JP3303961B2 - Method for producing kneaded polyurethane elastomer and polyurethane molded member - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a polyester-based kneaded polyurethane, which has greatly improved hydrolysis resistance while maintaining the original strength of the polyurethane.

[0002]

2. Description of the Related Art Polyurethane elastomers are classified into a casting type, a kneading type, a thermoplastic type and the like according to a molding method. Among them, a cast type is generally used because of its excellent various properties. On the other hand, the kneading type has an advantage that general rubber processing equipment such as a roll and a press can be used.

Cast-type and thermoplastic-type polyurethanes are known as typical examples of segmented elastomers such as thermoplastic elastomers, and have both rubber elasticity, abrasion resistance and strength. is there.
Among such polyurethanes, particularly when properties such as strength and abrasion resistance are emphasized, ethylene glycol adipate or butylene glycol adipate, hexanediol adipate, a soft segment comprising a crystalline long-chain polyol such as caprolactone, It comprises a hard segment comprising a polyisocyanate and a short-chain polyol / polyamine, and the hard segment has a structure that inhibits crystallization of the soft segment. In other words, in the normal state, the ends of the soft segments are randomly fixed by the hard segments, so that the crystallization of the soft segments is inhibited to form an amorphous polymer chain, which shows rubber elasticity as a whole, but in an excessively deformed state. The randomly fixed soft segments exhibit oriented crystallinity. Accordingly, the polyurethane has a good abrasion resistance and strength because the crystalline state of the soft segment portion changes between the normal state and the excessively deformed state. As described above, it is possible to use a highly crystalline polyol for the cast type and the thermoplastic type polyurethane.

On the other hand, kneaded polyurethane is an elastomer having no hard segment of a cast-type or thermoplastic-type polyurethane. Therefore, if a highly crystalline polyol is used, crystallization will occur even at a low temperature or at room temperature. It will no longer show rubber elasticity. As described above, in the kneading type polyurethane design method, since a highly crystalline polyol cannot be used in a normal state, a polyol having reduced crystallinity by introducing a side chain or random polymerization is designed. A technique has been adopted. Therefore, the polyols which have been put into practical use up to now are polyester copolymers such as polyethylene propylene adipate and polyethylene butylene adipate, and polyethers such as tetrahydrofuran (THF) -alkyl glycidyl ether macopolymer and the like. Is a polyol having reduced crystallinity by disturbing the structural regularity.

[0005]

The kneaded polyurethanes are roughly classified into polyester polyurethanes and polyether polyurethanes. Generally, polyesters have low hydrolysis resistance and polyethers have a low hydrolysis resistance. There is a problem that heat aging resistance is poor. Here, the problem that the heat aging resistance of the ether type is inferior is rather an essential problem, but the hydrolysis resistance of the ester type can be relatively easily improved by lowering the concentration of the ester group. Can be. However, in the case of ester-based polyurethane, if a linear long-chain diol adipate such as 1,4-butylene adipate or 1,6-hexane adipate is used in order to reduce the concentration of the ester group, the crystallinity is increased and the kneading type is used. Polyurethane cannot be used particularly at low temperatures, and a practical polyurethane having a wide range of use cannot be obtained. Poly-ε-caprolactone is also commonly used as a raw material for the hydrolysis-resistant polyurethane in cast-type or thermoplastic-type polyurethane, but cannot be used in the kneading type due to its high crystallinity. It is also common practice to homopolymerize or copolymerize a long-chain diol having a side chain such as a methyl group in order to lower the ester group concentration and lower the crystallinity. For example, 3-methyl-1,5-
When pentanediol adipate is used alone or when a copolyester of hexanediol and neopentyl glycol is used, there is no problem of crystallization at a low temperature, and an elastomer having excellent hydrolysis resistance can be obtained. There is a problem that mechanical strength such as abrasion resistance inherent in polyurethane cannot be obtained. The same applies when a dibasic acid other than adipic acid is used. As described above, conventionally, in order to improve the problem of crystallization at a low temperature, a means of randomly disturbing the structural regularity of the polyol has been used, so that crystallization is inhibited even in an excessively deformed state. As a result, oriented crystallization hardly occurs, and the original mechanical strength of polyurethane cannot be obtained.

In view of such circumstances, the present invention provides a polyester kneaded polyurethane having excellent hydrolysis resistance, no problem of crystallization at low temperature, and excellent mechanical properties such as abrasion resistance. It is an object of the present invention to provide a method for producing a kneaded polyurethane from which a product can be obtained.

[0007]

The first aspect of the present invention relates to a kneaded polyurethane which can be kneaded in a general rubber processing facility without substantially having a hard segment.
In the method for producing an elastomer , a poly-ε-caprolactone diol represented by the following formula,
The average value of the caprolactone chain in the ε-caprolactone diol is adjusted to a predetermined number, and the poly-ε
A step of producing a poly-ε-caprolactone-based diol having a molecular weight distribution Mw / Mn of 1.0 to 1.5 of the caprolactone-based diol; and reacting the poly-ε-caprolactone-based diol with a diisocyanate to form a crystal. Producing polyurethane having limited elasticity and rubbery elasticity, and kneaded polyurethane
Is crosslinked and molded using a curing agent to form a polyurethane elastomer.
Kneaded polyurethane elastomer
It is in the manufacturing method .

[0008]

Embedded image

(Where [] indicates a caprolactone chain portion, m and n indicate the number of chains, and R ₁ is derived from the polymerization initiator R ₁ (OH) ₂ ). _Second embodiment of the present invention Is the molecular weight distribution Mw / Mn of the poly-ε-caprolactone diol in the first embodiment.
In the manufacturing method of the kneading-type polyurethane elastomer, characterized in that but is 1.0 to 1.3.

