JPS6126656A - Molten blend of non-thermotropic and thermotropic fully aromatic polyester - Google Patents

Abstract

(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.

Description

DETAILED DESCRIPTION OF THE INVENTION Field of the Invention This invention relates to melt blends of melt processable thermotropic and non-thermodropink wholly aromatic polyesters. The properties and properties of such blends are significantly different from those expected when considering the properties of conventional mixtures and many polymer blends.

BACKGROUND OF THE INVENTION With some known exceptions, mixtures of polymeric materials are generally immiscible. That is, in the mixture, the polymeric materials constitute domains of chemically heterogeneous phases. Generally, one component forms a continuous phase;
The other component is almost spherical as an inclusion (aspect card is 3)
(less than) form a domain. In some cases, a bicontinuous structure in which both phases are continuous may be obtained. Mixing two arbitrarily chosen polymers usually results in degraded material that has no utility.

This is because the absence of adhesion between these two phases simply results in weakening of the continuous phase due to the dispersed phase. However, many useful blends are known that are favorable from the standpoint of morphology and phase interactions.

Some polymeric materials, such as polyalkylene terephthalates and most wholly aromatic polyesters, exhibit ordered structures in at least some regions of the polymer. This regular arrangement (order) may exist in one dimension, two dimensions, or three dimensions.

British Patent Publication No. 2,008,598 and U.S. Pat. No. 4,228,218 disclose that the composition of the present invention comprises not more than 20% by weight of a first rigid polymeric material and the balance, based on the total weight of the polymeric material, of a second polymeric material. , wherein the second polymeric material consists essentially of flexible molecular chains. This first polymeric material is dispersed in the second polymeric material forming regions with microscopic dimensions of 1 μm or less. The corresponding application publication number of this patent application in other countries is JP-A-54-065747,
France 2407956 and West Germany 2847782.

Blends of various thermotropic wholly aromatic polyesters are disclosed in commonly assigned U.S. Pat. No. 4,267.28.
It is disclosed in No. 9 and is publicly known. Blends of thermotropic fully aromatic polyesters and polyarylene sulfides are known as disclosed in US Pat. No. 4,267.397.

(Problems to be Solved by the Invention) It is an object of the present invention to provide a thermotropic total It is an object of the present invention to provide a blend of an aromatic polyester and a non-thermotropic wholly aromatic polyester.

Another object of the present invention is to provide a blend of thermotropic and non-thermotropic wholly aromatic polyesters that is significantly easier to process due to the viscosity-lowering effect of the thermotropic pink component.

Another object of the present invention is to provide thermotropic and non-thermotropic whole aromatic fragrances which are less expensive than the relatively expensive ingredients alone and which do not exhibit significant deterioration in mechanical properties due to the combination of relatively inexpensive ingredients. It is an object of the present invention to provide blends of family polyesters.

The above and other objects of the present invention, and its scope;
The nature and usefulness will become apparent from the detailed description below.

(Means for Solving the Problems) The present invention enables the ability to exhibit a melt phase containing both isotropic and anisotropic regions, and to form excipients with irregular mechanical properties. A polymer melt blend is provided having. This melt blend is approximately 2
a melt processable wholly aromatic polyester that is incapable of forming an anisotropic melt phase alone in an amount of 0 to 75% by weight, and (b): component (about 2% based on the combined weight of al and (b));
5 to 80% by weight of the anisotropic melt phase, substantially within the melt blend with an aspect ratio of at least about 3 and a volume of at least about 1! ! 3
It consists of a melt-processable wholly aromatic polyester present in the form of elongated domains.

The present invention also provides excipients formed from the blends described above.

DETAILED DESCRIPTION OF THE INVENTION The present invention, as described above, relates to melt blends of melt-addable thermotropic wholly aromatic polyesters and non-thermotropic wholly aromatic polyesters.

