FIBRES MELT-SPUN FROM A THERMOPLASTIC ALTERNATING COPOLYMER AND A PROCESS FOR PREPARING SUCH FIBRES

Abstract: Claimed are fibres melt-spun from a thermoplastic alternating copolymer composed of alkenes and carbon monoxide having a - tenacity BT > 900 mN/tex, - melting point Tm > 220 DEG C, - crystallinity Vc > 33%, and - birefringence DELTA n > 0,0550. The preparation of these fibres, in which process the copolymer is melt-spun and the resulting fibres are subsequently drawn, the spinning process being conducted using a polymer melt free of crystallisation nuclei at a temperature of at most 40K above the melting temperature of the polymer Tm (in K) and the drawing of the fibres being conducted at a temperature in the range of Tmc - 15K to Tmc - 90K, with Tmc representing the constrained melting temperature, at a draw ratio in the range of 5 to 12 and a drawing tension corrected for temperature DTd,corr. in the range of 105 to 300 mN/tex. The fibres were found to be pre-eminently suitable for use as reinforcing yarn in rubber articles such as car tyres.

Description: FIBRES MELT-SPUN FROM A THERMOPLASTIC ALTERNATING COPOLYMER AND A PROCESS FOR PREPARING SUCH FIBRES The invention pertains to fibres melt-spun from a thermoplastic alternating copolymer composed of alkenes and carbon monoxide, to a process for preparing such fibres, in which process the copolymer is melt-spun and the resulting fibres are subsequently drawn, as well as to rubber articles such as tyres incorporating such fibres. Melt-spun fibres of the aforesaid type are known from EP-B-0 310 171. According to the process described in said document, a thermoplastic alternating copolymer composed of an olefinically unsaturated compound and carbon monoxide is spun from the melt at a temperature of at least T m +20°C, and the fibres are then drawn at a temperature of at most T m -10°C, with T m representing the crystalline melting point of the polymer. Said patent publication offers no instructions whatsoever regarding the drawing tensions to be applied during the drawing process in order to obtain fibres of the listed breaking tenacity. In addition, the level of the spinning temperature of 560K (287°C) used in the examples makes it clear that the polymer has been seriously affected by thermal degradation. This results in a large number of problems such as an unstable spinning performance, the risk of yarn rupture, discolouration of the polymer, a wide variation in the properties of the formed fibres, and a marked deterioration of their mechanical properties. All that has been said about the process described in EP-B-0 310 171 is equally true, mutatis mutandis, for the brief descriptions of the melt-spinning processes in the Japanese patent publications listed below: JP-A-09-323011 , JP-A-09-323384, JP-A-09-324355, JP-A-09-324377, JP-A-09-328342,and JP-A-09-329198. No information whatsoever is provided regarding the drawing tensions applied during the drawing process. Moreover, the employed spinning temperature of 275°C is much too high to prevent degradation of the polymer, so also for that reason the quality of the obtained fibres is unsatisfactory. The invention now provides fibres melt-spun on a commercial scale from a thermoplastic alternating copolymer composed of alkenes and carbon monoxide, which differ from the known melt-spun fibres of the same composition through constant quality, high tenacity, high crystallinity, and high birefringence. The alternating copolymer composed of alkenes and carbon monoxide of which the melt-spun fibres are made generally has an intrinsic viscosity in m- cresol at 25°C of at least 0,3 dl/g. The melt-spun fibres according to the invention have a tenacity BT of more than 900 mN/tex and are further characterised by a melting point T m , determined using the DSC method, > 220°C, a crystallinity V c > 33%, and a birefringence Δn > 0,0550. Melt-spun fibres according to the invention having a tenacity BT > 1000 mN/tex are characterised by a melting point T m , determined using the DSC method, > 220°C, a crystallinity V c > 35%, and a birefringence Δn > 0,0570. According to the invention, fibres melt-spun from an alternating copolymer composed of ethylene/propylene and carbon monoxide with a propylene content between 4 and 0,5 mole%, calculated on ethylene, and a tenacity BT > 1000 mN/tex are characterised by a melting point determined using the DSC method > 240°C, a crystallinity V c > 40%, and a birefringence Δn > 0,0570. The invention also consists of a process of the known type mentioned in the opening paragraph by which melt-spun fibres of high tenacity can be obtained when in the spinning process use is made of a polymer melt free of crystallisation nuclei at a temperature of at most 40K above the melting temperature of the polymer T m (in K) and the drawing of the fibres takes place at a temperature in the range of T mc - 15K to T mc - 90K, with T mc representing the "constrained" melting temperature, at a draw ratio in the range of 5 to 12 and a drawing tension corrected for temperature DT d , cc . r r. in the range of 105 to 300 mN/tex, BT - . F °« - DR d.corr. oOOO/r,, ) _ e (1000/r_ c ) jθ.8 wherein F DR represents the force measured at a draw ratio DR (in mN) and T d represents the