|Publication number||US3686385 A|
|Publication date||Aug 22, 1972|
|Filing date||Feb 5, 1971|
|Priority date||Feb 5, 1971|
|Also published as||CA1005611A, CA1005611A1, CA1006321A, CA1006321A2, DE2205370A1, DE2205370B2|
|Publication number||US 3686385 A, US 3686385A, US-A-3686385, US3686385 A, US3686385A|
|Inventors||Charles L Rohn|
|Original Assignee||Mobil Oil Corp|
|Export Citation||BiBTeX, EndNote, RefMan|
|Patent Citations (9), Non-Patent Citations (2), Referenced by (32), Classifications (12)|
|External Links: USPTO, USPTO Assignment, Espacenet|
United States Patent Rohn  FORMATION OF ELASTIC AND HIGH- TENACITY FIBERS FROM BUTENEPI HOMOPOLYMERS AND COPOLYMERS  US. Cl. ..264/164, 264/176 F  Int. Cl. ..B29c 17/02, B28b 3/20  Field of Search ..260/88.2; 264/176 F, 210 F,
[ 51 Aug. 22, 1972 FOREIGN PATENTS OR APPLICATIONS 882,178 11/1961 Great Britain ..264/21 0 F 124,700 7/ 1947 Australia ..264/210 F OTHER PUBLICATlONS Spinning and Properties of Polyolefin Fibers by Oya et a1.
Sen-i to Kogyo V01. 2 (7) pp. 516- 23 (1969) Japan Primary ExaminerJay H. Woo Attorney-Oswald G. Hayes, Andrew L. Gaboriault and Hastings S. Trigg ABSIRACT  References Cited Fibers having properties of high elasticity or high tenacity'are formed by drawing from the melt polybu- UNITED STATES PATENTS tene-l or a copolymer of butene-l with up to 20 mole 3,048,467 8/1962 Roberts et a1. ..264/210F Per cent Propylene ethylene converting "B 3 330 897 7/1967 Tessier ..264/176 F draw fiber crystal! Form Case 0f 3 426 754 2/1969 Bierenbaurn etal .128/156 fibers The degree Of depends 3498042 341970 Polestak 57/140 upon the draw down who and the crystalhmty of the 3544662 12/1970 P l "5 211 polymer used, and, in the case of high tenacity fibers,
esta ct l the melt tem erature at the die orifice. 3,549,743 12/1970 RlOI'dOIl ..264/210 F p 3,558,764 1/1971 Isaacson et a1. ..264/210 F 3 Claims, 8 Drawing Figures IO 8 U1 8 53 a 6 A 0 IO 20 3O 4O 5O 6O 7O 8O FIGI PAIENTEDnuczz I972 3.686.385
sum 1 or 8 Elongation to Break,
O O s a a I 2 ouog UMOQ MDJQ INVEXTOR. Char/es L. Rah/7 m Hnsffngs 5. Tr/gg PATENTEmunzz 1912 Sfro'm,"/
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BY 6/mr/es L, [P
Hasf/hgs 5 Trigg ATTORNEY PATENTED I972 3.686.385
SHEET 5 BF 8 H Y Char/es L'. Rah/2 FIG.5
HUS/l/IQS 5 Trigg A'rrmmmv IOO Extension,
. 1 FORMATION OF ELASTIC AND HIGH-TENACITY FIBERS FROM BUTENE-l HOMOPOLYMERS AND cOPOLYMERs BACKGROUND OF THE INVENTION (annealing) step, sometimes with additional draw down in the cold or using a polymer containing an azido cross-linking agent. For example, U. S. Pat. No. 3,256,258 calls for spinning a polypropylene fiber and heat treating it at a temperature of 105C. 160C. U. S. Pat. No. 3,323,190 describes a process in which polypropylene is partially drawn from the melt, cooled, heat treated at 135C. 150C. and thereafter further drawn 40 to 80 per cent. A process for melt spinning polypropylene while drawing down into fibers and then subjecting the fibers to heat treatment under nonstretching conditions at a temperature above 85C. but below the melting point of the polymer is described in U. S. Pat. No. 3,330,897. U. S. Pat. No. 3,432,590 calls for a process of producing elastic polypropylene fibers which involves melt spinning, stretching, cold drawing, heat treating, and finally further cold drawing. U. S. Pat. No. 3,361,859 describes a process for spinning and drawing polypropylene and then cooling the fiber in a gaseous medium at a temperature decreasing with the distance from the spinneret, according to a time-temperature formula. In U. S. Pat. No. 3,377,415, there is described a process for spinning and heat treating polypropylene which calls for the addition of a azido cross-linking agent prior to spinning. U. S. Pat. No. 3,382,306 calls for formation of elastic polypropylene film which involves extruding and drawing the film quenching and heat treating. U. S. Pat. No. 3,485,906 calls for a process similar to that of U. S. Pat. No. 3,377,415 except that an azido cross-linking agent is added to the polypropylene prior to fiber formation.
