JP2007039490A - Fluidity improver, aromatic polycarbonate resin composition and molded product - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a fluidity improver improving the melt fluidity of an aromatic polycarbonate resin composition and chemical resistance of a molded product without deteriorating heat, peeling and impact resistances, transparency, etc., of the molded product of the aromatic polycarbonate resin. <P>SOLUTION: The aromatic polycarbonate resin composition is prepared by compounding 92.5 pts.mass of the aromatic polycarbonate resin with 7.5 pts.mass of the fluidity improver. In the resin composition, the fluidity improver satisfying the relationships of the absolute value of (n<SB>PC</SB>-n<SB>P</SB>)≤0.01, 0.01 μm≤dv≤0.3 μm and SPL≥1.2 L<SB>PC</SB>(wherein, n<SB>PC</SB>is the refractive index of the aromatic polycarbonate resin; n<SB>P</SB>is the refractive index of the fluidity improver; dv is the volume-average domain diameter of the fluidity improver dispersed in a matrix of the aromatic polycarbonate resin; SPL is the spiral flow length of the resin composition; and L<SB>PC</SB>is the spiral flow length of the aromatic polycarbonate resin) is used. <P>COPYRIGHT: (C)2007,JPO&INPIT

Description

  The present invention relates to a fluidity improver for an aromatic polycarbonate resin, an aromatic polycarbonate resin composition in which the fluidity improver is blended, and a molded article formed by molding the resin composition.

  Since molded products of aromatic polycarbonate resin are excellent in mechanical strength, heat resistance, electrical properties, dimensional stability, etc., OA (office automation) equipment, information / communication equipment, electronic / electric equipment, home appliances, Used in a wide range of fields such as automobiles and architecture. However, since the aromatic polycarbonate resin is amorphous, it has the following problems: (i) high molding processing temperature, poor melt fluidity, and (ii) poor chemical resistance.

  In recent years, molded products of aromatic polycarbonate resins have become larger, thinner, more complicated in shape and higher in performance, and with the growing interest in environmental issues, the molded products of aromatic polycarbonate resins have become superior. There is a need for a resin modifier (hereinafter referred to as a fluidity improver) that improves the melt fluidity of an aromatic polycarbonate resin and improves injection moldability without impairing properties, and a resin composition using the same. It has been.

The following methods are known as methods for improving the melt fluidity of an aromatic polycarbonate resin composition without impairing the properties (transparency, heat resistance, etc.) of the molded product of the aromatic polycarbonate resin.
(1) A method for reducing the molecular weight of an aromatic polycarbonate resin itself, which is a matrix resin.
(2) A method of polymerizing an aromatic polycarbonate resin and a specific styrene resin (for example, Patent Documents 1 and 2).
(3) A method of polymerizing an aromatic polycarbonate resin and a specific methacrylate resin (for example, Patent Document 3).
(4) A method of adding an aromatic vinyl resin having a polar group, which falls within a specific solubility parameter range, to an aromatic polycarbonate resin (for example, Patent Document 4).

However, these conventional methods have the following problems although the melt fluidity is improved to some extent.
In the method (1), although the melt fluidity is greatly improved, a decrease in molecular weight more than necessary impairs the heat resistance, chemical resistance and impact resistance of the molded product. Therefore, there is a limit to improving the melt fluidity of the aromatic polycarbonate resin composition by reducing the molecular weight of the aromatic polycarbonate resin while maintaining the excellent characteristics of the molded product.

  In the methods (2) to (4), the balance between the peel resistance of the molded product, the transparency, and the melt fluidity of the aromatic polycarbonate resin composition is still insufficient. Specifically, although the method (2) is excellent in the melt flowability of the aromatic polycarbonate resin composition, the compatibility is still insufficient, so that the molded product tends to peel off, and the appearance and mechanical strength are large. descend. The method (3) is excellent in the compatibility of the aromatic polycarbonate resin composition and the transparency of the molded product is good, but the effect of improving the melt fluidity of the aromatic polycarbonate resin composition is small. Therefore, in order to improve the melt fluidity, it is necessary to increase the amount of the methacrylate resin, and while maintaining the heat resistance, impact resistance, etc. of the molded product, the melt fluidity of the aromatic polycarbonate resin composition There are limits to improving

  As described above, in the methods (2) to (4), the melt fluidity of the aromatic polycarbonate resin composition is improved by adding the fluidity improver, but the surface layer peeling and the domain size of the fluidity improver are observed. It has been difficult to obtain molded products that satisfy the specifications required for optical materials such as headlamp lenses or light guide plates that place importance on transparency, due to the enlargement of layers and the layered structure of domains. .

The following methods can be considered as methods for increasing the domain size of the fluidity improver and improving the layered structure of the domain.
(5) A method of adding a polymer that stabilizes the interface between the fluidity improver and the aromatic polycarbonate resin (for example, Patent Documents 5 and 6).
However, the method (5) has not yet achieved both the transparency of the molded product and the melt fluidity of the aromatic polycarbonate resin composition.
As described above, any of the conventional methods is still insufficient in terms of improving the melt fluidity of the aromatic polycarbonate resin composition without impairing the excellent characteristics of the molded product.
Japanese Patent Publication No.59-42024 JP-A-62-138514 Japanese Patent No. 2622152 Japanese Patent Laid-Open No. 11-181197 JP 2001-172491 A JP 2003-147030 A

  The object of the present invention is to provide the melt fluidity (molding processability) and molding of an aromatic polycarbonate resin composition without impairing the heat resistance, peel resistance, impact resistance, transparency, etc. of the molded article of the aromatic polycarbonate resin. A fluidity improver that improves the chemical resistance of the product; it is possible to obtain molded products with excellent heat resistance, peel resistance, impact resistance, transparency, chemical resistance, etc., and melt fluidity (molding processability) It is an object of the present invention to provide an aromatic polycarbonate resin composition excellent in heat resistance, and a molded product excellent in heat resistance, peel resistance, impact resistance, transparency, chemical resistance and the like.

The fluidity improver of the present invention is represented by the following formulas (1-1) to (1-3) about a resin composition in which 7.5 parts by mass of a fluidity improver is blended with 92.5 parts by mass of an aromatic polycarbonate resin. It is characterized by satisfying the relationship.
| N _PC −n _P | ≦ 0.01 (1-1)
0.01 μm ≦ dv ≦ 0.3 μm (1-2)
SPL ≧ 1.2L _PC (1-3)
(Where n _PC is the refractive index of the aromatic polycarbonate resin, n _P is the refractive index of the flow improver, and dv is the volume average domain diameter of the flow improver dispersed in the matrix of the aromatic polycarbonate resin. , SPL is the spiral flow length of the resin composition, L _PC is a spiral flow length of the aromatic polycarbonate resin.)

