 2 :O 2 = 80:20% vol) with a flux rate of 20 mL/min. The study was carried out in the temperature range of 50-700 • C at a heating rate of 10 • C. The static mechanical properties were investigated using Autograph AG-X plus (Shimadzu, Kyoto, Japan). This machine is equipped with an optical extensometer, 1 kN Shimadzu load cell, the TRAPEZIUM X software. Polyesters and copoly(ether-ester)s at the beginning were extended to 1% with a crosshead speed of 1 mm/min. Then, the stress-strain curves for polyesters were obtained at a rate of 5 mm/min. However, the stress-strain curves for copoly(ether-ester)s were obtained at a rate of 100 mm/min. Each reported value is an average of five test specimens. The measurements were performed according to PN-EN ISO 527. Finally, the hardness of polyesters and copoly(ether-ester)s was investigated using a Zwick 3100 Shore D tester (Zwick GmbH, Ulm, Germany). The reported values are the mean values of twenty independent measurements.

Chemical Structure, Composition, and Basic Physico-Chemical Properties
Polyesters (PHF, PHT, PHN) and copoly(ether-ester)s based on these polyesters were synthesized by melt polycondensation which was described in the experimental session.
The theoretical chemical composition and the chemical composition estimated from 1 H NMR analysis are summarized in Table 3. The NMR spectra of polyesters shown in Figure 2 differ from each other. For PHF, two furanoate ring protons appear as a singlet signal at 7.20 ppm (d signal) [7]. The peak at 8.07 ppm (e signal) is assigned to the protons of the terephthalate ring. Signals at 8.59, 8.07, and 7.98 ppm (f, g, h signals) on the 1 H NMR spectra of PHN can be ascribed to protons of naphthalene ring [21]. The signals originating from methylene protons of hexylene glycol units appear at 1.45, 1.77, and 4.33 ppm for PHF [22]. However, signals of methylene protons of hexylene glycol units slightly differ for other polyesters (PHT, PHN). They can be found at higher values due to the impact of the aromatic ring on a magnetic field. Table 3. Calculated composition and basic physico-chemical properties of synthesized polymers.    H NMR spectra of polyesters and block copolymers. The 1 H NMR spectra of poly(ether-ester)s have four new resonance signals assigned to the protons of pTHF. Signal i is assigned to inner methylene protons of pTHF ether block at 1.6 ppm and outer methylene protons of ether block (signal k) that can be found at 3.42 ppm [22,23]. The last two new signals are caused by a transesterification reaction between polyesters and pTHF what leads to a change in resonance of methylene group proton in pTHF. This effect is visible at 4.37 and 1.64-1.73 ppm (signal l and j, respectively). Moreover, due to the impact of the naphthalene ring on magnetic field peaks ascribed to signals a, i, and c, l have merged. Signal m is visible in 1 H NMR spectra of PHN-b-N-pTHF 50/50 at 3.47-3.52 ppm and is ascribed to protons from the ending group of macromolecule -CH 2 -OH [24].         For estimation of the actual weight content of flexible segment, the Equation (1) was used:

Material
where I R is the internal signal intensities corresponding to rigid segment I F is the internal signal intensities corresponding to flexible segment, x is a number of protons assigned for an internal signal of a rigid segment (for all block copolymers x = 4), y is a number of protons assigned for an internal signal of the flexible segment (for all block copolymers y = 6), M WP and M WF are the molecular weights of the repeating units of the rigid and flexible segment, respectively. The difference between calculated composition and expected values is around 5%. The most accurate copoly(ether-ester) is PHF-b-F-pTHF 50/50, which calculated composition differs only about 2,49% from the expected value. The difference can be caused by the introduction of additional pTHF, due to losses in the dosing of the viscous substrate and distillation of the reaction substrate under reduced pressure [22].
