JP2004203928A - Thermoplastic resin composition - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a thermoplastic resin composition comprising a phyllosilicate finely dispersed therein, having good rigidity, good hydrolytic resistance and further good thermal stability, especially useful for a thermoplastic resin composition composed of an aromatic polycarbonate resin. <P>SOLUTION: The thermoplastic resin composition comprises (A) 100 pts. wt. of an amorphous thermoplastic resin (component A) and (B) 0.1-50 pts. wt. of a phyllosilicate (component B) having 50-200 mequivalents/100 g cation exchange capacity. The component B in the resin composition has 5-40 average number of laminates of the silicate layer determined by X-ray diffraction and the bottom face interval is within the range of 1.3-2.3 nm. <P>COPYRIGHT: (C)2004,JPO&NCIPI

Description

【００５６】
上記一般式（Ｉ）は次の条件を満足する。すなわち、Ｍは窒素原子またはリン原子であり、Ｒ¹およびＲ²はそれぞれ炭素原子数６〜１６のアルキル基である。Ｒ³は炭素原子数１〜１６のアルキル基であり、かつＲ⁴は炭素原子数１〜４のアルキル基である。なお、Ｒ¹とＲ²とは互いに同一の基であっても相異なる基であってもよく、また、Ｒ³とＲ⁴とは互いに同一の基であっても相異なる基であってもよい。
【００５７】
上記一般式（Ｉ）で示される有機オニウムイオンのより好適な態様は、（ｉ）前記Ｒ³が炭素原子数１〜４のアルキル基の場合である。より好しくは（ii）Ｒ³およびＲ⁴がそれぞれ炭素原子数１〜４のアルキル基であって、かつＲ¹およびＲ²がそれぞれ炭素原子数７〜１４のアルキル基の場合である。さらに好ましくは、（iii）Ｒ³およびＲ⁴がそれぞれ炭素原子数１〜４のアルキル基で、かつＲ¹およびＲ²は炭素原子数７〜１１のアルキル基の場合である。なお、これらのうちでも、Ｒ³およびＲ⁴が炭素原子数１〜３のアルキル基、より好ましくはメチル基またはエチル基、さらに好ましくはメチル基の４級アンモニウムイオンが特に好適である。
【００５８】
これら（ｉ）〜（iii）のより好適な態様（さらに好ましい態様を含む）によれば、樹脂組成物の耐加水分解性が特に優れたものとなり、本発明の熱可塑性樹脂組成物に良好な長期実用特性を与える。
【００５９】
なお、上記式（Ｉ）においてＲ¹〜Ｒ⁴はいずれも直鎖状および分岐状のいずれも選択できる。
【００６０】
かかる好適な４級アンモニウムイオンの例としては、ジメチルジオクチルアンモニウム、ジメチルジデシルアンモニウム、ジメチルジドデシルアンモニウム、ジメチルジテトラデシルアンモニウム、ジメチルジヘキサデシルアンモニウム、ジエチルジドデシルアンモニウム、ジエチルジテトラデシルアンモニウム、ジエチルジヘキサデシルアンモニウム、ジブチルジオクチルアンモニウム、ジブチルジデシルアンモニウム、ジブチルジドデシルアンモニウム等が例示される。
【００６１】
Ｂ成分の層状珪酸塩は、ＳｉＯ₂連鎖からなるＳｉＯ₄四面体シート構造とＡｌ、Ｍｇ、Ｌｉ等を含む八面体シート構造との組み合わせからなる層からなり、その層間に交換性陽イオンの配位した珪酸塩（シリケート）または粘土鉱物（クレー）である。これらの珪酸塩（シリケート）または粘土鉱物（クレー）は、スメクタイト系鉱物、バーミキュライト、ハロイサイトおよび膨潤性雲母等に代表される。具体的には、スメクタイト系鉱物としては、モンモリロナイト、ヘクトライト、フッ素ヘクトライト、サポナイト、バイデライト、スチブンサイト等が挙げられ、膨潤性雲母としては、Ｌｉ型フッ素テニオライト、Ｎａ型フッ素テニオライト、Ｎａ型四珪素フッ素雲母、Ｌｉ型四珪素フッ素雲母等の膨潤性合成雲母等が挙げられる。これら層状珪酸塩は天然品および合成品のいずれも使用可能である。合成品は、例えば、水熱合成、溶融合成、固体反応によって製造される。
【００６２】
層状珪酸塩のなかでも、陽イオン交換容量等の点から、モンモリロナイト、ヘクトライト等のスメクタイト系粘土鉱物、Ｌｉ型フッ素テニオライト、Ｎａ型フッ素テニオライト、Ｎａ型四珪素フッ素雲母等の膨潤性を持ったフッ素雲母が好適に用いられ、ベントナイトを精製して得られるモンモリロナイトや合成フッ素雲母が、純度等の点からより好適である。なかでも、良好な機械特性が得られる合成フッ素雲母が特に好ましい。
【００６３】
前記Ｂ成分である層状珪酸塩の陽イオン交換容量（陽イオン交換能ともいう）は、５０〜２００ミリ当量／１００ｇであることが必要とされ、好ましくは８０〜１５０ミリ当量／１００ｇ、さらに好ましくは１００〜１５０ミリ当量／１００ｇである。陽イオン交換容量は、土壌標準分析法として国内の公定法となっているショーレンベルガー改良法によってＣＥＣ値として測定される。すなわち、層状珪酸塩の陽イオン交換容量は、Ａ成分である非晶性熱可塑性樹脂への良好な分散性を得るために、５０ミリ当量／１００ｇ以上必要であるが、２００ミリ当量／１００ｇより大きくなると熱可塑性樹脂組成物（特に芳香族ポリカーボネート樹脂組成物）の熱劣化が大きくなり、それに伴って本発明の非晶性熱可塑性樹脂組成物の熱劣化への影響が大きくなってくる。この層状珪酸塩は、そのｐＨの値が９〜１０．５であることが好ましい。ｐＨの値が１０．５より大きくなると、本発明の熱可塑性樹脂組成物の熱安定性が低下する傾向が現れてくる。
【００６４】
層状珪酸塩への有機オニウムイオンのイオン交換は、極性溶媒中に分散させた層状珪酸塩に、有機オニウムイオン化合物（有機オニウムイオンの塩化合物）を添加し、析出してくるイオン交換化合物を収集することによって作成することができる。通常、このイオン交換反応は、有機オニウムイオン化合物を、層状珪酸塩のイオン交換容量の１当量に対し１．０〜１．５当量の割合で加えて、ほぼ全量の層間の金属イオンを有機オニウムイオンで交換させるのが一般的である。しかし、このイオン交換容量に対する交換割合を一定の範囲に制御することも、芳香族ポリカーボネート樹脂の熱劣化を抑制する上で有効である。ここで有機オニウムイオンでイオン交換される割合は、層状珪酸塩のイオン交換容量に対して４０％以上であることが好ましい。かかるイオン交換容量の割合は好ましくは４０〜９５％であり、特に好ましくは４０〜８０％である。ここで、有機オニウムイオンの交換割合は、交換後の化合物について、熱重量測定装置等を用いて、有機オニウムイオンの熱分解による重量減少を求めることにより算出することができる。
【００６５】
本発明の層状珪酸塩（Ｂ成分）のＸ線回折より求められるシリケート層の平均積層数は５〜４０（特徴Ａ）であり、好ましくは５〜３０、より好ましくは５〜２０、最も好ましくは５〜１５である。平均積層数が５未満であると熱可塑性樹脂組成物の熱安定性が低下する場合があり、４０を超えると剛性向上効果が低減する。
【００６６】
芳香族ポリカーボネート樹脂などの非晶性熱可塑性樹脂に層状珪酸塩を微分散させた熱可塑性樹脂組成物は、従来単に有機化層状珪酸塩などを層間部分で剥離させ、基体樹脂中において出来る限り微分散させることを課題としていた。しかし、分散が進みすぎると返って剛性向上効果が減少し、また熱安定性等が悪化する。そこで剛性向上や熱安定性の保持のために、本発明の適度な分散状態を必要とした。
【００６７】
本発明の層状珪酸塩（Ｂ成分）の熱可塑性樹脂組成物中の層状珪酸塩の底面間隔は、１．３〜２．３ｎｍ（特徴Ｂ）であり、より好ましくは１．５〜２．３ｎｍ、最も好ましくは１．８〜２．３ｎｍである。この底面間隔を得るためには、有機化層状珪酸塩を用いることが好ましい。底面間隔が、１．３ｎｍ未満であると剛性向上効果が不十分になることがあり、２．３ｎｍを超えると熱可塑性樹脂組成物の熱安定性が低下する場合がある。
【００６８】
上記の特徴Ｂは、Ｘ線回折測定における回折線の回折角度からＢｒａｇｇの条件により求められる。層状珪酸塩の底面間隔およびＸ線回折測定については、たとえば「粘土ハンドブック」（日本粘土学会編：技報堂出版）などに記載されている。有機化層状珪酸塩のＸ線回折測定を行うには、粉末状の試料を試料台に充填して測定することができ、また組成物中の層状珪酸塩のＸ線回折測定を行うには、組成物を例えば射出成形や押出成形などで平板に成形した後、平面部分を試料台開口部に、測定基準面と同一になるよう試料を設置し測定することができる。
【００６９】
本発明の熱可塑性樹脂組成物は、層状珪酸塩を微分散させる、すなわち上記特徴Ａ、更に特徴Ｂを兼ね備えることにより、良好な剛性を有し、良好な耐加水分解性を有し、更に良好な熱安定性を有する熱可塑性樹脂組成物を得るに至ったものである。
【００７０】
本発明における上記特徴Ａまたは特徴Ｂを達成する方法としては例えば次の方法が例示される。▲１▼特定範囲の陽イオン交換容量を有する層状珪酸塩を用いる、▲２▼多軸押出機を用いて拡散効率の高い溶融混練を行う、▲３▼特定の有機化層状珪酸塩を用いる、▲４▼非晶性樹脂と層状珪酸塩との相溶化剤（Ｃ成分等の第３成分）を配合する、▲５▼層状珪酸塩のマスターバッチを用いる等の方法があげられ、これらを組合せて用いることができ、殊に▲１▼〜▲４▼を組み合わせること、殊に好適には▲１▼〜▲５▼を組み合わせることが好ましい。
【００７１】
上記▲４▼の方法における第３成分としては、Ａ成分の非晶性熱可塑性樹脂と親和性を有し、かつ親水性成分を有する化合物が好適である。したがって本発明はより好適には、更にＡ成分１００重量部あたり、（Ｃ）Ａ成分の非晶性熱可塑性樹脂との親和性を有しかつ親水性成分を有する化合物（Ｃ成分）０．１〜５０重量部を含んでなる熱可塑性樹脂組成物を挙げることができる。
【００７２】
本発明で用いられるＢ成分の層状珪酸塩の、Ａ成分との組成割合は、Ａ成分１００重量部あたり０．１〜５０重量部、好ましくは０．５〜２０重量部、更に好ましくは０．５〜１０重量部である。この組成割合が０．１重量部より小さいときには芳香族ポリカーボネート樹脂など非晶性熱可塑性樹脂の機械特性の改良効果が見られず、また５０重量部より大きくなると、組成物の熱安定性が低下し実用的な熱可塑性樹脂組成物は得られにくい。
【００７３】
＜Ｃ成分について＞
本発明のＣ成分は、非晶性熱可塑性樹脂（Ａ成分）との親和性を有し、かつ親水性成分を有する化合物である。Ｃ成分のかかる構成は、非晶性熱可塑性樹脂および層状珪酸塩、殊に有機化層状珪酸塩の双方に対する良好な親和性を生み出す。非晶性熱可塑性樹脂および層状珪酸塩、殊に有機化層状珪酸塩双方に対する親和性は２種の成分の相溶性を向上させ、層状珪酸塩は非晶性熱可塑性樹脂中での微細かつ安定して分散するようになる。
【００７４】
有機化層状珪酸塩の分散に関するかかるＣ成分の働きは、異種ポリマー同士を相溶化させるために使用されるポリマーアロイ用相溶化剤（コンパティビライザー）と同様である。したがってＣ成分は低分子化合物よりも単量体が重合してなる重合体であることが好ましい。また重合体は混練加工時の熱安定性にも優れる。重合体の平均繰り返し単位数は２以上であることが必要であり、５以上が好ましく、１０以上がより好ましい。一方、重合体の平均分子量の上限においては数平均分子量で２，０００，０００以下であることが好ましい。かかる上限を超えない場合には良好な成形加工性が得られる。
【００７５】
本発明のＣ成分の基本的構造としては、例えば次の構造（ｉ）および（ｉｉ）を挙げることができる。
【００７６】
構造（ｉ）：非晶性熱可塑性樹脂に親和性を有する成分をα、親水性成分をβとするとき、αとβとからなるグラフト共重合体（主鎖：α、グラフト鎖：β、並びに主鎖：β、グラフト鎖：αのいずれも選択できる。）、αとβとからなるブロック共重合体（ジ−、トリ−、などブロックセグメント数は２以上を選択でき、ラジアルブロックタイプなどを含む。）、並びにαとβとからなるランダム共重合体。α、βはそれぞれ単一の重合体だけでなく共重合体であってもよい。
【００７７】
ここでαおよびβは重合体セグメント単位、および単量体単位のいずれも示す。α成分は非晶性熱可塑性樹脂との親和性の観点から重合体セグメント単位であることが好ましい。
【００７８】
構造（ｉｉ）：非晶性熱可塑性樹脂に親和性を有する成分をα、親水性成分をβとするとき、αの機能は重合体全体によって発現され、βは該α内に含まれる構造を有する重合体。
【００７９】
すなわちα単独では非晶性熱可塑性樹脂との親和性が十分ではないものの、αとβが組み合わされ一体化されることにより、非晶性熱可塑性樹脂との良好な親和性が発現する場合である。α単独の場合にも非晶性熱可塑性樹脂との親和性が良好であって、βとの組合せによって更に親和性が向上する場合もある。かかる態様は上記構造（ｉ）に含まれる。したがって構造（ｉ）および（ｉｉ）はその一部を重複する。一方、構造（ｉ）はα単独では非晶性熱可塑性樹脂との親和性が十分ではあるが、αとβが組み合わされ一体化されることにより、非晶性熱可塑性樹脂との良好な親和性が逆に低下する態様もあり得る。当然のことながらかかる態様はＣ成分に含まれる。
【００８０】
上記構造（ｉ）および（ｉｉ）は本発明においていずれも選択できる。殊に構造（ｉ）の条件および構造（ｉｉ）の条件を共に満足する態様、すなわちαのみでも非晶性熱可塑性樹脂に対する親和性が高く、βが付加したＣ成分全体において更にその親和性が高くなる態様が好適である。
【００８１】
本発明における非晶性熱可塑性樹脂に親和性を有する成分（以下、上記に従いαと称する場合がある）について説明する。上記の如くＣ成分は、ポリマーアロイにおける相溶化剤との同様の働きをすることから、αには相溶化剤と同様の重合体に対する親和性が求められる。したがってαは大きく非反応型と反応型とに分類できる。
【００８２】
非反応型では、以下の要因を有する場合に親和性が良好となる。即ち、非晶性熱可塑性樹脂とαとの間に、▲１▼化学構造の類似性、▲２▼溶解度パラメータの近似性（溶解度パラメータの差が１（ｃａｌ／ｃｍ³）^1/2以内、即ち約２．０５（ＭＰａ）^1/2以内が目安とされる）、▲３▼分子間相互作用（水素結合、イオン間相互作用など）、およびランダム重合体特有の擬引力的相互作用などの要因を有することが必要である。これらの要因は相溶化剤とポリマーアロイのベースになる重合体との親和性を判断する指標として知られている。
【００８３】
また反応型では、相溶化剤において非晶性熱可塑性樹脂と反応性を有する官能基として知られた各種を挙げることができる。例えば非晶性熱可塑性樹脂として好適な芳香族ポリカーボネート樹脂に対しては、カルボキシル基、カルボン酸無水物基、エポキシ基、オキサゾリン基、エステル基、エステル結合、カーボネート基、およびカーボネート結合などを例示することができる。
【００８４】
一方で、非晶性熱可塑性樹脂とαが良好な親和性を得た場合、その結果として非晶性熱可塑性樹脂とαとの混合物において単一のガラス転移温度（Ｔｇ）を示すか、または非晶性熱可塑性樹脂のＴｇがαのＴｇの側に移動する挙動が認められることも広く知られるところである。本発明において親和性を有する成分（α）として、かかる挙動を有する成分をその態様の１つとして挙げることができる。
【００８５】
上記の如く、本発明のＣ成分における非晶性熱可塑性樹脂と親和性を有する成分（α）は、各種の要因によりその親和性を発揮することが可能である。中でもαは非反応型であることが好ましく、殊に溶解度パラメータが近似することは、良好な親和性を発揮するので好ましい。これは反応型に比較して非晶性熱可塑性樹脂との親和性により優れるためである。また反応型は過度に反応性を高めた場合、副反応によって重合体の熱劣化が促進される欠点がある。
【００８６】
非晶性熱可塑性樹脂およびαの溶解度パラメータは次の関係を有することが好ましい。即ち、非晶性熱可塑性樹脂（Ａ成分）の溶解度パラメータをδ_A（（ＭＰａ）^1/2）、およびＣ成分におけるαの溶解度パラメータまたはＣ成分全体の溶解度パラメータをδα（（ＭＰａ）^1/2）としたとき、
δα＝δ_A±２ （（ＭＰａ）^1/2）
であることが好ましい。
【００８７】
例えば、Ａ成分として好適な芳香族ポリカーボネート樹脂の溶解度パラメータは通常約１０（ｃａｌ／ｃｍ³）^1/2（即ち約２０．５（（ＭＰａ）^1/2））とされていることから、かかるＡ成分におけるδαは１８．５〜２２．５（（ＭＰａ）^1/2）の範囲が好ましく、１９〜２２（（ＭＰａ）^1/2）の範囲がより好ましい。
【００８８】
例えばＡ成分として好適な芳香族ポリカーボネート樹脂におけるかかる溶解度パラメータδαを満足する重合体成分の具体例は、芳香族ポリエステル（ポリエチレンテレフタレート、ポリブチレンテレフタレート、およびシクロヘキサンジメタノール共重合ポリエチレンテレフタレートなどに代表される）、および脂肪族ポリエステル（ポリカプロラクトンに代表される）などのポリエステル系重合体が挙げられる。またかかる具体例としては、スチレンポリマー、アルキル（メタ）アクリレートポリマー、およびアクリロニトリルポリマー（ポリスチレン、スチレン−無水マレイン酸共重合体、ポリメチルメタクリレート、スチレン−メチルメタクリレート共重合体、およびスチレン−アクリロニトリル共重合体などに代表される）などのビニル系重合体を挙げることができる。本発明の組成物の耐熱性の保持のためには、Ｔｇの高い重合体成分を用いることが好ましい。
【００８９】
ここで溶解度パラメータは、「ポリマーハンドブック 第４版」（Ａ ＷＩＬＥＹ−ＩＮＴＥＲＳＣＩＥＮＣＥ ＰＵＢＬＩＣＡＴＩＯＮ，１９９９年）中に記載されたＳｍａｌｌの値を用いた置換基寄与法（Ｇｒｏｕｐ ｃｏｎｔｒｉｂｕｔｉｏｎ ｍｅｔｈｏｄｓ）による理論的な推算方法が利用できる。また非晶性熱可塑性樹脂のＴｇはＪＩＳ Ｋ７１２１に準拠した示差走査熱量計（ＤＳＣ）測定により求めることが可能である。
【００９０】
上記のＡ成分の非晶性熱可塑性樹脂に親和性を有する成分αは、Ｃ成分中５重量％以上であることが好ましく、１０重量％以上がより好ましく、３０重量％以上が更に好ましく、５０重量％以上が特に好ましい。Ｃ成分全体をαとする態様も可能であることから上限は１００重量％であってよい。
【００９１】
一方、Ｃ成分における親水性成分（以下、βと称する場合がある）は、親水基（水との相互作用の強い有機性の原子団）を有する単量体及び親水性重合体成分（重合体セグメント）より選択される。親水基はそれ自体広く知られ、下記の基が例示される。
１）強親水性の基：−ＳＯ₃Ｈ、−ＳＯ₃Ｍ、−ＯＳＯ₃Ｈ、−ＯＳＯ₃Ｈ、−ＣＯＯＭ、−ＮＲ₃Ｘ（Ｒ：アルキル基、Ｘ：ハロゲン原子、Ｍ：アルカリ金属、−ＮＨ₄） 等、
２）やや小さい親水性を有する基：−ＣＯＯＨ、−ＮＨ₂、−ＣＮ、−ＯＨ、−ＮＨＣＯＮＨ₂ 等、
３）親水性が無いか又は小さい基：−ＣＨ₂ＯＣＨ₃、−ＯＣＨ₃、−ＣＯＯＣＨ₃、−ＣＳ 等
上記１）〜３）の群の中で本発明における親水基は１）および２）に分類されるものが使用される。上記の例示以外にも、１）強親水性の基としてはスルフィン基などが例示され、２）あまり親水性の強くない基としては、カルボン酸無水物基、オキサゾリン基、ホルミル基およびピロリドン基などが例示される。
【００９２】
上記２）の親水基は非晶性熱可塑性樹脂、殊に本発明において好適な芳香族ポリカーボネート樹脂の溶融加工時の熱安定性により優れるため好ましい。親水性が高すぎる場合には芳香族ポリカーボネート樹脂などの熱劣化が生じやすくなる。これはかかる親水基が直接カーボネート結合と反応し、熱分解反応を生じるためである。
【００９３】
尚、本発明の親水基は１価および２価以上のいずれも含む。Ｃ成分が重合体の場合、２価以上の官能基とは該基が主鎖を構成しないものをを指し、主鎖を構成するものは結合として官能基とは区別する。具体的には、主鎖を構成する炭素などの原子に付加した基、側鎖の基、および分子鎖末端の基は、２価以上であっても官能基である。
【００９４】
親水基のより具体的な指標は、溶解度パラメータである。溶解度パラメータの値が大きいほど親水性が高くなることは広く知られている。基ごとの溶解度パラメータは、Ｆｅｄｏｒｓによる基ごとの凝集エネルギー（Ｅ_coh）および基ごとのモル体積（Ｖ）より算出することができる（「ポリマー・ハンドブック 第４版」（Ａ ＷＩＬＥＹ−ＩＮＴＥＲＳＣＩＥＮＣＥ ＰＵＢＬＩＣＡＴＩＯＮ），ＶＩＩ／６８５頁、１９９９年、またはＰｏｌｙｍ．Ｅｎｇ．Ｓｃｉ．，第１４巻，１４７および４７２頁，１９７４年等参照）。かかる算出方法は簡便であり広く知られる。更に親水性の大小関係のみを比較する観点からは、凝集エネルギー（Ｅ_coh）をモル体積（Ｖ）で除した数値（Ｅ_coh／Ｖ；以下単位は“Ｊ／ｃｍ³”とする）を親水性の指標として使用できる。
【００９５】
本発明のＣ成分におけるβに含まれる親水基は、Ｅ_coh／Ｖが６００以上であることが必要である。好ましくはＥ_coh／Ｖは８００以上であり、８００以上の場合には本発明のＡ成分として好適な芳香族ポリカーボネート樹脂におけるカーボネート結合のＥ_coh／Ｖを超え、カーボネート結合よりも高い親水性を有する。更にＥ_coh／Ｖは９００以上がより好ましく、９５０以上が更に好ましい。一方、親水性が高すぎる場合には、既に述べたように芳香族ポリカーボネート樹脂の熱劣化が生じ易くなる。このため、Ｅ_coh／Ｖは２，５００以下が好ましく、２，０００以下がより好ましく、１，５００以下がさらに好ましい。