It has been unexpectedly found that the blends of the present invention exhibit unique self-strengthening properties due to the inherent domain-forming nature of the thermodropink fully aromatic polyester used.

Such self-reinforcing properties eliminate the need for reinforcing fibers during blend formation.

The first component of the melt blend of the present invention is a non-thermodropink wholly aromatic polyester. The non-thermodropink wholly aromatic polyesters are incapable of forming an anisotropic melt phase by themselves.

This non-thermodropink wholly aromatic polyester is considered to be "wholly" aromatic in that all repeating components present in the polymer contribute at least one aromatic ring to the polymer backbone. . Such repeating components may be derived from aromatic diols, aromatic dicarboxylic acids and aromatic hydroxy acids. Examples of non-thermotropic wholly aromatic polyesters that may be used in the present invention include, but are not limited to, copolymers of bisphenol A and isophthalic or terephthalic acid or mixtures thereof. Such copolymers are described in U.S. Pat. Nos. 3,684,766 and 3,728. As can be seen from the disclosure in the former No. 6, this is well known in the technical field. Bisphenol A is generally present in such copolymers in an amount of about 50 mole percent, and the isophthalic acid or terephthalic acid component is also present in an amount of about 50 mole percent. When using a mixture of isophthalic acid and terephthalic acid, each of these components is
Each is generally present in an amount ranging from about 25 to 75 mole percent, based on the total amount of both components.

The second component of the melt blend of the present invention is a thermodropink fully aromatic polyester. Such polyesters are also well known to those skilled in the art. A thermodropink liquid crystal polymer is a polymer that is liquid crystalline (ie, anisotropic) in the melt phase.

Polymers of this type are known as "liquid crystalline", "liquid crystal-1", "mesomorphic J" and "
It has been described by various terms, including "anisotropy". Briefly, polymers of this type are thought to contain regular parallel arrays of molecular chains. The state in which the molecules are arranged in this manner is often called the liquid crystal state or the nematic phase of liquid crystal materials. Such polymers are generally elongated, flat, fairly rigid along the long axis of the molecule, and are usually formed from a series of extended bonds having a plurality of chains in either coaxial or parallel relationships.

Such polymers readily form liquid crystals (ie exhibit anisotropy) in the molten phase. Such properties can be confirmed by conventional polarization techniques using orthogonal polarizers. More specifically, confirmation of the anisotropic melt phase is based on Leitz
This can be carried out by observing a sample placed on a Leitz hot stage under a nitrogen atmosphere at a magnification of 40 times using a polarizing microscope.

The polymer used in the present invention is optically anisotropic.

That is, it transmits light when examined between orthogonal polarizers. Even if the sample is at rest, if it is optically anisotropic, it will transmit polarized light.

As in the case of the first component, the thermotropic wholly aromatic polyester used in the present invention is such that all of its repeating components contribute at least one aromatic ring to the polymer backbone and the polymer is in the melt phase. It is considered to be fully aromatic in the sense that it is a component that allows it to exhibit anisotropy. Such components may be derived from aromatic diols, aromatic dicarboxylic acids and aromatic hydroxy acids. Components that may be present in thermotropic liquid crystal polymers suitable for use in the present invention include, but are not limited to: The aromatic ring contained in the polymer main chain may have at least a portion of the hydrogen atoms bonded to the aromatic ring substituted.

Substituents on such aromatic rings include alkyl groups having up to 4 carbon atoms, alkoxy groups having up to 4 carbon atoms, halogen, and other aromatic rings such as phenyl and substituted phenyl. Preferred halogens include fluorine, chlorine and bromine.

Thermodropink liquid crystalline polymers suitable for use in the present invention are those in which, when forming a blend of the present invention, the polymer is substantially (e.g., at least 50% by volume of the polymer) of the present invention. It must be possible to form the necessary domain so that it exists in the form of a domain as defined in . The presence of domains can be confirmed by scanning electron micrographs of fractured surfaces of molded or extruded articles made from blends of the invention or of the fragments remaining after removal of the non-thermotropic polymeric material with a suitable solvent.

