Electrical insulation film and condenser

An electrical insulating film which comprises a styrene polymer having a syndiotactic configuration and containing not more than 1,000 ppm of residual aluminum derived from the catalyst used in the production of the styrene polymer, and not more than 3,000 ppm of residual styrene monomer, and a condenser comprising metal electrodes and the above film which is 0.5 to 30 .mu.m thick and has crystallinity of not less than 25%, are disclosed.

BACKGROUND OF THE INVENTION 
1. Field of the Invention 
The present invention relates to an electrical insulating film and a 
condenser, more specifically, it relates to an electrical insulating film 
which comprises a specific styrene polymer excellent in electrical 
insulating properties, heat resistance and the like, and further relates 
to a condenser which comprises said electrical insulating film and metal 
electrodes. 
2. Description of the Related Arts 
Hitherto, polyethylene terephthalate (PET), polypropylene (PP), styrene 
polymer having an atactic configuration and the like have been used as 
materials for electrical insulating films. However, these materials have 
insufficient heat resistance. Particularly, they have low resistance to 
heat of soldering during production of SMD (surface mount device) which 
has recently become an particularly important problem, resulting in 
difficulty in processing operation. 
Accordingly, polyphenylene sulfide (PPS), polyimide and the like have been 
developed as a heat resistant material. However, these materials are not 
practical because they are expensive and have problem in insulating 
properties. 
The film comprising styrene polymer having a syndiotactic configuration, 
which the present inventors have previously proposed (see Japanese Patent 
Application Laid-Open No. 316246/1989) is excellent in heat resistance, 
chemical resistance, electrical properties, mechanical strength and the 
like, and expected to be used as an electrical insulating material instead 
of the above materials. 
However, the previously proposed film which comprises a styrene polymer 
having a syndiotactic configuration has various problems for practical 
use, for example, when it is formed into a thin film, it may fail to show 
sufficient dielectric strength, and dielectric dissipation factor 
particularly in high frequency region may be high. 
Accordingly, the present inventors have studied intensively to develop a 
film comprising styrene polymer having a syndiotactic configuration which 
can be practically used as an electrical insulating material. As the 
result, it has been found that a film of the styrene polymer, wherein 
impurities mixed during an operation for production thereof is controlled 
at low concentration, is adequate to the above purpose and suitable an as 
electrical insulating film. Further, it has been found that the above film 
having a certain thickness and crystallinity provided with metal 
electrodes is useful as a condenser. The present invention has been 
accomplished based on such findings. 
SUMMARY OF THE INVENTION 
That is, the present invention provides an electrical insulating film 
comprising a styrene polymer having a syndiotactic configuration which 
contains not more than 1,000 ppm of residual aluminum derived from the 
catalyst use in the production of the styrene polymer, and not more than 
3,000 ppm of residual styrene monomer. Further, the present invention 
also provides a condenser which comprises metal electrodes and a 0.5 to 30 
.mu.m thick electrical insulating film comprising a styrene polymer having 
crystallinity of not less than 25% and a syndiotactic configuration which 
contains not more than 1,000 ppm of residual aluminum derived from 
catalyst used in the production of the styrene polymer, and not more than 
3,000 ppm of residual styrene monomer. 
Here, a styrene polymer having a syndiotactic configuration means a styrene 
polymer wherein stereochemical structure is a syndiotactic configuration, 
that is, the stereostructure in which phenyl groups or substituted phenyl 
groups as side chains are located alternately in opposite directions 
relative to the main chain consisting of carboncarbon bonds. Tacticity is 
quantitatively determined by the nuclear magnetic resonance method 
(.sup.13 C-NMR method) using 
carbon isotope. The tacticity measured by the .sup.13 C-NMR method can be 
indicated in terms of proportions of structural units continuously 
connected to each other, i.e., a diad in which two structural units are 
connected to each other, a triad in which three structural units are 
connected to each other and a pentad in which five structural units are 
connected to each other. The styrene polymer having a syndiotactic 
configuration in the present invention means styrene polymer having such 
syndiotacticity that the proportion of racemic diad is at least 75%, 
preferably at least 85%, or proportions of racemic pentad is at least 30% 
and preferably at least 50%. Examples of the styrene polymer include 
styrene, poly(alkylstyrene), poly(halogenated styrene), 
poly(alkoxystyrene), poly(vinylbenzoate), hydrogenated polymers thereof 
and mixture thereof, or copolymers containing these structural units. The 
poly(alkylstyrene) includes poly(methylstyrene), poly(ethylstyrene), 
poly(propylstyrene), poly(butylstyrene), poly(phenylstyrene), 
poly(vinylnaphthalene), poly(vinylstyrene), poly(acenaphthylene); and the 
poly(halogenated styrene) includes poly(chlorostyrene), poly(bromostyrene) 
and poly(fluorostyrene). The poly(alkoxystyrene)includes 
poly(methoxystyrene), poly(ethoxystyrene). Of these, a particularly 
preferred styrene polymer includes polystyrene, poly(p-methylstyrene), 
poly(m-methylstyrene), poly(p-tert-butylstyrene), poly(p-chlorostyrene), 
poly(m-chlorostyrene), poly(p-fluorostyrene) and further a copolymer of 
styrene and p-methylstyrene (see Japanese Patent Application Laid-Open No. 