【００９６】
Ｃ成分の親水性成分（β）として、親水性重合体成分（重合体セグメント）も選択される。したがってＣ成分の重合体中に含まれる親水性重合体のセグメントはβとなる、親水性重合体としては、例えばポリアルキレンオキシド、ポリビニルアルコール、ポリアクリル酸、ポリアクリル酸金属塩（キレート型を含む）、ポリビニルピロリドン、ポリアクリルアミド、およびポリヒドロキシエチルメタクリレートなどが例示される。これらの中でもポリアルキレンオキシド、ポリビニルアルコール、ポリアクリル酸、ポリビニルピロリドン、およびポリヒドロキシエチルメタクリレートが好ましく例示される。これらは良好な親水性と本発明において好適な芳香族ポリカーボネート樹脂に対する熱安定性（溶融加工時の芳香族ポリカーボネート樹脂の分解の抑制）とを両立できるためである。尚、ポリアルキレンオキシドとしては、ポリエチレンオキシドおよびポリプロピレンオキシドが好ましい。
【００９７】
親水基を有する単量体および親水性重合体成分のいずれにおいても、βは酸性の官能基（以下単に“酸性基”と称する場合がある）を有することが好ましい。酸性基は本発明において好適な芳香族ポリカーボネート樹脂を主成分とする熱可塑性樹脂組成物の溶融加工時の熱劣化を抑制する。とりわけ、窒素原子を含まない酸性基がより好適である。好適な酸性基としては、カルボキシル基、カルボン酸無水物基、スルホン酸基、スルフィン酸基、ホスホン酸基及びホスフィン酸基等が例示される。
【００９８】
これに比して、アミド基やイミド基等の窒素原子を含む官能基は溶融加工時の芳香族ポリカーボネート樹脂の熱劣化を十分には抑制しない場合がある。これは窒素原子が局所的に塩基性を有しカーボネート結合の熱分解を生じさせるためと考えられる。
【００９９】
Ｃ成分におけるβの割合は、βが親水基を有する単量体の場合、官能基１つ当たりの分子量である官能基当量として６０〜１０，０００であり、７０〜８，０００が好ましく、８０〜６，０００がより好ましく、１００〜３，０００が更に好ましい。またβが親水性重合体セグメントの場合、Ｃ成分１００重量％中βが５〜９５重量％の範囲にあることが適当であり、１０〜９０重量％が好ましい。とりわけ、３０〜７０重量％がより好ましく、３０〜５０重量％が更に好ましい。
【０１００】
非晶性熱可塑性樹脂に親和性を有する成分（α）と親水性成分（β）とを有する化合物の製造方法としては、βの単量体とαを構成する単量体とを共重合する方法、βの重合体成分をαとブロックまたはグラフト共重合する方法、およびβをαに直接反応させて付加する方法などが例示される。
【０１０１】
本発明のＣ成分の好ましい態様として、“Ａ成分の樹脂との親和性を有しかつ酸性の官能基を有する重合体”、“Ａ成分の樹脂との親和性を有しかつポリアルキレンオキシドセグメントを有する重合体”、“Ａ成分の樹脂との親和性を有しかつオキサゾリン基を有する重合体”、または“Ａ成分の樹脂との親和性を有しかつ水酸基を有する重合体”が例示される。これらのＣ成分として好ましい態様の重合体においては、その分子量は重量平均分子量において１万〜１００万の範囲が好ましく、５万〜５０万の範囲がより好ましい。かかる重量平均分子量は標準ポリスチレン樹脂による較正直線を使用したＧＰＣ測定によりポリスチレン換算の値として算出されるものである。
【０１０２】
上記の中でもＡ成分の樹脂との（より好適には芳香族ポリカーボネート樹脂との）親和性を有しかつ酸性の官能基を有する重合体が好ましく、更に好ましくは芳香族ポリカーボネート樹脂との親和性を有しかつカルボキシル基及び／又はその誘導体からなる官能基とを有する重合体である。また、芳香族ポリカーボネート樹脂の耐熱性保持効果の観点から、重合体は芳香環成分を主鎖に有するもの、およびスチレン成分を主鎖に有するものが好ましい。上記の点からカルボキシル基及び／又はその誘導体からなる官能基を有するスチレン含有重合体（Ｃ１成分）が本発明のＣ成分として特に好適である。ここでスチレン含有重合体とはスチレン等の芳香族ビニル化合物を重合した繰返し単位を重合体成分として含有する重合体を指す。
【０１０３】
本発明のＣ成分として特に好適なカルボキシル基及び／又はその誘導体からなる官能基を有するスチレン含有重合体（Ｃ１成分）について詳述する。かかるカルボキシル基及び／又はその誘導体からなる官能基の割合としては、０．１〜１２ミリ当量／ｇが好ましく、０．５〜５ミリ当量／ｇがより好ましい。ここでＣ１成分における１当量とは、カルボキシル基が１モル存在することをいい、かかる値は水酸化カリウムなどの逆滴定により算出することが可能である。
【０１０４】
カルボキシル基の誘導体からなる官能基としては、カルボキシル基の水酸基を（ｉ）金属イオンで置換した金属塩（キレート塩を含む）、（ｉｉ）塩素原子で置換した酸塩化物、（ｉｉｉ）−ＯＲで置換したエステル（Ｒは一価の炭化水素基）、（ｉｖ）−Ｏ（ＣＯ）Ｒで置換した酸無水物（Ｒは一価の炭化水素基）、（ｖ）−ＮＲ₂で置換したアミド（Ｒは水素又は一価の炭化水素基）、並びに（ｖｉ）２つのカルボキシル基の水酸基を＝ＮＲで置換したイミド（Ｒは水素又は一価の炭化水素基）などを挙げることができる。
【０１０５】
カルボキシル基及び／又はその誘導体からなる官能基（以下、単に“カルボキシル基類”と称する）を有するスチレン含有重合体の製造方法としては、従来公知の各種の方法を取ることができる。例えば、▲１▼カルボキシル基類を有する単量体とスチレン系単量体とを共重合する方法、及び▲２▼スチレン含有重合体に対してカルボキシル基類を有する化合物又は単量体を結合または共重合する方法などを挙げることができる。
【０１０６】
上記▲１▼の共重合においては、ランダム共重合体の他に交互共重合体、ブロック共重合体、テーパード共重合体などの各種形態の共重合体が使用できる。また共重合の方法においても溶液重合、懸濁重合、塊状重合などのラジカル重合法の他、アニオンリビング重合法やグループトランスファー重合法などの各種重合方法を取ることができる。更に一旦マクロモノマーを形成した後重合する方法も可能である。
【０１０７】
上記▲２▼の方法は、一般的にはスチレン含有重合体又は共重合体に必要に応じて、パーオキサイドや２，３−ジメチル−２，３ジフェニルブタン（ジクミル）などのラジカル発生剤を加えて、高温化で反応又は共重合する方法を挙げることができる。かかる方法はスチレン含有重合体または共重合体に熱的に反応活性点を生成し、かかる活性点に反応する化合物または単量体を反応させるものである。反応に要する活性点を生成するその他の方法として、放射線や電子線の照射やメカノケミカル手法による外力の付与などの方法も挙げられる。更にスチレン系共重合体中に予め反応に要する活性点を生成する単量体を共重合しておく方法も挙げられる。反応のための活性点としては不飽和結合、パーオキサイド結合、および立体障害が高く熱的に安定なニトロオキシドラジカルなどを挙げることができる。
【０１０８】
上記カルボキシル基類を有する化合物又は単量体としては、例えば、アクリル酸、メタクリル酸、アクリルアミド、メタクリルアミド等の不飽和モノカルボン酸及びその誘導体、無水マレイン酸、無水シトラコン酸、Ｎ−フェニルマレイミド、Ｎ−メチルマレイミド等の無水マレイン酸の誘導体、並びにグルタルイミド構造やアクリル酸と多価の金属イオンで形成されたキレート構造等が挙げられる。これらの中でも金属イオンや窒素原子を含まない官能基を有する単量体が好適であり、カルボキシル基およびカルボン酸無水物基を有する単量体がより好適である。これらの中でも特に好ましくは無水マレイン酸である。
【０１０９】
また、スチレン系単量体化合物としては、スチレン、α−メチルスチレン、ｏ−メチルスチレン、ｍ−メチルスチレン、ｐ−メチルスチレン、ｔｅｒｔ−ブチルスチレン、α−メチルビニルトルエン、ジメチルスチレン、クロルスチレン、ジクロルスチレン、ブロムスチレン、ジブロムスチレン、ビニルナフタレン等を用いることができるが、特にスチレンが好ましい。
【０１１０】
さらに、これらの化合物と共重合可能な他の化合物、例えばアクリロニトリル、メタクリロニトリル等を共重合成分として使用しても差し支えない。
【０１１１】
本発明におけるＣ成分として好ましいものは、カルボキシル基類を有する単量体を共重合してなるスチレン含有共重合体である。かかる共重合体においては比較的多くのカルボキシル基類を安定してスチレン含有重合体中に含むことが可能となるためである。より好適な態様としてカルボキシル基類を有する単量体とスチレン系単量体とを共重合してなるスチレン含有共重合体を挙げることができる。そして殊に好適な態様はスチレン−無水マレイン酸共重合体である。スチレン−無水マレイン酸共重合体は、層状珪酸塩中のイオン成分及び芳香族ポリカーボネート樹脂のいずれに対しても高い相溶性を有することから、層状珪酸塩（Ｂ成分）を良好に微分散させる。さらに、カルボン酸無水物基の作用により層状珪酸塩、殊に有機化層状珪酸塩を含有する樹脂組成物において良好な熱安定性が得られる。またかかる共重合体それ自体の熱安定性が良好であるため、芳香族ポリカーボネート樹脂の溶融加工に必要な高温条件に対しても高い安定性を有する。
【０１１２】
上記カルボキシル基類を有する単量体を共重合してなるスチレン含有共重合体の組成については上述のβの割合における条件を満足する限り制限されないが、カルボキシル基類を有する単量体からの成分を１〜３０重量％（特に５〜２５重量％）、スチレン系単量体化合物成分９９〜７０重量％（特に９５〜７５重量％）を含み、共重合可能な他の化合物成分を０〜２９重量％を含むものを用いるのが好ましく、カルボキシル基類を有する単量体を１〜３０重量％（特に５〜２５重量％）、スチレン系単量体化合物９９〜７０重量％（特に９５〜７５重量％）含む共重合体が特に好ましい。
【０１１３】
また、本発明のＣ成分の好ましい態様であるＣ１成分の分子量は特に制限されない。Ｃ１成分の重量平均分子量は１万〜１００万の範囲にあることが好ましく、５万〜５０万の範囲がより好ましい。尚、ここで示す重量平均分子量は、標準ポリスチレン樹脂による較正直線を使用したＧＰＣ測定によりポリスチレン換算の値として算出されたものである。
【０１１４】
本発明のＣ成分として好適なポリアルキレンオキシドセグメントを有する重合体、殊に好ましいポリエーテルエステル共重合体（Ｃ２成分）について説明する。
【０１１５】
ポリエーテルエステル共重合体は、ジカルボン酸、アルキレングリコール、およびポリ（アルキレンオキシド）グリコール、並びにこれらの誘導体から重縮合を行うことで製造される重合体である。殊に好適な例としては、下記式（ＩＩ）で示されるポリアルキレンオキシド単位を有するポリ（アルキレンオキシド）グリコールあるいはその誘導体（Ｃ２▲１▼成分）、テトラメチレングリコールを６５モル％以上含有するアルキレングリコールあるいはその誘導体（Ｃ２▲２▼成分）、およびテレフタル酸を６０モル％以上含有するジカルボン酸あるいはその誘導体（Ｃ２▲３▼成分）から製造される共重合体である。
【０１１６】
【化２】

【０１１７】
（ここで、Ｘは一価の有機基を表し、ｎおよびｍはいずれも０を含む整数であり、かつ１０≦（ｎ＋ｍ）≦１２０である。ｍが２以上の場合Ｘは互いに同一および異なる態様のいずれも選択できる。）
上記式（ＩＩ）においてＸは−ＣＨ₃、−ＣＨ₂Ｃｌ、−ＣＨ₂Ｂｒ、−ＣＨ₂Ｉ、および−ＣＨ₂ＯＣＨ₃から選択される少なくとも１種の置換基が好ましい。Ｘがこれら以外の場合には置換基による立体障害が大きくなり共重合体の重合度を上げることが困難となる。またｎ＋ｍが１０未満の場合には層状珪酸塩が十分に分散しない場合があり、ｎ＋ｍが１２０を超える場合には、重合度の高いポリエーテルエステル共重合体が得られ難くなり、Ｃ２成分の相溶化機能が低下する場合がある。
【０１１８】
上記式（ＩＩ）におけるポリアルキレンオキシド成分は、ポリエチレンオキシド成分と置換基Ｘを有する成分とのランダム共重合体、テーパード共重合体およびブロック共重合体のいずれも選択できる。上記式（ＩＩ）におけるポリアルキレンオキシドは、特にｍ＝０、すなわちポリエチレンオキシド成分のみからなる重合体成分が好ましい。
【０１１９】
Ｃ２▲１▼成分の共重合割合は、全グリコール成分の３０〜８０重量％であり、より好適には４０〜７０重量％である。Ｃ２▲１▼成分が３０重量％より少ない場合には層状珪酸塩は十分に分散されず、機械特性の低下や外観の悪化を生ずる場合がある。Ｃ２▲１▼成分が８０重量％より多い場合にも層状珪酸塩は十分に分散されず、またポリエーテルエステル共重合体自身の強度低下も加わることで、機械特性の低下や外観の悪化を生ずる場合がある。
【０１２０】
Ｃ２成分のポリエーテルエステル共重合体のＣ２▲２▼成分においては、テトラメチレングリコール以外のジオールを共重合することができる。かかるジオールとしては、エチレングリコール、トリメチレングリコール、１，５−ペンタンジオール、１，６−ヘキサンジオール、ジエチレングリコール、１，４−シクロヘキサンジオール、１，４−シクロヘキサンジメタノールが例示される。Ｃ２▲２▼成分中テトラメチレングリコールは６５モル％以上であり、７５モル％以上が好ましく、８５モル％以上がより好ましい。テトラメチレングリコールが６５モル％未満のポリエーテルエステル共重合体は、熱可塑性樹脂組成物の成形性の低下を招く。
【０１２１】
ポリエーテルエステル共重合体のジカルボン酸あるいはその誘導体（Ｃ２▲３▼成分においては、テレフタル酸以外のジカルボン酸（カルボキシル基が２を超えるものを含む）を共重合することができる。かかるジカルボン酸としては、イソフタル酸、フタル酸、アジピン酸、セバシン酸、アゼライン酸、ドデカン二酸、トリメリット酸、ピロメリット酸、ナフタレンジカルボン酸、シクロヘキサンジカルボン酸が例示される。イソフタル酸を共重合したポリエーテルエステル共重合体はＣ成分として特に好適である。Ｃ２▲３▼成分中テレフタル酸は６０モル％以上であり、７０モル％以上が好ましく、７５〜９５モル％がより好ましい。テレフタル酸が６０モル％未満のポリエーテルエステル共重合体は、共重合体の重合度が低下しやすく、十分な重合度のポリエーテルエステル共重合体の製造が困難となるため好ましくない。
【０１２２】
他の好適なＣ成分としては、親水基としてオキサゾリン基を含有するスチレン含有共重合体が挙げられる。かかる共重合体を形成するスチレン系単量体化合物としては、スチレン、α−メチルスチレン、ｏ−メチルスチレン、ｍ−メチルスチレン、ｐ−メチルスチレン、ｔｅｒｔ−ブチルスチレン、α−メチルビニルトルエン、ジメチルスチレン、クロルスチレン、ジクロルスチレン、ブロムスチレン、ジブロムスチレン、ビニルナフタレン等を用いることができる。さらに、これらの化合物と共重合可能な他の化合物、例えばアクリロニトリル、メタクリロニトリル等、を共重合成分として使用しても差し支えない。中でも、特に好適なものとして、スチレン（２−イソプロペニル−２−オキサゾリン）−スチレン−アクリロニトリル共重合体が例示される。
【０１２３】
本発明のＣ成分の組成割合は、Ａ成分１００重量部あたり０．５〜５０重量部が好ましく、０．５〜２０重量部がより好ましい。０．５重量部より少ない場合には層状珪酸塩の分散効果が十分でなく、また芳香族ポリカーボネート樹脂の熱劣化を抑制する効果も不十分となる場合がある。また５０重量部を超えると耐衝撃性および耐熱性などが低下する場合がある。
【０１２４】
本発明の熱可塑性樹脂組成物には、本発明の効果を発揮する範囲で、Ｂ成分以外の強化充填材を更に配合することができる。強化充填材としては、ガラス繊維、炭素繊維、ガラスフレーク、ワラストナイト、カオリンクレー、マイカ、タルクおよび各種ウイスカー類（チタン酸カリウムウイスカー、ホウ酸アルミニウムウイスカーなど）といった一般に知られている各種フィラーを併用することができる。形状は繊維状、フレーク状、球状、中空状を自由に選択できる。ガラス繊維、炭素繊維およびガラスフレークなどは熱可塑性樹脂組成物の強度や耐衝撃性の向上のためには好適である。一方本発明の樹脂組成物が有する極めて良好な表面外観（表面平滑性）をより有効に活用する場合には、強化充填材の大きさは微小であることが好ましい。具体的には繊維状充填材の場合にはその繊維径が、また板状充填材や粒状充填材の場合にはその大きさが、５μｍ以下が好ましく、４μｍ以下がより好ましく、３μｍ以下が更に好ましい。下限は０．０５μｍ程度が適切である。かかる微小な強化充填材としてはタルク、ワラストナイト、カオリンクレー、および各種ウイスカー類が例示される。強化充填材の配合量は、全熱可塑性樹脂組成物１００重量％あたり５０重量％以下が適切であり、０．５〜５０重量％の範囲が好ましく、１〜３５重量％の範囲がより好ましい。かかる配合量が５０重量％を超えると、成形加工性が悪化し、本発明の効果が得られないため好ましくない。
【０１２５】
さらに本発明の目的を損なわない範囲で、他の熱可塑性樹脂（例えば、ポリアミド樹脂、ポリアセタール樹脂、芳香族ポリエステル樹脂、液晶ポリエステル樹脂、ポリオレフィン樹脂、シンジオタクチックポリスチレン樹脂およびポリフェニレンサルファイド樹脂等の結晶性熱可塑性樹脂）、難燃剤（例えば、臭素化エポキシ樹脂、臭素化ポリスチレン、臭素化ポリカーボネート、臭素化ポリアクリレート、モノホスフェート化合物、ホスフェートオリゴマー化合物、ホスホネートオリゴマー化合物、ホスホニトリルオリゴマー化合物、ホスホン酸アミド化合物、有機スルホン酸アルカリ（土類）金属塩、シリコーン系難燃剤等）、難燃助剤（例えば、アンチモン酸ナトリウム、三酸化アンチモン等）、滴下防止剤（フィブリル形成能を有するポリテトラフルオロエチレン等）、核剤（例えば、ステアリン酸ナトリウム、エチレン−アクリル酸ナトリウム等）、酸化防止剤（例えば、ヒンダ−ドフェノ−ル系化合物、イオウ系酸化防止剤等）、衝撃改良剤、紫外線吸収剤、光安定剤、離型剤、滑剤、着色剤（染料、無機顔料等）、および蛍光増白剤等を配合してもよい。これら各種の添加剤は、芳香族ポリカーボネート樹脂に配合する際の周知の配合量で利用することができる。
【０１２６】
本発明の熱可塑性樹脂組成物は、リン系熱安定剤を含むことが好ましい。かかるリン系熱安定剤としてはトリメチルホスフェート等のリン酸エステル、トリフェニルホスファイト、トリスノニルフェニルホスファイト、ジステアリルペンタエリスリト−ルジホスファイト、ビス（２，６−ジ−ｔｅｒｔ−ブチル−４−メチルフェニル）ペンタエリスリト−ルジホスファイト、トリス（２，４−ジ−ｔｅｒｔ−ブチルフェニル）ホスファイト、２，２−メチレンビス（４，６−ジ−ｔｅｒｔ−ブチルフェニル）オクチルホスファイト、およびビス（２，４−ジ−ｔｅｒｔ−ブチルフェニル）ペンタエリスリトールジホスファイト等の亜リン酸エステル、並びにテトラキス（２，４−ジ−ｔｅｒｔ−ブチルフェニル）−４，４’−ビフェニレンジホスホナイト等の亜ホスホン酸エステルなど、芳香族ポリカーボネート樹脂のリン系熱安定剤として広く知られた化合物が好適に例示される。かかるリン系熱安定剤は全組成物１００重量％中０．００１〜１重量％を含むことが好ましく、０．０１〜０．５重量％を含むことがより好ましく、０．０１〜０．２重量％を含むことが更に好ましい。かかるリン系熱安定剤の配合によりさらに熱安定性が向上し良好な成形加工特性を得ることができる。
【０１２７】
本発明の熱可塑性樹脂組成物を製造するには、任意の方法が採用される。例えば各成分、並びに任意に他の成分を予備混合し、その後溶融混練し、ペレット化する方法を挙げることができる。予備混合の手段としては、ナウターミキサー、Ｖ型ブレンダー、ヘンシェルミキサー、メカノケミカル装置、押出混合機などを挙げることができる。予備混合においては場合により押出造粒器やブリケッティングマシーンなどにより造粒を行うこともできる。予備混合後、ベント式二軸押出機に代表される溶融混練機で溶融混練、およびペレタイザー等の機器によりペレット化する。溶融混練機としては他にバンバリーミキサー、混練ロール、恒熱撹拌容器などを挙げることができるが、ベント式二軸押出機に代表される多軸押出機が好ましい。かかる多軸押出機を用いることにより強力なせん断力で有機化層状珪酸塩は基体樹脂中に微分散させられる。一方その分散は層間を縮小させる作用が存在する下で行われることにより、層間のイオンの外部への露出は抑制される。結果して良好な分散と熱安定性とのより高度な両立が達成される。
【０１２８】
更に、本発明の熱可塑性樹脂組成物の溶融混練機による溶融混練において次の態様がより好適である。すなわち、５０〜２００ミリ当量／１００ｇの陽イオン交換能を有する層状珪酸塩（Ｂ成分）と、Ａ成分の非晶性熱可塑性樹脂との親和性を有しかつ親水性成分を有する化合物（Ｃ成分）、殊に好適にはカルボキシル基及び／又はその誘導体からなる官能基を有するスチレン含有重合体（Ｃ１成分）とを予め溶融混練しておく。その後該溶融混練物とＡ成分の非晶性熱可塑性樹脂、殊に好適には芳香族ポリカーボネート樹脂とを多軸押出機により溶融混練する。かかる溶融混練方法は非晶性熱可塑性樹脂の熱安定性を向上させるため好ましい。芳香族ポリカーボネート樹脂においてはその分子量低下が特に抑制されるため好ましい溶融混練方法である。これはＢ成分とＣ成分とが予め溶融混練されることによりＢ成分に対してＣ成分が十分に相互作用し、所定の効果が効率的に得られているためと考えられる。したがって本発明によれば上記Ｂ成分とＣ成分とを予め溶融混練した後に、該溶融混練物とＡ成分とを多軸押出機を用いて溶融混練してなる、本発明の樹脂組成物および該樹脂組成物の製造方法が提供される。
【０１２９】
より具体的には、例えば、（ｉ）Ｂ成分とＣ成分をベント式二軸押出機にて溶融混練しペレット化したものを、再度Ａ成分と溶融混練する方法や、（ｉｉ）Ｂ成分とＣ成分をベント式二軸押出機の主供給口より投入し、Ａ成分の一部または全部を二軸押出機の途中段階に設けられた供給口から、Ｂ成分とＣ成分が既に溶融混練された状態の中へ投入する方法などが挙げられる。これらＢ成分とＣ成分を予め溶融混練する方法においては、その溶融混練時に、Ａ成分の一部を含んでいても構わない。