Thermodropink fully aromatic polyester is a material well known to those skilled in the art. Recent publications disclosing such polyesters include:

(a) Helgie Patent Nos. 828,935 and 828.9
No. 36, (bl Dutch Patent No. 7,505,551,
(C) West German Patent No. 2,520.819; 2,520,
820. and No. 2,722,120, (d) Tokuko Sho 5
0-43223.52-132116.53-0176
92, and 53-021293, fe) U.S. Patent Nos. 3,991,013; 3,991,014; 4.0
57,597; 4,066.620.4,075,2
62; 4,118.372; 4,146,702;
4,153,779; 4,156,070; 4.
L59,365; 4,169,933; 4,1B1
,792; 4,1B8,476; 4,201,85
6; 4,226,970; 4,232,143;
4,232,144; 4,238,600; 4,2
45,082. and (f) British Patent Application Publication Box 2,002,404.

Thermotropic wholly aromatic polyesters are also disclosed in the following commonly assigned U.S. patents: No. 4,0
67.852; 4,083,829; 4,130,
545; 4,161.470; 4,184,996
．． 4,219,461.4,224,433; 4,2
38.598; 4,238,599; 4,256,6
24; 4,279,803; 4.299.756;
Nos. 4,330,557 and 4,337.191. The fully aromatic polyesters disclosed therein are generally capable of forming an anisotropic melt phase at temperatures below about 400°C, preferably below about 350°C.

Thermotropic fully aromatic polyesters suitable for use in the present invention can be produced by reacting organic monomer compounds bearing functional groups that form the necessary repeating units by condensation by a variety of ester-forming techniques. Can be implemented. For example, the functional groups of these organic monomer compounds may be carboxylic acid groups, hydroxyl groups, ester groups, acyloxy groups, acid halides, and the like. The above organic monomer compounds can be reacted without the presence of a heat exchange fluid by the melt acidolysis method.

In this method, the monomers are first heated together;
A molten liquid of the reactants is produced, and as the reaction continues, the produced polymer particles become suspended in the liquid.

Vacuum may be applied at the final stage of the condensation to facilitate removal of by-product volatiles (eg acetic acid or water).

US Pat. No. 4,083,829 describes a slurry polymerization process that can also be employed to produce wholly aromatic polymers suitable for use in the present invention.

According to this method, a solid product is obtained in suspension in a heat exchange medium.

Melt acidolysis method or U.S. Pat. No. 4,083,82
Regardless of which slurry polymerization method No. 9 is adopted, the organic monomer reactant for deriving the fully aromatic polyester used in the present invention is in a modified form in which the normal hydroxyl groups of this monomer are esterified (i.e., lower (as an acyl ester) may be subjected to the reaction. The lower acyl group preferably has about 2 to 4 carbon atoms. Preferably, the acetate ester of the organic monomer reactant is subjected to the reaction.

Melt acidolysis method or U.S. Pat. No. 4,083,82
Typical catalysts that can optionally be used in any of the No. 9 slurry polymerization methods include dialkyltin oxides (e.g., dibutyltin oxide), diaryltin oxides, titanium dioxide, antimony trioxide, alkoxytitanium silicates, titanium alkoxides, and carvone. Gaseous acid catalysts such as alkali and alkaline earth metal salts of acids (eg, zinc acetate), Lewis acids (eg, BF3), hydrogen halides (eg, HC#), and the like. Generally, the amount of catalyst used is about 0.001 to 1% by weight, most usually about 0.01 to 0.2% by weight, based on the total weight of monomers.

Thermotropic wholly aromatic polymers suitable for use in the present invention tend to be substantially insoluble in common solvents;
Therefore, it is difficult to undergo solution processing. However, as already mentioned, such polyesters can be easily processed using common melt processing methods. Particularly preferred wholly aromatic polymers are pentafluorophenol The preferred thermodropink wholly aromatic polyesters for use in the present invention generally have a molecular weight of about 2,000 to 200%.

