Plastic laminate structure and vessel

DESCRIPTION
BACKGROUND OF THE INVENTION
(1) Field of the Invention
The present invention relates to a plastic laminate. More particularly, the present invention relates to a plastic laminate structure comprising a layer of a creep-resistant resin represented by polyethylene terephthalate and a gas barrier layer of an olefin-vinyl alcohol copolymer, which are tightly bonded to each other through a copolyester type adhesive layer. Furthermore, the present invention relates to a multi-layer plastic vessel which is excellent in the combination of the gas barrier property, creep resistance, rigidity, impact resistance, heat resistance, interlaminar peel strength and transparency and is valuable for sealing and storing contents such as foods for a long time.
(2) Description of the Prior Art
Polyethylene terephthalate is excellent in moldability and mechanical properties such as creep resistance and can be molecularly biaxially oriented. Accordingly, polyethylene terephthalate is widely used for a light-weight plastic vessel, especially a bottle for a drink, which is excellent in such properties as creep resistance, impact resistance, rigidity, gas barrier property, light weight characteristic, heat resistance and transparency. However, the gas permeability of this polyester bottle is still higher than that of a glass bottle and cannot be neglected. For example, it is said that the shelf life of a small polyester bottle having an inner volume smaller than 1 litter, which is filled with a carbonated drink such as cola, is about 2 months at longest.
An olefin-vinyl alcohol copolymer such as a saponified ethylene-vinyl acetate copolymer is known as a heat-formable resin excellent in the oxygen barrier property, and it also is known that this resin is combined with an olefin resin excellent in the moisture resistance and the laminate is used for the production of an undrawn or drawn multi-layer plastic vessel.
Formation of a vessel from a laminate structure comprising a polyester layer and an olefin-vinyl alcohol copolymer layer has already been proposed. It is naturally expected that this laminate structure will be excellent in the combination of the gas barrier property, creep resistance, heat resistance, impact resistance and rigidity, but this laminate structure has not practically been used for a vessel, especially a biaxially drawn blow-formed vessel. The reason is considered to be that a thermoplastic adhesive capable of forming a strong interlaminar bond between a polyester and an olefin-vinyl alcohol copolymer has not been found out.
SUMMARY OF THE INVENTION
We found that a thermoplastic resin adhesive composed mainly of a specific copolyester described hereinafter tightly bonds in the melted state a layer of a creep-resistant layer such as a polyester or polycarbonate to a layer of an olefin-vinyl alcohol copolymer layer and the interlaminar bonding force of this adhesive is not lost under conditions for blow forming, thermoforming, draw-blow forming, draw forming or other vessel-forming operation.
It is therefore a primary object of the present invention to provide a plastic laminate structure comprising a layer of a creep-resistant resin such as polyethylene terephthalate and a layer of an olefin-vinyl alcohol copolymer, which are tightly bonded to each other.
Another object of the present invention is to provide a plastic laminate structure which is excellent in the gas barrier property, creep resistance, impact resistance, rigidity, heat resistance, interlaminar peel strength and transparency and is valuable as a material for the production of a sealed vessel in the form of a bottle or cup.
More specifically, in accordance with the present invention, there is provided a laminate structure comprising a layer of a creep-resistant resin composed mainly of ester recurring units and a gas barrier layer containing an olefin-vinyl alcohol copolymer, which are laminated through a thermoplastic resin adhesive layer, wherein the adhesive resin is composed of a copolyester or copolyester composition comprising in the main chain at least two acid components selected from (i) an isophthalic acid component, (ii) a terephthalic acid component and (iii) a linear or cyclic aliphatic dibasic acid component.
In accordance with the present invention, there also is provided a sealing multi-layer plastic vessel comprising the above-mentioned laminate structure.

BRIEF DESCRIPTION OF THE DRAWINGS
FIG. 1 is a sectional view of a draw-blow-formed vessel comprising a laminate structure of the present invention.
FIG. 2 is an enlarged view showing the sectional structure (II) of the vessel shown in FIG. 1.
FIG. 3 is a sectional side view showing an embodiment of a plastic laminate structure in the form of a cup.
FIG. 4 is an enlarged view showing the section of the laminate structure (IV) shown in FIG. 3.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
Referring to FIG. 1 illustrating an embodiment of a plastic laminate structure in the form of a bottle, this vessel comprises a barrel 1, a bottom 2 connected to the lower end of the barrel, a conical shoulder 3 connected to the upper end of the barrel and a neck 4 connected to the upper end of the shoulder, which are integrally formed from a multi-layer preform, described in detail hereinafter, by draw-blow forming.
This bottle is prepared by draw-blowing the preform biaxially, that is, by mechanically drawing the preform in the axial direction of the vessel and blowing a fluid into the preform to draw the preform in the circumferential direction. Accordingly, the resin constituting the barrel of the bottle is molecularly biaxially oriented, that is, in both the axial direction and circumferential direction of the bottle.
Referring to FIG. 2 which is an enlarged view showing the section of the wall of the barrel of the bottle shown in FIG. 1, the wall of the barrel comprises an inner surface layer of a polyester composed mainly of ethylene terephthalate units, an outer surface layer composed of the same polyester, and an intermediate gas barrier layer 7 containing an olefin-vinyl alcohol copolymer interposed between the inner and outer surface layers 5 and 6. These polyester layers 5 and 6 are tightly heat-bonded to the gas barrier layer 7 through adhesive layers 8 and 9 containing a copolyester described in detail hereinafter.
The present invention is characterized in that the creep-resistant resin layers 5 and 6 are heat-bonded to the olefin-vinyl alcohol copolymer-containing gas barrier layer 7 through an adhesive layer composed of a copolyester or copolyester composition comprising in the main chain at least two acid components selected from (i) an isophthalic acid component, (ii) a terephthalic acid component and (iii) a linear or cyclic aliphatic dibasic acid component.
The present invention utilizes the phenomenon that the above-mentioned specific copolyester adhesive forms a strong bond by heating between a creep-resistant resin composed of ester recurring units, such as polyethylene terephthalate, polybutylene terephthalate, polycarbonate or polyacrylate and an olefin-vinyl alcohol copolymer.
In the copolyester used in the present invention, the dibasic acid components are included in the polyester chain in the form of a combination of isophthalic acid and terephthalic acid or a combination of isophthalic acid and/or terephthalic acid with a linear or cyclic aliphatic dibasic acid.
From the viewpoint of the heat bondability to the olefin-vinyl alcohol copolymer, it is important that the copolyester should comprise in the main chain at least two dibasic acid components selected from the above-mentioned dibasic acid components (i) through (iii). Furthermore, from the viewpoint of the bondability to the creep-resistant resin, it is important that the aromatic dibasic acid component (i) and/or the aromatic dibasic acid component (ii) should be contained in the main chain.
In connection with the copolyester to be used for heat bonding of an olefin-vinyl alcohol copolymer to a creep-resistant resin such as polyethylene terephthalate, not only the bonding force or affinity to the two resin layers but also the crystallinity or physical characteristics of the copolyester per se should be taken into consideration. The reasons why the copolyester used in the present invention has an excellent bondability to both the olefin-vinyl alcohol copolymer and the creep-resistant resin, the strength of this bonding is not changed with the lapse of time and reduction of the bonding strength is very small even if the bonded structure is subjected to the forming operation such as draw forming are considered to be as follows.
