CA2404753A1 - Thermoplastic polyurethane elastomers (tpus) prepared with polytrimethylene carbonate soft segment - Google Patents

Abstract

A thermoplastic polyurethane elastomer (TPU) composition which comprises: a) a poly(trimethylene carbonate) diol (PTMC diol) as the soft segment; b) a diisocyanate; and c) at least one glycol which reacts with the diisocyanate to form the hard segment which comprises from 10 % to 55 % by weight of the composition wherein the hard segment is defined as the sum portion of diisocyanate that reacts with the glycol plus the unreacted glycol.

Description

THERMOPLASTIC POLYURETHANE ELASTOMERS (TPUs) PREPARED WITH POLYTRIMETHYLENE CARBONATE SOFT SEGMENT
FIELD OF THE INVENTION
The present invention relates to thermoplastic polyurethane elastomers (hereafter TPUs). More particularly, the present invention relates to a new class of TPUs prepared with poly(trimethylene carbonate) diol (PTMC diol) as the soft segment. The TPUs prepared using PTMC diols were extended with glycols, preferably lower functionality glycols, including, for example, 1,3-propanediol and 1,4-butanediol.
BACKGROUND OF THE INVENTION
TPUs are of technical importance because they offer a combination of high-quality mechanical properties with the known advantages of inexpensive thermoplastic processability. Much variation in mechanical properties can be achieved by the use of different chemical components. A survey of TPUs, their properties and applications are discussed, for example in Polyurethane Handbook, Gunter Oertel, Ed., Hanser Publishers, Munich, 1985, pp. 405-417.
TPUs are built up from linear polyols, usually polyesters or polyethers, organic diisocyanates and short-chain diols (chain extenders). The overall properties of the TPU will depend upon the type of polyol, its molecular weight, the structure of the isocyanate and of the chain extender, and the ratio of soft and hard segments.

Polyurethanes may be either thermoplastic or thermoset, depending on the degree of crosslinking present. Both thermoset and thermoplastic polyurethanes can be formed by a "one-shot" reaction between isocyanate and polyol or by a "pre-polymer" system, wherein a curative is added to the partially reacted polyol-isocyanate complex to complete the polyurethane reaction.
Thermoplastic urethanes do not have primary crosslinking while thermoset polyurethanes have a varying degree of crosslinking, depending upon the functionality of the reactants.
Thermoplastic polyurethanes are commonly based on methylene diisocyanate (MDI) or toluene diisocyanate (TDI) and include both polyester and polyether grades of polyols. For adjustment of the properties, the polyols, chain extenders, and diisocyanate components can be varied within relatively wide molar ratios.
For improvement of the processing behaviour, particularly in the case of products for processing by extrusion, increased stability and an adjustable melt flow are of great interest. This depends on the chemical and morphological structure of the TPUs. The structure necessary for an improved processing behaviour is conventionally obtained by the use of mixtures of chain extenders, e.g. 1,4-butanediol/1,6-hexanediol. As a result of this the arrangement of the rigid segments is so greatly distorted that, not only is the melt flow improved, but, simultaneously, the thermomechanical properties, e.g. tensile strength and resistance to thermal distortion, are often impaired.

The known TPUs and blends containing TPUs all suffer some drawbacks in one or more properties, including mechanical properties, colour stability to heat and light, clarity, heat distortion properties, and phase separation. Attempts to improve one property, such as hardness, often lead to degeneration of another property.
Thus, problems exist in achieving hardness and related mechanical properties, stable colour, clarity and higher heat distortion temperatures in TPUs and blends containing TPUs. There is a need in the art to discover new formulations of TPUs that provide a broader range of mechanical and thermal properties without the degeneration of existing properties.
The present invention is useful in overcoming one or more problems with known thermoplastic materials by providing a new class of TPUs which provide new possibilities for mechanical and thermal properties in TPU formulations, including improvements in clarity, hardness, higher elasticity modulus, and improved softening temperature and coefficient of thermal expansion.
SUMMARY OF THE INVENTION
The present invention provides a new class of TPUs with improved properties and is based on poly(1,3-propanediol carbonate) diol (PTMC diol), with a hard segment comprising the portion of an isocyanate that reacts with a glycol plus the glycol blended into the TPU, and a diisocyanate to cure the system. The elastomers are somewhat harder than corresponding TPUs based on polyols known in the art. The PTMC TPUs exhibited good physico-mechanical properties, including somewhat higher elasticity modulus than a control TPU.
The abrasion resistance and compression set was also very good, comparable to that of polyether TPUs. The softening temperature and the coefficient of thermal expansion was found to be improved over that of a control. In addition, using the PTMC polyol, it was possible to improve the clarity of the TPUs and in some examples even obtain completely clear material.
In accordance with the foregoing, the present invention comprises a thermoplastic polyurethane elastomer (TPU) composition which comprises:
a) a poly(trimethylene carbonate) diol (PTMC diol) as the soft segment;
b) a diisocyanate; and c) at least one glycol (sometimes referred to as a chain extender) which reacts with the diisocyanate to form the hard segment which comprises from 10% to 55% by weight of the composition wherein the hard segment is defined as the sum portion of diisocyanate that reacts with the glycol plus the unreacted glycol.
BRIEF DESCRIPTION OF THE DRAWINGS
The present invention will now be described by way of example with reference to the accompanying drawings, in which:
Figure 1 is a graph showing the viscosity of polycarbonate polyols;
Figure 2 is a bar graph showing stress at 100% strain of TPUs based on 1,4-butanediol (1,4 - BD);

