JP4926811B2

JP4926811B2 - Resin composition, prepreg, laminate and wiring board

Info

Publication number: JP4926811B2
Application number: JP2007116605A
Authority: JP
Inventors: 高示森田; 伸高根沢; 和永坂井; 裕介近藤
Original assignee: Hitachi Chemical Co Ltd; Showa Denko Materials Co Ltd; Resonac Corp
Current assignee: Resonac Corp
Priority date: 2006-04-28
Filing date: 2007-04-26
Publication date: 2012-05-09
Anticipated expiration: 2027-04-26
Also published as: JP2007314782A

Description

本発明は、樹脂組成物、プリプレグ、積層板及び配線板に関する。 The present invention relates to a resin composition, a prepreg, a laminated board, and a wiring board.

近年の電子機器の小型化・高性能化の流れに伴い、プリント配線板では配線ピッチが狭小化した、高密度の配線が要求されている。高密度配線に対応する半導体の実装方法としては、従来のワイヤボンディング方式に代わり、フリップチップ接続方式が広く用いられている。フリップチップ接続方式は、ワイヤに代えてはんだボールにより、配線板と半導体とを接続させる方法である。互いに向き合わせにした配線板と半導体との間にはんだボールを配置させ、全体に加熱して、はんだをリフロー（溶融接続）させて、配線板と半導体を接続させて実装している。この方法では、はんだリフロー時に３００℃近い熱が配線板等にかかる。この際、従来の樹脂組成物を材料として形成された配線板では、配線板が熱収縮して、配線板と半導体を接続するはんだボールに大きな応力が発生し、配線の接続不良を起こす場合があった。 With recent trend toward downsizing and higher performance of electronic devices, printed wiring boards are required to have high-density wiring with narrowed wiring pitch. As a semiconductor mounting method corresponding to high-density wiring, a flip chip connection method is widely used instead of the conventional wire bonding method. The flip chip connection method is a method of connecting a wiring board and a semiconductor by solder balls instead of wires. Solder balls are arranged between the wiring board and the semiconductor that face each other, and the whole is heated to reflow (melt connection) the solder, and the wiring board and the semiconductor are connected and mounted. In this method, heat close to 300 ° C. is applied to the wiring board and the like during solder reflow. At this time, in the wiring board formed using the conventional resin composition as the material, the wiring board may be thermally contracted, and a large stress is generated in the solder ball connecting the wiring board and the semiconductor, which may cause poor connection of the wiring. there were.

特開２００４−１８２８５１号公報JP 2004-182851 A 特許第２７４０９９０号公報Japanese Patent No. 2740990 特開２０００−２４３８６４号公報JP 2000-243864 A 特開２０００−１１４７２７号公報JP 2000-114727 A

上述の状況を背景として、低熱膨張率の積層板が求められている。従来、積層板としては、エポキシ樹脂を主剤とした樹脂組成物とガラス織布とを硬化・一体成形したものが一般的である。エポキシ樹脂は、絶縁性や耐熱性、コスト等のバランスに優れるが、熱膨張率が大きいため、シリカ等の無機充填材を添加して熱膨張を抑制するのが一般的である（特許文献１参照）。無機充填材を高い割合で充填することにより、さらなる低熱膨張を図ることも可能であるが、充填量を増やすことは吸湿による絶縁信頼性の低下や樹脂−配線層の密着不足、プレス成形不良を起こすことが知られている。そのため、多層配線板における用途では、無機充填材の高充填には限界がある。 Against the background described above, a laminate having a low coefficient of thermal expansion is required. Conventionally, a laminate is generally obtained by curing and integrally molding a resin composition mainly composed of an epoxy resin and a glass woven fabric. Epoxy resins have an excellent balance of insulation, heat resistance, cost, and the like, but since they have a large coefficient of thermal expansion, it is common to suppress thermal expansion by adding an inorganic filler such as silica (Patent Document 1). reference). It is possible to achieve further low thermal expansion by filling the inorganic filler at a high rate, but increasing the filling amount reduces the insulation reliability due to moisture absorption, insufficient adhesion of the resin-wiring layer, and poor press molding. It is known to wake up. For this reason, there is a limit to the high filling of inorganic fillers in applications in multilayer wiring boards.

また、樹脂の選択或いは改良により、低熱膨張を達成することが試みられている。例えば、芳香環を有するエポキシ樹脂の公知例としては、２官能のナフタレン骨格、あるいはビフェニル骨格を有するエポキシ樹脂を用いた低熱膨張性加圧成形用樹脂組成物（特許文献２）があるが、充填材を８０〜９２．５ｖｏｌ％配合している。また、従来、配線板用の樹脂組成物の低熱膨張率化は特許文献３、及び４に示すように架橋密度を高める、すなわち本願出願の架橋点間分子量を小さくし、Ｔｇを高くして熱膨張率を低減する方法が一般的である。しかしながら、架橋密度を高める、すなわち架橋点間分子量を小さくすることは官能基間の分子鎖を短くすることであるが、一定以上分子鎖を短くすることは反応性や樹脂強度等の点で不可能である。このため、架橋密度を高める手法での低熱膨張率化は限界となっていた。 In addition, attempts have been made to achieve low thermal expansion by selecting or improving the resin. For example, as a known example of an epoxy resin having an aromatic ring, there is a resin composition for low thermal expansion pressure molding using an epoxy resin having a bifunctional naphthalene skeleton or a biphenyl skeleton (Patent Document 2). 80-92.5 vol% of the material is blended. Conventionally, the reduction in the coefficient of thermal expansion of a resin composition for a wiring board is to increase the crosslink density as shown in Patent Documents 3 and 4, that is, to reduce the molecular weight between crosslink points in the present application and increase the Tg to increase the heat. A method for reducing the expansion coefficient is common. However, increasing the crosslink density, that is, reducing the molecular weight between crosslink points is to shorten the molecular chain between functional groups, but shortening the molecular chain beyond a certain level is not possible in terms of reactivity and resin strength. Is possible. For this reason, the low thermal expansion coefficient by the method of increasing the crosslinking density has been a limit.

熱膨張の小さい樹脂としてはポリイミドが広く知られているが、成形に高温を要する、コストが高いといった問題がある。また、フィルム状の形態であるためフレキシブル基板用の材料として適している反面、剛性を必要とする多層配線板用途には適さなかった。
本発明は、低コストで低熱膨張な樹脂組成物、プリプレグ、積層板及び配線板を提供することを目的とする。 Polyimide is widely known as a resin having low thermal expansion, but there are problems such as high temperature required for molding and high cost. Further, since it is in the form of a film, it is suitable as a material for a flexible substrate, but it is not suitable for multilayer wiring board applications that require rigidity.
An object of this invention is to provide the resin composition, prepreg, laminated board, and wiring board which are low-cost and low thermal expansion.

本発明は、次の態様を有する。
積層板の製造に用いられる樹脂組成物であって、樹脂組成物が芳香環を有する絶縁性樹脂を含み、かつ芳香環を有する絶縁性樹脂のＴｇ以上のせん断弾性率から求めた、絶縁性樹脂の架橋点間分子量が、積層板製造後の段階で３００〜１０００であることを特徴とする樹脂組成物。 The present invention has the following aspects.
A resin composition for use in the production of a laminate, wherein the resin composition contains an insulating resin having an aromatic ring, and the insulating resin is obtained from a shear elastic modulus of Tg or higher of the insulating resin having an aromatic ring The resin composition characterized in that the molecular weight between cross-linking points is 300 to 1000 at the stage after the production of the laminate.

芳香環を有する絶縁性樹脂が、多環式化合物を含むことを特徴とする樹脂組成物。
絶縁性樹脂が、ビフェニル構造、ナフタレン構造、アントラセン構造、及びジヒドロアントラセン構造のいずれか１つを有することを特徴とする樹脂組成物。
絶縁性樹脂が、エポキシ樹脂であることを特徴とする樹脂組成物。
エポキシ樹脂が結晶性エポキシ樹脂を１つ以上含むことを特徴とする樹脂組成物。 A resin composition, wherein the insulating resin having an aromatic ring contains a polycyclic compound.
A resin composition, wherein the insulating resin has any one of a biphenyl structure, a naphthalene structure, an anthracene structure, and a dihydroanthracene structure.
A resin composition, wherein the insulating resin is an epoxy resin.
A resin composition, wherein the epoxy resin contains one or more crystalline epoxy resins.

エポキシ樹脂が、下記の一般式（１）： The epoxy resin has the following general formula (1):

（式中、Ｒ^１〜Ｒ^４は同一、又は互いに異なるＣ_ｍＨ_２ｍ＋１基を表し、ここでｍは０又は１以上の整数を表し、ｎは０又は１以上の整数を表す）
のビフェニルノボラック型エポキシ樹脂、一般式（２）： (Wherein R ^{1 to} R ⁴ represent the same or different C _m H _{2m + 1} groups, where m represents 0 or an integer of 1 or more, and n represents 0 or an integer of 1 or more)
Biphenyl novolac epoxy resin, general formula (2):

（式中、Ｒ⁵〜Ｒ⁸は同一、又は互いに異なるＣ_ｐＨ_２ｐ＋１基を表し、ここでｐは０又は１以上の整数を表す）
のアントラセン型エポキシ樹脂、一般式（３）： (Wherein R ^{5 to} R ⁸ represent the same or different C _p H _{2p + 1} groups, where p represents 0 or an integer of 1 or more)
Anthracene type epoxy resin, general formula (3):

（式中、Ｒ⁹は同一、又は互いに異なるＣ_ｔＨ_２ｔ＋１基を表し（ここでｔは０又は１以上の整数を表す）、ｒは０〜４の整数を表し、Ｒ¹⁰は同一、又は互いに異なるＣ_ｕＨ_２ｕ＋１基を表し（ここでｕは０又は１以上の整数を表す）、ｓは０〜６の整数を示す）
のジヒドロアントラセン型エポキシ樹脂のいずれか１つ以上含むことを特徴とする請求項１〜５のいずれか１項記載の樹脂組成物。 (Wherein R ⁹ represents the same or different C _t H _{2t + 1} groups (where t represents 0 or an integer of 1 or more), r represents an integer of 0 to 4, and R ¹⁰ is the same, or Represents different C _u H _{2u + 1} groups (where u represents an integer of 0 or 1 or more, and s represents an integer of 0 to 6)
The resin composition according to any one of claims 1 to 5, comprising any one or more of dihydroanthracene type epoxy resins.