The fluidity improver of the present invention preferably contains a polymer (Z) obtained by polymerizing an unsaturated monomer in the presence of a macromonomer compatible with the aromatic polycarbonate resin.
The aromatic polycarbonate resin composition of the present invention contains an aromatic polycarbonate resin and the fluidity improver of the present invention.
The molded article of the present invention is formed by molding the aromatic polycarbonate resin composition of the present invention.

The fluidity improver of the present invention is a melt fluidity (molding processability) of an aromatic polycarbonate resin composition without impairing the heat resistance, peel resistance, impact resistance, transparency, etc. of the molded article of the aromatic polycarbonate resin. ) And chemical resistance of the molded product.
The aromatic polycarbonate resin composition of the present invention can provide a molded product excellent in heat resistance, peel resistance, impact resistance, transparency, chemical resistance, etc., and is excellent in melt fluidity (molding processability). .
The molded article of the present invention is excellent in heat resistance, peel resistance, impact resistance, transparency, chemical resistance, and the like.

<Fluidity improver>
The fluidity improver of the present invention is represented by the following formulas (1-1) to (1-3) about a resin composition in which 7.5 parts by mass of a fluidity improver is blended with 92.5 parts by mass of an aromatic polycarbonate resin. Satisfy the relationship.
| N _PC −n _P | ≦ 0.01 (1-1)
0.01 μm ≦ dv ≦ 0.3 μm (1-2)
SPL ≧ 1.2L _PC (1-3)
(Where n _PC is the refractive index of the aromatic polycarbonate resin, n _P is the refractive index of the flow improver, and dv is the volume average domain diameter of the flow improver dispersed in the matrix of the aromatic polycarbonate resin. , SPL is the spiral flow length of the resin composition, L _PC is a spiral flow length of the aromatic polycarbonate resin.)

  The aromatic polycarbonate resin used for the measurement of refractive index, volume average domain diameter, and spiral flow length is an aromatic polycarbonate resin to which a fluidity improver is to be blended when preparing the target aromatic polycarbonate resin composition. To do.

(Refractive index)
The difference (absolute value) between the refractive index n _{PC of the} aromatic polycarbonate resin (matrix) and the refractive index n _P of the fluidity improver (domain) is 0.01 or less. By setting the difference (absolute value) between the refractive index n _PC and the refractive index n _P within this range, the transparency of the molded product becomes a sufficient level. When the difference (absolute value) between the refractive index n _PC and the refractive index n _P exceeds 0.01, light scattering occurs, and the molded article has deteriorated transmittance and haze, and the performance is greatly reduced. .
When used for an optical material such as a headlamp lens or a light guide plate where transparency is regarded as important, the difference (absolute value) between the refractive index n _PC and the refractive index n _P is preferably 0.005 or less, 0.001 The following is more preferable.
The refractive index is measured in accordance with JIS K7142 using an Abbe refractometer.

(Volume average domain diameter)
The volume average domain diameter dv of the fluidity improver dispersed in the matrix of the aromatic polycarbonate resin is 0.01 to 0.3 μm. By setting the volume average domain diameter dv within this range, both the transparency of the molded product and the melt fluidity of the aromatic polycarbonate resin composition can be achieved. When the volume average domain diameter dv is less than 0.01 μm, there is no significant difference from the conventional methods for improving the melt fluidity, such as a method for reducing the molecular weight of the aromatic polycarbonate resin and a method for introducing a plasticizer. . Further, the impact resistance and heat resistance of the molded product are lowered as seen when a plasticizer is blended with the aromatic polycarbonate resin. When the volume domain diameter dv exceeds 0.3 μm, the impact resistance of the molded product is lowered, the surface layer is peeled off, and the like. In addition, speculation required for optical materials such as headlamp lenses or light guide plates that place importance on transparency, as the fluidity improver increases the domain size and the layered structure of the domain causes light scattering. It becomes difficult to clear.

When importance is attached to impact resistance, transparency, etc., the volume average domain diameter dv is preferably 0.25 μm or less, more preferably 0.2 μm or less, and further preferably 0.15 μm or less. Further, the volume average domain diameter dv is preferably 0.05 μm or more, more preferably 0.07 μm or more, and further preferably 0.1 μm or more.
The volume average domain diameter dv is determined by taking a TEM photograph of the resin composition using a transmission electron microscope (hereinafter referred to as “TEM”) and analyzing the photograph.

A sample of a resin composition used for taking a TEM photograph is prepared as follows.
Using an injection molding machine (“IS-100”, manufactured by Toshiba Machine Co., Ltd.), a flat molded product having a thickness of 2 mm and a length and width of 50 mm is produced under conditions of a molding temperature of 280 ° C. and a mold temperature of 80 ° C. . From the center of the molded product, slices were cut out with a freezing microtome, and the slices were stained with ruthenium tetroxide, osmium tetroxide, chlorosulfonic acid, uranyl acetate, phosphotungstic acid, iodine ions, trifluoroacetic acid and the like. Use to stain and obtain a sample. As the staining agent, an optimal one is selected according to the type of functional group contained in the resin composition. As the staining agent in the present invention, ruthenium tetroxide and osmium tetroxide are suitable.

A TEM photograph (for example, magnification: 5000 times) of the obtained sample is taken using TEM.
The volume average domain diameter dv is determined by image analysis of a TEM photograph. For image analysis, for example, Image-ProPlus Ver. 4.0 for Windows (registered trademark) or the like is used. From the image analysis, the area R _j (j = 1 to n) of each domain is obtained for all the domains (n) in the TEM photograph, and the area of the domain is converted into a perfect circle by the following formula (2). The diameter (d _j ) is calculated, and the volume average domain diameter dv is calculated from the diameter (d _j ) according to the following formula (3). Specifically, J. et al. MACROMOL. SCI. -PHYS. , B38 (5 & 6), 527 (1999).

  In addition, since the flow is applied to the obtained sample by injection molding, the domains (fluidity improvers) in the sample are oriented in the flow direction. Therefore, anisotropy may occur in the volume average domain diameter dv obtained by image analysis of the TEM photograph. Therefore, in the present invention, the surface of the thin piece used for taking the TEM photograph is a surface orthogonal to the flow direction.

(Spiral flow length)
The spiral flow length (SPL) of the resin composition needs to be 1.2 times or more longer than the spiral flow length (L _PC ) of the aromatic polycarbonate resin, preferably 1.3 times or more. More preferably, it is twice or more longer. If SPL is not more than 1.2 times longer L _PC, and melt fluidity of the aromatic polycarbonate resin composition, the impact resistance of the molded article, with respect to the balance between the transparency, low molecular weight molecular weight of the aromatic polycarbonate resin There is no significant difference from the conventional methods for improving melt fluidity such as the method of plasticizing and the method of introducing a plasticizer, and the increase in size, thickness, and shape of the molded product required in recent years is achieved. Therefore, it is not a fluidity improver that can achieve injection moldability.

