超好的环氧树脂复合材料英文文献

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高性能复合材料用环氧树脂胶黏剂的制备与性能_陈泽明

2.6 PSi/PMMA 改性氧树脂固化物 TEM 谱图分析由图 2.3 中的 DMA 测试可以看出增韧剂与环
氧树脂呈均相结构，通过增韧剂改性氧树脂固化物 TEM 谱图可以进一步确定增韧剂在环氧树脂中的
Keywords: High Properties；Composites；Adhesive
环氧树脂胶黏剂具有力学性能高、附着力强等优点，主要用于金属材料的粘接，但其对非金属材料粘接效果较差，如聚乙烯材料（PE）、片状模塑料（SMC）以及复合材料等【1- 。 2】近年来国内外对非金属材料用环氧树脂胶黏剂，尤其是先进树脂基复合材料用环氧胶黏剂的开展了大量的研究工作【3- 。 7】本文采用有机硅液体橡胶增韧环氧树脂胶黏剂，用于非金属材料和复合材料的粘接，获得了较高的力学性能，而且成本低。
2 结果与讨论
2.1 增韧剂含量对改性环氧树脂的粘度分析粘度是环氧树脂工艺性能的重要技术指标，本
文对改性环氧树脂进行了旋转粘度的测试分析，得到树脂粘度随加入增韧剂量的变化规律，如图 2-1 所示：
形成氢键同样较少，因此粘接强度下降。因此，增韧剂的含量为 5phr 最佳。 2.3 增韧剂含量对环氧树脂固化温度的影响
1 实验材料及方法
1.1 原材料环氧树脂 E51：岳阳树脂厂，工业级；200#聚酰
胺：天津延安化工厂，工业级；苄基-2-甲胺：嘉兴市精博化学品有限公司。工业级；有机硅液体橡胶：自制。 1.2 改性环氧树脂的制备
在室温条件下，将 200gE51 型环氧树脂与一定量的有机硅液体橡胶在反应器中混合均匀，加入 1.0g 苄基-2-甲胺作为催化剂，缓慢加热至 150℃，反应 1h，即制得有机硅液体橡胶含量的改性环氧树脂。 1.3 实验方法

复合材料聚合物基体第二章环氧树脂

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2.1引言>>2.1.2环氧树脂生产情况及应用
3）环氧树脂在各行业的分配风电、涂料行业和电子行业复合材料成型用环氧（主要应用于电子行业的印刷电路板）占四分之一。
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2.1引言>>2.1.2环氧树脂生产情况及应用
(1) 汽车工业：是我国四大支柱产业之一，且汽车需求量越来越大，电泳漆、另外维修用漆亦需环氧。 (2)船舶、海洋工业：我国是海洋大国，造船大国， 21世纪是海洋的世纪。船舶、码头设施、海上建筑、钻井平台、输油管道、海水养殖设施等等，需要大量的环氧涂料（防腐、防海洋生物污染）。
5
2.1 引言
1947年美国的DeVoe－Raynolds公司进行了第一次具有工业生产价值的环氧树脂的制造。不久，瑞士的CIBA公司，美国的Shell公司等都开始了环氧树脂的工业化 20世纪50年代初期，环氧树脂在电气绝缘浇铸、防腐蚀涂料、金属的粘结等应用领域有了突破，于是环氧树脂作为一个行业蓬勃地发展起来了
O H2C CH2CH2Cl + ROH
catalyst
H R O C C CH2Cl H2 OH
29
3）水解反应
高温下与碱液接触，会逐步水解成甘油
O H2C CH2CH2Cl OHH2O ClCH2 H C H2 C
(4)电子工业：为我国四大支柱产业之一，发展迅猛。 (5)集装箱工业：我国集装箱工业发展迅猛，已成为世界主要集装箱生产基地（占世界总量的 10%～15%）。集装箱用涂料，主要是环氧树脂。
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2.1引言>>2.1.2环氧树脂生产情况及应用
环氧树脂砂浆地坪
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2.1引言>>2.1.2环氧树脂生产情况及应用