Figure 3 is a bar graph showing stress at 300% strain of TPUs based on 1,4 - BD;
Figure 4 is a bar graph showing the tensile strength retention of TPUs based on 1,3-propanediol (1,3 - PDO);
Figure 5 is a bar graph showing weight change after a two-week immersion in water at 70°C;
Figure 6 is a bar graph showing tensile strength, originally, and after a two-week immersion in water at 70°C; and Figure 7 is a bar graph showing chemical resistance after a one-week immersion.
DETAILED DESCRIPTION OF THE PRESENT INVENTION
In the present invention a new class of thermoplastic polyurethanes (TPUs) was prepared using poly(trimethylene carbonate) diol as the soft segment, a hard segment containing a glycol, preferably a short chain glycol, and a diisocyanate. A suitable poly(trimethylene carbonate) glycol was prepared by a process described below and the specimen used in the Examples of the present invention was characterized by a molecular weight of about 2000.
Thermoplastic polyurethane elastomers based on the PTMC
diol were evaluated for their properties.
Both aromatic and cycloaliphatic TPUs based on PTMC
diols were prepared and evaluated. 4, 4'-Diphenylmethane diisocyanate (MDI) was utilized to prepare aromatic and methylene-bis(4-cyclohexyl isocyanate)(H12MDI) to prepare aliphatic TPUs. The elastomers were prepared using the one shot procedure. In Examples 2, 3, 5, and 10, 1,3-PDO
and 1,4-BD were used as chain extenders and the hard segment concentration was varied in the Examples from 22 to 35%. For comparison, TPUs based on a commercial poly(1,6 - hexanediol carbonate) glycol (Desmophen C-200, commercially available from Bayer Co.), and representative of polyols used in the art, were prepared S and evaluated.
The physico-mechanical properties (hardness, stress-strain properties, tear resistance, compression set, resilience and abrasion resistance) of TPUs were measured according to ASTM standard methods. The solvent resistance (paraffin oil, ethylene glycol, and diluted acid/bases) was determined by measuring the weight change upon immersion. Water resistance was evaluated by measuring the retention of stress-strain properties and the weight change upon immersion in water at 70°C.
The morphology of the elastomers was studied by thermal analysis including differential scanning calorimetry (DSC), thermo-mechanical analysis (TMA), and dynamic-mechanical analysis(DMA), as well as Fourier transform infra-red analysis (FTIR). The elastomer transparency was also measured by determining the light transmission (%) in the visible range of 474 to 630 nanometers.
Due to the rigid nature of the PTMC diol, the elastomers exhibited relatively high Tg (around 0°C).
Their hardness was somewhat higher than that of the corresponding TPUs based on, for example, Desmophen C-200, poly(tetramethyleneoxide)(PTMO) 2000 or caprolactone polyols (See Tables 17 & 18).
The PTMC 2000 TPUs exhibited good physico-mechanical properties. Their elasticity modulus was higher than Desmophen C-200 TPUs. The abrasion resistance and compression set of PTMC 2000 TPUs was very good, comparable to that of polyether TPUs.
The heat stability of PTMC 2000 TPUs, as indicated by the properties at elevated temperature, the softening temperature, and the coefficient of thermal expansion was found to be improved over that of Desmophen C-200 TPUs.
By using PTMC 2000 it is possible to improve the clarity of TPUs and to even obtain completely clear material with H12MDI .
The resistance of PTMC 2000 TPUs to oil was excellent and the resistance to other media such as diluted inorganic acids, bases, and ethylene glycol was excellent as well.
Poly(trimethylene carbonate) polyols Although higher functionality polyols can generally be used to prepare thermoset systems, the TPUs of the present invention utilize in the examples a PTMC diol prepared in a specific manner, a glycol, and a diisocyanate. The PTMC diols were prepared as described in our copending Application No. PCT/EPO1/02323. The PTMC diols described therein are characterized by improvements in clarity with virtually all end groups being hydroxypropyl groups, with no measurable allyl groups .
In order to produce poly(trimethylene carbonate) characterized by these desirable properties, trimethylene carbonate is reacted with a polyhydric alcohol in the presence of a catalyst, preferably under nitrogen The polyhydric alcohol can be a diol or triol or higher polyhydric alcohol, such as, for example, propanediol and trimethylolpropane, individually, or mixtures thereof.
The poly(trimethylene carbonate) can be prepared without a catalyst. However, the catalyst provides the S advantage of shorter reaction times. Suitable catalysts are selected from salts of Group IA or Group IIA of the Periodic Table. Good results were obtained using sodium acetate. The Group IA or IIA catalysts are effective in small amounts, ranging from less than 1 ppm to greater than 10,000, although one would typically expect to use an amount in the range of 5 to 1000 ppm, preferably about 10 to 100 ppm, and most preferably about 10-40 ppm.
The poly(trimethylene carbonate) is preferably produced without a solvent, although a solvent could be used .
The poly(trimethylene carbonate) is produced at a temperature in the range of 50-160°C. A preferred range is 100-150°C, and more preferably 110-130°C. Pressure is not critical, and actually almost any pressure could be used, but good results were obtained using ambient pressure.
The poly(trimethylene carbonate) will have properties that are determined by several factors, the most important factors being the amount and identity of any initiating alcohol(s), catalysts and catalyst amounts, and the process conditions. A manufacturer may vary the determining factors to predictably produce the molecular weight, polydispersity, and other characteristics needed for the intended application.