drawing temperature (in K), use being made in the calculation of the corrected drawing tension of the linear density of the fibres prior to the start of the drawing process. Surprisingly, it has been found that when the right combination of drawing temperature and drawing tension is applied, the fibres obtained are of exceptionally high and constant quality and high tenacity. According to the invention, preference is given to a process where the draw ratio employed is more than 7 at a drawing tension in the range of 120 to 280 mN/tex. The fibres obtained when using the process according to the invention generally have a tenacity in the range of 313ln(DT d , C orr) - 575 to It was found that when the process according to the invention is used, fibres having a breaking tenacity in excess of about 900 mN/tex can be obtained when use is made of a drawing tension corrected for temperature DT d , corr . of more than 140 mN/tex. According to the invention, the term fibres refers to staple fibres as well as short fibres, filaments, and yarns (an assembly of filaments). By alternating copolymers composed of alkenes and carbon monoxide are meant, according to the invention, polymers built up from alkene and carbon monoxide units in alternating sequence. This means that in the polymer chain each carbon monoxide unit will have two alkene units as its immediate neighbours, and vice versa. In the process according to the invention, in the preparation of fibres with properties rendering these fibres pre-eminently suitable for technical application, i.e. fibres of high breaking tenacity and high modulus, preferably use is made of a polymer where 80-100% of the alkene units is composed of ethylene and 20-0% is composed of propylene. Optimal results were obtained when use was made of an alternating copolymer composed of ethylene/propylene and carbon monoxide and with a propylene content between 4 and 0,5 mole%, calculated on ethylene. The preparation of alternating copolymers composed of alkenes and carbon monoxide is described, int. al., in EP-A-121 965, EP-A-222 454, EP-A-224 304, EP-A- 227 135, EP-A-228 733, EP-A-229 408, EP-A-235 865, EP-A-235 866, EP-A- 239 145, EP-A-245 893, EP-A-246 674, EP-A-246 683, EP-A-248 483, EP-A- 253 416, EP-A-254 343, EP-A-257 663, EP-A-259 914, EP-A-262 745, EP-A- 263 564, EP-A-264 159, EP-A-272 728, and EP-A-277 695. In order to improve the polymer's resistance to thermal degradation, adjuvants counteracting said degradation can be added to the polymer. Examples of such adjuvants are inorganic acid binding compounds such as calcium hydroxyapatite or alumina, polymer stabilisers such as ste cally hindered phenols, carbodiimides, epoxy compounds, and phosphites, or combinations thereof. In melt-spinning alternating copolymers composed of alkenes and carbon monoxide use may be made of equipment also known to be used for melt- spinning other thermoplastic polymers. For instance, in the extrusion of the polymer use may be made of a spinneret plate such as is employed in melt- spinning other polymers such as polyethylene terephthalate. Such a spinneret plate has a number of capillaries having a diameter of 200 to 2000 μm and an L/D ratio of 1 to 10. Highly advantageous results are obtained when the spinneret plate is connected up with a heated tube the temperature of which at most equals the spinning temperature (T sp j n ). Preferably, a heated tube with a temperature between T S p in - 50°C and T spi n is employed. After spinning the resulting fibres can be wound prior to being drawn. In that case preference is given to a process in which the fibres are drawn immediately following on from the spinning process. The resulting fibres are pre-eminently suitable for use as reinforcing yarn in tyres on account of the favourable combination of high breaking tenacity and modulus, good adhesion to rubber, and high fatigue resistance. Also, the fibres are highly suitable for reinforcing other rubber articles such as conveyor belts and V-belts. In addition, the fibres are highly suitable for use in technical fabπcs, e.g., such as are used in paper making, where high standards with regard to resistance to hydrolysis are imposed. Measuring methods Intrinsic viscosity [η] [η] is determined using the equation: [η] = lim c →o η sp ec/c = lim c→0 (t - t 0 )/t 0 .c and so stands for the ratio between the flow times t and to, with t 0 representing the flow time of the solvent and t representing the flow time of the polymer-containing solution in a capillary viscometer at 298K (25°C). c in this determination stands for the polymer concentration in m-cresol, expressed in grams per decilitre. The intrinsic viscosity of the polyketone employed generally is in the range of 0,5 to 5 dl/g, preference being given to an intrinsic viscosity of 1 ,2 - 4,5 dl/g, more particularly of 1 ,2 - 2,5 dl/g. In order to characterise the structure of the melt-spun yarns according to the invention, a two-phase model was adopted in which separate crystalline and amorphous domains can be discerned. Structural characterisation was carried out by combining the results of X-ray diffraction, density measurements, birefringence, and differential scanning calorimetry. X-rav diffraction (XRD) WAXS measurements were