In a third aspect of the present invention, in the first or second aspect, the polymerization initiator R ₁ (OH) ₂ of the poly-ε-caprolactone diol is a linear glycol having 2 to 12 carbon atoms. Neopentyl glycol, 3-methyl-
Diols having a side chain having 12 or less carbon atoms, such as 1,5-pentanediol; and 3-allyloxy-1,2
-At least one selected from the group consisting of diols having an unsaturated group having 12 or less carbon atoms, such as propanediol, wherein the average value of the caprolactone chain is 3 to 6
Kneaded polyurethane elastomer characterized by the following range:
In the method of manufacturing the stoma .

A fourth embodiment of the present invention is the third embodiment, wherein the poly-ε-caprolactone diol polymerization initiator R ₁ (OH) ₂ is a straight-chain glycol having 2 to 12 carbon atoms and methyl A method for producing a kneaded polyurethane elastomer , characterized in that it is at least one selected from the group consisting of those not containing side chains such as groups.

According to a fifth aspect of the present invention, in the first or second aspect, the polymerization initiator R ₁ (OH) ₂ of the poly-ε-caprolactone diol is 1,4-bis (hydroxyethoxy) benzene Diols containing an aromatic ring such as para-xylene glycol, cyclohexanediol,
A method for producing a kneaded polyurethane elastomer , which is at least one selected from the group consisting of alicyclic diols such as cyclohexanedimethanol, wherein the average value of the caprolactone chain is 4 to 8.

According to a sixth aspect of the present invention, in any one of the first to fifth aspects, the polyol contains a chain extender in addition to the long-chain diol containing the poly-ε-caprolactone diol. Kneading polyurethane elastomer characterized by the following
In the method of manufacturing the stoma .

A seventh aspect of the present invention is the kneaded polyurethane elastomer according to any one of the first to sixth aspects, wherein the kneaded polyurethane has a glass transition temperature Tg of -20 ° C or lower. In the manufacturing method.

According to an eighth aspect of the present invention, in any one of the first to seventh aspects, the diisocyanate is 2,6-toluene diisocyanate (TDI), 4,4'-diphenylmethane diisocyanate (MDI), paraphenylene A method for producing a kneaded polyurethane elastomer , which is at least one selected from diisocyanate (PPDI), 1,5-naphthalenediisocyanate (NDI) and 3,3-dimethyldiphenyl-4,4'-diisocyanate (TODI). It is in.

In a ninth aspect of the present invention, in any one of the first to eighth aspects, the poly-ε-caprolactone diol is reacted under a reaction condition of 130 ° C. or less using a tin catalyst represented by the following formula. A method for producing a kneading type polyurethane elastomer characterized by being produced.

[0017]

Embedded image

(Where R ₂ is hydrogen, an alkyl group or an aryl group, X is a hydroxyl group, an alkoxide group or a halogen other than fluorine)

According to a tenth aspect of the present invention , any one of the first to ninth aspects is provided.
In some embodiments, wherein the curing agent, an organic peroxide, sulfur, in the manufacturing method of the kneading type <br/> polyurethane elastomer, characterized in that at least one selected from organic nitrogenous compounds and an isocyanate compound .

An eleventh aspect of the present invention is a method for producing the kneaded polyurethane elastomer according to any one of the first to tenth aspects.
A polyurethane molded member characterized by being manufactured by:

According to a twelfth aspect of the present invention , in the eleventh aspect, the curing agent is at least one selected from organic peroxides, sulfur, organic nitrogen-containing compounds, and isocyanate compounds. In polyurethane molded parts.

The production method of the present invention is completely different from the conventional production method, and by controlling the number of caprolactone chains and the molecular weight distribution thereof, a monomer which was conventionally too strong in crystallinity and cannot be used. Thus, it is possible to design a polyurethane chain using ε-caprolactone, which improves the degree of freedom of obtaining a polyurethane having desired characteristics. That is, by controlling the average number of caprolactone chains and the molecular weight distribution thereof, crystallization of the ε-caprolactone is inhibited by the influence of the binding unit that binds to the caprolactone chain. Here, the coupling unit is ε
-Those derived from the initiator of ring-opening addition of caprolactone and urethane binding units at both ends. Further, in order to use the polyurethane thus prepared alone as an elastomer, the polyurethane preferably has a glass transition temperature of −20 ° C. or lower. It is well known that substantial Tg can be reduced by adding a plasticizer or other components.

Further, by using the method of the present invention, ε-
By controlling the molecular structure of the crystalline oligomer composed of caprolactone monomer, the crystalline and amorphous properties of urethane are reversibly controlled, and crystallization is inhibited in a deformed state in a normal environment. Thus, it becomes possible to prepare a high-performance or high-performance elastomer that acts as a rubber-like elastic body and exhibits crystallinity in an excessively deformed state.

For example, regarding polyurethane,
A polyurethane using a polycaprolactone polyol having a narrow molecular weight distribution is disclosed in, for example, Japanese Patent Publication No. 63-39007. However, the present invention is to develop a polyurethane having an excellent elastic recovery force as compared with a conventional product. Further, polyols having a narrow molecular weight distribution are described in, for example, Japanese Patent Publication No. 3-562.
No. 51, Japanese Patent Application Laid-Open No. 7-292083, and Japanese Patent Application Laid-Open No. 63-196623 also disclose a novel polyol which has never existed before.

That is, conventionally, there is no knowledge that the crystallinity of a polyol can be controlled by controlling the molecular weight and molecular weight distribution of a polyol within an appropriate range and reacting the polyol with a diisocyanate.

According to the present invention, in the case of poly-ε-caprolactone-based polyol, when a molecule having a predetermined ε-caprolactone chain or more is contained, the entire part thereof is crystallized, and many molecules having a predetermined molecular weight or less are used. In this case, the glass transition temperature Tg is not lowered, and the desired rubber-like elasticity cannot be obtained.

The method of the present invention is different from the conventional method in which a compound having a side chain such as a methyl group is copolymerized in order to reduce the concentration of an ester group to lower the crystallinity.
There is no decrease in mechanical properties such as abrasion resistance. This is considered to be because crystallization can be performed more quickly during stretching.