In the present invention, to prepare a new class of TPUs that provides new formulation options, good results were obtained using a PTMC diol prepared as described and having a molecular weight below about 10,000, preferably from 1000 to 3000. The TPUs in the Examples herein were prepared with a PTMC diol having a molecular weight of 2000.
Glycol f Chain Extender) The glycol component may be selected from aliphatic, alicyclic, aralkyl, and aromatic glycols. As would be known to those skilled in the art, higher functionality alcohols could be useful in many applications. In the present invention, however, good results were obtained using lower functionality glycols. Examples of glycols employed include, but are not limited to, ethylene glycol; propylene glycol; 1,3-propanediol; 2-methyl - 1,3 - propanediol; 2,4-dimethyl-2-ethylhexane-1,3-diol; 2,2-dimethyl-1,3-propanediol; 2-ethyl-2-butyl-1,3-propanediol; 2-ethyl-2-isobutyl-1,3-propanediol; 1,3-butanediol; 1,4-butanediol; 1,5-pentanediol; 1,6-hexanediol; 2,2,4-trimethyl-1,6-hexanediol;
thiodiethanol; 1,2-cyclohexanedimethanol; 1,3-cyclohexanedimethanol; 1,4-cyclohexanedimethanol;
2,2,4,4-tetramethyl-1,3-cyclobutanediol; and p-xylylenediol, or mixtures thereof. Additional examples of suitable glycols include hydroxyalkyl derivatives of hydroquinone, i.e. bis 2- hydroxyethyl ether (HQEE), and hydroxyalkyl derivatives of resorcinol and bisphenol A.
The glycol is preferably selected from 1,3-propanediol and 1,4-butanediol, or mixtures thereof. Examples 2, 3, and 10 demonstrate the use of 1,3 - propanediol and 1,4 - butanediol.
The hard segment concentration is the sum of the portion of isocyanate that reacts with the glycol plus 5 the unreacted glycol. The glycol hard segment is blended into the TPU in an amount which corresponds to 10 to 55%
hard segment concentration, preferably from 20 to 40%
hard segment concentration.
Isocyanate Isocyanates useful for curing polyurethane elastomers generally include aliphatic, aromatic or cycloaliphatic polyisocyanates. For the preparation of the TPUs of the present invention diisocyanates were employed. Suitable diisocyanates are aliphatic, aromatic or cycloaliphatic diisocyanates. An example of an aliphatic diisocyanate is hexamethylene diisocyanate. Examples of cycloaliphatic diisocyanates include isophorone diisocyanate, 1,4-cyclohexane diisocyanate, 1-methyl-2,4-and -2,6-cyclohexane diisocyanate, as well as the corresponding isomer mixtures, 4,4'-, 2,4'- and 2,2'-dicyclohexyl-methane diisocyanate, as well as the corresponding isomer mixtures. Examples of aromatic diisocyanates include 2,4-toluene diisocyanate, mixtures of 2,4- and 2,6-toluene diisocyanate, 4,4'-, 2,4'- and 2,2'-diphenylmethane diisocyanate, mixtures of 2,4'- and 4,4'-diphenylmethane diisocyanate, urethane-modified liquid 4,4'- and/or 2,4'-diphenylmethane diisocyanates, 4,4'-diisocyanatodiphenylethane-(1,2) and 1,5-naphthalene diisocyanate. Other examples of suitable diisocyanates include, but are not limited to, diphenylene-4-4'-l0 diisocyanate, 3,3'-dimethoxy-4-4'-diphenylene diisocyanate, methylene-bis-(4-cyclohexylisocyanate), tetramethylene diisocyanate, decamethylene diisocyanate, ethylene diisocyanate, ethylidene diisocyanate, S propylene-1,2-diisocyanate, cyclohexylene-1,2-diisocyanate, m-phenylene diisocyanate, p-phenylene diisocyanate, 3,3'-dimethyl-4,4'-biphenylene diisocyanate, 3,3'-dimethoxy-4,4'-biphenylene diisocyanate, 3,3'-diphenyl-4,4'-biphenylene diisocyanate, 4,4'-biphenylene diisocyanate, 3,3'-dichloro-4,4'-biphenylene diisocyanate, furfurylidene diisocyanate, xylylene diisocyanate, diphenyl propane-4,4'-diisocyanate, bis-(2-isocyanatoethyl) fumarate, naphthalene diisocyanate, and combinations thereof.