The copolyester used in the present invention comprises relatively hard or rigid ester segments derived from the aromatic dibasic acid component and relatively flexible or soft segments derived from the isophthalic acid or aliphatic dibasic acid component. Because of the presence of the relatively flexible or soft segments, the copolyester chain is liable to have an easily mobile structure, and the probability of formation of a hydrogen bond between the hydroxyl group of the olefin-vinyl alcohol copolymer and the ester carbonyl group or ether group is increased and the degree of actual formation of the hydrogen bond is increased. Furthermore, since the copolyester has aromatic ester segments, the copolyester is tightly bonded to the creep-resistant resin having similar aromatic ester segments.
As the inherent problem of the heat adhesive, there can be mentioned a crystallization tendency of the heat adhesive resin. The bonding of the olefin-vinyl alcohol copolymer to the creep-resistant resin should naturally be performed in the state where the copolyester is melted. If this copolyester is crystallized during cooling to room temperature from the melted state or during standing for a certain period or at the forming step such as the draw-forming step, the bonding strength is drastically reduced by molecular orientation due to crystallization or by changes of the physical properties due to crystallization. Since the copolyester used in the present invention contains the isophthalic acid component and/or the aliphatic dibasic acid component, the crystallinity of the copolyester is drastically reduced, and since the crystallization speed of the copolyester is increased by the isophthalic acid component and/or the aliphatic acid component, the maximum crystallization degree that the copolyester can take is controlled to a very low level and crystallization with the lapse of time is inhibited, with the result that the bonding strength is stabilized.
Furthermore, since the copolyester used in the present invention contains at least two dibasic acid components selected from the above-mentioned dibasic acid components (i) through (iii), the glass transition temperature (Tg) of the copolyester is controlled to a relatively low level, molecular orientation or orientation crystallization of the adhesive resin is prevented at the forming step such as the draw-forming step, or degradation of the adhesion is controlled at the forming step.
In case of an adhesive resin having highly elastomeric characteristics, the stress is left in the bonding interface under conditions for the forming operation such as draw forming, resulting in degradation of the adhesion. In contrast, in the copolyester used in the present invention, since hard ester segments and soft ester segments are contained with a good balance, it is considered that the adhesive layer has a softness enough to resist the forming operation and the stress left in the bonding interface is reduced.
The copolyester used in the present invention may be an optional copolyester or copolyester composition satisfying the above-mentioned condition.
For example, copolyesters comprising recurring units represented by the following formula: ##STR1## wherein R.sub.1 stands for an aliphatic divalent hydrocarbon group, and R.sub.2 stands for a divalent hydrocarbon group composed mainly of a p-phenylene group, an m-phenylene group or a linear or cyclic aliphatic hydrocarbon group, with the proviso that at least two kinds of these groups are present in all the recurring units, may be used singly or in the form of a blend of two or more of them.
Benzene-dicarboxylic acids such as isophthalic acid and terephthalic acid are preferred as the aromatic dibasic acid component. Furthermore, naphthalenedicarboxylic acid, diphenyl-dicarboxylic acid, diphenylmethane-dicarboxylic acid and 2,2-bis(4-carboxyphenyl)propane can be used.
Linear or cyclic aliphatic dibasic acids may be used. As the linear dicarboxylic acid, there can be mentioned succinic acid, fumaric acid, maleic acid, adipic acid, azelaic acid, sebacic acid, 1,8-octane-dicarboxylic acid, 1,10-decane-dicarboxylic acid, 1,12-dodecanedicarboxylic acid, 1,12-dodecane-dicarboxylic acid and dimer acid. As the cyclic aliphatic dicarboxylic acid, there can be mentioned 1,2-cyclohexane-dicarboxylic acid, 1,3-cyclohexane-dicarboxylic acid and 1,4-cyclohexanedicarboxylic acid.
As the glycol component, there can be mentioned ethylene glycol, propylene glycol, 1,4-butane-diol, neopentyl glycol, cyclohexane-diol, xylene glycol and hexahydroxylylene glycol.
It is preferred that the copolyester used in the present invention should comprise 1,4-butane-diol as the main glycol component. Namely, a copolyester comprising 1,4-butane-diol as the glycol component has a higher bonding force to the olefin-vinyl alcohol copolymer than a copolyester comprising other glycol component, and when this copolyester is used, reduction of the bonding force in the laminate with the lapse of time or degradation of the adhesion at the forming step is controlled to a very low level.
In accordance with one embodiment of the present invention, a copolyester containing isophthalic acid and terephthalic acid components in combination in the main chain is used.
In the copolyester of this type used in the present invention, the molar ratio between terephthalic acid and isophthalic acid can be changed within a considerably broad range as shown in Tables 1 and 2 given hereinafter. Of the dibasic acid components of this copolyester, the terephthalic acid component has a relation to the heat bondability to the creep-resistant resin layer such as a polyethylene terephthalate layer and also has a relation to the mechanical strength or heat resistance of the copolyester of the adhesive per se. On the other hand, the isophthalic acid component has a relation to the heat bondability to the olefin-vinyl alcohol copolymer layer and makes contributions to the improvement of the heat bondability by reduction of the melting point of the copolyester and to the improvement of such properties of the copolyester as the elasticity and flexibility. From the results shown in Tables 1 and 2, it will readily be understood that if the amount of isophthalic acid is at least 5 mole % based on the dibasic acid components in the copolyester, the adhesion strength to the ethylene-vinyl alcohol copolymer can prominently be improved.
If the content of terephthalic acid in the dibasic acid components is reduced, the bonding force to polyethylene terephthalate is reduced but this bonding force is still higher than the bonding force to the ethylenevinyl alcohol copolymer. It is generally preferred that the terephthalic acid/isophthalic acid molar ratio be in the range of from 95/5 to 35/65. In the case where the bonding force to polyethylene terephthalate may be at the same level as the bonding force to the ethylene-vinyl alcohol copolymer, the content of terephthalic acid in the dibasic acids may be as low as about 10 mole %.
In accordance with one preferred embodiment of the present invention, a copolyester or copolyester composition comprising at least 25 mole % of an aromatic dibasic acid component and 5 to 75 mole % of a linear or cyclic aliphatic dibasic acid component is used for the adhesive layer. From the viewpoint of the bondability to the olefin-vinyl alcohol copolymer, it is important that this copolyester should contain in the main chain an aliphatic dibasic acid component in an amount of 5 to 75 mole %, especially 10 to 70 mole %, based on the dibasic acid components. From the viewpoint of the bondability to the creep-resistant resin, it is important that an aromatic acid component should be contained in the main chain in an amount of at least 25 mole % based on the dibasic acid components.
A copolyester free of an aliphatic dibasic acid component or a copolyester in which the content of an aliphatic dibasic acid component is lower than 5 mole % based on the total dibasic acid components is generally poor in the heat bondability to an olefin-vinyl alcohol copolymer, and even if a high adhesion strength is obtained just after the heat bonding, the adhesion strength is drastically reduced with the lapse of time and extreme reduction of the adhesion strength is readily caused in the laminate structure at the forming step such as the draw-forming step.
A copolyester in which the content of the aliphatic dibasic acid component is higher than 75 mole %, that is, a copolyester in which the content of the aromatic dibasic acid component is lower than 25 mole %, is generally poor in the heat bondability to a creep-resistant resin such as polyethylene terephthalate, and the adhesion strength to the creep-resistant resin is readily reduced with the lapse of time or at the forming step such as the draw-forming step.
These facts will become apparent from the results shown in Examples and Comparative Examples given hereinafter.