【０１３０】
本発明の熱可塑性樹脂組成物は通常上記の如く製造されたペレットを射出成形して各種製品を製造することができる。かかる射出成形においては、通常の成形方法だけでなく、適宜目的に応じて、射出圧縮成形、射出プレス成形、ガスアシスト射出成形、発泡成形（超臨界流体の注入によるものを含む）、インサート成形、インモールドコーティング成形、断熱金型成形、急速加熱冷却金型成形、二色成形、サンドイッチ成形、および超高速射出成形などの射出成形法を用いて成形品を得ることができる。これら各種成形法の利点は既に広く知られるところである。また成形はコールドランナー方式およびホットランナー方式のいずれも選択することができる。
【０１３１】
また本発明の熱可塑性樹脂組成物は、押出成形により各種異形押出成形品、シート、フィルムなどの形で使用することもできる。またシート、フィルムの成形にはインフレーション法や、カレンダー法、キャスティング法なども使用可能である。更に特定の延伸操作をかけることにより熱収縮チューブとして成形することも可能である。また本発明の熱可塑性樹脂組成物を回転成形やブロー成形などにより中空成形品とすることも可能である。
【０１３２】
本発明の熱可塑性樹脂組成物は、良好な剛性を有し、良好な耐加水分解性を有し、更に良好な熱安定性を有する。したがって上記の如く得られた樹脂成形品は、実用上問題のない幅広い成形加工条件の下で製造され、かつ良好な剛性および良好な表面外観を有する。より具体的には本発明によれば、本発明の熱可塑性樹脂組成物より形成された樹脂成形品であって、その表面のＪＩＳ Ｂ０６０１に準拠して測定された算術平均粗さＲａの値が、０．１μｍ以下、かつＡＳＴＭ Ｄ７９０に準拠して測定された曲げ弾性率の値が、２，５００ＭＰａ以上であることを特徴とする樹脂成形品が提供され、かかる樹脂成形品はその工業的価値が更に高い。従来、樹脂成形品の曲げ弾性率を向上させるためには、繊維上強化材や無機充填材を配合するのが一般的であったが、その場合にはその表面粗さは顕著に低下し、上記のバランスをとることができるものが得られていなかったためである。
【０１３３】
樹脂成形品の算術表面粗さＲａの値は、より好ましくは０．０８μｍ以下であり、更に好ましくは０．０５μｍ以下である。かかる下限は成形を行う金型によるところが大きいが約０．００１μｍ程度が適切である。また、曲げ弾性率の値は、より好ましくは２，８００ＭＰａ以上であり、更に好ましくは３，０００ＭＰａ以上である。一方、その上限は８，０００ＭＰａが適切であり、７，０００ＭＰａが好ましく、６，０００ＭＰａがより好ましい。
【０１３４】
本発明の樹脂成形品には、表面改質を施すことにより、平滑性に優れた表面改質成形品を得ることができる。ここでいう表面改質とは、蒸着（物理蒸着、化学蒸着など）、メッキ（電気メッキ、無電解メッキ、溶融メッキなど）、塗装、コーティング、印刷などの樹脂成形品の表層上に新たな層を形成させるものであり、通常の芳香族ポリカーボネート樹脂に用いられる方法が適用できる。これら表面改質では、改質される樹脂成形品の表面平滑性が、改質後の表面性に大きな影響を与えるが、本発明の樹脂成形品を使用すると、表面平滑性に優れた成形品を得ることができる。一般にこれらの表面改質は、表面修飾や機能付与だけでなく、樹脂成形品の表面平滑性を高める目的で施されることもあり、表面平滑性が悪いと改質の厚さを大きくとる必要があるが、本発明の樹脂成形品では、薄い厚みにて効率よく改質することができる。すなわち、５０μｍ以下であることが本発明の効果が発揮され好ましい。更にかかる厚みは２０μｍ以下がより好ましく、５μｍ以下が更に好ましく、２μｍ以下が更に好ましい。下限値としては０．００１μｍ以上が適切である。更に、金属層または金属酸化物層を有しない樹脂成形品単体におけるＪＩＳ Ｂ０６０１に準拠して測定される算術平均粗さＲａの値に対して、かかるＲａの５００倍以内の厚みで表面改質を行うと、本発明の樹脂成形品の特長が生かされ、かかるＲａの２００倍以内の値の厚みであればより好ましく、１００倍以内は更に好ましく、５０倍以内は特に好ましい。本発明において好ましい表面改質方法は、蒸着、メッキなどの改質厚みの小さい手法である。
【０１３５】
本発明の熱可塑性樹脂組成物は、上記の特性を生かし樹脂材料として従来使用できなかった部品に用途展開が可能である。殊に従来ガラス成形品または金属の精密切削品でなければ達成できなかった極めて高い耐加水分解性と剛性が要求される用途に使用可能である。かかる用途としては例えば光学精密機器内に配されたミラー、レーザー式複写・印刷装置などに配されたポリゴンミラー、およびハードディスクなどが例示される。
【０１３６】
更に本発明の熱可塑性樹脂組成物は、各種電子・電気機器、ＯＡ機器、車両部品、機械部品、その他農業資材、漁業資材、搬送容器、包装容器、および雑貨などの各種用途にも有用である。本発明の熱可塑性樹脂組成物は成形加工性にも優れていることから、各種薄肉成形品にも好適であり、薄肉射出成形品の具体例としては、電池ハウジングなどの各種ハウジング成形品、鏡筒、メモリーカード、スピーカーコーン、ディスクカートリッジ、面発光体、マイクロマシン用機構部品、銘板、パソコンのハウジング、ＣＤやＤＶＤドライブのトレーやシャシー、複写機のトレーやシャシー、液晶装置の直下型バックライト用光拡散板（特に大型液晶表示装置（１５インチ以上の大型液晶テレビ）用直下型バックライト用光拡散板）およびＩＣカードなどが例示される。
【０１３７】
【実施例】
以下、実施例により本発明を詳述する。ただし、本発明はこれらに限定されるものではない。なお、実施例中の各種特性の測定は、以下の方法によった。原料は以下の原料を用いた。
（１）熱可塑樹脂組成物中の層状珪酸塩（無機分）の含有量
試験片を射出成形機（東芝機械（株）製：ＩＳ−１５０ＥＮ）によりシリンダー温度２６０℃、金型温度８０℃、成形サイクル４０秒で成形し、成形した試験片を切削してるつぼに入れて秤量し、６００℃まで昇温し、そのまま６時間保持した後で放冷し、るつぼに残った灰化残渣を秤量することで層状珪酸塩（無機分）の量を測定した。すなわち、樹脂組成物の曲げ弾性率（剛性）等の特性は無機分の割合によって影響されるため、各実施例および比較例２、３では、試験片中の無機分の割合を測定し、表１にＢ成分の無機分の割合（重量％）として表示した。
（２）熱可塑樹脂組成物中の層状珪酸塩のシリケート層の底面間隔および平均積層数
粉末Ｘ銭回折装置（ＲＩＧＡＫＵ ＲＯＴＡＦＬＥＸ ＲＵ３００：（株）リガク製）を用いて測定を行った。厚み６．４ｍｍの棒状試験片を（１）と同条件にて成形し、長さ２０ｍｍに切断した測定成形品を、試料台の開口部に測定基準面と同一面になるように固定して測定に供した。測定によって得られた回折ピークは層状珪酸塩の底面ピークであるが、そのうち、最も小角側の回折ピークが（００１）面の底面間隔に対応するピークであるとして、下記Ｂｒａｇｇの式により底面間隔を算出した。
ｄ＝λ／（２ｓｉｎθ）
（但し、式中 ｄ：底面間隔（層間距離）（ｎｍ）、２θ：回折ピークの回折角度（°）、λ：Ｘ線測定波長（ｎｍ））
更に、下記式から平均積層数（Ｎ）を求めた。
Ｎ＝（Ｄ／ｄ）＋１
（但し、式中 Ｎ：積層数（枚）、Ｄ：積層厚み（ｎｍ）、ｄ：底面間隔（ｎｍ））
Ｄ＝０．９＊λ／（βｃｏｓΘ）
（但し、式中 Ｄ：積層厚み（ｎｍ）、λ：Ｘ線測定波長（ｎｍ）、β：半値幅（ｒａｄ）、２Θ：回折ピークの回折角度（ｒａｄ）、ここで半値幅は回折ピークの最大値Ｉ₀の１／２の高さにおける２Θ（ｒａｄ）の幅であり、回折ピークの回折角度とはピークの最大値Ｉ₀部分での２Θの値を指す）
尚、測定の条件については以下に示す。
Ｘ−ｒａｙ ｓｏｕｒｃｅ：Ｃｕ−Ｋα（Ｘ線測定波長１．５４１８×１０^-10ｍ）、５０ｋＶ−２００ｍＡ
Ｓｌｉｔ：ＤＳ／ＳＳ １／２°
Ｒｓ ０．１５ｍｍ−ｇｒａｐｈｉｔｅ ｍｏｎｏｃｈｒｏｍｅｔｅｒ−０．４５ｍｍ
Ｍｅｔｈｏｄ：２θ−θ
Ｓｃａｎ：０．０５ｓｔｅｐ／１〜４ｓｅｃ
Ｓｃａｎ範囲：１〜２０°
【０１３８】
（３）熱可塑性樹脂組成物における粘度平均分子量
試験片を上記（１）と同条件で成形し、試験片の粘度平均分子量を本文中記載の方法にて測定した。
（４）曲げ弾性率
前記（１）と同条件で成形した同形状の試験片（寸法：長さ１２７ｍｍ×幅１２．７ｍｍ×厚み６．４ｍｍ）を、温度２３℃および相対湿度５０％ＲＨの雰囲気下においてＡＳＴＭ−Ｄ７９０に準拠の方法により曲げ弾性率（ＭＰａ）を測定した。この数値が大きいほど成形した樹脂組成物の剛性が優れていることを意味する。
（５）高温高湿試験後の粘度平均分子量の低下率（ΔＭ_ratio）
前記（１）と同条件で成形した同形状の試験片（寸法：長さ１２７ｍｍ×幅１２．７ｍｍ×厚み６．４ｍｍ）を温度１０５℃、相対湿度１００％のプレッシャークッカーに１０時間放置して処理した後、温度２３℃、相対湿度５０％の環境下で２４時間放置した試験片（処理後の試験片）を用いて測定した粘度平均分子量と、温度２３℃、相対湿度５０％の環境下で７４時間放置した試験片（処理前の試験片）を用いて測定した粘度平均分子量を、下記数式にしたがって計算し、恒温恒湿試験後の粘度平均分子量の低下率（ΔＭ_ratio）を算出した。
ΔＭ_ratio＝１００×［（処理前の試験片の粘度平均分子量）−（処理後の試験片の粘度平均分子量）］／（処理前の試験片の粘度平均分子量）
この数値が小さいほど成形した樹脂組成物の耐加水分解性が良好であることを示す。
【０１３９】
［原料］
原料としては、以下のものを用いた。
（Ａ成分：ポリカーボネート樹脂）
粘度平均分子量２３，８００のビスフェノールＡ型芳香族ポリカ−ボネ−ト樹脂パウダー［帝人化成（株）製「パンライトＬ−１２５０ＷＰ」］
【０１４０】
（Ｂ成分およびＢ成分以外）
Ｂ−１：合成雲母（ソマシフ ＭＥ−１００：コープケミカル（株）製、陽イオン交換容量：１１０ミリ当量／１００ｇ）
Ｂ−２：合成雲母（ソマシフ ＭＥ−１００：コープケミカル（株）製）にトリオクチルメチルアンモニウムクロライドをほぼ完全にイオン交換したもの
Ｂ−３：合成雲母（ソマシフ ＭＥ−１００：コープケミカル（株）製）にジデシルジメチルアンモニウムクロライドをほぼ完全にイオン交換したもの
Ｂ−４：合成雲母（ソマシフ ＭＥ−１００：コープケミカル（株）製）にトリフェニルメチルアンモニウムクロライドをほぼ完全にイオン交換したもの
Ｂ−５：合成雲母（ソマシフ ＭＥ−１００：コープケミカル（株）製）にジオクタデシルジメチルアンモニウムクロライドをほぼ完全にイオン交換したもの
【０１４１】
（Ｃ成分）
Ｃ−１：スチレン−無水マレイン酸共重合体（ノヴァケミカルジャパン（株）製：「ＤＹＬＡＲＫ ３３２−８０」、無水マレイン酸量約１５重量％）
（その他の成分）
ＴＭＰ：トリメチルホスフェート（大八化学工業（株）製：ＴＭＰ）、添加量は全ての組成物でＡ成分１００重量部当り０．１重量部。
【０１４２】
［実施例１、２、比較例１〜３］
Ｂ成分とＣ成分を、表１の量割合にて、径３０ｍｍφ、Ｌ／Ｄ＝３３．２、混練ゾーン２箇所のスクリューを装備したベント付き二軸押出機（（株）神戸製鋼所製：ＫＴＸ３０）を用い、シリンダー温度２００℃にて溶融混練し、押出し、ストランドカットしてペレットを得た。得られたペレットを用い、最終割合が表３に示す割合になるよう、上記Ｂ成分とＣ成分の混合物と、Ａ成分などをドライブレンドした後、径３０ｍｍφ、Ｌ／Ｄ＝３３．２、混練ゾーン２箇所のスクリューを装備したベント付き二軸押出機（（株）神戸製鋼所製：ＫＴＸ３０）を用い、シリンダー温度２８０℃にて溶融混練し、押出し、ストランドカットしてペレットを得た。
【０１４３】
得られたペレットを１００℃で５時間熱風循環式乾燥機により乾燥した。乾燥後、試験片を射出成形機（東芝機械（株）製：ＩＳ−１５０ＥＮ）によりシリンダー温度２６０℃、金型温度８０℃、成形サイクル４０秒で成形した。これらについての測定結果を表１に示す。
【０１４４】
【表１】

【０１４５】
上記表から明らかなように、本発明の熱可塑性樹脂組成物は特定の分散形態を満足することにより、良好な剛性および極めて良好な耐加水分解性を有し、更に良好な熱安定性を有する熱可塑性樹脂組成物を提供することがわかる。殊に熱安定性はＢ成分の層状珪酸塩とＣ成分とを予め混練した場合において特に良好である。これにより実用的であり幅広い分野において適用可能な層状珪酸塩を含んでなる熱可塑性樹脂組成物、殊に芳香族ポリカーボネート樹脂組成物が提供される。上記の特有の効果は具体的には本発明の特異な分散状態で得られていることが判る。この分散状態によって、剛性、耐加水分解性の向上が顕著になる。
【０１４６】
【発明の効果】
本発明の熱可塑性樹脂組成物は、良好な剛性を有し、良好な耐加水分解性を有し、更に良好な熱安定性を有する熱可塑性樹脂組成物、殊に芳香族ポリカーボネート樹脂からなる熱可塑性樹脂組成物である。更に本発明の熱可塑性樹脂組成物は射出成形および押出成形の双方に適した溶融粘度特性を有しており成形加工性に優れる。したがって本発明の熱可塑性樹脂組成物、電気電子部品分野、ＯＡ機器部品分野、自動車部品分野、農業資材分野、漁業資材分野、搬送容器分野、包装容器分野、および雑貨分野等の幅広い分野において有用であり、特に電気電子部品分野、のＯＡ機器部品分野、自動車部品分野に有用であり、その奏する工業的効果は格別である。[0001]
TECHNICAL FIELD OF THE INVENTION
The present invention relates to a thermoplastic resin composition comprising an amorphous thermoplastic resin and a layered silicate, particularly an organically modified layered silicate, wherein the layered silicate has a specific dispersion structure. In particular, the present invention is a thermoplastic resin composition having a high rigidity obtained by finely dispersing a layered silicate, has a small decrease in molecular weight, is excellent in thermal stability, and has environmental stability under high temperature and high humidity. The present invention relates to a novel thermoplastic resin composition having significantly improved hydrolysis resistance.
[0002]
[Prior art]
In recent years, the surface appearance and specific gravity of molded products have been improved by using clay minerals, especially layered silicates, as inorganic fillers and ion-exchanging the interlayer ions with various organic onium ions to facilitate dispersion in the resin. Many attempts have been made to improve the mechanical properties while maintaining the above conditions, especially for polyamide resins and polyolefin resins, and practical examples can be seen in these.
[0003]
However, at present, none of the resin compositions of aromatic polycarbonate resins in which these layered silicates or the like are finely dispersed have sufficient thermal stability and are poor in practicality. In other words, it has the same good surface appearance as a resin alone without an inorganic filler, etc., has the same rigidity as a resin reinforced with a reinforced filler, and exhibits practically sufficient thermal stability. At present, a thermoplastic resin composition comprising a thermoplastic resin has not been obtained.
[0004]
In general, as a means for improving the rigidity (flexural modulus) of a thermoplastic resin, mixing of a fibrous reinforcing material such as glass fiber and an inorganic filler has been performed. There are drawbacks in that the specific gravity increases and the surface appearance of the product is impaired.
[0005]
On the other hand, as one of the techniques for achieving a high flexural modulus with a relatively small amount of filler, a layered silicate as an inorganic filler, more preferably, an interlayer ion of such a layered silicate is ion-exchanged with various organic onium ions. A layered silicate obtained by finely dispersing in a thermoplastic resin, a layered silicate obtained by ion-exchanging interlayer ions between an aromatic polycarbonate resin and a layered silicate with various organic onium ions. Are also known (see Patent Documents 1 to 6).
[0006]
Examples of the organic onium ion for ion-exchanging interlayer ions of the layered silicate include an organic onium ion having an alkyl group having 12 or more carbon atoms represented by dimethyldioctadecyl ammonium ion and a polyethylene glycol chain. Have been proposed (see Patent Literature 2 and Patent Literature 3). Furthermore, for thermoplastic resins in general, a quaternary ammonium ion having 15 to 30 carbon atoms is preferable as an organic onium ion (see Patent Document 7), and a quaternary ammonium ion (or phosphonium ion) It has also been proposed that one of the organic groups has 8 or more carbon atoms and the other three organic groups are preferably organic onium ions having 1 to 4 carbon atoms (see Patent Document 8). ).
[0007]
In any of these proposals, there is no suggestion as to the hydrolysis resistance of the thermoplastic resin composition, and in fact, in the thermoplastic resin composition containing a layered silicate ion-exchanged with such an organic onium ion, Since there is a problem in hydrolysis resistance, the improvement of hydrolysis resistance in an amorphous thermoplastic resin composition such as an aromatic polycarbonate resin containing such a layered silicate is important for further increasing its practicality. Technical issues.