エポキシ樹脂の硬化剤が、フェノールノボラック樹脂、クレゾールノボラック樹脂、ビスフェノールＡ型ノボラック樹脂、アミノトリアジンノボラック樹脂、ビスマレイミド含有アミノトリアジンノボラック樹脂、ジシアンジアミド、ベンゾグアナミンのいずれか１つ以上含むことを特徴とする樹脂組成物。
上述の樹脂組成物を基材に塗布して含浸させ、次いで乾燥させて成るプリプレグ。
基材が、ガラス織布、ガラス不織布、アラミド不織布のいずれかであることを特徴とするプリプレグ。
本発明のプリプレグを、積層成形して成る積層板。
本発明の積層板を回路加工して成る配線板。 A resin characterized in that the epoxy resin curing agent includes at least one of phenol novolak resin, cresol novolak resin, bisphenol A type novolak resin, aminotriazine novolak resin, bismaleimide-containing aminotriazine novolak resin, dicyandiamide, and benzoguanamine. Composition.
A prepreg obtained by applying the above-described resin composition to a substrate, impregnating the substrate, and then drying.
A prepreg characterized in that the substrate is one of a glass woven fabric, a glass nonwoven fabric, and an aramid nonwoven fabric.
A laminate obtained by laminating the prepreg of the present invention.
A wiring board formed by subjecting the laminate of the present invention to circuit processing.

従来手法のように架橋密度を高めるのではなく、芳香環を有する樹脂組成物の架橋点間分子量が３００〜１０００になるように樹脂組成を調整し、適正な架橋密度にすることで、低コストで低熱膨張率の樹脂組成物、プリプレグ、積層板及び配線板を提供することが可能となった。 Low cost by adjusting the resin composition so that the molecular weight between cross-linking points of the resin composition having an aromatic ring is 300 to 1000 instead of increasing the cross-linking density as in the conventional method, thereby achieving an appropriate cross-linking density. Thus, it has become possible to provide a resin composition, a prepreg, a laminate and a wiring board having a low thermal expansion coefficient.

本発明者らが研究した結果、従来のように架橋密度を高める、すなわち本願出願の架橋点間分子量を小さくする手法は、熱膨張率の低減には不向きであるという意外な事実がわかった。さらに鋭意研究を進めた結果、芳香環を有する樹脂組成物の架橋密度を架橋点間分子量に換算して３００〜１０００の範囲になるように樹脂組成を適正化することが、熱膨張率の低減に効果が大きいという意外な事実を知見するに至った。本発明の樹脂組成物は、積層板の製造に用いられ、芳香環を有する絶縁性樹脂を含む。本発明に用いる芳香環を有する絶縁性樹脂は、積層板製造後の段階で、Ｔｇ以上のせん断弾性率から求めた架橋点間分子量が３００〜１０００である。絶縁性樹脂の架橋点間分子量を３００〜１０００にすることで芳香環同士の相互作用を強く発現でき、熱膨張率が低い樹脂組成物と多層配線板材料（プリプレグ、積層板）を得ることができる。また、架橋点間分子量が３００以下の場合は、芳香環を有する官能基数の少ない材料（ただし、単官能の材料を含まない）を配合して架橋点間分子量を３００以上にすることができる。また、官能基当量の大きな材料の配合も有効である。この際、芳香環が、多環式化合物を含むことが好ましく、ビフェニル構造、ナフタレン構造、アントラセン構造、及びジヒドロアントラセン構造のいずれかを有することがさらに好ましい。一方、架橋点間分子量が１０００以上の場合は、芳香環を有する官能基数の多い材料を配合して架橋点分子量を１０００以下にすることができる。また、官能基当量の少ない材料の配合も有効である。この場合も芳香環が前記多環式化合物を含むことが好ましい。なお積層板製造後の段階とは、例えば、積層板製造時、あるいは積層板を用い多層配線板等を製造した際、熱履歴工程が施された後である。また絶縁性樹脂のせん断弾性率は、一般的に動的粘弾性装置で測定される。 As a result of studies by the present inventors, it has been found that the conventional method of increasing the crosslinking density, that is, reducing the molecular weight between crosslinking points of the present application is not suitable for reducing the thermal expansion coefficient. As a result of further diligent research, it is possible to reduce the thermal expansion coefficient by optimizing the resin composition so that the crosslink density of the resin composition having an aromatic ring is in the range of 300 to 1000 in terms of the molecular weight between crosslinks. It came to discover the unexpected fact that it is effective. The resin composition of the present invention is used for production of a laminate and includes an insulating resin having an aromatic ring. The insulating resin having an aromatic ring used in the present invention has a molecular weight between crosslinking points of 300 to 1000 determined from a shear elastic modulus of Tg or more at the stage after the production of the laminate. By making the molecular weight between cross-linking points of the insulating resin 300 to 1000, the interaction between aromatic rings can be strongly expressed, and a resin composition and a multilayer wiring board material (prepreg, laminated board) having a low coefficient of thermal expansion can be obtained. it can. When the molecular weight between crosslinking points is 300 or less, a material having a small number of functional groups having an aromatic ring (but not including a monofunctional material) can be blended to increase the molecular weight between crosslinking points to 300 or more. It is also effective to mix a material having a large functional group equivalent. In this case, the aromatic ring preferably contains a polycyclic compound, and more preferably has any of a biphenyl structure, a naphthalene structure, an anthracene structure, and a dihydroanthracene structure. On the other hand, when the molecular weight between crosslinking points is 1000 or more, a crosslinking point molecular weight can be made 1000 or less by blending a material having a large number of functional groups having an aromatic ring. In addition, blending of materials having a small functional group equivalent is also effective. Also in this case, it is preferable that the aromatic ring contains the polycyclic compound. The stage after the production of the laminated board is, for example, after the thermal history process is performed when the laminated board is produced or when a multilayer wiring board or the like is produced using the laminated board. The shear modulus of the insulating resin is generally measured with a dynamic viscoelastic device.

ここで、動的粘弾性装置で測定し、Ｔｇ以上のせん弾性率弾性率から求められた架橋点間分子量とは、例えば、（株）化学同人社発行の高分子と複合材料の力学的性質（著者：Ｌ．Ｅ．Ｎｉｅｌｓｅｎ、訳者：小野木重治）に記載され、その本文中の記載から架橋点間分子量が求められる。すなわち、 Here, the molecular weight between crosslink points measured by a dynamic viscoelasticity device and obtained from the elastic modulus modulus of elasticity of Tg or more is, for example, the mechanical properties of the polymer and composite material issued by Chemical Dojin Co., Ltd. (Author: LE Nielsen, translator: Shigeharu Onoki), and the molecular weight between crosslinking points is determined from the description in the text. That is,

ｌｏｇＧ≒７．０＋２９３ρ／Ｍｃ（Ｇ：せん断弾性率、ρ：材料の密度、Ｍｃ：架橋点間分子量）…式（１） log G≈7.0 + 293ρ / Mc (G: shear modulus, ρ: material density, Mc: molecular weight between cross-linking points) Formula (1)

が実験結果と良く一致する経験式を利用し計算されたものである。本式において、せん断弾性率の単位はｄｙｎを用いる。
なお、式（１）中のＧ（せん断弾性率）は、一般的に動的粘弾性装置から算出された貯蔵弾性率ＥのＴｇ以上の値を下記式（２）の変換式から求められる。 Is calculated using an empirical formula that agrees well with the experimental results. In this formula, dyn is used as the unit of shear modulus.
In addition, G (shear elastic modulus) in Formula (1) is calculated | required from the conversion formula of following formula (2) the value more than Tg of the storage elastic modulus E generally calculated from the dynamic viscoelasticity apparatus.

Ｅ＝２Ｇ（１＋σ）（σ：ポアソン比）…式（２） E = 2G (1 + σ) (σ: Poisson's ratio) Equation (2)

動的粘弾性測定装置とは、一般的に試料に強制振動非共振法により引っ張り、圧縮、曲げ又はせん断方向に正弦波振動又は合成波振動を加えて動的粘弾性を測定するものである。市販されているものとして、（株）ＵＢＭ社製のＲｈｅｏｓｏｌ−Ｅ−４０００がある。測定方法は、恒温槽中の試料に正弦波又は合成波振動を設定された周波数と振幅で加えて、その時に発生する応力レスポンスを検出器でとらえ、貯蔵弾性率等に測定演算式から算出され求めることができる。 The dynamic viscoelasticity measuring apparatus generally measures dynamic viscoelasticity by applying a sinusoidal vibration or a synthetic wave vibration to a sample by a forced vibration non-resonance method, and applying a sinusoidal vibration or a synthetic wave vibration in a compression, bending or shear direction. As a commercially available product, there is Rheosol-E-4000 manufactured by UBM. In the measurement method, a sinusoidal wave or synthetic wave vibration is added to the sample in the thermostatic chamber with the set frequency and amplitude, the stress response generated at that time is captured by the detector, and the storage modulus is calculated from the measurement formula. Can be sought.

上記の測定装置により芳香環を有する絶縁性樹脂が、Ｔｇ以上のせん断弾性率から求めた架橋点間分子量は、３００〜１０００であり、３１０〜９００であることが好ましく、３１０〜８００であるとさらに好ましい。架橋点間分子量が３００未満では、芳香環の相互作用が弱く熱膨張率の低減効果が小さい。一方、架橋点間分子量が１０００より大きい場合、芳香環の相互作用は発現できるが、架橋密度が低下して熱膨張率の低減効果が小さくなる。 When the insulating resin having an aromatic ring by the above-described measuring apparatus has a molecular weight between crosslinking points determined from a shear modulus of Tg or more is 300 to 1,000, preferably 310 to 900, and 310 to 800. Further preferred. When the molecular weight between cross-linking points is less than 300, the aromatic ring interaction is weak and the effect of reducing the thermal expansion coefficient is small. On the other hand, when the molecular weight between cross-linking points is larger than 1000, the interaction of the aromatic ring can be expressed, but the cross-linking density is lowered and the effect of reducing the thermal expansion coefficient is reduced.