In accordance with another preferred embodiment of the present invention, a copolyester comprising an isophthalic acid component in an amount of at least 5 mole % based on the total dibasic acid components is used. More specifically, a copolyester derived from isophthalic acid has a higher bondability to an olefin-vinyl alcohol copolymer than a copolyester derived from terephthalic acid, when the comparison is made based on the same aromatic dibasic acid component content. It is considered that since isophthalic acid ester units form a more readily mobile polyester chain structure than p-oriented terephthalic acid ester units, bondability to the olefin-vinyl alcohol copolymer is improved in the above-mentioned copolyester.
It is preferred that the aliphatic dibasic acid component contained in the copolyester be composed mainly of a dibasic acid having 4 to 12 carbon atoms, especially 5 to 12 carbon atoms. If the carbon number of the aliphatic dibasic acid is larger than 12, the bonding force to the ethylene-vinyl alcohol copolymer tends to decrease, and if the carbon number is smaller than 4, the water resistance of the copolyester is reduced and the adhesion strength is reduced with the lapse of time.
The copolyester used in the present invention is composed mainly of the above-mentioned recurring units, but it may comprise minor amounts of other ester recurring units so far as the essential characteristics of the copolyester are not impaired.
It is preferred that the copolyester used in the present invention should have a glass transition temperature (Tg) of -40.degree. to 75.degree. C., especially -40.degree. to 40.degree. C. If the glass transition temperature Tg is too high and exceeds the above range, the adhesion strength is considerably reduced when the laminate is subjected to the forming operation such as the draw-forming operation. The reason is considered to be that if the glass transition temperature is too high, in the copolyester adhesive layer, molecular orientation or orientation crystallization is caused at the forming step or even when the copolyester has a high softness and is highly elastomeric, the elastic recovery stress is readily left in the bonding interface after the forming operation, and no good bonding force is obtained in each case. If the glass transition temperature Tg of the copolyester is too low and below the above range, the cohesive force of the copolyester per se at a temperature close to room temperature is drastically reduced, and also the bonding force is extremely reduced and reduction of the bonding force with the lapse of time becomes prominent. Furthermore, when the laminate structure is formed into a vessel, the appearance and dimension stability are drastically reduced.
It is ordinarily preferred that the intrinsic viscosity [.eta.] of the copolyester used in the present invention be 0.3 to 2.8 dl/g, especially 0.4 to 1.8 dl/g, as measured at a temperature of 30.degree. C. in a mixed solvent comprising phenol and tetrachloroethane at a weight ratio of 60/40. From the viewpoint of the adaptability to the heat bonding operation, it is preferred that the softening point of the copolyester be lower than 230.degree. C., especially -30.degree. to 200.degree. C., as measured according to the method described in the example.
The above-mentioned copolyesters may be used singly or in the form of a blend of two or more of them. Furthermore, the copolyester may be used in the form of a blend with other thermoplastic resin, for example, an olefin resin such as polyethylene, polypropylene, an ethylene-propylene copolymer, an ethylene-butene-1 copolymer, an ion-crosslinked olefin copolymer (ionomer), an ethylene-vinyl acetate copolymer, an ethylene-acrylic acid copolymer, ethylene-ethyl acrylate copolymer, acid-modified polyethylene or acid-modified polypropylene. The olefin resin is used in an amount of up to 50% by weight, especially up to 30% by weight, based on the total adhesive.
When the laminate structure of the present invention is used as a film or sheet, especially for the production of a vessel, in order to prevent deformation under application of a pressure and also from the viewpoint of the mechanical strength or water resistance, the creep-resistant resin layer should comprise ester recurring units.
A creep-resistant resin having such rheological properties that the sum of the initial elasticity modulus (Eg) and delayed elasticity modulus (El), as measured at a temperature of 23.degree. C. and a stress of 7.times.10.sup.7 dyne/cm.sup.2 is at least 1.times.10.sup.10 dyne/cm.sup.2, the steady flow viscosity coefficient (.eta..sub..infin.) is at least 1.times.10.sup.17 dyne/cm.sup.2 and the delay time (t.sub.R) is less than 6.times.10.sup.6 sec is advantageously used.
Ordinarily, when a stress S is applied to a viscoelastomer such as a thermoplastic polymer for a time t, with increase of the time t, not only influences of the elasticity but also influences of the viscosity are manifested and the system shows viscoelastic behaviors, and when the time t is sufficiently large, the viscous flow is caused. These viscoelastic behaviors can be typically represented by such characteristics as the above-mentioned factors Eg, El, .eta..sub..infin. and t.sub.R.
When the formed vessel is used as a pressure-resistant vessel such as a carbonated drink vessel or an aerosol vessel, the material constituting the vessel wall is required to have not only an excellent gas barrier property but also an appropriate hardness capable of resisting the pressure of the content and a good combination of the creep resistance and impact resistance.
Of the above-mentioned viscoelastic characteristics, the sum (Eg+El) of the initial elasticity modulus and delayed elasticity modulus has a relation to the hardness of the vessel. In the present invention, from the viewpoint of the pressure resistance, it is important that the value of (Eg+El) should be at least 1.times.10.sup.10 dyne/cm.sup.2, especially at least 2.times.10.sup.10 dyne/cm.sup.2, as measured at a temperature of 23.degree. C. and a stress of 7.times.10.sup.7 dyne/cm.sup.2. The steady flow viscosity coefficient (.eta..sub..infin.) and delay time (t.sub.R) have a relation to the creep resistance. In the present invention, in order to prevent the creep, it is important that the value .eta..sub..infin. should be at least 1.times.10.sup.17 poise, especially at least 5.times.10.sup.17 poise, and t.sub.R should be less than 6.times.10.sup.6 sec, especially less than 3.times.10.sup.6 sec.
In view of these characteristics, as the thermoplastic resin suitable for attaining the objects of the present invention, there can be mentioned, in the order of importance, polyethylene terephthalate (PET), polybutylene terephthalate (PBT), polycarbonate (PC) and polyacrylate (PAR). Blends of two or more of these resins can also be used. Furthermore, other thermoplastic resin may be blended, so far as the creep resistance is not impaired. The above-mentioned polyesters may be used in the form of so-called homopolymers, but in order to improve the characteristics at the heat forming step, small amounts of comonomers may be introduced into the main chains. For example, modified PET or modified PBT in which hexahydroxylylene glycol is incorporated as the glycol component for improving the drawdown characteristic can be used for attaining the objects of the present invention. The polycarbonate is a poly(carbonic acid ester) derived from a dihydroxy compound and phosgene. For example, there can be mentioned poly-p-xylyleneglycol biscarbonate, polydihydroxydiphenylmethane carbonate, polydihydroxydiphenyl-2,2-propane carbonate and polydihydroxydiphenyl-1,1-ethane carbonate. As the polyarylate, there can be mentioned a polymer comprising ester recurring units derived from terephthalic acid and/or isophthalic acid and a bisphenol.
Ordinarily, the creep-resistant resin should have a film-forming molecular weight.
As the olefin-vinyl alcohol copolymer, there can be used a copolymer comprising units of an olefin such as ethylene or propylene and vinyl alcohol units obtained by saponifying units of a vinyl ester such as vinyl acetate. From the viewpoint of the gas barrier property and moisture resistance, it is important that the olefin-vinyl alcohol copolymer should contain 40 to 80 mole %, especially 50 to 75 mole %, of the vinyl alcohol units, and the content of the residual vinyl ester units should be lower than 4 mole %, especially lower than 1 mole %. It is preferred that the olefin-vinyl alcohol copolymer should have an intrinsic viscosity [.eta.] of 0.7 to 1.7 dl/g as measured at 30.degree. C. in a mixed solvent comprising phenol and water at a weight ratio of 85/15.