[0008]
By the way, Non-Patent Documents 1 to 3 discuss a polycarbonate resin / compatibilizer / organic fluoromica-based resin composition by melt-kneading, and the composition has a relatively small decrease in molecular weight and heat resistance. Discloses that the flexural modulus is excellent. Further, Non-Patent Documents 2 and 3 also disclose that fluoromica is dispersed in 3 to 4 layers. However, such a non-patent document does not describe the distance between the bottom surfaces, and furthermore, has an appropriate dispersion state of the present invention and one of its effects, that is, good molded article having good hydrolysis resistance under high temperature and high humidity (hereinafter referred to as “hydrolysis resistance”). , Simply referred to as hydrolysis resistance.). In addition, the composition is not completely suppressed in molecular weight reduction, and has poor hydrolysis resistance under high temperature and high humidity, and has a low melting temperature at the time of pelletization and a high storage condition for molded articles. Care needed to be taken not to be humid.
[0009]
[Patent Document 1]
JP-A-3-215558
[Patent Document 2]
JP-A-7-207134
[Patent Document 3]
JP-A-7-228762
[Patent Document 4]
JP-A-7-331092
[Patent Document 5]
JP-A-9-143359
[Patent Document 6]
JP-A-10-60160
[Patent Document 7]
JP-A-2002-88255
[Patent Document 8]
WO 99/32403 (Japanese Unexamined Patent Publication No. 2001-526313)
[Non-patent document 1]
The 51st Annual Meeting of the Society of Polymer Science, Vol. 51 (No. 3), p. 669, 2002
[Non-patent document 2]
Molding '02, p. 15, 2002
[Non-Patent Document 3]
The 51st Symposium of the Society of Polymer Science, Vol. 51 (No. 11), p. 2645, 2002
[0010]
[Problems to be solved by the invention]
In view of the above problems, an object of the present invention is a thermoplastic resin composition in which a layered silicate has achieved an unprecedented finely dispersed state, and has a good rigidity and a good hydrolysis resistance. It is another object of the present invention to provide a thermoplastic resin composition having good thermal stability, in particular, having a small decrease in molecular weight and having a good thermal stability, particularly a thermoplastic resin composition comprising an aromatic polycarbonate resin.
[0011]
The present inventors have conducted intensive studies in order to achieve such an object, and as a result, a layered silicate is dispersed in a thermoplastic resin. It has been found that the above problems can be solved by being in the range, that is, by creating a dispersion state that cannot be achieved by a resin composition containing a conventional layered silicate. The present inventors have conducted further intensive studies based on such a finding, and have completed the present invention. That is, the characteristics of the thermoplastic resin composition of the present invention include a means for using a specific raw material, a means for using a high-purity raw material, a means for setting the composition ratio of the thermoplastic resin composition to a specific range, and preparation of a master batch in advance. However, this cannot be achieved even by using a single means, a means for applying a shearing force during melt-kneading, or the like. This has been achieved for the first time by obtaining the dispersion state of the present invention using a plurality of these various means.
[0012]
[Means for Solving the Problems]
The present invention relates to (1) (A) a layered silicate (component (B)) having a cation exchange capacity of 50 to 200 meq / 100 g per 100 parts by weight of an amorphous thermoplastic resin (component (A)). .1 to 50 parts by weight of the thermoplastic resin composition, wherein the component B has an average number of stacked silicate layers of 5 to 40 determined by X-ray diffraction in the resin composition, and the bottom surface interval is The present invention relates to a thermoplastic resin composition having a range of 1.3 to 2.3 nm.
[0013]
One preferred embodiment of the present invention is (2) an organically modified layered silicate in which the component B is ion-exchanged between layers of organic onium ions at a ratio of 40% or more of the cation exchange capacity of the layered silicate. The thermoplastic resin composition according to (1) above,
[0014]
One preferred embodiment of the present invention is that (3) the thermoplastic resin composition further has an affinity for (C) the amorphous thermoplastic resin of component (C) per 100 parts by weight of component A, and The thermoplastic resin composition according to any one of the above (1) and (2), comprising 0.1 to 50 parts by weight of a compound having a hydrophilic component (component C).
[0015]
One preferred embodiment of the present invention is the thermoplastic resin composition according to any one of (1) to (3), wherein (4) the component A is at least 50% by weight of an aromatic polycarbonate resin.
[0016]
One of preferred embodiments of the present invention is (5) the component (C), wherein the C component is a styrene-containing polymer having a functional group consisting of a carboxyl group and / or a derivative thereof. It is a thermoplastic resin composition.
[0017]
One preferred embodiment of the present invention is (6) after melt-kneading the components B and C in advance, and then melt-kneading the melt-kneaded product and the component A using a multi-screw extruder. The thermoplastic resin composition according to any one of (3) to (5).
[0018]
Hereinafter, the present invention will be described in detail.
<About component A>
In the present invention, examples of the amorphous thermoplastic resin (component A) include, for example, polystyrene, acrylic resin, AS resin (resin mainly composed of acrylonitrile-styrene copolymer), and SMA resin (styrene-maleic anhydride copolymer mainly). Resins), MS resins (resins mainly composed of methyl methacrylate-styrene copolymer), ABS resins (resins mainly composed of acrylonitrile-styrene-butadiene copolymer), and amorphous engineering plastics such as aromatic polycarbonate resins. Is exemplified.
[0019]
Further, a preferred amorphous thermoplastic resin in the present invention is an amorphous thermoplastic resin having a glass transition temperature (Tg) of 120 ° C. or higher. Such Tg is more preferably at least 130 ° C, further preferably at least 140 ° C. On the other hand, the Tg is suitably 280 ° C or lower, and preferably 250 ° C or lower. Such a high Tg amorphous thermoplastic resin requires a high molding temperature, and improvement of its thermal stability is more demanded. Incidentally, the glass transition temperature in the present invention is measured by a method specified in JIS K7121.
[0020]
Preferred embodiments of the amorphous thermoplastic resin, for example, aromatic polycarbonate resin, polyphenylene oxide resin, polysulfone resin, polyethersulfone resin, polyarylate resin, cyclic polyolefin resin, polyetherimide resin, polyamideimide resin, Examples thereof include a polyimide resin and a polyaminobismaleimide resin. More preferably, among these, an aromatic polycarbonate resin, a polyarylate resin, and a cyclic polyolefin resin which are excellent in moldability and can be applied to a wider range of fields are exemplified. As the amorphous thermoplastic resin of the present invention, among the above, an aromatic polycarbonate resin having particularly excellent mechanical strength is preferable. Therefore, at least 50% by weight of the component A is preferably an aromatic polycarbonate resin. Further, one or more kinds of other thermoplastic resins such as an ABS resin and an aromatic polyester resin may be used in combination with the aromatic polycarbonate resin.
[0021]
The aromatic polycarbonate resin particularly suitable as the amorphous thermoplastic resin of the component A of the present invention will be described.
[0022]
The representative aromatic polycarbonate resin of the present invention is obtained by reacting a dihydric phenol with a carbonate precursor, and the reaction may be performed by an interfacial polycondensation method, a melt transesterification method, or a solidification of a carbonate prepolymer. Examples include a phase transesterification method and a ring-opening polymerization method of a cyclic carbonate compound.
[0023]
Specific examples of the dihydric phenol include hydroquinone, resorcinol, 4,4′-biphenol, 1,1-bis (4-hydroxyphenyl) ethane, and 2,2-bis (4-hydroxyphenyl) propane (commonly called “bisphenol A ″), 2,2-bis (4-hydroxy-3-methylphenyl) propane, 2,2-bis (4-hydroxyphenyl) butane, 1,1-bis (4-hydroxyphenyl) -1-phenylethane 1,1-bis (4-hydroxyphenyl) cyclohexane, 1,1-bis (4-hydroxyphenyl) -3,3,5-trimethylcyclohexane, 2,2-bis (4-hydroxyphenyl) pentane, 4, 4 '-(p-phenylenediisopropylidene) diphenol, 4,4'-(m-phenylenediisopropylidene) Phenol, 1,1-bis (4-hydroxyphenyl) -4-isopropylcyclohexane, bis (4-hydroxyphenyl) oxide, bis (4-hydroxyphenyl) sulfide, bis (4-hydroxyphenyl) sulfoxide, bis (4- (Hydroxyphenyl) sulfone, bis (4-hydroxyphenyl) ketone, bis (4-hydroxyphenyl) ester, 2,2-bis (3,5-dibromo-4-hydroxyphenyl) propane, bis (3,5-dibromo- 4-hydroxyphenyl) sulfone, bis (4-hydroxy-3-methylphenyl) sulfide, 9,9-bis (4-hydroxyphenyl) fluorene, 9,9-bis (4-hydroxy-3-methylphenyl) fluorene, etc. Is mentioned. Among these, bis (4-hydroxyphenyl) alkane, particularly bisphenol A (hereinafter sometimes abbreviated as “BPA”) is widely used.