The FTIR analysis of polyesters and copoly(ether-ester)s was carried out to investigate their structure. In Figure 6, FTIR spectra of polyesters and copoly(ether-ester)s shown similarities that occur between 1255-1270 cm −1 and 1708-1715 cm −1 . Absorption peaks in that area are caused by C(=O)-O and C=O stretching mode of ester groups, respectively [7,21]. There are also characteristic bands of aromatic ring moieties shown near 724-764 cm −1 (ring out-ofplane deformation), 820-875 cm −1 (ring out-of-plane deformation), 1016-1130 cm −1 (ring in-plane deformation) [25,26]. Moreover, for PHF and PHF-b-F-pTHF signal associated at 1222 cm −1 , arising from the =C-O-C= furan ring vibration [22].  In addition, the polyesters and copoly(ether-ester)s were investigated in terms of limiting viscosity number, density, and water absorption. The results are summarized in Table 3. The polyester with the highest limiting viscosity number is PHT, moreover, PHN exhibits the lowest value of limiting viscosity number (0.626 dl/g) among other polyesters. Nevertheless, all synthesized polyesters exhibited high values of intrinsic viscosity, especially if compared to PET bottle grade (IV of: 0.70-0.78 (dl/g) [28], or to the previously synthesized PET (IV if 0.536 dl/g, Mn = 19,500 g/mol and Mw = 46,900g/mol [29]. Whereas, the previously synthesized furan-based polyesters [30] and copoly(ether-esters) [22], following the same procedure, also exhibited relatively high values of molecular masses. Obviously, the incorporation of flexible segments into polyester caused the increase in the The influence of soft segment on FTIR spectra is visible, especially at characteristic bands of C-O-C stretching vibration of pTHF between 1105-1125 cm −1 . Consequently, after adding pTHF there is a visible increase in absorption at a wavelength of 2847-2852 cm −1 and 2915-2919 cm −1 due to -C-H asymmetric and symmetric stretching vibrations in methylene groups [27]. Additionally, for PHF-b-F-pTHF 50/50 and PHT-b-T-pTHF 50/50 the absorption peak, associated with C=O stretching mode of the ester group, slightly increased. Finally, the absorption band of -OH groups near 3450 cm −1 is very weak. Therefore, it indicates the consumption of pTHF hydroxyl groups through copolymerization, which confirms the successful modification of polyesters [22,24].
The above observations on the chemical structure and composition of polyesters and copoly(ether-esters) based on 1,6-hexanediol are in the agreement with the previously published papers [10,12,22].
In addition, the polyesters and copoly(ether-ester)s were investigated in terms of limiting viscosity number, density, and water absorption. The results are summarized in Table 3. The polyester with the highest limiting viscosity number is PHT, moreover, PHN exhibits the lowest value of limiting viscosity number (0.626 dl/g) among other polyesters. Nevertheless, all synthesized polyesters exhibited high values of intrinsic viscosity, especially if compared to PET bottle grade (IV of: 0.70-0.78 (dl/g) [28], or to the previously synthesized PET (IV if 0.536 dl/g, Mn = 19,500 g/mol and Mw = 46,900g/mol [29]. Whereas, the previously synthesized furan-based polyesters [30] and copoly(ether-esters) [22], following the same procedure, also exhibited relatively high values of molecular masses. Obviously, the incorporation of flexible segments into polyester caused the increase in the value of intrinsic viscosity, which is due to change in molecular chains masses and their flexibility. This is in the agreement with our previously published papers [20,22]. All synthesized polyesters exhibited similar values of hydrostatic density. Whereas, the addition of pTHF lowers values of density of copoly(ether-ester)s. Figure 7 represents the water absorption of synthesized polymers at room temperature (CWA at 23 • C) and boiling water (HWA at 100 • C). It is well-known that polyesters absorb water, which affects their processing properties, thus of great importance is to evaluate their affinity for water absorption [30]. Polymer materials absorb water and moisture by various mechanisms [9]. One of them is due to the diffusion of water molecules to free volume between polymer chains [9,29,30]. PHN has the lowest value of absorption in both, cold and hot water. PHF and PHT exhibited similar values of cold water absorption. However, PHF shows a higher absorption of hot water than PHT. In turn, copoly(ether-ester)s show significantly higher values of cold water absorption than polyesters. The lower values of HWA in the case of block copolymers might be due to the relaxation in the temperature much above the glass transition.

Structural Properties
For an investigation of structural and thermal properties, DSC, DMTA, and XRD were used. DSC analysis is summarized in Table 4. Figure 8 represents DSC thermograms of synthesized polyesters recorded during cooling and second heating at heating/cooling rates of 10 °C/min and 3 °C/min. Polyester with the highest value of glass transition temperature is PHN, which was due to the double aromatic ring in its chain, lowering its

Structural Properties
For an investigation of structural and thermal properties, DSC, DMTA, and XRD were used. DSC analysis is summarized in Table 4. Figure 8 represents DSC thermograms of synthesized polyesters recorded during cooling and second heating at heating/cooling rates of 10 • C/min and 3 • C/min. Polyester with the highest value of glass transition temperature is PHN, which was due to the double aromatic ring in its chain, lowering its mobility. The glass transition temperatures of PHF and PHT are similar to one another. PHN has the highest value of melting temperature and it's the only synthesized polyester that shows cold crystallization at 194.7 • C at a heat rate of 10 • C/min. Whilst PHF has the lowest value of melting temperature. In turn, PHT has two melting temperatures, resulting from two crystal structures: α and β [13]. Moreover, all investigated polyesters were found to be semi-crystalline polymers, wherein the crystallization temperatures at heat rate of 10 • C/min of PHF (T c = 96.8 • C) and PHT (T c = 105.9 • C) appear to be very similar, while PHN has the highest value of crystallization temperature of 169.0 • C.