  The spiral flow length is measured using an injection molding machine (“IS-100”, manufactured by Toshiba Machine Co., Ltd.). The molding conditions are: molding temperature: 280 ° C., mold temperature: 80 ° C., injection pressure: 98 MPa, the thickness of the molded product is 2 mm, and the width is 15 mm.

(Polymer (Z))
As the fluidity improver, those containing a polymer (Z) obtained by polymerizing an unsaturated monomer in the presence of a macromonomer compatible with the aromatic polycarbonate resin are preferable. When the fluidity improver contains the polymer (Z), the relationship between the above formulas (1-1) to (1-3) is satisfied, and a headlamp lens, a light guide plate, etc. in which transparency is important. An aromatic polycarbonate resin composition and a molded article suitable for optical materials are obtained.
The polymer (Z) stabilizes the interface between the aromatic polycarbonate resin and the fluidity improver, and does not deteriorate the excellent properties of the aromatic polycarbonate resin. It improves the properties and the like.

  The content of the macromonomer in the polymer (Z) is preferably 5 to 95% by mass in the polymer (Z) (100% by mass). When the content of the macromonomer is less than 5% by mass, the volume domain diameter is increased, the domain size of the fluidity improver is increased, the layered structure of the domain is caused, and the transparency and mechanical strength tend to decrease. . When the content of the macromonomer exceeds 95% by mass, it is excessively compatible with the aromatic polycarbonate, and the fluidity tends to be lowered.

(Macromonomer)
A macromonomer is a polymer having a polymerizable functional group and is also called a macromer.
The “macromonomer compatible with the aromatic polycarbonate resin” in the present invention is a resin composition in which 95 parts by mass of the aromatic polycarbonate resin is mixed with 5 parts by mass of the macromonomer and is dispersed in the matrix of the aromatic polycarbonate resin. It means that no phase separation is observed when the volume average domain diameter dv of the macromonomer is 0.05 μm or more. The volume average domain diameter dv is measured in the same manner as described above. In addition, the aromatic polycarbonate resin used for the measurement of the volume average domain diameter is an aromatic polycarbonate resin to which a fluidity improver is to be blended when preparing the target aromatic polycarbonate resin composition.

  Examples of the macromonomer include those containing a monomer unit composed of a radical polymerizable monomer and represented by the following formula.

Wherein n is an integer, W is COOH (and its metal salt), COOR, CN, CONH ₂ , CONHR, or CONR ₂ ; S is H or R; T is COOH (and its metal salt), COOR, CN, CONH ₂ , CONHR, or CONR ₂ ; R represents an optional substituent; Q represents a hydrogen atom or a substituent derived from an initiator.

The macromonomer compatible with the aromatic polycarbonate resin is preferably a copolymer of styrene and phenyl methacrylate containing 90% by mass or more of phenyl methacrylate units.
The mass average molecular weight of the macromonomer is preferably 3000 to 100,000, and more preferably 5,000 to 50,000.

  The macromonomer can be produced by a known method. The production method is not particularly limited, but from the viewpoint of economics of the production process, for example, a production method using a cobalt chain transfer agent (for example, US Pat. No. 4,680,352), α-substitution such as α-bromomethylstyrene A method of using an unsaturated compound as a chain transfer agent (for example, WO 88/04304 pamphlet), a method of chemically bonding a polymerizable group (for example, JP-A-60-133007, US Pat. No. 5,147,952) ), A method by thermal decomposition (for example, JP-A-11-240854) is preferable.

(Unsaturated monomer)
The unsaturated monomer to be polymerized in the presence of the macromonomer includes (i) an unsaturated monomer (a) that satisfies the relationship of the following formula (4) and an unsaturated monomer that satisfies the relationship of the following formula (5). A mixture with a saturated monomer (b) (hereinafter referred to as an unsaturated monomer mixture (i)), or (ii) an unsaturated monomer (c) that satisfies the relationship of the following formula (6): A mixture with an unsaturated monomer (d) that satisfies the relationship of the following formula (7) (hereinafter referred to as an unsaturated monomer mixture (ii)) is preferred.
η _a ≦ η _PC and n _a ≧ n _PC (4)
η _b ≧ η _PC and n _b ≦ n _PC (5)
η _c ≧ η _PC and n _c ≧ n _PC (6)
η _d ≦ η _PC and n _d ≦ n _PC (7)

(Wherein η _PC is the solubility parameter of the aromatic polycarbonate resin, n _PC is the refractive index of the aromatic polycarbonate resin, η _a is the solubility parameter of the homopolymer comprising the unsaturated monomer (a), η _b is the solubility parameter of the homopolymer consisting of the unsaturated monomer (b), η _c is the solubility parameter of the homopolymer consisting of the unsaturated monomer (c), and η _d is the unsaturated monomer solubility parameter of the homopolymer consisting body (d), n _a is the refractive index of the homopolymer consisting unsaturated monomer (a), n _b is a homopolymer consisting of unsaturated monomer (b) refractive index, n _c is the refractive index of the homopolymer consisting unsaturated monomer (c), n _d is the refractive index of the homopolymer consisting unsaturated monomer (d).)

Solubility parameters are described by Joseph Bicerand, “Prediction of Polymer Properties”, p. The value of Fedors-type in the method described in 104-128 is used. Further, the solubility parameter can be easily determined by software “Cynthia” of Accelrys.
The refractive index is measured in accordance with JIS K7142 using an Abbe refractometer.

Examples of the unsaturated monomer (a) include styrene and α-methylstyrene. These may be used alone or in combination of two or more.
Examples of the unsaturated monomer (b) include phenyl methacrylate, acrylonitrile, acrylamide, methacrylamide, acrylic acid, methacrylic acid, 2-hydroxypropyl acrylate, 2-hydroxypropyl methacrylate, glycidyl methacrylate, methyl acrylate, dimethylaminoethyl methacrylate, etc. Is mentioned. These may be used alone or in combination of two or more.

Examples of the unsaturated monomer (c) include vinylidene chloride and p-chlorostyrene. These may be used alone or in combination of two or more.
Examples of the unsaturated monomer (d) include benzyl methacrylate, cyclohexyl acrylate, cyclohexyl methacrylate, 3,3,5-trimethylcyclohexyl methacrylate, isobornyl acrylate, isobornyl methacrylate, methyl methacrylate, pt-butylstyrene, etc. Is mentioned. These may be used alone or in combination of two or more.

