JPH01247445A - Resin composition for forming sheet - Google Patents

Abstract

PURPOSE:To obtain the title composition improved in modulus, heat resistance, transparency, low odor, secondary processability such as vacuum formability and impact resistance, by mixing a crystalline propylene (co)polymer with two specified ethylene (co)polymers. CONSTITUTION:The title composition of an MI of 0.1-10.0g/10min is obtained by mixing 95-45wt.% crystalline propylene (co)polymer (A) preferably comprising 75-100mol% propylene units and 0-25mol% monomer units selected from among ethylene units and linear or branched alpha-olefin units, having a xylene-soluble (20 deg.C) content <=40wt.% and containing 1-100000ppm wt. of a 6C or higher alpha-olefin branched at the position 3 or a vinylcycloalkane with 3-55wt.% ethylene (co)polymer (B) of a density of 0.950-0.890g/cc and a refractive index >= that of component A (e.g., branched low-density PE) and 2-40wt.% ethylene (co)polymer (C) having a refractive index lower than that of component A, having a refractive index of a mixture of component B and component C of -0.010-0.015 and a density of 0.890g/cc (e.g., copolymer of ethylene with an olefin).

Description

DETAILED DESCRIPTION OF THE INVENTION <Industrial Application Field> The present invention relates to a resin composition for sheet molding that has excellent elastic modulus, heat resistance, transparency, odor, and vacuum formability.

<Prior Art> Polypropylene has been widely used as a packaging material for foods, medicines, etc. because of its excellent oil resistance, elastic modulus, heat resistance, moisture resistance, etc. In particular, containers formed from sheets by secondary processing such as vacuum forming and pressure forming are economically superior and widely adopted because of their faster processing speed compared to other processing methods. However, polypropylene also has performance improvements to be made. In other words, polypropylene has higher transparency and
Poor elastic modulus, vacuum formability, and pressure formability. It also has the disadvantage of low impact strength at temperatures below room temperature.

As a method of improving the transparency and elastic modulus of polypropylene, Japanese Patent Application Laid-Open No. 58-80329 describes a method of adding aluminum salt or sodium salt of aromatic carboxylic acid,
JP-A-55-12460, JP-A-58-1290
No. 36 proposes a method of adding an aromatic carboxylic acid, an aromatic metal phosphate, a sorbitol derivative, etc. Among these methods, aromatic carboxylic acids, aromatic carboxylic hydrochloric acids, and aromatic phosphate metal salts improve transparency and elastic modulus, but to a small extent, while sorbitol derivatives have a large effect on improving transparency, but molding The value of the product is significantly reduced due to the strong odor during processing and molded products.

As a method to solve this problem, Japanese Patent Laid-Open No. 1397-1987
No. 10 proposes a method in which (a) polymerization of a vinylcycloalkane having 6 or more carbon atoms and (b) polymerization of propylene alone or copolymerized with ethylene are carried out in multiple stages. Furthermore, in JP-A-60-139731, branched α-
Crystalline polypropylene compositions containing olefins or vinylcycloalkanes have been proposed. Furthermore, JP-A-6
No. 1-21144 proposes a crystalline polypropylene sheet containing a branched α-olefin or vinylcycloalkane having 6 or more carbon atoms. These methods are excellent because transparency and elastic modulus are significantly improved and there is little odor.

On the other hand, known methods for improving impact strength include copolymerizing propylene with other α-olefins, particularly ethylene, and adding rubber-like substances. Common copolymerization methods include random copolymerization and block copolymerization, but in random copolymerization, the copolymerized α-
When the content of olefin is small, the effect of improving impact strength is small, and when the content is large, the elastic modulus decreases significantly.6 Moreover, block copolymerization method and method of adding rubbery substances do not improve impact strength. The effect is great, but the transparency is significantly reduced.

<Problem to be solved by the invention> However, JP-A-60-139710, JP-A-60-139731, JP-A-61-21144
Although the publication improves transparency, modulus of elasticity, etc., the resin composition for sheet molding is not satisfied with secondary processability such as vacuum formability and impact strength. The object of the present invention is to provide a resin composition for sheet molding that has excellent secondary processability such as hardness, odor, and vacuum formability, and impact resistance.