Structural Properties
For an investigation of structural and thermal properties, DSC, DMTA, and XRD were used. DSC analysis is summarized in Table 4. Figure 8 represents DSC thermograms of synthesized polyesters recorded during cooling and second heating at heating/cooling rates of 10 °C/min and 3 °C/min. Polyester with the highest value of glass transition temperature is PHN, which was due to the double aromatic ring in its chain, lowering its mobility. The glass transition temperatures of PHF and PHT are similar to one another. PHN has the highest value of melting temperature and it's the only synthesized polyester that shows cold crystallization at 194.7 °C at a heat rate of 10 °C/min. Whilst PHF has the lowest value of melting temperature. In turn, PHT has two melting temperatures, resulting from two crystal structures: α and β [13]. Moreover, all investigated polyesters were found to be semi-crystalline polymers, wherein the crystallization temperatures at heat rate of 10 °C/min of PHF (Tc = 96.8 °C) and PHT (Tc = 105.9 °C) appear to be very similar, while PHN has the highest value of crystallization temperature of 169.0 °C.  Figure 9 represents DSC thermograms of polyesters and copoly(ether-ester)s at heating/cooling rates of 10 • C/min and 3 • C/min. One can clearly observe the influence of flexible segment on the phase transition temperatures (T c , and T m ) that were shifted toward lower values. The phase separation between rigid and flexible segments was not visible at a heat rate of 10 • C/min due to crystallization of rigid segment during cooling, although one can observe two glass transitions at a heat ratio of 3 • C/min. For PHF-b-F-pTHF 50/50 and PHT-b-T-pTHF 50/50 value of glass transition of the rigid segment increased compared to PHF and PHT, respectively. In turn, PHN-b-N-pTHF 50/50 has a lower value of glass transition of the rigid segment in comparison to the corresponding polyester.  Figure 9 represents DSC thermograms of polyesters and copoly(ether-ester)s at heating/cooling rates of 10 °C/min and 3 °C/min. One can clearly observe the influence of flexible segment on the phase transition temperatures (Tc, and Tm) that were shifted toward lower values. The phase separation between rigid and flexible segments was not visible at a heat rate of 10 °C/min due to crystallization of rigid segment during cooling, although one can observe two glass transitions at a heat ratio of 3 °C/min. For PHF-b-F-pTHF 50/50 and PHT-b-T-pTHF 50/50 value of glass transition of the rigid segment increased compared to PHF and PHT, respectively. In turn, PHN-b-N-pTHF 50/50 has a lower value of glass transition of the rigid segment in comparison to the corresponding polyester.  The crystal structure of the synthesized materials was investigated using XRD analysis. Figure 10 represents diffraction patterns of synthesized polyesters and copoly(ether-ester)s. PHF's WAXS diffractogram has three sharp signals at 2θ = 13.67 • , 17.03 • , 24.91 • which are assigned respectively to planes (110), (010), (111) [14,22]. Similar to PHF, in WAXS diffractogram of PHN, three sharp signals at 2θ = 16.40 • , 21.34 • , 23.64 • that are assigned respectively to planes (010), (111), (100) can be observed [31]. In the case of PHT, the polymorphism, suspected from DSC analysis, was confirmed. The α structure signals can be observed at 2θ = 16 proves different crystal structures of all synthesized polyesters. In all cases of copolymers, peaks on the WAXS curves are less sharp than for polyesters due to a lower degree of crystallinity (estimated by DSC). It is especially noticeable for the β structure of PHT-b-T-pTHF 50/50 where that structure is almost not visible in the diffraction pattern.     Table 5. The sample with the highest value of E' at 25 • C among polyesters is PHF (2577 MPa), while PHT has the lowest value (2105 MPa). Copolymers have significantly lower values of the storage modulus at 25 • C. In the group of copoly(ether-ester)s PHF-b-F-pTHF 50/50 exhibits the value of E' at 25 • C higher than the others (181 MPa) when PHT-b-T-pTHF 50/50 and PHN-b-N-pTHF 50/50 differ only about 1 MPa. Copolymers show a wide plateau of elasticity that determines the possibility of using them as thermoplastic elastomers. Figure 11a represents tan δ for polyesters, where α-relaxation what can be recognized as T g is observed. PHN has the highest value of α 1 (73 • C) and PHT has the lowest value of α 1 (43 • C). For copoly(ether-ester)s one can clearly observe two peaks at tan δ, which are associated with α-relaxations of rigid (α 1 ) and flexible (α 2 ) segments. Temperatures