That is, in the present invention, even if an initiator having no side chain such as a methyl group is used, the crystallinity of the crystalline monomer can be restricted and the hydrolysis resistance can be improved. In other words, when an initiator having no side chain is used, a polyester-based polyurethane having improved hydrolysis resistance and very excellent mechanical properties can be obtained, and an initiator having a side chain can be used. Even when used, the mechanical properties are lower than when an initiator having no side chain is used, but a kneaded polyurethane comprising a poly ε-caprolactone unit having excellent hydrolysis resistance can be obtained.

The kneaded polyurethane used in the present invention is:
It can be obtained by reacting a long-chain polyol with a diisocyanate.

Here, the polyol used in the present invention uses a poly-ε-caprolactone diol as a main component. Here, the poly-ε-caprolactone diol is obtained by ring-opening polymerization of ε-caprolactone in the presence of a polymerization initiator having active hydrogen, and can be represented by the above formula (I). In the present invention, the average value of the caprolactone chain (the average value of the following m and n) is within a predetermined range, and the molecular weight distribution Mw / Mn of the caprolactone chain portion is preferably 1.0 to 1.5, more preferably Is 1.0
A very limited one of ~ 1.3 is used.

As described above, the average of the caprolactone chain of the poly-ε-caprolactone diol used in the present invention is set to a predetermined range, for example, 3 to 6, because the kneading of the present invention comprising a caprolactone chain portion and a polyurethane bond is performed. In the normal state where no strong stress is applied to the type polyurethane, the caprolactone chain part originally having strong crystallinity becomes an amorphous state due to the isocyanate unit constituting the urethane bond and R ₁ in the above formula, and as a whole becomes non-crystalline. It shows elasticity while maintaining its crystalline state, but maintains the reversible state in which the caprolactone chain shows its original oriented crystallinity and contributes to strength in an unusual state where it breaks under tension and other forces. That's why.

Further, the molecular weight distribution Mw / Mn of the caprolactone chain portion is set to 1.0 to 1.5, preferably 1.0 to 1.5.
The value of 1.3 is intended to limit the amount of the caprolactone chain having a larger number outside the predetermined range. That is, although the caprolactone chain varies depending on R ₁ , for example, when it is larger than 6 or 8, it becomes easy to crystallize in a stressed state, particularly in a state stored at a low temperature, and when crystallization starts in this portion. This is because, for example, a portion having a caprolactone chain of, for example, 3 to 6 or 4 to 8 is easily crystallized. This low-temperature crystallization has a serious defect in the functions of the elastomer such as viscoelasticity and high friction coefficient, and has a drawback that the use environment and the storage environment are greatly restricted.

On the other hand, when the caprolactone chain is small, Tg becomes high, and good rubber-like elasticity cannot be exhibited as an elastomer. The range in which good rubber-like elasticity cannot be exhibited as described above differs depending on the type of R _{1 in} the above formula. When R ₁ is derived from, for example, an aliphatic diol, it is not preferable if the number of chains is 2 or less, When R ₁ is derived from, for example, a diol containing an aromatic ring or the like, the chain is preferably 3 or less. In addition, Tg as an elastomer
Can be adjusted by adding a plasticizer or the like, so that a low chain can be selected depending on the use.

Incidentally, for example, JP-A-2-628 discloses a lactone polymer having a narrow molecular weight distribution, suggesting that it is useful as a urethane raw material. However, such prior art aims at reducing the viscosity of the lactone polymer to improve its handleability, and does not suggest the technology of the present invention. Further, it is needless to say that the description that it is useful for a urethane raw material means that it is used as a raw material for a cast polyurethane or a thermoplastic polyurethane according to the prior art. Also, JP-A-63-19662
No. 3 discloses a method for producing a lactone having a narrow molecular weight distribution, but this also has the same purpose and does not suggest the technology of the present invention.

It is considered that a raw material having high crystallinity such as ε-caprolactone polymer can be used as a polyol raw material of a cast or thermoplastic polyurethane composed of a hard segment composed of an isocyanate and a chain extender and a polyol soft segment. However, as a polyol raw material of a kneaded polyurethane composed of a polyol linked by a diisocyanate, a highly crystalline material cannot be used, and only a polyol having reduced crystallinity by introducing a branched chain or a copolymer component is used. It has been considered usable. Therefore, for those skilled in the art, the idea of using a highly crystalline lactone polymer as a raw material of a kneaded polyurethane,
There is no means of realizing the practical level taking into account long-term use at low temperatures, and only a limited number of polyol materials for kneaded polyurethanes, such as ethylene propylene glycol adipate or ethylene butylene adipate, have been used. It was only a polyol.

The present invention completely breaks such conventional technical knowledge. As described above, in the present invention, by adjusting the number of caprolactone chain portions, poly-ε which is inherently high in crystallinity can be obtained. - crystallization of the chain members of the caprolactone-based polyols, to obtain a kneading-type polyurethane having a preventing and elastic under the influence of the R ₁ of isocyanate units and the equations forming the urethane bond.

In the present invention, the polymerization initiator which forms the poly-ε-caprolactone diol, ie, the compound which forms the above R ₁ , has an active hydrogen and forms a diol after ring-opening polymerization. Is not particularly limited,
Diols and diamines can be used. However,
In order to remarkably exert the effects of the present invention, it is preferable to use a polymerization initiator having no molecular weight distribution, that is, a short-chain initiator. Poly-ε-caprolactone diol formed using such a short-chain initiator, for example,
R ₁ can be defined as having a molecular weight of 500 or less. Alternatively, the molecular weight of the whole poly-ε-caprolactone diol can be defined as 800 to 1500.

Further, such an initiator affects the crystallinity of the caprolactone chain portion as described above. Therefore, when R ₁ is, for example, a linear hydrocarbon, it is necessary to control the average value of the above-mentioned caprolactone chain to 3 to 6, but R ₁ is, for example, a steric hindrance such as an aromatic ring or an aliphatic ring. In this case, the average value of the caprolactone chain may be controlled to 4 to 8 when the initiator has a large effect on the crystallinity of the caprolactone chain portion. That is,
In the present invention, the average value of the caprolactone chain is appropriately controlled to a predetermined value according to the type of the polymerization initiator.