[0024]
In the present invention, besides the bisphenol A-based polycarbonate resin which is a general-purpose aromatic polycarbonate resin, for the purpose of obtaining better hydrolysis resistance, a special aromatic polycarbonate resin using other dihydric phenols is used. It can be used as the A component.
[0025]
For example, as part or all of the dihydric phenol component, 4,4 ′-(m-phenylenediisopropylidene) diphenol (hereinafter sometimes abbreviated as “BPM”), 1,1-bis (4-hydroxy Phenyl) cyclohexane, 1,1-bis (4-hydroxyphenyl) -3,3,5-trimethylcyclohexane (hereinafter sometimes abbreviated as “Bis-TMC”), 9,9-bis (4-hydroxyphenyl) Aromatic polycarbonate resins (homopolymers or copolymers) using fluorene and 9,9-bis (4-hydroxy-3-methylphenyl) fluorene (hereinafter sometimes abbreviated as “BCF”) are polymers themselves. Has good hydrolysis resistance, so that it is suitable for applications where dimensional changes and dimensional stability due to water absorption are particularly severe. These dihydric phenols other than BPA are preferably used in an amount of 5 mol% or more, particularly 10 mol% or more of the entire dihydric phenol component constituting the aromatic polycarbonate resin.
[0026]
Particularly, when high rigidity and better hydrolysis resistance are required, the component A constituting the aromatic polycarbonate resin composition is the following copolymerized polycarbonate resin (1) to (3). Is particularly preferred.
(1) BPM is 20 to 80 mol% (more preferably 40 to 75 mol%, and still more preferably 45 to 65 mol%) in 100 mol% of the dihydric phenol component constituting the aromatic polycarbonate resin. And a copolycarbonate resin having a BCF of 20 to 80 mol% (more preferably 25 to 60 mol%, and still more preferably 35 to 55 mol%).
(2) BPA is 10 to 95 mol% (more preferably 50 to 90 mol%, more preferably 60 to 85 mol%) in 100 mol% of the dihydric phenol component constituting the aromatic polycarbonate resin. And a copolycarbonate resin having a BCF of 5 to 90 mol% (more preferably 10 to 50 mol%, and still more preferably 15 to 40 mol%).
(3) BPM is 20 to 80 mol% (more preferably 40 to 75 mol%, more preferably 45 to 65 mol%) in 100 mol% of the dihydric phenol component constituting the aromatic polycarbonate resin. And a copolymer polycarbonate resin having a Bis-TMC of 20 to 80 mol% (more preferably 25 to 60 mol%, and still more preferably 35 to 55 mol%).
[0027]
These special aromatic polycarbonate resins may be used alone, or two or more kinds may be appropriately mixed and used. These can also be used by mixing with a commonly used bisphenol A type aromatic polycarbonate resin.
[0028]
The production method and properties of these special aromatic polycarbonate resins are described, for example, in JP-A-6-172508, JP-A-8-27370, JP-A-2001-55435, and JP-A-2002-117580. It is described in detail.
[0029]
Among the above-mentioned various aromatic polycarbonate resins, those whose water absorption and Tg (glass transition temperature) are adjusted to the following ranges by adjusting the copolymer composition and the like have the hydrolysis resistance of the polymer itself. Since it is excellent and has extremely low warpage after molding, it is particularly suitable in the field of, for example, a mirror or the like, which requires form stability.
(I) an aromatic polycarbonate resin having a water absorption of 0.05 to 0.15%, preferably 0.06 to 0.13%, and a Tg of 120 to 180 ° C, or
(Ii) Tg is 160 to 250 ° C, preferably 170 to 230 ° C, and water absorption is 0.10 to 0.30%, preferably 0.13 to 0.30%, more preferably 0.14 to 0.30%. Aromatic polycarbonate resin that is 0.27%.
[0030]
Here, the water absorption of the aromatic polycarbonate resin was measured using a disc-shaped test piece having a diameter of 45 mm and a thickness of 3.0 mm and immersed in water at 23 ° C. for 24 hours in accordance with ISO62-1980. Value. Further, Tg (glass transition temperature) is a value determined by a differential scanning calorimeter (DSC) measurement based on JIS K7121.
[0031]
On the other hand, as the carbonate precursor, carbonyl halide, carbonate ester, haloformate, or the like is used, and specific examples include phosgene, diphenyl carbonate, and dihaloformate of dihydric phenol.
[0032]
In producing a polycarbonate resin from such a dihydric phenol and a carbonate precursor by an interfacial polymerization method, if necessary, a catalyst, a terminal stopper and an antioxidant for preventing the dihydric phenol from being oxidized. An agent may be used. Further, the aromatic polycarbonate resin may be a branched polycarbonate resin obtained by copolymerizing a polyfunctional aromatic compound having three or more functional groups. Examples of the polyfunctional aromatic compound having three or more functional groups include 1,1,1-tris (4-hydroxyphenyl) ethane and 1,1,1-tris (3,5-dimethyl-4-hydroxy). Phenyl) ethane and the like.
[0033]
When a polyfunctional compound that produces a branched polycarbonate resin is contained, the proportion thereof is 0.001 to 1 mol%, preferably 0.005 to 0.9 mol%, and particularly preferably 0.01 to 1 mol%, based on the total amount of the aromatic polycarbonate resin. 0.8 mol%. In addition, particularly in the case of the melt transesterification method, a branched structure may occur as a side reaction, and the amount of such a branched structure is also 0.001 to 1 mol%, preferably 0.005 to 5 mol%, of the total amount of the aromatic polycarbonate resin. It is preferably 0.9 mol%, particularly preferably 0.01 to 0.8 mol%. In addition, about the ratio of such a branched structure,¹It can be calculated by 1 H-NMR measurement.
[0034]
Further, the aromatic polycarbonate resin as the component A includes a polyester carbonate obtained by copolymerizing an aromatic or aliphatic (including alicyclic) bifunctional carboxylic acid, and a bifunctional alcohol (including an alicyclic group). It may be a copolymerized polycarbonate resin and a polyester carbonate obtained by copolymerizing the bifunctional carboxylic acid and the bifunctional alcohol together. A mixture obtained by blending two or more of the obtained aromatic polycarbonate resins may be used.
[0035]
The aliphatic bifunctional carboxylic acid used here is preferably α, ω-dicarboxylic acid. Examples of the aliphatic bifunctional carboxylic acid include straight-chain saturated aliphatic dicarboxylic acids such as sebacic acid (decane diacid), dodecandioic acid, tetradecandioic acid, octadecandioic acid, and icosane diacid, and cyclohexanedicarboxylic acid. And the like. Preferred are alicyclic dicarboxylic acids. As the bifunctional alcohol, an alicyclic diol is more preferable, and examples thereof include cyclohexanedimethanol, cyclohexanediol, and tricyclodecanedimethanol.
[0036]
Further, in the present invention, it is possible to use a polycarbonate-polyorganosiloxane copolymer obtained by copolymerizing a polyorganosiloxane unit.
[0037]
The aromatic polycarbonate resin as the component A in the resin composition of the present invention includes various aromatic resins such as the above-described polycarbonate resins having different dihydric phenols, polycarbonate resins containing a branching component, polyester carbonate, and polycarbonate-polyorganosiloxane copolymer. It may be a mixture of two or more of the aromatic polycarbonate resins. Further, a mixture of two or more kinds of polycarbonate resins having different production methods, polycarbonate resins having different terminal stoppers and the like can also be used.
[0038]
In the polymerization reaction of the aromatic polycarbonate resin, the reaction by the interfacial polycondensation method is usually a reaction between dihydric phenol and phosgene, and is performed in the presence of an acid binder and an organic solvent. Examples of the acid binder include alkali metal hydroxides such as sodium hydroxide and potassium hydroxide and amine compounds such as pyridine. As the organic solvent, for example, halogenated hydrocarbons such as methylene chloride and chlorobenzene are used. In order to promote the reaction, a catalyst such as a tertiary amine such as triethylamine, tetra-n-butylammonium bromide, or tetra-n-butylphosphonium bromide, a quaternary ammonium compound, or a quaternary phosphonium compound is used. You can also. At that time, the reaction temperature is usually 0 to 40 ° C., the reaction time is preferably about 10 minutes to 5 hours, and the pH during the reaction is preferably maintained at 9 or more.
[0039]
In such a polymerization reaction, a terminal stopper is usually used. Monofunctional phenols can be used as such a terminal stopper. As the monofunctional phenols, it is preferable to use monofunctional phenols such as phenol, p-tert-butylphenol and p-cumylphenol. Further, examples of the monofunctional phenols include decylphenol, dodecylphenol, tetradecylphenol, hexadecylphenol, octadecylphenol, eicosylphenol, docosylphenol, and tricontylphenol. Such terminal stoppers may be used alone or in combination of two or more.
[0040]
The reaction by the melt transesterification method is usually a transesterification reaction between a dihydric phenol and a carbonate ester. The dihydric phenol and the carbonate ester are mixed while heating in the presence of an inert gas to form an alcohol or It is carried out by a method of distilling phenol. The reaction temperature varies depending on the boiling point of the alcohol or phenol to be formed, but in most cases is in the range of 120 to 350 ° C. In the late stage of the reaction, the reaction system was 1.33 × 10^ThreeThe alcohol or phenol produced by reducing the pressure to about 13.3 Pa is easily distilled. The reaction time is about 1 to 4 hours.
[0041]
Examples of the carbonate ester include an ester such as an aryl group having 6 to 10 carbon atoms which may have a substituent, an aralkyl group or an alkyl group having 1 to 4 carbon atoms, among which diphenyl carbonate is preferable. .
[0042]
Further, a polymerization catalyst can be used to increase the polymerization rate. Examples of such a polymerization catalyst include alkali metal compounds such as sodium hydroxide, potassium hydroxide, sodium salts and potassium salts of dihydric phenols; alkaline earth metal compounds such as calcium hydroxide, barium hydroxide, and magnesium hydroxide; A catalyst such as a nitrogen-containing basic compound such as methylammonium hydroxide, tetraethylammonium hydroxide, trimethylamine and triethylamine can be used. Further, esterification reaction, transesterification of alkali (earth) metal alkoxides, alkali (earth) metal organic acid salts, boron compounds, germanium compounds, antimony compounds, titanium compounds, zirconium compounds, etc. The catalyst used for the reaction can be used. The catalyst may be used alone or in combination of two or more. The amount of these polymerization catalysts used is preferably 1 × 10^-8~ 1 × 10^-3Equivalent, more preferably 1 × 10^-7~ 5 × 10^-FourIt is selected within the range of equivalents.
[0043]
In the reaction by the melt transesterification method, for example, 2-chlorophenylphenyl carbonate, 2-methoxycarbonylphenylphenyl carbonate, 2-ethoxycarbonyl, for the purpose of reducing the phenolic terminal group of the produced polycarbonate resin at a later stage or after completion of the polycondensation reaction. Compounds such as phenylphenyl carbonate can be added.
[0044]
Further, in the melt transesterification method, it is preferable to use a deactivator for neutralizing the activity of the catalyst. The amount of the deactivator is preferably 0.5 to 50 mol per 1 mol of the remaining catalyst. Moreover, it is suitable to use it at a ratio of 0.01 to 500 ppm, more preferably 0.01 to 300 ppm, particularly preferably 0.01 to 100 ppm, based on the polycarbonate resin after polymerization. Examples of preferred quenching agents include phosphonium salts such as tetrabutylphosphonium dodecylbenzenesulfonate and ammonium salts such as tetraethylammonium dodecylbenzyl sulfate.
[0045]
The viscosity average molecular weight of the aromatic polycarbonate resin as the component A is not limited. However, when the viscosity average molecular weight is less than 10,000, the strength and the like are reduced, and when the viscosity average molecular weight is more than 50,000, the molding characteristics are deteriorated. The range is more preferably from 3,000 to 30,000, and even more preferably from 14,000 to 28,000. In this case, it is also possible to mix a polycarbonate resin having a viscosity average molecular weight outside the above-mentioned range as long as the moldability and the like are maintained. For example, a high molecular weight aromatic polycarbonate resin component having a viscosity average molecular weight exceeding 50,000 can be blended.
[0046]
First, the viscosity average molecular weight referred to in the present invention is a specific viscosity (η) calculated by the following equation._SP) Was determined at 20 ° C. from a solution of 0.7 g of an aromatic polycarbonate resin dissolved in 100 ml of methylene chloride using an Ostwald viscometer.
Specific viscosity (η_SP) = (Tt)₀) / T₀
[T₀Is the number of seconds of falling methylene chloride, and t is the number of seconds of falling of the sample solution.
The calculated specific viscosity (η_SP) Is used to calculate the viscosity average molecular weight M by the following equation.
η_SP/C=[η]+0.45×[η]^Twoc (where [η] is the intrinsic viscosity)
[Η] = 1.23 × 10^-FourM^0.83
c = 0.7
[0047]
The viscosity average molecular weight of the thermoplastic resin composition of the present invention is measured in the following manner. That is, the composition is dissolved in 20 to 30 times the weight of methylene chloride, and the soluble matter is collected by filtration through celite, the solution is removed and dried sufficiently, and the solid matter soluble in methylene chloride is removed. obtain. From a solution of 0.7 g of the solid dissolved in 100 ml of methylene chloride, the specific viscosity at 20 ° C. calculated by the above equation is measured by using an Ostwald viscometer.
[0048]
<About component B>
The component B of the present invention is a layered silicate having a cation exchange capacity of 50 to 200 meq / 100 g. Further preferably, in the present invention, the component B of the present invention has a cation exchange capacity of 50 to 200 meq / 100 g, and an organic onium ion is present between the layers in an amount of 40% or more of the cation exchange capacity. It is a layered silicate that has been exchanged. Here, the ratio of 40% means, for example, when the cation exchange capacity of the layered silicate is 110 meq / 100 g, 44 meq / 100 g corresponding to 40% thereof is ion-exchanged with organic onium ions. Point. In the following, the “layer silicate having a cation exchange capacity and formed by ion exchange of organic onium ions between layers” may be simply referred to as “organized layered silicate”.
[0049]
The organic onium ion compound in the organically modified layered silicate of the present invention is generally handled as a salt with anions such as a halogen ion, a hydroxide ion and an acetate ion. It is obtained by reacting such a salt compound of an organic onium ion with a layered silicate. Here, examples of the organic onium ion include an ammonium ion, a phosphonium ion, a sulfonium ion, an onium ion derived from a heteroaromatic ring, and the like. As the onium ion, any of primary, secondary, tertiary, and quaternary can be used. However, a quaternary onium ion is preferable.
[0050]
As the onium ion compound, those having various organic groups bonded thereto can be used. The organic group is typically an alkyl group, but may have an aromatic group, or may have an ether group, an ester group, a double bond, a triple bond, a glycidyl group, a carboxylic acid group, or an acid anhydride group. And various functional groups such as a hydroxyl group, an amino group, an amide group and an oxazoline ring.
[0051]
Specific examples of the organic onium ion include quaternary ammonium having the same alkyl group such as tetraethylammonium and tetrabutylammonium, trimethyloctylammonium, trimethyldecylammonium, trimethyldodecylammonium, trimethyltetradecylammonium, trimethylhexadecylammonium, trimethyl Octadecyl ammonium, and trimethylalkylammonium such as trimethylicosanilammonium, trimethylalkenylammonium such as trimethyloctadecenylammonium, trimethylalkadienylammonium such as trimethyloctadecadienylammonium, triethyldodecylammonium, triethyltetradecylammonium, Triethylhexadecyl ammonium And triethylalkylammonium such as triethyloctadecyl ammonium, tributyldodecylammonium, tributyltetradecylammonium, tributylhexadecylammonium, and tributylalkylammonium such as tributyloctadecylammonium, dimethyldioctylammonium, dimethyldidecylammonium, dimethylditetradecylammonium, dimethyl Dihexadecyl ammonium, dimethyl dioctadecyl ammonium, dimethyl dialkyl ammonium such as dimethyl didodecyl ammonium, dimethyl dialkenyl ammonium such as dimethyl dioctadecenyl ammonium, dimethyl dialkadienyl ammonium such as dimethyl dioctadecadenyl ammonium, Diethyldi Diethyl ammonium, such as decyl ammonium, diethyl ditetradecyl ammonium, diethyl dihexadecyl ammonium, and diethyl dioctadecyl ammonium, dibutyl dioctyl ammonium, dibutyl didecyl ammonium, dibutyl didodecyl ammonium, dibutyl ditetradecyl ammonium, dibutyl dihexadecyl ammonium Ammonium, dibutyl dialkyl ammonium such as dibutyl dioctadecyl ammonium, methyl benzyl dialkyl ammonium such as methyl benzyl dihexadecyl ammonium, dibenzyl dialkyl ammonium such as dibenzyl dihexadecyl ammonium, trioctyl methyl ammonium, tridodecyl methyl ammonium, and Tritetradecyl methyl ammonium Trialkylmethylammonium, trioctylethylammonium, tridodecylethylammonium and the like trialkylethylammonium, trioctylbutylammonium, tridecylbutylammonium and the like trialkylbutylammonium, trimethylbenzylammonium and the like aromatic ring Quaternary ammonium, quaternary ammonium derived from aromatic amines such as trimethylphenylammonium, triethyl [PAG] ammonium such as methyl diethyl [PEG] ammonium, and methyl diethyl [PPG], and methyl dimethyl bis [PEG] ammonium Alkyltris [PAG] ammonium such as ammonium dialkylbis [PAG] and ethyltris [PEG] ammonium; Nitrogen atom-ion can be cited phosphonium ion replacing a phosphorus atom. These organic onium ions can be used either singly or in combination of two or more. The notation “PEG” indicates polyethylene glycol, the notation “PPG” indicates polypropylene glycol, and the notation “PAG” indicates polyalkylene glycol. A polyalkylene glycol having a molecular weight of 100 to 1,500 can be used.
[0052]
The molecular weight of these organic onium ion compounds is more preferably from 100 to 600. More preferably, it is 150 to 500. When the molecular weight is more than 600, the thermal deterioration of the amorphous thermoplastic resin such as an aromatic polycarbonate resin may be promoted in some cases, or the heat resistance of the thermoplastic resin composition tends to be impaired. The molecular weight of such an organic onium ion refers to the molecular weight of a single organic onium ion not including a counter ion such as a halogen ion.
[0053]
Preferred embodiments of the organic onium ion include trimethyloctylammonium, trimethyldecylammonium, trimethyldodecylammonium, trimethylhexadecylammonium, trimethyloctadecylammonium, methyltrioctylammonium, ethyltrioctylammonium, butyltrioctylammonium, triphenylmethylammonium, Organic onium ions such as trimethyloctylphosphonium, trimethyldecylphosphonium, trimethyldodecylphosphonium, trimethylhexadecylphosphonium, trimethyloctadecylphosphonium, methyltrioctylphosphonium, ethyltrioctylphosphonium, butyltrioctylphosphonium, and triphenylmethylphosphonium; Charcoal An alkyl group having 6 to 16 atoms (preferably having 7 to 14 carbon atoms, more preferably having 7 to 11 carbon atoms) and an alkyl group having 1 to 4 carbon atoms (preferably having 1 to 3 carbon atoms) And more preferably a methyl group or an ethyl group, and more preferably a methyl group).