(Polymer (X))
The unsaturated monomer mixture (i) is a polymer having a mass average molecular weight of 40,000 to 100,000 obtained by polymerizing the unsaturated monomer mixture (i) (hereinafter referred to as polymer (X)). However, with respect to the resin composition in which the glass transition temperature is 100 ° C. or higher and 92.5 parts by mass of the aromatic polycarbonate resin is blended with 7.5 parts by mass of the polymer (X), the following formulas (8-1) to (8) The unsaturated monomer mixture that satisfies the relationship -3) is preferable.
| N _PC −n _PX | ≦ 0.01 (8-1)
0.01 μm ≦ dv ≦ 0.5 μm (8-2)
SPL ≧ 1.2L _PC (8-3)
(Where n _PC is the refractive index of the aromatic polycarbonate resin, n _PX is the refractive index of the polymer (X), and dv is the volume average of the polymer (X) dispersed in the matrix of the aromatic polycarbonate resin. domain diameter, SPL is the spiral flow length of the resin composition, L _PC is a spiral flow length of the aromatic polycarbonate resin.)

The glass transition temperature refers to the peak of the loss modulus G ″ obtained by the viscoelasticity measurement method.
The refractive index is measured in accordance with JIS K7142 using an Abbe refractometer.
The volume average domain diameter dv and spiral flow length are measured in the same manner as described above. The aromatic polycarbonate resin used for the measurement of refractive index, volume average domain diameter, and spiral flow length is an aromatic polycarbonate to which a fluidity improver is blended when preparing the desired aromatic polycarbonate resin composition. Resin.

By satisfying the relationship of the formula (8-1), the transparency of the molded product becomes a sufficient level.
By satisfying the relationship of the formula (8-2), the dispersibility of the incompatible domain of the fluidity improver (including the polymer (X)) in the matrix of the aromatic polycarbonate resin is improved. The balance between transparency and the melt fluidity of the aromatic polycarbonate resin composition is improved.
By satisfying the relationship of the formula (8-3), the balance between the melt fluidity of the aromatic polycarbonate resin composition, the impact resistance of the molded product, and the transparency is improved.

  As a combination of the unsaturated monomer (a) and the unsaturated monomer (b) satisfying the relationships of the formulas (8-1) to (8-3), a combination of styrene and phenyl methacrylate is preferable. Content of the styrene unit in polymer (X) should just be content which satisfies the relationship of Formula (8-1)-(8-3), and 40 in polymer (X) (100 mass%). ˜99.5 mass% is preferred. If the content of the styrene unit exceeds 99.5% by mass, the compatibility between the fluidity improver and the aromatic polycarbonate resin becomes insufficient, resulting in a decrease in the peel resistance of the molded product. As a result, the molded article may cause delamination and impair mechanical properties. If the content of styrene units is less than 40% by mass, the compatibility between the fluidity improver and the aromatic polycarbonate resin becomes excessive, and does not exhibit sufficient phase separation behavior during melt-kneading and tends to lower the melt fluidity. At the same time, the chemical resistance of the molded product may be insufficient.

  The combination of the unsaturated monomer (a) and the unsaturated monomer (b) is preferably a combination of styrene and an unsaturated monomer containing a polar group. A combination is more preferred. In this case, content of the styrene unit in polymer (X) should just be content which satisfies the relationship of Formula (8-1)-(8-3), and 80-99.5 mass% is preferable. . If the content of the styrene unit exceeds 99.5% by mass, the compatibility between the fluidity improver and the aromatic polycarbonate resin becomes insufficient, resulting in a decrease in the peel resistance of the molded product. As a result, the molded article may cause delamination and impair mechanical properties. When the content of the styrene unit is less than 80% by mass, the difference in the refractive index (absolute value) between the fluidity improver and the aromatic polycarbonate resin becomes larger than 0.01, so that the transparency is lowered.

(Polymer (Y))
The unsaturated monomer mixture (ii) is a polymer having a mass average molecular weight of 40,000 to 100,000 obtained by polymerizing the unsaturated monomer mixture (ii) (hereinafter referred to as polymer (Y)). However, a resin composition in which the glass transition temperature is 100 ° C. or higher and 7.5 parts by mass of the polymer (Y) is blended with 92.5 parts by mass of the aromatic polycarbonate resin is represented by the following formulas (9-1) to (9). The unsaturated monomer mixture that satisfies the relationship -3) is preferable.
| N _PC −n _PY | ≦ 0.01 (9-1)
0.01 μm ≦ dv ≦ 0.5 μm (9-2)
SPL ≧ 1.2L _PC (9-3)
(Where n _PC is the refractive index of the aromatic polycarbonate resin, n _PY is the refractive index of the polymer (Y), dv is the volume average of the polymer (Y) dispersed in the matrix of the aromatic polycarbonate resin) domain diameter, SPL is the spiral flow length of the resin composition, L _PC is a spiral flow length of the aromatic polycarbonate resin.)

The glass transition temperature refers to the peak of the loss modulus G ″ obtained by the viscoelasticity measurement method.
The refractive index is measured in accordance with JIS K7142 using an Abbe refractometer.
The volume average domain diameter dv and spiral flow length are measured in the same manner as described above. The aromatic polycarbonate resin used for the measurement of refractive index, volume average domain diameter, and spiral flow length is an aromatic polycarbonate to which a fluidity improver is blended when preparing the desired aromatic polycarbonate resin composition. Resin.

By satisfying the relationship of the formula (9-1), the transparency of the molded product becomes a sufficient level.
By satisfying the relationship of the formula (9-2), the dispersibility of the incompatible domain of the fluidity improver (including the polymer (Y)) in the matrix of the aromatic polycarbonate resin is improved. The balance between transparency and the melt fluidity of the aromatic polycarbonate resin composition is improved.
By satisfying the relationship of the formula (9-3), the balance between the melt fluidity of the aromatic polycarbonate resin composition, the impact resistance of the molded product, and the transparency is improved.

  As a combination of the unsaturated monomer (c) and the unsaturated monomer (d) satisfying the relationship of the formulas (9-1) to (9-3), p-chlorostyrene and pt-butyl A combination with styrene is preferred. Content of the pt-butyl styrene unit in a polymer (Y) should just be content which satisfies the relationship of Formula (9-1)-(9-3), and polymer (Y) (100 20-30 mass% is preferable in the mass%). When the content of the pt-butylstyrene unit is outside the range of 20 to 30% by mass, the difference (absolute value) in the refractive index between the fluidity improver and the aromatic polycarbonate resin is greater than 0.01. Transparency decreases.

(Composition of fluidity improver)
The fluidity improver stabilizes the interface between the aromatic polycarbonate resin and the fluidity improver in order to improve the melt fluidity and chemical resistance of the molded product without degrading the excellent properties of the aromatic polycarbonate resin. It is preferable that the polymer (Z) to be converted is included. As for content of a polymer (Z), 10-100 mass% is preferable in a fluid improvement agent (100 mass%).