The olefin-vinyl alcohol copolymer alone may be used for the gas barrier layer. Furthermore, this copolymer may be used in the form of a blend with other thermoplastic resin for the gas barrier layer. As a preferred example of the blend, there can be mentioned a blend comprising an olefin-vinyl alcohol copolymer and a polyamide at a weight ratio of from 95/5 to 40/60, especially from 90/10 to 50/50. As described in Japanese Patent Publication No. 42493/82, this blend has a small oxygen permeation coefficient almost comparable to that of the olefin-vinyl alcohol copolymer and is excellent in the adaptability to the draw-forming operation. Accordingly, this blend is advantageously used for the production of a draw-blow-formed vessel or a sheet-formed vessel by drawing.
In the laminate structure of the present invention, the layer arrangement is not particularly critical, so far as the copolyester adhesive layer (CAP) is interposed between the creep-resistant resin layer (PT) and the olefin-vinyl alcohol copolymer layer (PEVA). For example, there can optionally be adopted a symmetric five-layer structure of PT/CAP/PEVA/CAP/PT shown in the drawings, a three-layer structure of PT/CAP/PEVA, and a four-layer structure of PT/CAP/PEVA/CAP.
Scraps formed by pulverizing defective articles in the vessel-forming process may be incorporated in the creep-resistant resin. In the present invention, there may be adopted laminate structures including a scrap layer (SR), such as a six-layer structure of SR/PT/CAP/PEVA/CAP/PT or PT/SR/CAP/PEVA/CAP/PT, and a seven-layer structure of SR/PT/CAP/PEVA/CAP/PT/SR or PT/SR/CAP/PEVA/CAP/SR/PT.
The thickness of each of the foregoing three layers may optionally be changed. However, in order to obtain an optimum combination of the gas barrier property, impact resistance, rigidity, heat resistance and interlaminar peel strength, it is preferred that the PT layer be thickest and the CAP and PEVA layers be thinner than the PT layer. More specifically, it is preferred that the PT/PEVA thickness ratio be in the range of from 100/1 to 5/1 and the PEVA/CAP thickness ratio be in the range of from 10/1 to 1/2. It is preferred that the entire thickness of the laminate in the form of a final vessel be 50 to 3000 microns, especially 100 to 2000 microns.
The laminate is formed preferably by co-extrusion of multiple layers. Since two resins are sufficiently mingled in the bonding interface between two adjacent resin layers if this co-extrusion is adopted, a laminate structure having an especially high adhesion strength can be obtained. In this co-extrusion method, the creep-resistant resin, gas barrier resin and copolyester adhesive are independently melt-kneaded in extruders for the respective resins, these resins are extruded through a multi-layer multi-ply die so that the copolyester is interposed between the creep-resistant resin layer and gas barrier resin layer, and the extrudate is formed into a film, a sheet, a pipe for a bottle or a preform for a bottle. Incidentally, a preform for a bottle is obtained by subjecting a molten resin parison formed by co-extrusion to preliminary blow forming in a mold or by cooling a pipe formed by co-extrusion, cutting the pipe into a predetermined length, heating the upper and lower end portions of the cut pipe again and forming a mouth screw and a bottom by compression forming or the like.
Formation of the laminate can also be accomplished according to the sandwich lamination method or extrusion coating method. For example, a copolyester adhesive is extruded in the form of a film between a preformed film of a creep-resistant resin such as polyethylene terephthalate and a preformed film of an olefin-vinyl alcohol copolymer, and the assembly is pressed, if necessary under heating, whereby a laminate structure is formed. According to another method, an olefin-vinyl alcohol copolymer as an intermediate layer and a copolyester adhesive as inner and outer layers are simultaneously extruded between two films of a creep-resistant resin, and the simultaneously extruded layers are sandwiched with the creep-resistant resin films and the assembly is pressed, whereby a laminate structure is obtained. Furthermore, there may be adopted a method in which a copolyester adhesive and an olefin-vinyl alcohol copolymer are extrustion-coated in succession on the surface of a creep-resistant resin film, and a method in which three kinds of preformed films are heat-pressed or heat-rolled in the above-mentioned lamination order.
Moreover, for formation of a multi-layer preform, there may be adopted a method in which a copolyester adhesive and an olefin-vinyl alcohol copolymer are inejcted in succession on the inner or outer surface of a bottomed preform composed of a creep-resistant resin such as polyethylene terephthalate, whereby a preform having a multi-layer structure is prepared.
The laminate structure of the present invention is especially valuable for the production of a draw-blow-formed vessel or a sheet-formed vessel by drawing. For example, draw-blow forming can be performed according to known procedures except that the above-mentioned multi-layer preform is used. At first, the multi-layer preform is preliminarily heated at a drawing temperature before draw blowing. This drawing temperature is a temperature lower than the crystallization temperature of the polyester used, at which drawing of the multi-layer preform is possible. For example, in case of polyethylene terephthalate, the drawing temperature is 80.degree. to 130.degree. C., especially 90.degree. to 110.degree. C.
Draw-blow forming of the preliminarily heated preform is accomplished by known means such as sequential draw-blow forming or simultaneous draw-blow forming. For example, in case of sequential draw-blow forming, the preform is drawn in the axial direction by blowing a fluid under a relatively low pressure, and the preform is expanded and drawn in the circumferential direction of the vessel by blowing a fluid under a relatively high pressure. In case of simultaneous draw-blow forming, drawing in the circumferential direction and drawing in the axial direction are simultaneously performed while blowing a fluid under a high pressure. Drawing of the preform in the axial direction can easily be accomplished, for example, by gripping the neck of the preform between a mold and a mandrel, applying a drawing rod to the inner surface of the bottom of the preform and stretching the drawing rod. It is preferred that the draw ratio be 1.5 to 2.5 in the axial direction and 1.7 to 4.0 in the circumferential direction.
In the barrel of the draw-blow-formed vessel, the polyethylene terephthalate layer is molecularly oriented so that the density of the polyethylene terephthalate layer is in the range of 1.350 to 1.402 g/cm.sup.3, whereby good impact resistance, rigidity and transparency desirable for a bottle-shaped vessel are obtained, and because of the presence of the olefin-vinyl alcohol copolymer layer, an excellent barrier property to oxygen, nitrogen, carbon dioxide gas and fragrance can be obtained. Furthermore, an excellent interlaminar adhesion can be maintained by the presence of the interposed copolyester adhesive layer.
For the production of a sheet-formed vessel, the above-mentioned multi-layer film or sheet is preliminarily heated at the above-mentioned drawing temperature, and the heated film or sheet is formed into a cup by vacuum forming, air-pressure forming, plug-assist forming or press forming.
The present invention will now be described in detail with reference to the following Examples that by no means limit the scope of the invention.
EXAMPLE 1
Molar ratios of ingredients in adhesive compositions used in this Example are shown in Table 1. These adhesive compositions were prepared according to the following method.