[0054]
In the present invention, a more preferred embodiment of the component B is a layered silicate ion-exchanged with an organic onium ion represented by the following general formula (I).
[0055]
Embedded image

[0056]
The general formula (I) satisfies the following condition. That is, M is a nitrogen atom or a phosphorus atom,¹And R^TwoIs an alkyl group having 6 to 16 carbon atoms. R^ThreeIs an alkyl group having 1 to 16 carbon atoms, and R^FourIs an alkyl group having 1 to 4 carbon atoms. Note that R¹And R^TwoMay be the same or different groups from each other.^ThreeAnd R^FourAnd may be the same or different groups.
[0057]
A more preferred embodiment of the organic onium ion represented by the general formula (I) is (i) the aforementioned R^ThreeIs an alkyl group having 1 to 4 carbon atoms. More preferably (ii) R^ThreeAnd R^FourIs an alkyl group having 1 to 4 carbon atoms, and R¹And R^TwoIs an alkyl group having 7 to 14 carbon atoms. More preferably, (iii) R^ThreeAnd R^FourIs an alkyl group having 1 to 4 carbon atoms, and R¹And R^TwoIs the case of an alkyl group having 7 to 11 carbon atoms. In addition, among these, R^ThreeAnd R^FourIs particularly preferably an alkyl group having 1 to 3 carbon atoms, more preferably a methyl group or an ethyl group, and still more preferably a quaternary ammonium ion of a methyl group.
[0058]
According to the more preferable embodiments (including the more preferable embodiments) of these (i) to (iii), the hydrolysis resistance of the resin composition is particularly excellent, and the thermoplastic resin composition of the present invention has a favorable hydrolysis resistance. Gives long-term practical properties.
[0059]
In the above formula (I), R¹~ R^FourCan be both linear and branched.
[0060]
Examples of such suitable quaternary ammonium ions include dimethyl dioctyl ammonium, dimethyl didecyl ammonium, dimethyl didodecyl ammonium, dimethyl ditetradecyl ammonium, dimethyl dihexadecyl ammonium, diethyl didodecyl ammonium, diethyl ditetradecyl ammonium, diethyl Examples include dihexadecyl ammonium, dibutyl dioctyl ammonium, dibutyl didecyl ammonium, dibutyl didodecyl ammonium, and the like.
[0061]
The layered silicate of the B component is SiO 2_TwoSiO consisting of chains_FourIt is a layer composed of a combination of a tetrahedral sheet structure and an octahedral sheet structure containing Al, Mg, Li, etc., and is a silicate (silicate) or clay mineral (clay) in which an exchangeable cation is coordinated between the layers. . These silicates (silicates) or clay minerals (clays) are represented by smectite-based minerals, vermiculite, halloysite, and swelling mica. Specifically, examples of smectite-based minerals include montmorillonite, hectorite, fluorine hectorite, saponite, beidellite, and stevensite, and examples of swelling mica include Li-type fluorine teniolite, Na-type fluorine teniolite, and Na-type tetrasilicon. And swellable synthetic mica such as fluorine mica and Li-type tetrasilicon fluorine mica. These layered silicates can be used in both natural products and synthetic products. Synthetic products are produced, for example, by hydrothermal synthesis, melt synthesis, and solid-state reactions.
[0062]
Among layered silicates, swelling properties such as smectite clay minerals such as montmorillonite and hectorite, Li-type fluorine teniolite, Na-type fluorine teniolite, and Na-type tetrasilicon fluorine mica are considered from the viewpoint of cation exchange capacity and the like. Fluorine mica is preferably used, and montmorillonite and synthetic fluoromica obtained by purifying bentonite are more preferable in terms of purity and the like. Among them, synthetic fluorine mica which can obtain good mechanical properties is particularly preferable.
[0063]
The cation exchange capacity (also referred to as cation exchange capacity) of the layered silicate as the component B is required to be 50 to 200 meq / 100 g, preferably 80 to 150 meq / 100 g, and more preferably. Is 100 to 150 meq / 100 g. The cation exchange capacity is measured as a CEC value by the Schollenberger improved method, which is the official method in Japan as a soil standard analysis method. That is, the cation exchange capacity of the layered silicate is required to be at least 50 meq / 100 g in order to obtain good dispersibility in the amorphous thermoplastic resin as the component A. As the size increases, the thermal deterioration of the thermoplastic resin composition (particularly, the aromatic polycarbonate resin composition) increases, and accordingly, the influence on the thermal deterioration of the amorphous thermoplastic resin composition of the present invention increases. This layered silicate preferably has a pH value of 9 to 10.5. When the pH value is higher than 10.5, the thermal stability of the thermoplastic resin composition of the present invention tends to decrease.
[0064]
For the ion exchange of organic onium ions into layered silicate, an organic onium ion compound (salt compound of organic onium ion) is added to the layered silicate dispersed in a polar solvent, and the ion exchange compound precipitated is collected. Can be created by doing Usually, in this ion exchange reaction, an organic onium ion compound is added at a ratio of 1.0 to 1.5 equivalents to 1 equivalent of the ion exchange capacity of the layered silicate, and almost all the metal ions between the layers are added to the organic onium ion. It is common to exchange with ions. However, controlling the exchange ratio with respect to the ion exchange capacity within a certain range is also effective in suppressing thermal deterioration of the aromatic polycarbonate resin. Here, the ratio of ion exchange with the organic onium ion is preferably 40% or more with respect to the ion exchange capacity of the layered silicate. The proportion of such ion exchange capacity is preferably 40-95%, particularly preferably 40-80%. Here, the exchange rate of the organic onium ion can be calculated by using a thermogravimeter or the like to determine the weight loss due to the thermal decomposition of the organic onium ion for the compound after the exchange.
[0065]
The average number of laminated silicate layers obtained by X-ray diffraction of the layered silicate (component B) of the present invention is 5 to 40 (feature A), preferably 5 to 30, more preferably 5 to 20, and most preferably. 5 to 15. If the average number of laminations is less than 5, the thermal stability of the thermoplastic resin composition may decrease, and if it exceeds 40, the effect of improving rigidity decreases.
[0066]
Conventionally, a thermoplastic resin composition in which a layered silicate is finely dispersed in an amorphous thermoplastic resin such as an aromatic polycarbonate resin has conventionally been obtained by simply peeling an organically modified layered silicate or the like at an interlayer portion, and removing the finely divided particles in the base resin as much as possible. The task was to disperse. However, if the dispersion proceeds too much, the effect of improving the rigidity is reduced, and the thermal stability and the like deteriorate. Therefore, in order to improve rigidity and maintain thermal stability, an appropriate dispersion state of the present invention is required.
[0067]
The distance between the bottom surfaces of the layered silicate in the thermoplastic resin composition of the layered silicate (component B) of the present invention is 1.3 to 2.3 nm (feature B), more preferably 1.5 to 2.3 nm. , Most preferably 1.8 to 2.3 nm. In order to obtain this bottom spacing, it is preferable to use an organically modified layered silicate. If the distance between the bottom surfaces is less than 1.3 nm, the effect of improving the rigidity may be insufficient, and if it exceeds 2.3 nm, the thermal stability of the thermoplastic resin composition may decrease.
[0068]
The feature B is obtained from the diffraction angle of the diffraction line in the X-ray diffraction measurement under the condition of Bragg. The bottom spacing and the X-ray diffraction measurement of the layered silicate are described in, for example, "Clay Handbook" (edited by The Clay Society of Japan: Gihodo Shuppan). In order to perform the X-ray diffraction measurement of the organically modified layered silicate, a powdery sample can be filled in a sample stage and measured.In addition, to perform the X-ray diffraction measurement of the layered silicate in the composition, After the composition is formed into a flat plate by, for example, injection molding, extrusion molding, or the like, a sample can be placed in the opening of the sample stage at the opening of the sample stage and measured by placing the sample on the same plane as the measurement reference plane.
[0069]
The thermoplastic resin composition of the present invention has fine rigidity by finely dispersing the layered silicate, that is, having both the above-mentioned feature A and further feature B, and has good rigidity, good hydrolysis resistance, and further good Thus, a thermoplastic resin composition having excellent thermal stability has been obtained.
[0070]
As a method for achieving the above feature A or feature B in the present invention, for example, the following method is exemplified. (1) using a layered silicate having a specific range of cation exchange capacity, (2) performing melt kneading with high diffusion efficiency using a multi-screw extruder, (3) using a specific organically modified layered silicate, {Circle around (4)} A method of blending a compatibilizer (third component such as component C) between the amorphous resin and the layered silicate, and {circle around (5)} using a layered silicate master batch, etc. It is particularly preferable to combine (1) to (4), particularly preferably to combine (1) to (5).
[0071]
As the third component in the above method (4), a compound having an affinity for the amorphous thermoplastic resin as the component A and having a hydrophilic component is preferable. Therefore, the present invention more preferably further comprises (C) a compound (C) having an affinity for the amorphous thermoplastic resin of the A component and having a hydrophilic component (C component) per 100 parts by weight of the A component. A thermoplastic resin composition comprising 50 parts by weight.
[0072]
The composition ratio of the layered silicate of the component B to the component A used in the present invention is 0.1 to 50 parts by weight, preferably 0.5 to 20 parts by weight, more preferably 0.5 to 20 parts by weight, per 100 parts by weight of the component A. It is 5 to 10 parts by weight. When the composition ratio is less than 0.1 part by weight, the effect of improving the mechanical properties of an amorphous thermoplastic resin such as an aromatic polycarbonate resin is not seen, and when the composition ratio is more than 50 parts by weight, the thermal stability of the composition decreases. However, it is difficult to obtain a practical thermoplastic resin composition.
[0073]
<About the C component>
The C component of the present invention is a compound having an affinity for the amorphous thermoplastic resin (A component) and having a hydrophilic component. Such a configuration of the C component produces a good affinity for both amorphous thermoplastics and layered silicates, especially organically modified layered silicates. Affinity for both amorphous thermoplastics and layered silicates, especially organically modified layered silicates, enhances the compatibility of the two components, and the layered silicates are fine and stable in amorphous thermoplastics And become dispersed.
[0074]
The function of the C component relating to the dispersion of the organically modified layered silicate is the same as that of a compatibilizer for polymer alloy (compatibilityizer) used for compatibilizing heterogeneous polymers with each other. Therefore, the component C is preferably a polymer obtained by polymerizing a monomer rather than a low molecular compound. Further, the polymer also has excellent thermal stability during kneading. The average number of repeating units of the polymer needs to be 2 or more, preferably 5 or more, more preferably 10 or more. On the other hand, at the upper limit of the average molecular weight of the polymer, the number average molecular weight is preferably 2,000,000 or less. If the upper limit is not exceeded, good moldability is obtained.
[0075]
Examples of the basic structure of the component C of the present invention include the following structures (i) and (ii).
[0076]
Structure (i): When the component having an affinity for the amorphous thermoplastic resin is α and the hydrophilic component is β, a graft copolymer composed of α and β (main chain: α, graft chain: β, And a main chain: β and a graft chain: α can be selected.), And a block copolymer composed of α and β (di-, tri-, etc., the number of block segments such as 2 or more can be selected, such as a radial block type). And a random copolymer comprising α and β. α and β may be not only single polymers but also copolymers.
[0077]
Here, α and β represent both a polymer segment unit and a monomer unit. The α component is preferably a polymer segment unit from the viewpoint of affinity with the amorphous thermoplastic resin.
[0078]
Structure (ii): When the component having an affinity for the amorphous thermoplastic resin is α and the hydrophilic component is β, the function of α is expressed by the entire polymer, and β is a structure contained in α. Having a polymer.
[0079]
In other words, although α alone does not have sufficient affinity with the amorphous thermoplastic resin, α and β are combined and integrated to exhibit good affinity with the amorphous thermoplastic resin. is there. Even in the case of α alone, the affinity with the amorphous thermoplastic resin is good, and the affinity may be further improved by combination with β. Such an embodiment is included in the above structure (i). Thus, structures (i) and (ii) partially overlap. On the other hand, in the structure (i), although α alone has a sufficient affinity with the amorphous thermoplastic resin, the combination of α and β with each other makes it possible to obtain a good affinity with the amorphous thermoplastic resin. On the contrary, there may be a mode in which the sex is reduced. Naturally, such an embodiment is included in the C component.
[0080]
The above structures (i) and (ii) can be selected in the present invention. In particular, an embodiment that satisfies both the condition of the structure (i) and the condition of the structure (ii), that is, even if only α is used, the affinity for the amorphous thermoplastic resin is high, and the affinity is further improved in the entire C component to which β is added. An aspect in which the height is increased is preferable.
[0081]
The component having an affinity for the amorphous thermoplastic resin in the present invention (hereinafter, sometimes referred to as α according to the above) will be described. As described above, the component C functions in the same manner as the compatibilizer in the polymer alloy, so that α is required to have the same affinity for the polymer as the compatibilizer. Therefore, α can be largely classified into a non-reactive type and a reactive type.
[0082]
In the non-reaction type, the affinity is good when the following factors are present. That is, between the amorphous thermoplastic resin and α, (1) similarity in chemical structure, (2) similarity of solubility parameter (difference in solubility parameter is 1 (cal / cm)^Three)^1/2Within, that is, about 2.05 (MPa)^1/2It is necessary to have factors such as (3) intermolecular interactions (hydrogen bonding, ionic interactions, etc.), and pseudo-attractive interactions peculiar to random polymers. These factors are known as indices for judging the affinity between the compatibilizer and the polymer on which the polymer alloy is based.
[0083]
In the reaction type, various types known as functional groups having reactivity with the amorphous thermoplastic resin in the compatibilizer can be exemplified. For example, for an aromatic polycarbonate resin suitable as an amorphous thermoplastic resin, a carboxyl group, a carboxylic anhydride group, an epoxy group, an oxazoline group, an ester group, an ester bond, a carbonate group, and a carbonate bond are exemplified. be able to.
[0084]
On the other hand, if the amorphous thermoplastic resin and α have a good affinity, the resulting mixture of amorphous thermoplastic resin and α shows a single glass transition temperature (Tg), or It is also widely known that a behavior in which the Tg of the amorphous thermoplastic resin moves toward the Tg of α is recognized. In the present invention, as the component (α) having affinity, a component having such behavior can be mentioned as one of the embodiments.
[0085]
As described above, the component (α) having an affinity with the amorphous thermoplastic resin in the component C of the present invention can exhibit the affinity due to various factors. Above all, α is preferably a non-reactive type, and in particular, it is preferable that the solubility parameter is close, because good affinity is exhibited. This is because it has better affinity with the amorphous thermoplastic resin than the reaction type. In addition, the reaction type has a disadvantage that when the reactivity is excessively increased, thermal degradation of the polymer is promoted by a side reaction.
[0086]
The solubility parameter of the amorphous thermoplastic resin and α preferably has the following relationship. That is, the solubility parameter of the amorphous thermoplastic resin (component A) is δ_A((MPa)^1/2) And the solubility parameter of α in the C component or the solubility parameter of the entire C component is δα ((MPa)^1/2),
δα = δ_A± 2 ((MPa)^1/2)
It is preferable that
[0087]
For example, the solubility parameter of an aromatic polycarbonate resin suitable as the component A is usually about 10 (cal / cm).^Three)^1/2(That is, about 20.5 ((MPa)^1/2)), Δα in the component A is 18.5 to 22.5 ((MPa)^1/2) Is preferable, and 19 to 22 ((MPa)^1/2Is more preferable.
[0088]
For example, specific examples of the polymer component satisfying the solubility parameter δα in an aromatic polycarbonate resin suitable as the component A are represented by aromatic polyesters (polyethylene terephthalate, polybutylene terephthalate, and cyclohexane dimethanol copolymerized polyethylene terephthalate). And polyester-based polymers such as aliphatic polyesters (typified by polycaprolactone). Specific examples thereof include styrene polymers, alkyl (meth) acrylate polymers, and acrylonitrile polymers (polystyrene, styrene-maleic anhydride copolymer, polymethyl methacrylate, styrene-methyl methacrylate copolymer, and styrene-acrylonitrile copolymer). Vinyl polymer). In order to maintain the heat resistance of the composition of the present invention, it is preferable to use a polymer component having a high Tg.
[0089]
Here, the solubility parameter is determined by a theoretical estimation method based on a group contribution method using Small values described in “Polymer Handbook 4th Edition” (A WILEY-INTERSCIENCE PUBLICATION, 1999). Available. The Tg of the amorphous thermoplastic resin can be determined by a differential scanning calorimeter (DSC) measurement in accordance with JIS K7121.
[0090]
The component α having an affinity for the amorphous thermoplastic resin of the component A is preferably 5% by weight or more, more preferably 10% by weight or more, still more preferably 30% by weight or more in the component C. % By weight or more is particularly preferred. Since an embodiment in which the entire C component is set to α is also possible, the upper limit may be 100% by weight.
[0091]
On the other hand, the hydrophilic component (hereinafter sometimes referred to as β) in the component C includes a monomer having a hydrophilic group (an organic atomic group having strong interaction with water) and a hydrophilic polymer component (polymer). Segment). The hydrophilic group is widely known per se, and the following groups are exemplified.
1) Strongly hydrophilic group: -SO_ThreeH, -SO_ThreeM, -OSO_ThreeH, -OSO_ThreeH, -COOM, -NR_ThreeX (R: alkyl group, X: halogen atom, M: alkali metal, -NH_Four) etc,
2) Slightly hydrophilic groups: -COOH, -NH_Two, -CN, -OH, -NHCONH_Two etc,
3) a group having no or little hydrophilicity: -CH_TwoOCH_Three, -OCH_Three, -COOCH_Three, -CS etc.
Among the groups 1) to 3), those classified into 1) and 2) are used as the hydrophilic group in the present invention. In addition to the above examples, 1) a strongly hydrophilic group includes a sulfine group and the like, and 2) a group having a low hydrophilicity includes a carboxylic anhydride group, an oxazoline group, a formyl group and a pyrrolidone group. Is exemplified.
[0092]
The hydrophilic group 2) is preferred because it is more excellent in thermal stability during melt processing of an amorphous thermoplastic resin, particularly an aromatic polycarbonate resin suitable in the present invention. If the hydrophilicity is too high, thermal deterioration of the aromatic polycarbonate resin or the like is likely to occur. This is because such a hydrophilic group directly reacts with a carbonate bond to cause a thermal decomposition reaction.
[0093]
In addition, the hydrophilic group of the present invention includes both monovalent and divalent or higher. When the component C is a polymer, a divalent or higher functional group refers to a group in which the group does not form a main chain, and a group forming the main chain is distinguished from a functional group as a bond. Specifically, a group added to an atom such as carbon constituting the main chain, a side chain group, and a group at the terminal of a molecular chain are functional groups even if they are divalent or higher.