carried out in transmission on samples prepared by winding a smooth layer of yarn filaments around a metal frame. The vertical diffractometer (Philips) was equipped with a quartz monochromator, Soller slits, a divergence slit (1°), a scatter slit (0.2 mm), a receiving slit (1°), and a sealed gas filled detector PW1711/10. The X-ray source was a CuKα tube with λ=1.5418 A. The diffractometer was coupled to a computer for collecting the data. The X-ray scans were fitted by means of Pearson VII functions. Density The density of the samples was determined at 23°C in a Davenport gradient column containing toluene and tetrachloromethane mixed in a ratio that gradually decreased downwards. The density measurements were carried out on three pieces of yarn. After 12 hours the density was calculated from their positions in the column. Birefringence Twenty filaments immersed in dibutyl phthalate were positioned parallel to each other between microscopic glasses and placed at an angle of 45° relative to the crossed polarisers of an optical microscope, which was equipped with a sodium lamp (λ = 0.5893 μm) and a Senarmont compensator. At the ends of the filaments, which were cut on the bias, the overall phase difference φ was determined by measuring the number of fringes (including partial fringes). For each filament the birefringence was calculated from Δn = ( φ/2π ) * ( λ/D ), with D representing the diameter of the filament. Melting point Tm The crystalline melting point T m of the polymer was determined with Differential Scanning Calorimetry (DSC). The melting peaks of the yam were determined with a Perkin Elmer DSC-7 by heating the sample (3-4 mg) in a cup at a rate of 20°C/min and recording the heat flow difference between the sample cup and an empty reference cup. T mc , the constrained melting temperature, was determined in a manner analogous to that for T m using Differential Scanning Calorimetry, with the proviso that this time instead of a sample of an isotropic polymer a yarn wound tightly around a metal strip was employed. T N F, the temperature at which the polymer is free of crystallisation nuclei (T NF ) was determined as follows: 3-4 mg of polymer were introduced into 10 μl aluminium cups provided with lids with holes punched into them. The cups were put into a Perkin Elmer DSC-7 Robotic system and then subjected to the following temperature programme: heating to T h0 i d at a heating-up rate of 10°C/min, with T h0 id > T m (the crystalline melting point of the polymer), keeping at a constant temperature of T h0 i d for t minutes, and cooling down to room temperature at a cooling rate of 10°C/min, with T ho i d being varied from T m to T m + 50 and with there preferably being 1-3 minutes of keeping at a constant temperature. Both the peak temperature of the recrystallisation (T rc ) and the onset of the recrystallisation (T rco ) can be derived from the cooling curve. The value of T rc or T rco measured over one and the same period of keeping at a constant temperature is then plotted against T h0 ι d . On the axis on which T h0 | d is plotted T NF can be read from the point of inflection in the curve found. Specific information on the crystalline part of the yarn was obtained from XRD measurements. Because of its polymorphic nature, the copolymer, hereinafter PK, can crystallise into two possible conformations, called PK-α and PK-β. Although PK-β is the more likely structure, both possibilities were taken into consideration. The total amount of crystalline volume, Vc, was calculated as D-D. V. D r c -D π a wherein D is the (measured) overall density, D a represents the amorphous density (for which a value of 1221 kg/m 3 was taken), and D c is the total crystalline density, defined as: D c = V α * D c,α + (1 - V α ) * D C β In this formula V α represents the (volume) percentage of crystalline material that is in the α-structure. This factor is determined directly from the quotient of areas of the respective (210) peaks in the XRD equator scan (after fitting), according to: D c , α and D Cγβ are the respective crystalline densities of the α- and β- structures. They can be calculated directly from the molar mass and the dimensions of the unit cell in the orthorhombic structure. These unit cell parameters a , b , and c are determined from the positions of the XRD (hkl) peaks after fitting, according to the following table: a axis b axis c axis α-structure (200) (210) and (200) (002) β-structure (210) and (200) (210) and (310) (002) Tenacitv: The tenacity (BT) as defined in ASTM D2256 - 88, published in April 1988, is obtained from the force-elongation curve and the measured filament tex. To determine the force-elongation curve a single filament or a multifilament yarn is stretched to rupture on an instron tensile tester. The length between grips for the single ruptured filament is 10 cm. The results for 3 filaments are averaged. All samples were stretched at a constant rate of elongation of 10 mm/min. The filament tex is calculated on the basis of the functional resonant frequency (ASTM D1577-66, Vol. 25, 1968) or by means of measurement by microscope. The tenacity is expressed in mN/tex and was measured on fibres conditioned at 20°C and 65% relative humidity for at least 24 hours. The