In Seni To Kogyo, 2(7), 516-23 (1969) there appears a review article on polyolefin fibers, based upon a lecture by Oya and Kitao. Although these authors discuss polybutene-l fibers (relatively briefly) prepared by spin-drawing, they neither discuss nor appear to recognize the importance and significance of the correlation of polymer crystallinity, melt temperature, and draw down ratio to obtain elastic fibers or high tenacity fibers. The present invention discloses to this important correlation. The present inventor has further discovered that fibers drawn from a die must be converted from Form II to Form 1, in order to obtain elastic fibers. The authors are silent on this point. The highest tenacity (g./denier) reported by the authors for polybutene-l is 2-4. The applicant, on the other hand, defines methods for preparing such fibers having tenacities as high as 15 g./denier.
BRIEF DESCRIPTION OF INVENTION The present invention provides a process for forming fibers having properties of elasticity or high tenacity which comprises melt drawing polybutene-1 or copolymers of butene-l with propylene or ethylene and converting to crystalline Form I. The degree of elasticity or tenacity is a function of draw down ratio and the crystallinity of the polymer, and in the case of high tenacity fibers, on melt temperature at the die.
DESCRIPTION OF THE DRAWINGS In the drawings,
FIG. 1 presents a curveshowing the relationship between draw down ratio and elongation to break for elastic fibers formed from polybutene of 53.5 per cent crystallinity.
FIG. 2 shows a curve defining the relationship between the crystallinity of polybutene-1 and the elongation at break.
FIG. 3 presents a curve showing the relationship between the stress-strain extension and recovery of a fiber prepared from polybutene-1 having 53.5 per cent crystallinity.
FIG. 4 shows a similar stress-strain relationship of a fiber prepared from polybutene-l having a crystallinity of 61 per cent.
FIG. 5 presents a curve showing the short time set and per cent extension for fibers prepared from polybutene having various crystallinities.
FIG. 6 presents a curve showing the relationship between the draw down ratio of polybutenes of high crystallinity and medium crystallinity and the crystallite orientation index.
FIG. 7 presents curves showing the relationship between tensile strength (and tenacity) and draw down ratio and melt index (M.l.) of polybutenes drawn at a melt temperature of C.
FIG. 8 presents curves showing the relationship between tensile strength (and tenacity) and draw down ratio and melt temperature of a polybutene-1 having a melt index of 0.4.
DESCRIPTION OF SPECIFIC EMBODIMENTS The polymers used in preparing the fibers in accordance with this invention are called, generically herein, butene-l based polymer. The term butene-l based polymer is used to mean tactic polybutene-1, tactic random copolymers of butene-l and up to 20 mole per cent ethylene, and tactic random copolymer of butene-l and up to 20 mole per cent propylene. These polymers and copolymers are prepared using conventional Ziegler-Natta polymerization processes. A particularly feasible process is carried out using solution polymerization as described in US. Pat. No. 3,362,940. It is to be understood, however, that the method of making the butene-l based polymer is not a critical factor herein, so long as the polymers are highly tactic and contain some crystallinity.
