外文翻译(中英文)制备及鼓风炉产生的玻璃陶瓷渣性能烧结过程.doc

Preparation and properties of glassceramics derived from blast-furnaceslag by a ceramic-sintering processAbstractGlassceramics were synthesized using ground blast-furnace slag and potash feldspar additives by a conventional ceramic-sintering route. The results show 5 wt% potash feldspar can enhance the sintering properties of blast-furnace slag glass and the results glassceramics have desirable mechanical properties. The main crystalline phase of the obtained glassceramic is gehlenite (2CaO_Al2O3_SiO2). A high microhardness of 5.2 GPa and a bending strength higher than 85 MPa as well as a water absorption lower than 0.14% were obtained. 2009 Elsevier Ltd and Techna Group S.r.l. All rights reserved.1. IntroductionGlassceramics are fine-grained polycrystalline materials formed when glasses of suitable compositions are heat-treated and thus undergo controlled crystallization to reach a lower energy crystalline state 1. Since the early 1960s, using waste to prepare glassceramics has been developed in Russia, by employing slag of ferrous and non-ferrous metallurgy, ashes and wastes from mining and chemical industries 2. Lately, the waste of coal combustion ash, fly ash and filter dusts from waste incinerators, mud from metal hydrometallurgy, pass cement dust, different types of sludge and glass cullet or mixtures of them have been considered for the production of glass ceramics 37. Using waste to prepare glassceramics is significant for industrial applications as well as for environment protection 8The conventional approaches to sinter glassceramics usually include two steps: first vitrifying raw materials at a high temperature (13001500 8C) and then following a nucleation and crystal growth step. The disadvantage of the conventional route is that it is difficult to vitrify the raw materials and the high energy consumption in this step. An alternative manufacturing method to produce sintered glass. ceramics, in which sintering and crystallization of fine glass powders take place simultaneously, has recently been reported9. In such route fine glass powders are pressed and sintered, and the crystallization occurs with densification. However, this route also needs a short time to vitrify raw materials at high temperature for preliminary glass-making.The blast-furnace slag is formed in the processes of pig iron manufacture from iron ore, contains combustion residue of coke, fluxes of limestone or serpentine, and other materials. If the molten slag was cooled quickly by high-pressure water, fine grain glass of vitreous CaAlMg silicate can be formed 10. This suggests the blast-furnace slag can be used as a glass source to make sintered glassceramics and vitrifying raw materials at high-temperature step can be omitted. The free glass surfaces are preferable sites for devitrification and thus crystallization may occur without any nucleating agent. Therefore, the finely ground slag powder can used as the main component of parent glass. Comparing with the two sintered methods mentioned above, a remarkable advantage of the present study is absent of vitrification step because of the using of blast-furnace slag. Thus a low energy cost and manufacture simplicity can be expected. However, in our previous studies glassceramics prepared with pure blastfurnace slag show poor properties 11. Therefore, some sintering additives are needed. In this study, we show when using blast-furnace slag to prepare glassceramics by a conventional ceramics route, if suitable amount of potashfeldspar is added. Glassceramics with high microhardness andbending strength as well as lower water absorption can be obtained.2. Experimental procedureThe slag (provided by Anyang iron Corporation of China) was pulverized by ball milling for about 24 h (size in the range of 1020 mm), and then blended with 510 wt% potash feldspar powder. The mixtures were ball milling for 2 h. We use K5, K8 and K10 to denote the weight percent of potash feldspar in the samples.The process used in our study is illustrated in Fig. 1. The blended powders were uniaxially pressed in a steel die at room temperature, using a hydraulic pressure of 4060 MP a without any binder. The obtained green bodies were sintered in air at nucleation temperature of 720760 and crystallization temperature of 800900 for different times (from 20 to 60 min), with heating rates of 25 /min, followed by a hightemperature treatment at 1200The blended powders were examined by differential scanning calorimetry (DSC) (Labsys, Setaram, France) in air with a heating rate of 10 /min from room temperature to 1100 . The phase of the blast-furnace slag and obtained glassceramics were examined by X-ray diffraction (XRD) (Model D/MAX-3B, RIGAKU, Japan). The samples surfaces were polished and corroded in HF (5 vol%) for 20 s and then observed by scanning electron microscopy (SEM) (Model JSM-5610LV, JEOL, Japan). The density of