000, preferably about 10,000 to 50,000, more preferably about 20,000 to 25,000.

This determination of molecular weight can be carried out by Kell transmission chromatography and other standard determination methods that do not involve solution formation of the polymer, such as end group determination by infrared spectroscopy on compression molded films. Moreover, the molecular weight can also be measured using a light scattering method in the state of a pentafluorophenol solution.

The thermodropink wholly aromatic polyester used in the present invention generally has 0%
．． at least about 2.0 when measured at a concentration of 1% by weight
dl/g, for example, about 2.0-10.0 dl/
The logarithmic viscosity number (T.v.) of g is shown.

Particularly preferred thermotropic wholly aromatic polymers are those of the aforementioned US Pat. Nos. 4,16L470;

No. 330,457.

The fully aromatic polyesters disclosed in US Pat. No. 4,161,470 are melt processable fully aromatic polyesters that can form an anisotropic melt phase at temperatures below about 350°C. This polyester consists of the following repeating components I and (1) as follows: This polyester consists of about 10-90 mole percent of component I and about 10-90 mole percent of component (2). In one embodiment, component (1) is about 65-85 mole %, preferably about 70-8
Present in an amount of 0 mole % (eg, about 75 mole %).

In another embodiment, component (I) is present in much smaller amounts, about 15-35 mole percent, preferably about 20-30 mole percent.

In addition, at least some of the hydrogen atoms bonded to the ring are
It may be optionally substituted with a substituent selected from the group consisting of an alkyl group having 1 to 4 carbon atoms, an alkoxy group having 1 to 4 carbon atoms, halogen, phenyl, substituted phenyl, and combinations thereof.

The polyesters disclosed in U.S. Pat. No. 4,330,457 are melt processable wholly aromatic polyester-amides that can form an anisotropic melt phase below about 400C. The polyester-amide consists essentially of the following repeating components I, (1), (2), and optionally (2).

11 Ni+C-A-C-)- (wherein A means a divalent group having at least one aromatic ring or a divalent trans-1+4-cyclohexylene group), m: -f-Y-Ar - Zsu [wherein, the total is a divalent group having at least one aromatic ring, Y is 0, NH or NR, Z is NH or NR (wherein R is an alkyl group or aryl group having 1 to 6 carbon atoms) ], TV: -f
O-Ar'-O] (wherein Ar' means a divalent group having at least one aromatic ring).

This poly(ester-amide) consists of about 10-90 mol% component (1), about 5-45 mol% component (2), about 5-45 mol% component (2), and about 0-40 mol% component (3). . Furthermore, at least some of the hydrogen atoms bonded to the ring are selected from the group consisting of an alkyl group having 1 to 4 carbon atoms, an alkoxy group having 1 to 4 carbon atoms, halogen, phenyl, substituted phenyl, and a combination thereof. may be optionally substituted with a substituent.

The blends of the present invention consist of about 20-75% by weight non-thermodropink wholly aromatic polyester component and about 25-80% by weight thermotropic wholly aromatic polyester component. Preferably, the blend contains about 30-50% by weight of the thermodropink wholly aromatic polyester component. The weight percentages listed in -1- are based on the total weight of the above two polymer components in the blend, excluding amounts of separately added ingredients such as fillers.

The blend of the present invention comprising the wholly aromatic polyester component described above may further contain various non-wholly aromatic polyester polymers in small amounts.

The thermotropic and non-thermotropic wholly aromatic polyester components may also contain small amounts of non-aromatic repeating components. Such additional non-wholly aromatic polymers or non-aromatic repeating components are present in an amount of up to about 50 weight percent, preferably up to about 25 weight percent, based on the combined weight of the polymer components.