<Means for Solving the Problem> That is, the present invention provides a method for preparing a 3-branched α-olefin having 6 or more carbon atoms or a vinylcycloalkane with a carbon number of 1 to 100,000.
Component (A) consisting of 95 to 40 wt% of a crystalline propylene polymer or copolymer containing wt ppm, a density of 0.950 to 0.890 g/CC, and a refractive index equal to or higher than component (A). 3 to 55 wt% of component (B) of a certain ethylene polymer or copolymer and 0.890 g/c
The present invention is a sheet-molding resin composition comprising 2 to 40 wt% of component (C) of an ethylene copolymer having a refractive index of at most c and a refractive index of component (A) or less.

A method for producing a crystalline propylene polymer or copolymer containing a 3-branched a-olefin having 6 or more carbon atoms or a vinylcycloalkane polymer as component (A) is as follows: +1+ In the presence of a Ziegler-Natsuta catalyst a step of polymerizing a 3-branched α-olefin having 6 or more carbon atoms or a vinylcycloalkane or copolymerizing it with another α-olefin; a step of copolymerizing propylene alone or with another α-olefin; A method in which the step of copolymerizing propylene alone or with other α-olefins is carried out at least once.

(2) A method of mixing the polymer obtained in the above (1) with propylene alone or a copolymer with other α-olefins.

(3) a 3-branched α-olefin having carbon v16 or more, or
A polymer of vinylcycloalkane or a copolymer with other α-olefins and a homopolymer of propylene or
A method of mixing propylene with a copolymer of other α-olefins.

etc. Among these methods, methods (1) and (2) are preferable because they have a large improvement effect on transparency, elastic modulus, and heat resistance, and method (1) is most preferable because it has the largest improvement effect.

As a method for copolymerizing a 3-branched α-olefin having 6 or more carbon atoms or a vinylcycloalkane with other α-olefins, either random copolymerization or block copolymerization may be used, but block copolymerization is most effective. Therefore, particularly preferable a-olefins to be copolymerized are linear or branched α-olefins having 2 to 20 carbon atoms.

The method for producing the crystalline propylene polymer or copolymer of component (A) includes polymerizing propylene alone using a catalyst system that provides isotactic polyprolene;
It can be obtained by copolymerizing propylene, ethylene, and at least one monomer selected from linear or branched α-olefins having 4 to 10 carbon atoms. As a copolymerization method, either a random copolymerization method or a block copolymerization method can be used, but the random copolymerization method is preferable because it has a greater effect of improving transparency.

If component (A) contains a large amount of low crystallinity components, the low crystallinity components will bleed onto the surface of the molded product, impairing its commercial value.6 According to the study results of the present inventors, at 20°C. It has been found that the above problem can be solved by reducing the content of xylene soluble components to a certain value or less. That is, component (A) preferably has a xylene soluble component content of 40 wt% or less at 20°C, and 30 wt%
The following is more preferable, and 15 wt% or less is most preferable6
In order to keep the content of xylene-soluble components in component (A) at 20°C within this range, it is necessary to use a catalyst system that provides highly isotactic polypropylene as described below, and to In the crystalline propylene polymer or copolymer portion, the content of at least one monomer selected from ethylene and linear or branched α-olefins having 4 to 10 carbon atoms to be copolymerized with propylene is preferably 20%. mol% or less, more preferably 15 mol% or less,
Most preferably, this can be achieved by controlling the content to 10 mol% or less.

Specific examples of the 3-branched α-olefin or vinylcycloalkane having 6 or more carbon atoms used in the present invention are 3
．． 3-dimethylbutene-1,3-methylpentene-1,
Examples include 3-methylhexene-1,3,'5°5-trimethylhexene-1, vinylcyclopentene, vinylcyclohexane, vinylnorbornane, and the like. Among these, olefins having 8 or more carbon atoms are more preferred.