  Moreover, the melt fluidity | liquidity of an aromatic polycarbonate resin composition can be improved greatly by using a polymer (Z) and a polymer (X) or a polymer (Y) together if necessary. The blending ratio of the polymer (X) or the polymer (Y) and the polymer (Z) is preferably such a ratio that satisfies the relationship of the above formulas (1-1) to (1-3). X) or polymer (Y) 50-99.5 parts by mass, polymer (Z) 0.5-50 parts by mass (the total of polymer (X) or polymer (Y) and polymer (Z) is 100 parts by mass) is particularly preferred. When the blending ratio of the polymer (Z) is less than 0.5 parts by mass, the dispersibility of the incompatible domain is not reduced, and the relations of the above formulas (1-1) to (1-3) are satisfied. May not. When the blending ratio of the polymer (Z) exceeds 50 parts by mass, if the polymer (X) or the polymer (Y) has a higher melt fluidity than the polymer (Z), the aromatic polycarbonate resin composition There is a risk of impairing melt fluidity. The total content of the polymer (X) or the polymer (Y) and the polymer (Z) is preferably 75 to 100% by mass in the fluidity improver (100% by mass).

<Aromatic polycarbonate resin composition>
The aromatic polycarbonate resin composition of the present invention contains an aromatic polycarbonate resin and the fluidity improver of the present invention.

  The blending ratio of the aromatic polycarbonate resin and the fluidity improver is preferably a ratio that satisfies the relationships of the above formulas (1-1) to (1-3). In order to improve the melt fluidity and chemical resistance of the molded product without deteriorating the excellent properties of the aromatic polycarbonate resin, 80 to 99.5 parts by mass of the aromatic polycarbonate resin, 0.5 to 0.5 20 parts by mass (the total of the aromatic polycarbonate resin and the fluidity improver is 100 parts by mass) is preferable. If the blending ratio of the fluidity improver is less than 0.5 parts by mass, the blending effect may not be sufficiently obtained. If the blending ratio of the fluidity improver exceeds 20 parts by mass, among the excellent properties of the aromatic polycarbonate resin, particularly mechanical properties may be impaired. The blending ratio of the fluidity improver is preferably 0.5 parts by mass or more, more preferably 1 part by mass or more, further preferably 2 parts by mass or more, and particularly preferably 3 parts by mass or more. Moreover, 20 mass parts or less are preferable, as for the mixture ratio of a fluid improvement agent, 15 mass parts or less are more preferable, and 10 mass parts or less are more preferable.

(Aromatic polycarbonate resin)
Examples of the aromatic polycarbonate resin include 4,4′-dioxydiarylalkane-based polycarbonates such as 2,2-bis (4-hydroxyphenyl) propane (ie, bisphenol A) polycarbonate.
The molecular weight of the aromatic polycarbonate resin may be appropriately determined as desired, and is not particularly limited.

  The aromatic polycarbonate resin can be produced by various conventionally known methods. For example, when producing 2,2-bis (4-hydroxyphenyl) propane-based polycarbonate, (i) 2,2-bis (4-hydroxyphenyl) propane is used as a raw material, and phosgene is present in the presence of an alkaline aqueous solution and a solvent. (Ii) A method of transesterifying 2,2-bis (4-hydroxyphenyl) propane and carbonic acid diester in the presence of a catalyst.

(Additive)
In the aromatic polycarbonate resin composition of the present invention, stabilizers, weathering agents, antistatic agents, mold release agents, dyes and pigments are added to the aromatic polycarbonate resin composition of the present invention as necessary, and the effects of the present invention such as transparency of molded products are not impaired. You may add in the range.
Examples of the stabilizer include triphenyl phosphite, tris (nonylphenyl) phosphite, distearyl pentaerythritol diphosphite, diphenyl hydrogen phosphite, irganox 1076 [stearyl-β- (3,5-di-). tert-butyl-4-hydroxyphenyl) propionate] and the like.
Examples of the weathering agent include 2- (2′-hydroxy-5′-methylphenyl) benzotriazole, 2- (2′-hydroxy-3 ′, 5′-di-tert-amylphenyl) benzotriazole, 2- (2′-hydroxy-4′-octoxyphenyl) benzotriazole, 2-hydroxy-4-octoxybenzophenone and the like.

  As a method for preparing the aromatic polycarbonate resin composition of the present invention, for example, a known kneading method using a Henschel mixer, a Banbury mixer, a simple screw extruder, a twin screw extruder, two rolls, a kneader, a Brabender, etc. Is mentioned.

<Molded product>
The molded article of the present invention is obtained by molding the aromatic polycarbonate resin composition of the present invention by a known method such as an injection molding method, an extrusion molding method, a compression molding method, a blow molding method, or a casting molding method. . The aromatic polycarbonate resin composition of the present invention is particularly useful as a raw material for injection molded products.
The molded product of the present invention can be used in a wide range of applications such as lamp covers, optical discs, light guide plates, medical materials, and miscellaneous goods.

  The fluidity improver of the present invention described above exhibits phase separation behavior with an aromatic polycarbonate resin during melt kneading by satisfying the relationships of the above formulas (1-1) to (1-3). While improving the melt fluidity of the aromatic polycarbonate resin composition, it exhibits a compatibility (affinity) that provides a good level of peel resistance in the use temperature range of the molded product. Thereby, the fluidity improver of the present invention has been conventionally applied to an aromatic polycarbonate resin composition without impairing the transparency, heat resistance, impact resistance, peel resistance, etc. of the molded product of the aromatic polycarbonate resin composition. It is possible to impart remarkable melt flowability (molding processability) and chemical resistance to the molded product.

Hereinafter, the present invention will be described in more detail with reference to examples. In the following description, “parts” and “%” mean “parts by mass” and “% by mass” unless otherwise specified.
The polymerization rate, mass average molecular weight, and number average molecular weight in Examples and Comparative Examples were determined by the following methods unless otherwise noted.
(Polymerization rate)
It calculated by mass conversion of the solid substance of the obtained polymer.
(Mass average molecular weight Mw, number average molecular weight Mn)
It calculated | required from the calibration curve by a standard polystyrene using gel permeation chromatography.

[Production Example 1]
Production of polymer (Z-1):
(Procedure 1)
A separable flask equipped with a condenser and a stirrer was charged with 550 parts of phenyl methacrylate, 1500 parts of toluene, and 0.007 part of a pre-synthesized cobalt glyoxime complex, and the cobalt glyoxime complex was heated to 70 ° C. The atmosphere was purged with nitrogen by nitrogen bubbling. Subsequently, 2 parts of 2,2′-azobisisobutyronitrile was added, and then the polymerization was completed by maintaining the internal temperature at 70 ° C. for 6 hours. The obtained polymer solution was poured into 6000 parts of methanol, and the precipitate was filtered to obtain a white solid. The white solid was washed with methanol and then purified by drying under reduced pressure to obtain a macromonomer (f-1) having a polymerizable unsaturated group. The mass average molecular weight of the macromonomer (f-1) was 11,000. The introduction rate of terminal double bonds in the macromonomer (f-1) was almost 100%.