invention will be further illustrated with reference to the following examples. Of course, the scope of the invention is not restricted to the specific details of the examples. Example I An alternating copolymer of ethylene/propylene and carbon monoxide having a propylene content of 7 mole% calculated on ethylene, a melting point of 225°C (determined using the DSC method), and an [η] = 1 ,5 was melted in an extruder equipped with five heating zones. The temperature/ residence time profile to be passed through was as follows: 248°C, 245°C, 245°C, 248°C, and 248°C. The overall residence time was 114 sec at a throughput of 92 g/minute. From the extruder the polymer was passed via a conveying pipe and a spinning pump to the spinning assembly including the spinneret plate. The temperature of the conveying pipe, the spinning pump, and the spinning assembly was 250°C. After an average residence time of 43 sec at said temperature the polymer was spun through a spinneret plate having 36 orifices each of 400 μm. Underneath the spinneret plate there was a 40 cm long hot tube with a wall temperature of 250°C and beneath that a cooling zone of 80 cm in length into which under a pressure of 125 N/m 2 cooled air of 20°C was introduced. The resulting as-spun yarn was wound at a rate of 400 m/min. Example II The as-spun yarn of Example I, having a linear density of 230 tex f36, was subjected to a number of drawing treatments. The drawing devices used for this had a length of 42 cm (hot plate) and 2 m (steamdrawing frame), respectively. The starting velocity in each case was 6 m/minute. The draw ratios were in the range of 4 to 10, while the temperatures at which drawing took place ranged from 150 to 220°C. The results of the drawing treatments and the values measured during these treatments for the draw ratio, the drawing device employed, the drawing temperature, the linear density of the feed yarn, the drawing tension DT d , and the drawing tension corrected for temperature DT dιC0rr. are all listed in the table below. In it DT d = F DR .DR/tex stands for the drawing tension, and DT d , cor r. for the corresponding drawing tension corrected for temperature according to the formula shown above. The constrained melting temperature, measured by DSC, of the yarns drawn to the highest degree was 240°C. Of the sixteen yarn samples drawn, samples 1 and 15 failed to meet the criterion of the invention that the drawing tension should exceed 105 mN/tex. Note that in sample 15 use was made of a drawing temperature close to the unconstrained melting temperature. This makes the drawing operation more critical. Table 1 The data listed in the table above clearly shows that when a drawing tension corrected for temperature of less than 105 mN/tex is employed, the fibres obtained have a tenacity which is too low for a wide range of commercial scale applications. It was also found that fibres having the highest tenacity are obtained when using a draw ratio of more than 7. Example III An alternating copolymer of ethylene/propylene and carbon monoxide having a propylene content of 3 mole%, calculated on ethylene, a melting point of 236°C (determined using the DSC method), and an [η] = 1 ,53 was melted in an extruder equipped with five heating zones. The temperature/ residence time profile to be passed through was as follows: 270°C, 265°C, 265°C, 265°C, and 265°C. The overall residence time was 114 sec at a throughput of 92 g/minute. From the extruder the polymer was passed via a conveying pipe and a spinning pump to the spinning assembly including the spinneret plate. The temperature of the conveying pipe, the spinning pump, and the spinning assembly was 265°C. After an average residence time of 43 sec at said temperature the polymer was spun through a spinneret plate having 36 orifices each of 400 μm. Underneath the spinneret plate there was a 50 cm long hot tube with a wall temperature of 265°C and beneath that a cooling zone of 80 cm in length into which under a pressure of 125 N/m 2 cooled air of 20°C was introduced. The resulting as-spun yarn was wound at a rate of 400 m/min. Example IV The as-spun yarn of Example III, having a linear density of 230 tex f36, was drawn in a steam box of 2 m in length. The starting velocity in each case was 6 m/minute. The draw ratios were in the range of 6,5 to 8,25, the temperature of the steam in each case was 215°C. The results of the drawing treatments and the values measured during these treatments for the draw ratio, drawing temperature, linear density of the feed yarn, drawing tension DT d , and drawing tension corrected for temperature DT dιCorr . are all listed in Table 2. In it DT d = F DR .DR/tex stands for the drawing tension, and DT dιCo rr. for the corresponding drawing tension corrected for temperature according to the formula shown above. The constrained melting temperature, measured by DSC, of the yarns drawn to the highest degree was 255°C. For that reason in the formula a value T m = 255°C was employed. All yarn samples 11 through 15 satisfied the criterion of the invention that the drawing tension DT dιC0r r. should exceed 105 mN/tex. Table 2 The data listed in the table above shows that fibres having a high tenacity are obtained when the draw ratio exceeds 7,5.