Additional diisocyanate compounds might include, for example: 1,4'-dicyclohexylmethane diisocyanate, 3-isocyanatomethyl-3,5,5-trimethylcyclohexyl isocyanate, cyclohexylene-1,4-diisocyanate, 4,4'-methylenebis(phenyl isocyanate), 2,2-diphenylpropane-4,4'-diisocyanate, p-phenylene diisocyanate, m-phenylene diisocyanate, xylene diisocyanate, 1,4-naphthalene diisocyanate, 4,4'-diphenyl diisocyanate, azobenzene-4,4'-diisocyanate, m- or p-tetramethylxylene diisocyanate and 1-chlorobenzene-2,4-diisocyanate, 1,6-hexamethylene diisocyanate, 4,6'-xylylene diisocyanate, 2,2,4-(2,4,4-)trimethylhexa-methylene diisocyanate, 3,3'-dimethyldiphenyl 4,4'-diisocyanate, 3,3'-dimethyl-diphenylmethane 4,4'-diisocyanate, and the like.
The preferred diisocyanates employed in the Examples to demonstrate the benefits of the present invention were 4, 4' - diphenylmethane diisocyanate (MDI) and methylene - bis(4-cyclohexyl isocyanate) (H12MDI).
Catal3rsts Where a catalyst is utilized, suitable catalysts are those which accelerate the reaction between the NCO
groups of the diisocyanates and the hydroxyl groups of the structural components. Examples include tertiary amines and organic metal compounds known in the art and described, for example, in US-A-6022939. Suitable compounds include, for example, triethylamine, dimethylcyclohexylamine, N-methylmorpholine, N,N'-dimethylpiperazine, 2-(dimethylaminoethoxy)ethanol and diazabicyclo(2,2,2)octane, and mixtures thereof, as well as organic metal compounds such as titanic acid esters, iron compounds, and tin compounds, examples of which include tin diacetate, tin dioctoate, tin dilaurate and the tin dialkyl salts of aliphatic carboxylic acids, such as dibutyltin diacetate and dibutyltin dilaurate, or mixtures thereof. The catalysts are usually used in quantities of 0.0005 to 0.5 parts per 100 parts of polyhydroxy compound.
Preparation The TPUs of the present invention were prepared by the one shot method. In the examples hard segments were included in the PTMC polyurethanes at concentrations ranging from about 10 to 55%, preferably 20 to 40% by weight.
The isocyanate index, ratio of isocyanate to hydroxyl equivalent, depends on the isocyanate and glycol (often called the chain extender) employed. In the case of thermoset elastomers in general the index may be anywhere from 0.105 to 600, or more. The isocyanate index in the present invention could be from 0.8 to 1.04, depending on the formulation, but is preferably close to about 1.02.
The polyol and glycol (chain extender) were heated at a temperature from 70 to 150°C, preferably 95 to 140°C, and in specific examples 100 to 135°C. Somewhat higher temperatures could be used, but, as is known in the art, are generally not recommended in order to avoid side reactions. The diisocyanate was preheated at the mixing temperature, added to the mixture of polyol and chain extender and all components were mixed vigorously for 5 to 10 seconds. The mixture was then poured in a preheated Teflon-coated mould (<150°C). Gelation was determined by string formation, which generally occurred within about 10-20 seconds, and when that occurred the mould was placed in a Carver press and the resin was compression-moulded at elevated pressure and moderately elevated temperature. The pressure is preferably from 137.9 to 206.8 Mpa (20,000 to 30,000 psi), and a suitable temperature is from 100°C to 140°C. Suitable pressures can be well above or below this range, as would be known to those skilled in the art. Afterwards the polyurethane sheet was post-cured in an oven at from 90 to 150°C, preferably 100 to 140°C, for a time that may be from several hours to several days, depending upon the temperature.
The following examples will serve to illustrate specific embodiments of the present invention disclosed herein. These examples are intended only as a means of illustration and should not be construed as limiting the scope of the present invention in any way. Those skilled in the art will recognize many variations that may be made without departing from the spirit of the disclosed present invention.
Experimental The materials utilized in the Examples are shown in Table 1. The isocyanates were used as received from the suppliers. The NCO% concentration was checked by titration by the di-n-butylamine method of ASTM D1638-74.
The hydroxyl number of the polyols was determined by using the standard phthalic anhydride esterification method (ASTM D4273).