Specific examples of the 3-branched α-olefin having 6 or more carbon atoms or the vinylcycloalkane used in the present invention include 3.3-dimethylbutene-1,3-methylpentene-1
, 3-methylhexene-1,3°5.5-1-limethylhexene-1, vinylcyclopentene, vinylcyclohexane, vinylnorbornane, and the like. Among these, olefins having 8 or more carbon atoms are more preferred.

If the content of the 3-branched α-olefin having 6 or more carbon atoms or the vinylcycloalkane polymer is less than 1 ppm, the effect of improving transparency and elastic modulus will be small when processed into a sheet, and if it is more than 1,100,000 ppm. On the contrary, transparency decreases. Therefore, the content is preferably 1 to LOOOOOppm, more preferably 100 to 70,000 ppm.
m and H1t are also preferably 500 to 50,000 ppm.

The production of crystalline propylene polymers or copolymers containing a 3-branched α-olefin having 6 or more carbon atoms or a vinylcycloalkane polymer is achieved by using a catalyst system that provides isotactic propylene. You can. As a catalyst system for producing isotactic polypropylene, a Ziegler-Natsuta type catalyst system can be most preferably used. Among the Ziegler-Natsuta type catalyst systems, a solid catalyst component containing at least titanium and chlorine, an organoaluminum compound, or further,
Preferably, those consisting of electron-donating compounds, more preferably 1 when the catalyst system is polymerized for 4 hours in liquefied propylene.
The xylene soluble portion of the polymer at 20° C. is 5% by weight or less, most preferably 4% by weight or less. 1. Solid catalyst components that can be suitably used in the present invention are explained in more detail below. do.

Methods for synthesizing solid catalyst components are broadly classified into two types. One of them is a solid catalyst component obtained by reducing a tetravalent titanium compound with hydrogen, metal aluminum, an organometallic compound, etc., or a solid catalyst component obtained by further crushing and activation of these, or a solid catalyst component obtained by reducing a tetravalent titanium compound with an organometallic compound. One method is to obtain a catalyst precursor by reduction with , and then perform various activation treatments to obtain a catalyst.The other method is to support a tetravalent titanium compound on a carrier such as magnesium chloride that has been subjected to an activation treatment. This is a method to obtain a catalyst. Among the former methods, methods in which a tetravalent titanium compound is reduced with an organometallic compound and then subjected to activation treatment include a method using an organoaluminum compound as a reducing reagent and a method using an organomagnesium compound. To give specific examples, 11) A method in which a reduced solid produced by reducing TiC1 with an organoaluminum compound is treated with a complexing agent and then reacted with TiC14, (Japanese Patent Publication No. 53-335
(2) A method in which a titanium compound represented by the general formula T i (OR) n X4-nt' is reduced with an organoaluminum compound and then treated with an ether compound and TiCl4,
(Unexamined Japanese Patent Publication No. 60-228504) (3) General formula “r”
i (OR)11
(Unexamined Japanese Patent Publication No. 61-287904) +41 A method of immobilizing the catalyst component obtained in (3) on a porous substance, (Unexamined Japanese Patent Publication No. 62-256802), and the like.

The polymerization method for producing component (A) may be any one of polymerization in an inert solvent, in a liquefied monomer, or in a gas phase. Furthermore, the polymerization may be carried out by continuous polymerization, batch polymerization, or a combination thereof, and each step of polymerization may be carried out in such a way that all or part of the solvent from the previous step remains. Any of the following methods may be used: a method in which the polymerization is carried out until the end of the reaction, a method in which the polymerization is carried out after all the solvent and monomer in the previous step have been removed, or a combination of these methods.