本発明で用いる絶縁性樹脂は芳香環を有していれば特に限定するものではないが、多層配線板用途では絶縁性や吸湿性の面で優れているエポキシ樹脂が好適に用いられる。用いるエポキシ樹脂は、分子内に２個以上のエポキシ基をもつ化合物であれば、限定されない。例えば、ナフタレン型エポキシ樹脂（特に２官能ナフタレン型エポキシ樹脂）、アントラセン型エポキシ樹脂、ジヒドロアントラセン型エポキシ樹脂、ビフェニル型エポキシ樹脂、ビスフェノールＡ型エポキシ樹脂、ビスフェノールＦ型エポキシ樹脂、ビスフェノールＳ型エポキシ樹脂、ビフェニルノボラック型エポキシ樹脂、フェノールノボラック型エポキシ樹脂、クレゾールノボラック型エポキシ樹脂等が例示される。これらのうち、結晶性エポキシ樹脂とは、結晶性の強いエポキシ樹脂であり、融点以下の温度では、高分子鎖が規則正しく配列する性質があり、固形樹脂でありながらも、溶融時には液状樹脂並みの低粘度となる熱硬化性のエポキシ樹脂である。結晶性エポキシ樹脂としては、ナフタレン型エポキシ樹脂、アントラセン型エポキシ樹脂、ジヒドロアントラセン型エポキシ樹脂、ビフェニルノボラック型エポキシ樹脂及びビフェニル型エポキシ樹脂等が挙げられ、これらは芳香環の相互作用を強める上で好ましく用いられる。これらの化合物の分子量はどのようなものでもよく、何種類かを併用することもできる。 The insulating resin used in the present invention is not particularly limited as long as it has an aromatic ring, but an epoxy resin excellent in insulation and moisture absorption is suitably used for multilayer wiring board applications. The epoxy resin to be used is not limited as long as it is a compound having two or more epoxy groups in the molecule. For example, naphthalene type epoxy resin (especially bifunctional naphthalene type epoxy resin), anthracene type epoxy resin, dihydroanthracene type epoxy resin, biphenyl type epoxy resin, bisphenol A type epoxy resin, bisphenol F type epoxy resin, bisphenol S type epoxy resin, Examples include biphenyl novolac type epoxy resins, phenol novolac type epoxy resins, cresol novolac type epoxy resins and the like. Among these, the crystalline epoxy resin is an epoxy resin having strong crystallinity, and has a property that the polymer chains are regularly arranged at a temperature below the melting point. It is a thermosetting epoxy resin with low viscosity. Examples of crystalline epoxy resins include naphthalene-type epoxy resins, anthracene-type epoxy resins, dihydroanthracene-type epoxy resins, biphenyl novolac-type epoxy resins, and biphenyl-type epoxy resins, which are preferable for enhancing the interaction of aromatic rings. Used. These compounds may have any molecular weight, and several types may be used in combination.

本発明の樹脂組成物においてエポキシ樹脂を用いる場合には、硬化剤を含むことが好ましい。硬化剤はエポキシ樹脂の硬化作用があれば特に限定されるものではないが、各種アミン類、酸無水物類、ノボラック樹脂類等が挙げられる。この中でも特に、フェノールノボラック樹脂、クレゾールノボラック樹脂、ビスフェノールＡ型ノボラック樹脂、アミノトリアジンノボラック樹脂、ビスマレイミド含有アミノトリアジンノボラック樹脂、ジシアンジアミド、ベンゾグアナミンが好ましく、単独又は二種以上で用いることができる。
また、本発明の樹脂組成物は、硬化促進剤を含むことができ、硬化促進剤は硬化促進作用があれば特に限定されるものではないが、エポキシ樹脂を用いる場合には、潜在性のある各種イミダゾールやイミダゾール誘導体、ＢＦ３アミン錯体、トリフェニルホスフィン、１，８−ジアザビシクロ−（５．４．０）ウンデセン−７、エチルトリフェニルホスホニウムブロミド、テトラメチルアンモニウムクロリド等が挙げられ、特にイミダゾールやイミダゾール誘導体が好ましい。 When using an epoxy resin in the resin composition of the present invention, it is preferable to include a curing agent. The curing agent is not particularly limited as long as it has an epoxy resin curing action, and includes various amines, acid anhydrides, novolak resins, and the like. Of these, phenol novolak resin, cresol novolak resin, bisphenol A type novolak resin, aminotriazine novolak resin, bismaleimide-containing aminotriazine novolak resin, dicyandiamide, and benzoguanamine are particularly preferable and can be used alone or in combination of two or more.
Further, the resin composition of the present invention can contain a curing accelerator, and the curing accelerator is not particularly limited as long as it has a curing accelerating action. However, when an epoxy resin is used, there is a potential. Examples include various imidazoles and imidazole derivatives, BF3 amine complexes, triphenylphosphine, 1,8-diazabicyclo- (5.4.0) undecene-7, ethyltriphenylphosphonium bromide, tetramethylammonium chloride, and the like. Derivatives are preferred.

また、本発明の樹脂組成物を混合するため、溶剤を加えることが好ましい。溶剤は、絶縁性樹脂と、これを硬化反応させる硬化剤等を溶解・混合させる性質を有する剤であれば限定されない。溶剤として、アセトン、メチルエチルケトン、メチルブチルケトン、トルエン、キシレン、酢酸エチル、Ｎ、Ｎ−ジメチルホルムアミド、Ｎ、Ｎ−ジメチルアセトアミド、エタノール、エチレングリコールモノメチルエーテル、プロピレングリコールモノメチルエーテル、プロピレングリコールモノメチルエーテルアセテート、シクロヘキサノン、シクロペンタノン等が樹脂組成物の溶解性に優れ、比較的沸点が低いため、好ましい。これらの溶剤の配合量は、絶縁性樹脂が溶解できればどのような量でもよいが、絶縁性樹脂と硬化剤の総量１００重量部に対して、２０〜３００重量部の範囲が好ましく、３０〜２００重量部の範囲がさらに好ましい。また、上記の溶剤は、組み合わせて用いても構わない。 Moreover, in order to mix the resin composition of this invention, it is preferable to add a solvent. A solvent will not be limited if it is an agent which has the property to melt | dissolve and mix insulating resin and the hardening | curing agent etc. which carry out a hardening reaction of this. As solvents, acetone, methyl ethyl ketone, methyl butyl ketone, toluene, xylene, ethyl acetate, N, N-dimethylformamide, N, N-dimethylacetamide, ethanol, ethylene glycol monomethyl ether, propylene glycol monomethyl ether, propylene glycol monomethyl ether acetate, Cyclohexanone, cyclopentanone, and the like are preferable because of their excellent solubility in the resin composition and relatively low boiling point. The amount of these solvents may be any amount as long as the insulating resin can be dissolved, but is preferably in the range of 20 to 300 parts by weight with respect to 100 parts by weight of the total amount of the insulating resin and the curing agent, and 30 to 200. A range of parts by weight is more preferred. Moreover, you may use said solvent in combination.

樹脂組成物に、無機充填材を配合することができる。無機充填材としては、シリカ、アルミナ、水酸化アルミニウム、炭酸カルシウム、クレイ、タルク、窒化珪素、窒化ホウ素、酸化チタン、チタン酸バリウム、チタン酸鉛、チタン酸ストロンチウム等を使用することができる。この無機充填材の配合量としては、本発明の樹脂組成物の絶縁性樹脂と硬化剤の総量１００重量部に対して、３００重量部以下とすることが好ましく、さらに２５０重量部以下にすることが本発明の多層配線板用材料（プリプレグ、積層板）が均一でかつ良好な取扱性を得るために好ましい。無機充填材を配合する場合は、均一に分散させるため、らいかい機、ホモジナイザー等を用いることが有効である。 An inorganic filler can be mix | blended with a resin composition. As the inorganic filler, silica, alumina, aluminum hydroxide, calcium carbonate, clay, talc, silicon nitride, boron nitride, titanium oxide, barium titanate, lead titanate, strontium titanate, or the like can be used. The blending amount of the inorganic filler is preferably 300 parts by weight or less, more preferably 250 parts by weight or less with respect to 100 parts by weight of the total amount of the insulating resin and the curing agent of the resin composition of the present invention. However, the multilayer wiring board material (prepreg, laminated board) of the present invention is preferable for obtaining uniform and good handling properties. When an inorganic filler is blended, it is effective to use a raking machine, a homogenizer, or the like in order to disperse uniformly.

本発明の樹脂組成物には、本発明の目的の範囲内において、更に、添加剤を含ませることができる。添加剤としては、各種シランカップリング剤、消泡剤等を使用できる。この配合量としては、絶縁性樹脂と硬化剤の総量１００重量部に対して、５重量部以下とすることが好ましく、さらに３重量部以下にすることが樹脂組成物の特性を維持する上で好ましい。 The resin composition of the present invention may further contain an additive within the scope of the object of the present invention. As the additive, various silane coupling agents, antifoaming agents and the like can be used. The blending amount is preferably 5 parts by weight or less with respect to 100 parts by weight of the total amount of the insulating resin and the curing agent, and further 3 parts by weight or less is necessary for maintaining the characteristics of the resin composition. preferable.

また、一般的に絶縁性樹脂に無機充填材を配合した場合の架橋点間分子量は、無機充填材の弾性率の影響で、樹脂組成物の弾性率が大きくなり、絶縁性樹脂単独の架橋点間分子量の値よりも見かけ上小さくなる。このため、無機充填材を除いた状態で弾性率を測定し、架橋点間分子量を計算することが好ましいが、無機充填材を除去できない場合、式（３）を用いて弾性率の修正を行い、前記式（１）及び式（２）を用いて計算された架橋点間分子量を、本発明の架橋点間分子量として適用することができる。ただし、式（３）を用いた弾性率の修正は、弾性率の単位としてＰａを用いて行い、式（１）でｄｙｎに修正し、式（２）のポアソン比及び比重は樹脂のみの値を用いる必要がある。実際に、測定できない場合には、ポアソン比０．５、比重１．２を代入して算出する。 In general, the molecular weight between cross-linking points when an inorganic filler is blended with an insulating resin is that the elastic modulus of the resin composition increases due to the effect of the elastic modulus of the inorganic filler. Apparently smaller than the value of intermolecular weight. For this reason, it is preferable to measure the elastic modulus without the inorganic filler and calculate the molecular weight between cross-linking points. However, if the inorganic filler cannot be removed, the elastic modulus is corrected using Equation (3). The molecular weight between crosslinking points calculated using the above formulas (1) and (2) can be applied as the molecular weight between crosslinking points of the present invention. However, the correction of the elastic modulus using the equation (3) is performed using Pa as a unit of the elastic modulus, corrected to dyn by the equation (1), and the Poisson's ratio and specific gravity of the equation (2) are values only for the resin. Must be used. Actually, when the measurement is impossible, the calculation is performed by substituting the Poisson's ratio 0.5 and the specific gravity 1.2.