of α-relaxations compared to values of T g resulting from DSC analysis at a heat rate of 3 • C/min exhibit similarities in case of values α 1 and T gR . The values of α 1 for PHF-b-F-pTHF 50/50 and PHT-b-T-pTHF 50/50 are higher than for PHF and PHT, respectively, when PHN-b-N-pTHF 50/50 has a lower value of α 1 in comparison to PHN. Moreover, PHF-b-F-pTHF 50/50 has the highest value of α 1 -relaxation between copoly(ether-ester)s. In turn, PHN-b-N-pTHF 50/50 has the lowest value of α 1 -relaxation, although it has the highest value of α 2 -relaxation what can indicate partial miscibility of amorphous phases of PHN and pTHF. (c) (d) Figure 11. The storage modulus E' (a,c) and tan δ (b,d) as a function of temperature for polyesters and copoly(ether-ester)s.

Thermal Properties
The thermal and thermo-oxidative stability of synthesized materials was investigated due to the importance of these parameters for the future application of materials. The thermal stability of materials was performed under an inert atmosphere (argon) and

Thermal Properties
The thermal and thermo-oxidative stability of synthesized materials was investigated due to the importance of these parameters for the future application of materials. The thermal stability of materials was performed under an inert atmosphere (argon) and thermo-oxidative stability was carried out under oxidative atmosphere (air). The characteristic temperatures for the mass losses of 5, 10, 50, 90% (T 5% , T 10% , T 50% , T 90% ) in both atmospheres and the temperatures corresponding to the maximum of mass losses (T DTG1 and T DTG2 ) are summarized in Table 6. In this study, the temperature for the mass loss of 5% is considered as the beginning of thermal degradation. Figure 12a,e represent the thermal-oxidative and thermal stability of polyesters, respectively. The values of each characteristic temperature for the mass losses and the temperatures corresponding to the maximum of mass losses in both atmospheres are almost similar. PHN has the best thermal and thermo-oxidative stability among investigated polyesters. The polyester which is most sensitive for degradation is PHF. The difference between values of T 5% , and T DTG1 in both atmospheres for PHF and PHN is almost about 20 • C. Table 6. TGA data: temperatures of 5%, 10%, 50%, 90% mass loss, the temperatures corresponding to Table 1 and T DTG2 ) in an oxidizing and inert atmosphere. atmosphere. The first step appears at 386-405 °C and its attributed to the decomposition of flexible and rigid segments. The second step appears at 470-529 °C, and it results from the decomposition of residue. The values of TDTG1 for polyesters and copoly(ether-ester)s do not show great differences, only about 2 °C. Although, there is a significant difference in the value of TDTG2 between them. For PHF-b-F-pTHF 50/50 value of TDTG2 is 24 °C higher than for PHF. A similar effect was observed by Szymczyk et al. [32] for poly(trimethylene terephthalate)-block-poly(ethylene oxide) (PTT-b-PEO) copolymers. The value of TDTG2 for PHT and PHT-b-T-pTHF 50/50 is almost similar; furthermore, PHN has a higher value of TDTG2 than PHN-b-N-pTHF 50/50.     Figure 12b-d,f-h represents thermo-oxidative and thermal stability of polyesters and copoly(ether-ester)s, respectively. The influence of soft segment in copoly(ether-ester)s is significant. Especially, it is noticeable in the decrease in the value of T 5% of mass loss of copoly(ether-ester)s in comparison to corresponding polyesters. The first derivative of the mass loss (DTG) curve in Figure 12b-d shows two-step decomposition under an oxidative atmosphere. The first step appears at 386-405 • C and its attributed to the decomposition of flexible and rigid segments. The second step appears at 470-529 • C, and it results from the decomposition of residue. The values of T DTG1 for polyesters and copoly(ether-ester)s do not show great differences, only about 2 • C. Although, there is a significant difference in the value of T DTG2 between them. For PHF-b-F-pTHF 50/50 value of T DTG2 is 24 • C higher than for PHF. A similar effect was observed by Szymczyk et al. [32] for poly(trimethylene terephthalate)-block-poly(ethylene oxide) (PTT-b-PEO) copolymers. The value of T DTG2 for PHT and PHT-b-T-pTHF 50/50 is almost similar; furthermore, PHN has a higher value of T DTG2 than PHN-b-N-pTHF 50/50. Figure 13 represents the stress-strain curves of the synthesized materials. The values of Young modulus (E), tensile strength at yield (σ y ), elongation at yield (ε y ), tensile strength at break (σ b ), and elongation at yield (ε y ) are summarized