The ethylene polymer or copolymer which is the component (B) of the present invention is a copolymer of linear ethylene and α-olefin, a branched ethylene polymer, or a copolymer with a polar monomer copolymerized with it. At least one resin composition selected from copolymers. To give a more specific example, as a linear ethylene copolymer, Ziegler
It is a copolymer of ethylene and other α-olefins that is polymerized using a Natsuta catalyst or a chromium-based catalyst, and is a hexa-branched ethylene polymer such as linear medium density polyethylene, linear low density polyethylene, etc. A copolymer with a polar monomer that can be copolymerized is generally produced by polymerizing ethylene using a radical catalyst under high pressure of 500 kg/crn' or more, or by copolymerizing ethylene with a polar monomer that can be copolymerized with ethylene. It is obtained by polymerization, and examples thereof include branched polyethylene, ethylene/vinyl acetate copolymer, ethylene/methyl methacrylate copolymer, and the like. Among these, branched ethylene polymers or copolymers of ethylene with a polar monomer copolymerized with ethylene are preferred because they have a large melt tension and can be easily vacuum formed, and branched polyethylene has good thermal stability. Therefore, it is odorless and has a good quality, which is the most preferable.

As the ethylene copolymer which is component (C) of the present invention,
It is a copolymer of ethylene and linear or branched α-olefin that is polymerized using a Ziegler-Natsuta catalyst. copolymers), etc.

The excellent transparency of the final resin composition is due to the fact that the refractive index of component (B) is higher than that of component (A) and that component (C)
This can be achieved when the refractive index of component (A) is less than or equal to that of component (A). Furthermore, when component (B) and component (C) are mixed, the refractive index of the mixture is - with respect to component (A).
Range of 0,010 to 0°015, preferably -0,005
~0.12, most preferably -o, ooo~o,
The composition of component (B) and component (C) is particularly preferred because it is possible to obtain a sheet-molding resin composition having extremely excellent transparency when the molecular size is within the range of Even if the resin composition is not uniform, a transparent resin composition of the present invention can be obtained.

In this case, the refractive index of the composition consisting of component (B) and component (C) will be a value close to the weighted average value of the refractive index of each component.

If the final resin composition has an extremely low melt index, the surface will become rough during sheet processing and transparency will decrease, which is undesirable.If the final resin composition has an extremely high melt index, it will not be suitable for secondary processing, especially vacuum forming. In the step of heating the sheet, the sheet may sag, resulting in problems such as not being able to form a uniform molded product or, in some cases, coming into contact with a heating device. Therefore, the melt index of the final resin composition is 0.1-10.0g/10
min is preferable, 0.2 to 8.0 is more preferable, and 0.3
~5°0 is most preferred.

Further, known inorganic or organic fillers and resins can be added to the resin composition of the present invention.

The method of processing the resin composition of the present invention into a sheet is not particularly limited, but extrusion molding or calendering is generally used. In particular, the extrusion molding method is preferably employed because the processing speed is generally high. There are no particular limitations on the cooling method for the extruded molten resin, but
Known methods such as a method using a cooling roll, a method using an air knife, a method using a liquid medium such as water, or a combination of these methods can be used.

Sheets generally include single-layer sheets and multi-layer sheets for the purpose of improving gas barrier properties, etc., but the resin composition of the present invention can be used as a single-layer sheet or as part of a multi-layer sheet. It can be used.

The sheet produced by the above method can be subjected to secondary processing by known processing methods such as vacuum forming and pressure forming, and can also be used as a sheet as in book binders, video cassette cases, etc.

EXAMPLES Hereinafter, the present invention will be specifically explained with reference to Examples, but the present invention is not limited by these descriptions.

The physical property values shown in the following Examples and Comparative Examples were measured by the following method.

(1) [η] Measured in tetralin at 135°C using an Ubbelohde viscometer.

(3) Melt index Measured according to JIS K6758.

(4) Press sweat epsilon It was molded according to JIS K6758.

(5) Diffuse transmitted light intensity (LSI) Measured using an LSI tester manufactured by Toyo Seiki (receives scattered transmitted light at 0.2° to 2°).

(6) Haze Measured according to ASTM DIO03.

(7) Flexural modulus Measured according to JIS K7203.

(8) Izotsu impact strength Measured according to JIS K7110.

(9) Vicat softening temperature Measured according to JIS K7206-B method.

(lO) Melt tension Using Toyo Seiki blade melt tension tester type II, L
/D=4 (D=2mm) tie, resin temperature 1
90°C, extrusion speed 0.32g/min, withdrawal speed 1
The tension applied to the monofilament was measured at a speed of 5.7 m/min.