Ｅｂ＝Ｅａ−（０．０６５×Ｖｆ×Ｖｆ＋０．０２３×Ｖｆ＋０．００１）×Ｖｆ×Ｅｆ／８…式（３）
（Ｖｆ：無機充填材の体積分率、Ｅａ：無機充填材を配合した状態の貯蔵弾性率、Ｅｂ：修正した貯蔵弾性率、Ｅｆ：無機充填材の弾性率） Eb = Ea- (0.065 * Vf * Vf + 0.023 * Vf + 0.001) * Vf * Ef / 8 ... Formula (3)
(Vf: volume fraction of inorganic filler, Ea: storage elastic modulus in a state where inorganic filler is blended, Eb: corrected storage elastic modulus, Ef: elastic modulus of inorganic filler)

本発明のプリプレグは、上述の樹脂組成物を基材に塗布乾燥させて得られる。また本発明の積層板は、プリプレグを、積層成形して得られる。積層成形条件は特に限定されず、また、積層成形の際、金属箔を配し、金属張積層板としてもよい。また本発明の配線板は、上述の積層板に一般的な回路加工を施して得られる。 The prepreg of the present invention is obtained by applying and drying the above resin composition on a substrate. The laminate of the present invention can be obtained by laminating a prepreg. Lamination molding conditions are not particularly limited, and a metal foil may be provided at the time of lamination molding to form a metal-clad laminate. The wiring board of the present invention is obtained by subjecting the above-mentioned laminated board to general circuit processing.

基材は、樹脂組成物を含浸させて、熱硬化・一体化できるものであればよく、ガラス織布、ガラス不織布、アラミド不織布が好適に用いられる。例えば、合成繊維の不織布、又は織布、紙等用いることができる。また、樹脂組成物と基材とを熱硬化・一体化させた場合、基材の弾性率の影響で、樹脂組成物の弾性率が大きくなり、絶縁性樹脂単独の架橋点間分子量の値よりも見かけ上小さくなる。このため、基材から分離させた樹脂単独の弾性率から架橋点間分子量を計算することが好ましいが、基材と分離できない場合、式（４）を用いて基材と一体化した状態で測定した弾性率の修正を行うことができる。修正した貯蔵弾性率を用いて、式（１）、式（２）を用いて算出した架橋点間分子量を本発明の架橋点間分子量として適用することができ、式（２）のポアソン比及び比重は樹脂のみの値を用いる必要がある。実際に、測定できない場合には、ポアソン比０．５、比重１．２を代入して算出する。 The base material only needs to be impregnated with the resin composition and can be thermoset and integrated, and glass woven fabric, glass nonwoven fabric, and aramid nonwoven fabric are preferably used. For example, synthetic nonwoven fabric, woven fabric, paper, or the like can be used. In addition, when the resin composition and the substrate are thermoset and integrated, the elastic modulus of the resin composition increases due to the influence of the elastic modulus of the substrate, and the molecular weight value between the crosslinking points of the insulating resin alone Is also apparently smaller. For this reason, it is preferable to calculate the molecular weight between crosslinking points from the elastic modulus of the resin alone separated from the base material, but when it cannot be separated from the base material, it is measured in the state integrated with the base material using Equation (4). It is possible to correct the elastic modulus. Using the corrected storage elastic modulus, the molecular weight between cross-linking points calculated using the formula (1) and the formula (2) can be applied as the molecular weight between cross-linking points of the present invention, and the Poisson's ratio of the formula (2) and It is necessary to use a specific gravity value only for the resin. Actually, when the measurement is impossible, the calculation is performed by substituting the Poisson's ratio 0.5 and the specific gravity 1.2.

Ｅａ＝０．１１×Ｅｂ−６．２５×１０^８・・・式（４）
（Ｅａ：修正後の貯蔵弾性率、Ｅｂ：基材と一体化した状態の貯蔵弾性率）
なお無機充填材が配合されている場合は、式（４）で計算された弾性率を、前記の式（３）でさらに弾性率の修正を行う必要がある。 Ea = 0.11 × Eb−6.25 × 10 ⁸ Formula (4)
(Ea: storage elastic modulus after correction, Eb: storage elastic modulus in an integrated state with the base material)
In addition, when the inorganic filler is mix | blended, it is necessary to correct the elasticity modulus calculated by Formula (4) further by said Formula (3).

以下に、本発明を実施例に基づいて詳細に説明するが、本発明は実施例に示される態様に限定されるものではない。 Hereinafter, the present invention will be described in detail based on examples, but the present invention is not limited to the embodiments shown in the examples.

実施例１
下記組成の絶縁性樹脂ワニスを作製した。この時のエポキシに対する熱硬化剤の当量は１．０当量とした。この絶縁性樹脂ワニスをＰＥＴフィルム上に塗工し、１２０℃で１０分間乾燥させて、半硬化状態とし、膜厚７０±５μmの絶縁性樹脂付フィルムを作製した。絶縁性樹脂付フィルムから半硬化した樹脂を採取して粉末にした。半硬化樹脂の粉末から、次の手順で樹脂板を作製した。スペーサ及び離型シートとして、樹脂板の型として５０ｍｍ角に穴明をしたフッ素樹脂シートを配置し、この中に樹脂粉を入れ、この上下に銅箔を配置して、１７５℃、９０分、２．５ＭＰａのプレス条件で硬化させた。その後銅箔をエッチング除去し、樹脂板はフッ素樹脂シートから剥がして、厚さ０．２ｍｍの熱膨張率・弾性率測定用樹脂板を作製した。
・２官能ナフタレン型エポキシ樹脂：ＨＰ−４０３２Ｄ：１００ｇ（商品名、大日本インキ化学工業株式会社製）
・アミノトリアジンノボラック樹脂：ＬＡ−３０１８：５２．９ｇ（商品名、大日本インキ化学工業株式会社製）
・硬化促進剤：１−シアノエチル−２−フェニルイミダゾール：２ＰＺ−ＣＮ：０．５ｇ（商品名、四国化成工業株式会社製）
・溶剤：メチルエチルケトン：２５０ｇ Example 1
An insulating resin varnish having the following composition was prepared. The equivalent of the thermosetting agent to the epoxy at this time was 1.0 equivalent. This insulating resin varnish was applied onto a PET film and dried at 120 ° C. for 10 minutes to obtain a semi-cured state, whereby a film with an insulating resin film thickness of 70 ± 5 μm was produced. The semi-cured resin was collected from the film with insulating resin and powdered. A resin plate was prepared from the semi-cured resin powder by the following procedure. As a spacer and a release sheet, a fluororesin sheet having a hole of 50 mm square is disposed as a mold of a resin plate, resin powder is put therein, copper foil is disposed above and below, and 175 ° C., 90 minutes, Curing was performed under a press condition of 2.5 MPa. Thereafter, the copper foil was removed by etching, and the resin plate was peeled off from the fluororesin sheet to produce a 0.2 mm thick resin plate for measuring the thermal expansion coefficient and elastic modulus.
-Bifunctional naphthalene type epoxy resin: HP-4032D: 100 g (trade name, manufactured by Dainippon Ink & Chemicals, Inc.)
Aminotriazine novolak resin: LA-3018: 52.9 g (trade name, manufactured by Dainippon Ink & Chemicals, Inc.)
Curing accelerator: 1-cyanoethyl-2-phenylimidazole: 2PZ-CN: 0.5 g (trade name, manufactured by Shikoku Kasei Kogyo Co., Ltd.)
・ Solvent: Methyl ethyl ketone: 250 g

実施例２
エポキシ樹脂を、ジヒドロアントラセン型エポキシ樹脂：ＹＸ−８８００（商品名、ジャパンエポキシレジン株式会社製）１００ｇに代え、硬化剤であるアミノトリアジンノボラック樹脂ＬＡ−３０１８を、５２．９ｇから３９．８ｇにした以外は、実施例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Example 2
The epoxy resin was replaced with 100 g of dihydroanthracene type epoxy resin: YX-8800 (trade name, manufactured by Japan Epoxy Resin Co., Ltd.), and the aminotriazine novolak resin LA-3018 as a curing agent was changed from 52.9 g to 39.8 g. Except for the above, a resin plate for measuring thermal expansion coefficient and elastic modulus was obtained in the same manner as in Example 1.

実施例３
エポキシ樹脂をビフェニルノボラック型エポキシ樹脂：ＮＣ−３０００−Ｈ（商品名、日本化薬株式会社製）１００ｇに代え、硬化剤であるアミノトリアジンノボラック樹脂ＬＡ−３０１８を２４．９ｇにした以外は、実施例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Example 3
Except that the epoxy resin was replaced with 100 g of biphenyl novolac type epoxy resin: NC-3000-H (trade name, manufactured by Nippon Kayaku Co., Ltd.), and the aminotriazine novolak resin LA-3018 as a curing agent was changed to 24.9 g. In the same manner as in Example 1, a resin plate for measuring the thermal expansion coefficient and elastic modulus was obtained.

実施例４
実施例１の組成に、シリカ：ＳＯ−Ｇ１（商品名、株式会社アドマテックス製、平均粒径０．２〜０．４μｍ）を１８７．５ｇ加えた以外は、実施例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Example 4
Heat was applied in the same manner as in Example 1 except that 187.5 g of silica: SO-G1 (trade name, manufactured by Admatechs Co., Ltd., average particle size: 0.2 to 0.4 μm) was added to the composition of Example 1. A resin plate for measuring expansion coefficient and elastic modulus was obtained.