[0094]
A more specific indicator of a hydrophilic group is a solubility parameter. It is widely known that the greater the value of the solubility parameter, the higher the hydrophilicity. The solubility parameter per group is determined by the aggregation energy (E_coh) And the molar volume (V) of each group ("A WILEY-INTERSCIENCE PUBLICATION", VII / 685, 1999, or Polym. Eng. Sci., No. 14, 147 and 472, 1974, etc.). Such a calculation method is simple and widely known. Further, from the viewpoint of comparing only the magnitude relation of hydrophilicity, the cohesive energy (E_coh) Divided by the molar volume (V) (E)_coh/ V; the unit is “J / cm^Three") Can be used as an index of hydrophilicity.
[0095]
The hydrophilic group contained in β in component C of the present invention is E_coh/ V needs to be 600 or more. Preferably E_coh/ V is 800 or more, and when it is 800 or more, E of the carbonate bond in the aromatic polycarbonate resin suitable as the component A of the present invention._coh/ V and has a higher hydrophilicity than a carbonate bond. Further E_coh/ V is more preferably 900 or more, and even more preferably 950 or more. On the other hand, if the hydrophilicity is too high, the aromatic polycarbonate resin is likely to be thermally degraded as described above. Therefore, E_coh/ V is preferably 2,500 or less, more preferably 2,000 or less, and still more preferably 1,500 or less.
[0096]
A hydrophilic polymer component (polymer segment) is also selected as the hydrophilic component (β) of the component C. Therefore, the segment of the hydrophilic polymer contained in the polymer of the component C is β. Examples of the hydrophilic polymer include polyalkylene oxide, polyvinyl alcohol, polyacrylic acid, and metal salts of polyacrylic acid (including chelate type). ), Polyvinylpyrrolidone, polyacrylamide, polyhydroxyethyl methacrylate, and the like. Among these, polyalkylene oxide, polyvinyl alcohol, polyacrylic acid, polyvinyl pyrrolidone, and polyhydroxyethyl methacrylate are preferably exemplified. These are because both good hydrophilicity and thermal stability to the aromatic polycarbonate resin suitable in the present invention (suppression of decomposition of the aromatic polycarbonate resin during melt processing) can be achieved. As the polyalkylene oxide, polyethylene oxide and polypropylene oxide are preferable.
[0097]
In both the monomer having a hydrophilic group and the hydrophilic polymer component, β preferably has an acidic functional group (hereinafter sometimes simply referred to as “acid group”). The acidic group suppresses thermal deterioration during melt processing of a thermoplastic resin composition containing an aromatic polycarbonate resin suitable as a main component in the present invention. In particular, an acidic group containing no nitrogen atom is more preferable. Suitable acidic groups include a carboxyl group, a carboxylic acid anhydride group, a sulfonic acid group, a sulfinic acid group, a phosphonic acid group, a phosphinic acid group, and the like.
[0098]
In contrast, a functional group containing a nitrogen atom such as an amide group or an imide group may not sufficiently suppress thermal deterioration of the aromatic polycarbonate resin during melt processing. This is considered to be because the nitrogen atom has local basicity and causes thermal decomposition of the carbonate bond.
[0099]
In the case where β is a monomer having a hydrophilic group, the ratio of β in the component C is 60 to 10,000 as a functional group equivalent, which is the molecular weight per functional group, preferably 70 to 8,000, and 80 -6,000 is more preferable, and 100-3,000 is still more preferable. When β is a hydrophilic polymer segment, β is suitably in the range of 5 to 95% by weight, preferably 10 to 90% by weight, in 100% by weight of the component C. Especially, 30 to 70% by weight is more preferable, and 30 to 50% by weight is further preferable.
[0100]
As a method for producing a compound having a component (α) having an affinity for an amorphous thermoplastic resin and a hydrophilic component (β), a monomer of β and a monomer constituting α are copolymerized. Examples include a method, a method of block- or graft-copolymerizing a polymer component of β with α, and a method of directly reacting β with α to add.
[0101]
As preferred embodiments of the component C of the present invention, "a polymer having an affinity for the resin of the component A and having an acidic functional group", "a polymer having an affinity for the resin of the component A and having a polyalkylene oxide segment" A polymer having affinity for the resin of component A and having an oxazoline group, or a polymer having affinity for the resin of component A and having a hydroxyl group. You. In the polymer of the preferred embodiment as the C component, its molecular weight is preferably in the range of 10,000 to 1,000,000 in weight average molecular weight, more preferably in the range of 50,000 to 500,000. The weight average molecular weight is calculated as a value in terms of polystyrene by GPC measurement using a calibration straight line with a standard polystyrene resin.
[0102]
Among the above, a polymer having an affinity with the resin of the component A (more preferably with the aromatic polycarbonate resin) and having an acidic functional group is preferable, and more preferably a polymer having an affinity with the aromatic polycarbonate resin. And a functional group comprising a carboxyl group and / or a derivative thereof. Further, from the viewpoint of the effect of maintaining the heat resistance of the aromatic polycarbonate resin, the polymer is preferably one having an aromatic ring component in the main chain and one having a styrene component in the main chain. From the above points, a styrene-containing polymer (component C1) having a functional group consisting of a carboxyl group and / or a derivative thereof is particularly suitable as the component C of the present invention. Here, the styrene-containing polymer refers to a polymer containing, as a polymer component, a repeating unit obtained by polymerizing an aromatic vinyl compound such as styrene.
[0103]
The styrene-containing polymer (component C1) having a functional group comprising a carboxyl group and / or a derivative thereof particularly suitable as the component C of the present invention will be described in detail. The ratio of the functional group comprising a carboxyl group and / or a derivative thereof is preferably from 0.1 to 12 meq / g, more preferably from 0.5 to 5 meq / g. Here, one equivalent in the C1 component means that one mole of a carboxyl group is present, and such a value can be calculated by back titration with potassium hydroxide or the like.
[0104]
Examples of the functional group comprising a derivative of a carboxyl group include (i) a metal salt (including a chelate salt) in which a hydroxyl group of a carboxyl group is substituted with a metal ion, (ii) an acid chloride in which a chlorine atom is substituted, (iii) -OR (R is a monovalent hydrocarbon group), (iv) an acid anhydride (R is a monovalent hydrocarbon group) substituted with -O (CO) R, (v) -NR_Two(R is hydrogen or a monovalent hydrocarbon group), and (vi) an imide (R is hydrogen or a monovalent hydrocarbon group) in which two carboxyl groups are substituted with ＮＲNR. Can be.
[0105]
As a method for producing a styrene-containing polymer having a functional group consisting of a carboxyl group and / or a derivative thereof (hereinafter, simply referred to as “carboxyl groups”), various conventionally known methods can be used. For example, (1) a method of copolymerizing a monomer having a carboxyl group and a styrene-based monomer, and (2) a method of bonding a compound or monomer having a carboxyl group to a styrene-containing polymer or Copolymerization methods and the like can be mentioned.
[0106]
In the copolymerization of the above (1), various copolymers such as alternating copolymers, block copolymers and tapered copolymers can be used in addition to random copolymers. In addition, in the method of copolymerization, various polymerization methods such as anionic living polymerization method and group transfer polymerization method can be used in addition to radical polymerization methods such as solution polymerization, suspension polymerization and bulk polymerization. Further, a method of polymerizing once after forming a macromonomer is also possible.
[0107]
In the above method (2), generally, a radical generator such as peroxide or 2,3-dimethyl-2,3-diphenylbutane (dicumyl) is added to a styrene-containing polymer or copolymer as necessary. And a method of reacting or copolymerizing at a high temperature. In such a method, a reactive active site is thermally generated in a styrene-containing polymer or copolymer, and a compound or monomer that reacts with the active site is reacted. Other methods for generating active sites required for the reaction include irradiation with radiation or an electron beam, and application of an external force by a mechanochemical technique. Further, there is a method in which a monomer that generates an active site required for the reaction is previously copolymerized in the styrene-based copolymer. Examples of the active site for the reaction include an unsaturated bond, a peroxide bond, and a thermally stable nitroxide radical having high steric hindrance.
[0108]
As the compound or monomer having a carboxyl group, for example, acrylic acid, methacrylic acid, acrylamide, unsaturated monocarboxylic acids such as methacrylamide and derivatives thereof, maleic anhydride, citraconic anhydride, N-phenylmaleimide, Derivatives of maleic anhydride, such as N-methylmaleimide, as well as glutarimide structures and chelate structures formed of acrylic acid and polyvalent metal ions. Among these, a monomer having a functional group containing no metal ion or nitrogen atom is preferable, and a monomer having a carboxyl group and a carboxylic anhydride group is more preferable. Among these, maleic anhydride is particularly preferred.
[0109]
Further, as the styrene monomer compound, styrene, α-methylstyrene, o-methylstyrene, m-methylstyrene, p-methylstyrene, tert-butylstyrene, α-methylvinyltoluene, dimethylstyrene, chlorostyrene, Dichlorostyrene, bromostyrene, dibromostyrene, vinylnaphthalene and the like can be used, but styrene is particularly preferred.
[0110]
Further, other compounds copolymerizable with these compounds, such as acrylonitrile and methacrylonitrile, may be used as a copolymerization component.
[0111]
Preferred as the C component in the present invention is a styrene-containing copolymer obtained by copolymerizing a monomer having a carboxyl group. This is because in such a copolymer, a relatively large number of carboxyl groups can be stably contained in the styrene-containing polymer. A more preferred embodiment is a styrene-containing copolymer obtained by copolymerizing a monomer having a carboxyl group and a styrene-based monomer. A particularly preferred embodiment is a styrene-maleic anhydride copolymer. The styrene-maleic anhydride copolymer has high compatibility with both the ionic component and the aromatic polycarbonate resin in the layered silicate, and thus finely disperses the layered silicate (component B). Furthermore, good thermal stability is obtained in a resin composition containing a layered silicate, particularly an organically modified layered silicate, by the action of a carboxylic anhydride group. Further, since the copolymer itself has good thermal stability, it has high stability even at the high temperature conditions required for melt processing of the aromatic polycarbonate resin.
[0112]
The composition of the styrene-containing copolymer obtained by copolymerizing the above-mentioned monomer having a carboxyl group is not limited as long as the above-mentioned condition of the ratio of β is satisfied. Of 1 to 30% by weight (particularly 5 to 25% by weight) and 99 to 70% by weight (particularly 95 to 75% by weight) of a styrenic monomer compound component. It is preferable to use one containing 1 to 30% by weight (particularly 5 to 25% by weight) of a monomer having a carboxyl group, and 99 to 70% by weight (particularly 95 to 75%) % By weight) are particularly preferred.
[0113]
The molecular weight of the component C1, which is a preferred embodiment of the component C of the present invention, is not particularly limited. The weight average molecular weight of the C1 component is preferably in the range of 10,000 to 1,000,000, and more preferably in the range of 50,000 to 500,000. The weight average molecular weight shown here is calculated as a value in terms of polystyrene by GPC measurement using a calibration straight line with a standard polystyrene resin.
[0114]
A polymer having a polyalkylene oxide segment suitable as the component C of the present invention, particularly a preferable polyetherester copolymer (component C2) will be described.
[0115]
The polyetherester copolymer is a polymer produced by performing polycondensation from dicarboxylic acid, alkylene glycol, and poly (alkylene oxide) glycol, and derivatives thereof. Particularly preferred examples include poly (alkylene oxide) glycol having a polyalkylene oxide unit represented by the following formula (II) or a derivative thereof (C2-1 component), and an alkylene containing at least 65 mol% of tetramethylene glycol. It is a copolymer produced from glycol or a derivative thereof (C2 component), and a dicarboxylic acid or a derivative thereof containing 60% by mole or more of terephthalic acid (C2 component).
[0116]
Embedded image

[0117]
(Where X represents a monovalent organic group, n and m are each an integer including 0, and 10 ≦ (n + m) ≦ 120. When m is 2 or more, Xs are the same or different from each other Any of the embodiments can be selected.)
In the above formula (II), X is -CH_Three, -CH_TwoCl, -CH_TwoBr, -CH_TwoI, and -CH_TwoOCH_ThreeAt least one substituent selected from When X is other than these, steric hindrance by the substituent becomes large, and it becomes difficult to increase the degree of polymerization of the copolymer. When n + m is less than 10, the layered silicate may not be sufficiently dispersed. When n + m exceeds 120, a polyetherester copolymer having a high degree of polymerization is hardly obtained, and the phase of the C2 component is hardly obtained. The solubilizing function may be reduced.
[0118]
As the polyalkylene oxide component in the above formula (II), any of a random copolymer, a tapered copolymer and a block copolymer of a polyethylene oxide component and a component having a substituent X can be selected. The polyalkylene oxide in the above formula (II) is particularly preferably m = 0, that is, a polymer component consisting of only a polyethylene oxide component.
[0119]
The copolymerization ratio of the C2-1 component is 30 to 80% by weight, more preferably 40 to 70% by weight of the total glycol component. If the amount of the component C2 (1) is less than 30% by weight, the layered silicate is not sufficiently dispersed, which may cause a decrease in mechanical properties and a deterioration in appearance. Even when the content of the C2 component (1) is more than 80% by weight, the layered silicate is not sufficiently dispersed and the strength of the polyetherester copolymer itself is reduced, thereby deteriorating mechanical properties and deteriorating appearance. There are cases.
[0120]
In the C2 component of the C2 component polyetherester copolymer, diols other than tetramethylene glycol can be copolymerized. Examples of such a diol include ethylene glycol, trimethylene glycol, 1,5-pentanediol, 1,6-hexanediol, diethylene glycol, 1,4-cyclohexanediol, and 1,4-cyclohexanedimethanol. The content of tetramethylene glycol in the component C2 (2) is 65 mol% or more, preferably 75 mol% or more, and more preferably 85 mol% or more. A polyetherester copolymer having less than 65 mol% of tetramethylene glycol causes a decrease in moldability of the thermoplastic resin composition.
[0121]
A dicarboxylic acid of a polyetherester copolymer or a derivative thereof (in the component C2-3), dicarboxylic acids other than terephthalic acid (including those having a carboxyl group of more than 2) can be copolymerized. Examples thereof include isophthalic acid, phthalic acid, adipic acid, sebacic acid, azelaic acid, dodecanedioic acid, trimellitic acid, pyromellitic acid, naphthalenedicarboxylic acid, and cyclohexanedicarboxylic acid. The copolymer is particularly suitable as the component C. In the component C2-3, terephthalic acid is at least 60 mol%, preferably at least 70 mol%, more preferably from 75 to 95 mol%, and preferably at least 60 mol%. The polyetherester copolymer of less than tends to decrease the degree of polymerization of the copolymer. It is not preferable because the production of sufficient degree of polymerization of the polyether ester copolymer becomes difficult.
[0122]
Other suitable C components include styrene-containing copolymers containing oxazoline groups as hydrophilic groups. Styrene monomer compounds forming such a copolymer include styrene, α-methylstyrene, o-methylstyrene, m-methylstyrene, p-methylstyrene, tert-butylstyrene, α-methylvinyltoluene, dimethyl Styrene, chlorostyrene, dichlorostyrene, bromostyrene, dibromostyrene, vinylnaphthalene, and the like can be used. Further, other compounds copolymerizable with these compounds, such as acrylonitrile and methacrylonitrile, may be used as a copolymerization component. Among them, styrene (2-isopropenyl-2-oxazoline) -styrene-acrylonitrile copolymer is particularly preferable.
[0123]
The composition ratio of the component C of the present invention is preferably 0.5 to 50 parts by weight, more preferably 0.5 to 20 parts by weight, per 100 parts by weight of the component A. When the amount is less than 0.5 part by weight, the effect of dispersing the layered silicate is not sufficient, and the effect of suppressing the thermal deterioration of the aromatic polycarbonate resin may be insufficient. If the amount exceeds 50 parts by weight, impact resistance and heat resistance may be reduced.
[0124]
The thermoplastic resin composition of the present invention may further contain a reinforcing filler other than the component B as long as the effects of the present invention are exhibited. Various commonly known fillers such as glass fiber, carbon fiber, glass flake, wollastonite, kaolin clay, mica, talc and various whiskers (potassium titanate whisker, aluminum borate whisker, etc.) are used as the reinforcing filler. Can be used together. The shape can be freely selected from fibrous, flake, spherical, and hollow shapes. Glass fibers, carbon fibers, glass flakes, and the like are suitable for improving the strength and impact resistance of the thermoplastic resin composition. On the other hand, in order to more effectively utilize the extremely good surface appearance (surface smoothness) of the resin composition of the present invention, the size of the reinforcing filler is preferably minute. Specifically, in the case of a fibrous filler, its fiber diameter is, and in the case of a plate-like filler or a granular filler, its size is preferably 5 μm or less, more preferably 4 μm or less, and still more preferably 3 μm or less. preferable. The lower limit is appropriately about 0.05 μm. Examples of such a minute reinforcing filler include talc, wollastonite, kaolin clay, and various whiskers. The compounding amount of the reinforcing filler is suitably 50% by weight or less per 100% by weight of the entire thermoplastic resin composition, preferably in the range of 0.5 to 50% by weight, and more preferably in the range of 1 to 35% by weight. If the amount is more than 50% by weight, the moldability deteriorates and the effect of the present invention cannot be obtained, which is not preferable.
[0125]
In addition, other thermoplastic resins (for example, polyamide resins, polyacetal resins, aromatic polyester resins, liquid crystal polyester resins, polyolefin resins, syndiotactic polystyrene resins, polyphenylene sulfide resins, etc. Thermoplastic resins), flame retardants (e.g., brominated epoxy resins, brominated polystyrene, brominated polycarbonate, brominated polyacrylate, monophosphate compounds, phosphate oligomer compounds, phosphonate oligomer compounds, phosphonitrile oligomer compounds, phosphonamide compounds, Alkali (earth) metal salts of organic sulfonates, silicone-based flame retardants, etc.), flame retardant aids (eg, sodium antimonate, antimony trioxide, etc.), anti-dripping agents (having fibril-forming ability) Polytetrafluoroethylene, nucleating agents (eg, sodium stearate, ethylene-sodium acrylate, etc.), antioxidants (eg, hindered phenolic compounds, sulfur-based antioxidants, etc.), impact modifiers, An ultraviolet absorber, a light stabilizer, a release agent, a lubricant, a coloring agent (dye, inorganic pigment, etc.), a fluorescent whitening agent, and the like may be blended. These various additives can be used in a known blending amount when blended with the aromatic polycarbonate resin.