(11) Refractive index A 0.1 mm sheet was processed by the method described in (4) and measured using an Atsbe refractometer model 2T (manufactured by Atago ■) using the sodium D line.

(Amount of xylene soluble components at 12120°C Sample 0
The sample was dissolved by adding 100 ml of xylene to 5 g of the sample and keeping it boiling for 30 minutes. The solution was then kept under stirring in a thermostatic bath kept at 20° C. for 1 hour to separate the solution, and the liquid phase was evaporated to dryness to determine the proportion of the dissolved polymer.

(13) Density Measured by JIS K7112 A method.

<Examples> Example 1-3, Comparative Example 1-3 (Synthesis of titanium trichloride solid catalyst) A titanium trichloride solid catalyst was synthesized according to the method disclosed in JP-A-60-228504. Internal volume 3 with stirrer
After purging the reactor of rn' with nitrogen, n-hexane 78
8β, titanium tetrachloride at 73°C, and tetra-n-butoxytitanium 223e were charged into the reactor and the temperature inside the reactor was maintained at 20°C while stirring. A solution consisting of n-hexane 3732 and diethylaluminum chloride 172I2 was gradually added dropwise over 4.5 hours while keeping the temperature inside the reactor at 20°C. 6 After the dropwise addition was completed, the temperature was kept at 20°C for 30 minutes.
The mixture was heated to 0° C. and stirred for 1 hour, then left to stand at room temperature to separate solid and liquid, and washed three times with n-hexane 1rrl' to obtain a solid product.

After adding n-hexane lrn' to the obtained solid product to form a slurry, diethylaluminum chloride 8.31
2 was added, the temperature was adjusted to 42°C, and 33 kg of ethylene gas was supplied over about 1 hour to obtain a prepolymerized solid.Next, after solid-liquid separation, 1rrl of n-hexane was added to form a slurry, and the temperature inside the reactor was adjusted. was maintained at 30°C. Di-isoamyl ether 267β was added to this slurry, and the slurry was heated at 30°C for 1
The temperature in the reactor was then raised to 75° C., and titanium tetrachloride 3622 was added and treated for 2 hours. After solid-liquid separation, washing was repeated four times with n-hexane 1rrf' and then flow-dried using hydrogen gas to obtain 250 kg of a titanium trichloride solid catalyst.

(Synthesis of vinylcycloalkane copolymer) 3.5β of dehydrated n-hesaquine, 165 mmol of diethylaluminum chloride, and 500 g of the above titanium trichloride solid catalyst were added to a 5I2 glass flask, and the temperature was raised to 40°C. Then, propylene was supplied so that the partial pressure was 200 mmHH to start polymerization.6 The amount of polymerization was 400 g.
Polymerization of propylene was carried out until the temperature reached 0. Then, the temperature was raised to 60°C, and 700 g of vinylcyclohexane was fed in three portions at 30 minute intervals, and then the temperature was maintained at 60°C for 2 hours to continue polymerization. The obtained polymer containing the titanium trichloride solid catalyst was washed with 1.5β of n-hexane and then dried at 40° C. under reduced pressure for 6 hours to obtain a polymer containing 1580 g of active catalyst component. . As a result of calculating the material balance, the propylene polymer is 0.8g and the vinylcyclohexane polymer is 1.3g per 1g of solid catalyst component.
This means that 6g was polymerized.

(Synthesis of crystalline polypropylene copolymer) Pressure regulated at 35°C with propylene at 10.5 kg/crn”G
, 7rr? In a stainless steel reactor equipped with a stirrer, 2.7 moles of dehydrated and purified n-hebutane, 22.5 moles of diethylaluminium chloride, and 0.24 moles of ε-caprolactone were added.
mol, and a polymer 205 containing the active catalyst component described above.
Then, the temperature was adjusted to 50℃, and after feeding 23kg of butene-1, 500kg of propylene was added.
g/hr, butene-1 was supplied at a rate of 50 kg/hr, and the pressure inside the reactor was increased to 4 kg/cm'G. After increasing the pressure, propylene and butene-1 were supplied so as to maintain the pressure inside the reactor at 4 kg/ctrl"G. During this time, the supply of propylene and butene-1 was changed to propylene/butene-1.
During zero polymerization, the hydrogen concentration in the gas phase of the reactor was maintained at 110.045 (weight ratio) at approximately 0.75 vol.
It was kept at 1%. When the amount of propylene supplied reached 902 kg, the monomer supply was stopped.