実施例５
（１）ガラス織布含浸用樹脂の作製
以下に示す組成のガラス織布含浸用樹脂ワニスを作製した。
・２官能ナフタレン型エポキシ樹脂：ＨＰ−４０３２Ｄ：１００ｇ（商品名、大日本インキ化学工業株式会社製）
・アミノトリアジンノボラック樹脂：ＬＡ−３０１８：５２．９ｇ（商品名、大日本インキ化学工業株式会社製）
・硬化促進剤：２ＰＺ−ＣＮ：０．５ｇ（商品名、四国化成工業株式会社製）
・シリカ：ＳＯ−Ｇ１：１８７．５ｇ（商品名、株式会社アドマテックス製、平均粒径０．２〜０．４μｍ）
・溶剤：メチルエチルケトン：４００ｇ Example 5
(1) Preparation of resin for impregnating glass woven fabric A resin varnish for impregnating glass woven fabric having the composition shown below was prepared.
-Bifunctional naphthalene type epoxy resin: HP-4032D: 100 g (trade name, manufactured by Dainippon Ink & Chemicals, Inc.)
Aminotriazine novolak resin: LA-3018: 52.9 g (trade name, manufactured by Dainippon Ink & Chemicals, Inc.)
Curing accelerator: 2PZ-CN: 0.5 g (trade name, manufactured by Shikoku Kasei Kogyo Co., Ltd.)
Silica: SO-G1: 187.5 g (trade name, manufactured by Admatechs Co., Ltd., average particle size 0.2 to 0.4 μm)
・ Solvent: Methyl ethyl ketone: 400g

（２）熱膨張率測定基板の作製
（１）で作製したガラス織布含浸用樹脂ワニスを厚みが０．２ｍｍのガラス織布（坪量２１０ｇ／ｍ^２）に含浸し、１６０℃で３分間加熱して半硬化（Ｂステージ状態）のプリプレグを得た。このプリプレグを４枚重ね、その両側に金属箔として厚さ１８μｍの商品名Ｆ２−ＷＳ銅箔（Ｒｚ：２．０μｍ、Ｒａ：０．３μｍ）を重ね、１７５℃、９０分、２．５ＭＰａのプレス条件で両面銅張積層板を作製した。この銅張り積層板を過硫酸アンモニウム１５０ｇ／ｌの水溶液に４０℃−２０分間浸漬して銅箔をエッチング除去し、熱膨張率・弾性率測定用基板を得た。 (2) Production of thermal expansion coefficient measurement substrate The glass woven fabric impregnating resin varnish produced in (1) was impregnated into a glass woven fabric having a thickness of 0.2 mm (basis weight 210 g / m ² ), and at 160 ° C. for 3 minutes. A semi-cured (B stage state) prepreg was obtained by heating. Four sheets of this prepreg are stacked, and a product name F2-WS copper foil (Rz: 2.0 μm, Ra: 0.3 μm) having a thickness of 18 μm is stacked on both sides of the prepreg as 175 ° C., 90 minutes, 2.5 MPa. A double-sided copper-clad laminate was produced under pressing conditions. This copper-clad laminate was immersed in an aqueous solution of 150 g / l ammonium persulfate at 40 ° C. for 20 minutes to remove the copper foil by etching to obtain a substrate for measuring thermal expansion coefficient / elastic modulus.

実施例６
エポキシ樹脂としてジヒドロアントラセン型エポキシ樹脂：ＹＸ−８８００（商品名、ジャパンエポキシレジン株式会社製）を１００ｇ、ビフェニルノボラック型エポキシ樹脂：ＮＣ−３０００−Ｈ（商品名、日本化薬株式会社製）６５．８ｇ、クレゾールノボラック樹脂：ＫＡ−１１６５（商品名、大日本インキ化学工業株式会社製）を８４．５ｇ、プロピレングリコールモノメチルエーテルに２重量％溶解したジシアンジアミド（関東化学株式会社製）をジシアンジアミド換算で１．６６ｇにした以外は、実施例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Example 6
As an epoxy resin, 100 g of dihydroanthracene type epoxy resin: YX-8800 (trade name, manufactured by Japan Epoxy Resin Co., Ltd.), biphenyl novolac type epoxy resin: NC-3000-H (trade name, manufactured by Nippon Kayaku Co., Ltd.) 8 g, cresol novolak resin: 84.5 g of KA-1165 (trade name, manufactured by Dainippon Ink & Chemicals, Inc.), dicyandiamide (manufactured by Kanto Chemical Co., Ltd.) dissolved in 2% by weight in propylene glycol monomethyl ether is 1 in terms of dicyandiamide. A resin plate for measuring the coefficient of thermal expansion / elastic modulus was obtained in the same manner as in Example 1 except that the amount was changed to .66 g.

実施例７
エポキシ樹脂としてジヒドロアントラセン型エポキシ樹脂：ＹＸ−８８００（商品名、ジャパンエポキシレジン株式会社製）を１００ｇ、ビフェニルノボラック型エポキシ樹脂：ＮＣ−３０００−Ｈ（商品名、日本化薬株式会社製）６５．８ｇ、クレゾールノボラック樹脂：ＫＡ−１１６５（商品名、大日本インキ化学工業株式会社製）を７５．１ｇ、ベンゾグアナミン（関東化学株式会社製）９．９ｇにした以外は、実施例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Example 7
As an epoxy resin, 100 g of dihydroanthracene type epoxy resin: YX-8800 (trade name, manufactured by Japan Epoxy Resin Co., Ltd.), biphenyl novolac type epoxy resin: NC-3000-H (trade name, manufactured by Nippon Kayaku Co., Ltd.) 8 g, cresol novolak resin: KA-1165 (trade name, manufactured by Dainippon Ink & Chemicals, Inc.) was changed to 75.1 g, and benzoguanamine (manufactured by Kanto Chemical Co., Ltd.) was changed to 9.9 g. A resin plate for measuring thermal expansion coefficient and elastic modulus was obtained.

実施例８
エポキシ樹脂として２官能ナフタレン型エポキシ樹脂：ＨＰ−４０３２Ｄ（商品名、大日本インキ化学工業株式会社製）を１００ｇ、ビスマレイミド含有アミノトリアジンノボラック樹脂：ＩＺ−９８７２（商品名、大日本インキ化学工業株式会社製）を４７８ｇにした以外は、実施例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Example 8
100 g of bifunctional naphthalene-type epoxy resin: HP-4032D (trade name, manufactured by Dainippon Ink & Chemicals, Inc.) as an epoxy resin, bismaleimide-containing aminotriazine novolak resin: IZ-9872 (trade name, Dainippon Ink & Chemicals, Inc.) A resin plate for measuring the coefficient of thermal expansion / elastic modulus was obtained in the same manner as in Example 1 except that the product was 478 g.

実施例９
エポキシ樹脂としてジヒドロアントラセン型エポキシ樹脂：ＹＸ−８８００（商品名、ジャパンエポキシレジン株式会社製）を１００ｇ、フェノールノボラック型エポキシ樹脂：Ｎ−７７０（商品名、大日本インキ化学工業株式会社製）４４．８ｇ、ＬＡ−３０１８を５９．６ｇに代え、更に、シリカ：ＳＯ−Ｇ１（商品名、株式会社アドマテックス製、平均粒径０．２〜０．４μm）を２４９．８ｇ加えた以外は、実施例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Example 9
100 g of dihydroanthracene type epoxy resin: YX-8800 (trade name, manufactured by Japan Epoxy Resin Co., Ltd.) as an epoxy resin, phenol novolac type epoxy resin: N-770 (trade name, manufactured by Dainippon Ink & Chemicals, Inc.) 44. 8 g, LA-3018 was replaced with 59.6 g, and silica: SO-G1 (trade name, manufactured by Admatechs Co., Ltd., average particle size 0.2 to 0.4 μm) was added, except that 249.8 g was added. In the same manner as in Example 1, a resin plate for measuring the thermal expansion coefficient and elastic modulus was obtained.

実施例１０
エポキシ樹脂としてジヒドロアントラセン型エポキシ樹脂：ＹＸ−８８００（商品名、ジャパンエポキシレジン株式会社製）を１００ｇ、フェノールノボラック型エポキシ樹脂：Ｎ−７４０（商品名、大日本インキ化学工業株式会社製）４２．６ｇ、硬化剤としてのＬＡ−３０１８を５９．６ｇに代え、更に、シリカ：ＳＯ−Ｇ１（商品名、株式会社アドマテックス製、平均粒径０．２〜０．４μm）を２４７．１ｇ加えた以外は、実施例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Example 10
100 g of dihydroanthracene type epoxy resin: YX-8800 (trade name, manufactured by Japan Epoxy Resin Co., Ltd.) as an epoxy resin, phenol novolac type epoxy resin: N-740 (trade name, manufactured by Dainippon Ink & Chemicals, Inc.) 6g, LA-3018 as a curing agent was replaced with 59.6 g, and 247.1 g of silica: SO-G1 (trade name, manufactured by Admatechs Co., Ltd., average particle size 0.2 to 0.4 μm) was further added. Except for the above, a resin plate for measuring thermal expansion coefficient and elastic modulus was obtained in the same manner as in Example 1.

実施例１１
エポキシ樹脂としてジヒドロアントラセン型エポキシ樹脂：ＹＸ−８８００（商品名、ジャパンエポキシレジン株式会社製）を１００ｇ、ビスフェノールＡ型エポキシ樹脂：Ｎ−８６５（商品名、大日本インキ化学工業株式会社製）４９．５ｇ、硬化剤としてのＬＡ−３０１８を５９．６ｇに代え、更に、シリカ：ＳＯ−Ｇ１（商品名、株式会社アドマテックス製、平均粒径０．２〜０．４μm）を２５５．６ｇ加えた以外は、実施例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Example 11
As an epoxy resin, 100 g of dihydroanthracene type epoxy resin: YX-8800 (trade name, manufactured by Japan Epoxy Resin Co., Ltd.), bisphenol A type epoxy resin: N-865 (trade name, manufactured by Dainippon Ink & Chemicals, Inc.) 49. 55.6 g, LA-3018 as a curing agent was replaced with 59.6 g, and further, 255.6 g of silica: SO-G1 (trade name, manufactured by Admatechs Co., Ltd., average particle size 0.2 to 0.4 μm) was added. Except for the above, a resin plate for measuring thermal expansion coefficient and elastic modulus was obtained in the same manner as in Example 1.