  5 parts of macromonomer (f-1), aromatic polycarbonate resin ("Panlite L1225Z-100", manufactured by Teijin Chemicals Ltd., viscosity average molecular weight 22,000, refractive index 1.587) 95 parts (100 parts in total) Using an injection molding machine (“IS-100”, manufactured by Toshiba Machine Co., Ltd.), molding is performed under the conditions of molding temperature: 280 ° C. and mold temperature: 80 ° C. Was made. A thin piece was cut out from the center of the molded product, and the volume average domain diameter dv was measured by the method described above. As a result, phase separation was not observed with a volume average domain diameter dv of 0.05 μm or more. Therefore, the macromonomer (f-1) is a “macromonomer compatible with the aromatic polycarbonate resin” defined in the present invention.

(Procedure 2)
A separable flask equipped with a condenser and a stirrer was charged with 100 parts of macromonomer (f-1), 264 parts of toluene, 181 parts of styrene and 19 parts of phenyl methacrylate as the unsaturated monomer mixture (i), and nitrogen bubbling was performed. The atmosphere was replaced with nitrogen. Subsequently, 2 parts of 2,2′-azobisisobutyronitrile was added, and the polymerization was completed by maintaining the internal temperature at 90 ° C. for 6 hours. The obtained polymer solution was poured into 6000 parts of methanol, and the precipitate was filtered to obtain a white solid. The white solid was washed with methanol and then purified by drying under reduced pressure to obtain a polymer (Z-1). The mass average molecular weight of the polymer (Z-1) was 20000, and the molecular weight distribution (Mw / Mn) was 2.3. From the gas chromatography measurement, the styrene / phenyl methacrylate mass ratio of the trunk segment constituting the graft copolymer was 85/15, and the mass ratio of the trunk segment to the phenyl methacrylate branch segment was 50/50.

[Production Example 2]
Polymer (Z-2):
In a separable flask equipped with a condenser and a stirrer, 14.3 parts of macromonomer (f-1), 264 parts by mass of toluene, and 200 parts of styrene as an unsaturated monomer were charged and heated to 70 ° C. The atmosphere was replaced with nitrogen by nitrogen bubbling. Subsequently, 2 parts of 2,2′-azobisisobutyronitrile was added, and the polymerization was completed by maintaining the internal temperature at 90 ° C. for 6 hours. The obtained polymer solution was poured into 6000 parts by mass of methanol, and the precipitate was filtered to obtain a white solid. This white solid was washed with methanol and then purified by drying under reduced pressure to obtain a polymer (Z-2). The mass average molecular weight of the polymer (Z-2) was 23000, and the molecular weight distribution (Mw / Mn) was 2.3. From the gas chromatography measurement, the mass ratio of the styrene trunk segment and the phenyl methacrylate branch segment constituting the graft copolymer was 85/15.

[Production Example 3]
Polymer (Z-3):
(Procedure 1)
A separable flask equipped with a condenser and a stirrer was charged with 550 parts of phenyl methacrylate, 1500 parts of toluene, and 0.002 part of a pre-synthesized cobalt glyoxime complex. The atmosphere was purged with nitrogen by nitrogen bubbling. Subsequently, 2 parts of 2,2′-azobisisobutyronitrile was added, and then the polymerization was completed by maintaining the internal temperature at 70 ° C. for 6 hours. The obtained polymer solution was poured into 6000 parts of methanol, and the precipitate was filtered to obtain a white solid. The white solid was washed with methanol and then purified by drying under reduced pressure to obtain a macromonomer (f-2) having a polymerizable unsaturated group. The mass average molecular weight of the macromonomer (f-2) was 28000. Moreover, the introduction rate of the terminal double bond of the macromonomer (f-2) was almost 100%.

  5 parts of macromonomer (f-2), aromatic polycarbonate resin ("Panlite L1225Z-100", manufactured by Teijin Chemicals Ltd., viscosity average molecular weight 22,000, refractive index 1.587) 95 parts (100 parts in total) Using an injection molding machine (“IS-100”, manufactured by Toshiba Machine Co., Ltd.), molding is performed at a molding temperature of 280 ° C. and a mold temperature of 80 ° C., and a flat molded product having a thickness of 2 mm and a length and width of 50 mm. Was made. A thin piece was cut out from the center of the molded product, and the volume average domain diameter dv was measured by the method described above. As a result, phase separation was not observed with a volume average domain diameter dv of 0.05 μm or more. Accordingly, the macromonomer (f-2) is a “macromonomer compatible with the aromatic polycarbonate resin” defined in the present invention.

(Procedure 2)
In a separable flask equipped with a condenser and a stirrer, 14.3 parts of macromonomer (f-2), 264 parts by mass of toluene, and 200 parts of styrene as an unsaturated monomer were charged and heated to 70 ° C. The atmosphere was replaced with nitrogen by nitrogen bubbling. Subsequently, 2 parts of 2,2′-azobisisobutyronitrile was added, and the polymerization was completed by maintaining the internal temperature at 90 ° C. for 6 hours. The obtained polymer solution was poured into 6000 parts of methanol, and the precipitate was filtered to obtain a white solid. This white solid was washed with methanol and then purified by drying under reduced pressure to obtain a polymer (Z-3). The mass average molecular weight of the polymer (Z-3) was 30000. From the gas chromatography measurement, the mass ratio of the styrene trunk segment and the phenyl methacrylate branch segment constituting the graft copolymer was 85/15.

[Production Example 4]
Polymer (Z-4):
A separable flask equipped with a condenser and a stirrer was charged with 1.2 parts of calcium phosphate, 1 part of sodium sulfate, and 300 parts of distilled water. While stirring sufficiently in a nitrogen atmosphere, 56 parts of styrene and α-methylstyrene 24 A mixture of 20 parts of macromonomer (f-2) and 2 parts of azobisisobutyronitrile was added. Thereafter, the temperature was raised to 90 ° C. and stirred for 360 minutes to complete the polymerization. The polymerization rate was 95%. The obtained polymer was sufficiently washed with water and dried to obtain a polymer (Z-4). The mass average molecular weight of the polymer (Z-4) was 17000. From the gas chromatography measurement, the total composition mass ratio was styrene / α-methylstyrene / phenyl methacrylate = 56/24/20.