Examples of the short-chain initiator that can be used in the present invention include straight-chain glycols having 2 to 12 main chain elements such as ethylene glycol, 1,3-propylene glycol, and 1,4-butylene glycol. Diols having a side chain having 12 or less carbon atoms such as neopentyl glycol and 3-methyl-1,5 pentanediol; having an unsaturated group having 12 or less carbon atoms such as 3-allyloxy-1,2-propanediol. Diols; and diols having 20 or less carbon atoms containing an aromatic ring such as 1,4-bis (hydroxyethoxy) benzene and para-xylene glycol; alicyclic diols such as cyclohexanediol and cyclohexanedimethanol; Can be mentioned.
Of course, these short-chain initiators may be used as a mixture of two or more.

In order to form the poly-ε-caprolactone diol used in the present invention, it is important to select a catalyst in addition to ε-caprolactone and a polymerization initiator. As the catalyst capable of restricting the molecular weight distribution narrowly, it is preferable to use a metal compound catalyst containing a halogen or an organic acid group, for example, chlorine, bromine, stannous halide such as iodine, or the above formula (II) The tin catalyst shown can be exemplified.

The poly-ε-caprolactone suitable for use in the present invention and having a narrow and restricted molecular weight distribution is, in particular, a tin catalyst represented by the above general formula (II), for example, monobutyltin oxide or tin halide except fluorine. Using,
It is preferably produced by polymerization under a low temperature condition of preferably 130 ° C. or less. When monobutyltin oxide or tin halide other than fluorine is used as described above, a monodispersed poly-ε-caprolactone having a molecular weight distribution of 1.0 to 1.3 can be obtained even at a temperature of 100 to 200 ° C. The crystallization is unlikely to occur with the progress of the reaction, and it can be carried out without a solvent. On the other hand, for example, the technology disclosed in Japanese Patent Application Laid-Open No. 63-196623 discloses a ring-opening polymerization of lactone at a temperature of 100 ° C. or less using an inorganic acid catalyst as a catalyst at a conventional reaction temperature of 100 to 200 ° C. By doing so, a very monodispersed lactone polymer having a molecular weight distribution Mw / Mn of 1.0 to 1.2 is obtained. In such bulk polymerization at a relatively low temperature, crystallization is likely to occur as the polymerization proceeds, and it is said that the reaction is preferably carried out in an inert organic solvent such as benzene or toluene. A step of removing the solvent from the reaction completed solution or a step of recovering the solvent is required, which may be a problem in industrialization.

In the present invention, as a main component of the polyol,
Although the above-mentioned specific poly-ε-caprolactone diol which is a long-chain polyol is used, other generally used long-chain polyols and chain extenders can be used as long as the object of the present invention is not impaired. As a generally used long-chain polyol, any of a polyester-based polyol and a polyether-based polyol may be used, or a blend or a partially modified one thereof may be used. As the chain extender, for example, ethylene glycol, thiodiethanol,
Linear glycols having 2 to 12 main chain elements such as propylene glycol and butylene glycol; diols having a side chain having 12 or less carbon atoms such as neopentyl glycol and 3-methyl-1,5-pentanediol; 3 12 carbon atoms such as allyloxy-1,2-propanediol
Diols having the following unsaturated groups; and 1,4-
Examples thereof include diols having an aromatic ring such as bis (hydroxyethoxy) benzene and para-xylene glycol having 20 or less carbon atoms and hydrogenated products thereof. Further, triols such as trimethylol, Stearyl alcohol, hydroxyethyl acrylate and the like can also be used.

When the polyurethane obtained by the method of the present invention is crosslinked with sulfur, a compound having an unsaturated bond is used as a part of an initiator or a chain extender according to a conventional method.

As the polyisocyanate for forming the polyurethane of the present invention by reacting with such a polyol, 2,6-toluene diisocyanate (TD
I), 4,4'-diphenylmethane diisocyanate (MDI), paraphenylene diisocyanate (PPD)
I), 1,5-naphthalenediisocyanate (ND
I) and 3,3-dimethyldiphenyl-4,4'-diisocyanate (TODI). In particular, 4,4'-diphenylmethane diisocyanate (MD
The use of a polyisocyanate containing I) is preferred because it is known to act as a crosslinking point for peroxide crosslinking.

The mixing ratio of the polyol and the diisocyanate may be a general ratio, for example, such that the active hydrogen such as the hydroxyl group of the diol and the isocyanate group are almost equimolar. For example, a hydroxyl value (OHv: KOH
mg / g) 112, 25 parts by weight of MDI per 100 parts by weight of diol, and OHv94, diol 1
20.8 parts by weight of MDI and OHv7
In the case of No. 5, MDI is added to 100 parts by weight of diol.
6.7 parts by weight.

The kneading type polyurethane of the present invention is kneaded with a curing agent and heat cured (crosslinked). Examples of such a curing agent include organic peroxides, sulfur, organic sulfur-containing compounds, and isocyanates for general synthetic rubber. Here, an organic peroxide is generally used, and examples of the organic peroxide include dicumyl peroxide and α, α′-bis (t-butylperoxyisopropyl) benzene. The compounding amount of the organic peroxide is 0.5 to 10 parts by weight, preferably about 1.5 to 5 parts by weight, based on 100 parts by weight of the total of the polyol and the isocyanate. Further, sulfur, the organic sulfur-containing compound can be used as a curing agent when the above-mentioned polymerization initiator or chain extender has an unsaturated bond, for example,
This is the case of 3-allyl-1,2-propanediol.
Here, examples of the organic sulfur-containing compound include thiuram-based vulcanization accelerators such as TMTD (tetramethylthiuram disulfide), TETD (tetraethylthiuram disulfide) and DPTT (dipentamethylenethiuram tetrasulfide), and 4,4′-dithiomorpholine. And the like.

When kneading and curing as described above,
Commonly used additives, namely, carbon black, reinforcing materials such as silica, anti-adhesives such as wax,
A plasticizer such as dioctyl phthalate (DOP) can be used.

