US3686385A - Formation of elastic and high-tenacity fibers from butene-1 homopolymers and copolymers - Google Patents

Formation of elastic and high-tenacity fibers from butene-1 homopolymers and copolymers Download PDF

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Publication number
US3686385A
US3686385A US112990A US3686385DA US3686385A US 3686385 A US3686385 A US 3686385A US 112990 A US112990 A US 112990A US 3686385D A US3686385D A US 3686385DA US 3686385 A US3686385 A US 3686385A
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fibers
fiber
per cent
butene
tenacity
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Charles L Rohn
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Mobil Oil AS
ExxonMobil Oil Corp
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Mobil Oil AS
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    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
    • D01F6/00—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof
    • D01F6/28—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from copolymers obtained by reactions only involving carbon-to-carbon unsaturated bonds
    • D01F6/30—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from copolymers obtained by reactions only involving carbon-to-carbon unsaturated bonds comprising olefins as the major constituent
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L23/00—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers
    • C08L23/02—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers not modified by chemical after-treatment
    • C08L23/18—Homopolymers or copolymers of hydrocarbons having four or more carbon atoms
    • C08L23/20—Homopolymers or copolymers of hydrocarbons having four or more carbon atoms having four to nine carbon atoms
    • D—TEXTILES; PAPER
    • D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
    • D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
    • D01F6/00—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof
    • D01F6/02—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from homopolymers obtained by reactions only involving carbon-to-carbon unsaturated bonds
    • D01F6/04—Monocomponent artificial filaments or the like of synthetic polymers; Manufacture thereof from homopolymers obtained by reactions only involving carbon-to-carbon unsaturated bonds from polyolefins
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2203/00—Applications
    • C08L2203/12—Applications used for fibers

Definitions

  • 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.
  • 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.
  • butene-l based polymer 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.
  • 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.
  • the draw down ratio is increased, the elongation decreases, i.e., the fiber becomes less elastic and tends to become more tenacious.
  • elastic fibers are prepared using a draw down ratio between about 10 and about 50.
  • the high tenacity fibers are obtained using draw down ratios between about 10 and about 300, as discussed hereinafter and dependent on relationship between variables.
  • the properties of the finished fiber are also dependent upon the crystallinity of the butene based polymer used.
  • FIG. 2 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.
  • 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
  • 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.
  • 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.
  • 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.
  • DDR draw down ratio
  • MI melt index
  • draw down ratio is the ratio between the diameter of the die orifice to the diameter of the final fiber.
  • 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.
  • the highest tenacity fiber is obtained with the lowest M.l. material for a given melt temperature and maximum DDR.
  • 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.
  • 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.
  • fibers can be prepared having n wide range oi'elasticity and tenacity properties by the process of this invention.
  • 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.
  • 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.
  • the draw down ratio will be between about 10 and about 50 and the F will be between about 0.5 and 0.965.
  • the correlation between variables will be as tabulated hereinbefore. I
  • 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.
  • said butene based polymer is polybutene-l homopolymer.

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  • Chemical & Material Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Textile Engineering (AREA)
  • Health & Medical Sciences (AREA)
  • Medicinal Chemistry (AREA)
  • Polymers & Plastics (AREA)
  • Organic Chemistry (AREA)
  • Artificial Filaments (AREA)
  • Addition Polymer Or Copolymer, Post-Treatments, Or Chemical Modifications (AREA)
US112990A 1971-02-05 1971-02-05 Formation of elastic and high-tenacity fibers from butene-1 homopolymers and copolymers Expired - Lifetime US3686385A (en)

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CA (2) CA1005611A (en:Method)
DE (1) DE2205370B2 (en:Method)
FR (1) FR2124454B1 (en:Method)
GB (1) GB1332611A (en:Method)
IT (1) IT947303B (en:Method)
NL (1) NL169906C (en:Method)