A four-neck flask was charged with predetermined amounts of a phthalic acid ester such as dimethyl terephthalate (hereinafter referred to as "DMT") or dimethyl isophthalate (hereinafter referred to as "DMI"), a glycol such as ethylene glycol (hereinafter referred to as "EG") or 1,4-butane-diol (hereinafter referred to as "BD") and a catalyst, and ester exchange reaction was carried out with stirring. The reaction was started at 165.degree. C. and the temperature was elevated to 200.degree. C. at a rate of 0.5.degree. C. per minute. Within 85 minutes from the start of the reaction, methanol was distilled in an amount corresponding to 90% of the theoretical amount. Then, a predetermined amount of trimethyl phosphite (hereinafter referred to as "TMPA") was added to the reaction mixture at 200.degree. C. and the reaction was conducted for 35 minutes. Then, the temperature was elevated to 240.degree. C. over a period of 30 minutes to effect esterification. Then, the temperature was elevated to 265.degree. C. and polymerization was conducted under 0.1 mmHg for 4 to 6 hours.
The final composition of the obtained polymer was determined by the proton NMR analysis and gas chromatography. The determined composition is expressed by mole % in Table 1.
Twenty four kinds of the so-formed adhesive compositions (CAP-1 through CAP-24) were formed into films by a hot press and were rapidly cooled in water to form samples. These adhesive films were laminated with a biaxially drawn polyethylene terephthalate film (hereinafter referred to as "PET-F"), a biaxially drawn polybutylene terephthalate film (hereinafter referred to as "PBT-F"), a polycarbonate film (hereinafter referred to as "PC-F"), a polyarylate film (hereinafter referred to as "PAR-F") or a film of an ethylene-vinyl alcohol copolymer having a vinyl alcohol content of 56 mole %, an ethylene content of 43.6 mole % and a residual vinyl ester content of 0.4 mole % (hereinafter referred to as "PEVA-F") by using a hot press. Each of the films laminated with the adhesive films had a thickness of 200 microns. Formation of these laminated films was accomplished according to the method in which the above-mentioned 24 adhesive films were piled on PET-F, PBT-F, PC-F, PAR-F or PEVA-F, kept under no compression in a hot press maintained at 270.degree. C. for 120 seconds and then kept under a pressure of 5 kg/cm.sup.2 for 60 seconds.
Specimens having a width of 10 mm were sampled from the resulting laminated films, and the T-peel test was carried out at a tensile speed of 100 mm/min in a tensile tester. The obtained results are shown in Table 2.
TABLE 1__________________________________________________________________________Composition of AdhesivePhthalic Acid Ester Component (mole %) Glycol Component (mole %) dimethyl terephtha- dimethyl isophtha- 1,4-butane- ethylene glycolAdhesive late (DMT) late (DMI) diol (BD) (EG)__________________________________________________________________________CAP-1 100 0 100CAP-2 95 5 100CAP-3 90 10 100CAP-4 85 15 100CAP-5 80 20 100CAP-6 70 30 100CAP-7 60 40 100CAP-8 55 45 100CAP-9 50 50 100CAP-10 45 55 100CAP-11 40 60 100CAP-12 35 65 100CAP-13 100 0 100CAP-14 95 5 100CAP-15 90 10 100CAP-16 85 15 100CAP-17 80 20 100CAP-18 70 30 100CAP-19 60 40 100CAP-20 55 45 100CAP-21 50 50 100CAP-22 45 55 100CAP-23 40 60 100CAP-24 35 65 100__________________________________________________________________________
TABLE 2__________________________________________________________________________Adhesion Strength (g/10 mm width: T-peel) polyethylene polybutylene polycar- ethylene-vinyl terephthalate terephthalate bonate polyarylate alcohol copolymerAdhesive (PET-F) (PBT-F) (PC-F) (PAR-F) (PEVA-F)__________________________________________________________________________CAP-1 peeling peeling peeling 5100 78 impossible impossible impossibleCAP-2 peeling peeling peeling 5250 1060 impossible impossible impossibleCAP-3 4640 peeling 4670 5400 1450 impossibleCAP-4 4280 5960 3980 5600 1680CAP-5 3820 5630 3760 5760 1780CAP-6 3660 5310 3440 5800 1890CAP-7 3440 4850 2980 5840 1810CAP-8 3280 4640 2750 peeling 1750 impossibleCAP-9 2770 4430 2530 peeling 1540 impossibleCAP-10 2550 4220 2310 peeling 1290 impossibleCAP-11 2330 3750 1880 peeling 1090 impossibleCAP-12 2190 3510 1550 5980 920CAP-13 peeling peeling peeling 5000 63 impossible impossible impossibleCAP-14 peeling peeling peeling 5100 1000 impossible impossible impossibleCAP-15 peeling 4770 4610 5200 1220 impossibleCAP-16 5330 4580 4210 5300 1390CAP-17 4850 4340 3800 5400 1430CAP-18 4640 3910 3510 peeling 1490 impossibleCAP-19 4430 3720 3220 peeling 1320 impossibleCAP-20 4280 3550 2910 peeling 1290 impossibleCAP-21 3730 3380 2720 peeling 1110 impossibleCAP-22 3510 3190 2550 peeling 1040 impossibleCAP-23 3320 2900 2180 peeling 1010 impossibleCAP-24 3190 2710 1870 peeling 900 impossible__________________________________________________________________________
EXAMPLE 2
Adhesive resin compositions were prepared by melt-mixing the polyester type adhesive resins CAP-6 and CAP-16 used in Example 1 at weight ratios of 10/90, 20/80, 30/70, 40/60, 50/50, 60/40, 70/30, 80/20 and 90/10.
Nine adhesive films having a thickness of 80 to 100 microns were prepared from these adhesive resin compositions (referred to as "adhesives CAP-25 through CAP-33") in the same manner as described in Example 1. These nine adhesive films were laminated with PET-F, kept in a hot press maintained at 270.degree. C. under no compression for 120 seconds and then kept under a pressure of 5 kg/cm.sup.2. Specimens having a width of 10 mm were sampled from the so-obtained laminate films, and the T-peel test was carried out at a tensile speed of 100 mm/min in a tensile tester. Similarly, bonding strength values of the foregoing nine adhesives to PBT-F, PC-F, PAR-F and PEVA-F were measured. The obtained results are shown in Table 3.
TABLE 3______________________________________Adhesion Strength (g/10 mm width: T-peel)Adhesive PET-F PBT-F PC-F PAR-F PEVA-F______________________________________CAP-25 3980 3420 2100 2300 1620CAP-26 3810 3510 2170 2380 1660CAP-27 3620 3640 2220 2420 1696CAP-28 3410 3760 2360 2500 1700CAP-29 3200 3890 2240 2590 1730CAP-30 2790 4090 2180 2660 1890CAP-31 2560 4130 2120 2780 1890CAP-32 2420 4330 1990 3000 1780CAP-33 2330 4440 1700 3200 1720______________________________________
EXAMPLE 3
A polyethylene terephthalate resin (PET) having an intrinsic viscosity [.eta.] of 0.87 dl/g as measured at 30.degree. C. in a mixed solvent comprising phenol and tetrachloroethane at a weight ratio of 60/40 was used as the resin for innermost and outermost layers, an ethylene-vinyl alchol copolymer (PEVA) having a vinyl alcohol content of 56 mole %, a residual vinyl ester concentration of 0.5 mole % and a melting point of 162.degree. C. was used as the resin for the intermediate layer, and the adhesive CAP-33 used in Example 2 was used as the resin for the adhesive layer. A symmetric five-layer pipe having a structure of PET/CAP-33/PEVA/CAP-33/PET was prepared by melt extrusion using an extruding apparatus comprising an extruder for the innermost and outermost layers, which was provided with a full-flighted screw having a diameter of 65 mm and an effective length of 1430 mm, an extruder for the intermediate layer, which was provided with a full-flighted screw having a diameter of 38 mm and an effective length of 950 mm, an extruder for the adhesive layer, which was provided with a full-flighted screw having a diameter of 40 mm and an effective length of 1000 mm, a feed pipe and a three-resin five-layer die, and the pipe was preliminarily blow-formed in a split mold to obtain a bottomed preform having an inner diameter of 27.7 mm, a length of 138 mm and an average thickness of 3.5 mm. Incidentally, extrusion conditions were controlled so that the PET/CAP-33/PEVA weight ratio in the preform was 91/4/5.