実施例１２
エポキシ樹脂としてジヒドロアントラセン型エポキシ樹脂：ＹＸ−８８００（商品名、ジャパンエポキシレジン株式会社製）を１００ｇ、及びビフェニルノボラック型エポキシ樹脂：ＮＣ−３０００−Ｈ（商品名、日本化薬株式会社製）６５．８ｇ、硬化剤としてのクレゾールノボラック樹脂：ＫＡ−１１６５（商品名、大日本インキ化学工業株式会社製）を８４．５ｇ、及びプロピレングリコールモノメチルエーテルに２重量％溶解したジシアンジアミド（関東化学株式会社製）をジシアンジアミド換算で１．６６ｇにし、シリカ：ＳＯ−Ｇ１（商品名、株式会社アドマテックス製、平均粒径０．２〜０．４μｍ）を、３０８．０ｇとした以外は、実施例５と同様にして熱膨張率・弾性率測定用基板を得た。 Example 12
100 g of dihydroanthracene type epoxy resin: YX-8800 (trade name, manufactured by Japan Epoxy Resin Co., Ltd.) as an epoxy resin, and biphenyl novolac type epoxy resin: NC-3000-H (trade name, manufactured by Nippon Kayaku Co., Ltd.) 65 .8 g, cresol novolak resin as a curing agent: 84.5 g of KA-1165 (trade name, manufactured by Dainippon Ink & Chemicals, Inc.) and dicyandiamide (manufactured by Kanto Chemical Co., Ltd.) dissolved in 2% by weight in propylene glycol monomethyl ether ) To 1.66 g in terms of dicyandiamide, and Example 5 except that the silica: SO-G1 (trade name, manufactured by Admatechs Co., Ltd., average particle size 0.2 to 0.4 μm) was 308.0 g. Similarly, a thermal expansion coefficient / elastic modulus measurement substrate was obtained.

比較例１
下記組成の絶縁性樹脂ワニスを作製した。この時のエポキシに対する熱硬化剤の当量は１．０当量とした。この絶縁性樹脂ワニスをＰＥＴフィルム上に塗工し、１２０℃−１０分乾燥させて、膜厚７０±５μｍの絶縁性樹脂付フィルムを作製した。絶縁性樹脂付フィルムから半硬化樹脂を採取して粉末にした。半硬化樹脂の粉末から、次の手順で樹脂板を作製した。スペーサ及び離型シートとして、樹脂板の型として５０ｍｍ角に穴明をしたフッ素樹脂シートを配置し、この中に樹脂粉を入れ、この上下に銅箔を配置して、１７５℃、９０分、２．５ＭＰａのプレス条件で硬化させた。その後銅箔をエッチング除去し、樹脂板はフッ素樹脂シートから剥がして、厚さ０．２ｍｍの熱膨張率・弾性率測定用樹脂板を作製した。
・フェノールノボラック型エポキシ樹脂：Ｎ−７７０：１００ｇ（商品名、大日本インキ化学工業株式会社製）
・フェノールノボラック樹脂：ＨＰ−８５０：５３．３ｇ（商品名、日立化成工業株式会社製）
・ジシアンジアミド：０．１３ｇ（商品名、関東化学株式会社製）
・硬化促進剤：２ＰＺ−ＣＮ：０．５ｇ（商品名、四国化成工業株式会社製）
・溶剤：メチルエチルケトン：２５０ｇ Comparative Example 1
An insulating resin varnish having the following composition was prepared. The equivalent of the thermosetting agent to the epoxy at this time was 1.0 equivalent. This insulating resin varnish was applied onto a PET film and dried at 120 ° C. for 10 minutes to produce a film with an insulating resin having a thickness of 70 ± 5 μm. Semi-cured resin was collected from the film with insulating resin and powdered. A resin plate was prepared from the semi-cured resin powder by the following procedure. As a spacer and a release sheet, a fluororesin sheet having a hole of 50 mm square is disposed as a mold of a resin plate, resin powder is put therein, copper foil is disposed above and below, and 175 ° C., 90 minutes, Curing was performed under a press condition of 2.5 MPa. Thereafter, the copper foil was removed by etching, and the resin plate was peeled off from the fluororesin sheet to produce a 0.2 mm thick resin plate for measuring the thermal expansion coefficient and elastic modulus.
-Phenol novolac type epoxy resin: N-770: 100 g (trade name, manufactured by Dainippon Ink & Chemicals, Inc.)
-Phenol novolac resin: HP-850: 53.3 g (trade name, manufactured by Hitachi Chemical Co., Ltd.)
・ Dicyandiamide: 0.13 g (trade name, manufactured by Kanto Chemical Co., Inc.)
Curing accelerator: 2PZ-CN: 0.5 g (trade name, manufactured by Shikoku Kasei Kogyo Co., Ltd.)
・ Solvent: Methyl ethyl ketone: 250 g

比較例２
エポキシ樹脂として４官能ナフタレン型エポキシ樹脂：ＨＰ−４７００（商品名、大日本インキ化学工業株式会社製）を１００ｇ、硬化剤としてアミノトリアジンノボラック樹脂：ＬＡ−３０１８（商品名、大日本インキ化学工業株式会社製）を４３．４ｇにした以外は、比較例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Comparative Example 2
100 g of tetrafunctional naphthalene type epoxy resin: HP-4700 (trade name, manufactured by Dainippon Ink & Chemicals, Inc.) as an epoxy resin, and aminotriazine novolak resin: LA-3018 (trade name, Dainippon Ink & Chemicals, Inc.) as a curing agent A resin plate for measuring the coefficient of thermal expansion / elastic modulus was obtained in the same manner as in Comparative Example 1 except that the product was 43.4 g.

比較例３
（ＨＰ−４０３２反応物の作製）
温度計、冷却管、攪拌装置を備えた１リットルの４つ口セパラブルフラスコに、下記の組成１を投入し、１００℃で２時間反応させた。室温（２５℃）まで冷却し、下記の組成２を投入して絶縁性樹脂ワニスを作製した。この絶縁性樹脂ワニスをＰＥＴフィルム上に塗工し、１６０℃−１０分乾燥させて、膜厚７０±５μｍの絶縁性樹脂付フィルムを作製した。絶縁性樹脂付フィルムから半硬化樹脂を採取して粉末にした。半硬化樹脂の粉末から、次の手順で樹脂板を作製した。スペーサ及び離型シートとして、樹脂板の型として５０ｍｍ角に穴明をしたフッ素樹脂シートを配置し、この中に樹脂粉を入れ、この上下に銅箔を配置して、１７５℃、９０分、２．５ＭＰａのプレス条件で硬化させた。その後銅箔をエッチング除去し、樹脂板はフッ素樹脂シートから剥がして、厚さ０．２ｍｍの熱膨張率・弾性率測定用樹脂板を作製した。
「組成１」
・２官能ナフタレン型エポキシ樹脂：ＨＰ−４０３２Ｄ：８３．２ｇ（商品名、大日本インキ化学工業株式会社製）
・ビスフェノールＡ：６９．８ｇ（試薬、関東化学株式会社製）
・硬化促進剤：２ＰＺ−ＣＮ：０．４ｇ（商品名、四国化成工業株式会社製）
「組成２」
・２官能ナフタレン型エポキシ樹脂：ＨＰ−４０３２Ｄ：１００ｇ（商品名、大日本インキ化学工業株式会社製）
・アミノトリアジンノボラック樹脂：ＬＡ−３０１８：５２．９ｇ（商品名、大日本インキ化学工業株式会社製）
・硬化促進剤：２ＰＺ−ＣＮ：０．５ｇ（商品名、四国化成工業株式会社製）
・溶剤：シクロヘキサノン：２５０ｇ Comparative Example 3
(Preparation of HP-4032 reactant)
The following composition 1 was put into a 1 liter four-necked separable flask equipped with a thermometer, a condenser, and a stirrer, and reacted at 100 ° C. for 2 hours. It cooled to room temperature (25 degreeC), the following composition 2 was thrown in, and the insulating resin varnish was produced. This insulating resin varnish was coated on a PET film and dried at 160 ° C. for 10 minutes to produce a film with an insulating resin having a film thickness of 70 ± 5 μm. Semi-cured resin was collected from the film with insulating resin and powdered. A resin plate was prepared from the semi-cured resin powder by the following procedure. As a spacer and a release sheet, a fluororesin sheet having a hole of 50 mm square is disposed as a mold of a resin plate, resin powder is put therein, copper foil is disposed above and below, and 175 ° C., 90 minutes, Curing was performed under a press condition of 2.5 MPa. Thereafter, the copper foil was removed by etching, and the resin plate was peeled off from the fluororesin sheet to produce a 0.2 mm thick resin plate for measuring the thermal expansion coefficient and elastic modulus.
“Composition 1”
-Bifunctional naphthalene type epoxy resin: HP-4032D: 83.2 g (trade name, manufactured by Dainippon Ink & Chemicals, Inc.)
-Bisphenol A: 69.8 g (reagent, manufactured by Kanto Chemical Co., Inc.)
Curing accelerator: 2PZ-CN: 0.4 g (trade name, manufactured by Shikoku Kasei Kogyo Co., Ltd.)
“Composition 2”
-Bifunctional naphthalene type epoxy resin: HP-4032D: 100 g (trade name, manufactured by Dainippon Ink & Chemicals, Inc.)
Aminotriazine novolak resin: LA-3018: 52.9 g (trade name, manufactured by Dainippon Ink & Chemicals, Inc.)
Curing accelerator: 2PZ-CN: 0.5 g (trade name, manufactured by Shikoku Kasei Kogyo Co., Ltd.)
・ Solvent: Cyclohexanone: 250 g

比較例４
シリカ：ＳＯ−Ｇ１（商品名、株式会社アドマテックス製、平均粒径０．２〜０．４μｍ）を１８８．２ｇ加えた以外は、比較例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Comparative Example 4
Silica: Same as Comparative Example 1 except that 188.2 g of SO-G1 (trade name, manufactured by Admatechs Co., Ltd., average particle size 0.2 to 0.4 μm) was added. A resin plate was obtained.