Claims: Claims 1. Fibres melt-spun from a thermoplastic alternating copolymer composed of alkenes and carbon monoxide having a - tenacity BT > 900 mN/tex, - melting point Tm > 220°C, - crystallinity Vc > 33%, and - birefringence Δn > 0,0550. 2. Fibres melt-spun from a thermoplastic alternating copolymer composed of alkenes and carbon monoxide having a - tenacity BT > 1000 mN/tex, - melting point Tm > 220°C, - crystallinity Vc > 35%, and - birefringence Δn > 0,0570. 3. Fibres melt-spun from a thermoplastic alternating copolymer composed of ethylene/propylene and carbon monoxide and with a propylene content between 4 and 0,5 mole%, calculated on ethylene, having a - tenacity BT > 1000 mN/tex, - melting point Tm > 240°C, - crystallinity Vc > 40%, and - birefringence Δn > 0,0570. 4. A process for preparing fibres from a thermoplastic alternating copolymer composed of alkenes and carbon monoxide, in which process the copolymer is melt-spun and the resulting fibres are subsequently drawn, characterised in that the spinning process is conducted using a polymer melt free of crystallisation nuclei at a temperature of at most 40K above the melting temperature of the polymer T m (in K) and the drawing of the fibres is conducted at a temperature in the range of T mc - 15K to T mc - 90K, with T mc representing the constrained melting temperature, at a draw ratio in the range of 5 to 12 and a drawing tension corrected for temperature DT d , corr . in the range of 105 to 300 mN/tex, F nB DR DT DR d.corr ejc L(iooo/r,) _ g (looo/r ^ ) lo.s wherein FDR represents the force measured at a draw ratio DR (in mN) and T d represents the drawing temperature (in K), use being made in the calculation of the corrected drawing tension of the linear density of the fibres prior to the start of the drawing process. 5. A process according to claim 4, characterised in that the draw ratio is at least 7 and the drawing tension corrected for temperature is in the range of 120 to 280 mN/tex. 6. A process according to claim 4, characterised in that the tenacity of the obtained fibres (in mN/tex) is in the range of 313ln(DT d , CO rr.) - 575 to 313ln(DT d,corr. ) - 755. 7. A process according to claim 4, characterised in that fibres having a tenacity of more than about 900 mN/tex can be obtained when use is made of a drawing tension corrected for temperature DT d , corr . of more than 140 mN/tex. 8. A process according to claim 4, characterised in that the alternating copolymer contains ethylene. 9. A process according to claim 8, characterised in that in the alternating copolymer 80 to 100% of the alkene units is composed of ethylene. 10. A process according to claim 4, characterised in that the alternating copolymer is composed of ethylene/propylene and carbon monoxide and with a propylene content between 4 and 0,5 mole %, calculated on ethylene. 11. A rubber article into which fibres according to one or more of claims 1-3 or fibres obtained using a process according to one or more of claims 4- 10 have been incorporated. 12. Tyres, more particularly car tyres, into which fibres according to one or more of claims 1-3 or fibres obtained using a process according to one or more of claims 4-10 have been incorporated.

Inventors: DE VRIES ADRIAAN JACOBUS, JUIJN JOHANNES ANTHONIJ, DE VRIES, ADRIAAN, JACOBUS, JUIJN, JOHANNES, ANTHONIJ
Applicants: AKZO NOBEL NV, JUIJN JOHANNES ANTHONIJ, VRIES ADRIAAN JACOBUS DE, AKZO NOBEL N.V., DE VRIES, ADRIAAN, JACOBUS, JUIJN, JOHANNES, ANTHONIJ
Application year: 1999
Main classification: D01F6
IPC codes: D01F6