The fibers are readily formed by extruding the butene-l based polymer through a small die orifice and drawing down the extrudate while still in the molten state.
ELASTIC FIBERS After the fiber is formed and is cooled to the solid state, in preparing elastic fibers, it is in the Fonn II crystallinity state. It must then be converted to the Form I crystalline state to form elastic fibers, in accordance with this invention. The transformation from Form II to Form I is carried out at room temperature (25-30C.) and usually takes from a few days up to as long as about days. If the transformation is carried out at temperatures below 25C. or above 30C. the transformation is much slower. Accordingly, annealing the fiber at elevated temperatures, as called for by the prior art, is detrimental to the process of this invention. The transformation from Form II to Form I can be carried out in a matter of about 5 minutes if the fiber is subjected to pressures in the order of about 30,000 p.s.i. If the draw down to form fiber is carried out using a copolymer of butene-l and 5-9 mole per cent propylene, as is described in US. Pat. No. 3,464,962, the transformation from Form H to Form I is extremely rapid. In fact, the transformation is so rapid that crystalline Form II is virtually undetectable in the freshly formed fiber.
The degree of elasticity can be varied over a wide range depending upon the draw down ratio used and the crystallinity of the polymer. In FIG. 1, a curve is presented showing the relationship between draw down ratio and the elongation to break of fibers formed from polybutene-l having 53.5 per cent crystallinity, based upon a series of runs at various draw down ratios. As the draw down ratio is increased, the elongation decreases, i.e., the fiber becomes less elastic and tends to become more tenacious. There appears to be a minimum elongation of about -20 per cent even when draw down ratio is increased well above about 50. In general, elastic fibers are prepared using a draw down ratio between about 10 and about 50. The high tenacity fibers, on the other hand, are obtained using draw down ratios between about 10 and about 300, as discussed hereinafter and dependent on relationship between variables.
As has been indicated herein before, the properties of the finished fiber are also dependent upon the crystallinity of the butene based polymer used. This is shown in FIG. 2 which presents a curve showing the relationship between the crystallinity and the per cent elongation to break of fibers prepared from polybutene-l polymers having varying degrees of crystallinity using a draw down ratio of about 13. It will be noted that, as crystallinity decreases, the elongation increases. This would appear to indicate that if a high elastic fiber is desired, it can be more conveniently prepared from a butene-l based polymer of relatively low crystallinity. For comparison purposes, the fiber was made from polypropylene by extruding and drawing the molten polymer to a draw down ratio of 12, as described in U. S. Pat. No. 3,323,190. The fibers, after draw down, were heat treated for 10 minutes at 140C. and then cold drawn 100 per cent. The fiber was elongated 65 per cent and permitted to relax. The fiber recovered 84 per cent of its original length. Stressstrain extension and recovery with the polypropylene fiber shows that the degree of set is much higher (approximately 16 per cent) for the polypropylene fiber than for polybutene-l fiber.
A conventional method for measuring the elasticity of a fiber is by means of the so-called stress-strain relationship. This is demonstrated in FIGS. 3 and 4.
FIG. 3 presents the stress-strain relationship of a fiber prepared at a draw down ratio of 10, at a melt temperature of 190C., using polybutene-l having crystallinity of 53.5 per cent. The data on the curve shown in FIG. 3 were obtained by stretching the fiber to a point below its break point while noting the amount of stress to give a given degree of strain, i.e., per cent of stretch or elongation. Curve A shows this relationship while stretching the polybutene fiber and Curve B shows the relationship as stress is removed and the fiber is permitted to relax. It will be noted that the per cent recovery of the fiber after stress was quite high. Indeed, within 24 hours the fiber has relaxed to its original length. The measurements shown in FIG. 3 were made at 2 minutes after relaxation of the fiber.