When the pressure inside the reactor reached 2 kg/crn', the slurry containing the polymer was transferred to a cleaning tank with an internal volume of 20 rn' and replaced with nitrogen, and 2.4 rn' of n-hebutane and n-
Polymerization was stopped by adding 85 ρ of butanol.

After stirring at 60°C for 1 hour, 1.2 g of water was added and KOF was added so that the pH of the aqueous phase was 11.
Stir for 30 minutes at ~55°C. Then, stirring was stopped, the aqueous phase was separated and removed, and the remaining heptane slurry was decanted.
The recovered polymer cake, which was subjected to solid-liquid separation, was dried with hot nitrogen at 70 to 80° C. for about 30 hours to obtain 850 kg of white polymer. Polymer rnl is 3.
20dl/g, butene-1 content is 6.0, and polyvinylcyclohexane polymer content is 11038pp.
, the amount of components soluble in xylene at 20℃ is 1.9w
It was t%.

(Preparation of resin composition) The crystalline polypropylene copolymer synthesized by the above method as component (A) was mixed with the crystalline polypropylene copolymer synthesized by the above method as component (B) with a density of 0.
919 g/cc, melt index 0.9 g/10 min branched low density polyethylene and component (C) density 0.868 g/cc, melt index 0.7 g/1
An ethylene butene-1 rubber-like polymer having a 0.0 minute content was blended with the composition shown in Table 1, melt-kneaded using a 65 mmφ extruder, extruded into a strand, and then pelletized. In order to prevent other deterioration of the resin during melt cross-talk, 0.05 parts of potassium stearate and Tris (
023 parts of 2,4-di-tert-butylphenyl) phosphite and 0.18 parts of tetra[methylene-3-(3,5-diter-butyl-4-hydroxyphenyl) propionate comethane] were added.

The obtained pellets were molded into a sheet using a hot press molding machine, and the physical properties were measured.The results are shown in Table 2.

Also, the obtained pellet was 65 mm with a T”J die installed.
The results of measuring the physical properties of the molded product obtained by sheet molding using a φ extruder are shown in Table 2. The sheet molding was performed under the following conditions.

Cooling method: Air knife method Die width: 600mm Resin temperature: Approximately 290°C Roll temperature First roll: 60°C Second roll: 2Q”C Roll speed: 1.5m/min As a result of measuring the refractive index of each resin component, The crystalline polypropylene copolymer had a molecular weight of 1,501, the branched low density polyethylene had a molecular weight of 1.515, and the ethylene/butene-1 rubbery polymer had a molecular weight of 1.483.

In the resin compositions of Examples 1 and 2, component (B) and component (C
) In order to determine the refractive index of the mixture, branched low-density polyethylene and ethylene/butene-1 rubbery copolymer were melt-kneaded in the composition corresponding to each example, and then the refractive index of the mixture was measured. did.

The refractive index is 1508.1.504.1°510 respectively.
and the difference in refractive index for the crystalline polypropylene copolymer is 0.007, 0.004, and 0.009, respectively.
Met.

\ Table 2 Table 3 Comparative Example 4-5 Crystalline polypropylene polymer having [η] of 3.30 parts g/g as component (A) and a xylene soluble portion at 20°C of 3.9 wt% , density 0 as component (B)
．． 919g/cc, melt index 0.9g/10
Branched low-density polyethylene was blended with the composition shown in Table 4, and the mixture was melt-kneaded using an extruder and pelletized. In order to prevent thermal deterioration of the resin during melt cross-contact,
0.05 parts of calcium stearate, 0.05 parts of tris(2,4-ditertibutylphenylphite)
．． 23 ffl and 0.08 part of tetra[methylene-3-(3,5-ditertiarybutyl-4-hydroxyphenyl)propionate]methane were added. The obtained pellets were press-molded and extruded into sheets under the same conditions as in the above example. The results of measuring the physical properties of the obtained molded products are shown in Tables 5 and 6.