Further, the wholly aromatic polyester component used in the present invention may contain a small amount of amide bond in addition to the ester bond in one polymer chain, and in this sense also includes polyester-amide.

To make the blends of the invention, both components are usually provided in the form of chips or pellets.

After weighing each component separately, both components are physically mixed in a suitable device such as a ball mill. This physical mixture is then dried at a temperature of about 100° C. overnight to about 24 hours. Any suitable equipment may be used to dry the mixture, but it is generally convenient to dry the mixture in a vacuum dryer or a circulating air dryer. The purpose of this drying step is to remove moisture from the resulting physical mixture to prevent polymer degradation during subsequent melt blending operations. Once the mixture of solid polymer particles has been dried, a polymer melt blend can be produced. A convenient method for forming polymer melt blends is melt extrusion. After thoroughly mixing the polymers in the molten state using an extrusion device, the resulting blend is extruded in the form of strands. The strands may be chopped into chips or pellets after assimilation.

Note that in the present invention, melt blend means a composition obtained by a melt blend operation.

As mentioned above, it is known in the art that melt blends of two types of polymers tend to undergo phase separation due to the incompatibility of the two polymers, resulting in a decrease in properties. However, it has been found that the blends of the present invention give unexpected results. That is, the mechanical properties of the blends of the present invention were found to be significantly and effectively improved over the continuous phase non-thermotropic wholly aromatic polyester matrix alone.

It has been found that such physical advantages are the result of the liquid crystalline polymer component forming domains that act as reinforcements to the blend. Such domains may be of very elongated dimensions and may, for example, take a sheet-like or fibrous form. The aspect ratio of this domain (i.e., the ratio of its length to its maximum thickness) is at least greater than about 3=1, and generally ranges within or above about 10=1 to 10 (1:), e.g. , the aspect ratio of a sheet-like domain is the ratio of the length of the sheet to the thickness of the sheet. Typical domain lengths are in the range of about 5-100 μ, but there are domains much longer than this. The main volume is at least about 1 μ3.

The domains are oriented in the melt processing direction (ie, melt flow or extrusion direction) of the blend and provide a substantial reinforcing effect in this melt processing direction.

Such domains are advantageous as reinforcing materials because they can have significantly longer dimensions than reinforcing fibers commonly used in the form of separate additions to blends prior to melt processing. Limitations are imposed by the length of reinforcing fibers added to such blends, the need to maintain satisfactory melt processing properties, and the possibility of breakage of the added fibers during the blending operation; It is said that the inclusion of long reinforcing fibers is not desirable.

In contrast, the liquid crystalline polymers used in the blends of the present invention, when processed by conventional melt processing techniques,
It does not suffer from the drawbacks listed in (-) due to its inherent ability to form self-reinforcing domains within the blend during melt processing. Although the arrangement of the domains is not spatially regular, it is often observed that the domains are oriented with their long axes essentially parallel. Such parallel alignment enhances the reinforcing properties of the domains.

Blends of the present invention can be melt processed at temperatures within the range of about 240-400°C. Preferably, the blend is capable of undergoing melt processing at a temperature within the range of about 275-350°C.

The blends of the invention exhibit anisotropy in the melt phase. This was found to be because the thermotropic wholly aromatic polyester component in Blen 1'' still retained its anisotropic properties despite the coexistence of other components.

This liquid crystalline polymer component therefore provides the blends of the present invention with uniquely reduced processability.

The blends of this invention are useful as molding resins, especially injection molding resins. This blend can also be used to form extrusions and fibers and films. The molded product obtained by molding the blend of the present invention has tensile strength, tensile modulus,
Bending strength, flexural modulus, notched Izod impact strength,
and has excellent mechanical properties such as heat distortion temperature.

