共查询到18条相似文献,搜索用时 171 毫秒
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大掺量矿渣复合胶凝材料的硬化浆体形貌特征 总被引:1,自引:1,他引:0
通过扫描电镜观察了大掺量矿渣复合胶凝材料在不同水化龄期的硬化浆体形貌,并与水泥硬化浆体形貌进行对比,研究了矿渣在复合胶凝材料中的水化性能与硬化浆体形貌特征的关系.结果显示:大掺量矿渣复合胶凝材料水化早期的浆体结构比水泥浆体结构疏松,28天的浆体结构比水泥浆体结构致密.水化早期,矿渣颗粒被水泥水化产物包裹,与水泥浆体界面薄弱;水化后期,矿渣颗粒的水化产物与水泥水化产物紧密结合,颗粒与水泥浆体的界面牢固. 相似文献
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研究了掺50%矿渣的水泥-矿渣复合胶凝材料3 a龄期的硬化浆体C-S-H凝胶特性,结果显示:3 a龄期时矿渣反应程度为68.3%,大部分小颗粒矿渣已反应,但许多大颗粒矿渣几乎未反应;长龄期时浆体中Ca(OH)2没有消耗殆尽,从SEM图像中可以发现Ca(OH)2大量存在;水泥-矿渣复合胶凝材料体系3 a龄期的C-S-H凝胶的Ca/Si比、(Al+Mg)/Si比均值分别为1.88和0.60,相较于水泥生成的C-S-H凝胶,水泥-矿渣复合胶凝体系的C-S-H凝胶Ca/Si比较低,且含有大量Al。但Ca/Si比明显高于水泥-粉煤灰复合胶凝材料生成的C-S-H凝胶。 相似文献
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养护高温对复合胶凝材料水化性能的影响 总被引:5,自引:1,他引:4
养护温度对胶凝材料的水化速度和硬化浆体结构有重大影响。本文重点对比研究在常温(20℃)以及高温(65℃)下养护的不同组成的胶凝材料水化性能和硬化浆体的显微结构。原材料采用北京兴发水泥有限公司生产的混凝土外加剂性能检测用基准水泥与内蒙古元宝山一级粉煤灰。试验组C为纯水泥净浆试样,F1为粉煤灰掺量为25%的净浆试样,水胶比(w/b)均采用0.4。 相似文献
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为了使超高性能混凝土能够适应现场施工及泵送要求,文章设计配制了6组超高性能混凝土并进行试验研究,分析了水胶比、钢纤维掺量及粉煤灰对超高性能混凝土性能的影响并对泵送提出建议。结果表明,随着水胶比的降低和钢纤维掺量的增加,混凝土和易性减小,强度增加,粉煤灰的掺入可以明显改善和易性,并且可以提高后期强度。在施工中,宜使用高压砼泵及泵管,采用减少泵管线路的长度及转弯等措施。 相似文献
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复合胶凝材料水化过程的ESEM观察 总被引:4,自引:0,他引:4
利用环境扫描电镜(ESEM)和X射线衍射分析(XRD)研究了由硅酸盐水泥、粉煤灰和膨胀剂组成的复合胶凝材料的水化产物形貌和硬化浆体结构。复合胶凝材料水化初期有过渡产物钾石膏片状晶体生成,CSH凝胶为约1μm长的晶须,而钙矾石则以六方片状晶核形式存在。在粉煤灰颗粒表面有通过溶解-结晶机制生成的水化产物。在水化后期,CSH成为无特征形貌的致密浆体,其中分布有充分发育的棒状钙矾石晶体。粉煤灰颗粒由表面生成的水化产物与周围的浆体紧密结合成为一个整体。 相似文献
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使用活性低的矿渣作为细骨料配制矿渣砂混凝土,将该混凝土与使用普通河砂的混凝土进行强度实验对比,并通过扫描电子显微镜观察混凝土硬化浆体中矿渣砂和普通河砂的微观形貌,研究了矿渣砂作为细骨料使用时对混凝土强度的影响。结果显示:无论是在标准养护条件还是高温蒸养条件下,矿渣砂混凝土各个龄期的抗压强度都略低于普通河砂混凝土,但是两者的劈裂抗拉强度相差不大,矿渣砂混凝土后期的劈裂抗拉强度甚至超过普通砂混凝土。部分矿渣砂的表面发生了水化反应,其水化产物与水泥的水化产物相互搭接,对混凝土的劈裂抗拉强度有一定的贡献。 相似文献
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本文通过X射线衍射仪(XRD)、同步热分析仪、扫描电子显微镜(SEM)及能谱仪(EDS)研究了蒸养条件下水泥-磷渣复合胶凝材料一年龄期的水化产物的特征.结果表明:含磷渣的复合胶凝材料并未产生不同于水泥的晶态水化产物,但促进了钙矾石(AFt)向单硫型水化硫铝酸钙(AFm)的转化;1年龄期时,经80℃蒸养的水泥-磷渣复合胶凝材料的硬化浆体中仍能明显观察到未反应的磷渣颗粒;磷渣的火山灰反应消耗了一部分Ca(OH)2,磷渣颗粒与周围结构中的Ca(OH)2及C-S-H凝胶粘结紧密;水泥-磷渣复合胶凝材料水化产生的C-S-H凝胶的Ca/Si比低于纯水泥水化产生的C-S-H凝胶. 相似文献
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The joint shape, microstructure, and shear strength of 95Sn5Sb solder joints with components with different terminal metallizations
(AgPd and Ni/AgPd) were investigated and compared to 62Sn36Pb2Ag solder. The rapid reaction between SnSb solder and AgPd leads
to the solder not spreading entirely on the Cu pad but agglomerating on the component termination. The shear strength of the
SnSb/AgPd solder joint is very low and fracture occurs at the original interface of the AgPd/ceramic. The Ni layer in the
SnSb/Ni/AgPd joint effectively avoids interdiffusion between the AgPd and the solder so that a high-strength solder joint
with an ideal shape is achieved. However, the terminations of the components have little effect on the shape and the shear
strength of the SnPbAg solder joint. Fracture occurs in the SnPbAg solder after shear testing to failure. 相似文献