Table 4 Results of measuring the refractive index of crystalline polypropylene polymer,
It was 1.503.

Table 5 Table 6 Comparative Example 1 is a composition containing only component (A) consisting of a crystalline propylene copolymer containing the 3-branched a-olefin having 6 or more carbon atoms or the vinylcycloalkane of the present invention. However, it can be seen that the transparency was extremely excellent compared to the case of the ordinary crystalline propylene polymer shown in Comparative Example 4. Furthermore, even though butene-1 was copolymerized in the process of polymerizing crystalline propylene, the flexural modulus and Vicat softening temperature were excellent, with no color retention, compared to the propylene homopolymer of Comparative Example 4. It is. However, the melt tension, which is a measure of vacuum formability, is low, and the isot impact strength has not been improved in any way.

It can be seen from Tables 2 and 3 that Examples 1 to 3 have improved melt tension and impact strength without impairing the transparency of Comparative Example 1. Furthermore, Examples 1 to 3 are Comparative Example 1
Although its flexural modulus and Vicat softening temperature are slightly lower than that of polypropylene, it maintains the excellent level inherent to polypropylene.

Comparative Example 2 is a system in which component (B) is added to component (A), but it is inferior to the examples in terms of transparency and impact strength. Comparative Example 3 is a system in which component (C) is added to component (A), but the transparency is inferior to that of the example. Comparative Example 5 is a system in which component (B) is added to ordinary crystalline polypropylene, but its transparency and impact strength are poor.

<Effect of the invention> Component (A) consisting of a crystalline propylene polymer or copolymer containing a 3-branched α-olefin having 6 or more carbon atoms or a vinylcycloalkane, and a density of 0.950.
Component (B) of an ethylene polymer or copolymer having a refractive index of 0-890 g/cc or higher than component (A), and a component (B) of an ethylene polymer or copolymer having a density of 0,890 g/cc or lower and a refractive index of The composition is composed of component (C) of an ethylene copolymer having a composition equal to or less than that of component (A), and has the composition specified in the present invention, and has good transparency, elastic modulus, thermal properties, and low odor. This is a resin composition for sheet molding that exhibits excellent properties such as hardness, melt tension, and impact strength.

Claims (6)

[Claims] (1) Component (A) consisting of 95 to 40 wt% of a crystalline propylene polymer or copolymer containing 1 to 100,000 wtppm of a 3-branched α-olefin having 6 or more carbon atoms or a vinylcycloalkane, and a density of 0 .950~
An ethylene polymer or copolymer component having a refractive index of 0.890 g/cc and higher than component (A) (
B) 3 to 55 wt%, and 2 to 40 wt% of component (C) of an ethylene copolymer having a density of 0.890 g/cc or less and a refractive index of component (A) or less. A resin composition for sheet molding. (2) The crystalline propylene polymer or copolymer of component (A) contains 75 to 100 mol% of propylene units, and at least one kind selected from ethylene and a linear or branched α-olefin having 4 to 10 carbon atoms. 0 monomer units
25 mol %, and the amount of component (A) soluble in xylene at 20° C. is 40 wt % or less. (3) The resin composition for sheet molding according to claim 1, wherein component (B) is branched low-density polyethylene. (4) The resin composition for sheet molding according to claim 1, wherein component (C) is a copolymer of ethylene and α-olefin. (5) The resin composition for sheet molding according to claim 1, wherein the refractive index of the mixture of component (B) and component (C) with respect to component (A) is in the range of -0.010 to 0.015. (6) The melt index of the composition is 0.1 to 10.
The resin composition for sheet molding according to claim 1, which has a yield of 0 g/10 minutes.