POSS改性环氧树脂制备及性能研究进展文献综述

POSS改性环氧树脂制备及性能研究进展文献综述近年来，随着科学技术的快速发展，环氧树脂作为一种重要的高性能材料得到了广泛的应用。

而POSS作为环氧树脂的一种新型改性剂，具有独特的结构和卓越的性能，引起了广泛的研究兴趣。

本文将综述近年来在POSS改性环氧树脂制备及性能研究方面的最新进展。

首先，POSS改性环氧树脂的制备方法可以分为两类，即物理混合和化学改性。

物理混合是将POSS和环氧树脂机械混合，通过表面张力和分散力使POSS分散在环氧树脂中。

而化学改性是通过共聚或交联反应将POSS与环氧树脂进行共价结合，形成POSS改性环氧树脂。

其次，POSS改性环氧树脂的性能也受到了广泛关注。

研究表明，POSS的加入可以显著改善环氧树脂的力学性能，如增加抗拉强度、弯曲强度和冲击强度。

同时，POSS还可以提高环氧树脂的玻璃化转变温度和热稳定性，减少热膨胀系数和燃烧性能。

此外，POSS改性环氧树脂还具有良好的阻燃性能、耐化学性能和耐热老化性能等。

最后，POSS改性环氧树脂在应用方面也取得了显著的进展。

例如，POSS改性环氧树脂可以用于制备高性能复合材料，如航空航天材料、高性能涂层和电子封装材料等。

此外，POSS改性环氧树脂还可以用于制备低介电常数、低介质损耗的微波介质材料。

另外，POSS改性环氧树脂还可以用于制备纳米复合涂料、纳米填料和纳米复合材料等。

总结起来，POSS改性环氧树脂在制备及性能研究方面取得了显著的进展。

然而，目前仍存在一些问题需要进一步研究解决。

例如，POSS的加入量、POSS在环氧树脂中的分散性以及POSS改性环氧树脂的界面相容性等问题需要深入研究。

同时，对于POSS改性环氧树脂的结构和性能之间的关系还有待深入探索。

我们相信，随着研究的不断推进，POSS改性环氧树脂将在未来得到更广泛的应用。

环氧树脂胶粘剂英语

环氧树脂胶粘剂英语英文回答：Epoxy adhesives are a type of structural adhesive that is widely used in various industries, including aerospace, automotive, and construction. They are known for their excellent bonding strength, durability, and resistance to chemicals and environmental factors. Epoxy adhesives are typically formulated using two components: a resin and a hardener. The resin is the main adhesive component, while the hardener initiates the curing process. When the two components are mixed together, they react to form a strong, cross-linked polymer network that provides the adhesive bond.Epoxy adhesives offer several advantages over other types of adhesives. They have high shear and peel strength, making them ideal for applications where the bonded jointis subjected to significant stress. Epoxy adhesives also exhibit good impact resistance and fatigue strength,ensuring the longevity of the bond under dynamic loading conditions. Additionally, epoxy adhesives have excellent chemical resistance, making them suitable for use in environments with exposure to solvents, acids, and bases.The bonding process of epoxy adhesives involves several steps. The first step is surface preparation, which includes cleaning and roughening the surfaces to be bonded to ensure proper adhesion. The next step is mixing the resin and hardener components in the correct proportions, typically using a 1:1 or 2:1 ratio. The mixed adhesive is then applied to one of the surfaces to be bonded, and the two surfaces are brought together and held in place until the adhesive cures. The curing time of epoxy adhesives can vary depending on the specific formulation and the temperature at which they are applied.中文回答：环氧树脂胶粘剂是一种广泛应用于航空航天、汽车和建筑等行业的结构胶粘剂。

有机累托石／环氧树脂(OREC／EP)复合材料的制备和性能研究

自制热变形温度仪、ＨＩＡＣ一７ＴＨＩ５０型电镜扫描仪、日本理学Ｄ／ＭＡＸ一Ｃ型ｘ射线衍射仪、ＰＳｌ３ＹＲ型ＤＳＣ测试仪、真空系统、油浴加热系统、紫外老
鹱
素
静
化系统，其他常规仪器。
１３配方，
１实验部分
１１原料．
２１ＯＲＣ对树脂体系力学性能的影响．Ｅ按Ｇ５０１８和Ｇ５１１８标准测试Ｂ２７ — ９１Ｂ２７ — ９１
Ｅ５环氧树脂（氧６８：星辰化］无锡树脂一ｌ环ｌ）：厂；２一乙基一一４甲基咪唑：天津天锋化学品公司；有机累托石：自制；ｌ２（２７氯化十二烷基二甲基苄
ｍ（一ｌ氧树脂）ｍ（一Ｅ５环：２乙基一一甲基眯唑）４＝
１０：．０３５
收稿臼期：０８０ — ５２０ — ４２
作者简介：王娟娟（９一，，西礼泉人，究方向为商分子复合材料及胶黏剂的改性、能陶瓷的制备及其改性。１７）女陕７研功
入及其含量对复合材料ＯＲＥＥＰ体系的力学性能、耐介质性能和耐紫外线性能的影响。研究发现：Ｃ／
ＯＥＲＣ是一种良好的环氧树脂增韧改性剂，ＯＥＲＣ的加入可改善复合材料的综合性能。当ＯＥＲＣ质量分数为３时，冲击强度和弯曲强度提高幅度最大，分别为６２％．８３％，耐海水性能效果最好；在添加％．５和．９

AlN／低粘度环氧树脂复合材料的性能研究

ｔｅＡＩｖｌｍｅｆａｔｏｆ４％．ｈＮｏｕｒｃｉｎｏ６
Ｋｅｒｓ：ｉｕａｉｇｍａｅｉｌｔｅｍａ－ｏｄｃｉｇｃｍｐｓｅｔｅｍａｎｕｔｉｙｒｉｉｉｙｙｗｏｄｓｎｌｔｔｒ；ｈｒｌｎｕｔｎｏｏｉ；ｈｒｌｄｃｉｔ；ｅｓｖｔｎａｃｔｏｃｖｓｔ
填料的形态，用纤维状填料代替颗粒状填料［，如７方］
便导热通道的形成。事实上，绝缘导热填料的添加量和综合性能受
具有高的热导率，不绝缘，时耐化学腐蚀性能但同差；高分子材料绝缘性能和耐化学腐蚀性能好，热但导率很低；因此这２种材料都无法满足特殊领域对
维普资讯
国外建材科技
２００８年
第２９卷
第３期
Ａｌｆ度环氧树脂复合材料的性能研究Ｎ／氐粘
徐信，学单刚王钧任鲁林，云，
（汉理工大学材料科学与工程学院，汉４０７）武武３００
ＸＵｎｘｉＬＵｅｌｎ，ＳＲｅ — ｎ，Ｘｕ－ｉＨＡＮｎｇｎ，ＷＡＮＧＪｎＹｕ — ａｇｕ
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木质素环氧树脂复合材料