The bottomed preform was heated by an infrared ray heater so that the highest temperature in the bottomed preform was 108.degree. C. and the lowest temperature in the bottomed preform was 98.degree. C., and the preform was draw-blow-formed according to the sequential biaxial draw-blow forming method so that the draw ratio in the axial direction was 2.0 and the draw ratio in the circumferential direction was 3.0, whereby a bottle (B-1) having an average thickness of 0.40 mm, an inner volume of 1040 cc and a weight of 36 g was obtained.
For comparison, a bottomed preform having the same dimensions as described above was prepared by using polyethylene terephthalate (PET) alone, and a biaxially draw-blow-formed bottle (B-2) having the same dimensions as described above was prepared in the same manner as described above.
With respect to each of the foregoing bottles, the transparency (haze), oxygen permeability and falling impact strength were determined, and occurrence of the interlaminar peeling phenomenon was checked at the falling test. The obtained results are shown in Table 4.
TABLE 4______________________________________ Oxygen Per- Falling meability** Impact Transparency (cc/m.sup.2 .multidot. day .multidot. Strength InterlaminarBottle (haze)* (%) atm) (N/10)*** Peeling****______________________________________B-1 4.1 1.5 0/10 0/20B-2 4.0 12 0/10 --______________________________________ Note *A square sample of 30 mm .times. 30 mm was cut out from the barrel of th bottle, and the haze was measured according to the method of JIS K6714. **According to the method for measuring the oxygen permeability of a bottle, disclosed in Japanese Patent Publication No. 48459/82, the oxygen permeability was measured at 37.degree. C. and under a relative humidity of 100% inside the bottle and a relative humidity of 20% outside the vessel. ***A bottle was filled with 1 Kg of a saline solution and was sealed by a aluminum cap. The bottle was stored in a low temperature store chamber maintained at 5.degree. C. for 1 day. The bottle was let to fall down on concrete surface from a height of 2 mm while the normal posture was maintained. The ratio of the number of broken bottles to the number of th total bottles tested is expressed by "N/10". ****A bottle filled and stored in the same manner as at the test for measuring the falling impact strength was similarly let to fall down whil the normal posture was maintained or the recumbent posture was maintained In case of the bottle B1, no interlaminar peeling was observed when 10 bottles were let to fall down in the normal posture and another 10 bottle were let to fall down in the recumbent posture.
EXAMPLE 4
The copolyester CAP-6 used in Example 1 was melt-mixed with maleic anhydride-modified polypropylene having a melting point of 160.degree. C., a density of 0.91 g/cm.sup.3, a melt index of 1.5 g/10 min (as determined at 210.degree. C. under a load of 2160 g) and a maleic anhydride content of 0.6% by weight at a weight ratio of 80/20 to form a resin mixture CAP-6-M.
The copolyester CAP-6 used in Example 1 was melt-mixed with polyethylene terephthalate having a melting point of 255.degree. C. and an intrinsic viscosity [.eta.] of 0.65 dl/g and a sodium salt-modified ionomer having a melt index of 0.9 g/10 min and a density of g/cm.sup.3 at a weight ratio of 10/80/10 to form a resin mixture of CAP-6-I.
The copolyester CAP-6 used in Example 1 was melt-mixed with an ethylene-vinyl acetate copolymer having a melting point of 96.degree. C., a density of 0.93 g/cm.sup.3 and a vinyl acetate conent of 11% by weight at a weight ratio of 80/20 to form a resin mixture CAP-6-P.
Three films were prepared from these three resin mixtures in the same manner as described in Example 1. Then, in the same manner as described in Example 1, these three films were laminated with PET-F, PBT-F, PC-F, PAR-F or PEVA-F. These laminated films were subjected to the peeling test in the same manner as described in Example 1. The obtained results are shown in Table 5.
TABLE 5______________________________________Adhesion Strength (g/10 mm width: T-peel)Adhesive PET-F PBT-F PC-F PAR-F PEVA-F______________________________________CAP-6-M 1110 1130 1120 1130 980CAP-6-I 1280 1260 1240 1200 1100CAP-6-P 1130 1140 1150 1100 1060______________________________________
EXAMPLES 5 and 6
[Synthesis of Copolyester Adhesive and Formation of Sheet]
Copolyester adhesives used in these Examples were prepared by polycondensation according to the method described below, and they were formed into film samples. A glass reaction vessel was charged with predetermined amounts of corresponding acid and glycol components and about 0.04% by weight of a catalyst such as tetra-n-butyl titanate, and the mixture was heated at 200.degree. C. with stirring and ester exchange reaction was continued for about 100 minutes while removing formed methanol. Then, the temperature was elevated to about 260.degree. C. and polymerization was carried out under a reduced pressure of 0.1 to 0.5 mmHg for about 2 hours. The obtained copolyester was inserted between two Teflon sheets and formed into a filmy sheet having a thickness of about 200 to about 300 microns in a hot press at a temperature higher by 20.degree. to 30.degree. C. than the melting or softening point of the resin. The final composition of each sample was confirmed by the proton NMR analysis and gas chromatography. The obtained analysis results are shown in Tables 6 and 7. The glass transition temperature (Tg) of each sample was measured by using a thermal mechanical analysis apparatus (TMA) supplied by Rigaku Denki at a temperature-elevating rate of 10.degree. C./min according to the customary penetration method. The obtained results are shown in Tables 6 and 7.
[Preparation of Test Piece for Adhesion Test]
As the creep-resistant resin to be bonded, there were used polyethylene terephthalate (PET) having a softening point of 265.degree. C. and a glass transition temperature (Tg) of 80.degree. C., polybutylene terephthalate (PBT) having a softening point of 225.degree. C. and a glass transition temperature (Tg) of 37.degree. C., polycarbonate (PC) having a softening point of 155.degree. C., and an ethylenevinyl alcohol copolymer (PEVA) having a vinyl alcohol content of 69 mole %, a residual vinyl ester concentration of 0.4 mole %, a softening point of 182.degree. C. and a glass transition temperature (Tg) of 72.degree. C. Each of these creep-resistant resins was used in the form of a sheet having a thickness of 1.5 mm, which was formed by extrusion.
The above-mentioned copolyester adhesive sheet was inserted between two sheets of the creep-resistant resin, and the assembly was kept in a hot press maintained at a temperature higher by 20.degree. C. than the softening point of the creep-resistant resin under application of no pressure for 120 seconds and was compressed under 5 kg/cm.sup.2 for 60 seconds. Thus, laminate structures shown in Tables 6 and 7 were obtained.
Some of these laminates were monoaxially drawn at a draw ratio of 2 by a bench-scale biaxially drawing apparatus (Bistron BT-1 supplied by Iwamoto Seisakusho). The drawing temperature was 105.degree. C. (PET), 85.degree. C. (PBT), 170.degree. C. (PC) or 130.degree. C. (PEVA).