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0416620A3 (en) * 1989-09-08 1991-11-21 Kimberly-Clark Corporation Nonwoven fabric laminates
US20040106723A1 (en) * 2002-08-12 2004-06-03 Yang Henry Wu-Hsiang Plasticized polyolefin compositions
US20050106982A1 (en) * 2003-11-17 2005-05-19 3M Innovative Properties Company Nonwoven elastic fibrous webs and methods for making them
US20060189744A1 (en) * 2002-08-12 2006-08-24 Tse Mun F Articles from plasticized thermoplastic polyolefin compositions
US20080317990A1 (en) * 2003-08-12 2008-12-25 Exxonmobil Chemical Company Inc. Crosslinked polyethylene articles and processes to produce same
US7531594B2 (en) 2002-08-12 2009-05-12 Exxonmobil Chemical Patents Inc. Articles from plasticized polyolefin compositions
US7622523B2 (en) 2002-08-12 2009-11-24 Exxonmobil Chemical Patents Inc. Plasticized polyolefin compositions
US7652094B2 (en) 2002-08-12 2010-01-26 Exxonmobil Chemical Patents Inc. Plasticized polyolefin compositions
WO2010077929A1 (en) 2008-12-30 2010-07-08 3M Innovative Properties Company Elastic nonwoven fibrous webs and methods of making and using
US7985801B2 (en) 2002-08-12 2011-07-26 Exxonmobil Chemical Patents Inc. Fibers and nonwovens from plasticized polyolefin compositions
US7998579B2 (en) 2002-08-12 2011-08-16 Exxonmobil Chemical Patents Inc. Polypropylene based fibers and nonwovens
US8003725B2 (en) 2002-08-12 2011-08-23 Exxonmobil Chemical Patents Inc. Plasticized hetero-phase polyolefin blends
US8389615B2 (en) 2004-12-17 2013-03-05 Exxonmobil Chemical Patents Inc. Elastomeric compositions comprising vinylaromatic block copolymer, polypropylene, plastomer, and low molecular weight polyolefin
US8513347B2 (en) 2005-07-15 2013-08-20 Exxonmobil Chemical Patents Inc. Elastomeric compositions

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB882178A (en) * 1957-06-10 1961-11-15 Union Carbide Corp Melt spinning of polyolefines
US3048467A (en) * 1957-06-10 1962-08-07 Union Carbide Corp Textile fibers of polyolefins
US3330897A (en) * 1961-02-07 1967-07-11 Chemcell 1963 Ltd Production of fibers of improved elastic recovery
US3426754A (en) * 1964-06-12 1969-02-11 Celanese Corp Breathable medical dressing
US3498042A (en) * 1966-11-02 1970-03-03 Celanese Corp Staple blend of 3-methylbutene-1 copolymer and cellulosic fibers
US3544662A (en) * 1966-11-02 1970-12-01 Celanese Corp High-melting polymer compositions comprising a 3-methyl-1-butene polymer and another polyolefin
US3549743A (en) * 1967-05-15 1970-12-22 Chemcell Ltd Multistage drawing technique
US3558764A (en) * 1966-09-06 1971-01-26 Celanese Corp Process for preparing microporous film

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR1184914A (fr) * 1956-10-26 1959-07-28 Montedison Spa Perfectionnements aux matières filamenteuses

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB882178A (en) * 1957-06-10 1961-11-15 Union Carbide Corp Melt spinning of polyolefines
US3048467A (en) * 1957-06-10 1962-08-07 Union Carbide Corp Textile fibers of polyolefins
US3330897A (en) * 1961-02-07 1967-07-11 Chemcell 1963 Ltd Production of fibers of improved elastic recovery
US3426754A (en) * 1964-06-12 1969-02-11 Celanese Corp Breathable medical dressing
US3558764A (en) * 1966-09-06 1971-01-26 Celanese Corp Process for preparing microporous film
US3498042A (en) * 1966-11-02 1970-03-03 Celanese Corp Staple blend of 3-methylbutene-1 copolymer and cellulosic fibers
US3544662A (en) * 1966-11-02 1970-12-01 Celanese Corp High-melting polymer compositions comprising a 3-methyl-1-butene polymer and another polyolefin
US3549743A (en) * 1967-05-15 1970-12-22 Chemcell Ltd Multistage drawing technique

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
Sen i to Kogyo Vol. 2 (7) pp. 516 23 (1969) Japan *
Spinning and Properties of Polyolefin Fibers by Oya et al. *