187708/1987). 
Comonomer of the styrene copolymer includes, in addition to the 
above-described monomer of styrene polymer, olefin monomer such as 
ethylene, propylene, butene, hexene, octene; diene monomer such as 
butadiene, isoprene; cyclic diene monomer or polar vinyl monomer such as 
methyl methacrylate, maleic anhydride, acrylonitrile. 
Molecular weight of the styrene polymer is not particularly limited, but 
the styrene polymers having weight average molecular weight of 10,000 tO 
3,000,000, especically, 50,000 to 1,500,000 are most suitable. When weight 
average molecular weight is less than 10,000, the product may not be 
sufficiently stretched. Further, the range of molecular-weight 
distribution is not limited and various styrenes can be used. The value, 
(weight average molecular weight (Mw)/number average molecular weight 
(Mn)), is preferably 1.5 to 8. The styrene polymer having a syndiotactic 
configuration is much superior in heat resistance to the conventional 
styrene polymer having an atactic configuration 
The styrene polymer of the present invention having a syndiotactic 
configuration is as described above and is of high purity with extremely 
low impurities content. That is, the aluminum content in the styrene 
polymer should be not more than 1,000 ppm, preferably 800 ppm, said 
aluminum being derived from the catalyst used in the process for 
production wherein a styrene monomer is polymerized to produce the styrene 
polymer, and the residual styrene monomer content in the styrene polymer 
should be not more than 3,000 ppm, preferably, 2,000 ppm. 
The aluminum in the styrene polymer is derived from the catalyst comprising 
titanium compound and aluminum compound used conventionally. The styrene 
monomer is unreacted monomer among starting monomers used for production 
of the styrene polymer and includes the other residue monomer when a 
monomer other than styrene monomer is used to obtain a copolymer. 
The methods for production of such styrene polymer of high purity includes 
various ones as shown below. In this case, the monomer corresponding to 
the above-described polymer is used as a starting material. Firstly for 
control of the residual aluminum content and residual styrene monomer 
content within the above range, (1) a method in which a highly active 
catalyst is used to produce a styrene polymer (see, Japanese Patent 
Application Laid-Open No. 294705/1989) or (2) a method which comprises 
deashing and washing, that is, a method wherein a styrene monomer is 
polymerized using a conventional organometallic compound of group IVA 
described, for example, in Japanese Patent Application Laid-Open No. 
187708/1987 (e.g. an organic titanium compound) and alkylaluminoxane such 
as methylaluminoxane as the catalyst components, then the resulting 
styrene polymer having a syndiotactic configuration is deashed with a 
solution of acid or alkali in a suitable solvent, and washed with a 
suitable solvent. 
As mentioned above, a styrene polymer having a syndiotactic configuration 
with less residual aluminum content can be obtained by the method (1) or 
(2). Further, the product is treated by the following method (3) or (4) to 
control the residual styrene monomer content below 5,000 ppm. When the 
residual styrene monomer content of the product in this step is not more 
than 5,000 ppm, the product may be formed into a film with the residue 
content of the desired value, i.e. 3,000 ppm or less. 
(3) A method wherein the above styrene polymer is dried under reduced 
pressure. 
For drying under reduced pressure, it is efficient to set the drying 
temperature at the glass transition temperature of the polymer or higher. 
(4) A method wherein the above styrene polymer is degassed by an extruder. 
Such treatment provides a styrene polymer of high purity which contains 
less residual aluminum and residual styrene monomer and has a high degree 
of syndiotactic configuration. 
It is preferable from the viewpoint of electrical properties to control the 
content of the residual group IVA element compound particularly derived 
from the catalyst, for example, the residual titanium content to not more 
than 10 ppm, preferably not more than 7 ppm, and the content of the 
halogen compound to not more than 50 ppm, and the content of alkali metal 
compound to not more than 100 ppm, by deashing operation. 
Electrically inactive inorganic filler, antioxidant, antistatic agent, 
flame retardant or other resin may be added to thus produced styrene 
polymer as needed, so long as they do not inhibit the objective effect of 
the present invention. 