Thermochimica Acta431(2005)76–80Glass transition and thermal decomposition ofepoxy resins from the carboxylic acid systemconsisting of ester-carboxylic acid derivatives ofalcoholysis lignin and ethylene glycol with variousdicarboxylic acidsShigeo Hirose a,∗,Tatsuko Hatakeyama b,Hyoe Hatakeyama ca National Institute of Advanced Industrial Science and Technology,Central5,Tsukuba,Ibaraki305-8565,Japanb Otsuma Women’s University,12Sanbancho,Chiyoda-ku,Tokyo102-8537,Japanc Fukui University of Technology,3-6-1Gakuen,Fukui910-8501,JapanReceived14October2004;received in revised form10December2004;accepted21January2005Available online23May2005AbstractAlcoholysis lignin(AL)was dissolved in ethylene glycol and the obtained mixture was reacted with succinic anhydride to form a mixture of ester-carboxylic acid derivatives of AL and ethylene glycol(AL-poly(ester-carboxylic acid),ALEGPA).The obtained ALEGPA was mixed with dicarboxylic acids with different alkylene chain length such as succinic acid(alkylene chain,C2),adipic(C4)acid and sebacic acid(C8). The obtained mixture of ALEGPA and dicarboxylic acid was reacted with ethylene glycol diglycidyl ether in the presence of a catalytic amount of dimethylbenzylamine to form ester-epoxy resins.The curing reaction was carried out at130◦C for5h.The molar ratio of epoxy groups to carboxylic acid groups([EPOXY]/[AA]ratios,mol/mol)was1.0.The ALEGPA content in the above mixture was varied from0to100%. Thermal properties of epoxy resins were studied by differential scanning calorimetry(DSC)and thermogravimetry(TG).Glass transition temperatures(T g’s)increased with increasing ALEGPA contents,suggesting that lignin acts as a hard segment in epoxy resin networks.The values of T g’s of epoxy resins with dicarboxylic acids increased in the following order;epoxy resins with succinic acid(alkylene chain,C2), adipic acid(C4)and sebacic acid(C8).Thermal degradation temperatures(T d’s)of epoxy resins slightly decreased with increasing ALEGPA contents.The values of mass residue at500◦C(MR500)increased with increasing AL contents in epoxy resins and also with decreasing chain lengths of dicarboxylic acids.©2005Elsevier B.V.All rights reserved.Keywords:Glass transition;Thermal decomposition;Epoxy resins;Alcoholysis lignin;Aliphatic dicarboxylic acids1.IntroductionLignin is recognized as one of the most important renew-able resources,since the amount of production is very large [1].Lignin has a highly branched chemical structure con-sisting of phenyl propane units which are connected mainly by ether linkage.It is known that lignin shows insufﬁcient ∗Corresponding author.Tel.:+81298616250;fax:+81298616250.E-mail address:s-hirose@aist.go.jp(S.Hirose).mechanical properties in solid state as a polymeric material [2].Many attempts in chemical and physical modiﬁcations of lignin have been made in order to solve the above problems in its utilization as a polymeric material.In the last10years, we have extensively studied synthetic polymers from lignin [3,4].In the above studies,synthetic polymers were derived from lignin on the basis of molecular design concerning the basic structures such as phenyl propane units,and also the functional groups in lignin molecules such as hydroxyl and methoxyl groups.Recently,it was found that polyurethanes0040-6031/$–see front matter©2005Elsevier B.V.All rights reserved. doi:10.1016/j.tca.2005.01.043S.Hirose et al./Thermochimica Acta431(2005)76–8077derived from lignin and also from lignin-based caprolactones show excellent thermal and mechanical properties and also biodegradability[5–9].Epoxy resins are recognized as one of the important ther-moset polymers,since they are used in various materials such as adhesives,matrix of composites and elastomers. In the past,many researchers studied ether type of lignin-based epoxy resins prepared from lignin[10–12].Recently, aliphatic polyesters,such as polycaprolactones,poly ethy-lene succinate,polylactic acid,have received considerable attention due to the fact that they are biodegradable.In our previous study,we investigated synthesis and thermal prop-erties of the ester type of epoxy resins,which can be derived from lignin,polyethylene glycol diglycidyl ether and azelaic anhydride[13].We also studied epoxy resins which can be prepared from an ester-carboxylic acid derivative of lignin synthesized from alcoholysis lignin(AL)and succinic acid anhydride.The obtained ester-carboxylic acid derivative of AL(ALEGPA)was reacted with ethylene glycol diglycidyl ether(EGDGE)to form epoxy resins under various condi-tions.The behavior in curing reactions was studied by differ-ential scanning calorimetry(DSC).Furthermore,the thermal properties of the obtained epoxy resins were studied by DSC and thermogravimetry(TG)[14].In the present study,epoxy resins were prepared from a carboxylic acid system consist-ing of ALEGPA with aliphatic dicarboxylic acids with dif-ferent alkylene chain lengths such as succinic acid(alkylene chain,C2),adipic acid(C4)and sebacic acid(C8).The ther-mal properties such as glass transition and thermal decompo-sition of the obtained epoxy resins were studied by DSC and TG.The inﬂuence of the difference in chemical structure of epoxy resins on thermal properties is investigated.2.Experimental2.1.MaterialsAlcoholysis lignin(AL)was kindly supplied by Repap Co.,USA,and was dried in vacuum at70◦C.Other reagents such as ethylene glycol(EG),ethylene glycol diglycidyl ether(EGDGE),dimethylbenzylamine(DMBA),succinic acid,adipic acid and sebacic acid were commercially ob-tained from Wako Pure Chemical Industries Ltd.,Japan.The above reagents were used without further puriﬁcation.2.2.Preparation of epoxy resinsAL polyacid(ALEGPA)was prepared from AL,EG and succinic anhydride,according to the method previously re-ported[14].ALEGPA and a dicarboxylic acid(DCA)was mixed well with EGDGE at80◦C,and the mixture was al-lowed to stand at130◦C for5h in an oven.Each of succinic acid,adipic acid and sebacic acid was used as an aliphatic di-carboxylic acid(DCA).The molar ratios of carboxylic acid groups to epoxy groups[EPOXY]/[ACID]ratio(mol mol−1)was maintained at1.0.ALEGPA contents were varied at0, 20,40,60,80and100%.The[EPOXY]/[ACID]ratios and the ALEGPA contents were calculated by the following equa-tions:[EPOXY]/[ACID]ratio(mol/mol)=(M EGDGE W EGDGE)/ (M ALEGPA W ALEGPA+M DCA W DCA),ALEGPA content(%) =[W ALEGPA/(W ALEGPA+W DCA)]×100where M EGDGE is the mole number of epoxy groups per gram of EGDGE(7.7mmol g−1),W EGDGE the weight of EGDGE, M ALEGPA the mole number of carboxylic acid groups per gram of ALEGPA(6.62mmol g−1),W ALEGPA the weight of ALEGPA,M DCA the mole number of carboxylic acid groups per gram of DCA,W DCA the weight of DCA.2.3.MeasurementsA Perkin-Elmer Spectrum One Fourier transform infrared spectrometer equipped with a universal ATR unit was used for infrared spectrometry.A Seiko DSC220was used for dif-ferential scanning calorimetry(DSC).The measurements of glass transition of epoxy resins were carried out ranging from −60to80◦C at a heating rate of10◦C min−1using ca.5mg of samples.The samples were heated to130◦C and main-tained for10min,and then they were quenched to−60◦C in DSC aluminum vessels before measurements.The glass transition temperatures(T g’s)were determined according to a method reported by Nakamura et al.