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为了研究脉冲能量和烧蚀坑重叠率对7075-T6铝基板粘接强度影响, 采用纳秒光纤脉冲激光在粘接区域加工烧蚀坑阵列微结构, 通过表面形貌、剪切强度和断裂模式等实验参量对粘接效果进行了分析。结果表明, 脉冲能量对表面形貌、剪切强度及断裂模式几乎无影响; 随着烧蚀坑重叠率的增加, 表面粗糙度先增加后减小, 表面面积增加比一直增加; 与原始材料相比, 激光处理后剪切强度至少提升150%;当烧蚀坑重叠率为30%时, 粘接区域发生内聚断裂的面积最大, 剪切强度提升最明显; 脉冲能量为880μJ、烧蚀坑重叠率为30%时, 剪切强度为27.76MPa, 提升最大。该研究对激光烧蚀提高7075-T6粘接强度是有帮助的。 相似文献
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Hwa-Teng Lee Ming-Hung Chen Huei-Mei Jao Chin-Jui Hsu 《Journal of Electronic Materials》2004,33(9):1048-1054
This study investigates the influence of adding Sb on the microstructure and adhesive strength of the Sn3.5Ag solder. Both
solidus and liquidus temperatures increase as Sb additions increase. Adding 1.5wt.%Sb leads to the narrowest range (6.6°C)
between the solidus and liquidus temperature of the solder. Adding Sb decomposes the as-soldered ringlike microstructure of
Sn3.5Ag and causes solid-solution hardening. The as-soldered hardness increases with increasing Sb addition. For long-term
storage, adding Sb reduces the size of the rodlike Ag3Sn compounds. The hardness also increases with increasing Sb addition. Adding Sb depresses the growth rate of interfacial
intermetallic compounds (IMCs) layers, but the difference between 1% and 2% Sb is not distinct. For mechanical concern, adding
Sb improves both adhesive strength and thermal resistance of Sn3.5Ag, where 1.5% Sb has the best result. However, adding Sb
causes a variation in adhesive strength during thermal storage. The more Sb is added, the higher the variation reveals, and
the shorter the storage time requires. This strength variation helps the solder joints to resist thermal storage. 相似文献
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Law C.M.T. Wu C.M.L. Yu D.Q. Li M. Chi D.Z. 《Advanced Packaging, IEEE Transactions on》2005,28(2):252-258
Rare earth (RE) elements, primarily La and Ce, were doped in Sn-Zn solder to improve its properties such as wettability. The interfacial microstructure evolution and shear strength of the Sn-9Zn and Sn-9Zn-0.5RE (in wt%) solder bumps on Au/Ni/Cu under bump metallization (UBM) in a ball grid array (BGA) were investigated after thermal aging at 150 /spl deg/C for up to 1000 h. In the as-reflowed Sn-9Zn solder bump, AuSn/sub 4/ intermetallic compounds (IMCs) and Au-Zn circular IMCs formed close to the solder/UBM interface, together with the formation of a Ni-Zn-Sn ternary IMC layer of about 1 /spl mu/m in thickness. In contrast, in the as-reflowed Sn-9Zn-0.5RE solder bump, a spalled layer of Au-Zn was formed above the Ni layer. Sn-Ce-La and Sn-Zn-Ce-La phases were found near the interface at positions near the surface of the solder ball. Upon thermal aging at 150 /spl deg/C, the concentration of Zn in the Ni-Zn-Sn ternary layer of Sn-9Zn increased with aging time. For Sn-9Zn-0.5RE, the Au-Zn layer began to dissolve after 500 h of thermal aging. The shear strength of the Sn-9Zn ball was decreased after the addition of RE elements, although it was still higher than that of the Sn-37Pb and Sn-36Pb-2Ag Pb-bearing solders. The fracture mode of the Sn-9Zn system was changed from ductile to partly brittle after adding the RE elements. This is mainly due to the presence of the brittle Au-Zn layer. 相似文献