In this case, the electrically inactive inorganic filler means oxide, 
hydroxide, sulfide, nitride, halide, carbonate, sulfate, acetate, 
phosphate, phosphite, organic carboxylate, silcate, titanate or borate of 
the group IA, IIA, IVA, VIA, VIIA, VIII, IB, IIB, IIIB or IVB element, and 
hydrate compound thereof, complex compound containing them as a center, 
natural mineral particles. 
For example, group IA element compound such as lithium fluoride, borax 
(hydrate salt of sodium borate); group IIA element compound such as 
magnesium carbonate, magnesium phosphate, magnesium oxide (magnesia), 
magnesium chloride, magnesium acetate, magnesium fluoride, magnesium 
titanate, magnesium silicate, hydrate salt of magnesium silicate (talc), 
calcium carbonate, calcium phosphate, calcium phosphite, calcium sulfate 
(gypsum), calcium acetate, calcium terephthalate, calcium hydroxide, 
calcium silicate, calcium fluoride, calcium titanate, strontium titanate, 
barium carbonate, barium phosphate, barium sulfate, barium phosphite; 
group IVA element compound such as titanium dioxide (titania), titanium 
mono-oxide, titanium nitride, zirconium dioxide (zirconia), zirconium 
monooxide; group VIA element compound such as molybdenum dioxide, 
molybdenum trioxide, molubdenum sulfide; group VIIA element compound such 
as manganese chloride, manganese acetate; group VIII element compound such 
as cobalt chloride, cobalt acetate; group IB element compound such as 
copper iodide; group IIB element compound such as zinc oxide, zinc 
acetate; group IIIB element compound such as aluminum oxide (alumina), 
aluminum hydroxide, aluminum fluoride, aluminosilicate (alumina silicate, 
kaolin, kaolinite); group IVB element compound such as plumbago, carbon, 
graphite, glass; particulate natural mineral such as carnallite, kainite, 
isinglass (mica, phlogoite), and pyrolusite. 
The average particle diameter of the inorganic filler is not particularly 
limited, but preferably, 0.01 to 3 .mu.m, more preferably, 0.01 to 1 
.mu.m. The content in the molded product is 0.001 to 1 wt%, preferably, 
0.005 to 1 wt%. The inorganic filler is contained in the final molded 
product and the method for compounding is not limited. For example, it may 
be added in the optional step during polymerization, or added in the 
optional step during melt extrusion. 
The other resin which can be added to the above styrene polymer includes 
various kinds, for example, styrene polymer having an atactic 
configuration, styrene polymer having an isotactic configuration, 
polyphenylene ether and the like. Such resins may be readily 
compatibilized with the above styrene polymer having a syndiotactic 
configuration and effective to control crystallization when pre-molded 
product for stretching is prepared, thereby providing a film with enhanced 
stretching properties and excellent in dynamic properties, whose 
stretching conditions may be readily controlled. Among them, when styrene 
polymer having an atactic and/or isotactic configuration is compounded, it 
is preferably composed of the same monomers as those of the styrene 
polymer having a syndiotactic configuration. The content of the compatible 
resin component is 70 to 1 wt%, preferably, 50 to 2 wt%. When the content 
of the compatible resin component exceeds 70 wt%, heat resistance, which 
is an advantage of the styrene polymer having a syndiotactic 
configuration, may be undesirably spoiled. The other non-compatible resins 
which can be added to the polymer of the present invention include, a 
polyolefin such as polyethylene, polypropylene, polybutene, polypentene; a 
polyester such as polyethylene terephthalate, polybutylene terephthalate, 
polyethylene naphthalate; a polyamide such as nylon-6, nylon-6,6; a 
polythioether such as polyphenylene sulfide, a polycarbonate, a 
polyarylate, a polysulfone, a polyether ether ketone, a polyethersulfone, 
a polyimide, a halogenated vinyl polymer such as Teflon, an acrylic 
polymer such as polymerthyl methacrylate, a polyvinyl alcohol, and all but 
the aforementioned compatible resins. There are also cross linked resins 
containing the aforementioned compatible resins. 
When the styrene polymer of the present invention having a syndiotactic 
configuration contains a small amount of the above resin, such resin, 
which is incompatible with the above styrene polymer, can be dispersed 
like islands in the styrene polymer having a syndiotactic configuration. 
Accordingly, it is effective to provide proper gross and to improve 
smoothness of the surface after stretching. The content of these 
non-compatible resin is 50 to 2 wt% for the purpose of providing gloss, 
and 0.001 to 5 wt% for the purpose of controlling the surface properties. 
When the temperature at which the product is used is high, no-compatible 
resin with considerable heat resistance is preferably used. 
The present invention is an electrical insulating film formed using the 
aforementioned styrene polymer of high purity having a syndiotactic 
configuration as a starting material. The process for production of such 
film is not particularly limited. The film may be produced by the process 
wherein these materials are heat-melted to obtain pre-molded product, then 
heat-stretched and heat-treated, if necessary. 