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Example 1 In Example 1 the viscosity of the polyols was tested.
The viscosity of PTMC 2000 at room temperature was found to be much higher than that of Desmophen C-200, which is due to the higher concentration of stiff carbonate groups in PTMC 2000 (Table 2, Figure 1). The viscosity was significantly decreased by temperature. Due to the shorter hydrocarbon sequence (three CHz groups) the glass transition temperature of PTMC 2000 was found to be -28.5°C, significantly higher than that of Desmophen C-200, which has six CHZ groups (-58.3°C).
Table 2 Viscosity of the Polycarbonate Polyols Viscosity mPa.s (cps Temperature (°C) PTMC 2000 Desmophen c-200 36 >100000 Example 2 In Example 2 the compatibility of the chain extenders with the polyols was examined. The compatibility of PTMC
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Table 3 The Compatibility of Polycarbonate Diols with the Chain Extenders H. S. 22 25 28 35 Temperature RT 70 90 RT 70 90 RT 70 90 RT 70 90 (C) 1,3-PDO

Desmophen PC C C PC C C PC C C NC C C

1,4-BD

Desmophen PC C C PC C C PC C C NC C C

C = Compatible; PC = Partially Compatible;
NC = No Compatibility Example 3 In Example 3 TPUs were prepared by the one-shot method at hard segment concentrations of 22, 25, 28, and 35%. Prior to elastomer preparation polyols and chain extenders were vacuum dried at 70°C for at least 24 hours. The diisocyanates were used as received from the suppliers. The NCO% was checked by titration by the di-n-butylamine method ( ASTM D1638-74). The isocyanate index (isocyanate to hydroxyl equivalent ratio) was 1.02.
Polyol and chain extender were weighed in a plastic cup and heated at 100°C or 135°C. Benzoyl chloride was added to the mixture of polyol and chain extender.
Diisocyanate, which was previously heated at the mixing temperature, was added to the mixture of polyol and chain extender and all components were mixed vigorously for 5-10 seconds. The mixture was then poured into a Teflon-coated mould, which was preheated at 105°C or 135°C.
When gelation occurred (as determined by string formation), the mould was placed in a Carver press and the resin was compression-moulded at 165.5 Mpa (24,000 psi) at 105°C or 135°C. Afterwards, the polyurethane sheet was post-cured in an oven at 105°C or 135°C for 24 hours (or 135°C for 20 hours and 150°C for 4 hours).
Post-curing is not always necessary. The curing and postcuring conditions in the preparation of aromatic TPUs are shown in Table 4 and for the aliphatic TPUs in Tables 13 and 14. The polyurethane elastomers were tested one week after preparation.

Table 4 Curing and Post-Curing Conditions in the Preparation of MDI-TPUs PTMC 2000 Desmophen C