[Evaluation of Adhesion Strength]
Test pieces having a length of 100 mm and a width of 10 mm were taken out from laminated sheets just after bonding and also from drawn laminated sheets. In case of the drawn laminated sheets, the test pieces were taken out so that the longitudinal direction of the test piece was in agreement with the drawing direction. The adhesion strength was determined at room temperature at a tensile speed of 100 mm/min by the T-peel test using a tensile tester. The T-peel test was similarly carried out after the test pieces had been stored in an atmosphere of a temperature of 37.degree. C. and a relative humidity (R.H.) of 97%. The test was conducted 5 times under the above conditions and the average peel strength was evaluated based on the arithmetic mean value at each measurement. The obtained results are shown in Tables 6 and 7.
TABLE 6-1__________________________________________________________________________ Composition and Properties of Adhesive Acid Components (mole %) C.sub.4 -C.sub.12 linear or cyclic Glycol ComponentAdhe- aromatic dibasic acids aliphatic Other (mole %) Tgsive I T other dibasic acids acids BD other (.degree.C.)__________________________________________________________________________Run 1 C1 5 20 A(60) DA(15) 80 HG(20) -35Run 2 C2 15 15 TP(60) DA(10) 90 PG(10) -26Run 3 C3 40 A(30), SE(30) 100 -25Run 4 C4 40 10 A(40), SE(10) 100 -12Run 5 C5 50 20 0(10) SE(20) 80 NG(20) 5Run 6 C6 60 A(40) 100 0Run 7 C7 60 20 SE(20) 100 3Run 8 C8 70 10 Az(20) 95 EG(5) 12Run 9 C9 90 SE(10) 80 PG(20) 29Run 10 C10 30 50 Az(10) DA(10) 100 32Run 11 C11 90 5 SE(5) 100 37Compar- CE1 A(100) 60 PG(40) -30tiveRun 1Compara- CE2 100 EG(100) 80tiveRun 2Run 12 C12 40 50 A(10) 80 EG(20) 41__________________________________________________________________________
TABLE 6-2__________________________________________________________________________ Undrawn Samples after 1 month's storage at 37.degree. C. just after bonding and 97% RH PET PBT PC PEVA PET PBT PC PEVA__________________________________________________________________________Run 1 2200 2300 2000 1800 1700 1400 1800 1200Run 2 2600 2700 2400 2200 2300 2200 2000 1600Run 3 3400 3700 2900 2600 3200 3300 2500 2200Run 4 3500 3500 3200 2700 3300 3400 2900 2300Run 5 3700 3900 2700 2300 3400 3700 2400 2100Run 6 3100 3200 2400 2400 2800 3000 2300 2000Run 7 3400 3600 2800 2500 3200 3500 2700 2400Run 8 3200 3500 2600 2300 2600 3300 2400 2000Run 9 3400 3600 2400 2000 3200 3000 2000 1800Run 10 3600 3800 2700 2100 3400 3500 2400 1900Run 11 3300 3500 2600 1800 2700 3200 1800 1600Comparative 1300 1600 1300 1000 1000 1400 900 600Run 1Comparative * * * 63 * * * 35Run 2Run 12 3200 3400 2400 1700 2800 3100 1700 1100__________________________________________________________________________ *peeling impossible
TABLE 6-3__________________________________________________________________________ Samples Drawn at Draw Ratio of 2 after 1 month's storage at 37.degree. C. just after drawing and 97% RH PET PBT PC PEVA PET PBT PC PEVA__________________________________________________________________________Run 1 1900 1700 1700 1300 1400 1300 1200 1000Run 2 2400 2300 2300 2000 2000 1900 1700 1400Run 3 3500 3800 2600 2400 3000 3100 2100 2100Run 4 3200 3600 3000 2500 2900 3200 2400 2200Run 5 3600 4100 2400 2000 3300 3400 2000 1800Run 6 2900 3400 2600 2200 2700 3200 2100 1700Run 7 3500 3700 2800 2400 3300 3600 2400 2200Run 8 3100 3400 2500 2200 2300 2800 1900 1800Run 9 2100 2300 2100 1600 1900 1700 1400 1300Run 10 2400 2600 2200 1800 2200 2300 1800 1300Run 11 1700 2200 1600 1600 1500 2000 1300 1100Comparative 400 800 700 800 200 500 600 300Run 1Comparative 4500 4000 3900 30 4100 3800 3600 15Run 2Run 12 1600 2000 1500 1500 1300 1800 1100 800__________________________________________________________________________
TABLE 7-1__________________________________________________________________________ Composition and Properties of Adhesive Acid Components (mole %) C.sub.4 -C.sub.12 linear or cyclic Glycol ComponentAdhe- aromatic dibasic acids aliphatic Other (mole %) Tgsive I T other dibasic acids acids BD other (.degree.C.)__________________________________________________________________________Run 13 C13 60 20 SA(20) 100 34Run 14 C14 50 GA(50) 70 EG(30) 18Run 15 C15 25 10 A(65) 80 PG(20) -2Run 16 C16 30 DPA(40) Az(30) 100 15Run 17 C17 30 30 DDA(10) DA(30) 60 HG(40) -39Run 18 C18 60 20 MA(20) 100 38Run 19 C19 60 20 DA(20) 100 -1Compara- CE3 20 SE(80) 100 -46tiveRun 3Compara- CE4 5 A(80) DA(15) 100 -43tiveRun 4__________________________________________________________________________
TABLE 7-2__________________________________________________________________________ Undrawn Samples after 1 month's storage at 37.degree. C. just after bonding and 97% RH PET PBT PC PEVA PET PBT PC PEVA__________________________________________________________________________Run 13 3500 3600 2800 2600 3300 3400 2500 2300Run 14 3700 3800 3200 2300 3500 3400 3000 2000Run 15 2700 3200 2600 2400 2600 3000 2300 2100Run 16 3000 2900 3600 2500 2800 2700 3300 1800Run 17 3500 3300 2400 1800 2200 2000 2000 1000Run 18 2800 3300 2700 2100 1400 2000 1500 1200Run 19 2700 3200 2600 1500 2400 2600 2000 1200Comparative 2300 2500 1800 1500 800 1000 1000 800Run 3Comparative 600 1000 700 900 400 700 300 400Run 4__________________________________________________________________________
TABLE 7-3__________________________________________________________________________ Samples Drawn at Draw Ratio of 2 after 1 month's storage at 37.degree. C. just after drawing and 97% RH PET PBT PC PEVA PET PBT PC PEVA__________________________________________________________________________Run 13 2700 2600 2300 2100 2400 2400 2000 1800Run 14 2600 3200 2900 2000 2400 2900 2200 1600Run 15 2400 2800 2300 2300 2200 2600 2100 2000Run 16 3300 3200 3300 2200 2600 2600 3200 1900Run 17 2800 2400 2200 1200 1900 1600 1800 900Run 18 2400 2700 2200 1800 1100 1600 1000 900Run 19 2400 2300 2100 1200 1800 2000 1700 1000Comparative 2100 1900 1600 1300 800 1100 800 500Run 3Comparative 800 900 800 800 300 600 200 300Run 4__________________________________________________________________________ Note The abbreviations used in Tables 6 and 7 stand for the following acid or glycol components. Acid Components T: terephthalic acid I: isophthalic acid O: orthophthalic acid DPA: diphenolic acid TP: tetrahydrophthalic acid MA: malonic acid A: adipic acid SE: sebacic acid SA: succinic acid AZ: azelaic acid DA: dimer acid GA: glutaric acid DDA: 1,10decane-dicarboxylic acid Glycol Components BD: 1,4butane-diol EG: ethylene glycol PG: propylene glycol NG: neopentyl glycol HG: hexahydroxylylene glycol
EXAMPLE 7
A polyethylene terephthalate resin (PET) having an intrinsic viscosity [.eta.] of 0.91 dl/g as measured at 30.degree. C. in a mixed solvent comprising phenol and tetrachloroethane at a weight ratio of 60/40 was used as the resin for innermost and outermost layers, an ethylenevinyl alcohol copolymer (PEVA) having a vinyl alcohol content of 69 mole %, a residual vinyl ester content of 0.6 mole % and a melting point of 182.degree. C. was used as the resin for the intermediate layer, and the copolyester adhesive C7 used in Example 5 was used as the resin for the adhesive layer. A symmetric five-layer pipe having a structure of PET/C7/PEVA/C7/PET was prepared by melt extrusion using an extruding apparatus comprising an extruder for the innermost and outermost layers, which was provided with a full-flighted screw having a diameter of 65 mm and an effective length of 1430 mm, an extruder for the intermediate layer, which was provided with a full-flighted screw having a diameter of 38 mm and an effective length of 950 mm, an extruder for the adhesive layer, which was constructed by remodeling a high-temperature type hot melt adhesive applicator provided with a gear pump, a feed pipe and a three-resin five-layer die, and the pipe was preliminarily blow-formed in a split mold to obtain a bottomed preform having an inner diameter of 27.7 mm, a length of 138 mm and an average thickness of 3.5 mm. Incidentally, extrusion conditions were controlled so that the PET/C7/PEVA weight ratio in the preform was 90/4/6.