The operations from heat melting to heat treatment (annealing) will be 
explained in detail. 
Firstly, thus obtained styrene polymer as a material for molding is usually 
extruded to give a pre-molded product for stretching (film, sheet or 
tube). In this molding, the aforementioned heat-melted material for 
molding is generally molded into a desired form by an extruder. 
Alternatively, the material for molding may be molded without heat melting 
while it is softened. An extruder used in this case may be either a 
uniaxial extruder or a biaxial extruder, with or without vent. A uniaxial 
tandem type is preferred. Using an extruder with a suitable mesh, 
impurities and contaminants can be removed. As for the shape of the mesh, 
for example, plane or cylinder mesh may be properly selected and used. 
The extrusion conditions are not particularly limited and properly selected 
depending on the various circumstances. Preferably, the temperature is 
selected in the range from melting point to the temperature 50.degree. C. 
higher than decomposition temperature of the material for molding, and 
shear stress is not more than 5.times.10.sup.6 dyne/cm.sup.2. The die used 
is a T-die, a ring die or the like. 
After the above extrusion, the resulting pre-molded product is cooled and 
solidified. As a refrigerant used in this step, for example, gas, liquid, 
metal roller and the like may be used. When a metal roller is used, it is 
effective to prevent uneven thickness and surge by using air knife, air 
chamber, touch roll, electrostatic application and the like. 
The temperature of cool solidification is generally 0.degree. C. to 
30.degree. C. higher than glass transition temperature of the premolded 
product for stretching, preferably from 70.degree. C. lower than glass 
transition temperature to glass transition temperature. The cooling rate 
is properly selected within the range from 200 to 3.degree. C./sec. 
In the present invention, the cooled and solidified pre-molded product is 
preferably uni- or bi-axially stretched. For biaxial stretching, 
transverse direction (TD) stretching and machine direction (MD) stretching 
may be simultaneously conducted, or successively conducted in suitable 
order. Alternatively, stretching may be conducted in one step, or in 
multiple steps. Stretch ratio is not less than 2, preferably not less than 
3 as a ratio of area. When stretch ratio is within this range, 
crystallinity of the film becomes not less than 25%, and product with good 
physical properties can be obtained. 
Methods for stretching include various methods such as a method using a 
tenter, a method wherein the product is stretched between rollers, a 
method by bubbling using a pressure of a gas, a method by rolling and the 
like. These methods may be applied singly or in combination. The 
temperature for stretching is generally set between glass transition 
temperature of the pre-molded product and melting point of the pre-molded 
product. The stretching rate is generally 1.times.10 to 1.times.10.sup.5 
%/min., preferably, 1.times.10.sup.3 to 1.times.10.sup.5 %/min. It is 
preferable to conduct heat treatment (annealing or heat setting) for the 
stretched film obtained by stretching under the aforementioned conditions 
when dimensional stability, heat resistance, strength balance of the 
surface of the film are further required. Heat setting may be conducted by 
the usual method. It can be conducted by maintaining the stretched film in 
the temperature range from glass transition temperature to melting point 
of the film, preferably, 100.degree. C. lower than melting point to a 
little lower than melting point for 0.5 to 120 seconds under a state of 
tension, a relaxed state or a state of controlling shrinkage. Such heat 
setting may be conducted twice or more changing the conditions within the 
above range. The heat setting may be conducted in an atmosphere of inert 
gas such as argon gas, nitrogen gas or the like. 
Thus produced film of the present invention has excellent heat resistance 
and crystallinity is generally not less than 25%. Further, the film of 0.5 
to 500 .mu.m thickness has low dielectric dissipation factor (1 MHz, room 
temperature), i.e., not more than 0.002 and has extremely good dielectric 
breakdown strength. For example, when the 7 thickness of the film is not 
more than 20 .mu.m, dielectric breakdown voltage is not less than 150 
kV/mm (room temperature). Accordingly, among these films, 0.5 to 12 .mu.m 
thick films, 20 to 150 .mu.m thick films, 100 to 500 .mu.m thick films and 
10 to 50 .mu.m thick films are suitably used as plastic dielectric, base 
meterials for flexible printed boards, general insulating plates and 
insulating tapes, respectively. 
The condenser of the present invention comprises an aforementioned 
insulating film with crystallinity of 25% or more and thickness of 0.5 to 
30 .mu.m, and metal electrodes provided on the film. 
The base film (dielectric) for the condenser of the present invention is a 
film of the above styrene polymer having syndiotactic configuration 
(hereinafter referred to as SPS film) and has crystallinity of not less 
than 25%, preferably not less than 30%. When crystallinity is less than 
25%, the film may shrink at the temperature higher than glass transition 
temperature, resulting in adverse effect on dielectric properties. The 
thickness is 0.5 to 30 .mu.m, preferably, 0.5 to 15 .mu.m. When the 
thickness is less than 0.5 .mu.m, it is difficult to form film, and when 
it exceeds 30 .mu.m, the condenser may undesirably become larger. 