Mixing Conditions 135°C for 10 sec. 105°C for 5 2 drops Benzoyl Chloride sec.
(1,4-BD) 4 drops Benzoyl Chloride (1,3-PBD) Curing Conditions 135°C for 1 hr 105°C for 1 hr (pressed at 165.5 MPa (24000 (pressed at psi) 165.5 MPa (24000 lbs) ) Post-curing 135°C for 20 hrs (1,4-BD) 105°C for 24 Conditions 135°C for 20 hrs hrs 150°C for 4 hrs (1,3-PDO) S Example 4 In Example 4, the formulations and properties of MDI-based TPUs based on PTMC 2000 and Desmophen C-2000 extended with 1,3 - PDO were tested.
The data are shown in Tables 5 and 6. Increasing the hard segment concentration from 22 to 35% resulted in the hardness of PTMC 2000 TPUs increasing from 73 to 91 Shore A. The hardness of Desmophen C-200 TPUs was somewhat lower at the same hard segment concentration. In general, the tensile strength, elasticity modulus and Die C tear resistance of TPUs increased with the hard segment concentration as expected. The abrasion resistance of PTMC 2000 elastomers was very good, better than that obtained for Desmophen C-200. This could possibly be due to the reinforcing effect of hydrogen bonds in PTMC 2000 polyurethanes, which contain a high proportion of carbonate groups capable of forming hydrogen bonds. The abrasion resistance of PTMC 2000 TPUs was similar to or even better than that of PTMO 2000 and TONE
polycaprolactone TPUs. Some examples of PTMO 2000 TPUs have abrasion resistance indices of, for example, 13 and 20. See Tables 6-A, 17, and 18, which contain data regarding properties of TPUs based on commercial polyols.
PTMC TPUs demonstrated relatively low compression set (4 to 7%), lower than that of Desmophen C-200 TPUs (14.3 to 23.50). It is interesting to note that the resilience of 1,3 - PDO extended polycarbonate TPUs increased with increase of the hard segment concentration.

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Example 5 In Example 5 PTMC TPUs were prepared with 1,4 -BD
chain extender at a hardness range from 22 to 35% and examined for various properties. Data are shown in Tables 7 and 8. The strength properties (tensile strength, 100°s and 300% elasticity modulus, Young's modulus and toughness) and Die C tear strength of PTMC
2000 and Desmophen C-200 TPUs changed quite uniformly with increase in the hard segment concentration. The tensile strength of the PTMC-TPUs was found to be somewhat lower compared to Desmophen C-200, but modulus values were somewhat higher in the former case (Figures 2 & 3). The properties such as elongation at break, modulus, and resilience indicate that 1,4 - BD extended TPUs are more flexible than those extended with 1,3 -PDO. It was found repeatedly that the resilience of PTMC
TPUs increased with increase of hard segment concentration.

.

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Example 6 In Example 6 the heat resistance of the elastomers was evaluated by measuring the stress-strain properties at 70°C. The retention of the tensile strength was found to be somewhat higher for PTMC 2000/1,3 - PDO/MDI TPUs than for Desmophen C-200/1,3 - PDO/MDI TPU (See Figure 4). The elongation at break of PTMC 2000 increased significantly upon heating and the elasticity modulus decreased (See Table 5). The heat resistance of Desmophen C-200/1,4 - BD/MDI TPUs was poor (See Table 8).
The coefficient of thermal expansion, as measured by TMA
was found to be lower for PTMC TPUs than for Desmophen C-200 (See Table 9). The softening temperature of the TPUs as measured by TMA was in the range of 160 to 209°C for PTMC 2000 and 160 to 175°C for the corresponding Desmophen C-200 polyurethanes. The softening temperature of Desmophen C-200 was not affected significantly by the chain extender.

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Examp~ a 7 In Example 7 morphology was examined. The glass transition temperature of PTMC TPUs was about 0°C and shifted about 10°C when measured by DMA. The relatively high Tg defines these polyurethanes more as elastoplastic materials with very good elasticity above room temperature. The glass transition temperature of Desmophen C-200 TPUs was about 30 degrees lower. An insight into the morphology was also obtained by FTIR
spectroscopy. The FTIR spectra of the elastomers exhibited the bands typical for polycarbonate aromatic polyurethanes: -NH, (free and bonded) at 3300-3400 cm-1;
CH2 at 2900-2970 cm-1; C=O in carbonate and bonded urethane group at 1740 - 1759 cm-1; C=O free urethane group at 1706 cm-1; aromatic group at 1600 cm-1 and -C-O-C- in ether group at 1033 cm-1. The ratio of absorbance 1705 cm-1/1745 cm-1 increased with an increase of the hard segment concentration indicating probably an increase in the proportion of unbonded urethane groups.
This ratio was found to be higher with the PTMC TPUs.
The hydrogen bonds in the polycarbonate polyurethanes are formed between urethane groups, and by bridging carbonate and urethane groups.