The bottomed preform was heated by an infrared ray heater so that the highest temperature in the bottomed preform was 108.degree. C. and the lowest temperature in the bottomed preform was 98.degree. C., and the preform was draw-blow-formed according to the sequential biaxial draw-blow forming method so that the draw ratio in the axial direction was 2.0 and the draw ratio in the circumferential direction was 3.0, whereby a bottle (B-3) having an average thickness of 0.40 mm, an inner volume of 1040 cc and a weight of 36 g was obtained.
For comparison, a bottomed preform having the same dimensions as described above was prepared by using polyethylene terephthalate (PET) alone, and a biaxially draw-blow-formed bottle (B-4) having the same dimensions as described above was prepared in the same manner as described above.
With respect to each of the foregoing bottles, the transparency (haze), oxygen permeability and falling impact strength were determined, and occurrence of the interlaminar peeling was checked. Furthermore, with respect to the bottle B-3, the interlaminar peel strength between the PET and C7 layers in the barrel and the interlaminar peel strength between the PEVA and C7 layers in the barrel were measured. The obtained results are shown in Table 8.
When the bottle B-3 was filled with a synthetic carbonated drink and stored at room temperature for 6 months, it was found that the loss of the volume of the gas was very small and no interlaminar peeling was caused. Accordingly, it was confirmed that this bottle was practically satisfactory.
TABLE 8__________________________________________________________________________ Interlaminar Peel Falling Test Strength*****Transparency Oxygen Permeability** impact interlaminar (g/10 mm width)Bottle (haze)* (%) (cc/m.sup.2 .multidot. day .multidot. atm) strength*** peeling**** PET/C7 C7/PEVA__________________________________________________________________________B-3 4.1 1.0 0/10 0/20 >1,700 1,700B-4 4.0 12 0/10 -- -- --__________________________________________________________________________ Note *A square sample of 30 mm .times. 30 mm was taken out and the haze was measured according to the method of JIS K6714. **The oxygen permeability was measured according to the method described in Example 3 (Table 4). ***The impact strength was measured according to the method described in Example 3 (Table 4). ****The interlaminar peeling was checked according to the method describe in Example 3 (Table 4). *****A rectangular sample having a width of 10 mm and a length of 60 mm i the height direction of the bottle was taken out from the central portion of the barrel of the bottle, and the Tpeel test was carried out at room temperature at a tensile speed of 100 mm/min by using a tensile tester.
EXAMPLE 8
The same polyethylene terephthalate (PET) as used in Example 7 was used for the polyester layer, an ethylene-vinyl alcohol copolymer (PEVA) having a vinyl alcohol content of 69.0 mole %, a residual vinyl ester content of 0.6 mole % and a melting point of 182.degree. C. was used for the barrier layer, and the same copolyester adhesive (C7) as used in Example 7 was used for the adhesive layer. From these resins, a symmetric three-resin five-layer laminate sheet of a PET layer/C7 layer/PEVA layer/C7 layer/PET layer structure having a total thickness of 2.30 mm (PET/C7/PEVA thickness ratio=100/3/5) and a width of 400 mm was prepared by using an extruder for the polyester layer, which was provided with a screw having a diameter of 50 mm and an effective length of 1300 mm, an extruder for the adhesive layer, which was provided with a screw having a diameter of 30 mm and an effective length of 750 mm, an extruder for the barrier layer, which was provided with a screw having a diameter of 38 mm and an effective length of 950 mm, a three-resin five-layer feed block, a single manifold T-die and a five-roll sheet-forming device. The formed sheet was rapidly cooled so that crystallization was not caused in the PET layers. The density of the PET layers of the obtained sheet was lower than 1.340 g/cm.sup.3. Since the sheet could not be wound on a roll, the sheet was cut into a length of 1000 mm by a traveling cutter just after the forming operation.
The obtained sheet was heated at 100.degree. C. by an infrared ray heater and was formed into a cup having a flange width of 5 mm, an inner mouth diameter of 60 mm, an outer bottom diameter of 40 mm and a height of 80 mm by using a plug-assist vacuum-air pressure forming machine. The average thickness of the barrel of the obtained cup was 0.39 mm and the density was 1.36 to 1.366 g/cm.sup.3, and strong orientation of crystals was observed in the radial direction of the bottom. The bottom and barrel of the obtained cup were very excellent in the transparency, and no breakage of the ethylene-vinyl alcohol copolymer layer was observed. Rectangular samples having a width of 10 mm and a length of 30 mm were taken out from the barrel and bottom of the cup, and the interlaminar peel strength was measured between the PET and C7 layers and between the PEVA and C7 layers in the same manner as described in Example 7. The obtained results are shown in Table 9.
TABLE 9______________________________________ Interlaminar Peel Strength** (g/10 mm width, T-peel)Sample- PET layer/ adhesive layer/Collecting Peeling Direc- adhesive gas barrierPosition tion* layer*** layer****______________________________________barrel height direction 1,800 1,750 of cupbarrel circumferential 1,900 1,800 direction of cupbottom radial direction 2,200 1,950______________________________________ Note *The sample was taken out so that the direction of the long side of the sample was in agreement with the direction of the height of the cup, and by "height direction", it is meant that the peeling direction at the peeling test was in agreement with the abovementioned direction of the height of the cup. **The measurement was made on 10 samples and the mean value is shown. ***With respect to one sample vessel (cup), the interlaminar peel strengt between the PET layer and adhesive layer was measured on both the outer surface side and the inner surface side, and the mean value is shown. ****With respect to one sample vessel (cup), the interlaminar peel strength between the gas barrier layer and adhesive layer was measured on both the outer surface side and the inner surface side, and the mean valu is shown.

Number	Date	Country	Kind
58-18041	Feb 1983	JPX
58-213334	Nov 1983	JPX

Number	Name	Date
4281045	Sumi et al.	Jul 1981
4299934	Petke et al.	Nov 1981
4407897	Farrell et al.	Oct 1983
4415649	Munger et al.	Nov 1983
4430288	Bonis	Feb 1984

Plastic laminate structure and vessel

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