The material for metal film of the metal electrode used for the condenser 
of the present invention is not particularly limited. Aluminum, zinc, 
nickel, chromium, copper, or alloy thereof is preferred. 
The condenser of the present invention may not be particularly limited so 
long as it is composed essentially of the above SPS film and metal 
electrodes provided on the film. 
The shape of the condenser of the present invention may be either ordinary 
type with lead wire or that without lead wire which is directly soldered 
(so-called chip condenser). 
The SPS film itself is not affected by moisture of atmosphere, but when the 
electrode is formed by a thin film of aluminum, which is affected by 
moisture of atmosphere, it is preferable to form a jacket enclosing the 
condenser. 
The material for such jacket includes metal such as aluminum, inorganic 
material such as glass, plastics and the like. For chip condenser, resin 
composition with softening temperature of not lower than 200.degree. C., 
preferably not lower than 240.degree. C. is preferred. 
The preferable process for production of the condenser in the present 
invention will be explained. 
Using the SPS film as a dielectric and metal film as an electrode, 
condenser element is formed by the known method. That is, when metallic 
foil is used as an electrode, a wind-up method wherein the shredded film 
and metallic foil are laminated and wound up into cylinder can be 
employed, and when a thin film of metal is used as an electrode, a method 
wherein a thin film layer of metal is formed on the film by metallizing 
method, metal plating method or the like, then the product is formed into 
a condenser element. 
In both cases, the product after winding is pressed in the vertical 
direction to the surface of the film at the temperature from ambient 
temperature to ca 200.degree. C. to stabilize the capacity and dielectric 
breakdown voltage. 
In the present invention, a condenser means one of passive circuit elements 
of an electric circuit, which is provided with a electrostatic capacity 
between two electrodes by providing a pair of electrodes consisting of 
conductor which are separated by a dielectric, and has the same meaning as 
that called as an accumulator or a capacitor. 
A metal foil means a self-supporting metal membrane and its thickness is 
preferably 3 to 15 .mu.m. 
A thin film of metal is a metal film which is not self-supporting and 
formed on the surface of the aforementioned film as a substrate by a 
metallizing method, a metal plating method or the like. The thickness is 
preferably 0.01 to 0.5 .mu.m. 
The condenser of the present invention is characterized by having the above 
SPS film as a dielectric, and an insulating film other than SPS film may 
coexist with SPS film between electrodes without any trouble so long as it 
should not spoil the essential advantage of the condenser having stretched 
film of styrene polymer having a syndiotactic configuration as dielectric, 
for example, the temperature properties, frequency properties. 
When a metal film layer is formed on the film, treatment for enhancement of 
adhesion such as corona treatment, plasma treatment and the like may be 
previously conducted onto the surface of the film. 
If necessary, the above condenser element may be treated to make its edge 
face conductive, lead wire is fixed or a jacket is formed to give a 
condenser. 
Further, the condenser of the present invention is dipped in oil, 
electrolytic solution or the like to give a so-called dipping condenser. 
Thus obtained condenser is excellent in heat resistance and electrical 
properties. 
As mentioned above, the electrical insulating film of the present invention 
has high heat resistance which is a characteristic of the raw material, 
i.e. styrene polymer, and resistant to a treatment at a high temperature 
such as soldering. Further, since it is a film of high purity containing 
less impurities, dielectric dissipation factor is extremely low and 
dielectric breakdown voltage is high, that is, the film is excellent in 
electrical properties. 
Thus, the electrical insulating film of the present invention can be widely 
used as an electrical insulating material, for example, as a condenser, a 
member for distributing board, insulating film, insulating tape or the 
like. 
Moreover, a condenser prepared by providing metal electrodes on the above 
insulating film has high heat stability and low dielectric dissipation 
factor (tan .delta.) which is a change in capacity with the change of 
frequency, which hardly changes with temperature. 
The condenser of the present invention which is resistant to soldering can 
be used as a so-called chip condenser without having lead wire and 
directly soldered onto a printed plate board. It is definitely superior to 
the conventional film condensers in package efficiency. 
Accordingly, the condenser of the present invention shows excellent 
characteristics when used under any circumstances and can be applied for 
producing SMD. Thus, it is useful for miniaturization of circuit plate and 
enhancement of efficiency of operation. 
Accordingly, the condenser of the present invention can be widely and 
effectively used for various application, for example, general electronic 
equipment, heat resistance, tone quality, oscillating circuit, high 
voltage electronic equipment, high frequency circuit, radio interference 
suppression. 
The present invention will be described in more detail with reference to 
examples and comparative examples. 