Table 9 Some Morphological Properties of TPUs Tg(DMA) Tg(DSC) Tm(TMA) Coef. Of Thermal Exp.
(C) (C) (C) (mm~a1 C) SPM-22 13.96 -1.12 159.86 123.00 SPM-25 9.88 0.36 201.97 87.20 SPM-28 11.89 0.19 206.67 231.00 SPM-35 9.71 2.88 208.64 149.00 DPM-22 -28.34 -29.76 175.01 426.00 DPM-25 -30.00 -31.54 161.10 281.00 DPM-28 -31.60 -31.80 169.47 224.00 DPM-35 -28.53 -30.32 162.02 219.00 Example 8 In Example 8 the water resistance of the formulations with PDO/MDI was examined. The water resistance was evaluated by measuring the weight gain and change in stress-strain properties upon immersion in water at 70°C
for two weeks. The results are shown in Tables 10 and 11 and in Figures 5 and 6. The weight gain of PTMC TPUs was 1.2 to 1.6%, and less (0.8 to 10) for Desmophen C-200.
These results correlate well with the change in tensile strength, which was 8 to 57o for PTMC 2000(depending on the hard segment concentration) and 3.6 to 33.50 for Desmophen C-200. The better water resistance of Desmophen C-200 is due to the more hydrophobic structure ( six -CHZ groups ) .
The relative transparency was measured by determining the light transmission (o) in the visible range of 474 to 630 nanometers. The degree of transparency decreased with increase of the hard segment concentration. PTMC
2000 TPUs exhibited significantly higher transparency at different hard segment concentrations as compared to Desmophen C-200. This could be due to the less ordered structure of PTMC backbone or the higher degree of phase mixing of flexible and hard segments.

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Example 9 In Example 9 the chemical resistance of TPUs was measured in various media including oil (100% neutral paraffinic oil), Fisher Brand 19, ethylene glycol, dilute acids (10°s HZSOQ and 10% HCl) and sodium hydroxide.
Results are shown in Table 12 and in Figure 7. The weight gain in hydraulic oil was low while in inorganic acids, it was higher, especially with PTMC TPUs. The weight gain in sodium hydroxide was relatively low except for Desmophen C-200 at 35% hard segment concentration.
Unexpectedly, the weight gain in ethylene glycol was much lower with PTMC than with Desmophen C-200 TPUs. Overall the resistance of TPU in this media was good. For reference the resistance of TPUs based on poly(oxytetramethylene) glycols is shown in Table 12 -A.
Table 12 Chemical Resistance after One-week Immersion at Room Temperature Oil Ethylene HCI 10%

10% NaOH
10%

Glycol Weight change (o) DPM TPUs* 0.0-0.32 1.00-1.26 0.22-0.830.14-0.53 0.0-1.10 DBM TPUs* 0.0-0.28 0.90-0.92 0.22-0.440.00-0.58 0.35-0.48 SPM TPUs* 0.15-0.310.39-0.63 0.80-1.510.66-1.52 0.00-0.58 * Hard Segment Concentration was varied from 22 to 350.

Table 12-A
Resistance after One-Week Immersion of TPUs Based on POTMG 1000/1,4 - BD/MDI, 35% Hard Segment Concentration*
Weight Increase HZSO4, 30% 1.1 NaOH 10% 1.6 Ethylene Glycol 41.4 Oil 3.1 * Reactivity Studies and Cast Elastomers Based on Trans-cyclohexane - 1,4-Diisocyanate and 1,4-Phenylene Diisocyanate, S.
W. Wong and K. C. Frisch, Advances in Urethane Science and Technology, Vol. 8, page 74 (1981).
Example 10 In Example 10 TPUs based on the cycloaliphatic diisocyanate H12MDI and PTMC 2000 were cured. The curing conditions are shown in Tables 13 and 14. In the designations in the first row of each table, SPH-25 to SPH-35 corresponds to PTMC2000/1,3 -PDO/H12MDI with the hard segment concentration from 25 to 35%. SBH-25 to SBH-35 corresponds to PTMC2000/1,4 - BD/H12MDI with the hard segment concentration from 25 to 35%.
The tensile strength, which increased with hard segment concentrations, exhibited moderate values, somewhat higher with 1,3 - PDO than with 1,4 - BD chain extender. PTMC 2000 TPUs exhibited better properties with 1,3 - PDO than with 1,4 - BD chain extender, with both MDI and H12MDI. It could be noted that H12MDI TPUs were cured at lower temperatures than MDI TPUs, due to their lower green strength.
The glass transition temperature was determined by differential scanning calorimetry and dynamic-mechanical method. The DSC glass transition temperature of H12MDI
TPUs was somewhat below 0°C, lower than that of MDI based TPUs, indicating less interaction of the flexible segment with H12MDI. The softening temperature of H12MDI was typically in the range of 175 to 193°C. 1,3 - PDC
extended TPUs were transparent at 25o hard segment concentration and translucent at 28 to 35o hard segment concentrations. 1,4 - BD extended TPUs were translucent at 25% hard segment and hazy at higher hard segment concentration. As a reference some properties of TPUs based on H12MDI/PTM02000/1,4 - BD are shown in Table 13 -A.
The weight change of SPH-TPUs upon immersion in water at 70°C for two weeks was 1.2 to 1.73%, similar to MDI-TPUs (See Table 15).
The resistance of H12MDI - TPUs in hydraulic oil, ethylene glycol, 10% HCl, 10°s H2S04, and 10% NaOH, as measured by the weight gain is shown in Table 16. The resistance to oil was excellent (no weight increase).
The weight gain in acid, sodium hydroxide and especially in ethylene glycol was higher.