It is also possible to mold articles from compounded materials containing the blends of the invention as one component. Such molding compositions are comprised of solid fillers and/or reinforcements incorporated into the blends of the invention in an amount of about 1 to 50% by weight, preferably about 10 to 30% by weight, based on the total weight of the molding composition. Typical fibers that can act as reinforcing media include glass fibers, asbestos, graphitic carbon fibers, amorphous carbon fibers, synthetic polymer fibers, aluminum fibers, aluminum silicate fibers, aluminum oxide J fibers, titanium fibers, Examples include magnesium fiber, rock wool fiber, steel fiber, tungsten fiber, cotton, wool, and wood cellulose fiber. Typical filler materials include calcium silicate,
Examples include silica, clay, talc, mica, polytetrafluoroethylene, graphite, alumina trihydrate, thorium aluminum carbonate, and barium ferrite.

To form a molded article by injection molding from a blend of the present invention or from a molding material containing a blend of the present invention,
This blend) or the melting temperature of the blend (
(eg, 280-300°C) and then injected into the mold cavity. The mold cavity is typically maintained at a temperature of about 100°C or less (eg, about 90-100°C). Apply the molten blend to the mold cavity at approximately 10,000 psi.
Inject at a pressure of (approximately 700 kg/c+J). The cycle time (i.e., the time for each injection stroke) for the blends of the present invention is typically about 10 to 40 seconds.

The properties of the molded article formed from the blend composition of the present invention are as follows:
This can be improved by heat-treating to promote the transesterification reaction between image components. Heat treatment of molded parts should be carried out in an inert atmosphere (e.g. nitrogen, argon, helium).
Alternatively, it can be carried out in a flowing oxygen-containing atmosphere (eg, air).

It has been observed that the properties of molded articles formed from the blends of the present invention vary with processing conditions such as mold temperature, injection molding pressure, and cycle time. However, those skilled in the art will be able to easily determine experimentally the conditions that will maximize the properties of molded articles formed from the blends of the present invention.

The following examples illustrate the invention.

However, it goes without saying that the present invention is not limited to these specific examples. Examination of the data shown in the examples reveals that the mechanical properties of the non-liquid crystalline wholly aromatic polyester used as the matrix polymer according to the present invention are improved as a result of the presence of domains of the liquid crystalline wholly aromatic polyester. It will be recognized that there is.

1-Bisphenol A1 A polymer blend (trade name: Ardel from Union Carhide Co., Ltd.) consisting mainly of a non-thermodropink wholly aromatic polyester produced from isophthalic acid and terephthalic acid, with a small amount of nylon added thereto. commercially available as 8X-1500), 40 mol% of p-oxybenzoyl component and 6-
A blend consisting of 60 mol% of oxy-2-naphthoyl component and 30% by weight of thermotropic liquid crystalline wholly aromatic polyester was prepared by physically mixing both components in the form of pellets, and then extruding this mixture using a single screw extruder. It was formed by melt extrusion blending and re-pelletizing the resulting blend. The resulting pelleted blend was then injection molded at a temperature of 300° C. and a mold temperature of 66° C. to form tensile and bending test specimens. The mechanical properties of these specimens were determined according to ASTM D638 (Tensile properties, test area 0.125 Xo, 075 S'<3.2X1.9
+in>) and ^STM D790 (bending properties) results are shown in Table 1 as sample A. For comparison, tensile test pieces and bend test pieces made only of ArdelAX-1500 were similarly formed, and their mechanical properties were measured. The results are shown as sample B in Table 1. An approximately 35% reduction in injection molding pressure was observed for the Sample A blend compared to the Sample B blend.

Table 1 The fracture surface of molded sample A was examined using a scanning electron microscope at a magnification of 3500 times (FIG. 1). Figure 1 shows (1) and (2).
) have an average diameter of about 1 micron and a visible length of at least about 10 microns.
Met. Specifically, the diameter of domain (1) is approximately 1μ
, the diameter of domain (2) was approximately 3μ.