Reference Example 1 
(1) Preparation of contact product of trimethylaluminum and water 
In a 500-milliliter glass vessel which had been purged with argon were 
placed 17.8 g (71 mmol) of copper sulfate pentahydrate 
(CuSO.sub.4.5H.sub.2 O), 200 ml of toluene and 24 ml (250 mmol) of 
trimethylaluminum, which were then reacted at 40.degree. C. for 8 hours. 
Then, solid component was separated from the reaction mixture to prepare 
solution, and toluene was distilled away from the solution as obtained 
above under reduced pressure at room temperature to obtain 6.7 g of a 
contact product. The molecular weight of the product as determined by the 
freezing point depression method was 610. 
(2) Production of styrene polymer 
0.5 Parts by weight of dry method silica (Aerosil TT-600 (diameter of 
primary particle, 40 .mu.m) manufactured by Degussa Co.) was added to 99.5 
parts by weight of pure styrene monomer, and the resultant was mixed and 
stirred in a cylindrical container using T. K. Homomixer type L 
(manufactured by Tokushukika Kogyo Co., Ltd.) to prepare a styrene 
mixture. In this step, 0.1 parts by weight of calcium stearate was added. 
Subsequently, in a 2 liter reactor were placed 5 mmol as aluminum atom of 
the contact product obtained in (1) above, 5 mmol of triisobutylaluminum, 
0.025 mmol of pentamethylcyclopentadienyltitanium trimethoxide and 1 liter 
of the above styrene mixture, and polymerization was carried out at 
90.degree. C. for 5 hours. Then, methanol was poured to cease 
polymerization, and the resultant was dried to give 300 g of polymer. 
Subsequently, this polymer was extracted with methyl ethyl ketone using a 
Soxhlet extractor to give 98.0% of extraction residue (MIP). Weight 
average molecular weight of the resulting polymer was 390,000, and the 
value (weight average molecular weight)/(number average molecular weight) 
was 2.6. Melt viscosity (300.degree. C.; shear rate, 200/sec) was 
2.times.10.sup.4 poise. The resulting polymer was confirmed to be a 
polystyrene having a syndiotactic configuration by measurement of melting 
point and .sup.13 C-NMR spectrum. The polymer composition was repeatedly 
washed with methanol after deashed with a solution of sodium hydroxide in 
methanol. 
The residual titanium content, aluminum content and sodium content in this 
polymer composition were not more than 2 ppm, 16 ppm and 33 ppm, 
respectively. 
The polymer was dissolved in 1,2,4-trichlorobenzene at 130.degree. C. and 
the silica content in the polymer was determined. This solution was 
dropped onto a slide glass, and observed by a microscope to determine an 
average particle diameter of silica. As the result, the silica content was 
0.5 wt%, and the average particle diameter was 0.08 .mu.m. 
Reference Example 2 
(1) Preparation of contact product of water and aluminum compound 
In a 500-milliliter glass vessel which had been purged with argon were 
placed 200 ml of toluene, 23.1 g (95 mmol) of copper sulfate pentahydrate 
(CuSO.sub.4.5H.sub.2 O) and 24 ml (250 mmol) of trimethylaluminum, which 
were then reacted at 30.degree. C. for 30 hours. After the reaction was 
over, solid component was removed from the reaction mixture to prepare a 
solution, and volatile components were distilled away from the solution as 
obtained above under reduced pressure to obtain 7.04 g of a contact 
product. The molecular weight of the product as determined by the freezing 
point depression method (in benzene solution) was 1,100. 
(2) Production of styrene polymer 
In a 500 ml glass vessel equipped with a stirrer were placed 50 ml of 
toluene and 3 mmol as aluminum atom of the contact product obtained in (1) 
above, then 3 mmol of triisobutylaluminum, 0.06 mmol of 
pentamethylcyclopentadienyltitanium trimethyl and 200 ml of styrene were 
added thereto, and polymerization was carried out at 70.degree. C. for an 
hour. After the reaction was over, the product was washed with methanol 
and dried to give 36.1 g of a polymer. Weight average molecular weight of 
the resulting polymer was 400,000 and number average molecular weight was 
200,000. The resulting polymer was confirmed to be a polystyrene having a 
syndiotacticity of 97% as racemic pentad by measurement of melting point 
and .sup.13 C-NMR spectrum. The aluminum content and titanium content were 
4,500 ppm and 8 ppm, respectively.