in Table 7. All polyesters show a strain hardening effect due to the orientation of macromolecular chains and crystallization during stretching. PHN has the highest value of Young modulus among other polyesters, by about 1 TPa. Moreover, the values of tensile strength at yield and tensile strength at break of PHN are higher than for PHF and PHT. However, the polyester that characterizes significantly better elongation is PHT, which elongation at break differs from others around 100%. The addition of soft segment results in the disappearance of yield point, significant increase value of elongation at break, and decrease in value of tensile strength at break. The disappearance of yield point is due to the initiation of highly elastic deformations at low deformation. These characteristics are typical for elastomeric materials. The most promising copoly(ether-ester) is PHN-b-N-pTHF 50/50. This material has the highest value of tensile strength at break and its value of elongation at break classify between PHF-b-F-pTHF 50/50 and PHT-b-T-pTHF 50/50. Due to the addition of pTHF ability to crystallization decreased and it caused a decrease in a strain hardening effect. The hardness of polyesters and copoly(ether-ester)s are summarized in Table 7. The polyester with the highest value of Shore D hardness in PHN. The hardness value of PHF and PHT slightly differs. However, the addition of soft segment results in a decrease in hardness in copoly(ether-ester)s in comparison to polyesters. has the highest value of tensile strength at break and its value of elongation at break classify between PHF-b-F-pTHF 50/50 and PHT-b-T-pTHF 50/50. Due to the addition of pTHF ability to crystallization decreased and it caused a decrease in a strain hardening effect. The hardness of polyesters and copoly(ether-ester)s are summarized in Table 7. The polyester with the highest value of Shore D hardness in PHN. The hardness value of PHF and PHT slightly differs. However, the addition of soft segment results in a decrease in hardness in copoly(ether-ester)s in comparison to polyesters.

Conclusions
The synthesis of PHF, PHT, PHN, and copoly(ether-ester)s by two-step melt polycondensation was carried out successfully. Synthesized materials were investigated and compared in terms of chemical structure, mechanical, thermal, utilitarian properties. The chemical structure of materials was analyzed by FTIR spectroscopy and 1 H quantitative nuclear magnetic resonance (NMR) and it confirmed that real composition is similar to feed one. Using DSC, DMTA, TGA thermal properties and phase structure of synthesized materials were studied. The crystal structure was investigated by XRD analysis. The static tensile performance was carried out for polyesters and copoly(ether-ester)s. Moreover, intrinsic viscosity number, density, and water absorption were studied. All investigated polyesters are semicrystalline. The obtained copolymers are characterized by high values of deformation. Additionally, synthesized copolymers can be processed by injection molding. These characteristics prove the attainment of TPE. Among synthesized materials, the most prominent are PHN and PHN-b-N-pTHF 50/50 due to their properties. They characterize by the most rigid macromolecular chain since their value of glass transition temperature and thermal stability are significantly higher than others. Moreover, their values of hardness, Young modulus, and tensile strength at break are higher as well. However, dimethyl naphthalate is more expensive than traditional TPA so complete replacement of it is not profitable. PHF and PHT show similarities in phase transition temperatures and hardness. PHT has slightly better thermal and thermal-oxidative properties than PHF, although PHF is characterized by a higher value of Young modulus and tensile strength at break than PHT. In the future, PHF could be prioritized over PHT due to being a bio-based material and a decrease in the price of FDCA. Moreover, if comparing the synthesized copoly(ether-ester)s, based on PHF and PHN, with commercially available thermoplastic elastomers with similar values of hardness (Shore hardness ca. 40 ShD)-for instance, Hytrel ® 4056 [33,34]-the obtained materials are found to have higher values of elongation and tensile stress at break. A slightly lower value of σ b was observed for PHT-b-T-pTHF 50/50, when keeping the excellent value of ε b , comparable to the values typically observed for commercially available TPE. The above-mentioned statement clearly demonstrates the application potential of the synthesized TPEs based on all employed diesters.