In the polyurethane of the present invention, a hydrolysis inhibitor such as polycarbodiimide may be used in a usual amount of about 0.2 to 3% by weight based on 100 parts by weight of the polyurethane. Since the hydrolysis resistance of the polyurethane member of the present invention is about twice or more higher than that of the conventional thermosetting kneading type polyurethane, when the hydrolysis inhibitor is used as in the conventional case, the hydrolysis resistance is reduced by that much. Although the hydrolyzability is improved, the amount of addition can be reduced to about 20% to 50% in order to obtain the same level of hydrolyzability as before. Since hydrolysis inhibitors are generally expensive, they can greatly contribute to cost reduction.

The reaction conditions of the kneaded polyurethane are generally 70 ° C. to 150 ° C. for 30 minutes to 10 hours.
Thereafter, if necessary, aging is performed at 40 ° C. to 120 ° C. for about 6 to 48 hours. In addition, when using an organic peroxide as a curing agent, the thermosetting conditions are determined based on the decomposition characteristics of the organic peroxide to be used.
It is preferable to set the condition to 60 minutes.

[0050]

DESCRIPTION OF THE PREFERRED EMBODIMENTS Hereinafter, the present invention will be described in more detail with reference to embodiments.

(Production example 1 of poly-ε-caprolactone diol) Ethylene glycol as a polymerization initiator,
Various poly-ε-caprolactone diols were produced by using ε-caprolactone and parts by weight shown in Table 1 and reacting appropriately in the presence of SnCl ₂ or TBT as a catalyst.

Here, Examples 1-4 and Comparative Examples 1-3
Group (referred to as group A) has a molecular weight distribution of 1.
The molecular weight distribution of the group of Comparative Examples 4 to 10 (referred to as group B) is 2.2, which is 2.2, which is as narrow as about 4. Table 1 shows the amount of catalyst used and the reaction temperature, the designed and calculated values of the number of ε-caprolactone chains, the designed and measured average molecular weights, and the molecular weight distribution (Mw / Mn) for each reaction.

The average molecular weight is a value obtained by measuring the hydroxyl value of a polyol in accordance with JIS K1557, 6.4, and calculating from the following equation.

Molecular weight = 56.1 × N × 1000 / hydroxyl value N: Number of functional groups of initiator The molecular weight distribution was determined by gel permeation chromatography (GPC) under the following conditions.

[0055]

[0056]

[Table 1]

(Production Example 1 of Kneaded Polyurethane) Each poly-ε-caprolactone diol produced as described above was reacted with an equimolar amount of 4,4′-diphenylmethane diisocyanate (MDI) at 100 ° C. for 5 hours. Thus, various kneaded polyurethanes were obtained.

In order to determine the characteristics of these kneaded polyurethanes as amorphous polymer chains, the glass transition point Tg of each kneaded polyurethane and stability at low temperature storage were examined. Stability at low temperature storage is -15
Judgment was made from the flexibility at 5, 5 and 25 ° C.
Table 2 shows the results.

In both the group A having a narrow molecular weight distribution of the poly-ε-caprolactone polyol and the group B having a wide molecular weight distribution, the crystallinity increases as the number of average chains of ε-caprolactone increases. Was observed. Further, it has been clarified that the temperature range in which the amorphous state can be maintained is wider in Group A where the molecular weight distribution is narrower than in Group B.

[0060]

[Table 2]

(Production Example 1 of Crosslinked Polyurethane) A crosslinking agent dicumyl peroxide (manufactured by NOF Corporation; Parkmill D (trade name)) was added to 100 parts by weight of the kneaded polyurethane of each of the above Examples and Comparative Examples. After adding 1.5 parts by weight and kneading with an open roll,
Press molding was performed for minutes to obtain various crosslinked elastomers.

(Measurement of Physical Properties) Using the molded articles of the examples and comparative examples, the hardness (Hs:
JIS A scale), JIS K6255 (ISO4
662), rebound resilience (Rb:%), JI
According to SK6251 (according to ISO 37), tensile strength (Tb: MPa) and elongation (Eb:%), and J
According to IS K6252 (based on ISO34), the tear strength (Tr: N / m
m) was measured. The initial hardness was measured after a heat treatment at 60 ° C. for 30 minutes and a standing at 23 ° C. for 3 hours. Table 3 shows the results. Further, the hardness after being left at each temperature for 3 days was measured. The results are also shown in Table 3. further,
The temperature dependence of the rebound resilience at −20 ° C. to 60 ° C. was measured for Samples 3, 4, 9, and 10. The result is shown in FIG.

When a phenomenon (cold hardening) in which the hardness of each crosslinked elastomer was increased by crystallization from the hardness after being left at each temperature for 3 days was observed, it was preferably used for a conventional cast elastomer. It was found that those using poly-ε-caprolactone having a molecular weight of 1500 (average number of chains: 6) showed an increase in hardness even at room temperature. Further, even if the average number of chains is reduced to 3 or less, the crystallinity is not observed in the elastomer using the one having 3 or less, but the temperature dependence of the physical properties becomes large even at around normal temperature, causing a problem as the elastomer. On the other hand, it was found that when poly-ε-caprolactone having a narrow molecular weight distribution was used, an elastomer having a low temperature dependency was obtained while preventing an increase in hardness.

From these facts, it is considered that the increase in hardness due to crystallization depends on the number of chains of the lactone monomer. Conversely, if the number of chains increases more than a predetermined value, the crystallinity increases, and the elastomer as an amorphous polymer chain in the elastomer is increased. It is considered that a defect occurs. Further, when the average value of the chains is less than a predetermined number (for example, less than 3), the concentration of urethane groups in the amorphous polymer chain increases, so that the glass transition point becomes high, and a problem occurs in temperature dependency. Therefore, in order to obtain a practically low glass transition point (for example, −20 ° C. or less) as an elastomer while suppressing crystallization, it is useful to regulate the distribution of ε-caprolactone chains to a very high degree. Furthermore, based on the finding that it is the ε-caprolactone chain that is to be crystallized, fine adjustment of crystallinity, which has been difficult in the past, was achieved by selectively arranging molecules that regulate crystallization on both sides of the lactone chain. It is considered possible.