EXAMPLE 1 
The styrene polymer powder obtained in Reference Example 1 was dried in a 
vacuum at 150.degree. C. for 2 hours with stirring. The powder was melt 
extruded by a vented uniaxial extruder equipped with a die containing 
several capillaries at the end thereof, then cooled and cut to prepare 
material for extrusion (pellet). In this step, the melt temperature was 
300.degree. C., a screw of the extruder was full flighted type with a 
diameter of 50 mm, extrusion rate was 30 kg/hr, and vent pressure was set 
at 10 mmHg. Then, the pellet was crystallized and dried in a hot air with 
stirring. The residual styrene monomer content in the resulting pellet was 
1,100 ppm, and the crystallinity was 35%. This pellet was extruded by a 
vibration-proofing apparatus comprising a serial tandem type uniaxial 
extruder with a T-die at the tip thereof. The extrusion temperature was 
320.degree. C., and shear stress was 3.times.10.sup.5 dyne/cm.sup.2. 
The melt extruded sheet was contacted and cooled onto a metal cooling 
roller by electrostatic application to prepare a raw sheet for stretching. 
In this step, the metal cooling roller was controlled at 70.degree. C. The 
cooling rate was 50.degree. C./sec. The thickness and crystallinity of the 
prepared raw sheet were 50 .mu.m and 15%, respectively. This raw sheet was 
biaxially stretched in MD and TD to the extrusion direction (sequentially, 
by three times, each) using a table tenter at 110.degree. C. and 3,000 
%/min. Then, the stretched film thus obtained was heat treated under a 
state of controlling shringkage at 260.degree. C. for 30 seconds. The 
thickness and crystallinity of the resulting film was 6 .mu.m and 55%, 
respectively. 
Dielectric dissipation factor of the film measured at 1 MHz at room 
temperature was 0.0008. Dielectric breakdown voltage was 307 kV/mm when 
measured according to ASTM D 149. 
The residual monomer content in the film was 800 ppm. 
EXAMPLES 2 AND 3 
The procedure in Example 1 was repeated, except that extruded amount and 
lip opening were controlled to provide a product of the thickness shown in 
Table 1. Thus, a film was prepared. The results are shown in Table 1. 
EXAMPLE 4 
The procedure in Example 1 was repeated, except that the amount of methanol 
for washing in Reference Example 1 was changed to produce a styrene 
polymer with a residual aluminum content of 250 ppm and the obtained 
product was used. Thus, a film was prepared. The results are shown in 
Table 1. 
COMATIVE EXAMPLE 1 
The procedure in Example 1 was repeated, except that the material for 
molding was pelletized by a uniaxial extruder without vent, and a film was 
prepared. The results are shown in Table 1. 
COMATIVE EXAMPLE 2 
The procedure in Example 1 was repeated, except that a material of 
Reference Example 2 was used, and a film was prepared. The results are 
shown in Table 1. 
TABLE 1 
______________________________________ 
Residual Dielectric 
Residual Mono- Dissipation 
Dielectric 
Al mer Thick- 
Factor Breakdown 
Example 
Content Content ness (tan .delta.) 
Strength* 
No. (ppm) (ppm) (.mu.m) 
(1 MHz) (kV/mm) 
______________________________________ 
Example 
75 800 6 0.0008 350 
Example 
75 750 50 0.0009 200 
2 
Example 
75 820 175 0.0009 150 
3 
Example 
250 760 6 0.0010 330 
4 
Compar- 
75 6,000 6 0.0045 125 
ative 
Example 
1 
Compar- 
4,500 800 6 0.0025 137 
ative 
Example 
2 
______________________________________ 
*Measured according to ASTM D149 
EXAMPLE 5 
The styrene polymer powder obtained in Reference Example 1 was dried under 
reduced pressure at 150.degree. C. with stirring. The powder was heated 
and melted at 300.degree. C., then extruded by a biaxial extruder and cut 
into pellet 
This pellet was heated, melted at 330.degree. C. and extruded by an 
apparatus comprising a serial tandem type uniaxial extruder with a T-die 
at the tip thereof. The shear stress was 3.times.10.sup.5 dyne/cm.sup.2. 
The melt extruded sheet was contacted and cooled onto a metal cooling 
roller by electrostatic application to prepare a raw sheet for stretching. 
In this step, the metal cooling roller was 70.degree. C. and cooling rate 
was 45.degree. C./sec. The thickness and crystallinity of the prepared raw 
sheet were 50 m and 14%, respectively. This raw sheet was stretched 
sequentially in MD at 110.degree. C. and 3,000%/min, and in TD at 
110.degree. C. and 3,000%/min (by three times, each) using a table tenter. 
Then, the stretched film was heated and treated in a state of controlling 
shrinkage at 255.degree. C. for 30 seconds. The thickness of the resulting 
film was 6 .mu.m. Crystallinity measured by a differential scanning 
calorimeter was 49%. 
The film was cut into a strip of 5.0 mm wide and 200 mm long, and aluminum 
was metallized in 4.0 mm width on one surface, while an edge (0.5 mm 
width) was left unmetallized. 