[Production Example 5]
Polymer (X-1):
A separable flask equipped with a condenser and a stirrer was charged with 1.0 part (solid content) of an anionic emulsifier ("Latemul ASK", manufactured by Kao Corporation, solid content 28%) and 290 parts of distilled water, and nitrogen. Heated to 60 ° C. in a water bath under atmosphere. Next, 0.0001 part of ferrous sulfate, 0.0003 part of ethylenediaminetetraacetic acid disodium salt and 0.3 part of Rongalite were dissolved in 5 parts of distilled water, and then 87.5 parts of styrene and 12.5 parts of phenyl methacrylate were added. A mixture of 0.2 part of t-butyl hydroperoxide and 0.5 part of n-octyl mercaptan was added dropwise over 180 minutes. Thereafter, the mixture was stirred for 60 minutes to complete the polymerization. The polymerization rate was 98%.

Next, 750 parts of a 0.08% aqueous sulfuric acid solution was heated to 70 ° C. and stirred. In this, the obtained polymer emulsion was dripped gradually, and the polymer was solidified. The coagulated product was separated and washed, and then dried at 75 ° C. for 24 hours to obtain a polymer (X-1). The mass average molecular weight of the polymer (X-1) was 50,000.
Table 1 shows that the polymer (X-1) corresponds to the polymer (X) in the present invention.

[Production Example 6]
Polymer (X-2):
Into a flask equipped with a condenser, 21.5 parts of toluene was charged. In a dropping funnel, 99 parts of styrene, 1 part of methacrylic acid, 0.5 part of 2,2′-azobisisobutyronitrile and 21.5 parts of toluene were charged. Connected to flask with condenser. The atmosphere in the flask was replaced with nitrogen by nitrogen bubbling. In a state heated to 90 ° C., the unsaturated monomer solution of the dropping funnel was dropped over 4 hours and held for 2 hours to complete the polymerization. The obtained polymer solution was poured into 500 parts of methanol, and the precipitate was filtered to obtain a white solid. This white solid was washed with methanol and then purified by drying under reduced pressure to obtain a polymer (X-2). The mass average molecular weight of the polymer (X-2) was 42,000.
Table 1 shows that the polymer (X-2) corresponds to the polymer (X) in the present invention.

[Production Example 7]
Polymer (X-3):
A separable flask equipped with a condenser and a stirrer was charged with 1.0 part (solid content) of an anionic emulsifier ("Latemul ASK", manufactured by Kao Corporation, solid content 28%) and 290 parts of distilled water, and nitrogen. Heated to 60 ° C. in a water bath under atmosphere. Next, 0.0001 part of ferrous sulfate, 0.0003 part of ethylenediaminetetraacetic acid disodium salt and 0.3 part of Rongalite were dissolved in 5 parts of distilled water, and then 56 parts of styrene, 24 parts of α-methylstyrene, phenyl methacrylate. A mixture of 20 parts, 0.2 parts of t-butyl hydroperoxide and 0.5 parts of n-octyl mercaptan was added dropwise over 360 minutes. Thereafter, the mixture was stirred for 60 minutes to complete the polymerization. The polymerization rate was 96%.

  Next, 750 parts of a 0.08% aqueous sulfuric acid solution was heated to 70 ° C. and stirred. In this, the obtained polymer emulsion was dripped gradually, and the polymer was solidified. The coagulated product was separated and washed, and then dried at 75 ° C. for 24 hours to obtain a polymer (X-3). The mass average molecular weight of the polymer (X-3) was 50,000.

[Production Example 8]
Polymer (Y-1):
A separable flask equipped with a condenser and a stirrer was charged with 1.0 part (solid content) of an anionic emulsifier ("Latemul ASK", manufactured by Kao Corporation, solid content 28%) and 290 parts of distilled water, and nitrogen. Heated to 60 ° C. in a water bath under atmosphere. Next, 0.0001 part of ferrous sulfate, 0.0003 part of ethylenediaminetetraacetic acid disodium salt and 0.3 part of Rongalite were dissolved in 5 parts of distilled water and then added to 80 parts of p-chlorostyrene and p-tbutylstyrene. A mixture of 20 parts, t-butyl hydroperoxide 0.2 parts, and n-octyl mercaptan 0.7 parts was added dropwise over 180 minutes. Thereafter, the mixture was stirred for 60 minutes to complete the polymerization. The polymerization rate was 97%.

Next, 750 parts of a 0.08% aqueous sulfuric acid solution was heated to 70 ° C. and stirred. In this, the obtained polymer emulsion was dripped gradually, and the polymer was solidified. The coagulated product was separated and washed, and then dried at 75 ° C. for 24 hours to obtain a polymer (Y-1). The mass average molecular weight of the polymer (Y-1) was 50,000.
Table 1 shows that the polymer (Y-1) corresponds to the polymer (Y) in the present invention.

[Production Example 9]
Polymer (B-1):
A separable flask equipped with a condenser and a stirrer was charged with 1.0 part (solid content) of an anionic emulsifier ("Latemul ASK", manufactured by Kao Corporation, solid content 28%) and 290 parts of distilled water, and nitrogen. Heated to 80 ° C. in a water bath under atmosphere. Next, 0.0001 part of ferrous sulfate, 0.0003 part of disodium ethylenediaminetetraacetate and 0.3 part of Rongalite were dissolved in 5 parts of distilled water, and then 100 parts of styrene and 0. A mixture of 2 parts and 0.5 part of n-octyl mercaptan was added dropwise over 180 minutes. Thereafter, the mixture was stirred for 60 minutes to complete the polymerization. The polymerization rate was 97%.

  Next, 750 parts of a 0.08% aqueous sulfuric acid solution was heated to 70 ° C. and stirred. In this, the obtained polymer emulsion was dripped gradually, and the polymer was solidified. The coagulated product was separated and washed, and then dried at 75 ° C. for 24 hours to obtain a polymer (B-1). The mass average molecular weight of the polymer (B-1) was 50,000.

[Examples 1-14, Comparative Examples 1-4]
A mixture of an aromatic polycarbonate resin and a fluidity improver in the ratio (mass ratio) shown in Table 2 is supplied to a twin-screw extruder (model name “TEM-35”, manufactured by Toshiba Machine), and 280 An aromatic polycarbonate resin composition was obtained by melt-kneading at 0 ° C.
The following evaluation was performed about the aromatic polycarbonate resin composition and the molded article which shape | molded this. The evaluation results are shown in Tables 2-4.

(Evaluation methods)
(1) Melt fluidity:
The spiral flow length (SPL) of the aromatic polycarbonate resin composition was evaluated using an injection molding machine (“IS-100”, manufactured by Toshiba Machine Co., Ltd.). The molding temperature was 280 ° C., the mold temperature was 80 ° C., and the injection pressure was 98 MPa. The thickness of the molded product was 2 mm and the width was 15 mm.