[0065]

[Table 3]

(Production Example 2 of Poly-ε-caprolactone-based diol) As shown in Table 5, ethylene glycol as a polymerization initiator and ε-caprolactone were used, and the catalyst and reaction temperature were changed to obtain various poly-ε-caprolactone diols. A -ε-caprolactone diol was produced.

Here, Examples 5 to 7 and Comparative Example 11,
Twelve groups C were obtained by changing the molecular weight distribution between 1.15 and 2.13 with the number of ε-caprolactone average chains being 6, and were obtained in Examples 8 to 10 and Comparative Examples 13 and 14.
In the group D, the molecular weight distribution was changed from 1.18 to 2.21 with the number of average chains of ε-caprolactone being 5.

Table 4 shows the amount of catalyst used and the reaction temperature, the designed and calculated values of the number of ε-caprolactone chains, the designed and measured average molecular weights, and the molecular weight distribution (Mw / Mn) of each reaction. Show.

[0069]

[Table 4]

(Production Example 2 of Kneaded Polyurethane) In the same manner as in Production Example 1 described above, each of the poly-ε-caprolactone diols and an equimolar amount of 4,4′-diphenylmethane diisocyanate (MDI) were added at 100 ° C. for 5 minutes. The reaction was carried out for each time to obtain various kneaded polyurethanes.

In order to determine the properties of these kneaded polyurethanes as amorphous polymer chains, the glass transition point Tg of each kneaded polyurethane and the stability in low-temperature storage were examined. Stability at low temperature storage is -15
Judgment was made from the flexibility at 5, 5 and 25 ° C.
Table 5 shows the results.

[0072]

[Table 5]

(Production Example 2 of Crosslinked Polyurethane) Using the kneaded polyurethanes of Production Example 2 described above, various crosslinked polyurethanes were obtained in the same manner as in Production Example 1. In addition, physical properties tests were similarly performed on each crosslinked polyurethane. Table 6 shows the results.

From the change in the hardness of the cross-linked polyurethane, the molecular weight distribution of the raw material poly-ε-caprolactone diol has a large effect on the increase in hardness (cold hardening) due to the low-temperature crystallization of the elastomer, and the polyol having an extremely narrow molecular weight distribution. It was found that kneading-type elastomers having adjusted low-temperature crystallinity can be provided by using.
In the present invention, the maximum effect can be obtained by using a polyol having a molecular weight distribution of 1.5 or less, preferably 1.3 or less, which is close to monodispersion, which shows a distribution of caprolactone chains. That is, since the average number of chains can be further increased under the condition that the crystallinity is controlled, it becomes possible to obtain a practical glass transition point as a rubber-like elastic body, and a high glass transition point which was conventionally considered to be incompatible can be obtained. It becomes possible to produce an amorphous elastomer composed of a crystalline unit using a general-purpose rubber facility. The practical glass transition point for the rubber-like elastic material here is
For example, it can be defined as −20 ° C. If the glass transition point is -20 ° C or higher, rubber elasticity at room temperature cannot be maintained in a low-temperature environment (0 ° C) that can occur normally.

[0075]

[Table 6]

(Production Example 3 of Poly-ε-caprolactone diol) As shown in Table 9, as a polymerization initiator, 1,
4-butanediol (1,4-BD), 1,5-pentanediol (1,5-PD), 1,6-hexanediol (1,6-HD), nonanediol (ND), neopentyl glycol ( NPG), 3-methyl-1,5-pentanediol (3MPG), cyclohexane dimethanol (CHDM), para-xylene glycol (PX
G), 1,4-bis (hydroxyethoxy) benzene (BHEB), and BPE-2 (Sanyo Chemical Industries, Ltd.)
Examples: Examples 11 to 53 were prepared by reacting ε-caprolactone under predetermined conditions with ethylene oxide added to both ends of bisphenol A in an amount of 1 mol at each end.
Of various poly-ε-caprolactone diols were produced. In addition, all the reactions were carried out under a nitrogen stream, and the solution was aged until the residual caprolactone monomer became 1% or less by gas chromatography.

Table 7 shows the amount of catalyst used and the reaction temperature of each reaction, the designed and calculated values of the number of ε-caprolactone chains, the designed and measured average molecular weights, and the molecular weight distribution (Mw / Mn). Show.

[0078]

[Table 7] In Table 7, MBTO is monobutyltin oxide,
TBT is tetrabutyl titanate.

(Production Example 3 of Kneaded Polyurethane) Similarly to Production Example 1 described above, each poly-ε-caprolactone diol and an equimolar amount of 4,4′-diphenylmethane diisocyanate (MDI) were added at 100 ° C. for 5 hours. Each was reacted to obtain various kneaded polyurethanes.

In order to determine the properties of these kneaded polyurethanes as amorphous polymer chains, the glass transition point Tg and relative crystallinity of each kneaded polyurethane were determined. Here, relative crystallinity refers to the amount of heat of fusion after holding at -10 ° C for 10 hours using a differential scanning calorimeter (DS).
C), which was expressed as weak (weak), medium (medium), and strong (strong) as compared with natural rubber. Table 8 shows the results. In addition, the measurement and analysis of DSC were performed with the following equipment.

[Measurement] Differential Scanning Calorimeter DSC620
0: Seiko Denshi Kogyo Co., Ltd. [Analysis] Thermal analysis, rheology system EXSTAR6
000: manufactured by Seiko Electronic Industry Co., Ltd. As a result, it was clarified that the crystallinity can be finely controlled by setting simple parameters such as the type of initiator and the average number of chains.