[0126]
The thermoplastic resin composition of the present invention preferably contains a phosphorus-based heat stabilizer. Examples of such a phosphorus-based heat stabilizer include phosphate esters such as trimethyl phosphate, triphenyl phosphite, trisnonylphenyl phosphite, distearyl pentaerythritol diphosphite, and bis (2,6-di-tert-butyl-4). -Methylphenyl) pentaerythritol-diphosphite, tris (2,4-di-tert-butylphenyl) phosphite, 2,2-methylenebis (4,6-di-tert-butylphenyl) octyl phosphite, and Phosphites such as bis (2,4-di-tert-butylphenyl) pentaerythritol diphosphite, and tetrakis (2,4-di-tert-butylphenyl) -4,4'-biphenylenediphosphonite Aromatic polycarbonate such as phosphonite Compounds widely known as the phosphorus-based heat stabilizer is preferably exemplified. The phosphorus-based heat stabilizer preferably contains 0.001 to 1% by weight, more preferably 0.01 to 0.5% by weight, and more preferably 0.01 to 0.2% by weight, based on 100% by weight of the total composition. It is even more preferred that it comprises% by weight. By adding such a phosphorus-based heat stabilizer, the heat stability is further improved, and good molding characteristics can be obtained.
[0127]
To produce the thermoplastic resin composition of the present invention, any method is employed. For example, there can be mentioned a method in which each component and optionally other components are premixed, then melt-kneaded, and pelletized. Examples of premixing means include a Nauter mixer, a V-type blender, a Henschel mixer, a mechanochemical device, and an extrusion mixer. In the pre-mixing, granulation can also be carried out by an extrusion granulator or a briquetting machine, if necessary. After the preliminary mixing, the mixture is melt-kneaded by a melt-kneader represented by a vent-type twin-screw extruder, and pelletized by a device such as a pelletizer. Other examples of the melt kneader include a Banbury mixer, a kneading roll, and a thermostatic stirring vessel. A multi-screw extruder represented by a vented twin-screw extruder is preferable. By using such a multi-screw extruder, the organically modified layered silicate is finely dispersed in the base resin with a strong shearing force. On the other hand, since the dispersion is performed in the presence of the action of reducing the size of the interlayer, exposure of ions between the layers to the outside is suppressed. As a result, a higher balance between good dispersion and thermal stability is achieved.
[0128]
Further, in the melt kneading of the thermoplastic resin composition of the present invention by a melt kneader, the following embodiment is more preferable. That is, a compound (C) having an affinity between the layered silicate (B component) having a cation exchange capacity of 50 to 200 meq / 100 g and the amorphous thermoplastic resin of the A component and having a hydrophilic component (C) Component), particularly preferably a styrene-containing polymer having a functional group comprising a carboxyl group and / or a derivative thereof (component C1) is melt-kneaded in advance. Thereafter, the melt-kneaded product and the amorphous thermoplastic resin of component A, particularly preferably an aromatic polycarbonate resin, are melt-kneaded by a multi-screw extruder. Such a melt-kneading method is preferable for improving the thermal stability of the amorphous thermoplastic resin. This is a preferred melt-kneading method for the aromatic polycarbonate resin since the decrease in the molecular weight is particularly suppressed. This is considered to be because the C component sufficiently interacts with the B component when the B component and the C component are melt-kneaded in advance, and a predetermined effect is efficiently obtained. Therefore, according to the present invention, after melt-kneading the components B and C in advance, the melt-kneaded product and the component A are melt-kneaded using a multi-screw extruder. A method for producing a resin composition is provided.
[0129]
More specifically, for example, (i) a method of melt-kneading the components B and C with a vented twin-screw extruder to form a pellet, and then melt-kneading with the component A again, or (ii) mixing the component B with the component B The component C is introduced from the main supply port of the vented twin-screw extruder, and part or all of the component A is already melt-kneaded with the components B and C from the supply port provided in the middle stage of the twin-screw extruder. The method of throwing into the state where it was put is mentioned. In the method in which the components B and C are melt-kneaded in advance, a part of the component A may be included during the melt-kneading.
[0130]
The thermoplastic resin composition of the present invention can be used to produce various products by injection molding the pellets produced as described above. In such injection molding, not only ordinary molding methods but also, as appropriate, injection compression molding, injection press molding, gas assist injection molding, foam molding (including injection by supercritical fluid), insert molding, A molded article can be obtained by using an injection molding method such as in-mold coating molding, heat-insulating mold molding, rapid heating and cooling mold molding, two-color molding, sandwich molding, and ultra-high-speed injection molding. The advantages of these various molding methods are already widely known. For the molding, either a cold runner method or a hot runner method can be selected.
[0131]
Further, the thermoplastic resin composition of the present invention can be used in the form of various shaped extruded products, sheets, films and the like by extrusion. For forming a sheet or film, an inflation method, a calendar method, a casting method, or the like can be used. Furthermore, it is also possible to form a heat-shrinkable tube by performing a specific stretching operation. Further, the thermoplastic resin composition of the present invention can be formed into a hollow molded article by rotational molding or blow molding.
[0132]
The thermoplastic resin composition of the present invention has good rigidity, good hydrolysis resistance, and good thermal stability. Therefore, the resin molded product obtained as described above is manufactured under a wide range of molding processing conditions that have no practical problem, and has good rigidity and good surface appearance. More specifically, according to the present invention, a resin molded article formed from the thermoplastic resin composition of the present invention has a surface having a value of arithmetic average roughness Ra measured in accordance with JIS B0601. , 0.1 μm or less, and a flexural modulus measured in accordance with ASTM D790 of 2,500 MPa or more. Is even higher. Conventionally, in order to improve the bending elastic modulus of a resin molded product, it was common to mix a reinforcing material on a fiber or an inorganic filler, but in that case, the surface roughness is significantly reduced, This is because a product that can achieve the above balance has not been obtained.
[0133]
The value of the arithmetic surface roughness Ra of the resin molded product is more preferably 0.08 μm or less, and further preferably 0.05 μm or less. The lower limit largely depends on the mold used for molding, but about 0.001 μm is appropriate. The value of the flexural modulus is more preferably 2,800 MPa or more, and still more preferably 3,000 MPa or more. On the other hand, the upper limit is suitably 8,000 MPa, preferably 7,000 MPa, and more preferably 6,000 MPa.
[0134]
By subjecting the resin molded article of the present invention to surface modification, a surface modified molded article having excellent smoothness can be obtained. The term “surface modification” here means a new layer on the surface of resin molded products such as vapor deposition (physical vapor deposition, chemical vapor deposition, etc.), plating (electroplating, electroless plating, hot-dip plating, etc.), painting, coating, printing, etc. And a method used for a general aromatic polycarbonate resin can be applied. In these surface modifications, the surface smoothness of the resin molded product to be modified greatly affects the surface properties after the modification. However, when the resin molded product of the present invention is used, a molded product having excellent surface smoothness is obtained. Can be obtained. Generally, these surface modifications are performed not only for surface modification and function addition, but also for the purpose of enhancing the surface smoothness of the resin molded product.If the surface smoothness is poor, it is necessary to increase the thickness of the modification. However, the resin molded product of the present invention can be efficiently modified with a small thickness. That is, the thickness is preferably 50 μm or less because the effects of the present invention are exhibited. Further, the thickness is more preferably 20 μm or less, still more preferably 5 μm or less, and still more preferably 2 μm or less. As the lower limit, 0.001 μm or more is appropriate. Further, with respect to the value of the arithmetic average roughness Ra measured according to JIS B0601 in a single resin molded product having no metal layer or metal oxide layer, surface modification is performed with a thickness of 500 times or less of the Ra. When carried out, the characteristics of the resin molded product of the present invention are utilized, and the thickness is more preferably 200 times or less, more preferably 100 times or less, and particularly preferably 50 times or less of Ra. A preferable surface modification method in the present invention is a method with a small modified thickness such as vapor deposition and plating.
[0135]
The thermoplastic resin composition of the present invention can be applied to parts which could not be used as a resin material conventionally by taking advantage of the above characteristics. In particular, the present invention can be used for applications requiring extremely high hydrolysis resistance and rigidity, which could not be achieved unless a conventional glass molded product or a precision cut metal product is used. Such applications include, for example, mirrors arranged in optical precision equipment, polygon mirrors arranged in laser type copying / printing apparatuses, and hard disks.
[0136]
Further, the thermoplastic resin composition of the present invention is useful for various applications such as various electronic / electric devices, OA devices, vehicle parts, machine parts, other agricultural materials, fishing materials, transport containers, packaging containers, and miscellaneous goods. . Since the thermoplastic resin composition of the present invention is also excellent in moldability, it is also suitable for various thin molded products. Specific examples of the thin injection molded products include various housing molded products such as a battery housing and mirrors. Tubes, memory cards, speaker cones, disk cartridges, surface light emitters, mechanical parts for micromachines, nameplates, personal computer housings, CD and DVD drive trays and chassis, copier trays and chassis, direct-lit backlights for liquid crystal devices Light diffusion plates (in particular, light diffusion plates for direct-type backlights for large liquid crystal display devices (large liquid crystal televisions of 15 inches or more)) and IC cards are exemplified.
[0137]
【Example】
Hereinafter, the present invention will be described in detail with reference to examples. However, the present invention is not limited to these. In addition, the measurement of various characteristics in an Example was based on the following method. The following raw materials were used.
(1) Content of layered silicate (inorganic component) in thermoplastic resin composition
The test piece was molded using an injection molding machine (manufactured by Toshiba Machine Co., Ltd .: IS-150EN) at a cylinder temperature of 260 ° C., a mold temperature of 80 ° C. and a molding cycle of 40 seconds, and the molded test piece was cut and placed in a crucible. It was weighed, heated to 600 ° C., kept as it was for 6 hours, allowed to cool, and weighed the incinerated residue remaining in the crucible to measure the amount of layered silicate (inorganic component). That is, since the properties such as the flexural modulus (rigidity) of the resin composition are affected by the proportion of the inorganic component, in each of Examples and Comparative Examples 2 and 3, the proportion of the inorganic component in the test piece was measured, 1 is shown as a ratio (% by weight) of the inorganic component of the B component.
(2) Bottom spacing and average number of laminated silicate layers of layered silicate in the thermoplastic resin composition
The measurement was performed using a powder X-ray diffractometer (RIGAKU ROTAFLEX RU300: manufactured by Rigaku Corporation). A rod-shaped test piece having a thickness of 6.4 mm was molded under the same conditions as in (1), and a measurement molded product cut to a length of 20 mm was fixed to the opening of the sample table so as to be flush with the measurement reference plane. It was used for measurement. The diffraction peak obtained by the measurement is the bottom peak of the layered silicate. Among them, the diffraction peak on the smallest angle side is the peak corresponding to the bottom spacing of the (001) plane, and the bottom spacing is determined by the following Bragg formula. Calculated.
d = λ / (2 sin θ)
(Where d: bottom surface interval (interlayer distance) (nm), 2θ: diffraction angle of diffraction peak (°), λ: X-ray measurement wavelength (nm))
Further, the average number of layers (N) was determined from the following equation.
N = (D / d) +1
(Wherein, N: number of layers (sheets), D: layer thickness (nm), d: bottom interval (nm))
D = 0.9 * λ / (βcosΘ)
(Where D: lamination thickness (nm), λ: X-ray measurement wavelength (nm), β: half width (rad), 2Θ: diffraction angle of the diffraction peak (rad), where half width is the diffraction peak Maximum value I₀Is the width of 2Θ (rad) at a height of, and the diffraction angle of the diffraction peak is the maximum value I₀(Refers to the value of 2Θ in the part)
The measurement conditions are described below.
X-ray source: Cu-Kα (X-ray measurement wavelength 1.5418 × 10^-Tenm), 50kV-200mA
Slit: DS / SS 1/2 °
Rs 0.15mm-graphite monochromator-0.45mm
Method: 2θ-θ
Scan: 0.05 step / 1 to 4 sec
Scan range: 1 to 20 °
[0138]
(3) Viscosity average molecular weight in thermoplastic resin composition
The test piece was molded under the same conditions as in the above (1), and the viscosity average molecular weight of the test piece was measured by the method described in the text.
(4) Flexural modulus
A test piece (dimensions: length 127 mm × width 12.7 mm × thickness 6.4 mm) molded under the same conditions as the above (1) was subjected to ASTM-D790 under an atmosphere of a temperature of 23 ° C. and a relative humidity of 50% RH. The flexural modulus (MPa) was measured by the method according to the above. The larger the value, the better the rigidity of the molded resin composition.
(5) Decrease in viscosity average molecular weight after high temperature and high humidity test (ΔM_ratio)
A test piece of the same shape (dimensions: length 127 mm × width 12.7 mm × thickness 6.4 mm) molded under the same conditions as the above (1) was left for 10 hours in a pressure cooker at a temperature of 105 ° C. and a relative humidity of 100% for 10 hours. After the treatment, the viscosity-average molecular weight measured using a test piece (test piece after treatment) left for 24 hours in an environment of a temperature of 23 ° C. and a relative humidity of 50%, and an environment of a temperature of 23 ° C. and a relative humidity of 50% The viscosity average molecular weight measured using a test piece (test piece before treatment) left for 74 hours at was calculated according to the following formula, and the decrease rate (ΔM) of the viscosity average molecular weight after the constant temperature and constant humidity test was calculated._ratio) Was calculated.
ΔM_ratio= 100 x [(viscosity average molecular weight of test specimen before treatment)-(viscosity average molecular weight of test specimen after treatment)] / (viscosity average molecular weight of test specimen before treatment)
The smaller the value, the better the hydrolysis resistance of the molded resin composition.
[0139]
[material]
The following were used as raw materials.
(A component: polycarbonate resin)
Bisphenol A type aromatic polycarbonate resin powder having a viscosity average molecular weight of 23,800 ["Panlite L-1250WP" manufactured by Teijin Chemicals Ltd.]
[0140]
(B component and other than B component)
B-1: Synthetic mica (Somasif ME-100: manufactured by Corp Chemical Co., Ltd., cation exchange capacity: 110 meq / 100 g)
B-2: Synthetic mica (Somasif ME-100: manufactured by Corp Chemical Co., Ltd.) obtained by substantially completely ion-exchanging trioctylmethylammonium chloride.
B-3: Synthetic mica (Somasif ME-100: manufactured by Corp Chemical Co., Ltd.) obtained by ion exchange of didecyldimethylammonium chloride almost completely.
B-4: Synthetic mica (Somasif ME-100: manufactured by Corp Chemical Co., Ltd.) obtained by almost completely ion-exchanging triphenylmethylammonium chloride.
B-5: Synthetic mica (Somasif ME-100: manufactured by Corp Chemical Co., Ltd.) obtained by almost completely ion-exchanging dioctadecyldimethylammonium chloride.
[0141]
(C component)
C-1: Styrene-maleic anhydride copolymer (manufactured by Nova Chemical Japan Co., Ltd .: “DYLARK 332-80”, maleic anhydride content: about 15% by weight)
(Other components)
TMP: trimethyl phosphate (manufactured by Daihachi Chemical Industry Co., Ltd .: TMP), and the amount added was 0.1 part by weight per 100 parts by weight of component A in all compositions.
[0142]
[Examples 1 and 2, Comparative Examples 1 to 3]
The B component and the C component were mixed in the amount ratio shown in Table 1 with a diameter of 30 mmφ, L / D = 33.2, and a vented twin-screw extruder equipped with screws in two kneading zones (manufactured by Kobe Steel Ltd.): Using KTX30), the mixture was melt-kneaded at a cylinder temperature of 200 ° C., extruded, and strand-cut to obtain pellets. Using the obtained pellets, dry-blending the mixture of the component B and the component C and the component A so that the final ratio is as shown in Table 3, then a diameter of 30 mmφ, L / D = 33.2, and kneading. Using a vented twin-screw extruder equipped with screws in two zones (KTX30, manufactured by Kobe Steel Ltd.), the mixture was melt-kneaded at a cylinder temperature of 280 ° C., extruded, and strand-cut to obtain pellets.
[0143]
The obtained pellets were dried at 100 ° C. for 5 hours using a hot-air circulation dryer. After drying, the test piece was molded by an injection molding machine (manufactured by Toshiba Machine Co., Ltd .: IS-150EN) at a cylinder temperature of 260 ° C, a mold temperature of 80 ° C, and a molding cycle of 40 seconds. Table 1 shows the measurement results for these.
[0144]
[Table 1]

[0145]
As is clear from the above table, the thermoplastic resin composition of the present invention has a good rigidity and a very good hydrolysis resistance by satisfying a specific dispersion form, and further has a good heat stability. It can be seen that a thermoplastic resin composition is provided. In particular, the thermal stability is particularly good when the layered silicate of the component B and the component C are kneaded in advance. This provides a thermoplastic resin composition, particularly an aromatic polycarbonate resin composition, comprising a layered silicate which is practical and applicable in a wide range of fields. It can be seen that the specific effects described above are specifically obtained in the unique dispersion state of the present invention. Due to this dispersion state, the rigidity and hydrolysis resistance are significantly improved.
[0146]
【The invention's effect】
The thermoplastic resin composition of the present invention has good rigidity, has good hydrolysis resistance, and further has a good thermal stability. It is a plastic resin composition. Further, the thermoplastic resin composition of the present invention has melt viscosity characteristics suitable for both injection molding and extrusion molding, and is excellent in moldability. Therefore, it is useful in a wide range of fields such as the thermoplastic resin composition of the present invention, electric and electronic parts, OA equipment parts, automobile parts, agricultural materials, fishery materials, transport containers, packaging containers, and miscellaneous goods. It is particularly useful in the field of electrical and electronic parts, OA equipment parts, and automobile parts, and the industrial effects achieved are outstanding.

Claims (6)

(B) 0.1 to 50 parts by weight of a layered silicate (component B) having a cation exchange capacity of 50 to 200 meq / 100 g per 100 parts by weight of the amorphous thermoplastic resin (component A) In the thermoplastic resin composition, the B component has an average number of silicate layers of 5 to 40 determined by X-ray diffraction in the resin composition, and a bottom surface interval of 1.3 to 2.3 nm. The thermoplastic resin composition which is within the range of. The thermoplastic resin composition according to claim 1, wherein the B component is an organically modified layered silicate obtained by ion-exchanging organic onium ions between layers at a rate of 40% or more of the cation exchange capacity of the layered silicate. The thermoplastic resin composition further comprises (C) a compound having an affinity for the amorphous thermoplastic resin of component (C) and having a hydrophilic component (component (C)) of 0.1 to 100 parts by weight per component A. The thermoplastic resin composition according to any one of claims 1 to 2, comprising 50 parts by weight. The thermoplastic resin composition according to any one of claims 1 to 3, wherein at least 50% by weight of the component A is an aromatic polycarbonate resin. 5. The thermoplastic resin composition according to claim 3, wherein the C component is a styrene-containing polymer having a functional group comprising a carboxyl group and / or a derivative thereof. 6. The thermoplastic resin according to any one of claims 3 to 5, wherein after melt-kneading the component (B) and the component (C), the melt-kneaded product and the component (A) are melt-kneaded using a multi-screw extruder. Resin composition.