(2) Chemical resistance:
The aromatic polycarbonate resin composition is molded using an injection molding machine (“IS-100” manufactured by Toshiba Machine Co., Ltd.) to produce a 2 mm thick, 15 cm square flat plate, which is cut into a thickness. A molded product (test piece) of 2 mm, 3.5 cm × 15 cm was obtained.
After the specimen was annealed at 120 ° C. for 2 hours, a 1/4 ellipsoidal solvent test (constant strain test) was performed, the crack generation position 60 minutes after solvent application was measured, and the limit stress (MPa) was calculated. . The measurement conditions were a test temperature of 23 ° C. and a solvent [toluene / isooctane = 1/1 vol%].
In addition, in order to use as a headlamp etc., such as a motor vehicle, it is preferable that the said chemical resistance exists in the range of 8.5 Mpa or more.

(3) Surface peelability (peeling resistance):
The aromatic polycarbonate resin composition was molded using an injection molding machine (“IS-100”, manufactured by Toshiba Machine Co., Ltd.) to produce a flat molded product having a thickness of 3 mm and a length and width of 5 cm. The extruding pin mark of the molded product was cut with a cutter, and the peeled state was visually observed. The abbreviations in the table indicate the following contents.
○: Good without peeling.
X: Surface layer peeling is seen.

(4) Deflection temperature under load (heat resistance):
The aromatic polycarbonate resin composition was molded using an injection molding machine (“IS-100”, manufactured by Toshiba Machine Co., Ltd.) to produce a molded product having a thickness of ¼ inch. The deflection temperature under load of the molded product was measured in accordance with ASTM D648. Annealing was performed at 120 ° C. for 1 hour, and the load was 1.82 MPa.

(5) Transparency:
The aromatic polycarbonate resin composition was molded using an injection molding machine (“IS-100”, manufactured by Toshiba Machine Co., Ltd.) to produce a flat molded product having a thickness of 3 mm and a length and width of 5 cm. The total light transmittance and haze of the molded product were measured at 23 ° C. according to ASTM D1003.

(6) Drop weight impact strength (impact resistance):
The falling weight impact strength of the molded product was measured in accordance with ASTM D3763-86. The speed was 7 m / s and the load was 3.76 kg.

(7) Volume average domain diameter dv:
Using an injection molding machine (“IS-100”, manufactured by Toshiba Machine Co., Ltd.), a flat molded product having a thickness of 2 mm and a length and width of 50 mm was produced under the conditions of molding temperature: 280 ° C. and mold temperature: 80 ° C. . A thin piece was cut out from the center of the molded product so that the surface perpendicular to the flow direction in the molded product was the surface of the thin piece. The flakes were stained with a ruthenium tetroxide stain to obtain a sample. A TEM photograph (magnification: 5000 times) of the obtained sample was taken using TEM.
As image analysis software, Image-ProPlus Ver. Using 4.0 for Windows (registered trademark), the area R _j (j = 1 to n) of each domain is obtained for all domains (n) in the TEM photograph by image analysis, and the above equation (2) is obtained. ) _{Was used} to calculate the diameter (d _j ) when converted into a perfect circle from the domain area, and the volume average domain diameter dv was calculated from the diameter (d _j ) using the above equation (3).

(8) Glass transition temperature:
The aromatic polycarbonate resin composition was molded using an injection molding machine (“IS-100”, manufactured by Toshiba Machine Co., Ltd.) to produce a flat molded product having a thickness of 3 mm and 6 cm × 1 cm. Using the molded article, dynamic viscoelasticity measurement was performed to determine the glass transition temperature. The measurement conditions are shown below.
Device: Seiko Electronics Co., Ltd. DMS110 tension bending method,
Measurement temperature: 20 ° C. to 200 ° C. at a heating rate of 3 ° C./min.
Frequency: 10Hz,
Strain amount: 20 μm.
The glass transition temperature was the peak value of the loss elastic modulus G ″. In the aromatic polycarbonate resin composition, each of the peak of the aromatic polycarbonate resin and the peak of the fluidity improver is detected. The G ″ peak of the example aromatic polycarbonate resin (PC-1) was detected at 160 to 170 ° C.

(9) Refractive index:
The refractive index of the fluidity improver was measured according to JIS K7142.
Proportions (mass ratio) of polymers (X-1) to (X-3), (Y-1), (B-1) and polymers (Z-1) to (Z-3) shown in Table 2 ) Was supplied to PL2000 type (Plavender, model number W-50E, 2-zone type) and melt kneaded at 200 ° C. to obtain a fluidity improver. A fluidity improver was heated and pressed to produce a molded product having a length and width of 20 mm × 8 mm and a thickness of 2 mm, and the refractive index was measured under the following measurement conditions.
Abbe refractometer: NAR-2 (manufactured by Atago Co., Ltd.)
Measurement conditions: measurement temperature 23 ± 1 ° C., measurement humidity 50 ± 5% RH (relative humidity).

Abbreviations in the table are as follows.
PC-1: Aromatic polycarbonate resin (“Panlite L1225Z-100”, manufactured by Teijin Chemicals Ltd., viscosity average molecular weight 22,000, refractive index 1.587)).
PC-2: aromatic polycarbonate resin (“Panlite L1225ZL-100”, manufactured by Teijin Chemicals Ltd., viscosity average molecular weight 18,000, refractive index 1.587).

According to the fluidity improver of the present invention, melt flowability (molding) can be achieved in an aromatic polycarbonate resin composition without impairing the transparency, heat resistance, peel resistance, impact resistance, etc. of the molded article of the aromatic polycarbonate resin. Processability) and chemical resistance to the molded product. Therefore, the present invention can be applied to a wide range of applications such as lamp covers, optical discs, light guide plates, medical materials, and miscellaneous goods.

Claims (4)

A fluidity improver that satisfies the following formulas (1-1) to (1-3) for a resin composition in which 7.5 parts by mass of a fluidity improver is blended with 92.5 parts by weight of an aromatic polycarbonate resin: .
| N _PC −n _P | ≦ 0.01 (1-1)
0.01 μm ≦ dv ≦ 0.3 μm (1-2)
SPL ≧ 1.2L _PC (1-3)
(Where n _PC is the refractive index of the aromatic polycarbonate resin, n _P is the refractive index of the flow improver, and dv is the volume average domain diameter of the flow improver dispersed in the matrix of the aromatic polycarbonate resin. , SPL is the spiral flow length of the resin composition, L _PC is a spiral flow length of the aromatic polycarbonate resin.)   The fluidity improver according to claim 1, comprising a polymer (Z) obtained by polymerizing an unsaturated monomer in the presence of a macromonomer compatible with an aromatic polycarbonate resin. An aromatic polycarbonate resin;
An aromatic polycarbonate resin composition comprising the fluidity improver according to claim 1 or 2. A molded article obtained by molding the aromatic polycarbonate resin composition according to claim 3.