比較例５
（１）ガラス織布含浸用樹脂の作製
以下に示す組成のガラス織布含浸用樹脂ワニスを作製した。
・フェノールノボラック型エポキシ樹脂：Ｎ−７７０：１００ｇ（商品名、大日本インキ化学工業株式会社製）
・フェノールノボラック樹脂：ＨＰ−８５０：５３．３ｇ（商品名、日立化成工業株式会社製）
・ジシアンジアミド：０．１３ｇ（商品名、関東化学株式会社製）
・硬化促進剤：２ＰＺ−ＣＮ：０．５ｇ（商品名、四国化成工業株式会社製）
・シリカ：ＳＯ−Ｇ１：１８８．２ｇ（商品名、株式会社アドマテックス製、平均粒径０．２〜０．４μｍ）
・溶剤：メチルエチルケトン：４００ｇ Comparative Example 5
(1) Preparation of resin for impregnating glass woven fabric A resin varnish for impregnating glass woven fabric having the composition shown below was prepared.
-Phenol novolac type epoxy resin: N-770: 100 g (trade name, manufactured by Dainippon Ink & Chemicals, Inc.)
-Phenol novolac resin: HP-850: 53.3 g (trade name, manufactured by Hitachi Chemical Co., Ltd.)
・ Dicyandiamide: 0.13 g (trade name, manufactured by Kanto Chemical Co., Inc.)
Curing accelerator: 2PZ-CN: 0.5 g (trade name, manufactured by Shikoku Kasei Kogyo Co., Ltd.)
Silica: SO-G1: 188.2 g (trade name, manufactured by Admatechs Co., Ltd., average particle size: 0.2 to 0.4 μm)
・ Solvent: Methyl ethyl ketone: 400g

（２）熱膨張率測定基板の作製
（１）で作製したガラス織布含浸用樹脂ワニスを厚みが０．２ｍｍのガラス織布（坪量２１０ｇ／ｍ^２）に含浸し、１６０℃で３分間加熱して半硬化（Ｂステージ状態）のプリプレグを得た。このプリプレグを４枚重ね、その両側に１８μｍの商品名Ｆ２−ＷＳ銅箔（Ｒｚ：２．０μｍ、Ｒａ：０．３μｍ）を重ね、１７５℃、９０分、２．５ＭＰａのプレス条件で両面銅張積層板を作製した。この銅張り積層板を過硫酸アンモニウム１５０ｇ／ｌの水溶液に４０℃−２０分間浸漬して銅箔をエッチング除去し、熱膨張率・弾性率測定用基板を得た。 (2) Production of thermal expansion coefficient measurement substrate The glass woven fabric impregnating resin varnish produced in (1) was impregnated into a glass woven fabric having a thickness of 0.2 mm (basis weight 210 g / m ² ), and at 160 ° C. for 3 minutes. A semi-cured (B stage state) prepreg was obtained by heating. Four prepregs are stacked, and 18 μm product name F2-WS copper foil (Rz: 2.0 μm, Ra: 0.3 μm) is stacked on both sides of the prepreg, and copper is coated on both sides under a pressing condition of 175 ° C., 90 minutes, 2.5 MPa. A tension laminate was produced. This copper-clad laminate was immersed in an aqueous solution of 150 g / l ammonium persulfate at 40 ° C. for 20 minutes to remove the copper foil by etching to obtain a substrate for measuring thermal expansion coefficient / elastic modulus.

比較例６
シリカＳＯ−Ｇ１配合量を２８２．３ｇにした以外は比較例５と同様にして熱膨張率・弾性率測定用基板を得た。 Comparative Example 6
A thermal expansion coefficient / elastic modulus measurement substrate was obtained in the same manner as in Comparative Example 5 except that the amount of silica SO-G1 was changed to 282.3 g.

比較例７
シリカＳＯ−Ｇ１配合量を４２２．０ｇにした以外は比較例５と同様にしてサンプル作製を行ったが、プレス成形性が悪く、サンプルが作製できなかった。 Comparative Example 7
A sample was prepared in the same manner as in Comparative Example 5 except that the amount of silica SO-G1 was changed to 422.0 g, but the press moldability was poor and the sample could not be prepared.

比較例８
エポキシ樹脂として２官能ナフタレン型エポキシ樹脂：ＨＰ−４０３２Ｄ（商品名、大日本インキ化学工業株式会社製）を１００ｇ、硬化剤としてビスフェノールＡ（関東化学株式会社製）を８３．８ｇにし、ジシアンジアミドを添加しない以外は、比較例１と同様にしてサンプル作製を行ったが、Ｔｇ以上では測定装置の荷重でサンプルが伸びてしまい、Ｔｇ以上での貯蔵弾性率を測定できなかった。 Comparative Example 8
100 g of bifunctional naphthalene type epoxy resin: HP-4032D (trade name, manufactured by Dainippon Ink & Chemicals, Inc.) as an epoxy resin, 83.8 g of bisphenol A (manufactured by Kanto Chemical Co., Ltd.) as a curing agent, and dicyandiamide added A sample was prepared in the same manner as in Comparative Example 1 except that the sample was stretched by the load of the measuring device above Tg, and the storage elastic modulus above Tg could not be measured.

比較例９
硬化剤としてトリフェノールメタン：ＭＥＨ−７５００（商品名、明和化成株式会社製）を５８．６ｇにした以外は、比較例２と同様にして、熱膨張率・弾性率測定用樹脂板を得た。 Comparative Example 9
A thermal expansion coefficient / elastic modulus measurement resin plate was obtained in the same manner as in Comparative Example 2 except that 58.6 g of triphenolmethane: MEH-7500 (trade name, manufactured by Meiwa Kasei Co., Ltd.) was used as the curing agent. .

比較例１０
エポキシ樹脂としてジヒドロアントラセン型エポキシ樹脂：ＹＸ−８８００（商品名、ジャパンエポキシレジン株式会社製）を１００ｇ、硬化剤としてビスフェノールＡ（関東化学株式会社製）を６３．０ｇにした以外は、比較例１と同様にしてサンプル作製を行ったが、Ｔｇ以上では測定装置の荷重でサンプルが伸びてしまい、Ｔｇ以上での貯蔵弾性率を測定できなかった。 Comparative Example 10
Comparative Example 1 except that 100 g of dihydroanthracene type epoxy resin: YX-8800 (trade name, manufactured by Japan Epoxy Resin Co., Ltd.) was used as the epoxy resin and 63.0 g of bisphenol A (manufactured by Kanto Chemical Co., Ltd.) was used as the curing agent. Samples were prepared in the same manner as described above, but the sample was stretched by the load of the measuring device above Tg, and the storage elastic modulus above Tg could not be measured.

比較例１１
エポキシ樹脂としてナフタレンノボラック型エポキシ樹脂：ＮＣ−７０００Ｌ（商品名、日本化薬株式会社製）を１００ｇ、硬化剤としてフェノールノボラック樹脂：ＨＰ−８５０（商品名、日立化成工業株式会社製）を４５．５ｇにした以外は、比較例１と同様にして熱膨張率・弾性率測定用樹脂板を得た。 Comparative Example 11
100 g of naphthalene novolac type epoxy resin: NC-7000L (trade name, manufactured by Nippon Kayaku Co., Ltd.) as the epoxy resin, and 45 g of phenol novolac resin: HP-850 (trade name, manufactured by Hitachi Chemical Co., Ltd.) as the curing agent. A resin plate for measuring the coefficient of thermal expansion / elastic modulus was obtained in the same manner as in Comparative Example 1 except that the amount was 5 g.

[熱膨張率の測定]
実施例１〜４、６〜１１、比較例１〜４、８〜１１の銅箔を取り除いた熱膨張率・弾性率測定用樹脂板から４×２０ｍｍの試験片を切り出して、ＴＡインスツルメンツ株式会社製ＴＭＡ試験装置（ＴＭＡ−２９４０）を用いて、昇温１０℃／min、引張り法でＴｇ未満の熱膨張率を測定した。実施例５、１２、比較例５〜７の銅箔を取り除いた熱膨張率・弾性率測定用基板から５ｍｍ角の試験片を切り出して、ＴＡインスツルメンツ株式会社製ＴＭＡ試験装置（ＴＭＡ−２９４０）を用いて、昇温１０℃／min、圧縮法でＴｇ未満の熱膨張率を測定した。 [Measurement of thermal expansion coefficient]
TA Instruments Co., Ltd. cut out the test piece of 4 * 20 mm from the resin plate for thermal expansion coefficient and elastic modulus measurement from which the copper foils of Examples 1 to 4, 6 to 11 and Comparative Examples 1 to 4 and 8 to 11 were removed. A thermal expansion coefficient of less than Tg was measured by a tensile method using a TMA test apparatus (TMA-2940) manufactured by TMA. A 5 mm square test piece was cut out from the thermal expansion coefficient / elastic modulus measurement substrate from which the copper foils of Examples 5 and 12 and Comparative Examples 5 to 7 were removed, and a TMA test apparatus (TMA-2940) manufactured by TA Instruments Co., Ltd. was used. A thermal expansion coefficient of less than Tg was measured by a compression method using a temperature increase of 10 ° C./min.

[貯蔵弾性率の測定]
銅箔を除去した熱膨張率・弾性率測定用樹脂板、熱膨張率・弾性率測定用基板から５×３０ｍｍの試験片を切り出して、動的粘弾性測定装置（株式会社ＵＢＭ製Ｅ−４０００）を用いて昇温；５℃／ｍｉｎ、自動静荷重の条件で貯蔵弾性率を測定した。 [Measurement of storage modulus]
A 5 × 30 mm test piece was cut out from the thermal expansion coefficient / elastic modulus measurement resin plate from which the copper foil was removed, and the thermal expansion coefficient / elastic modulus measurement substrate, and a dynamic viscoelasticity measurement apparatus (E-4000 manufactured by UBM Co., Ltd.). The storage elastic modulus was measured under the conditions of 5 ° C./min and automatic static load.

[ガラスクロス含浸時の取扱い性（粉落ち）]
作製したプリプレグをカッターで切断し、その粉落ち状態を目視で観察した。 [Handability when impregnating glass cloth (powder fall)]
The prepared prepreg was cut with a cutter, and the state of powder falling was visually observed.

実施例で作製した熱膨張率・弾性率測定用の樹脂板（樹脂を含み、無機充填剤、ガラスクロスを含まない）の長さ方向の貯蔵弾性率、Ｔｇ未満の熱膨張率の測定結果を表１、３に示す。
また、実施例で作製した熱膨張率・弾性率測定用の基板（樹脂と、無機充填剤及び/又はガラスクロスとを含む）の面方向の貯蔵弾性率、Ｔｇ未満の熱膨張率測定結果も表１、３に併せて示す。 Measurement results of storage modulus in the length direction of the thermal expansion coefficient / elastic modulus measurement resin plate (including resin, not including inorganic filler and glass cloth) produced in the examples, and thermal expansion coefficient less than Tg Tables 1 and 3 show.
Further, the storage elastic modulus in the surface direction of the substrate for thermal expansion coefficient / elastic modulus measurement (including resin, inorganic filler and / or glass cloth) produced in the examples, and the thermal expansion coefficient measurement result less than Tg Tables 1 and 3 are also shown.