[15].A Seiko TG/DTA 220was used for thermogravimetry(TG).The measurements were carried out using ca.5mg of samples at a heating rate of10◦C min−1in nitrogenﬂow of300mL min−1.Thermal decomposition temperatures(T d’s)were determined accord-ing to a method reported by Hatakeyama and coworkers [16].3.Results and discussionIn the present study,epoxy resins were obtained by the reaction of a mixture ALEGPA/DCA with EGDGE. The reaction scheme is shown in Scheme1.The chemical structure of the obtained ALEGPA is conﬁrmed by FT-IR. FT-IR spectrum of ALEGPA is shown in Fig.1.The characteristic absorption peaks of carboxylic acid groups at1780,around2700and3200cm−1,and also of ester groups at1720,1200cm−1are observed in the spectrum. The FT-IR spectrum of an epoxy resin with succinic acid with ALEGPA content60%after curing at130◦C for5h is also shown in Fig.1.The characteristic absorption peaks for ester groups1720and1200cm−1and also hydroxyl groups at3300cm−1are observed.Glass transition of epoxy resins was studied by DSC.Fig.2 shows DSC curves of epoxy resins with various ALEGPA contents.A heat capacity gap in baseline due to glass transi-78S.Hirose et al./Thermochimica Acta 431(2005)76–80Scheme 1.Reaction scheme for the preparation of epoxyresins.Fig.1.FT-IR spectra of ALEGPA,EGDGE and an epoxy resin with succinicacid.Fig.2.DSC curves of epoxy resins with various ALEGPA contents in a ALEGPA/succinic acid system.Numbers indicate ALEGPA contents.tion is observed in each DSC curve.T g ’s change according to the change in ALEGPA contents of epoxy resins in the ALEGPA/succinic acid system.Fig.3shows the relationship between T g and ALEGPA content of epoxy resins with dicar-boxylic acids (DCA)with various alkylene chain lengths.T g increases with increasing ALEGPA content of epoxy resin.The above results indicate that lignin acts as a hard segment in epoxy resin molecules.It is known that lignin is a highly branched polymer consisting of phenylpropane units mainly connected by ether linkage.It has also a number of hydroxyl groups in a molecule [1].Therefore,it is considered that lignin exists as cross-linking points.The chain lengths of epoxy resins between cross-linking points decrease with in-creasing ALEGPA content in epoxy resins.The increase in the chain lengths between cross-linking points enhances the main chain molecular motion.The T g values are high intheFig.3.Relationship between T g and ALEGPA content of epoxy resins with DCA with various alkylene chain lengths.C 2(᭹),C 4( )and C 8( ).S.Hirose et al./Thermochimica Acta 431(2005)76–8079Fig.4.TG and differential TG (DTG)curves of the starting materials such as ALPA,EGDGE and AL.order of epoxy resins with succinic acid (C 2),adipic acid (C 4)and sebacic acid (C 8).The above results are reasonable when we consider that the ﬂexibility of main chains in epoxy resin molecules increases with increasing chain lengths of dicarboxylic acids.Thermal decomposition behavior of starting materials and epoxy resins was studied by TG.Fig.4shows TG and dif-ferential TG (DTG)curves of the starting materials such as ALEGPA,EGDGE and AL.TG and DTG curves of DCA are not shown in Fig.4,since only the evaporation of the above compounds was observed in TG measurements.It is observed that thermal decomposition apparently proceeds in two steps.T d ’s at lower temperature regions (T d1)and also T d ’s at higher temperature regions (T d2)were determined.T d1’s of the start-ing materials are 189.6and 133.3◦C while T d2’s 335.3and 233.2◦C,respectively.It is known that epoxy groups are rel-atively unstable [17].Accordingly,it is considered that the above group starts to decompose at T d1region.Fig.5shows TG and differential TG (DTG)curves of epoxy resins with various ALEGPA contents in the ALEGPA/DCA systems with succinic acid,adipic acid and sebacic acid.It is observed that the decomposition apparently proceeds in a smooth step.The thermal degradation at T d1re-gion,that is observed in TG curves of the startingmaterialsFig.5.TG and differential TG (DTG)curves of epoxyresins.Fig.6.Relationship between T d ALEGPA content of epoxy resins.C 2(᭹),C 4( )and C 8( ).(Fig.4),is not observed.This indicates that thermally un-stable carboxylic acid and epoxy groups were converted into thermally stable ester groups.Thermal decomposition tem-peratures (T d ’s)and mass residue at 500◦C (MR 500)were determined from TG curves.Fig.6shows the relationship be-tween T d and ALEGPA content of epoxy resins.T d slightly decreases with increasing ALEGPA content.However,the degree of the decrease in T d values is very small.It is known that lignin is relatively thermally unstable [6].As shown in Fig.4,T d of AL was determined as 284.3◦C.The T d values of epoxy resins from AL are much higher than that of AL.There-fore,it can be considered that lignin becomes thermally stable after introduction into the epoxy resin molecules.As shown in Fig.6,T d values are almost the same regardless of the dif-ference in alkylene chain lengths of DCA.In order to clarify the inﬂuence of lignin in epoxy resins on MR 500values,AL contents in epoxy resins were calculated.The relationship be-tween AL contents and MR 500is shown in Fig.7.As clearly seen in Fig.7,MR 500values increase with increasing AL con-tents in epoxy resins.It is known that lignin molecules react with each other to form a condensed char-like material,when they are heated in nitrogen.Therefore,it is considered that the materials in the residue at 500◦C are mainly formed by the reaction with lignin in epoxy resins during the decompo-sition process.The above consideration can be supported by the fact that the MR 500value of ALEGPA is higher than that of SA,as shown in Fig.4.As shown in Fig.7,MR 500vales are always high in the order of epoxy resins with succinic acid (C 2),adipic acid (C 4)and sebacinic acid (C 8),suggesting that dicarboxylic acids with longer alkylene chains give smaller amounts of residual materials after thermal decomposition up to 500◦C.However,the above difference in MR 500values be-comes smaller when AL contents are increased.Accordingly,it can be said that the AL contents in epoxy resins strongly affect MR 500values in the higher AL contents region.80S.Hirose et al./Thermochimica Acta431(2005)76–80Fig.7.Relationship between MR500’s and AL contents in epoxy resins.C2 (᭹),C4( )and C8( ).4.ConclusionEpoxy resins were obtained by the reaction of the ester-carboxylic acid derivatives of alcoholysis lignin (ALEGPA)/aliphatic dicarboxylic acids(DCA)system with EGDGE.T g increased with increasing ALEGPA contents in epoxy resins,suggesting that lignin acts as a hard segment in epoxy resins.It was found that T g’s of epoxy resins decreased with increasing alkylene chain lengths of dicarboxylic acids from C2to C8.T d slightly decreased with increasing ALEGPA content in epoxy resin.The difference in alkylene chain length of DCA does not affect T d values of epoxy resins,while it affects MR500values.It was also found that AL contents in epoxy resins strongly affect MR500values particularly in the higher AL contents region.References[1]K.Kringstad,in:L.E.St.Pierre,et al.(Eds.),Future Sources ofOrganic Raw Mterials—CHEMRAWN I,Pergamon Press,1980,p.627.[2]G.Dai,in:K.V.Sarkanene, C.H.Ludwig(Eds.),Lignins,Wi-ley/Interscience,New York,1971,p.697.[3]H.Hatakeyama,J.Therm.Anal.Calorimetry70(2002)755–795.[4]T.Hatakeyama,H.Hatakeyama,Thermal Properties of GreenPolymers and Biocomposites,Kluwer Academic Publishers, 2004.[5]K.Nakamura,T.Hatakeyama,H.Hatakeyama,Polym.Adv.Technol.2(1992)41–47.[6]S.Hirose,K.Kobashigawa,Y.Izuta,H.Hatakeyama,Polym.Int.47(1998)247–256.[7]H.Hatakeyama,Y.Izuta,S.Hirose,T.Yoshida,T.Hatakeyama,in:J.F.Kennedy,P.A.Williams,G.O.Phillips,H.Hatakeyama(Eds.), Recent Advances in Environmentally Compatible Polymers,Wood-head Publisher Ltd.,Chichester,2001,pp.33–46.[8]T.Hatakeyama,Y.Izuta,S.Hirose,H.Hatakeyama,Polymer43(2002)1177.[9]S.Hirose,T.Hatakeyama,Y.Izuta,H.Hatakeyama,J.Therm.Anal.Calorimetry70(2002)853–860.[10]D.Feldman, D.Banu,J.Polym.Sci.,Polym.Chem.26(1988)973–983.[11]H.Ito,N.Shiraishi,Mokuzai Gakkaishi33(1987)393–399.[12]K.Hofmann,W.G.Glasser,Macromol.Chem.Phys.195(1994)65–80.[13]S.Hirose,M.Kobayashi,H.Kimura,H.Hatakeyama,in:J.F.Kennedy,P.A.Williams,G.O.Phillips,H.Hatakeyama(Eds.),Re-cent Advances in Environmentally Compatible Polymers,Woodhead Publisher Ltd.,Chichester,2001,pp.73–78.[14]S.Hirose,T.Hatakeyama,H.Hatakeyama,Macromol.Symp.197(2003)157–169.[15]S.Nakamura,M.Todoki,K.Nakamura,H.Kanetsuna,Thermochim.Acta136(1988)163–178.[16]T.Hatakeyama, F.X.Quin,Thermal Analysis,Wiley,Chichester,1994,pp.38–64.[17]J.D.Roberts,M.C.Caserio,Basic Principles of Organic Chemistry,2nd ed.,Wiley,New York,1980,pp.661–665.。