FIG. 4 presents a stress-strain relationship of a fiber prepared from polybutene-l having 61 per cent crystallinity using a draw down ratio of 10, at a melt temperature of C. Curve C shows the relationship while stress is being applied and Curve D shows the relationship upon relaxation. It will be noted again that the amount of recovery after 2 minutes was very high. It is also noteworthy that in comparing FIGS. 3 and 4 the fiber prepared from a more highly crystalline polybutene could be stretched to a lesser degree than that prepared from a less crystalline polybutene, although the recovery was greater.
The recovery and short time set of elastic fibers made in accordance with this invention was measured at different amounts of stretching. The property of set is the ability of the fiber to return to its original length when it is relaxed after being subjected to single or repeated stresses. In this work, set was determined two minutes after the stretching force was relaxed. It has been found that by increasing the crystallinity of the fiber, the amount of short time set for extensions up to 50 per cent is decreased. FIG. 5 presents curves showing the relationship between the short time set and per cent extension of fibers prepared at a draw down ratio of 10, at a melt temperature of 190C., with polybutenes of different crystallinities. Curve E was obtained using polybutene having 33 per cent crystallinity. Curve F was obtained from a polybutene having a crystallinity of 53.5 per cent and Curve G was obtained using a polybutene having a crystallinity of 61 per cent. As shown in FIG. 5 the fibers prepared from polybutenes of lower crystallinity tend to have greater short time sets. The short time sets of these fibers, however, are not permanent and within 16-24 hours recover completely to their original length.
A series of fibers were prepared using polybutene-1 homopolymers having varying degrees of crystallinity and using varying draw down ratios. Stretch, recovery, and tensile data for fibers prepared from these polymers are set forth in Table I.
Similarly, fibers were prepared from a copolymer prepared from 92 mole per cent butene-l and 8 mole per cent ethylene, said copolymer having a crystallinity of about 39 per cent, at various draw down ratios. Pertinent data for these fibers are set forth in Table H.
' ELASTIC VS. HIGH TENACITY FIBER It has been found that by following the operations within the parameters of this invention, there is a correlation between the crystalline'orientation index and the draw down ratio which appears to be independent of the crystallinity. The curve in FIG. 6 was obtained from aszimuthal beams on the (1 l0) reflection of Form I modification of polybutene-1 for fibers drawn in accordance with this invention. On the curve in FIG. 6, there is plotted the Fl 10 vs. the square root of the draw down ratio. In this work, a portion of the curve between A and B represents the area for elastic fibers. The portion of the curve from B to C represents the area for high tenacity fibers.
HIGH TENACITY FIBERS There are two main factors in addition to draw down ratio (DDR) that affect the tenacity of polybutene based polymer fibers. These are, melt index (MI) of the polymer and the melt temperature in the die. As is well known to those familiar with the art, draw down ratio is the ratio between the diameter of the die orifice to the diameter of the final fiber. Tensile strength and tenacity are related by the following formula:
Tensile strength, p.s.i. 12,800
X Tenacity wifi astiest??? FIG. 7 shows how the tenacity (tensile strength) of polybutene fibers increase with increasing M.I. when drawn over a range of DDR at 190C. melt temperature. In general, the highest tenacity fiber is obtained with the lowest M.l. material for a given melt temperature and maximum DDR. For example, a 0.4 M.I. fiber and a 5 M.I. fiber, both drawn at a DDR of I40 and melt temperature of 190C., have tenacities of 14 g./denier and 4 g./denier, respectively.
Increasing temperature affects the tenacity of polybutene fibers in a similar way that Ml. does. FIG. 8 shows how the tenacity of 0.4 Ml. polybutene fiber decreases with increasing melt temperature. For each isotherm, the tenacity increases linearly with increasing DDR, and then reaches a plateau or upper limit. This limit decreases with increasing melt temperature.