The crystallinity of the crosslinked elastomer can be adjusted to some extent by the crosslinked structure and additives. However, in order to use it at room temperature (20 ° C.), at least the relative crystallinity is at a high level by crystallization. Failures may occur and are difficult to use. Therefore, in a system using an aliphatic diol as an initiator, the average chain needs to be 6 or less. In other words, if the average chain is 7 or more, crystallization occurs even at room temperature, making it difficult to use as a polymer chain in the elastomer. When the initiator has a side chain of a methyl group, crystallinity is reduced, but strength is also significantly reduced. On the other hand, when a planar bulky substituent such as a benzene ring or a cyclohexane ring is introduced instead of a methyl group, the crystallinity is moderately moderated, and at the same time, an oriented crystallinity is exhibited at the time of extension to obtain a high-strength elastomer. When a cyclic structure is introduced as described above, the crystallinity is reduced, and the average number of lactone chains can be used up to about 8. However, since the glass transition point is also increased by the introduction of the cyclic structure, the average number of chains is desirably 4 or more in order to keep Tg at -20 ° C or less.

[0083]

[Table 8]

(Production Example 3 of Crosslinked Polyurethane) Examples 10, 13, 18, 23, 25, 28,
Using the kneaded polyurethanes of Nos. 33, 37, 42, 46 and 50, various crosslinked polyurethanes were obtained as described above. Regarding various crosslinked elastomers, JIS K625
Hardness (Hs: JIS A scale), JI
According to S K6255 (based on ISO4662), rebound resilience (Rb:%), JIS K6251 (ISO37)
Tensile strength (Tb: MPa) and elongation (Eb:%), and JIS K6252 (ISO3).
4), the tear strength (Tr: N / mm) was measured using a cut-in angle-free test piece. The initial hardness was measured after a heat treatment at 60 ° C. for 30 minutes and a standing at 23 ° C. for 3 hours. Table 9 shows the results.

[0085]

[Table 9]

(Comparison Test on Crystallinity) The crystallinity of Examples 3 and 4 of Group A having a narrow molecular weight distribution and Comparative Examples 7 and 8 of the group having a wide molecular weight distribution were compared as follows. 1. As measured by a differential scanning calorimeter (DSC),
Measurement of Crystallinity of Amorphous Polymer Chain Before Crosslinking FIG. 2 to FIG. 5 show the results of DSC measurement of the melting behavior of each sample after holding at −10 ° C. for a predetermined time. FIG. 6 shows the measurement results of natural rubber (NR) for comparison.

Comparative Example 7 of Group B having a wide molecular weight distribution
In Examples 8 and 8 , Examples 3 and 3 of Group A having a narrow molecular weight distribution were used.
It is observed that crystallization is faster than that of No. 4 . It is also recognized that crystallization of caprolactone having an average chain number of 5 is slower than that of 6 having caprolactone. From this, it became clear that fine adjustment of crystallinity can be achieved by setting the average number of chains by using an oligomer having a reduced molecular weight. 2. Comparison of Crystallinity of Crosslinked Elastomer Based on Wide Angle X-Ray Diffraction (WAXD) Measurement Results FIG. 7 to FIG. 10 show WAXD measurement results of each sample. The sample is 1mm thick and 3mm wide
And processed while varying the elongation. The measurement temperature is 22 ° C. The measurement of WAXD was performed by Liger Flex (manufactured by Rigaku Denki Co., Ltd.) and the output was 40k.
V, 27.5 mA.

In Comparative Examples 7 and 8 of Group B having a wide molecular weight distribution, a diffraction peak due to crystallization is observed even in a non-extended state. Since the peak at 2θ of about 21 ° observed here coincides with the peak position of poly-ε-caprolactone, it is presumed that the extension crystallization of the crosslinked elastomer is caused by crystals of the caprolactone chain.

On the other hand, Examples 3 and 4 of Group A having a narrow molecular weight distribution show an amorphous state in the unstretched and low-stretched regions, and it is presumed from the low glass transition temperature that they can be a rubber-like elastic material. When the elongation is further increased, crystallization is observed. This is a rubbery elastic body in the deformed state usually used as an elastomer,
This indicates that oriented crystallization occurs in an excessively deformed state such as wear or breakage. In addition, the degree of crystallinity can be finely adjusted by the average chain of caprolactone.

Comparative Examples 15 to 18 Ethylene glycol butanediol core dipate (EG: BG = 1: 1)
(Comparative Example 15), 3-methyl-1,5-pentanediol adipate (Comparative Example 16), neopentyl glycol adipate / caprolactone copolymer (NPG / AA:
CL = 1: 2) (Comparative Example 17). In addition, commercially available ester-based millable urethane (Sumipan 64
0S: Product name: Sumitomo Bayer Urethane Co., Ltd.)
And 8.

(Hydrolysis test)
11, 33, 38, 42 and Comparative Examples 13, 15 to 18
The hardness (JIS A) change when left standing in water at 85 ° C. was measured using each of the crosslinked elastomer molded products. The result is shown in FIG. For each crosslinked elastomer, the hardness (Hs:
JIS A scale), JIS K6255 (ISO4
662), rebound resilience (Rb:%), JI
According to SK6251 (according to ISO 37), tensile strength (Tb: MPa) and elongation (Eb:%), and J
70 according to IS K6262 (conforms to ISO815)
The permanent compression set (Cs:%) was measured at 22 ° C. for 22 hours. The results are shown in Table 10 together with the composition of the polyol, the properties of the polyol, and the glass transition point Tg of the kneaded polyurethane.

[0092]

[Table 10]

From these results, it can be seen that the molded products of the examples using the millable urethane of the present invention have extremely high hydrolysis resistance as compared with the molded products of Comparative Examples 15 and 18 using the conventional millable urethane. It turned out to be excellent. In Comparative Examples 16 and 17, the hydrolysis resistance was good because the crystallinity was reduced by introducing a side chain composed of a methyl group. Since it is difficult to show the properties, it is not possible to obtain the original high physical properties of polyurethane. However, it was found that the molded article of the example exhibited oriented crystallinity at the time of elongation, and high physical properties inherent to polyurethane were obtained.