耐高温拉挤环氧树脂及其复合材料性能研究

耐高温拉挤环氧树脂及其复合材料性能研究王成忠 1 陈伟明1梁平辉2杨小平1(1北京化工大学碳纤维及复合材料研究所，北京 1000292 常熟佳发化学有限责任公司，常熟 215533)摘要：研究了------型耐高温环氧树脂的固化动力学，分析了该树脂体系的浇注体性能，制备了碳纤维拉挤复合材料，并通过热机械分析（DMTA）考察了树脂浇注体及其复合材料的动态热机械性能。

结果表明，树脂体系的凝胶化温度与固化温度相差较小，固化反应放热集中，适合于快速拉挤成型，其复合材料具有优良的耐高温性能，Tg达到210℃以上。

关键词：耐高温拉挤成型环氧树脂复合材料keywords: heat-resistance pultrusion epoxy resin composites前言拉挤成型是制造高性能、低成本连续复合材料的一种重要方法，拉挤成型工艺要求基体树脂应具有反应速度快、粘度低、适用期长等特点，常用的快速拉挤用树脂主要是自由基固化型的不饱和聚酯树脂和乙烯基酯树脂[1,2]。

此类树脂的拉挤工艺性能优良，但存在耐热性能较低的缺点，虽然部分树脂品种具有较好的耐热性，但其固化物的Tg一般不高于180℃[3]，而且对于高性能碳纤维拉挤复合材料往往存在界面性能较差的问题[4]。

采用环氧树脂制备的碳纤维复合材料具有优良的力学性能，但对通用型环氧树脂来说，以胺类固化剂的树脂体系粘度较大，添加稀释剂后力学性能和热性能会大幅度下降；以液体酸酐为固化剂的树脂体系往往需要高温长时间固化，所以环氧树脂较少用于拉挤成型。