Two metallized films were laminated and wound and both edge faces were 
treated to be conductive. Electrode pulling fitments were welded and 
enclosed in a jacket using an epoxy resin as transfer mold to give a 
condenser of the present invention. 
Dielectric dissipation factor (tan .delta.) of the condenser was measured 
at room temperature and 1 kHz; at 150.degree. C. and 1 kHz; and at room 
temperature and 10 kHz. Rate of change of electrostatic capacity 
.DELTA.C/C was measured based on the value at room temperature and 1 kHz. 
Further, the change of the rate after soldering the condenser at 
250.degree. C. was determined at room temperature and 1 kHz. 
EXAMPLE 6 
The styrene polymer obtained in Reference Example 1 was deashed with sodium 
hydroxide/methanol, and repeatedly washed with methanol. The residual 
aluminum content, residual styrene monomer content and titanium content in 
this polymer were 50 ppm, 600 ppm and less than 2 ppm, respectively. 
The procedure of Example 5 was repeated to prepare a condenser, except that 
the film of this polymer was used. The results are shown in Table 2. 
EXAMPLE 7 
The procedure in Example 6 was repeated except that lip-opening of T-die 
and take-off speed were controlled to obtain a 30 .mu.m thick raw sheet 
for stretching. The thickness of the film used for dielectric was 3 .mu.m. 
EXAMPLE 8 
The procedure in Example 6 was repeated except that lip-opening of a T-die 
and take-off speed were controlled to obtain a 160 .mu.m thick raw sheet 
for stretching which was biaxially stretched and stretched in MD again by 
1.5 times. Thus, a condenser was prepared. The thickness of the film used 
for dielectric was 12 .mu.m. 
COMATIVE EXAMPLE 3 
The procedure in Example 5 was repeated, except that a styrene polymer of 
Reference Example 2 was used. 
COMATIVE EXAMPLE 4 
The procedure in Example 5 was repeated, except that the dryness of the 
sample was changed and biaxially stretched film containing 3,580 ppm of 
styrene monomer was prepared from the pellet containing 5,000 ppm of the 
styrene monomer, which was used as dielectric. 
COMATIVE EXAMPLE 5 
Lip opening of a T-die and take-off speed were controlled to obtain 
unstretched film of 12 .mu.m thickness. The procedure of example 5 was 
repeated except that the film was neither stretched nor heat treated. The 
crystallinity of the film was 14%. The film was brittle and it was 
difficult to make a condenser using this film compared with the case using 
other films. 
When the prepared condenser was heated at the temperature higher than glass 
transition temperature, for example, the film was cracked and sufficient 
characteristics were not obtained. 
COMATIVE EXAMPLE 6 
The procedure in Example 5 was repeated except that polyethylene 
terephthalate film (tetoron film, F-6, thickness; 6 .mu.m) was used. 
The results are shown in Table 2. 
TABLE 2 
__________________________________________________________________________ 
Dielectric Film Condenser Characteristics 
Mono- 
Thick- 
Dielectric Dissipation Factor 
Rate of Change in.sup.2) 
Al mer ness 
(tan .delta.) Electrostatic Capacity 
Soldering 
Example No. 
Resin.sup.1) 
(ppm) 
(ppm) 
(.mu.m) 
1 kHz/RT 
1 kHz/150.degree. C. 
10 kHz/RT 
1 kHz/150.degree. C. 
10 kHz/RT 
Test.sup.3) 
__________________________________________________________________________ 
Example 5 
SPS 880 1,200 
6 0.0012 
0.0010 0.0018 
-3 -1 .smallcircle. 
Example 6 
SPS 50 600 
6 0.0011 
0.0011 0.0017 
-3 -1 .smallcircle. 
Example 7 
SPS 50 750 
3 0.0010 
0.0010 0.0020 
-3 -1 .smallcircle. 
Example 8 
SPS 50 960 
12 0.0009 
0.0009 0.0016 
-3 -1 .smallcircle. 
Comparative 
SPS 4,500 
1,030 
6 0.003 0.002 0.003 -4 -2 x 
Example 3 
Comparative 
SPS 880 3,580 
6 0.004 0.003 0.004 -4 -2 x 
Example 4 
Comparative 
SPS 880 1,200 
12 0.0015 
Cannot be 
0.0018 
Cannot be 
-1 x 
Example 5 Measured Measured 
Comparative 
PET -- -- 6 0.003 0.003 0.005 +3 -3 x 
Example 6 
__________________________________________________________________________ 
.sup.1) SPS: Syndiotactic polystyrene, PET: Polyethylene terephthalate 
.sup.2) Rate of change (%) based on a capacity at 1 kHz at room 
temperature 
.sup.3) change in capacity after soldering at 250.degree. C. 
.smallcircle.: not exceeding 10%, x: over 10% 
PET did not function as condenser because it melted.