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Table 15 Weight change after Two-Week Immersion in Water at 70°C
Initial Weight Final Weight Weight Change (gr) (gr) SPH-25 0.1860 0.1882 1.20 SPH-28 0.1305 0.1327 1.72 SPH-30 0.1925 0.1952 1.42 SPH-35 0.2025 0.2087 1.73 Table 16 Chemical Resistance after One-Week Immersion at Room Temperature Oil H2S04 Ethylene NaOH

10%

Glycol 100 Weight change (%) SPH TPUs*0.0 1.20-2.30 1.26-2.001.20-1.701.26-2.35 SPH TPUs*0.0 2.30-3.33 0.70-1.000.80-1.000.86-1.00 * Hard Segment Concentration was varied from 25 to 35%.
Table 17 The Effect of Hard Segment Concentration on the Hardness of TPUs Based on PTMG 2000*

Hard Segment 22 33 Concentration(%) Hardness Shore A 70 85 Shore D 33 38 * M. Vlajic, E. Torlic, A. Sendijarevic, and V.
Sendijarevic, Polimeri, Vol. 10(3), pages 62-66, 1989.

Table 18 The Effect of Hard Segment Concentration on the Hardness of TPUs Based on CPL 2000*

Hard Segment 22 32 39 Conc . ( % ) Hardness Shore A 72 82 89 Shore D 33 39 44 * M. Vlajic, E.Torlic, A. Sendijarevic, and V.
Sendijarevic, Polimeri, Vol. 10(3), pages 62-66, 1989.

Claims (10)

1. A thermoplastic polyurethane elastomer (TPU) composition which comprises:
a) a poly(trimethylene carbonate) diol (PTMC diol) as the soft segment;
b) a diisocyanate; and c) at least one glycol which reacts with the diisocyanate to form the hard segment which comprises from 10% to 55% by weight of the composition wherein the hard segment is defined as the sum portion of diisocyanate that reacts with the glycol plus the unreacted glycol.

2. The composition of Claim 1 wherein the molecular weight of the poly(trimethylene carbonate) diol is from 300 to 6000.

3. The composition of Claim 2 wherein the molecular weight of the poly(trimethylene carbonate) diol is from 1000 to 3000.

4. The composition of Claim 1, 2 or 3 wherein the functionality of the poly(trimethylene carbonate) is about two.

5. The composition of Claim 1, 2, 3 or 4 wherein the hard segment is blended in an amount of 10 to 50%
concentration.

6. The composition of Claim 5 wherein the hard segment is blended in an amount of 20 to 40% concentration.

7. The composition of any one of the preceding Claims wherein the glycol in the hard segment is selected from aliphatic, alicyclic, aralkyl, and aromatic glycols.

8. The composition of Claim 7 wherein the glycol is selected from ethylene glycol; propylene glycol; 1,3-propanediol; 2, methyl - 1,3 - propanediol; 2,4-dimethyl-2-ethylhexane-1,3-diol; 2,2-dimethyl-1,3-propanediol; 2-ethyl-2-butyl-1,3-propanediol; 2-ethyl-2-isobutyl-1,3-propanediol; 1,3-butanediol; 1,4-butanediol; 1,5-pentanediol; 1,6-hexanediol; 2,2,4-trimethyl-1,6-hexanediol; thiodiethanol; 1,2-cyclohexanedimethanol;
1,3-cyclohexanedimethanol; 1,4-cyclohexanedimethanol;
2,2,4,4-tetramethyl-1,3-cyclobutanediol; and p-xylylenediol, or mixtures thereof.

9. The composition of Claim 8 wherein the glycol is selected from 1,3-propanediol and 1,4-butanediol, or mixtures thereof.

10. The composition of any one of the preceding Claims wherein the diisocyanate is selected from aromatic, aliphatic, or cycloaliphatic diisocyanates.