高性能拉挤复合材料的发展，急需可适用于拉挤成型工艺的高性能环氧树脂，要求树脂具有反应速度快、耐热性能高、强度高等特点。

通过对通用型环氧树脂进行改性虽可以获得较高的耐热性能[5]，但难以适用于规模化生产。

本文研究了一种改性多元芳香族缩水甘油胺型环氧树脂的固化特性，并与液体酸酐配合进行了拉挤成型工艺研究，认为该树脂体系具有优良的拉挤工艺性能，其碳纤维拉挤复合材料的耐热性达到210℃以上，该树脂克服了常规耐高温环氧树脂粘度高、使用工艺性差的缺点，具有良好的加工工艺性，是一种新型的耐高温拉挤树脂。

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/Journal of Reinforced Plastics and Composites/content/30/19/1621The online version of this article can be found at:DOI: 10.1177/07316844114268102011 30: 1621 originally published online 7 November 2011Journal of Reinforced Plastics and Composites N. Venkateshwaran, A. ElayaPerumal and M. S. JagatheeshwaranEffect of fiber length and fiber content on mechanical properties of banana fiber/epoxy compositePublished by: can be found at:Journal of Reinforced Plastics and Composites Additional services and information for/cgi/alerts Email Alerts:/subscriptions Subscriptions: /journalsReprints.nav Reprints:/journalsPermissions.nav Permissions:/content/30/19/1621.refs.html Citations:What is This?- Nov 7, 2011OnlineFirst Version of Record- Dec 16, 2011Version of Record >>ArticleEffect of fiber length and fiber contenton mechanical properties of banana fiber/epoxy compositeN.Venkateshwaran,A.ElayaPerumal and M.S.JagatheeshwaranAbstractThe main factors that influence the properties of composite are fiber length and content.Hence the prediction of optimum fiber length and content becomes important,so that composite can be prepared with best mechanical prop-erties.Experiments are carried out as per ASTM standards to find the mechanical properties namely,tensile strength and modulus,flexural strength and modulus,and impact strength.In addition to mechanical properties,water absorption capacity of the composite is also studied.Further,fractured surface of the specimen are subjected to morphological study using scanning electron microscope.The investigation revealed the suitability of banana fiber as an effective reinforce-ment in epoxy matrix.Keywordspolymer composites,banana fiber,mechanical properties,scanning electron microscopeIntroductionNowadays,polymers are used everywhere in the day-to-day life.Plastics found its way when the need for low weight high strength material became important for various applications.The research in theﬁeld of poly-mer and polymer-based components has gained wide-spread recognition owing to its property;however,its bio-degradability is still a matter of concern.Further, glassﬁber reinforced polymers(GFRP)have become appealing substitutes for aluminum,concrete,and steel due to its high strength-to-weight ratio,ease of handling,and for being corrosion-free.Moreover, they can also be engineered to get the desired proper-ties.1Since large-scale production and fabrication of glassﬁber causes environmental problems and also health hazards,a suitable alternate which is environ-mental friendly is the need of the hour.Naturalﬁbers that are low cost,lightweight and environmental friendly provide an excellent alternative to glassﬁber. Joshi et al.2reviewed the life cycle assessment of natural ﬁber and glassﬁber composite and found that natural ﬁbers are environmentally superior to glassﬁber,and also reduces the polymer content as reinforcement. Schmidt and Beyer,Wotzel et al.,and Corbiere et al.carried out some important works using the natural ﬁbers as reinforcement in polymer matrix for use in automobile parts.Schmit and Beyer3have replaced the glassﬁber polypropylene(PP)with hemp-PP com-posite for auto-insulation application.Wotzel et al.4 have used hemp-epoxy to replace glassﬁber acryloni-trile butadien–styrene(ABS)for usage in auto-side panel.Similarly,Corbiere et al.5replaced glassﬁber PP with Curaua PP for transporting pallet.All these studies revealed that the naturalﬁber based polymer composite has successfully replaced the glassﬁber. Pothan et al.6studied the eﬀect ofﬁber length and con-tent on the mechanical properties of the short banana/ polyester composite.Study shows that30–40mmﬁber length and40%ﬁber loading provides better mechan-ical properties.Idicula et al.7investigated the mechan-ical performance of banana/sisal hybrid composite and Department of Mechanical Engineering,Anna University,Chennai,India.Corresponding author:N.Venkateshwaran,Department of Mechanical Engineering,Anna University,Chennai,IndiaEmail:venkatcad@Journal of Reinforced Plasticsand Composites30(19)1621–1627!The Author(s)2011Reprints and permissions:/journalsPermissions.navDOI:10.1177/0731684411426810the positive hybrid eﬀect for tensile strength was found to be in the ratio of4:1(banana:sisal). Further,the tensile strength of the composite is better when bananaﬁber is used as skin and sisal as core material.Visco-elastic property of the banana/ sisal(1:1ratio)hybrid composite was studied by Idicula et al.8The study shows that sisal/polyester composite has maximum damping behavior and high-est impact strength as compared to banana/polyester and hybrid composite.Sapuan et al.9prepared the composite by reinforcing woven bananaﬁbers with epoxy matrix.Tensile test result showed that the woven kind of reinforcement has better strength and the same was conﬁrmed using Anova technique also. Venkateshwaran and ElayaPerumal10reviewed the various work in theﬁeld of bananaﬁber reinforced with polymer matrix composite with reference to phys-ical properties,structure,and application. Venkateshwaran et al.11studied the eﬀect of hybridi-zation on mechanical and water absorption properties. Investigation revealed that the addition of sisal in bananaﬁber composite upto50%increases the mechanical properties.Sapuan et al.12designed and fabricated the household telephone stand using woven banana fabric and epoxy as resin.Zainudin et al.13studied the thermal stability of banana pseudo-stem(BPS)ﬁlled unplastisized polyvinyl chlo-ride(UPVC)composites using thermo-gravimetric analysis.The study revealed that the incorporation of bananaﬁller decreases the thermal stability of the composite.Zainudin et al.14investigated the eﬀect of bananaﬁller content in the UPVC matrix.The inser-tion ofﬁller