the samples was measured by the Archimedes method. The microhardness was measured by a microhardness-tester (Model HX- 1000TM, Taiming, China) with a measuring force of 9.807 N and a load time 20 s. Samples for bending strength tests with dimensions of 3 mm _ 4 mm_ 30 mm were carefully polished and tested by a universal testing machine (Zwick/Roell Z030, Germany). The chemical resistance of glassceramics was tested by a chemical etch method. The samples were corroded in the HCl (0.5 vol%) and NaOH (0.5 vol%) solution for 95 h and then the residual rate was calculated.3. Results and discussionTable 1 shows the chemical composition of blast-furnace slag obtained by X-ray fluorescence. The nominal composition of the blended mixture is given in Table.2. Fig.2 shows the XRD patterns of the blast-furnace slag.It can be seen that the chemical composition of the slag involves SiO2, CaO, Al2O3, and MgO as its major components. Fe2O3 and TiO2 that act as nucleating agents can greatly enhance the crystallization. Due the presence of Fe2O3 and TiO2, other nucleating agents are not needed. A small amount of gehlenite exists in the amorphous glass( Fig.2). The primary-precipitated phase can act as heterogeneous nucleating centers. In fact, crystallization is favored at the surface of glass particles and primary-precipitated phase, since nuclei may be formed without the impedance of the surrounding materials, taking into account the volume variation from glass to crystal.Fig.3shows the DSC curves of the blended mixture. The small endothermic peak (737741 ) indicates the molecular rearrangement in this temperature. The exothermic peak (800900 ) corresponds to the crystallization reaction of the glass. With 5 wt% potash feldspar additive, the glass powders have an intense exothermic effect at 840 , indicating the formation and growth crystals. With more potash feldspar additive, the exothermic peak increases slightly. Therefore, a nucleationtemperature in the range of 720760 and a crystallization temperature in the range of 800900 were employed, respectively.Fig.4shows the SEM images of the samples. The results show that crystallization is mainly induced by surface nucleation in samples K8 and K10, but by both surface and bulk nucleation in sample K5 since crystallization take place throughout the entire volume in the sample. Uniform, ultrafine crystalline grains with sizes of 25 mm exist in sample K5. In contrast, there are only small amounts of crystalline phases in K8 and K10 as shown by XRD patterns (Fig.5). Alkali feldspar crystals are known to give excellent glasses but they are unable to be crystallized in practical periods of time. They have been successfully developed by exploiting the tendency of powdered glass to devitrify during appropriate heat treatments in recent works . Our results show glass powder with 5 wt% potash feldspar can be successfully devitrified during the heat treatment because potash feldspar can act as fluxing agents during sintering process thus decrease the sintering temperature and reduce the viscosity of glass. The value of viscosity during sintering and crystallization is very important. If the value of viscosity is too low, crystallization will be too fast, which can hinder sintering and creates a large amount of porosities. On the other hand, if the value of viscosity is too high, crystallization is difficult. Therefore, controlling the glass viscosity is very important. With more potash feldspar additive, the crystallization rate of the glass will decrease. According to our experimental data add 5 wt% potash feldspar will be an appropriate amount.制备及鼓风炉产生的玻璃陶瓷渣性能烧结过程摘要微晶玻璃利用地面合成高炉矿渣和钾肥由传统陶瓷烧结路线长石添加剂。结果显示5 wt的钾长石可以提高高炉矿渣微晶玻璃的烧结性能，结果玻璃陶瓷具有理想的力学性能。所获得的主要晶相玻璃Ceramic是gehlenite（2CaO氧化铝二氧化硅）。高硬度的5.2 GPa和弯曲强度高于85兆帕以及吸水率低于0.14获得。2009爱思唯尔集团有限公司和Techna S.r.l.保留所有权利。1简介微晶玻璃是细晶材料时形成合适的眼镜组成热处理，从而达到控制结晶接受较低的能源结晶状态。20世纪60年代初以来，利用废旧准备微晶玻璃在俄罗斯已经制定了雇用采矿和化学工业，黑色和有色金属冶金，灰烬和废物渣。最近，煤炭燃烧废弃物粉煤灰，粉煤灰从湿法冶炼金属灰和过滤粉尘废弃物焚化炉，泥浆，通过水泥粉尘，污泥和玻璃碎玻璃或它们的混合物，不同类型的被认为对玻璃陶瓷3生产-7。用废准备玻璃陶瓷工业应用对环境的保护以及显着。对烧结玻璃陶瓷的传统方法通常包括两个步骤：首先在一个较高的玻璃化温度的原材料（1300-15008C条），然后下面的成核和晶体生长的一步。而传统路由的缺点是，它是很难玻璃化的原材料和在此步骤中能耗高。另一种制造方法，生产烧结玻璃。陶瓷，其中玻璃烧结和细粉末结晶同时发生，最近有报道。该高炉矿渣是在猪铁从铁矿石制造过程中形成的，包含燃烧残留焦炭，石灰石或蛇纹石通量和其他材料。如果冷却液渣用高压水，玻璃体钙铝镁硅酸盐细晶玻璃能迅速形成。这表明，高炉炉渣可作为源使用，使玻璃在高温烧结步玻璃陶瓷和玻璃化原料可以省略。免费的脱玻化玻璃表面是最好的网站，因此没有任何可能发生的结晶成核剂。因此，磨细矿渣粉可以作为家长玻璃的主要成分。与上述两种烧结方法相比，一本研究的显着优点是由于玻璃化高炉矿渣使用STEP缺席。因此，一个低能源成本和制造简单可以预期。然而，在我们以前的研究显示玻璃与陶瓷材料制备纯矿渣性能差。因此，一些烧结添加剂是必要的。在这项研究中，我们证明在使用高炉矿渣准备通过一条路线传统陶瓷玻璃陶瓷，如果potashfeldspar适量添加。玻璃硬度高andbending强度以及低吸水性，陶瓷可以得到。2实验过程矿渣（由安阳钢铁公司提供的中国）是由球磨粉碎约24小时（1020毫米范围的大小），然后用510 wt的钾长石粉混合。该混合物球磨2小时我们使用K5号的K8和K10来表示钾肥样品中长石重量百分比。在我们的研究中使用的过程如图所示。1。混合粉末的单轴压在在室温下钢模具，采用无任何粘结剂40-60国会议员的液压压力。所获得的绿色尸体在空气中烧结温度为720-760成核和结晶800-900不同时间（从20到60分钟）温度，加热速率2-5/分钟一个高温之后，在1200处理。该混合粉末进行了研究用差示扫描量热法（DSC）在空气中（Labsys，塞塔拉姆，法国）108C/min速率从室温加热到11008C条。该高炉矿渣，并获得微晶玻璃相，用X射线衍射仪（XRD）（型号D/MAX-3B，日本理学，日本）。样品表面进行了抛光和侵蚀的短波20秒（5 vol的），然后用扫描电子