[0094]

As described above, the polyurethane of the present invention is a kneaded polyurethane which can be produced by using a conventional general rubber processing equipment, and comprises a poly-ε-caprolactone diol as a main component and the poly-ε. The average value of the ε-caprolactone chain in the caprolactone-based diol is within a predetermined range, and the molecular weight distribution Mw / Mn of the poly-ε-caprolactone-based diol is 1.5 or less. Can also exhibit excellent mechanical strength without causing crystallization, and can significantly improve hydrolysis resistance.

[Brief description of the drawings]

FIG. 1 is a diagram showing the temperature dependence of rebound resilience.

FIG. 2 is a view showing a measurement result of a DSC of Example 3.

FIG. 3 is a view showing a DSC measurement result of Comparative Example 7.

FIG. 4 is a view showing a measurement result of a DSC of Example 4.

FIG. 5 is a view showing a measurement result of a DSC of Comparative Example 8.

FIG. 6 is a diagram showing the measurement results of DSC of natural rubber.

FIG. 7 is a view showing a measurement result of WAXD in Example 3.

FIG. 8 is a view showing a measurement result of WAXD of Comparative Example 7.

FIG. 9 is a diagram showing a measurement result of WAXD in Example 4.

FIG. 10 is a view showing a measurement result of WAXD of Comparative Example 8.

FIG. 11 is a view showing a test result of hydrolyzability.

──────────────────────────────────────────────────続 き Continuation of the front page (56) References JP-A-57-155230 (JP, A) JP-A-2-628 (JP, A) JP-A-63-196623 (JP, A) JP-A 9- 208656 (JP, A) UK Patent 2140436 (GB, B) (58) Fields investigated (Int. Cl. ⁷ , DB name) C08G 18/00-18/87 C08G 85/00

Claims (12)

(57) [Claims] 1. A method for producing a kneaded polyurethane elastomer which can be kneaded in a general rubber processing facility without substantially having a hard segment, comprising a poly-ε-caprolactone diol represented by the following formula: The average value of the caprolactone chain in the poly-ε-caprolactone diol is adjusted to a predetermined number, and the molecular weight distribution Mw of the poly-ε-caprolactone diol is adjusted.
/ Mn is from 1.0 to 1.5 to produce a poly-ε-caprolactone-based diol; and reacting the poly-ε-caprolactone-based diol with diisocyanate to limit crystallinity and rubber-like elasticity. a method for producing a polyurethane having, kneaded poly
Crosslinking and molding urethane using a curing agent to form polyurethane
Kneaded polyurethane characterized by being an elastomer
Elastomer manufacturing method. Embedded image (Here, [] indicates a caprolactone chain portion, and m
And n indicate the number of chains, and R ₁ is a polymerization initiator R ₁ (O
H) derived from ₂ ) 2. The poly-ε-caprolactone diol according to claim 1, wherein the molecular weight distribution Mw / Mn of the poly-ε-caprolactone diol is 1.0.
Kneading-type polyurethane d, which is a 1.3
The method of manufacturing the last . 3. The method according to claim 1, wherein the poly-
ε-caprolactone diol polymerization initiator R ₁ (O
H) ₂ is a linear glycol having 2 to 12 carbon atoms; diols having a side chain having 12 or less carbon atoms such as neopentyl glycol and 3-methyl-1,5-pentanediol;
And at least one selected from the group consisting of diols having an unsaturated group having 12 or less carbon atoms, such as 3-allyloxy-1,2-propanediol, wherein the average value of the caprolactone chain is in the range of 3 to 6. A method for producing a kneaded polyurethane elastomer , characterized in that: 4. The poly-ε-caprolactone diol polymerization initiator R ₁ (OH) _{2 according} to claim 3, wherein the poly-ε-caprolactone diol polymerization initiator R ₁ (OH) ₂ is a straight-chain glycol having 2 to 12 carbon atoms and does not contain a side chain such as a methyl group. Kneaded polyurethane elastomer characterized by at least one selected from the group consisting of:
Production method between. 5. The method according to claim 1, wherein the poly-
ε-caprolactone diol polymerization initiator R ₁ (O
H) ₂ is at least selected from the group consisting of diols containing an aromatic ring such as 1,4-bis (hydroxyethoxy) benzene and para-xylene glycol; and alicyclic diols such as cyclohexanediol and cyclohexanedimethanol. A method for producing a kneaded polyurethane elastomer , wherein the average value of the caprolactone chain is 4 to 8. 6. The kneaded polyurethane elastomer according to claim 1, wherein the polyol contains a chain extender in addition to the long-chain diol containing the poly-ε-caprolactone-based diol. Manufacturing method. 7. The kneaded polyurethane elastomer according to claim 1, wherein the kneaded polyurethane has a glass transition temperature Tg of -20 ° C. or lower.
Production method between. 8. The diisocyanate according to claim 1, wherein the diisocyanate is 2,6-toluene diisocyanate (TDI), 4,4′-diphenylmethane diisocyanate (MDI), paraphenylene diisocyanate (PDI).
PDI), 1,5-naphthalenediisocyanate (ND
A method for producing a kneaded polyurethane elastomer, which is at least one selected from I) and 3,3-dimethyldiphenyl-4,4'-diisocyanate (TODI). 9. The kneading method according to claim 1, wherein the poly-ε-caprolactone diol is produced under a reaction condition of 130 ° C. or less using a tin catalyst represented by the following formula. manufacturing method of the type polyurethane elastomer. Embedded image (Where R ₂ represents hydrogen, an alkyl group or an aryl group, X represents a hydroxyl group, an alkoxide group or a halogen other than fluorine) 10. The kneaded polyurethane according to claim 1 , wherein the curing agent is at least one selected from organic peroxides, sulfur, organic nitrogen-containing compounds, and isocyanate compounds. Elastomer manufacturing method. 11. A kneaded polyurethane elastomer produced by the method according to claim 1.
Polyurethane molded member, characterized in that that. 12. The method according to claim 11 , wherein the curing agent is
A molded polyurethane member, which is at least one selected from organic peroxides, sulfur, organic nitrogen-containing compounds and isocyanate compounds.