increases the modulus of the composite and not the tensile andﬂexural strength.Zainudin et al.15studied the eﬀect of temperature on storage modulus and damping behavior of bananaﬁber rein-forced with UPVC.Uma Devi et al.16studied the mechanical properties of pineapple leafﬁber rein-forced with polyester composite.Study found that optimum mechanical properties are achieved at 30mmﬁber length and30%ﬁber content.Dabade et al.17investigated the eﬀect ofﬁber length and weight ratio on tensile properties of sun hemp and palmyra/polyester composite.The optimumﬁber length and weight ratio were30mm and around 55%,respectively.From the above literatures,it is evident that the ﬁber length and content are the important factors that aﬀect properties of the composite.Hence in this work,the eﬀect ofﬁber length and weight percentage on the mechanical and water absorption properties of the bananaﬁber epoxy composite is investigated. Further,the fractured surface of the composite are subjected to fractography study to evaluate the frac-ture mechanism.ExperimentalFabrication of compositeA molding box made of well-seasoned teak wood of dimensions300Â300Â3mm3is used to make a com-posite specimen.The top,bottom surfaces of the mold and the walls are coated with remover and kept for drying.Fibers of diﬀerent length(5,10,15,and 20mm)and weight percentage(8,12,16,and20)are used along with Epoxy(LY556)and Hardener (HY951)for the preparation of composite.Testing standardsThe tensile strength of the composite was determined using Tinnus Olsen Universal Testing Machine (UTM)as per ASTM D638standard.The test speed was maintained at5mm/min.In this case,ﬁve specimens were tested with variedﬁber length andﬁber weight ratio.The average value of tensile load at breaking point was calculated.Theﬂexural strength was determined using the above-mentioned UTM as per ASTM D790procedure.The test speed was maintained between1.3and1.5mm/min. In this case,ﬁve samples were tested and the average ﬂexural strength was reported.The impact strength of the composite specimen was determined using an Izod impact tester according to ASTM D256 Standards.In this case,ﬁve specimens were tested to obtain the average value.Figures1to5show the eﬀect ofﬁber length and weight content on ten-sile,ﬂexural,and impact properties.Water absorp-tion behavior of banana/epoxy composites in water at room temperature was studied as per ASTM D570to study the kinetics of water absorption. The samples were taken out periodically andFigure1.Effect of fiber length and weight percentage on tensile strength.1622Journal of Reinforced Plastics and Composites30(19)weighed immediately,after wiping out the water from the surface of the sample and using a precise 4-digit balance to ﬁnd out the content of water absorbed.All the samples were dried in an oven until constant weight was reached before immersing again in the water.The percentage of moisture absorption was plotted against time (hours)and are shown in Figures 6–13.Scanning electron microscopeThe fractured surfaces of the specimens were exam-ined directly by scanning electron microscope Hitachi-S3400N.The fractured portions of the sam-ples were cut and gold coated over the surface uni-formly for examination.The accelerating voltage used in this work was 10kV.Figures 14to 17show the fractured surface characteristics of the compositespecimen.Figure 6.Effect of moisture on fiber content;Fiber length –5mm.Figure 3.Effect of fiber length and weight percentage on flexural strength.Figure 2.Effect of fiber length and weight percentage on tensilemodulus.Figure 4.Effect of fiber length and weight percentage on flexuralmodulus.Figure 5.Effect of fiber length and weight percentage on impact strength.Venkateshwaran et al.1623Figure 12.Effect of moisture on fiber length;Fiber wt%–16.Figure 7.Effect of moisture on fiber content;Fiber length –10mm.Figure 11.Effect of moisture on fiber length;Fiber wt%–12.Figure 10.Effect of moisture on fiber length;Fiber wt%–8.Figure 8.Effect of moisture on fiber content;Fiber length –15mm.Figure 9.Effect of moisture on fiber content;Fiber length –20mm.1624Journal of Reinforced Plastics and Composites 30(19)Results and discussion Mechanical propertiesFor the tensile test,composite specimens are made of ﬁbers of diﬀerent length (5,10,15,and 20mm)and weight ratio (8,12,16,and 20)were used to calculate the tensile strength.Figures 1and 2show the eﬀect of ﬁber length and weight ratios on tensile strength and modulus of the composite,respectively.Figure 1shows that the increase in ﬁber length and weight ratio increases the tensile strength and modulus upto 15mm ﬁber length and 12%weight ratio.Further increases cause the properties to decrease because of lower ﬁber–matrix adhesion and the quantity of ﬁber content being more than matrix.From Figures 1and 2,the maximum tensile strength and modulus oftheFigure 14.SEM micrograph of tensile fracturedspecimen.Figure 15.SEM micrograph of fractured specimen under flexuralload.Figure 16.SEM micrograph of fractured specimen under impactload.Figure 17.Micrograph of poorinterface.Figure 13.Effect of moisture on fiber length;Fiber wt%–20.Venkateshwaran et al.1625composite are16.39MPa and0.652GPa,respectively for theﬁber length of5mm and12%weight ratio. Flexural strength and modulus for diﬀerentﬁber lengths(5,10,15,and20mm)and weight ratios(8, 12,16,and20)are shown in Figures3and4,respec-tively.It was found that the maximumﬂexural strength and modulus are57.53MPa and8.92GPa,respectively for theﬁber length of15mm andﬁber weight of16%.The results of the pendulum impact test are shown in Figure 5.As theﬁber weight and length increases impact strength also increases upto16%ﬁber weight ratio and then begin to decrease.The maximum impact strength of 2.25J/m was found for theﬁber length 20mm and16%ﬁber weight.Although the variousﬁber lengths and weight per-centage provides the maximum mechanical properties, from Figures10,12,and14it can be concluded that the optimumﬁber length andﬁber weight percentage is 15mm and16%respectively as the properties