Butene based polymer fibers with tenacities greater than 4 g./denier can only be made within certain ranges of M.I. and melt temperatures. These ranges are specified in the following table.
CONDITIONS FOR MAKING PB-l FIBERS WITH TENACITIES ABOVE 4 GJDENIER The reason 4 g./denier was taken as a lower limit of tenacity is because conventional fiber spinning processes can be used which will make poly(butylene) fibers with tenacities between 2-4 g./denier. Also, conditions exist for the melt drawing process that will produce fibers in this tenacity range. For example, polybutene fiber with M1. of 5 and drawn at a melt temperature of 240C. and a maximum DDR has a tenacity of 3.1 g./denier and a break elongation of 47 percent Note that these tensile properties are similar to those of the poly(butylene) fibers reported on page 20 of the translation of article Spinning and Properties of P0ly(olefin) Fibers by Seigo Oya and Tashio Kitao. (p. 522 of the original Japanese article.)
As will be noted from the foregoing description, fibers can be prepared having n wide range oi'elasticity and tenacity properties by the process of this invention. Thus, the crystallinity and draw down ratios can be selected to give a desired property depending upon the intended end use. If dimensional stability is the primary requirement, such as in the case of mens suits or tailored clothing, then the available stretch levels should be 20-30 per cent. On the other hand, if comfort is the primary requirement, as in the case of sport-. swear, the stretch level should be about 25-40 per cent. Tensioned slacks with foot stirrups use more of the available fabric stretch than any other outer wear garment. The stretch level for such slacks should be about 40-50 per cent.
The fibers produced by the process of this invention can also be used to make ropes. If high strength is required, the ropes should be made from fibers having high tenacity. If, on the other hand, a rope is desired that has a certain amount of give, as in the case of safety lines or tow ropes, then elasticity would be a more desirable factor at the expense of lesser tenacity.
SUMMARY In general in reducing fibers from butene based polymer, in accordance with this invention, the draw down ratio can be between about 10 and about 300. The melt temperature can be between about 120C. and about 270C. The butene based polymer can have a crystallinity of between about 30 per cent and about 65 per cent and a melt index of between about 0.4 or less and about 20. In the preparation of elastic fibers, the draw down ratio will be between about 10 and about 50 and the F will be between about 0.5 and 0.965. In the case of high tenacity fibers, the correlation between variables will be as tabulated hereinbefore. I
Although the present invention has been described in conjunction with preferred embodiments, it is to be understood that modifications and variations may be resorted to without departing from the spirit and scope thereof, as those skilled in the art will readily understand. Such variations and modifications are considered to be within the purview and scope of the appended claims.
What is claimed is:
1. A process for forming fibers having properties of elasticity or high tenacity which comprises melt drawing from a die butene based polymer selected from the group consisting of tactic polybutene-l, tactic random copolymers of butene-1 and up to 20 mole per cent ethylene, and tactic random copolymers of butene-1 and up to 20 mole per cent propylene, at a draw down ratio of between about 10 and about 300, at a melt temperature between about 120C. and 270C, said butene based polymer having a crystallinity between about 30 and about 65 and a melt index of 0.4 or less to about in the case of forming elastic fibers, said draw down Melt Temperature Range, C. Minimum DDR 2. The process of claim 1 wherein said butene based polymer is polybutene-l homopolymer. I
3. The process of claim 1 wherein said butene based polymer is a copolymer of 92 mole per cent butene-l with 8 mole per cent ethylene.
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|1||*||Sen i to Kogyo Vol. 2 (7) pp. 516 23 (1969) Japan|
|2||*||Spinning and Properties of Polyolefin Fibers by Oya et al.|
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|U.S. Classification||264/164, 526/348.1, 264/210.8|
|International Classification||D01F6/04, D01F6/28, C08L23/20|
|Cooperative Classification||D01F6/04, D01F6/30, C08L23/20, C08L2203/12|
|European Classification||D01F6/30, D01F6/04|