一方、比較例で作製した熱膨張率・弾性率測定用の樹脂板の長さ方向の貯蔵弾性率、Ｔｇ未満の熱膨張率の測定結果を表２、４に示す。
また、比較例で作製した熱膨張率・弾性率測定用の基板の面方向の貯蔵弾性率、Ｔｇ未満の熱膨張率測定結果も表２、４に併せて示す。 On the other hand, Tables 2 and 4 show the measurement results of the storage elastic modulus in the length direction and the thermal expansion coefficient less than Tg of the resin plate for measuring the thermal expansion coefficient and elastic modulus produced in the comparative example.
In addition, Tables 2 and 4 also show the storage elastic modulus in the surface direction of the substrate for measuring the thermal expansion coefficient and elastic modulus produced in the comparative example, and the thermal expansion coefficient measurement results less than Tg.

材料の比重は、実施例１〜３、６〜８、比較例１〜３、８〜１１では１．２とした。実施例４、９〜１１、比較例４は、材料の比重を１．６とした。実施例５、１２、比較例５、６は、材料の比重を２．０とした。比較例７は、材料の比重を２．２とした。架橋点間分子量の修正は、シリカの貯蔵弾性率は８０ＧＰａとして貯蔵弾性率の修正を行い、材料の比重は１．２として架橋点間分子量を算出した。また、ポアソン比は、全て０．５とした。 The specific gravity of the materials was 1.2 in Examples 1 to 3, 6 to 8 and Comparative Examples 1 to 3 and 8 to 11. In Examples 4, 9 to 11, and Comparative Example 4, the specific gravity of the material was 1.6. In Examples 5 and 12, and Comparative Examples 5 and 6, the specific gravity of the material was 2.0. In Comparative Example 7, the specific gravity of the material was 2.2. The molecular weight between crosslink points was calculated by correcting the storage elastic modulus of silica at 80 GPa and the specific gravity of the material at 1.2. All Poisson's ratios were set to 0.5.

樹脂板である実施例１〜３及び６〜８のＴｇ未満の熱膨張率が５５〜６４ｐｐｍ／℃であるのに対し、比較例１〜３及び８〜１１のＴｇ未満の熱膨張率は６８〜８７ｐｐｍ／℃と、最小で４ｐｐｍ／℃最大で３２ｐｐｍ／℃低いＴｇ未満の熱膨張率を示していることがわかる。ここで、比較例８及び１０は、Ｔｇ以上では測定装置の荷重でサンプルが伸びてしまい、Ｔｇ以上での貯蔵弾性率の測定ができなかった。この時、実施例１〜３及び６〜８の架橋点間分子量は請求範囲の３００〜１０００の範囲であるが、比較例１〜３及び９、１１の架橋点間分子量は２５０以下を示し、架橋密度が高く、芳香環の相互作用を充分に発現できず、熱膨張率が下がらなかった。 The thermal expansion coefficient of less than Tg of Examples 1 to 3 and 6 to 8 which are resin plates is 55 to 64 ppm / ° C., whereas the thermal expansion coefficient of less than Tg of Comparative Examples 1 to 3 and 8 to 11 is 68. It can be seen that the coefficient of thermal expansion is less than Tg less than Tg of -87 ppm / ° C, a minimum of 4 ppm / ° C and a maximum of 32 ppm / ° C. Here, in Comparative Examples 8 and 10, the sample was stretched by the load of the measuring device at Tg or higher, and the storage elastic modulus at Tg or higher could not be measured. At this time, the molecular weights between the crosslinking points of Examples 1 to 3 and 6 to 8 are in the range of 300 to 1000 of the claims, but the molecular weights between the crosslinking points of Comparative Examples 1 to 3, 9, and 11 are 250 or less, The crosslink density was high, the interaction of aromatic rings could not be sufficiently expressed, and the coefficient of thermal expansion did not decrease.

また、実施例１に実施例１と同じエポキシ樹脂を用いた反応物を配合し、架橋点間分子量を３８６０にした比較例３のＴｇ未満の熱膨張率は６８ｐｐｍ／℃であった。このことから、芳香環を有する絶縁性樹脂を配合するだけでは芳香環同士の相互作用によって、Ｔｇ未満の熱膨張率を低くさせることは不可能であり、本発明の架橋点間分子量を３００〜１０００の範囲に樹脂組成を設定することが芳香環同士の相互作用による低熱膨張率化に重要であることがわかる。 Moreover, the thermal expansion coefficient less than Tg of the comparative example 3 which mix | blended the reaction material using the same epoxy resin as Example 1 and set the molecular weight between crosslinking points to 3860 was 68 ppm / degreeC. For this reason, it is impossible to reduce the thermal expansion coefficient below Tg by the interaction between aromatic rings only by blending an insulating resin having an aromatic ring. It can be seen that setting the resin composition in the range of 1000 is important for reducing the thermal expansion coefficient due to the interaction between the aromatic rings.

実施例４、９〜１１と比較例４は無機の充填剤としてシリカを配合したものである。実施例４、９〜１１のＴｇ未満の熱膨張率は、３４〜３６ｐｐｍ／℃であるが、比較例４は４０ｐｐｍ／℃であった。このときの修正後の架橋点間分子量は実施例４が４５８、実施例９が３２０、実施例１０が５６４、実施例１１が３６５であるのに対し、比較例４が２３５であった。実施例１〜３の絶縁性樹脂と同様に実施例４、９〜１１は芳香環同士の相互作用により低熱膨張率化が発現していることがわかる。また、絶縁性樹脂の架橋点間分子量を本願特許の範囲にすることで、充填剤を配合した場合でも従来材料に比較して低いＴｇ未満の熱膨張率を示すことがわかった。 In Examples 4, 9 to 11, and Comparative Example 4, silica is blended as an inorganic filler. The thermal expansion coefficient of less than Tg of Examples 4 and 9 to 11 was 34 to 36 ppm / ° C., but Comparative Example 4 was 40 ppm / ° C. The molecular weights between the crosslinking points after correction were 458 in Example 4, 320 in Example 9, 564 in Example 10, and 365 in Example 11, while 235 in Comparative Example 4. As with the insulating resins of Examples 1 to 3, it can be seen that Examples 4 and 9 to 11 exhibit low thermal expansion due to the interaction between aromatic rings. In addition, it was found that by setting the molecular weight between the crosslinking points of the insulating resin within the range of the patent of the present application, even when a filler is blended, the coefficient of thermal expansion is less than Tg, which is lower than that of the conventional material.

実施例５と比較例５は、実施例４と比較例４をガラスクロスに含浸したものである。実施例５のＴｇ未満の熱膨張率は、１３．５ｐｐｍ／℃であるが、比較例５は１５ｐｐｍ／℃であった。このときの貯蔵弾性率の修正を行った架橋点間分子量は実施例５が４５８、比較例５が２３３であった。
また、実施例１２は実施例６にシリカを配合しガラスクロスに含浸したものである。実施例１２のＴｇ未満の熱膨張率は、１２．５ｐｐｍ／℃である。このときの貯蔵弾性率の修正を行った架橋点間分子量は３１４であった。
また、比較例６、７は比較例５にシリカ配合量を増やしたものである。比較例６のＴｇ未満の熱膨張率は、１３．５ｐｐｍ／℃であるもののガラスクロス含浸時の取り扱い性は粉落ちが多く望ましくない。比較例７はプレス成形性に問題があり、サンプルを作製できなかった。このときの貯蔵弾性率の修正を行った架橋点間分子量は比較例６が２１８であった。絶縁性樹脂の架橋点間分子量を３００から１０００の範囲に樹脂組成を設定することが芳香環同士の相互作用を発現して低熱膨張率化する上で重要であることがわかる。 In Example 5 and Comparative Example 5, glass cloth was impregnated with Example 4 and Comparative Example 4. The thermal expansion coefficient of Example 5 below Tg was 13.5 ppm / ° C., but Comparative Example 5 was 15 ppm / ° C. The molecular weight between cross-linking points at which the storage elastic modulus was corrected at this time was 458 in Example 5 and 233 in Comparative Example 5.
Moreover, Example 12 mixes a silica with Example 6, and impregnates the glass cloth. The thermal expansion coefficient less than Tg of Example 12 is 12.5 ppm / ° C. At this time, the molecular weight between cross-linking points where the storage elastic modulus was corrected was 314.
Further, Comparative Examples 6 and 7 are obtained by increasing the amount of silica added to Comparative Example 5. Although the thermal expansion coefficient less than Tg of Comparative Example 6 is 13.5 ppm / ° C., the handleability at the time of impregnation with glass cloth is not desirable because it causes powder falling off. Comparative Example 7 had a problem in press formability, and a sample could not be produced. In Comparative Example 6, the molecular weight between cross-linking points where the storage elastic modulus was corrected was 218 in Comparative Example 6. It can be seen that setting the resin composition so that the molecular weight between cross-linking points of the insulating resin is in the range of 300 to 1000 is important in terms of reducing the coefficient of thermal expansion by expressing the interaction between aromatic rings.

従来の充填剤を増やす方法の低熱膨張率化では、プレス成形不良を起こすＴｇ未満の熱膨張率でも実施例１２では達成しており、本願特許の有効性を示すものである。 In the conventional method of increasing the filler, a low thermal expansion coefficient is achieved in Example 12 even with a thermal expansion coefficient of less than Tg that causes press molding failure, which shows the effectiveness of the present patent.

以下の表中、配合の単位はグラムである。 In the following table, the unit of blending is gram.

本発明の例等で用いた樹脂の構造を以下に示す。

The structure of the resin used in the examples of the present invention is shown below.

本発明によれば、架橋点間分子量が３００〜１０００の範囲に入るように芳香環を有する絶縁性樹脂の樹脂組成を制御することで低熱膨張率の樹脂組成物を得ることができる。 According to the present invention, a resin composition having a low coefficient of thermal expansion can be obtained by controlling the resin composition of an insulating resin having an aromatic ring so that the molecular weight between crosslinking points is in the range of 300 to 1,000.

低コストで架橋密度を上げることなく、低熱膨張な樹脂組成物、プリプレグ、積層板及び配線板を提供することが可能となった。 It has become possible to provide a low thermal expansion resin composition, prepreg, laminate and wiring board without increasing the crosslink density at low cost.

Claims

It is a resin composition used for manufacture of a laminated board, Comprising : A resin composition is following formula (4):

Includes bifunctional naphthalene type epoxy resin and a curing agent shown in,
The curing agent is an aminotriazine novolak resin or a bismaleimide-containing aminotriazine novolak resin;
A resin composition having a molecular weight between crosslinking points of 300 to 800 determined from a shear elastic modulus of Tg or more after curing of the resin composition.