variation with15mm and16%are negligible when compared to the maximum mechanical properties provided by diﬀer-entﬁber lengths and weight percentage indicated as above.The mechanical properties provided above are better than coir18and palmyra.19Water absorption studyThe eﬀects ofﬁber length and content on the water absorption study are shown in Figures6–13.Figures 6to9show the eﬀect ofﬁber content on the water absorption property of the banana/epoxy composite. It shows that as theﬁber content increases the moisture uptake of the composite also increases.This is due to the aﬃnity of the bananaﬁber towards the moisture. The maximum moisture absorption for the composite is around5%for all length and weight percentage of composite.Figures10to13show the eﬀect ofﬁber length on the water uptake capability of composite.It indicates that the variation of length(5,10,15,and 20mm)does not have much impact as compared with theﬁber content.The moisture absorption percentage of bananaﬁber/epoxy composite seems to be lesser than hempﬁber20andﬂaxﬁber21composite. Fractography studyMicrographs of fractured tensile,ﬂexural,and impact specimens are shown in Figures14–17.Figure14shows the micrograph of fractured surface of specimen under tensile load.It clearly indicates that the failure is due to ﬁber pull out phenomenon.Figure15shows the frac-tured surface of the specimen under bending load. Micrograph also shows the bending ofﬁbers due to the application of load.Figure16shows the failure of the composite under impact load.Further,it also shows the striation occurring on the matrix surface and the presence of hole due toﬁber pull out.Figure17shows the micrograph of20mmﬁber length and20%ﬁber weight composite specimen.It clearly indicates that the clustering ofﬁbers result in poor interface with matrix,and in turn decreases the mechanical properties of the composite.ConclusionBased on theﬁndings of this investigation the following conclusions can be drawn:.The optimumﬁber length and weight ratio are 15mm and16%,respectively for bananaﬁber/ epoxy composite..Moisture absorption percentage of banana/epoxy composite for all length and weight percentage is around5..Also,the moisture uptake capability of the compos-ite is greatly inﬂuenced byﬁber content than length. .SEM image shows that increasing theﬁber content above16%results in poor interface betweenﬁber and matrix.References1.Houston N and Acosta F.Environmental effect of glassfiber reinforced polymers.In:Proceedings of2007Earth Quake Engineering Symposium for Young Researcher, Seattle,Washington,2007.2.Joshi SV,Drzal LT,Mohanty AK and Arora S.Are nat-ural fiber composites environmentally superior to glass fiber reinforced posite Part A2004;35: 371–376.3.Schmidt WP and Beyer HM.Life cycle study on a naturalfiber reinforced component.In:SAE Technical Paper 982195.SAE Total Life-Cycle Conference,1–3 December,1998,Graz,Austria.4.Wotzel K,Wirth R and Flake R.Life cycle studies onhemp fiber reinforced components and ABS for automo-tive parts.Die Angewandte Makromolekulare Chemie1999;272:121–127.5.Corbiere-Nicollier T,Laban BG and Lundquist.Lifecycleassessment of bio-fibers replacing glass fibers as reinforce-ment in plastics.Resour Conserv Recycl2001;33:267–287.6.Pothan LA,Thomas S and Neelakantan NR.Shortbanana fiber reinforced polyester composites:mechanical, failure and aging characteristics.J Reinf Plast Compos 1997;16:744–765.7.Idicula M,Neelakantan NR and Oommen Z.A study ofthe mechanical properties of randomly oriented short banana and sisal hybrid fibre reinforced polyester compos-ites.J Appl Polym Sci2005;96:1699–1709.1626Journal of Reinforced Plastics and Composites30(19)8.Idicula M,Malhotra SK,Joseph K and Thomas S.Dynamic mechanical analysis of randomly oriented short banana/sisal hybrid fibre reinforced polyester pos Sci Technol2005;65:1077–1085.9.Sapuan SM,Leenie A,Harimi M and Beng YK.Mechanical property analysis of woven banana/epoxy composite.Mater Design2006;27:689–693.10.Venkateshwaran N and ElayaPerumal A.Banana fiberreinforced polymer composite-a review.J Reinf Plast Compos2010;29:2387–2396.11.Venkateshwaran N,ElayaPerumal A,Alavudeen A andThiruchitrambalam M.Mechanical and water absorption behavior of banana/sisal reinforced hybrid composites.Mater Design2011;32:4017–4021.12.Sapuan SM and Maleque MA.Design and fabrication ofnatural woven fabric reinforced epoxy composite for household telephone stand.Mater Design2005;26: 65–71.13.Zainudin ES,Sapuan SM,Abdan K and MohamadMTM.Thermal degradation of banana pseudo-stem fibre reinforced unplastisized polyvinyl chloride compos-ites.Mater Design2009;30:557–562.14.Zainudin ES,Sapuan SM,Abdan K and MohamadMTM.The mechanical performance of banana pseudo-stem reinforced unplastisized polyvinyl chloride compos-ites.Polym Plast Technol Eng2009;48:97–101.15.Zainudin ES,Sapuan SM,Abdan K and MohamadMTM.Dynamic mechanical behaviour of bananapseudo-stem filled unplasticized polyvinyl chloride com-posites.Polym Polym Compos2009;17:55–62.16.Uma Devi L,Bhagawan SS and Sabu Thomas.Mechanical properties of pineapple leaf fiber-reinforced polyester composites.J Appl Polym Sci1997;64: 1739–1748.17.Dabade BM,Ramachandra Reddy G,Rajesham S andUdaya kiran C.Effect of fiber length and fiber weight ratio on tensile properties of sun hemp and palmyra fiber reinforced polyester composites.J Reinf Plast Compos 2006;25:1733–1738.18.Harish S,Peter Michael D,Bensely A,Mohan Lal D andRajadurai A.Mechanical property evaluation of natural fiber coir composite.Mater Characterisation2009;60: 44–49.19.Velmurugan R and Manikandan V.Mechanical proper-ties of palmyra/glass fiber hybrid posite Part-A2009;38:2216–2226.20.Dhakal HN,Zhang ZY and Richardson MOW.Effect ofwater absorption on the mechanical properties of hemp fibre reinforced unsaturated polyester composites.Compos Sci Technol2007;67:1674–1683.21.Alix S,Philippe E,Bessadok A,Lebrun V,Morvan V andMarais S.Effect of chemical treatments on water sorption and mechanical properties of flax fibres.Bioresour Technol2009;100:4742–4749.Venkateshwaran et al.1627。