Cited By (32)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0416620A3 (en) * 1989-09-08 1991-11-21 Kimberly-Clark Corporation Nonwoven fabric laminates
US5188885A (en) * 1989-09-08 1993-02-23 Kimberly-Clark Corporation Nonwoven fabric laminates
US7652093B2 (en) 2002-08-12 2010-01-26 Exxonmobil Chemical Patents Inc. Plasticized polyolefin compositions
US7985801B2 (en) 2002-08-12 2011-07-26 Exxonmobil Chemical Patents Inc. Fibers and nonwovens from plasticized polyolefin compositions
US20060189763A1 (en) * 2002-08-12 2006-08-24 Yang Henry W Plasticized polyolefin compositions
US20060189744A1 (en) * 2002-08-12 2006-08-24 Tse Mun F Articles from plasticized thermoplastic polyolefin compositions
US8217112B2 (en) 2002-08-12 2012-07-10 Exxonmobil Chemical Patents Inc. Plasticized polyolefin compositions
US8211968B2 (en) 2002-08-12 2012-07-03 Exxonmobil Chemical Patents Inc. Plasticized polyolefin compositions
US20070100053A1 (en) * 2002-08-12 2007-05-03 Chapman Bryan R Plasticized polyolefin compositions
US7998579B2 (en) 2002-08-12 2011-08-16 Exxonmobil Chemical Patents Inc. Polypropylene based fibers and nonwovens
US7531594B2 (en) 2002-08-12 2009-05-12 Exxonmobil Chemical Patents Inc. Articles from plasticized polyolefin compositions
US7619026B2 (en) 2002-08-12 2009-11-17 Exxonmobil Chemical Patents Inc. Plasticized polyolefin compositions
US7619027B2 (en) * 2002-08-12 2009-11-17 Exxonmobil Chemical Patents Inc. Plasticized polyolefin compositions
US7622523B2 (en) 2002-08-12 2009-11-24 Exxonmobil Chemical Patents Inc. Plasticized polyolefin compositions
US7632887B2 (en) 2002-08-12 2009-12-15 Exxonmobil Chemical Patents Inc. Plasticized polyolefin compositions
US7652094B2 (en) 2002-08-12 2010-01-26 Exxonmobil Chemical Patents Inc. Plasticized polyolefin compositions
US7652092B2 (en) 2002-08-12 2010-01-26 Exxonmobil Chemical Patents Inc. Articles from plasticized thermoplastic polyolefin compositions
US20040106723A1 (en) * 2002-08-12 2004-06-03 Yang Henry Wu-Hsiang Plasticized polyolefin compositions
US8003725B2 (en) 2002-08-12 2011-08-23 Exxonmobil Chemical Patents Inc. Plasticized hetero-phase polyolefin blends
US7875670B2 (en) 2002-08-12 2011-01-25 Exxonmobil Chemical Patents Inc. Articles from plasticized polyolefin compositions
US20110111153A1 (en) * 2003-08-12 2011-05-12 Exxonmobil Chemical Company Inc. Crosslinked polyethylene process
US20080317990A1 (en) * 2003-08-12 2008-12-25 Exxonmobil Chemical Company Inc. Crosslinked polyethylene articles and processes to produce same
US8192813B2 (en) 2003-08-12 2012-06-05 Exxonmobil Chemical Patents, Inc. Crosslinked polyethylene articles and processes to produce same
US8703030B2 (en) 2003-08-12 2014-04-22 Exxonmobil Chemical Patents Inc. Crosslinked polyethylene process
US20050106982A1 (en) * 2003-11-17 2005-05-19 3M Innovative Properties Company Nonwoven elastic fibrous webs and methods for making them
US7744807B2 (en) 2003-11-17 2010-06-29 3M Innovative Properties Company Nonwoven elastic fibrous webs and methods for making them
US20060266462A1 (en) * 2003-11-17 2006-11-30 3M Innovative Properties Company Nonwoven elastic fibrous webs and methods for making them
US20060270303A1 (en) * 2003-11-17 2006-11-30 3M Innovative Properties Company Nonwoven elastic fibrous webs and methods for making them
US8389615B2 (en) 2004-12-17 2013-03-05 Exxonmobil Chemical Patents Inc. Elastomeric compositions comprising vinylaromatic block copolymer, polypropylene, plastomer, and low molecular weight polyolefin
US8513347B2 (en) 2005-07-15 2013-08-20 Exxonmobil Chemical Patents Inc. Elastomeric compositions
WO2010077929A1 (en) 2008-12-30 2010-07-08 3M Innovative Properties Company Elastic nonwoven fibrous webs and methods of making and using
US9840794B2 (en) 2008-12-30 2017-12-12 3M Innovative Properties Compnay Elastic nonwoven fibrous webs and methods of making and using

Also Published As

Publication number Publication date
CA1005611A (en) 1977-02-22
DE2205370B2 (de) 1980-03-13
GB1332611A (en) 1973-10-03
FR2124454B1 (en:Method) 1975-10-24
NL169906B (nl) 1982-04-01
DE2205370A1 (de) 1972-08-17
CA1006321A (en) 1977-03-08
BE778764A (fr) 1972-07-31
IT947303B (it) 1973-05-21
FR2124454A1 (en:Method) 1972-09-22
NL7201525A (en:Method) 1972-08-08
NL169906C (nl) 1982-09-01

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