Non-smotropic wholly aromatic polyester made from bisphenol A1 isophthalic acid and terephthalic acid (trade name Ardel D from Union Carbide)
-100) 70% by weight, 60 mol% of 6-hydroxy-2-naphthoic acid, 20% of terephthalic acid.
mol% and p-acetoxyacetanilide 20 mol%
A thermodropink liquid crystalline wholly aromatic polyester produced from 30 wt. was formed by re-pelletizing the blend. The resulting pelleted blend was then heated at a temperature of 350°C and a mold temperature of 100°C.
℃ injection molding to form tensile and bending specimens. The mechanical properties of these test pieces were measured in the same manner as in Example 1, and the results are shown in Table 2 as Sample A.

For comparison, bow 1 consisting only of 8rdelll-1,00, a non-thermotropic wholly aromatic polyester.
Tension specimens and bend specimens were also formed and their mechanical properties were measured. The results are shown as sample B in Table 2.

35 for blending into the sample compared to sample B polymer.
% reduction in injection molding pressure was observed.

The fracture surface of molded sample A in Table 2 was examined using a scanning electron microscope at a magnification of 5,000 times (FIG. 2). The domains of typical liquid crystalline polymer components shown as (11 to (5)) in Figure 2 are:
with an average diameter of about 1 tt and a visible length of at least about 10/
! Met. Figure 3 is also an electron micrograph showing the fracture surface of a molded sample containing domains of the liquid crystalline polymer component at a magnification of 5,000 times, and the domains are elongated, parallel, and
It is irregular in width and fairly flat. The width of the domain is within the range of approximately 0.2 to 2°5μ, with an average width of approximately 0.
．． It was 5μ.

Jisan' contains 70% by weight of a non-thermotropic wholly aromatic polyester (as described in Example 1) commercially available from Union Carbide under the trade name Ardel AX-1500, and 6-
A blend consisting of 30 mol% of thermotropisoc liquid crystalline fully aromatic polyester prepared from 60 mol% of hydroxy-2-naphthoic acid, 20 mol% of terephthalic acid and 20 mol% of p-acetoxyacetanilide was mixed into pellets of both polymers. This mixture is melt extrusion blended in a single screw extruder, and the resulting blubber is mixed physically.
It was formed by re-pelletizing nondo. The obtained knot-shaped blend was then injection molded at a temperature of 350° C. and a mold temperature of 100° C. 1 to form a tensile test piece.

The fracture surfaces of the molded specimens thus obtained were examined with a scanning electron microscope at magnifications of 1500x (FIG. 4) and 2000x (FIG. 5). The domain size of the typical liquid crystalline polymer components shown as (1) and (2) in FIG. 4 had an average diameter of about 2 microns and a length of at least about 10 microns. The domains shown as (3) in Figure 5 had an average diameter of about 2μ and a visible length of at least 30μ.

Although the principles, preferred embodiments, and details of implementation of the present invention have been described above, these are intended to be illustrative only and not limiting, and the invention is not limited to the specific forms disclosed herein. do not have. Various changes and modifications can be made by those skilled in the art within the scope of the present invention.

[Brief explanation of the drawing]

FIG. 1 is a scanning electron micrograph at a magnification of 3500 times of the fracture surface of a molded specimen made from the blend of the present invention, and FIGS. 2 and 3 are the fracture surfaces of a molded specimen made from the blend of the present invention. Figure 4 is a scanning electron micrograph at 1500x magnification of the fracture surface of a molded specimen made of the blend of the present invention, and Figure 5 is a scanning electron micrograph at 1500x magnification of It is a scanning electron micrograph at a magnification of 2000 times of the fracture surface of a molded test piece made of a blend.

Claims (16)

[Claims] (1) A polymer melt blend capable of exhibiting an anisotropic melt phase and forming an excipient with excellent mechanical properties, wherein: (a): Sum of components (a) and (b). Approximately 2 based on weight
a melt-processable wholly aromatic polyester that is incapable of forming an anisotropic melt phase by itself in an amount of 0 to 75% by weight, and (b): based on the combined weight of components (a) and (b) about 2
5 to 80% by weight, which is capable of forming an anisotropic melt phase by itself, substantially in the form of elongated domains having an aspect ratio of at least about 3 and a volume of at least about 1 μ^3 within the blend. A polymer melt blend consisting of a melt-processable wholly aromatic polyester, present. (2) The polymer blend of claim 1 which is capable of undergoing melt processing at temperatures within the range of about 240-400°C. (3) The polymer blend of claim 1 which is capable of undergoing melt processing at temperatures within the range of about 275-350°C. 4. The polymer blend of claim 1, wherein component (a) is a copolymer of bisphenol A, isophthalic acid and terephthalic acid. (5) The polymer blend according to claim 1, wherein component (a) is a copolymer of bisphenol A and terephthalic acid. 6. The polymer blend of claim 1, wherein component (b) alone is capable of forming an anisotropic melt phase at temperatures below about 400°C. (7) Component (b) alone exhibits a logarithmic viscosity of at least 2.0 dl/g when dissolved in pentafluorophenol at a concentration of 0.1% by weight at 60°C. Polymer blend according to range 1. (8) The polymer blend of claim 1 comprising an amount of component (a) within the range of about 70-50% by weight and component (b) in an amount within the range of about 30-50% by weight. . (9) The polymer of claim 1 in the form of a molding material, comprising about 1 to 50% by weight of solid fillers and/or reinforcements incorporated into the polymer blend, based on the total weight of the molding material. blend. (10) The amount of solid filler and/or reinforcing material is about 10 to 30% by weight based on the total weight of the molding material.
A polymer blend in the form of a molding material according to claim 9. (11) The polymer blend according to claim 1 in the form of a molded article. (12) A polymer blend according to claim 1 in the form of an extrudate. (13) The polymer blend of claim 1 in the form of melt-spun fibers. (14) Claim 1 in the form of melt-extruded film
Polymer blends as described in Section. (15) Component (b) is essentially the following repeating components I and II: I: ▲ There are mathematical formulas, chemical formulas, tables, etc. ▼ II: ▲ There are mathematical formulas, chemical formulas, tables, etc. ▼ (In the above formula, aromatic ring At least some of the hydrogen atoms bonded to are optionally selected from the group consisting of an alkyl group having 1 to 4 carbon atoms, an alkoxy group having 1 to 4 carbon atoms, halogen, phenyl, substituted phenyl, and combinations thereof. (optionally substituted with a substituent), consisting of approximately 10 to 90 mol% of component I and
2. The polymer blend of claim 1, wherein the polymer blend is a polyester containing from about 10 to 90 mole percent. (16) Component (b) is essentially the following repeating component I, II
, III, and optionally IV: I: ▲ There are mathematical formulas, chemical formulas, tables, etc. ▼ II: ▲ There are mathematical formulas, chemical formulas, tables, etc. ▼ (wherein A is a divalent group having at least one aromatic ring or means a divalent trans-1,4-cyclohexylene group) III: -[Y-Ar-Z]- (wherein Ar is a divalent group having at least one aromatic ring, Y is O, NH or NR and Z each mean NH or NR, R means an alkyl group or aryl group having 1 to 6 carbon atoms) IV: -[O-Ar'-O-]- (wherein Ar' is at least (means a divalent group having one aromatic ring) (In the formula, at least a part of the hydrogen atoms bonded to the ring may optionally be an alkyl group having 1 to 4 carbon atoms, or an alkyl group having 1 to 4 carbon atoms.) (optionally substituted with a substituent selected from the group consisting of an alkoxy group, halogen, phenyl, substituted phenyl, and a combination thereof), containing about 10 to 90 mol% of component I and about 5 to 45% of component II 2. The polymer blend of claim 1, wherein the polymer blend is a polyester-amide containing about 5 to 45 mole percent of component III and about 0 to 40 mole percent of component IV.